page	source_page_order	layout_page_order	layout_order	ref	label	role_guess	included_in_body	excluded_risk_level	body_decision_reason	parser_body_decision_reason	production_usage	visual_asset_type	visual_asset_label	visual_asset_caption_preview	truncation_marker	inside_body_region	body_region_id	zone	column	column_index	column_count	region_id	background_rgb	background_class	is_gray_background	has_frame_evidence	bbox	text_preview	cleaned_text_preview	text	cleaned_text
1	2	1	0	#/texts/1	page_header	page_header	False	low	docling_page_header	docling_page_header						False	None	top_margin	column_2_of_2	2	2	p1:top_margin:column_2_of_2:colored	[130, 171, 211]	colored	False	True	[519.14, 60.77, 38.3, 6.98]	Perspective	Perspective	Perspective	Perspective
1	3	2	1	#/texts/2	text	metadata	False	low	document_web_address	document_web_address						False	None	page_body	column_2_of_2	2	2	p1:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[504.74, 77.04, 59.66, 6.98]	pubs.acs.org/JPCL	pubs.acs.org/JPCL	pubs.acs.org/JPCL	pubs.acs.org/JPCL
1	4	3	2	#/texts/3	section_header	title_candidate	False	low	non_body_heading	non_body_heading						True	p1:body_region:0	page_body	column_1_of_2	1	2	p1:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 116.21, 480.4, 37.86]	High-Energy Cathode Materials (Li2MnO3 -LiMO2) for Lithium-Ion Batteries	High-Energy Cathode Materials (Li2MnO3 -LiMO2) for Lithium-Ion Batteries	High-Energy Cathode Materials (Li2MnO3 -LiMO2) for Lithium-Ion Batteries	High-Energy Cathode Materials (Li2MnO3 -LiMO2) for Lithium-Ion Batteries
1	5	4	3	#/texts/4	text	affiliation	False	low	front_matter_author_line	front_matter_author_line						True	p1:body_region:0	page_body	column_1_of_2	1	2	p1:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 156.08, 173.08, 17.32]	Haijun Yu † and Haoshen Zhou * , † , ‡	Haijun Yu † and Haoshen Zhou * , † , ‡	Haijun Yu † and Haoshen Zhou * , † , ‡	Haijun Yu † and Haoshen Zhou * , † , ‡
1	6	5	4	#/texts/5	footnote	footnote	False	low	docling_footnote	docling_footnote						True	p1:body_region:0	page_body	column_1_of_2	1	2	p1:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 179.44, 503.93, 24.77]	† Energy Technology Research Institute, National Institute of Advanced Industrial Science and Technology (AIST), Umezono 1-1-1, Tsukuba, 305-8568, Japan	† Energy Technology Research Institute, National Institute of Advanced Industrial Science and Technology (AIST), Umezono 1-1-1, Tsukuba, 305-8568, Japan	† Energy Technology Research Institute, National Institute of Advanced Industrial Science and Technology (AIST), Umezono 1-1-1, Tsukuba, 305-8568, Japan	† Energy Technology Research Institute, National Institute of Advanced Industrial Science and Technology (AIST), Umezono 1-1-1, Tsukuba, 305-8568, Japan
1	7	6	5	#/texts/6	footnote	footnote	False	low	docling_footnote	docling_footnote						True	p1:body_region:0	page_body	column_1_of_2	1	2	p1:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 204.44, 503.98, 24.77]	‡ National Laboratory of Solid state Microstructures & Department of Energy Science and Engineering, Nanjing University, Nanjing 210093, China	‡ National Laboratory of Solid state Microstructures & Department of Energy Science and Engineering, Nanjing University, Nanjing 210093, China	‡ National Laboratory of Solid state Microstructures & Department of Energy Science and Engineering, Nanjing University, Nanjing 210093, China	‡ National Laboratory of Solid state Microstructures & Department of Energy Science and Engineering, Nanjing University, Nanjing 210093, China
1	1	7	6	#/texts/0	page_header	page_header	False	low	docling_page_header	docling_page_header						False	None	page_body	column_1_of_2	1	2	p1:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[3.61, 229.45, 15.98, 342.05]	Downloaded via JILIN UNIV on July 12, 2026 at 04:31:17 (UTC). See https:/pubs.acs.org/sharingguidelines for options on how to legitimately share published articles.	Downloaded via JILIN UNIV on July 12, 2026 at 04:31:17 (UTC). See https:/pubs.acs.org/sharingguidelines for options on how to legitimately share published articles.	Downloaded via JILIN UNIV on July 12, 2026 at 04:31:17 (UTC). See https:/pubs.acs.org/sharingguidelines for options on how to legitimately share published articles.	Downloaded via JILIN UNIV on July 12, 2026 at 04:31:17 (UTC). See https:/pubs.acs.org/sharingguidelines for options on how to legitimately share published articles.
1	8	8	7	#/texts/7	text	abstract_candidate	False	medium	inline_abstract	inline_abstract						True	p1:body_region:0	page_body	column_1_of_2	1	2	p1:page_body:column_1_of_2:colored	[255, 242, 208]	colored	False	False	[69.45, 247.25, 341.67, 111.16]	ABSTRACT: Lithium-rich layered oxide materials x Li2MnO3 · (1 -x )LiMO2 (M = Mn, Ni, Co, Fe, Cr, etc.) have attracted much attention for the use of cathode materials in lithiumion batteries in recent years. However, the…	ABSTRACT: Lithium-rich layered oxide materials x Li2MnO3 · (1 -x )LiMO2 (M = Mn, Ni, Co, Fe, Cr, etc.) have attracted much attention for the use of cathode materials in lithiumion batteries in recent years. However, the…	ABSTRACT: Lithium-rich layered oxide materials x Li2MnO3 · (1 -x )LiMO2 (M = Mn, Ni, Co, Fe, Cr, etc.) have attracted much attention for the use of cathode materials in lithiumion batteries in recent years. However, there are many issues still unclear (the structure and reaction mechanism are ambiguous until now), and numerous scienti fi c challenges (low initial Coulombic e ffi ciency, poor rate capability, and voltage degradation during cycling) of these materials that must be overcome to realize their utilization in commercial lithium-ion batteries. This Perspective focuses on the challenges and prospects associated with the current researching results of these lithium-rich layered cathode materials. Speci fi cally, their average/local structures, reaction mechanisms, and electrochemical properties are discussed.	ABSTRACT: Lithium-rich layered oxide materials x Li2MnO3 · (1 -x )LiMO2 (M = Mn, Ni, Co, Fe, Cr, etc.) have attracted much attention for the use of cathode materials in lithiumion batteries in recent years. However, there are many issues still unclear (the structure and reaction mechanism are ambiguous until now), and numerous scienti fi c challenges (low initial Coulombic e ffi ciency, poor rate capability, and voltage degradation during cycling) of these materials that must be overcome to realize their utilization in commercial lithium-ion batteries. This Perspective focuses on the challenges and prospects associated with the current researching results of these lithium-rich layered cathode materials. Speci fi cally, their average/local structures, reaction mechanisms, and electrochemical properties are discussed.
1	9	9	8	#/texts/8	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p1:body_region:0	page_body	column_1_of_2	1	2	p1:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 409.33, 240.06, 123.08]	A s the problems of fossil energy exhaustion, global warming, and environment pollution plague modern society, sustainable energies have gradually become a worldwide topic. There have also been increasing demands for wi…	A s the problems of fossil energy exhaustion, global warming, and environment pollution plague modern society, sustainable energies have gradually become a worldwide topic. There have also been increasing demands for wi…	A s the problems of fossil energy exhaustion, global warming, and environment pollution plague modern society, sustainable energies have gradually become a worldwide topic. There have also been increasing demands for wind or solar power stations and low-emission or zero-emission electric vehicles. Lithium-ion batteries are of great signi fi cance as power sources to satisfy these demands and realize a lowcarbon society. 1 -5 However, the energy density of current lithium-ion batteries is still not enough for market requirements, and their cost and environment-related issues should be also considered for much broader market penetration. 6,7	A s the problems of fossil energy exhaustion, global warming, and environment pollution plague modern society, sustainable energies have gradually become a worldwide topic. There have also been increasing demands for wind or solar power stations and low-emission or zero-emission electric vehicles. Lithium-ion batteries are of great signi fi cance as power sources to satisfy these demands and realize a lowcarbon society. 1 -5 However, the energy density of current lithium-ion batteries is still not enough for market requirements, and their cost and environment-related issues should be also considered for much broader market penetration. 6,7
1	10	10	9	#/texts/9	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p1:body_region:0	page_body	column_1_of_2	1	2	p1:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 534.71, 239.99, 132.68]	Owing to the key roles of cathode materials on energy density and the cost of current lithium-ion batteries, several alternative cathode materials, such as LiCoO2, LiNi0.8 Co0.15 Al0.05O2, LiNi0.33 Co0.33Mn0.33O2, spine…	Owing to the key roles of cathode materials on energy density and the cost of current lithium-ion batteries, several alternative cathode materials, such as LiCoO2, LiNi0.8 Co0.15 Al0.05O2, LiNi0.33 Co0.33Mn0.33O2, spine…	Owing to the key roles of cathode materials on energy density and the cost of current lithium-ion batteries, several alternative cathode materials, such as LiCoO2, LiNi0.8 Co0.15 Al0.05O2, LiNi0.33 Co0.33Mn0.33O2, spinel LiMn2O4, olive LiFePO4, and so on, have been commercially used in lithium ion batteries. 3,4 However, the available rechargeable capacity for all of these materials almost approaches their limits (120 -200 mAh/g), thus cathode materials associated with higher speci fi c capacity are needed to meet the demand for further energy density enhancement of lithium-ion batteries. During the past two decades, much e ff ort on exploiting new cathode materials has been done (Figure 1). 3,7 -10	Owing to the key roles of cathode materials on energy density and the cost of current lithium-ion batteries, several alternative cathode materials, such as LiCoO2, LiNi0.8 Co0.15 Al0.05O2, LiNi0.33 Co0.33Mn0.33O2, spinel LiMn2O4, olive LiFePO4, and so on, have been commercially used in lithium ion batteries. 3,4 However, the available rechargeable capacity for all of these materials almost approaches their limits (120 -200 mAh/g), thus cathode materials associated with higher speci fi c capacity are needed to meet the demand for further energy density enhancement of lithium-ion batteries. During the past two decades, much e ff ort on exploiting new cathode materials has been done (Figure 1). 3,7 -10
1	11	11	10	#/texts/10#prov0	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p1:body_region:0	bottom_margin	column_1_of_2	1	2	p1:bottom_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 669.75, 239.98, 89.31]	Among the reported cathode materials so far, the lithium-rich layered oxide materials (LLOs) have attracted much attention in recent years because their capacities can be larger than 280 mAhg -1 with 3.6 V or larger ope…	Among the reported cathode materials so far, the lithium-rich layered oxide materials (LLOs) have attracted much attention in recent years because their capacities can be larger than 280 mAhg -1 with 3.6 V or larger ope…	Among the reported cathode materials so far, the lithium-rich layered oxide materials (LLOs) have attracted much attention in recent years because their capacities can be larger than 280 mAhg -1 with 3.6 V or larger operating voltages when these materials are charged to over 4.6 V at room temperature. 11 -15 These LLOs can be described with two completely di ff erent notations: x Li2MnO3 · (1 -x )LiMO2 (M = Mn, Ni, Co, Fe, Cr, etc.) and Li 1+( x /(2+ x ))M ′ 1 -( x /(2+ x ))O2 (M ′ = Mn+M). Both	Among the reported cathode materials so far, the lithium-rich layered oxide materials (LLOs) have attracted much attention in recent years because their capacities can be larger than 280 mAhg -1 with 3.6 V or larger operating voltages when these materials are charged to over 4.6 V at room temperature. 11 -15 These LLOs can be described with two completely di ff erent notations: x Li2MnO3 · (1 -x )LiMO2 (M = Mn, Ni, Co, Fe, Cr, etc.) and Li 1+( x /(2+ x ))M ′ 1 -( x /(2+ x ))O2 (M ′ = Mn+M). Both
1	20	12	11	#/texts/18	page_footer	page_footer	False	low	first_page_metadata	first_page_metadata						True	p1:body_region:0	bottom_margin	column_1_of_2	1	2	p1:bottom_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[168.49, 771.47, 95.03, 5.58]	© 2013 American Chemical Society	© 2013 American Chemical Society	© 2013 American Chemical Society	© 2013 American Chemical Society
1	13	13	12	#/texts/11	caption	caption	False	low	outside_body_flow_caption	outside_body_flow_caption						False	None	page_body	column_2_of_2	2	2	p1:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 595.55, 239.98, 17.9]	Figure 1. Voltage and capacity of the main cathode materials for lithium-ion batteries.	Figure 1. Voltage and capacity of the main cathode materials for lithium-ion batteries.	Figure 1. Voltage and capacity of the main cathode materials for lithium-ion batteries.	Figure 1. Voltage and capacity of the main cathode materials for lithium-ion batteries.
1	12	14	13	#/texts/10#prov1	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						False	None	page_body	column_2_of_2	2	2	p1:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 635.06, 240.04, 74.79]	notations are equal to the same material and have been used extensively in the published literature. For example, the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 material can also be described as Li[Li 0.2 Mn0.567 Ni0.166 C…	notations are equal to the same material and have been used extensively in the published literature. For example, the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 material can also be described as Li[Li 0.2 Mn0.567 Ni0.166 C…	notations are equal to the same material and have been used extensively in the published literature. For example, the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 material can also be described as Li[Li 0.2 Mn0.567 Ni0.166 Co0.067]O2. 13 -15 In this Perspective, we will focus on the challenges and prospects of these LLOs with three sections for the next-generation lithiumion batteries. In the fi rst section, the design theory and average/	notations are equal to the same material and have been used extensively in the published literature. For example, the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 material can also be described as Li[Li 0.2 Mn0.567 Ni0.166 Co0.067]O2. 13 -15 In this Perspective, we will focus on the challenges and prospects of these LLOs with three sections for the next-generation lithiumion batteries. In the fi rst section, the design theory and average/
1	15	15	14	#/texts/13	text	metadata	False	low	first_page_metadata	first_page_metadata						True	p1:body_region:0	page_body	column_2_of_2	2	2	p1:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[367.99, 727.13, 54.32, 7.92]	January 7, 2013	January 7, 2013	January 7, 2013	January 7, 2013
1	14	16	15	#/texts/12	text	metadata	False	low	first_page_metadata	first_page_metadata						True	p1:body_region:0	page_body	column_2_of_2	2	2	p1:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 727.21, 34.65, 7.77]	Received:	Received:	Received:	Received:
1	17	17	16	#/texts/15	text	metadata	False	low	first_page_metadata	first_page_metadata						True	p1:body_region:0	page_body	column_2_of_2	2	2	p1:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[367.99, 738.19, 55.06, 7.92]	March 28, 2013	March 28, 2013	March 28, 2013	March 28, 2013
1	16	18	17	#/texts/14	text	unknown_text	False	medium	outside_body_flow	outside_body_flow						True	p1:body_region:0	page_body	column_2_of_2	2	2	p1:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 738.27, 35.4, 7.77]	Accepted:	Accepted:	Accepted:	Accepted:
1	19	19	18	#/texts/17	text	metadata	False	low	first_page_metadata	first_page_metadata						True	p1:body_region:0	bottom_margin	column_2_of_2	2	2	p1:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[367.99, 749.19, 55.06, 7.92]	March 28, 2013	March 28, 2013	March 28, 2013	March 28, 2013
1	18	20	19	#/texts/16	text	metadata	False	low	first_page_metadata	first_page_metadata						True	p1:body_region:0	bottom_margin	column_2_of_2	2	2	p1:bottom_margin:column_2_of_2:white	[254, 254, 254]	white	False	False	[324.45, 749.27, 37.75, 7.77]	Published:	Published:	Published:	Published:
1	22	21	20	#/texts/20	page_footer	page_footer	False	low	first_page_metadata	first_page_metadata						False	None	bottom_margin	column_2_of_2	2	2	p1:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[387.33, 769.98, 177.16, 7.74]	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280
1	21	22	21	#/texts/19	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						True	p1:body_region:0	bottom_margin	column_2_of_2	2	2	p1:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[304.5, 770.73, 15.93, 6.54]	1268	1268	1268	1268
2	1	1	22	#/texts/21	page_header	page_header	False	low	docling_page_header	docling_page_header						True	p2:body_region:0	top_margin	column_1_of_2	1	2	p2:top_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 48.93, 181.19, 8.72]	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters
2	3	2	23	#/texts/23	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p2:body_region:0	page_body	column_1_of_2	1	2	p2:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 69.37, 239.98, 52.8]	local structures are discussed. The second section discusses the reaction mechanisms, especially the fi rst charge and discharge processes. The third section describes the electrochemical performance, current main probl…	local structures are discussed. The second section discusses the reaction mechanisms, especially the fi rst charge and discharge processes. The third section describes the electrochemical performance, current main probl…	local structures are discussed. The second section discusses the reaction mechanisms, especially the fi rst charge and discharge processes. The third section describes the electrochemical performance, current main problems, and improving methods of these LLOs.	local structures are discussed. The second section discusses the reaction mechanisms, especially the fi rst charge and discharge processes. The third section describes the electrochemical performance, current main problems, and improving methods of these LLOs.
2	4	3	24	#/texts/24	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p2:body_region:0	page_body	column_1_of_2	1	2	p2:page_body:column_1_of_2:colored	[255, 242, 208]	colored	False	False	[88.5, 135.92, 183.96, 109.37]	The rechargeable capacity and energy density of LLO materials at room temperature can be close to 280 mAhg -1 and 1000 Whkg -1 , respectively, which are about twice that of current commercial cathode materials for lithi…	The rechargeable capacity and energy density of LLO materials at room temperature can be close to 280 mAhg -1 and 1000 Whkg -1 , respectively, which are about twice that of current commercial cathode materials for lithi…	The rechargeable capacity and energy density of LLO materials at room temperature can be close to 280 mAhg -1 and 1000 Whkg -1 , respectively, which are about twice that of current commercial cathode materials for lithium ion batteries.	The rechargeable capacity and energy density of LLO materials at room temperature can be close to 280 mAhg -1 and 1000 Whkg -1 , respectively, which are about twice that of current commercial cathode materials for lithium ion batteries.
2	5	4	25	#/texts/25	caption	caption	False	low	docling_caption	docling_caption						True	p2:body_region:0	page_body	column_1_of_2	1	2	p2:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 262.87, 239.98, 32.52]	These LLOs were fi rst researched as cathode materials for rechargeable lithium batteries by Thackeray et al. when they were researching the LiMnO2 layered materials. 16,17 In 1991,	These LLOs were fi rst researched as cathode materials for rechargeable lithium batteries by Thackeray et al. when they were researching the LiMnO2 layered materials. 16,17 In 1991,	These LLOs were fi rst researched as cathode materials for rechargeable lithium batteries by Thackeray et al. when they were researching the LiMnO2 layered materials. 16,17 In 1991,	These LLOs were fi rst researched as cathode materials for rechargeable lithium batteries by Thackeray et al. when they were researching the LiMnO2 layered materials. 16,17 In 1991,
2	2	5	26	#/texts/22	page_header	page_header	False	low	docling_page_header	docling_page_header						True	p2:body_region:1	top_margin	column_2_of_2	2	2	p2:top_margin:column_2_of_2:colored	[125, 168, 209]	colored	False	True	[519.14, 50.28, 38.3, 6.98]	Perspective	Perspective	Perspective	Perspective
2	6	6	27	#/texts/26#prov0	text	caption_continuation	False	low	caption_continuation_used_by_asset	inside_front_matter	caption_continuation_used_by_asset	figure	Fig. 2	Figure 2. Crystal structure of the (a) rhombohedral LiMO2 structure (space group: R 3 ̅ m , M = Ni, Co, Mn, Fe, Cr, etc.) and (b) monoclinic Li2MnO3 structure (space group: C 2/ m ) viewed from the [100] crystallographi…		True	p2:body_region:1	page_body	column_2_of_2	2	2	p2:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 67.46, 240.03, 226.77]	inspired by Hunter ' s discovery that acid treatment of the spinel LiMn2O4 yielded λ -MnO2 with a Mn2O4 spinel framework, Thackeray et al. synthesized the layered lithium -manganese oxide compound Li2 -x MnO3 -x /2 (0 <…	inspired by Hunter ' s discovery that acid treatment of the spinel LiMn2O4 yielded λ -MnO2 with a Mn2O4 spinel framework, Thackeray et al. synthesized the layered lithium -manganese oxide compound Li2 -x MnO3 -x /2 (0 <…	inspired by Hunter ' s discovery that acid treatment of the spinel LiMn2O4 yielded λ -MnO2 with a Mn2O4 spinel framework, Thackeray et al. synthesized the layered lithium -manganese oxide compound Li2 -x MnO3 -x /2 (0 < x < 2) with a cubic-closepacked oxygen anion array by chemical leaching of Li2O from the rock salt phase Li2MnO3 (Li2O · MnO2) with acid at 25 ° C, a n d g o t t h e c o m p o u n d L i 1 . 0 9 Mn0.91 O 2 o r 0.2Li2MnO3 · 0.8LiMnO2 after relithiation in an electrochemical cell. 16,17 The structure stability of this compound is much better than that of the pure layered LiMnO 2 cathode material during electrochemical cycling, and then the x Li2MnO3 · (1 -x )LiMnO2 material concept is fi rst introduced. When Kalyani et al. fi rst found that the monoclinic Li2MnO3 material could be activated electrochemically by charging the Li/Li2MnO3 cell to 4.5 V, the x Li2MnO3 · (1 -x )LiMO2 (M = Mn, Ni, Co, Fe, Cr, etc.) materials became more and more attractive. 18 This notation can not only describe the electrochemical processes of these LLOs combining with the single LiMO2 (M = Mn, Ni, Co, Fe, Cr, etc.) and Li2MnO3 component electrochemical process, but also indicates that the cathode materials for lithium	inspired by Hunter ' s discovery that acid treatment of the spinel LiMn2O4 yielded λ -MnO2 with a Mn2O4 spinel framework, Thackeray et al. synthesized the layered lithium -manganese oxide compound Li2 -x MnO3 -x /2 (0 < x < 2) with a cubic-closepacked oxygen anion array by chemical leaching of Li2O from the rock salt phase Li2MnO3 (Li2O · MnO2) with acid at 25 ° C, a n d g o t t h e c o m p o u n d L i 1 . 0 9 Mn0.91 O 2 o r 0.2Li2MnO3 · 0.8LiMnO2 after relithiation in an electrochemical cell. 16,17 The structure stability of this compound is much better than that of the pure layered LiMnO 2 cathode material during electrochemical cycling, and then the x Li2MnO3 · (1 -x )LiMnO2 material concept is fi rst introduced. When Kalyani et al. fi rst found that the monoclinic Li2MnO3 material could be activated electrochemically by charging the Li/Li2MnO3 cell to 4.5 V, the x Li2MnO3 · (1 -x )LiMO2 (M = Mn, Ni, Co, Fe, Cr, etc.) materials became more and more attractive. 18 This notation can not only describe the electrochemical processes of these LLOs combining with the single LiMO2 (M = Mn, Ni, Co, Fe, Cr, etc.) and Li2MnO3 component electrochemical process, but also indicates that the cathode materials for lithium
2	7	7	28	#/texts/27	caption	caption	False	low	outside_body_flow_caption	outside_body_flow_caption						False	None	bottom_margin	column_1_of_2	1	2	p2:bottom_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 702.98, 503.98, 59.97]	Figure 2. Crystal structure of the (a) rhombohedral LiMO2 structure (space group: R 3 ̅ m , M = Ni, Co, Mn, Fe, Cr, etc.) and (b) monoclinic Li2MnO3 structure (space group: C 2/ m ) viewed from the [100] crystallographi…	Figure 2. Crystal structure of the (a) rhombohedral LiMO2 structure (space group: R 3 ̅ m , M = Ni, Co, Mn, Fe, Cr, etc.) and (b) monoclinic Li2MnO3 structure (space group: C 2/ m ) viewed from the [100] crystallographi…	Figure 2. Crystal structure of the (a) rhombohedral LiMO2 structure (space group: R 3 ̅ m , M = Ni, Co, Mn, Fe, Cr, etc.) and (b) monoclinic Li2MnO3 structure (space group: C 2/ m ) viewed from the [100] crystallographic direction. (c) Synchrotron powder X-ray di ff raction pattern and Rietveld re fi nement pro fi le of the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 material with rhombohedral and monoclinic structures. Reprinted with permission from ref 13. Copyright 2012 Royal Society of Chemistry. (d) Bragg fi ltered high-angle annular dark fi eld scanning transmission electron microscopy (STEM-HAADF) image of the Li1.2Mn0.61Ni0.18Mg0.01O2 material, containing Li 2 MnO3 parts (blue) and LiNi0.45 Mn0.525Mg0.025O2 ones (green). Reprinted with permission from ref 33. Copyright 2012 American Chemical Society.	Figure 2. Crystal structure of the (a) rhombohedral LiMO2 structure (space group: R 3 ̅ m , M = Ni, Co, Mn, Fe, Cr, etc.) and (b) monoclinic Li2MnO3 structure (space group: C 2/ m ) viewed from the [100] crystallographic direction. (c) Synchrotron powder X-ray di ff raction pattern and Rietveld re fi nement pro fi le of the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 material with rhombohedral and monoclinic structures. Reprinted with permission from ref 13.
2	9	8	29	#/texts/29	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						True	p2:body_region:1	bottom_margin	column_2_of_2	2	2	p2:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[387.33, 773.27, 177.16, 7.74]	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280
2	8	9	30	#/texts/28	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						False	None	bottom_margin	column_2_of_2	2	2	p2:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[304.5, 774.02, 15.93, 6.54]	1269	1269	1269	1269
3	2	1	31	#/texts/30	page_header	page_header	False	low	docling_page_header	docling_page_header						True	p3:body_region:0	top_margin	column_1_of_2	1	2	p3:top_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 48.93, 181.19, 8.72]	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters
3	3	2	32	#/texts/31	page_header	page_header	False	low	docling_page_header	docling_page_header						True	p3:body_region:1	top_margin	column_2_of_2	2	2	p3:top_margin:column_2_of_2:colored	[125, 168, 209]	colored	False	True	[519.14, 50.28, 38.3, 6.98]	Perspective	Perspective	Perspective	Perspective
3	4	3	33	#/texts/32	caption	caption	False	low	outside_body_flow_caption	outside_body_flow_caption						False	None	page_body	column_1_of_2	1	2	p3:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 455.66, 503.95, 42.02]	Figure 3. (a) XRD patterns and (b) hexagonal lattice parameters of the x Li2MnO3 · (1 -x )LiNi1/2Mn1/2O2 ( x = 0, 1/3, 1/2, and 1) materials. Reprinted with permission from ref 40. Copyright 2012 Royal Society of Chemis…	Figure 3. (a) XRD patterns and (b) hexagonal lattice parameters of the x Li2MnO3 · (1 -x )LiNi1/2Mn1/2O2 ( x = 0, 1/3, 1/2, and 1) materials. Reprinted with permission from ref 40.	Figure 3. (a) XRD patterns and (b) hexagonal lattice parameters of the x Li2MnO3 · (1 -x )LiNi1/2Mn1/2O2 ( x = 0, 1/3, 1/2, and 1) materials. Reprinted with permission from ref 40. Copyright 2012 Royal Society of Chemistry. (c) Homogeneous solid solution structure with partial ordered C 2/ m monoclinic phase viewed from the [100] crystallographic direction. (d) Aberration-corrected scanning transmission electron microscopy (STEM) image of the Li[Li0.2Ni0.2Mn0.6]O2 crystal. Reprinted with permission from ref 37. Copyright 2011 American Chemical Society.	Figure 3. (a) XRD patterns and (b) hexagonal lattice parameters of the x Li2MnO3 · (1 -x )LiNi1/2Mn1/2O2 ( x = 0, 1/3, 1/2, and 1) materials. Reprinted with permission from ref 40.
3	1	4	34	#/texts/26#prov1	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p3:body_region:0	page_body	column_1_of_2	1	2	p3:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 509.59, 240.0, 120.09]	ion batteries can be designed with di ff erent contents of LiMO 2 (M = Mn, Ni, Co, Fe, Cr, etc.) and Li2MnO3 components, realizing the variational electrochemical performances (rechargeable capacity, rate performance, a…	ion batteries can be designed with di ff erent contents of LiMO 2 (M = Mn, Ni, Co, Fe, Cr, etc.) and Li2MnO3 components, realizing the variational electrochemical performances (rechargeable capacity, rate performance, a…	ion batteries can be designed with di ff erent contents of LiMO 2 (M = Mn, Ni, Co, Fe, Cr, etc.) and Li2MnO3 components, realizing the variational electrochemical performances (rechargeable capacity, rate performance, and cycle stability) of lithium ion batteries. 11,19 -24 Following this materials designation proposition, many other composite materials between Li2NO3 (N = Mn, Ti, and Zr) and layered LiMO2 (M = Mn, Ni, Co, Fe, Cr, etc.) or spinel LiMn2O4 have also been proposed and researched during the past decade. 25 -28 Among them, these LLOs are hot topics of research for their high energy density and low cost.	ion batteries can be designed with di ff erent contents of LiMO 2 (M = Mn, Ni, Co, Fe, Cr, etc.) and Li2MnO3 components, realizing the variational electrochemical performances (rechargeable capacity, rate performance, and cycle stability) of lithium ion batteries. 11,19 -24 Following this materials designation proposition, many other composite materials between Li2NO3 (N = Mn, Ti, and Zr) and layered LiMO2 (M = Mn, Ni, Co, Fe, Cr, etc.) or spinel LiMn2O4 have also been proposed and researched during the past decade. 25 -28 Among them, these LLOs are hot topics of research for their high energy density and low cost.
3	5	5	35	#/texts/33	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p3:body_region:0	page_body	column_1_of_2	1	2	p3:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 632.0, 240.0, 108.98]	Owing to the importance of the relationship between the structure and electrochemical performance of electrode materials for lithium-ion batteries, it is necessary to reveal the actual structure of these LLOs to deeply …	Owing to the importance of the relationship between the structure and electrochemical performance of electrode materials for lithium-ion batteries, it is necessary to reveal the actual structure of these LLOs to deeply …	Owing to the importance of the relationship between the structure and electrochemical performance of electrode materials for lithium-ion batteries, it is necessary to reveal the actual structure of these LLOs to deeply understand and precisely control their electrochemical performance. Until now, there has been an ongoing debate in the literature on whether these LLOs form homogeneous solid solutions or Li2MnO3 domains within a LiMO2 matrix. 3,20,27,29 -42 In this Perspective, fi rst, we will discuss the pristine structures of these LLOs based on the average and local structures analysis.	Owing to the importance of the relationship between the structure and electrochemical performance of electrode materials for lithium-ion batteries, it is necessary to reveal the actual structure of these LLOs to deeply understand and precisely control their electrochemical performance. Until now, there has been an ongoing debate in the literature on whether these LLOs form homogeneous solid solutions or Li2MnO3 domains within a LiMO2 matrix. 3,20,27,29 -42 In this Perspective, fi rst, we will discuss the pristine structures of these LLOs based on the average and local structures analysis.
3	6	6	36	#/texts/34#prov0	text	unknown_text	False	high	inside_front_matter	inside_front_matter						True	p3:body_region:0	bottom_margin	column_1_of_2	1	2	p3:bottom_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 743.23, 239.97, 21.8]	Figure 2a,b shows the rhombohedral LiMO2 structure (space group: R 3 ̅ m , M = Co, Ni, Mn, Fe, Cr, etc.) and monoclinic	Figure 2a,b shows the rhombohedral LiMO2 structure (space group: R 3 ̅ m , M = Co, Ni, Mn, Fe, Cr, etc.) and monoclinic	Figure 2a,b shows the rhombohedral LiMO2 structure (space group: R 3 ̅ m , M = Co, Ni, Mn, Fe, Cr, etc.) and monoclinic	Figure 2a,b shows the rhombohedral LiMO2 structure (space group: R 3 ̅ m , M = Co, Ni, Mn, Fe, Cr, etc.) and monoclinic
3	7	7	37	#/texts/34#prov1	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p3:body_region:1	bottom_margin	column_2_of_2	2	2	p3:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 509.59, 240.03, 255.43]	Li2MnO3 structure (space group: C 2/ m ) viewed from their [100] crystallographic direction, respectively. As the Li2MnO3 structure can be reformulated with Li[Li 1/3Mn2/3]O2, the monoclinic Li2MnO3 structure is very si…	Li2MnO3 structure (space group: C 2/ m ) viewed from their [100] crystallographic direction, respectively. As the Li2MnO3 structure can be reformulated with Li[Li 1/3Mn2/3]O2, the monoclinic Li2MnO3 structure is very si…	Li2MnO3 structure (space group: C 2/ m ) viewed from their [100] crystallographic direction, respectively. As the Li2MnO3 structure can be reformulated with Li[Li 1/3Mn2/3]O2, the monoclinic Li2MnO3 structure is very similar to the rhombohedral LiMO2 structure, and can be considered as a particular case of LiMO2 with an M layer consisting of a periodic sequence of one Li and two Mn atoms. Thus, both of these two structures can be considered layered α -NaFeO2-type rock salt structures, and all the octahedral sites of their closepacked oxygen arrays are occupied. The experimental synchrotron X-ray di ff raction (SXRD) patterns of the LLO (0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2) is shown as the cyan circles in Figure 2 c. 13 It is clear that all peaks can be well indexed on the basis of LiNiO2 structure with a space group R 3 ̅ m except for those weak peaks around 6.4 -8 ° . These peaks can be indexed to the (020), (110), and (1 ̅ 11) lattice planes of a Li 2 MnO3-like unit cell with monoclinic ( C 2/ m ) symmetry, indicating the existence of Li2MnO3-like phase structure. On the basis of the Rietveld structure re fi nement of this material with di ff erent models by the RIETAN-FP program, the whole di ff raction pattern, including the weak peaks around 6.4 -8 ° , can be re fi ned well if the two-phase model consisting of rhombohedral LiMn0.42Ni0.42Co0.16O2 (space group R 3 ̅ m ) and	Li2MnO3 structure (space group: C 2/ m ) viewed from their [100] crystallographic direction, respectively. As the Li2MnO3 structure can be reformulated with Li[Li 1/3Mn2/3]O2, the monoclinic Li2MnO3 structure is very similar to the rhombohedral LiMO2 structure, and can be considered as a particular case of LiMO2 with an M layer consisting of a periodic sequence of one Li and two Mn atoms. Thus, both of these two structures can be considered layered α -NaFeO2-type rock salt structures, and all the octahedral sites of their closepacked oxygen arrays are occupied. The experimental synchrotron X-ray di ff raction (SXRD) patterns of the LLO (0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2) is shown as the cyan circles in Figure 2 c. 13 It is clear that all peaks can be well indexed on the basis of LiNiO2 structure with a space group R 3 ̅ m except for those weak peaks around 6.4 -8 ° . These peaks can be indexed to the (020), (110), and (1 ̅ 11) lattice planes of a Li 2 MnO3-like unit cell with monoclinic ( C 2/ m ) symmetry, indicating the existence of Li2MnO3-like phase structure. On the basis of the Rietveld structure re fi nement of this material with di ff erent models by the RIETAN-FP program, the whole di ff raction pattern, including the weak peaks around 6.4 -8 ° , can be re fi ned well if the two-phase model consisting of rhombohedral LiMn0.42Ni0.42Co0.16O2 (space group R 3 ̅ m ) and
3	9	8	38	#/texts/36	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						True	p3:body_region:1	bottom_margin	column_2_of_2	2	2	p3:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[387.33, 773.27, 177.16, 7.74]	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280
3	8	9	39	#/texts/35	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						False	None	bottom_margin	column_2_of_2	2	2	p3:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[304.5, 774.02, 15.93, 6.54]	1270	1270	1270	1270
4	2	1	40	#/texts/37	page_header	page_header	False	low	docling_page_header	docling_page_header						True	p4:body_region:0	top_margin	column_1_of_2	1	2	p4:top_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 48.93, 181.19, 8.72]	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters
4	3	2	41	#/texts/38	page_header	page_header	False	low	docling_page_header	docling_page_header						True	p4:body_region:1	top_margin	column_2_of_2	2	2	p4:top_margin:column_2_of_2:colored	[125, 168, 209]	colored	False	True	[519.14, 50.28, 38.3, 6.98]	Perspective	Perspective	Perspective	Perspective
4	4	3	42	#/texts/39	caption	caption	False	low	outside_body_flow_caption	outside_body_flow_caption						False	None	page_body	column_1_of_2	1	2	p4:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 206.55, 503.96, 30.97]	Figure 4. The expected morphology evolution of the TM plane in x Li2MnO3 · (1 -x )LiCoO2, showing the coexistence of Co and LiMn2 domains: (a) x = 0.15; (b) x = 0.45; (c) x = 0.75; and (d) x = 0.90. The rhombohedral ( R…	Figure 4. The expected morphology evolution of the TM plane in x Li2MnO3 · (1 -x )LiCoO2, showing the coexistence of Co and LiMn2 domains: (a) x = 0.15; (b) x = 0.45; (c) x = 0.75; and (d) x = 0.90. The rhombohedral ( R…	Figure 4. The expected morphology evolution of the TM plane in x Li2MnO3 · (1 -x )LiCoO2, showing the coexistence of Co and LiMn2 domains: (a) x = 0.15; (b) x = 0.45; (c) x = 0.75; and (d) x = 0.90. The rhombohedral ( R ) and monoclinic ( M ) unit cells are indicated in the fi gure. Reprinted with permission from ref 29. Copyright 2011 American Chemical Society.	Figure 4. The expected morphology evolution of the TM plane in x Li2MnO3 · (1 -x )LiCoO2, showing the coexistence of Co and LiMn2 domains: (a) x = 0.15; (b) x = 0.45; (c) x = 0.75; and (d) x = 0.90. The rhombohedral ( R ) and monoclinic ( M ) unit cells are indicated in the fi gure. Reprinted with permission from ref 29.
4	1	4	43	#/texts/34#prov2	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p4:body_region:0	page_body	column_1_of_2	1	2	p4:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 250.45, 240.03, 54.81]	monoclinic Li2MnO3 (space group C 2/ m ) structures are chosen. The phase fractions of the rhombohedral and monoclinic components are 43% and 57%, respectively, and very close t o t h e composition of t h e studied 0.5L…	monoclinic Li2MnO3 (space group C 2/ m ) structures are chosen. The phase fractions of the rhombohedral and monoclinic components are 43% and 57%, respectively, and very close t o t h e composition of t h e studied 0.5L…	monoclinic Li2MnO3 (space group C 2/ m ) structures are chosen. The phase fractions of the rhombohedral and monoclinic components are 43% and 57%, respectively, and very close t o t h e composition of t h e studied 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42 Co0.16 O2 material. 13	monoclinic Li2MnO3 (space group C 2/ m ) structures are chosen. The phase fractions of the rhombohedral and monoclinic components are 43% and 57%, respectively, and very close t o t h e composition of t h e studied 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42 Co0.16 O2 material. 13
4	5	5	44	#/texts/40	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p4:body_region:0	page_body	column_1_of_2	1	2	p4:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 306.35, 239.99, 278.86]	By the high-resolution transmission electron microscopy (HRTEM) technique combined with electron energy-loss spectroscopy (EELS) technique, Wen, Abraham, Tabuchi et al. fi nd that the locally monoclinic (Li 2 MnO3-like)…	By the high-resolution transmission electron microscopy (HRTEM) technique combined with electron energy-loss spectroscopy (EELS) technique, Wen, Abraham, Tabuchi et al. fi nd that the locally monoclinic (Li 2 MnO3-like)…	By the high-resolution transmission electron microscopy (HRTEM) technique combined with electron energy-loss spectroscopy (EELS) technique, Wen, Abraham, Tabuchi et al. fi nd that the locally monoclinic (Li 2 MnO3-like) regions are existed in the parent rhombohedral structure of these LLOs, 22,29,31,36 and there are obvious Mn-rich nanodomains. 22,32,43 The recent research on these LLOs by highangle annular dark fi eld scanning transmission electron microscopy (HAADF-STEM) also reveals the coexistence of t wo phases i n s i d e t h e Li 1. 2 Mn0.61Ni0.18 Mg 0.01 O 2 (0.6Li2MnO3 · 0.4LiNi 0.45 Mn0.525 Mg0.025 O2) material; the C 2/ m structure with accentuated contrast slab and the R 3 ̅ m structure with attenuated contrast slab are encountered in the blue and green parts (Figure 2d), respectively, and the proportion of these two structures are about 55% and 45%, respectively, which is in agreement with the component composition of their studied material. 33 In addition, both extended X-ray absorption fi ne structure (EXAFS) and Li magic-angle spinning (MAS) nuclear magnetic resonance (NMR) spectroscopy techniques studies on these LLOs also state that most Mn 4+ in Li2MnO3like atomic environments and M n + in LiMO2-like (M = Co, Ni, Mn, Fe, Cr; 2 ≤ n ≤ 4) atomic environments are contained inside these LLOs, and the locally monoclinic Li2MnO3-like structures are probably quasi-random distributed within the rhombohedral α -NaFeO2 framework. 27,29,38,39	By the high-resolution transmission electron microscopy (HRTEM) technique combined with electron energy-loss spectroscopy (EELS) technique, Wen, Abraham, Tabuchi et al. fi nd that the locally monoclinic (Li 2 MnO3-like) regions are existed in the parent rhombohedral structure of these LLOs, 22,29,31,36 and there are obvious Mn-rich nanodomains. 22,32,43 The recent research on these LLOs by highangle annular dark fi eld scanning transmission electron microscopy (HAADF-STEM) also reveals the coexistence of t wo phases i n s i d e t h e Li 1. 2 Mn0.61Ni0.18 Mg 0.01 O 2 (0.6Li2MnO3 · 0.4LiNi 0.45 Mn0.525 Mg0.025 O2) material; the C 2/ m structure with accentuated contrast slab and the R 3 ̅ m structure with attenuated contrast slab are encountered in the blue and green parts (Figure 2d), respectively, and the proportion of these two structures are about 55% and 45%, respectively, which is in agreement with the component composition of their studied material. 33 In addition, both extended X-ray absorption fi ne structure (EXAFS) and Li magic-angle spinning (MAS) nuclear magnetic resonance (NMR) spectroscopy techniques studies on these LLOs also state that most Mn 4+ in Li2MnO3like atomic environments and M n + in LiMO2-like (M = Co, Ni, Mn, Fe, Cr; 2 ≤ n ≤ 4) atomic environments are contained inside these LLOs, and the locally monoclinic Li2MnO3-like structures are probably quasi-random distributed within the rhombohedral α -NaFeO2 framework. 27,29,38,39
4	6	6	45	#/texts/41#prov0	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p4:body_region:0	bottom_margin	column_1_of_2	1	2	p4:bottom_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 586.36, 240.0, 176.84]	Although there is much two-phase evidence of these LLOs by average and local structure studies, on the other hand, some researchers think that these LLOs are homogeneous solid solutions between the two components Li2MnO…	Although there is much two-phase evidence of these LLOs by average and local structure studies, on the other hand, some researchers think that these LLOs are homogeneous solid solutions between the two components Li2MnO…	Although there is much two-phase evidence of these LLOs by average and local structure studies, on the other hand, some researchers think that these LLOs are homogeneous solid solutions between the two components Li2MnO3 and LiMO2 (M = Co, Ni, Mn, Fe, Cr), because their lattice parameters vary linearly with the composition of its end members (Figure 3 b). 20,35,37,40 This indicates that these samples follow Vegard ' s rule. These weak peaks around 25 -35 ° (XRD data) are also proposed as the result from long-rang Li ordering with a √ 3ahex × √ 3bhex superstructure in the transition-metal layer (Figure 3 a). 35 Note that, although some researchers take the solid solution opinion, the crystal symmetries of these LLOs are also being debated. Some researchers consider these LLOs as being composed of a solid solution with R 3 ̅ m rhombohedral symmetry, 20,35 while others indicate that these LLOs belong to a solid solution with C 2/ m monoclinic symmetry. 37 It is	Although there is much two-phase evidence of these LLOs by average and local structure studies, on the other hand, some researchers think that these LLOs are homogeneous solid solutions between the two components Li2MnO3 and LiMO2 (M = Co, Ni, Mn, Fe, Cr), because their lattice parameters vary linearly with the composition of its end members (Figure 3 b). 20,35,37,40 This indicates that these samples follow Vegard ' s rule. These weak peaks around 25 -35 ° (XRD data) are also proposed as the result from long-rang Li ordering with a √ 3ahex × √ 3bhex superstructure in the transition-metal layer (Figure 3 a). 35 Note that, although some researchers take the solid solution opinion, the crystal symmetries of these LLOs are also being debated. Some researchers consider these LLOs as being composed of a solid solution with R 3 ̅ m rhombohedral symmetry, 20,35 while others indicate that these LLOs belong to a solid solution with C 2/ m monoclinic symmetry. 37 It is
4	7	7	46	#/texts/41#prov1	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p4:body_region:1	page_body	column_2_of_2	2	2	p4:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 250.45, 240.03, 109.6]	worth noting that the X-ray di ff raction techniques (XRD or SXRD) can only provide key information on the average crystal structure. As a matter of fact, the large di ff erence between the atomic number, size, and tend…	worth noting that the X-ray di ff raction techniques (XRD or SXRD) can only provide key information on the average crystal structure. As a matter of fact, the large di ff erence between the atomic number, size, and tend…	worth noting that the X-ray di ff raction techniques (XRD or SXRD) can only provide key information on the average crystal structure. As a matter of fact, the large di ff erence between the atomic number, size, and tendency for like or unlike atom clusters of the elements (Li, Mn, Ni, Co, Fe, Cr) inside these LLOs can induce large lattice distortions, although these LLOs can preserve the periodical long-range structure. There are many examples of multistructural phases existing inside one material although their long-range structures can be considered a solid solution. 29,44,45	worth noting that the X-ray di ff raction techniques (XRD or SXRD) can only provide key information on the average crystal structure. As a matter of fact, the large di ff erence between the atomic number, size, and tendency for like or unlike atom clusters of the elements (Li, Mn, Ni, Co, Fe, Cr) inside these LLOs can induce large lattice distortions, although these LLOs can preserve the periodical long-range structure. There are many examples of multistructural phases existing inside one material although their long-range structures can be considered a solid solution. 29,44,45
4	8	8	47	#/texts/42#prov0	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p4:body_region:1	bottom_margin	column_2_of_2	2	2	p4:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 362.36, 240.03, 400.84]	Thus, the local structure studies on these LLOs are very important to investigate their actual structure. Jarvis et al. carefully investigated the Li[Li 0.2 Ni0.2Mn0.6]O2 material with a di ff raction scanning transmiss…	Thus, the local structure studies on these LLOs are very important to investigate their actual structure. Jarvis et al. carefully investigated the Li[Li 0.2 Ni0.2Mn0.6]O2 material with a di ff raction scanning transmiss…	Thus, the local structure studies on these LLOs are very important to investigate their actual structure. Jarvis et al. carefully investigated the Li[Li 0.2 Ni0.2Mn0.6]O2 material with a di ff raction scanning transmission electron microscopy (DSTEM) technique, and indicated that this material formed a partial ordered solid solution (Figure 3c,d). 37 At the same time, they also concluded that, although two phases have not been observed for their studied material, other compositions, especially those with less excess lithium, may result in twophase regions. 37 For Li2 MnO3 material, there is no doubt that this material has been evidenced as the monoclinic structure with C 2/ m space group. 46 The ratio of Li and Mn content inside this material is 2. In particular, there are about 0.33 Li and 0.67 Mn atoms located at the monoclinic ordering of LiMn2 planes with Li -Mn -Mn periodic arrangement. For Li[Li 0.2 Mn0.567 Ni0.166 Co0.067 ]O2, Li[Li 0.2 Co0.4 Mn0.4]O2, or other LLOs associated with less lithium, the composition of these materials can be described as the common formulation Li[Li x M1 -x ]O2 (M = Mn, Ni, Co, etc.; x < 0.33). 13,29,36 It is obvious that there are not enough lithium sources to support the overall LiM2 periodic ordering. Therefore, two-phase domains with M -M (M = Mn, Ni, Co, Fe, and Cr) and Li -M ′ -M ′ (M ′ = Mn, etc.) periodic ordering in local regions most probably exist inside these LLOs when their compositions are located between the LiMO2 (M = Mn, Ni, Co, Fe, and Cr) and Li2MnO3 components. Experiments by Dahn et al. also con fi rmed that more and more Li atoms occupied the Ni and Mn layer with the increase of y at fi xed x = 1.1 for the Li x Mn y Ni x O2 (0.9 ≤ x ≤ 1.2; 0.1 ≤ y ≤ 0.5) material, the solid solution series Li x Mn y Ni x O2 as a single phase could only be prepared for x near 1 and 0 ≤ y ≤ 0.5, and more impurities (especially Li2MnO3) were shown with more larger y ( y = 0.6). 47 In addition, the raw materials, preparation methods, and calcination temperatures are also the important in fl uence factors for determining the structure of these LLOs with homogeneous solid solution or two phases. Therefore, the	Thus, the local structure studies on these LLOs are very important to investigate their actual structure. Jarvis et al. carefully investigated the Li[Li 0.2 Ni0.2Mn0.6]O2 material with a di ff raction scanning transmission electron microscopy (DSTEM) technique, and indicated that this material formed a partial ordered solid solution (Figure 3c,d). 37 At the same time, they also concluded that, although two phases have not been observed for their studied material, other compositions, especially those with less excess lithium, may result in twophase regions. 37 For Li2 MnO3 material, there is no doubt that this material has been evidenced as the monoclinic structure with C 2/ m space group. 46 The ratio of Li and Mn content inside this material is 2. In particular, there are about 0.33 Li and 0.67 Mn atoms located at the monoclinic ordering of LiMn2 planes with Li -Mn -Mn periodic arrangement. For Li[Li 0.2 Mn0.567 Ni0.166 Co0.067 ]O2, Li[Li 0.2 Co0.4 Mn0.4]O2, or other LLOs associated with less lithium, the composition of these materials can be described as the common formulation Li[Li x M1 -x ]O2 (M = Mn, Ni, Co, etc.; x < 0.33). 13,29,36 It is obvious that there are not enough lithium sources to support the overall LiM2 periodic ordering. Therefore, two-phase domains with M -M (M = Mn, Ni, Co, Fe, and Cr) and Li -M ′ -M ′ (M ′ = Mn, etc.) periodic ordering in local regions most probably exist inside these LLOs when their compositions are located between the LiMO2 (M = Mn, Ni, Co, Fe, and Cr) and Li2MnO3 components. Experiments by Dahn et al. also con fi rmed that more and more Li atoms occupied the Ni and Mn layer with the increase of y at fi xed x = 1.1 for the Li x Mn y Ni x O2 (0.9 ≤ x ≤ 1.2; 0.1 ≤ y ≤ 0.5) material, the solid solution series Li x Mn y Ni x O2 as a single phase could only be prepared for x near 1 and 0 ≤ y ≤ 0.5, and more impurities (especially Li2MnO3) were shown with more larger y ( y = 0.6). 47 In addition, the raw materials, preparation methods, and calcination temperatures are also the important in fl uence factors for determining the structure of these LLOs with homogeneous solid solution or two phases. Therefore, the
4	10	9	48	#/texts/44	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						True	p4:body_region:1	bottom_margin	column_2_of_2	2	2	p4:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[387.33, 773.27, 177.16, 7.74]	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280
4	9	10	49	#/texts/43	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						False	None	bottom_margin	column_2_of_2	2	2	p4:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[304.5, 774.02, 15.93, 6.54]	1271	1271	1271	1271
5	2	1	50	#/texts/45	page_header	page_header	False	low	docling_page_header	docling_page_header						True	p5:body_region:0	top_margin	column_1_of_2	1	2	p5:top_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 48.93, 181.19, 8.72]	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters
5	3	2	51	#/texts/46	page_header	page_header	False	low	docling_page_header	docling_page_header						True	p5:body_region:1	top_margin	column_2_of_2	2	2	p5:top_margin:column_2_of_2:colored	[125, 168, 209]	colored	False	True	[519.14, 50.28, 38.3, 6.98]	Perspective	Perspective	Perspective	Perspective
5	4	3	52	#/texts/47	caption	caption	False	low	outside_body_flow_caption	outside_body_flow_caption						False	None	page_body	column_1_of_2	1	2	p5:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 503.26, 503.99, 31.53]	Figure 5. (a) Reaction pathways diagram through controlling the activation of the Li2MnO3 phase inside the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 material based on the three-dimensional compositional phase diagram. (b)…	Figure 5. (a) Reaction pathways diagram through controlling the activation of the Li2MnO3 phase inside the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 material based on the three-dimensional compositional phase diagram. (b)…	Figure 5. (a) Reaction pathways diagram through controlling the activation of the Li2MnO3 phase inside the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 material based on the three-dimensional compositional phase diagram. (b) The charge and (c) discharge curves with three di ff erent current densities. (a -c) Reprinted with permission from ref 13. Copyright 2012 Royal Society of Chemistry.	Figure 5. (a) Reaction pathways diagram through controlling the activation of the Li2MnO3 phase inside the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 material based on the three-dimensional compositional phase diagram. (b) The charge and (c) discharge curves with three di ff erent current densities. (a -c) Reprinted with permission from ref 13.
5	1	4	53	#/texts/42#prov1	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p5:body_region:0	page_body	column_1_of_2	1	2	p5:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 547.13, 240.0, 54.95]	domains with Li2MnO3-like components most probably exist inside these LLOs, increased with the lithium and manganese content (in proportion to x in the x Li2MnO3 · (1 -x )LiCoO2 equation) increasing, which is described …	domains with Li2MnO3-like components most probably exist inside these LLOs, increased with the lithium and manganese content (in proportion to x in the x Li2MnO3 · (1 -x )LiCoO2 equation) increasing, which is described …	domains with Li2MnO3-like components most probably exist inside these LLOs, increased with the lithium and manganese content (in proportion to x in the x Li2MnO3 · (1 -x )LiCoO2 equation) increasing, which is described by the simulated fi gure in Figure 4. 29	domains with Li2MnO3-like components most probably exist inside these LLOs, increased with the lithium and manganese content (in proportion to x in the x Li2MnO3 · (1 -x )LiCoO2 equation) increasing, which is described by the simulated fi gure in Figure 4. 29
5	5	5	54	#/texts/48	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p5:body_region:0	page_body	column_1_of_2	1	2	p5:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 604.56, 239.98, 66.52]	The reaction mechanisms of these LLOs are very complicated, and have been extensively researched and discussed in the past decade. 6,11,12,25,35,40,42,48 -55 However, these reaction mechanisms proposed are still being d…	The reaction mechanisms of these LLOs are very complicated, and have been extensively researched and discussed in the past decade. 6,11,12,25,35,40,42,48 -55 However, these reaction mechanisms proposed are still being d…	The reaction mechanisms of these LLOs are very complicated, and have been extensively researched and discussed in the past decade. 6,11,12,25,35,40,42,48 -55 However, these reaction mechanisms proposed are still being debated, and most of them cannot explain all of the electrochemical phenomena or are merely supposition.	The reaction mechanisms of these LLOs are very complicated, and have been extensively researched and discussed in the past decade. 6,11,12,25,35,40,42,48 -55 However, these reaction mechanisms proposed are still being debated, and most of them cannot explain all of the electrochemical phenomena or are merely supposition.
5	6	6	55	#/texts/49#prov0	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p5:body_region:0	bottom_margin	column_1_of_2	1	2	p5:bottom_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 673.55, 239.99, 89.65]	In order to understand the complex electrochemical or chemical reaction processes during the fi rst and following cycles of these LLOs, one of the reaction mechanisms associated with an integrated three-dimensional comp…	In order to understand the complex electrochemical or chemical reaction processes during the fi rst and following cycles of these LLOs, one of the reaction mechanisms associated with an integrated three-dimensional comp…	In order to understand the complex electrochemical or chemical reaction processes during the fi rst and following cycles of these LLOs, one of the reaction mechanisms associated with an integrated three-dimensional compositional phase diagram (Figure 5a) is introduced based on Thackeray ' s two-dimensional phase diagram and our previous structure studies of these LLOs. 13 Following this phase diagram, the reaction pathways, phase composition change, and the reaction mechanism of	In order to understand the complex electrochemical or chemical reaction processes during the fi rst and following cycles of these LLOs, one of the reaction mechanisms associated with an integrated three-dimensional compositional phase diagram (Figure 5a) is introduced based on Thackeray ' s two-dimensional phase diagram and our previous structure studies of these LLOs. 13 Following this phase diagram, the reaction pathways, phase composition change, and the reaction mechanism of
5	7	7	56	#/texts/49#prov1	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p5:body_region:1	page_body	column_2_of_2	2	2	p5:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 547.12, 239.94, 20.31]	these LLOs during lithium extraction and insertion processes can be well explained.	these LLOs during lithium extraction and insertion processes can be well explained.	these LLOs during lithium extraction and insertion processes can be well explained.	these LLOs during lithium extraction and insertion processes can be well explained.
5	8	8	57	#/texts/50	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p5:body_region:1	page_body	column_2_of_2	2	2	p5:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 566.65, 240.04, 162.2]	For the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 electrode material, the reaction pathways and phase composition changes during the fi rst charge region below 4.4 V with di ff erent current densities vary along the green…	For the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 electrode material, the reaction pathways and phase composition changes during the fi rst charge region below 4.4 V with di ff erent current densities vary along the green…	For the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 electrode material, the reaction pathways and phase composition changes during the fi rst charge region below 4.4 V with di ff erent current densities vary along the green lines in Figure 5a,b, from point 1 to point 2. During this period, maximum 0.5 Li + ions can be e x t r a c t e d f r o m t h e l i t h i u m l a y e r o f t h e 0.5LiMn0.42 Ni0.42Co0.16O2 component associated predominantly with the oxidation of nickel ions from Ni 2+ to Ni 4+ and followed by the trivalent cobalt oxidation process at higher voltage. The practical charge capacity is 111, 108, and 103 mAh/g, respectively, associated with 5, 20, and 50 mA/g initial current density at room temperature, which is a little smaller than the theoretical capacity (126 mAh/g, assuming all the nickel and cobalt are oxidized to tetravalent).	For the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 electrode material, the reaction pathways and phase composition changes during the fi rst charge region below 4.4 V with di ff erent current densities vary along the green lines in Figure 5a,b, from point 1 to point 2. During this period, maximum 0.5 Li + ions can be e x t r a c t e d f r o m t h e l i t h i u m l a y e r o f t h e 0.5LiMn0.42 Ni0.42Co0.16O2 component associated predominantly with the oxidation of nickel ions from Ni 2+ to Ni 4+ and followed by the trivalent cobalt oxidation process at higher voltage. The practical charge capacity is 111, 108, and 103 mAh/g, respectively, associated with 5, 20, and 50 mA/g initial current density at room temperature, which is a little smaller than the theoretical capacity (126 mAh/g, assuming all the nickel and cobalt are oxidized to tetravalent).
5	9	9	58	#/texts/51#prov0	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p5:body_region:1	bottom_margin	column_2_of_2	2	2	p5:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 731.26, 240.03, 31.93]	When the electrochemical potential of the Li/ 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 cell increases from 4.4 to 4.8 V during the fi rst charge process, presented with the blue	When the electrochemical potential of the Li/ 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 cell increases from 4.4 to 4.8 V during the fi rst charge process, presented with the blue	When the electrochemical potential of the Li/ 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 cell increases from 4.4 to 4.8 V during the fi rst charge process, presented with the blue	When the electrochemical potential of the Li/ 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 cell increases from 4.4 to 4.8 V during the fi rst charge process, presented with the blue
5	11	10	59	#/texts/53	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						True	p5:body_region:1	bottom_margin	column_2_of_2	2	2	p5:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[387.33, 773.27, 177.16, 7.74]	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280
5	10	11	60	#/texts/52	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						False	None	bottom_margin	column_2_of_2	2	2	p5:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[304.5, 774.02, 15.93, 6.54]	1272	1272	1272	1272
6	3	1	61	#/texts/54	page_header	page_header	False	low	docling_page_header	docling_page_header						True	p6:body_region:0	top_margin	column_1_of_2	1	2	p6:top_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 48.93, 181.19, 8.72]	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters
6	1	2	62	#/texts/51#prov1	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p6:body_region:0	page_body	column_1_of_2	1	2	p6:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 69.37, 239.98, 106.2]	long voltage plateaus in Figure 5 b, more lithium ions can be extracted from the Li2MnO3 component together with the loss of oxygen and structure rearrangement, and there is probably a new phase (MnO2) formed. The oxyge…	long voltage plateaus in Figure 5 b, more lithium ions can be extracted from the Li2MnO3 component together with the loss of oxygen and structure rearrangement, and there is probably a new phase (MnO2) formed. The oxyge…	long voltage plateaus in Figure 5 b, more lithium ions can be extracted from the Li2MnO3 component together with the loss of oxygen and structure rearrangement, and there is probably a new phase (MnO2) formed. The oxygen accompanied with lithium ions extraction and structure rearrangement phenomena during this process have been con fi rmed by Armstrong using in situ di ff erential electrochemical mass spectrometry (DEMS) (Figure 6a), Yabuuchi using SXRD, and Lu using Rietveld analysis. 50,52,56 It is clear that the evolution of oxygen	long voltage plateaus in Figure 5 b, more lithium ions can be extracted from the Li2MnO3 component together with the loss of oxygen and structure rearrangement, and there is probably a new phase (MnO2) formed. The oxygen accompanied with lithium ions extraction and structure rearrangement phenomena during this process have been con fi rmed by Armstrong using in situ di ff erential electrochemical mass spectrometry (DEMS) (Figure 6a), Yabuuchi using SXRD, and Lu using Rietveld analysis. 50,52,56 It is clear that the evolution of oxygen
6	5	3	63	#/texts/56	caption	caption	False	low	outside_body_flow_caption	outside_body_flow_caption						True	p6:body_region:0	bottom_margin	column_1_of_2	1	2	p6:bottom_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 655.02, 239.98, 107.93]	Figure 6. (a) Mass spectrometry analysis of O2 evolved on the 1st charging process of the Li/Li[Ni 0.2 Li 0.2Mn0.6]O2 cell. Reprinted with permission from ref 52. Copyright 2006 American Chemical Society. (b) First-prin…	Figure 6. (a) Mass spectrometry analysis of O2 evolved on the 1st charging process of the Li/Li[Ni 0.2 Li 0.2Mn0.6]O2 cell. Reprinted with permission from ref 52.	Figure 6. (a) Mass spectrometry analysis of O2 evolved on the 1st charging process of the Li/Li[Ni 0.2 Li 0.2Mn0.6]O2 cell. Reprinted with permission from ref 52. Copyright 2006 American Chemical Society. (b) First-principle calculation sketch of partial oxygen layer in Li x /14Ni1/4Mn7/12O2 (pink balls: oxygen ions; colored polyhedrons: adjacent TM slab) and its calculated spin density at (c) x = 14, (d) x = 8, and (e) x = 0. Reprinted with permission from ref 34. Copyright 2011 Royal Society of Chemistry. (f) Schemes of the proposed surface reaction mechanisms in the Li 1.2 Ni0.13Co0.13Mn0.54O2 material. Reprinted with permission from ref 50. Copyright 2011 American Chemical Society.	Figure 6. (a) Mass spectrometry analysis of O2 evolved on the 1st charging process of the Li/Li[Ni 0.2 Li 0.2Mn0.6]O2 cell. Reprinted with permission from ref 52.
6	4	4	64	#/texts/55	page_header	page_header	False	low	docling_page_header	docling_page_header						True	p6:body_region:1	top_margin	column_2_of_2	2	2	p6:top_margin:column_2_of_2:colored	[125, 168, 209]	colored	False	True	[519.14, 50.28, 38.3, 6.98]	Perspective	Perspective	Perspective	Perspective
6	2	5	65	#/texts/51#prov2	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p6:body_region:1	page_body	column_2_of_2	2	2	p6:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 69.37, 240.04, 371.81]	gas quantity in Figure 6a is associated with the voltage increasing, and the large amount of oxygen gas is emitted above 4.5 V, corresponding to the charge plateau of these LLOs. Through fi rst-principles calculations, …	gas quantity in Figure 6a is associated with the voltage increasing, and the large amount of oxygen gas is emitted above 4.5 V, corresponding to the charge plateau of these LLOs. Through fi rst-principles calculations, …	gas quantity in Figure 6a is associated with the voltage increasing, and the large amount of oxygen gas is emitted above 4.5 V, corresponding to the charge plateau of these LLOs. Through fi rst-principles calculations, the oxygen 2p electron clouds change signi fi cantly with the lithium extraction during the fi rst charge process, indicating that extra electrons that cannot be provided by the transitional metal redox couples are coming from oxygen ions (Figure 6b -e). 34 However, it is very di ffi cult to unambiguously determine whether the new phase is MnO2, although new phases created during the fi rst charge process have been reported by Simonin and Gray in Li[Li 0.2 Mn0.61 Ni0.18Mg0.01]O2 and Li[Li 1/9Ni1/3Mn5/9]O2 materials, respectively. 57,58 In our opinion, based on electrochemical performances, d Q /d V curves and kinetic analysis of these LLOs during cycling, the new phase (MnO2 ) is most likely to appear during the fi rst charge process above 4.4 V, and transfer to the cubic spinel-like framework (MnMO4, M = Ni, Co, and Mn) during the following cycles. 13,15 The theoretical capacity of this process (from 4.4 V to 4.8 V) is calculated to be 251 mAh/g if we suppose all of the lithium (0.5 Li 2 O) can be extracted from the 0.5Li 2 MnO3 component. The practical charged capacities of this process are 205, 162, and 139 mAh/g, respectively, corresponding to di ff erent current densities (5, 20, and 50 mA/ g) at room temperature. All of the practical charged capacities are close but smaller than those of theoretical capacity. Thus, the reaction pathways and compositional changes of this process at room temperature can be described with the blue lines in Figure 5a, from point 2 to points 3, 3 ′ , and 3 ″ , respectively. During these charge regions, when all of Li2O are extracted from the Li2MnO3 component, the oxidized electrode material will be Mn 0.712 Ni0.208 Co0.08O2 with α = 0.208 and β = 0.08 in MO2 (M = Mn1 -α -β Ni α Co β ; 0 ≤ α ≤ 5/12, 0 ≤ β ≤ 1/6), and the electrode composition changes along the blue dashed line until it reaches the apex C of the tie-triangle in Figure 5a.	gas quantity in Figure 6a is associated with the voltage increasing, and the large amount of oxygen gas is emitted above 4.5 V, corresponding to the charge plateau of these LLOs. Through fi rst-principles calculations, the oxygen 2p electron clouds change signi fi cantly with the lithium extraction during the fi rst charge process, indicating that extra electrons that cannot be provided by the transitional metal redox couples are coming from oxygen ions (Figure 6b -e). 34 However, it is very di ffi cult to unambiguously determine whether the new phase is MnO2, although new phases created during the fi rst charge process have been reported by Simonin and Gray in Li[Li 0.2 Mn0.61 Ni0.18Mg0.01]O2 and Li[Li 1/9Ni1/3Mn5/9]O2 materials, respectively. 57,58 In our opinion, based on electrochemical performances, d Q /d V curves and kinetic analysis of these LLOs during cycling, the new phase (MnO2 ) is most likely to appear during the fi rst charge process above 4.4 V, and transfer to the cubic spinel-like framework (MnMO4, M = Ni, Co, and Mn) during the following cycles. 13,15 The theoretical capacity of this process (from 4.4 V to 4.8 V) is calculated to be 251 mAh/g if we suppose all of the lithium (0.5 Li 2 O) can be extracted from the 0.5Li 2 MnO3 component. The practical charged capacities of this process are 205, 162, and 139 mAh/g, respectively, corresponding to di ff erent current densities (5, 20, and 50 mA/ g) at room temperature. All of the practical charged capacities are close but smaller than those of theoretical capacity. Thus, the reaction pathways and compositional changes of this process at room temperature can be described with the blue lines in Figure 5a, from point 2 to points 3, 3 ′ , and 3 ″ , respectively. During these charge regions, when all of Li2O are extracted from the Li2MnO3 component, the oxidized electrode material will be Mn 0.712 Ni0.208 Co0.08O2 with α = 0.208 and β = 0.08 in MO2 (M = Mn1 -α -β Ni α Co β ; 0 ≤ α ≤ 5/12, 0 ≤ β ≤ 1/6), and the electrode composition changes along the blue dashed line until it reaches the apex C of the tie-triangle in Figure 5a.
6	6	6	66	#/texts/57	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p6:body_region:1	page_body	column_2_of_2	2	2	p6:page_body:column_2_of_2:colored	[255, 242, 208]	colored	False	False	[352.46, 454.93, 183.98, 81.36]	The reaction mechanisms associated with the mysterious anomalous capacity of these LLOs at high temperature may be di ff erent compared with those at room temperature, and are still unclear.	The reaction mechanisms associated with the mysterious anomalous capacity of these LLOs at high temperature may be di ff erent compared with those at room temperature, and are still unclear.	The reaction mechanisms associated with the mysterious anomalous capacity of these LLOs at high temperature may be di ff erent compared with those at room temperature, and are still unclear.	The reaction mechanisms associated with the mysterious anomalous capacity of these LLOs at high temperature may be di ff erent compared with those at room temperature, and are still unclear.
6	7	7	67	#/texts/58#prov0	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p6:body_region:1	bottom_margin	column_2_of_2	2	2	p6:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 555.81, 240.03, 207.39]	During the fi rst discharge process, lithium ions will insert into the Mn0.42Ni0.42Co0.16O2 and newly formed MnO2 components, respectively, while the unactivated Li2MnO3 component still exist in these ' composite ' laye…	During the fi rst discharge process, lithium ions will insert into the Mn0.42Ni0.42Co0.16O2 and newly formed MnO2 components, respectively, while the unactivated Li2MnO3 component still exist in these ' composite ' laye…	During the fi rst discharge process, lithium ions will insert into the Mn0.42Ni0.42Co0.16O2 and newly formed MnO2 components, respectively, while the unactivated Li2MnO3 component still exist in these ' composite ' layered materials. Our previous and Yabuuchi ' s research results show that the activated manganese redox reaction (Mn 3+ /Mn 4+ ) occurs after the fi rst cycle of these LLOs. 13,50 Therefore, the electrochemical reaction pathways and composition change of the fi rst discharge process is not suitable to be located in the Li2MnO3 -LiMO2 (M = Mn, Ni, and Co) tie-line in Figure 4 of ref 11, and should be located in the face compositing Li2MnO3, LiMnO2, and LiMO2 (M = Mn, Ni, and Co) components. The reaction pathways and compositional changes during the fi rst discharge processes of these LLOs with di ff erent current densities can follow the red lines in Figure 5a. During this process, the theoretical discharge capacity is calculated to be 269 mAh/g b a s e d o n t h e w e i g h t o f t h e 0.5LiMnO2 · 0.5LiMn0.42 Ni0.42 Co0.16O2, while the practical discharge capacity, corresponding to 5, 20, and 50 mA/g initial	During the fi rst discharge process, lithium ions will insert into the Mn0.42Ni0.42Co0.16O2 and newly formed MnO2 components, respectively, while the unactivated Li2MnO3 component still exist in these ' composite ' layered materials. Our previous and Yabuuchi ' s research results show that the activated manganese redox reaction (Mn 3+ /Mn 4+ ) occurs after the fi rst cycle of these LLOs. 13,50 Therefore, the electrochemical reaction pathways and composition change of the fi rst discharge process is not suitable to be located in the Li2MnO3 -LiMO2 (M = Mn, Ni, and Co) tie-line in Figure 4 of ref 11, and should be located in the face compositing Li2MnO3, LiMnO2, and LiMO2 (M = Mn, Ni, and Co) components. The reaction pathways and compositional changes during the fi rst discharge processes of these LLOs with di ff erent current densities can follow the red lines in Figure 5a. During this process, the theoretical discharge capacity is calculated to be 269 mAh/g b a s e d o n t h e w e i g h t o f t h e 0.5LiMnO2 · 0.5LiMn0.42 Ni0.42 Co0.16O2, while the practical discharge capacity, corresponding to 5, 20, and 50 mA/g initial
6	9	8	68	#/texts/60	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						True	p6:body_region:1	bottom_margin	column_2_of_2	2	2	p6:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[387.33, 773.27, 177.16, 7.74]	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280
6	8	9	69	#/texts/59	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						False	None	bottom_margin	column_2_of_2	2	2	p6:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[304.5, 774.02, 15.93, 6.54]	1273	1273	1273	1273
7	3	1	70	#/texts/61	page_header	page_header	False	low	docling_page_header	docling_page_header						True	p7:body_region:0	top_margin	column_1_of_2	1	2	p7:top_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 48.93, 181.19, 8.72]	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters
7	4	2	71	#/texts/62	page_header	page_header	False	low	docling_page_header	docling_page_header						True	p7:body_region:1	top_margin	column_2_of_2	2	2	p7:top_margin:column_2_of_2:colored	[125, 168, 209]	colored	False	True	[519.14, 50.28, 38.3, 6.98]	Perspective	Perspective	Perspective	Perspective
7	5	3	72	#/texts/63	caption	caption	False	low	outside_body_flow_caption	outside_body_flow_caption						False	None	page_body	column_1_of_2	1	2	p7:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 255.34, 503.93, 20.9]	Figure 7. Charge and discharge curves of the Li/Li[Li 1/5Ni1/5Mn3/5]O2 cell at (a) 55 ° C and (b) 85 ° C. Reprinted with permission from ref 40. Copyright 2011 Royal Society of Chemistry.	Figure 7. Charge and discharge curves of the Li/Li[Li 1/5Ni1/5Mn3/5]O2 cell at (a) 55 ° C and (b) 85 ° C. Reprinted with permission from ref 40.	Figure 7. Charge and discharge curves of the Li/Li[Li 1/5Ni1/5Mn3/5]O2 cell at (a) 55 ° C and (b) 85 ° C. Reprinted with permission from ref 40. Copyright 2011 Royal Society of Chemistry.	Figure 7. Charge and discharge curves of the Li/Li[Li 1/5Ni1/5Mn3/5]O2 cell at (a) 55 ° C and (b) 85 ° C. Reprinted with permission from ref 40.
7	1	4	73	#/texts/58#prov1	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p7:body_region:0	page_body	column_1_of_2	1	2	p7:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 289.17, 239.99, 76.04]	charge/discharge currents, is 272, 224, and 184 mAh/g, respectively (Figure 5c). It is obvious that all of the discharge capacity except for the value with small current density ( ≤ 5 mA/g) can be explained by the propo…	charge/discharge currents, is 272, 224, and 184 mAh/g, respectively (Figure 5c). It is obvious that all of the discharge capacity except for the value with small current density ( ≤ 5 mA/g) can be explained by the propo…	charge/discharge currents, is 272, 224, and 184 mAh/g, respectively (Figure 5c). It is obvious that all of the discharge capacity except for the value with small current density ( ≤ 5 mA/g) can be explained by the proposed reaction mechanism. On the basis of surface reaction investigation of these LLOs, it is suggested that some of the extra discharge capacity for these LLOs originated from the electrochemical reduction reaction of	charge/discharge currents, is 272, 224, and 184 mAh/g, respectively (Figure 5c). It is obvious that all of the discharge capacity except for the value with small current density ( ≤ 5 mA/g) can be explained by the proposed reaction mechanism. On the basis of surface reaction investigation of these LLOs, it is suggested that some of the extra discharge capacity for these LLOs originated from the electrochemical reduction reaction of
7	2	5	74	#/texts/58#prov2	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p7:body_region:0	page_body	column_1_of_2	1	2	p7:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 367.54, 239.96, 48.47]	the oxygen molecules at the electrode surface ( ⎯ ⎯⎯⎯⎯⎯⎯⎯→ -O O 2 reduction 2 ), but these contribution are suppressed by the accumulated lithium carbonate formation at the electrode surface (Figure 6f). 50	the oxygen molecules at the electrode surface ( ⎯ ⎯⎯⎯⎯⎯⎯⎯→ -O O 2 reduction 2 ), but these contribution are suppressed by the accumulated lithium carbonate formation at the electrode surface (Figure 6f). 50	the oxygen molecules at the electrode surface ( ⎯ ⎯⎯⎯⎯⎯⎯⎯→ -O O 2 reduction 2 ), but these contribution are suppressed by the accumulated lithium carbonate formation at the electrode surface (Figure 6f). 50	the oxygen molecules at the electrode surface ( ⎯ ⎯⎯⎯⎯⎯⎯⎯→ -O O 2 reduction 2 ), but these contribution are suppressed by the accumulated lithium carbonate formation at the electrode surface (Figure 6f). 50
7	6	6	75	#/texts/64	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p7:body_region:0	page_body	column_1_of_2	1	2	p7:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 418.32, 240.01, 176.95]	Nevertheless, with the temperature increased to 55 and 85 ° C, the rechargeable charge/discharge capacity of the Li/ Li[Li1/5Ni1/5Mn3/5]O2 can reach 300 mAh/g (Figure 7a), and even 350 mAh/g (Figure 7b), which are much …	Nevertheless, with the temperature increased to 55 and 85 ° C, the rechargeable charge/discharge capacity of the Li/ Li[Li1/5Ni1/5Mn3/5]O2 can reach 300 mAh/g (Figure 7a), and even 350 mAh/g (Figure 7b), which are much …	Nevertheless, with the temperature increased to 55 and 85 ° C, the rechargeable charge/discharge capacity of the Li/ Li[Li1/5Ni1/5Mn3/5]O2 can reach 300 mAh/g (Figure 7a), and even 350 mAh/g (Figure 7b), which are much larger than the theoretical capacity if we just consider the nickel (Ni 2+ /Ni 4+ ) and manganese (Mn 3+ /Mn 4+ ) valence variation. 40 Ozhuku et al. speculated that the highest rechargeable theoretical capacity at high temperature was contributed by the possible ' cation ' redox reaction (Mn 4+ /Mn 5+ , Mn 5+ /Mn 6+ ) or ' anion ' redox (O 2 -/O2 2 -) in a solid matrix in terms of lithium insertion scheme. 40 The reaction mechanism of these LLOs at high temperature may be di ff erent and more complex compared with those at room temperature, and more experimental evidence or theoretical calculations for supporting these hypotheses need to be conducted in the future to explain the high mysterious rechargeable capacity of these LLOs.	Nevertheless, with the temperature increased to 55 and 85 ° C, the rechargeable charge/discharge capacity of the Li/ Li[Li1/5Ni1/5Mn3/5]O2 can reach 300 mAh/g (Figure 7a), and even 350 mAh/g (Figure 7b), which are much larger than the theoretical capacity if we just consider the nickel (Ni 2+ /Ni 4+ ) and manganese (Mn 3+ /Mn 4+ ) valence variation. 40 Ozhuku et al. speculated that the highest rechargeable theoretical capacity at high temperature was contributed by the possible ' cation ' redox reaction (Mn 4+ /Mn 5+ , Mn 5+ /Mn 6+ ) or ' anion ' redox (O 2 -/O2 2 -) in a solid matrix in terms of lithium insertion scheme. 40 The reaction mechanism of these LLOs at high temperature may be di ff erent and more complex compared with those at room temperature, and more experimental evidence or theoretical calculations for supporting these hypotheses need to be conducted in the future to explain the high mysterious rechargeable capacity of these LLOs.
7	7	7	76	#/texts/65	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p7:body_region:0	page_body	column_1_of_2	1	2	p7:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 597.58, 240.0, 120.89]	Although there are many debates on these LLOs currently, their large electrochemical capacities are still very attractive for utilization as cathode materials in lithium ion batteries. In the past, di ff erent compositi…	Although there are many debates on these LLOs currently, their large electrochemical capacities are still very attractive for utilization as cathode materials in lithium ion batteries. In the past, di ff erent compositi…	Although there are many debates on these LLOs currently, their large electrochemical capacities are still very attractive for utilization as cathode materials in lithium ion batteries. In the past, di ff erent composition, preparation methods, fi rst or second crystalline grain morphology, surface treatments and doping elements of these LLOs have been extensively studied. 40,42,59 -67 However, many problems of these LLOs still exist at present. For example, the initial coulombic e ffi ciency is low, 14,68 and the cycle stability 13,69 and rate performance 15,62 of these materials still need to be amended to satisfy the application requirements.	Although there are many debates on these LLOs currently, their large electrochemical capacities are still very attractive for utilization as cathode materials in lithium ion batteries. In the past, di ff erent composition, preparation methods, fi rst or second crystalline grain morphology, surface treatments and doping elements of these LLOs have been extensively studied. 40,42,59 -67 However, many problems of these LLOs still exist at present. For example, the initial coulombic e ffi ciency is low, 14,68 and the cycle stability 13,69 and rate performance 15,62 of these materials still need to be amended to satisfy the application requirements.
7	8	8	77	#/texts/66#prov0	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p7:body_region:0	bottom_margin	column_1_of_2	1	2	p7:bottom_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 720.72, 239.99, 42.48]	Low initial Coulombic e ffi ciency associated with large irreversible capacity can result in mass ionized lithium, and the formation of a solid electrolyte interface (SEI) layer, thus reducing the energy density of the …	Low initial Coulombic e ffi ciency associated with large irreversible capacity can result in mass ionized lithium, and the formation of a solid electrolyte interface (SEI) layer, thus reducing the energy density of the …	Low initial Coulombic e ffi ciency associated with large irreversible capacity can result in mass ionized lithium, and the formation of a solid electrolyte interface (SEI) layer, thus reducing the energy density of the lithium-ion battery and	Low initial Coulombic e ffi ciency associated with large irreversible capacity can result in mass ionized lithium, and the formation of a solid electrolyte interface (SEI) layer, thus reducing the energy density of the lithium-ion battery and
7	9	9	78	#/texts/66#prov1	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p7:body_region:1	page_body	column_2_of_2	2	2	p7:page_body:column_2_of_2:colored	[255, 242, 208]	colored	False	False	[353.82, 295.45, 181.27, 95.31]	Currently, the low initial coulombic e ffi ciency, unsatis fi ed rate performance, and cycle stability of these LLOs are still the main problems preventing their utilization in practical lithium ion batteries.	Currently, the low initial coulombic e ffi ciency, unsatis fi ed rate performance, and cycle stability of these LLOs are still the main problems preventing their utilization in practical lithium ion batteries.	Currently, the low initial coulombic e ffi ciency, unsatis fi ed rate performance, and cycle stability of these LLOs are still the main problems preventing their utilization in practical lithium ion batteries.	Currently, the low initial coulombic e ffi ciency, unsatis fi ed rate performance, and cycle stability of these LLOs are still the main problems preventing their utilization in practical lithium ion batteries.
7	10	10	79	#/texts/67	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p7:body_region:1	page_body	column_2_of_2	2	2	p7:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 412.83, 240.04, 207.34]	presenting a serious trade-o ff in lithium-ion battery design. At present, most of the initial Coulombic e ffi ciencies of these LLOs in the published literature are smaller than 80% at room temperature, and the main re…	presenting a serious trade-o ff in lithium-ion battery design. At present, most of the initial Coulombic e ffi ciencies of these LLOs in the published literature are smaller than 80% at room temperature, and the main re…	presenting a serious trade-o ff in lithium-ion battery design. At present, most of the initial Coulombic e ffi ciencies of these LLOs in the published literature are smaller than 80% at room temperature, and the main reason is due to the irreversible reaction resulting from the fi rst charge plateau above 4.4 V. In order to improve the initial Coulombic e ffi ciency, the preconditioned methods with NH3 and HNO3, 53 surface modi fi cation with nanostructured Al2O3, AlPO4, or RuO2, 70 and ruthenium substitution 14 for manganese on these LLOs have been conducted. The experiment results of ruthenium substitution for manganese (Figure 8) show that all of the initial columbic e ffi ciency increased with the ruthenium content increasing, and the highest initial columbic e ffi ciency is 86% with 284 mAh/g discharge capacity at room temperature when the content of substituted ruthenium is 5 mol %. 14 The initial Coulombic e ffi ciency improvements are most probably contributed by the content decrease of the Li2MnO3 component or Li2MnO3 component, which can be activated inside these materials.	presenting a serious trade-o ff in lithium-ion battery design. At present, most of the initial Coulombic e ffi ciencies of these LLOs in the published literature are smaller than 80% at room temperature, and the main reason is due to the irreversible reaction resulting from the fi rst charge plateau above 4.4 V. In order to improve the initial Coulombic e ffi ciency, the preconditioned methods with NH3 and HNO3, 53 surface modi fi cation with nanostructured Al2O3, AlPO4, or RuO2, 70 and ruthenium substitution 14 for manganese on these LLOs have been conducted. The experiment results of ruthenium substitution for manganese (Figure 8) show that all of the initial columbic e ffi ciency increased with the ruthenium content increasing, and the highest initial columbic e ffi ciency is 86% with 284 mAh/g discharge capacity at room temperature when the content of substituted ruthenium is 5 mol %. 14 The initial Coulombic e ffi ciency improvements are most probably contributed by the content decrease of the Li2MnO3 component or Li2MnO3 component, which can be activated inside these materials.
7	11	11	80	#/texts/68	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p7:body_region:1	bottom_margin	column_2_of_2	2	2	p7:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 622.36, 240.04, 140.84]	Although most of the published literature shows that the cycle performance based on the charge and discharge capacity of these LLOs is good, their voltage degradation after long cycling is extremely serious, which can l…	Although most of the published literature shows that the cycle performance based on the charge and discharge capacity of these LLOs is good, their voltage degradation after long cycling is extremely serious, which can l…	Although most of the published literature shows that the cycle performance based on the charge and discharge capacity of these LLOs is good, their voltage degradation after long cycling is extremely serious, which can largely lower the energy output and e ffi ciency of the lithium-ion batteries. 69,71 In order to investigate the cycle stability of these materials in detail, long time cycling of the Li/0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 cell has been conducted. 13 It is obvious that two cycling stages (Stage I in Figure 9a and Stage II in Figure 9c) exist during long time cycling. During Stage I (from about the second cycle to the 25th cycle), the charge and discharge capacities (especially below 3.5 V) increase with cycling, while those decrease during Stage II (from about the 26th cycle to the	Although most of the published literature shows that the cycle performance based on the charge and discharge capacity of these LLOs is good, their voltage degradation after long cycling is extremely serious, which can largely lower the energy output and e ffi ciency of the lithium-ion batteries. 69,71 In order to investigate the cycle stability of these materials in detail, long time cycling of the Li/0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 cell has been conducted. 13 It is obvious that two cycling stages (Stage I in Figure 9a and Stage II in Figure 9c) exist during long time cycling. During Stage I (from about the second cycle to the 25th cycle), the charge and discharge capacities (especially below 3.5 V) increase with cycling, while those decrease during Stage II (from about the 26th cycle to the
7	13	12	81	#/texts/70	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						True	p7:body_region:1	bottom_margin	column_2_of_2	2	2	p7:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[387.33, 773.27, 177.16, 7.74]	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280
7	12	13	82	#/texts/69	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						False	None	bottom_margin	column_2_of_2	2	2	p7:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[304.5, 774.02, 15.93, 6.54]	1274	1274	1274	1274
8	1	1	83	#/texts/71	page_header	page_header	False	low	docling_page_header	docling_page_header						True	p8:body_region:0	top_margin	column_1_of_2	1	2	p8:top_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 48.93, 181.19, 8.72]	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters
8	3	2	84	#/texts/73	caption	caption	False	low	outside_body_flow_caption	outside_body_flow_caption						True	p8:body_region:0	page_body	column_1_of_2	1	2	p8:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 269.11, 239.95, 37.92]	Figure 8. The initial Coulombic e ffi ciency and the charge/discharge capacity of the Li 1.2 Mn0.567 -x Ru x Ni0.166 Co0.067O2 ( x = 0.00, 0.03, 0.05, and 0.07) materials. Adapted from ref 14. Copyright 2012 Royal Socie…	Figure 8. The initial Coulombic e ffi ciency and the charge/discharge capacity of the Li 1.2 Mn0.567 -x Ru x Ni0.166 Co0.067O2 ( x = 0.00, 0.03, 0.05, and 0.07) materials. Adapted from ref 14.	Figure 8. The initial Coulombic e ffi ciency and the charge/discharge capacity of the Li 1.2 Mn0.567 -x Ru x Ni0.166 Co0.067O2 ( x = 0.00, 0.03, 0.05, and 0.07) materials. Adapted from ref 14. Copyright 2012 Royal Society of Chemistry.	Figure 8. The initial Coulombic e ffi ciency and the charge/discharge capacity of the Li 1.2 Mn0.567 -x Ru x Ni0.166 Co0.067O2 ( x = 0.00, 0.03, 0.05, and 0.07) materials. Adapted from ref 14.
8	4	3	85	#/texts/74#prov0	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p8:body_region:0	page_body	column_1_of_2	1	2	p8:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 324.66, 239.99, 107.85]	151st cycle). The increased capacity in Stage I is obvious and corresponds to the new redox peaks (Ox3 /Re3 ) increasing after the fi rst cycle (Figure 9b). This indicates that the content of activated manganese increas…	151st cycle). The increased capacity in Stage I is obvious and corresponds to the new redox peaks (Ox3 /Re3 ) increasing after the fi rst cycle (Figure 9b). This indicates that the content of activated manganese increas…	151st cycle). The increased capacity in Stage I is obvious and corresponds to the new redox peaks (Ox3 /Re3 ) increasing after the fi rst cycle (Figure 9b). This indicates that the content of activated manganese increases step by step during Stage I. Consequently, the charge/discharge capacity increases, and the charge voltage decreases gradually, attributed to the lower redox reaction voltage of Mn 3+ /Mn 4+ with respect to that of nickel and cobalt. During Stage II, both the charge/discharge capacity and discharge plateaus decrease with cycling. The decreased discharge plateaus are mostly contributed to the	151st cycle). The increased capacity in Stage I is obvious and corresponds to the new redox peaks (Ox3 /Re3 ) increasing after the fi rst cycle (Figure 9b). This indicates that the content of activated manganese increases step by step during Stage I. Consequently, the charge/discharge capacity increases, and the charge voltage decreases gradually, attributed to the lower redox reaction voltage of Mn 3+ /Mn 4+ with respect to that of nickel and cobalt. During Stage II, both the charge/discharge capacity and discharge plateaus decrease with cycling. The decreased discharge plateaus are mostly contributed to the
8	2	4	86	#/texts/72	page_header	page_header	False	low	docling_page_header	docling_page_header						True	p8:body_region:1	top_margin	column_2_of_2	2	2	p8:top_margin:column_2_of_2:colored	[125, 168, 209]	colored	False	True	[519.14, 50.28, 38.3, 6.98]	Perspective	Perspective	Perspective	Perspective
8	5	5	87	#/texts/74#prov1	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p8:body_region:1	page_body	column_2_of_2	2	2	p8:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 69.37, 240.01, 30.97]	reduction peaks shifting to the lower voltage region (Figure 9d), indicating that the structures of these LLOs are not stable during long cycling.	reduction peaks shifting to the lower voltage region (Figure 9d), indicating that the structures of these LLOs are not stable during long cycling.	reduction peaks shifting to the lower voltage region (Figure 9d), indicating that the structures of these LLOs are not stable during long cycling.	reduction peaks shifting to the lower voltage region (Figure 9d), indicating that the structures of these LLOs are not stable during long cycling.
8	6	6	88	#/texts/75	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p8:body_region:1	page_body	column_2_of_2	2	2	p8:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 102.54, 240.03, 186.03]	Observing Figure 9b,d, we found that there are obvious swellings on the oxidation curves of d Q /d V between 3.0 and 3.2 V during Stage I, and this swelling become more and more obvious during Stage II. These phenomena …	Observing Figure 9b,d, we found that there are obvious swellings on the oxidation curves of d Q /d V between 3.0 and 3.2 V during Stage I, and this swelling become more and more obvious during Stage II. These phenomena …	Observing Figure 9b,d, we found that there are obvious swellings on the oxidation curves of d Q /d V between 3.0 and 3.2 V during Stage I, and this swelling become more and more obvious during Stage II. These phenomena indicate that the cubic spinel-like phase transformation of layered phase in local regions may arise during stage I and gradually completed during Stage II. In order to con fi rm these phase transformation, the Raman spectroscopies of these materials with di ff erent initial charge/discharge states were investigated. From observing Figure 9e -i, it is clear that the shoulders characterizing cubic spinel-like phase spectroscopy between 630 and 670 cm -1 appear and become more and more obvious with the cycle number and initial charge/discharge current density increasing. In addition, X-ray absorption spectroscopy (XAS), 55 HRTEM techniques, 33,72 and d Q /d V curves 42 studies on these LLOs also show that the cubic spinel-like phases appear after long cycling.	Observing Figure 9b,d, we found that there are obvious swellings on the oxidation curves of d Q /d V between 3.0 and 3.2 V during Stage I, and this swelling become more and more obvious during Stage II. These phenomena indicate that the cubic spinel-like phase transformation of layered phase in local regions may arise during stage I and gradually completed during Stage II. In order to con fi rm these phase transformation, the Raman spectroscopies of these materials with di ff erent initial charge/discharge states were investigated. From observing Figure 9e -i, it is clear that the shoulders characterizing cubic spinel-like phase spectroscopy between 630 and 670 cm -1 appear and become more and more obvious with the cycle number and initial charge/discharge current density increasing. In addition, X-ray absorption spectroscopy (XAS), 55 HRTEM techniques, 33,72 and d Q /d V curves 42 studies on these LLOs also show that the cubic spinel-like phases appear after long cycling.
8	7	7	89	#/texts/76#prov0	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p8:body_region:1	page_body	column_2_of_2	2	2	p8:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 290.76, 240.02, 141.69]	Surface coating with Al2O3, CeO2, ZrO2, SiO2, ZnO, AlPO4, and Li -Ni -PO4 and mildly acidic treatment on these LLOs can enhance the cycling stability, but these coatings cannot adequately overcome the voltage decay. 53,…	Surface coating with Al2O3, CeO2, ZrO2, SiO2, ZnO, AlPO4, and Li -Ni -PO4 and mildly acidic treatment on these LLOs can enhance the cycling stability, but these coatings cannot adequately overcome the voltage decay. 53,…	Surface coating with Al2O3, CeO2, ZrO2, SiO2, ZnO, AlPO4, and Li -Ni -PO4 and mildly acidic treatment on these LLOs can enhance the cycling stability, but these coatings cannot adequately overcome the voltage decay. 53,73,74 That means that the phase transitions from layered structure into cubic spinellike structure of these LLOs not only occurs on the particle surface, but also inside the particle bulk. As a matter of fact, the transformation of layered Li 0.5 MO2 (delithiation) into the ideal cubic spinel phase (Li)8a[M2]16dO4 just requires a migration of one-fourth of the transition metal ion from the octahedral sites (3b sites) of the M planes into the empty octahedral sites (3a sites) of the lithium planes and to what become 16d positions of spinel without changing the framework of closed-paced	Surface coating with Al2O3, CeO2, ZrO2, SiO2, ZnO, AlPO4, and Li -Ni -PO4 and mildly acidic treatment on these LLOs can enhance the cycling stability, but these coatings cannot adequately overcome the voltage decay. 53,73,74 That means that the phase transitions from layered structure into cubic spinellike structure of these LLOs not only occurs on the particle surface, but also inside the particle bulk. As a matter of fact, the transformation of layered Li 0.5 MO2 (delithiation) into the ideal cubic spinel phase (Li)8a[M2]16dO4 just requires a migration of one-fourth of the transition metal ion from the octahedral sites (3b sites) of the M planes into the empty octahedral sites (3a sites) of the lithium planes and to what become 16d positions of spinel without changing the framework of closed-paced
8	8	8	90	#/texts/77	caption	caption	False	low	outside_body_flow_caption	outside_body_flow_caption						False	None	bottom_margin	column_1_of_2	1	2	p8:bottom_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 705.02, 503.99, 57.93]	Figure 9. Charge/discharge and d Q /d V pro fi les at di ff erent cycling stages ((a,b), Stage I: from the 2nd cycle to the 25th cycle; (c,d), Stage II: from the 26th cycle to the 151st cycle) of the Li/0.5Li2MnO3 · 0.5…	Figure 9. Charge/discharge and d Q /d V pro fi les at di ff erent cycling stages ((a,b), Stage I: from the 2nd cycle to the 25th cycle; (c,d), Stage II: from the 26th cycle to the 151st cycle) of the Li/0.5Li2MnO3 · 0.5…	Figure 9. Charge/discharge and d Q /d V pro fi les at di ff erent cycling stages ((a,b), Stage I: from the 2nd cycle to the 25th cycle; (c,d), Stage II: from the 26th cycle to the 151st cycle) of the Li/0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42 Co0.16 O2 cell. Raman pro fi les of the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 materials with di ff erent testing conditions: (e) pristine material; (f,g,h) electrode materials after 51 electrochemical cycles with 50 mA/g, 20 mA/g and 5 mA/g initial charge/discharge current density and 2.0 -4.8 V cuto ff voltage: (i) electrode material after 151 electrochemical cycles with 20 mA/g initial charge/discharge current density and 2.0 -4.6 V cuto ff voltage. (a -i) Reprinted with permission from ref 13. Copyright 2012 Royal Society of Chemistry.	Figure 9. Charge/discharge and d Q /d V pro fi les at di ff erent cycling stages ((a,b), Stage I: from the 2nd cycle to the 25th cycle; (c,d), Stage II: from the 26th cycle to the 151st cycle) of the Li/0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42 Co0.16 O2 cell. Raman pro fi les of the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 materials with di ff erent testing conditions: (e) pristine material; (f,g,h) electrode materials after 51 electrochemical cycles with 50 mA/g, 20 mA/g and 5 mA/g initial charge/discharge current density and 2.0 -4.8 V cuto ff voltage: (i) electrode material after 151 electrochemical cycles with 20 mA/g initial charge/discharge current density and 2.0 -4.6 V cuto ff voltage. (a -i) Reprinted with permission from ref 13.
8	10	9	91	#/texts/79	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						True	p8:body_region:1	bottom_margin	column_2_of_2	2	2	p8:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[387.33, 773.27, 177.16, 7.74]	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280
8	9	10	92	#/texts/78	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						False	None	bottom_margin	column_2_of_2	2	2	p8:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[304.5, 774.02, 15.93, 6.54]	1275	1275	1275	1275
9	3	1	93	#/texts/80	page_header	page_header	False	low	docling_page_header	docling_page_header						False	None	top_margin	column_1_of_2	1	2	p9:top_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 48.93, 181.19, 8.72]	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters
9	4	2	94	#/texts/81	page_header	page_header	False	low	docling_page_header	docling_page_header						False	None	top_margin	column_2_of_2	2	2	p9:top_margin:column_2_of_2:colored	[125, 168, 209]	colored	False	True	[519.14, 50.28, 38.3, 6.98]	Perspective	Perspective	Perspective	Perspective
9	5	3	95	#/texts/82	caption	caption	False	low	outside_body_flow_caption	outside_body_flow_caption						False	None	page_body	column_1_of_2	1	2	p9:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 344.29, 503.99, 49.53]	Figure 10. Galvanostatic intermittent titration technique (GITT) in the fi rst, second, and third (a) charge and (b) discharge processes, Li + di ff usion coe ffi cients during the fi rst three (c) charge and (d) discha…	Figure 10. Galvanostatic intermittent titration technique (GITT) in the fi rst, second, and third (a) charge and (b) discharge processes, Li + di ff usion coe ffi cients during the fi rst three (c) charge and (d) discha…	Figure 10. Galvanostatic intermittent titration technique (GITT) in the fi rst, second, and third (a) charge and (b) discharge processes, Li + di ff usion coe ffi cients during the fi rst three (c) charge and (d) discharge processes, and interface activation energy of di ff erent states during the fi rst charge (e), discharge (f), and the second charge (g) processes of the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42 Co0.16 O2 electrode material. The inset fi gures in panels e, f, and g are the d Q /d V curves during the fi rst charging, discharging, and second charging processes, respectively. (a) Reprinted with permission from ref 15. Copyright 2012 Royal Society of Chemistry.	Figure 10. Galvanostatic intermittent titration technique (GITT) in the fi rst, second, and third (a) charge and (b) discharge processes, Li + di ff usion coe ffi cients during the fi rst three (c) charge and (d) discharge processes, and interface activation energy of di ff erent states during the fi rst charge (e), discharge (f), and the second charge (g) processes of the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42 Co0.16 O2 electrode material. The inset fi gures in panels e, f, and g are the d Q /d V curves during the fi rst charging, discharging, and second charging processes, respectively. (a) Reprinted with permission from ref 15.
9	6	4	96	#/texts/83	caption	caption	False	low	outside_body_flow_caption	outside_body_flow_caption						False	None	page_body	column_1_of_2	1	2	p9:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 683.42, 503.99, 27.94]	Figure 11. (a) TEM image and (b) rate capabilities of Li[Ni 0.25 Li 0.15Mn0.6]O2 nanowires. Reprinted with permission from ref 77. Copyright 2009 Royal Society of Chemistry. (c) SEM image and (d) discharge curves with d…	Figure 11. (a) TEM image and (b) rate capabilities of Li[Ni 0.25 Li 0.15Mn0.6]O2 nanowires. Reprinted with permission from ref 77.	Figure 11. (a) TEM image and (b) rate capabilities of Li[Ni 0.25 Li 0.15Mn0.6]O2 nanowires. Reprinted with permission from ref 77. Copyright 2009 Royal Society of Chemistry. (c) SEM image and (d) discharge curves with di ff erent rates (6, 3, 1, 0.5, and 0.1C) of the Li[Li 1/3 -2 x /3Ni x Mn2/3 -x /3]O2 habit-tuned nanoplate material. Reprinted with permission from ref 78. Copyright 2010 Wiley-VCH.	Figure 11. (a) TEM image and (b) rate capabilities of Li[Ni 0.25 Li 0.15Mn0.6]O2 nanowires. Reprinted with permission from ref 77.
9	1	5	97	#/texts/76#prov1	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						False	None	bottom_margin	column_1_of_2	1	2	p9:bottom_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 730.02, 239.97, 33.18]	oxygen arrays. 75 Thus, the voltage degradations of these LLOs during cycling are also believed to be associated with both internal and surface phase transition to a cubic spinel-like phase	oxygen arrays. 75 Thus, the voltage degradations of these LLOs during cycling are also believed to be associated with both internal and surface phase transition to a cubic spinel-like phase	oxygen arrays. 75 Thus, the voltage degradations of these LLOs during cycling are also believed to be associated with both internal and surface phase transition to a cubic spinel-like phase	oxygen arrays. 75 Thus, the voltage degradations of these LLOs during cycling are also believed to be associated with both internal and surface phase transition to a cubic spinel-like phase
9	2	6	98	#/texts/76#prov2	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						False	None	bottom_margin	column_2_of_2	2	2	p9:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 732.4, 240.02, 30.8]	by the migration of transition metal ions. At present, the stepwise precycling treatment on these LLOs is used and can improve their cyclic durability. 76 The reason may be	by the migration of transition metal ions. At present, the stepwise precycling treatment on these LLOs is used and can improve their cyclic durability. 76 The reason may be	by the migration of transition metal ions. At present, the stepwise precycling treatment on these LLOs is used and can improve their cyclic durability. 76 The reason may be	by the migration of transition metal ions. At present, the stepwise precycling treatment on these LLOs is used and can improve their cyclic durability. 76 The reason may be
9	8	7	99	#/texts/85	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						False	None	bottom_margin	column_2_of_2	2	2	p9:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[387.33, 773.27, 177.16, 7.74]	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280
9	7	8	100	#/texts/84	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						False	None	bottom_margin	column_2_of_2	2	2	p9:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[304.5, 774.02, 15.93, 6.54]	1276	1276	1276	1276
10	2	1	101	#/texts/86	page_header	page_header	False	low	docling_page_header	docling_page_header						True	p10:body_region:0	top_margin	column_1_of_2	1	2	p10:top_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 48.93, 181.19, 8.72]	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters
10	3	2	102	#/texts/87	page_header	page_header	False	low	docling_page_header	docling_page_header						True	p10:body_region:1	top_margin	column_2_of_2	2	2	p10:top_margin:column_2_of_2:colored	[125, 168, 209]	colored	False	True	[519.14, 50.28, 38.3, 6.98]	Perspective	Perspective	Perspective	Perspective
10	4	3	103	#/texts/88	caption	caption	False	low	outside_body_flow_caption	outside_body_flow_caption						False	None	page_body	column_1_of_2	1	2	p10:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 384.09, 503.99, 18.97]	Figure 12. Current debates on structure and reaction mechanism, problems on electrochemical properties, and keys to the study in the future of Li 2 MnO3-based lithium-rich layered cathode materials.	Figure 12. Current debates on structure and reaction mechanism, problems on electrochemical properties, and keys to the study in the future of Li 2 MnO3-based lithium-rich layered cathode materials.	Figure 12. Current debates on structure and reaction mechanism, problems on electrochemical properties, and keys to the study in the future of Li 2 MnO3-based lithium-rich layered cathode materials.	Figure 12. Current debates on structure and reaction mechanism, problems on electrochemical properties, and keys to the study in the future of Li 2 MnO3-based lithium-rich layered cathode materials.
10	1	4	104	#/texts/76#prov3	text	unknown_text	False	high	inside_front_matter	inside_front_matter						True	p10:body_region:0	page_body	column_1_of_2	1	2	p10:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 414.92, 239.98, 31.48]	contributed by the weakened structure damage and little structure arrangement after electrochemical cycling of these materials with this pretreatment method.	contributed by the weakened structure damage and little structure arrangement after electrochemical cycling of these materials with this pretreatment method.	contributed by the weakened structure damage and little structure arrangement after electrochemical cycling of these materials with this pretreatment method.	contributed by the weakened structure damage and little structure arrangement after electrochemical cycling of these materials with this pretreatment method.
10	5	5	105	#/texts/89#prov0	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p10:body_region:0	bottom_margin	column_1_of_2	1	2	p10:bottom_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 448.76, 240.0, 314.44]	In order to reveal the kinetically controlled charge and discharge processes of these cathode materials, the lithium ion di ff usion in active material and lithium ion transfer at the e l e c t r o d e / e l e c t r o l…	In order to reveal the kinetically controlled charge and discharge processes of these cathode materials, the lithium ion di ff usion in active material and lithium ion transfer at the e l e c t r o d e / e l e c t r o l…	In order to reveal the kinetically controlled charge and discharge processes of these cathode materials, the lithium ion di ff usion in active material and lithium ion transfer at the e l e c t r o d e / e l e c t r o l y t e i n t e r f a c e o f t h e LLO (0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2) during the fi rst three cycles were studied in detail by means of galvanostatic intermittent titration (GITT; Figure 10a -d) and electrochemical impedance spectroscopy for interface activation energies (Figure 10e -g) methods. 15 Fifteen points in the fi rst charge process, and 11 points in the fi rst discharge and second and third charge/discharge processes were chosen for lithium ion di ff usion coe ffi cient calculation of this LLO (Figure 10a,b). Results show that the variation of lithium ion di ff usion coe ffi cient can be separated into two stages in all three charge and discharge processes (Figure 10c,d). On the basis of the two-phase model of this LLO, the lithium ion di ff usion coe ffi c i e n t s associated with LiMO2/MO2 (M = Mn0.42 Ni0.42 Co0.16 ) components are much larger than those associated with Li2MnO3, LiMnO2/MnO2 components. In addition, it is also obvious that the interface activation energy associated with LiMO2 (20 kJ/mol) and MO2 (31 kJ/mol, M = Mn0.42 Ni0.42Co0.16) components (Figure 10e -g) is small, while that associated with Li2MnO3 (35 kJ/mol), LiMnO2 (32 kJ/ mol), and MnO2 (35 kJ/mol) components is large. The lithium ion di ff usion coe ffi cient variations during the fi rst three charge/ discharge processes and interface activation energy variations of the electrode materials with di ff erent states, corresponding to lithium ions extraction/insertion from/into the di ff erent	In order to reveal the kinetically controlled charge and discharge processes of these cathode materials, the lithium ion di ff usion in active material and lithium ion transfer at the e l e c t r o d e / e l e c t r o l y t e i n t e r f a c e o f t h e LLO (0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2) during the fi rst three cycles were studied in detail by means of galvanostatic intermittent titration (GITT; Figure 10a -d) and electrochemical impedance spectroscopy for interface activation energies (Figure 10e -g) methods. 15 Fifteen points in the fi rst charge process, and 11 points in the fi rst discharge and second and third charge/discharge processes were chosen for lithium ion di ff usion coe ffi cient calculation of this LLO (Figure 10a,b). Results show that the variation of lithium ion di ff usion coe ffi cient can be separated into two stages in all three charge and discharge processes (Figure 10c,d). On the basis of the two-phase model of this LLO, the lithium ion di ff usion coe ffi c i e n t s associated with LiMO2/MO2 (M = Mn0.42 Ni0.42 Co0.16 ) components are much larger than those associated with Li2MnO3, LiMnO2/MnO2 components. In addition, it is also obvious that the interface activation energy associated with LiMO2 (20 kJ/mol) and MO2 (31 kJ/mol, M = Mn0.42 Ni0.42Co0.16) components (Figure 10e -g) is small, while that associated with Li2MnO3 (35 kJ/mol), LiMnO2 (32 kJ/ mol), and MnO2 (35 kJ/mol) components is large. The lithium ion di ff usion coe ffi cient variations during the fi rst three charge/ discharge processes and interface activation energy variations of the electrode materials with di ff erent states, corresponding to lithium ions extraction/insertion from/into the di ff erent
10	6	6	106	#/texts/89#prov1	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p10:body_region:1	page_body	column_2_of_2	2	2	p10:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 414.92, 240.01, 110.74]	components and interfaces (between electrode and electrolyte) are very consistent with the two-phase models proposed and con fi rmed in Figure 2. Therefore, the electrochemical kinetics of the lithium ion extraction and…	components and interfaces (between electrode and electrolyte) are very consistent with the two-phase models proposed and con fi rmed in Figure 2. Therefore, the electrochemical kinetics of the lithium ion extraction and…	components and interfaces (between electrode and electrolyte) are very consistent with the two-phase models proposed and con fi rmed in Figure 2. Therefore, the electrochemical kinetics of the lithium ion extraction and insertion reactions in these LLOs is mainly controlled by the Li2MnO3 component inside these LLOs. Even though this component can be activated after the fi rst charge process, the novel possible MnO 2 and LiMnO2 components still have lower lithium ion di ff usion coe ffi cients and higher interface reaction barriers with large activation energy.	components and interfaces (between electrode and electrolyte) are very consistent with the two-phase models proposed and con fi rmed in Figure 2. Therefore, the electrochemical kinetics of the lithium ion extraction and insertion reactions in these LLOs is mainly controlled by the Li2MnO3 component inside these LLOs. Even though this component can be activated after the fi rst charge process, the novel possible MnO 2 and LiMnO2 components still have lower lithium ion di ff usion coe ffi cients and higher interface reaction barriers with large activation energy.
10	7	7	107	#/texts/90	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p10:body_region:1	page_body	column_2_of_2	2	2	p10:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 528.02, 240.03, 201.33]	Thus, in order to improve the rate performance of these LLOs, the materials with low Li2MnO3 component proportion, short lithium ion di ff usion pathway, and small interface reaction barrier should be introduced to thes…	Thus, in order to improve the rate performance of these LLOs, the materials with low Li2MnO3 component proportion, short lithium ion di ff usion pathway, and small interface reaction barrier should be introduced to thes…	Thus, in order to improve the rate performance of these LLOs, the materials with low Li2MnO3 component proportion, short lithium ion di ff usion pathway, and small interface reaction barrier should be introduced to these materials. Kim et al. have prepared Li[Ni0.25 Li 0.15Mn0.6]O2 nanowires with an aspect ratio of several hundreds and a diameter of about 30 nm (Figure 11a), exhibiting a rate capability of 95% at 4C (=1200 mA/g) (Figure 11b). 77 Meanwhile, Wei et al. have reported that a crystal habit-tuned nanoplate materials of Li[Li 0.17 Ni0.25 Mn0.58 ]-O2, associated with signi fi cantly increased (010) nanoplates (Figure 10 c), exhibits high rate performance (Figure 10 d). 78 Through surface modi fi cation with insulating materials (Al2O3 and AlPO4), Manthiram et al. also found that the rate capability of these LLOs can be improved, which may be contributed to the lower charge-transfer resistance with small activation energy compared with the unmodi fi ed sample. 70 Thus, the crystal grain and particle surface modi fi cation of these LLOs are very useful to improve their rate performance.	Thus, in order to improve the rate performance of these LLOs, the materials with low Li2MnO3 component proportion, short lithium ion di ff usion pathway, and small interface reaction barrier should be introduced to these materials. Kim et al. have prepared Li[Ni0.25 Li 0.15Mn0.6]O2 nanowires with an aspect ratio of several hundreds and a diameter of about 30 nm (Figure 11a), exhibiting a rate capability of 95% at 4C (=1200 mA/g) (Figure 11b). 77 Meanwhile, Wei et al. have reported that a crystal habit-tuned nanoplate materials of Li[Li 0.17 Ni0.25 Mn0.58 ]-O2, associated with signi fi cantly increased (010) nanoplates (Figure 10 c), exhibits high rate performance (Figure 10 d). 78 Through surface modi fi cation with insulating materials (Al2O3 and AlPO4), Manthiram et al. also found that the rate capability of these LLOs can be improved, which may be contributed to the lower charge-transfer resistance with small activation energy compared with the unmodi fi ed sample. 70 Thus, the crystal grain and particle surface modi fi cation of these LLOs are very useful to improve their rate performance.
10	8	8	108	#/texts/91#prov0	text	body_candidate_excluded	False	high	inside_front_matter	inside_front_matter						True	p10:body_region:1	bottom_margin	column_2_of_2	2	2	p10:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 731.72, 239.97, 31.48]	The LLOs are very attractive for utilization as cathode materials for lithium ion batteries. Although researchers have put forth much e ff ort in studying these materials in the past,	The LLOs are very attractive for utilization as cathode materials for lithium ion batteries. Although researchers have put forth much e ff ort in studying these materials in the past,	The LLOs are very attractive for utilization as cathode materials for lithium ion batteries. Although researchers have put forth much e ff ort in studying these materials in the past,	The LLOs are very attractive for utilization as cathode materials for lithium ion batteries. Although researchers have put forth much e ff ort in studying these materials in the past,
10	10	9	109	#/texts/93	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						True	p10:body_region:1	bottom_margin	column_2_of_2	2	2	p10:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[387.33, 773.27, 177.16, 7.74]	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280
10	9	10	110	#/texts/92	page_footer	page_footer	False	low	docling_page_footer	docling_page_footer						False	None	bottom_margin	column_2_of_2	2	2	p10:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[304.5, 774.02, 15.93, 6.54]	1277	1277	1277	1277
11	2	1	111	#/texts/94	page_header	page_header	False	low	docling_page_header	docling_page_header						True	p11:body_region:0	top_margin	column_1_of_2	1	2	p11:top_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 48.93, 181.19, 8.72]	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters
11	1	2	112	#/texts/91#prov1	text	unknown_text	False	high	inside_front_matter	inside_front_matter						True	p11:body_region:0	page_body	column_1_of_2	1	2	p11:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 69.37, 239.99, 20.2]	many debates and issues over these materials still exist, and need to be clari fi ed and solved in the future (Figure 12).	many debates and issues over these materials still exist, and need to be clari fi ed and solved in the future (Figure 12).	many debates and issues over these materials still exist, and need to be clari fi ed and solved in the future (Figure 12).	many debates and issues over these materials still exist, and need to be clari fi ed and solved in the future (Figure 12).
11	8	7	117	#/texts/100	section_header	body_heading	False	low	body_heading	body_heading						True	p11:body_region:0	page_body	column_1_of_2	1	2	p11:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 675.56, 125.07, 23.65]	■ AUTHOR INFORMATION	■ AUTHOR INFORMATION	■ AUTHOR INFORMATION	■ AUTHOR INFORMATION
11	9	8	118	#/texts/101	section_header	body_heading	False	low	body_heading	body_heading						True	p11:body_region:0	page_body	column_1_of_2	1	2	p11:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 703.39, 93.07, 8.29]	Corresponding Author	Corresponding Author	Corresponding Author	Corresponding Author
11	10	9	119	#/texts/102	text	metadata	False	low	metadata_line	metadata_line						True	p11:body_region:0	page_body	column_1_of_2	1	2	p11:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 712.69, 239.94, 23.07]	* Fax: +81-29-861-3489; Tel: 81-29-861-5795; E-mail: hs. zhou@aist.go.jp.	* Fax: +81-29-861-3489; Tel: 81-29-861-5795; E-mail: hs. zhou@aist.go.jp.	* Fax: +81-29-861-3489; Tel: 81-29-861-5795; E-mail: hs. zhou@aist.go.jp.	* Fax: +81-29-861-3489; Tel: 81-29-861-5795; E-mail: hs. zhou@aist.go.jp.
11	11	10	120	#/texts/103	section_header	body_heading	False	low	body_heading	body_heading						True	p11:body_region:0	page_body	column_1_of_2	1	2	p11:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 741.55, 23.72, 8.29]	Notes	Notes	Notes	Notes
11	3	12	122	#/texts/95	page_header	page_header	False	low	docling_page_header	docling_page_header						False	None	top_margin	column_2_of_2	2	2	p11:top_margin:column_2_of_2:colored	[125, 168, 209]	colored	False	True	[519.14, 50.28, 38.3, 6.98]	Perspective	Perspective	Perspective	Perspective
11	13	13	123	#/texts/105	section_header	body_heading	False	low	body_heading	body_heading						False	None	page_body	column_2_of_2	2	2	p11:page_body:column_2_of_2:white	[253, 253, 253]	white	False	False	[324.45, 68.77, 48.74, 8.29]	Biographies	Biographies	Biographies	Biographies
11	16	16	126	#/texts/108	section_header	back_matter_heading	False	low	back_matter_heading	back_matter_heading					stop_trigger	False	None	page_body	column_2_of_2	2	2	p11:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 272.93, 114.79, 23.65]	■ ACKNOWLEDGMENTS	■ ACKNOWLEDGMENTS	■ ACKNOWLEDGMENTS	■ ACKNOWLEDGMENTS
11	17	17	127	#/texts/109	text	back_matter_text	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p11:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 298.08, 240.0, 31.36]	This work was partially supported fi nancially by the Funding Program for World-Leading Innovative R&D on Science and Technology (FIRST Program).	This work was partially supported fi nancially by the Funding Program for World-Leading Innovative R&D on Science and Technology (FIRST Program).	This work was partially supported fi nancially by the Funding Program for World-Leading Innovative R&D on Science and Technology (FIRST Program).	This work was partially supported fi nancially by the Funding Program for World-Leading Innovative R&D on Science and Technology (FIRST Program).
11	18	18	128	#/texts/110	section_header	back_matter_heading	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p11:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 329.62, 73.27, 23.65]	■ REFERENCES	■ REFERENCES	■ REFERENCES	■ REFERENCES
11	19	19	129	#/texts/111	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p11:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 355.0, 239.97, 18.56]	Tarascon, J. M.; Armand, M. Issues and Challenges Facing Rechargeable Lithium Batteries. Nature 2001 , 414 , 359 -367.	Tarascon, J. M.; Armand, M. Issues and Challenges Facing Rechargeable Lithium Batteries. Nature 2001 , 414 , 359 -367.	Tarascon, J. M.; Armand, M. Issues and Challenges Facing Rechargeable Lithium Batteries. Nature 2001 , 414 , 359 -367.	Tarascon, J. M.; Armand, M. Issues and Challenges Facing Rechargeable Lithium Batteries. Nature 2001 , 414 , 359 -367.
11	20	20	130	#/texts/112	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p11:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 375.01, 239.97, 18.56]	Armand, M.; Tarascon, J. M. Building Better Batteries. Nature 2008 , 451 , 652 -657.	Armand, M.; Tarascon, J. M. Building Better Batteries. Nature 2008 , 451 , 652 -657.	Armand, M.; Tarascon, J. M. Building Better Batteries. Nature 2008 , 451 , 652 -657.	Armand, M.; Tarascon, J. M. Building Better Batteries. Nature 2008 , 451 , 652 -657.
11	21	21	131	#/texts/113	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p11:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 395.03, 239.99, 18.56]	Goodenough, J. B.; Kim, Y. Challenges for Rechargeable Li Batteries. Chem. Mater. 2010 , 22 , 587 -603.	Goodenough, J. B.; Kim, Y. Challenges for Rechargeable Li Batteries. Chem. Mater. 2010 , 22 , 587 -603.	Goodenough, J. B.; Kim, Y. Challenges for Rechargeable Li Batteries. Chem. Mater. 2010 , 22 , 587 -603.	Goodenough, J. B.; Kim, Y. Challenges for Rechargeable Li Batteries. Chem. Mater. 2010 , 22 , 587 -603.
11	22	22	132	#/texts/114	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p11:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 414.98, 239.98, 18.61]	Whittingham, M. S. Lithium Batteries and Cathode Materials. Chem. Rev. 2004 , 104 , 4271 -4301.	Whittingham, M. S. Lithium Batteries and Cathode Materials. Chem. Rev. 2004 , 104 , 4271 -4301.	Whittingham, M. S. Lithium Batteries and Cathode Materials. Chem. Rev. 2004 , 104 , 4271 -4301.	Whittingham, M. S. Lithium Batteries and Cathode Materials. Chem. Rev. 2004 , 104 , 4271 -4301.
11	23	23	133	#/texts/115	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p11:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 435.0, 240.03, 28.59]	Etacheri, V.; Marom, R.; Elazari, R.; Salitra, G.; Aurbach, D. Challenges in the Development of Advanced Li-Ion Batteries: A Review. Energ. Environ. Sci. 2011 , 4 , 3243 -3262.	Etacheri, V.; Marom, R.; Elazari, R.; Salitra, G.; Aurbach, D. Challenges in the Development of Advanced Li-Ion Batteries: A Review. Energ. Environ. Sci. 2011 , 4 , 3243 -3262.	Etacheri, V.; Marom, R.; Elazari, R.; Salitra, G.; Aurbach, D. Challenges in the Development of Advanced Li-Ion Batteries: A Review. Energ. Environ. Sci. 2011 , 4 , 3243 -3262.	Etacheri, V.; Marom, R.; Elazari, R.; Salitra, G.; Aurbach, D. Challenges in the Development of Advanced Li-Ion Batteries: A Review. Energ. Environ. Sci. 2011 , 4 , 3243 -3262.
11	24	24	134	#/texts/116	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p11:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 464.99, 240.01, 37.97]	Thackeray, M. M.; Wolverton, C.; Isaacs, E. D. Electrical Energy Storage for Transportation -Approaching the Limits of, and Going Beyond, Lithium-ion Batteries. Energ. Environ. Sci. 2012 , 5 , 7854 -7863.	Thackeray, M. M.; Wolverton, C.; Isaacs, E. D. Electrical Energy Storage for Transportation -Approaching the Limits of, and Going Beyond, Lithium-ion Batteries. Energ. Environ. Sci. 2012 , 5 , 7854 -7863.	Thackeray, M. M.; Wolverton, C.; Isaacs, E. D. Electrical Energy Storage for Transportation -Approaching the Limits of, and Going Beyond, Lithium-ion Batteries. Energ. Environ. Sci. 2012 , 5 , 7854 -7863.	Thackeray, M. M.; Wolverton, C.; Isaacs, E. D. Electrical Energy Storage for Transportation -Approaching the Limits of, and Going Beyond, Lithium-ion Batteries. Energ. Environ. Sci. 2012 , 5 , 7854 -7863.
11	25	25	135	#/texts/117	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p11:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 505.02, 240.04, 28.59]	He, P.; Yu, H. J.; Li, D.; Zhou, H. S. Layered Lithium Transition Metal Oxide Cathodes towards High Energy Lithium-Ion Batteries. J. Mater. Chem. 2012 , 22 , 3680 -3695.	He, P.; Yu, H. J.; Li, D.; Zhou, H. S. Layered Lithium Transition Metal Oxide Cathodes towards High Energy Lithium-Ion Batteries. J. Mater. Chem. 2012 , 22 , 3680 -3695.	He, P.; Yu, H. J.; Li, D.; Zhou, H. S. Layered Lithium Transition Metal Oxide Cathodes towards High Energy Lithium-Ion Batteries. J. Mater. Chem. 2012 , 22 , 3680 -3695.	He, P.; Yu, H. J.; Li, D.; Zhou, H. S. Layered Lithium Transition Metal Oxide Cathodes towards High Energy Lithium-Ion Batteries. J. Mater. Chem. 2012 , 22 , 3680 -3695.
11	26	26	136	#/texts/118	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p11:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 535.01, 240.02, 28.59]	Yamada, A.; Iwane, N.; Harada, Y.; Nishimura, S.; Koyama, Y.; Tanaka, I. Lithium Iron Borates as High-Capacity Battery Electrodes. Adv. Mater. 2010 , 22 , 3583 -3587.	Yamada, A.; Iwane, N.; Harada, Y.; Nishimura, S.; Koyama, Y.; Tanaka, I. Lithium Iron Borates as High-Capacity Battery Electrodes. Adv. Mater. 2010 , 22 , 3583 -3587.	Yamada, A.; Iwane, N.; Harada, Y.; Nishimura, S.; Koyama, Y.; Tanaka, I. Lithium Iron Borates as High-Capacity Battery Electrodes. Adv. Mater. 2010 , 22 , 3583 -3587.	Yamada, A.; Iwane, N.; Harada, Y.; Nishimura, S.; Koyama, Y.; Tanaka, I. Lithium Iron Borates as High-Capacity Battery Electrodes. Adv. Mater. 2010 , 22 , 3583 -3587.
11	27	27	137	#/texts/119	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p11:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 565.0, 240.01, 28.59]	Nishimura, S.; Nakamura, M.; Natsui, R.; Yamada, A. New Lithium Iron Pyrophosphate as 3.5 V Class Cathode Material for Lithium Ion Battery. J. Am. Chem. Soc. 2010 , 132 , 13596 -13597.	Nishimura, S.; Nakamura, M.; Natsui, R.; Yamada, A. New Lithium Iron Pyrophosphate as 3.5 V Class Cathode Material for Lithium Ion Battery. J. Am. Chem. Soc. 2010 , 132 , 13596 -13597.	Nishimura, S.; Nakamura, M.; Natsui, R.; Yamada, A. New Lithium Iron Pyrophosphate as 3.5 V Class Cathode Material for Lithium Ion Battery. J. Am. Chem. Soc. 2010 , 132 , 13596 -13597.	Nishimura, S.; Nakamura, M.; Natsui, R.; Yamada, A. New Lithium Iron Pyrophosphate as 3.5 V Class Cathode Material for Lithium Ion Battery. J. Am. Chem. Soc. 2010 , 132 , 13596 -13597.
11	28	28	138	#/texts/120	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p11:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 594.99, 240.02, 48.6]	Barpanda, P.; Ati, M.; Melot, B. C.; Rousse, G.; Chotard, J. N.; Doublet, M. L.; Sougrati, M. T.; Corr, S. A.; Jumas, J. C.; Tarascon, J. M. A 3.90 V Iron-Based Fluorosulphate Material for Lithium-Ion Batteries Crystall…	Barpanda, P.; Ati, M.; Melot, B. C.; Rousse, G.; Chotard, J. N.; Doublet, M. L.; Sougrati, M. T.; Corr, S. A.; Jumas, J. C.; Tarascon, J. M. A 3.90 V Iron-Based Fluorosulphate Material for Lithium-Ion Batteries Crystall…	Barpanda, P.; Ati, M.; Melot, B. C.; Rousse, G.; Chotard, J. N.; Doublet, M. L.; Sougrati, M. T.; Corr, S. A.; Jumas, J. C.; Tarascon, J. M. A 3.90 V Iron-Based Fluorosulphate Material for Lithium-Ion Batteries Crystallizing in the Triplite Structure. Nat. Mater. 2011 , 10 , 772 -779.	Barpanda, P.; Ati, M.; Melot, B. C.; Rousse, G.; Chotard, J. N.; Doublet, M. L.; Sougrati, M. T.; Corr, S. A.; Jumas, J. C.; Tarascon, J. M. A 3.90 V Iron-Based Fluorosulphate Material for Lithium-Ion Batteries Crystallizing in the Triplite Structure. Nat. Mater. 2011 , 10 , 772 -779.
11	29	29	139	#/texts/121	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p11:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 645.0, 240.0, 38.61]	Thackeray, M. M.; Kang, S. H.; Johnson, C. S.; Vaughey, J. T.; Benedek, R.; Hackney, S. A. Li2MnO3-Stabilized LiMO2 (M = Mn, Ni, Co) Electrodes for Lithium-Ion Batteries. J. Mater. Chem. 2007 , 17 , 3112 -3125.	Thackeray, M. M.; Kang, S. H.; Johnson, C. S.; Vaughey, J. T.; Benedek, R.; Hackney, S. A. Li2MnO3-Stabilized LiMO2 (M = Mn, Ni, Co) Electrodes for Lithium-Ion Batteries. J. Mater. Chem. 2007 , 17 , 3112 -3125.	Thackeray, M. M.; Kang, S. H.; Johnson, C. S.; Vaughey, J. T.; Benedek, R.; Hackney, S. A. Li2MnO3-Stabilized LiMO2 (M = Mn, Ni, Co) Electrodes for Lithium-Ion Batteries. J. Mater. Chem. 2007 , 17 , 3112 -3125.	Thackeray, M. M.; Kang, S. H.; Johnson, C. S.; Vaughey, J. T.; Benedek, R.; Hackney, S. A. Li2MnO3-Stabilized LiMO2 (M = Mn, Ni, Co) Electrodes for Lithium-Ion Batteries. J. Mater. Chem. 2007 , 17 , 3112 -3125.
11	30	30	140	#/texts/122	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p11:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 685.01, 240.0, 28.59]	Thackeray, M. M.; Johnson, C. S.; Vaughey, J. T.; Li, N.; Hackney, S. A. Advances in Manganese-Oxide ' Composite ' Electrodes for Lithium-Ion Batteries. J. Mater. Chem. 2005 , 15 , 2257 -2267.	Thackeray, M. M.; Johnson, C. S.; Vaughey, J. T.; Li, N.; Hackney, S. A. Advances in Manganese-Oxide ' Composite ' Electrodes for Lithium-Ion Batteries. J. Mater. Chem. 2005 , 15 , 2257 -2267.	Thackeray, M. M.; Johnson, C. S.; Vaughey, J. T.; Li, N.; Hackney, S. A. Advances in Manganese-Oxide ' Composite ' Electrodes for Lithium-Ion Batteries. J. Mater. Chem. 2005 , 15 , 2257 -2267.	Thackeray, M. M.; Johnson, C. S.; Vaughey, J. T.; Li, N.; Hackney, S. A. Advances in Manganese-Oxide ' Composite ' Electrodes for Lithium-Ion Batteries. J. Mater. Chem. 2005 , 15 , 2257 -2267.
11	31	31	141	#/texts/123	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	bottom_margin	column_2_of_2	2	2	p11:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 715.0, 240.02, 48.6]	Yu, H. J.; Kim, H. J.; Wang, Y. R.; He, P.; Asakura, D.; Nakamura, Y.; Zhou, H. S. High-Energy ' Composite ' Layered Manganese-Rich Cathode Materials via Controlling Li2MnO3 Phase Activation for Lithium-Ion Batteries. P…	Yu, H. J.; Kim, H. J.; Wang, Y. R.; He, P.; Asakura, D.; Nakamura, Y.; Zhou, H. S. High-Energy ' Composite ' Layered Manganese-Rich Cathode Materials via Controlling Li2MnO3 Phase Activation for Lithium-Ion Batteries. P…	Yu, H. J.; Kim, H. J.; Wang, Y. R.; He, P.; Asakura, D.; Nakamura, Y.; Zhou, H. S. High-Energy ' Composite ' Layered Manganese-Rich Cathode Materials via Controlling Li2MnO3 Phase Activation for Lithium-Ion Batteries. Phys. Chem. Chem. Phys. 2012 , 14 , 6584 -6595.	Yu, H. J.; Kim, H. J.; Wang, Y. R.; He, P.; Asakura, D.; Nakamura, Y.; Zhou, H. S. High-Energy ' Composite ' Layered Manganese-Rich Cathode Materials via Controlling Li2MnO3 Phase Activation for Lithium-Ion Batteries. Phys. Chem. Chem. Phys. 2012 , 14 , 6584 -6595.
11	33	32	142	#/texts/125	page_footer	page_footer	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	bottom_margin	column_2_of_2	2	2	p11:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[387.33, 773.27, 177.16, 7.74]	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280
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12	1	1	144	#/texts/126	page_header	page_header	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	top_margin	column_1_of_2	1	2	p12:top_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 48.93, 181.19, 8.72]	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters
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12	4	3	146	#/texts/129	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p12:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 110.54, 239.98, 40.16]	Yu, H. J.; Wang, Y. R.; Asakura, D.; Hosono, E.; Zhou, H. S. Electrochemical Kinetics of the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 ' Composite ' Layered Cathode Material for Lithium-Ion Batteries. RSC Adv. 2012 , 2 , …	Yu, H. J.; Wang, Y. R.; Asakura, D.; Hosono, E.; Zhou, H. S. Electrochemical Kinetics of the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 ' Composite ' Layered Cathode Material for Lithium-Ion Batteries. RSC Adv. 2012 , 2 , …	Yu, H. J.; Wang, Y. R.; Asakura, D.; Hosono, E.; Zhou, H. S. Electrochemical Kinetics of the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 ' Composite ' Layered Cathode Material for Lithium-Ion Batteries. RSC Adv. 2012 , 2 , 8797 -8807.	Yu, H. J.; Wang, Y. R.; Asakura, D.; Hosono, E.; Zhou, H. S. Electrochemical Kinetics of the 0.5Li2MnO3 · 0.5LiMn0.42 Ni0.42Co0.16O2 ' Composite ' Layered Cathode Material for Lithium-Ion Batteries. RSC Adv. 2012 , 2 , 8797 -8807.
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12	6	5	148	#/texts/131	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p12:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 183.17, 239.98, 40.15]	Rossouw, M. H.; Liles, D. C.; Thackeray, M. M. Synthesis and Structural Characterization of a Novel Layered Lithium Manganese Oxide, Li 0.36 Mn0.91O2, and Its Lithiated Derivative, Li 1.09 Mn0.91O2. J. Solid State Chem.…	Rossouw, M. H.; Liles, D. C.; Thackeray, M. M. Synthesis and Structural Characterization of a Novel Layered Lithium Manganese Oxide, Li 0.36 Mn0.91O2, and Its Lithiated Derivative, Li 1.09 Mn0.91O2. J. Solid State Chem.…	Rossouw, M. H.; Liles, D. C.; Thackeray, M. M. Synthesis and Structural Characterization of a Novel Layered Lithium Manganese Oxide, Li 0.36 Mn0.91O2, and Its Lithiated Derivative, Li 1.09 Mn0.91O2. J. Solid State Chem. 1993 , 104 , 464 -466.	Rossouw, M. H.; Liles, D. C.; Thackeray, M. M. Synthesis and Structural Characterization of a Novel Layered Lithium Manganese Oxide, Li 0.36 Mn0.91O2, and Its Lithiated Derivative, Li 1.09 Mn0.91O2. J. Solid State Chem. 1993 , 104 , 464 -466.
12	7	6	149	#/texts/132	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p12:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 224.72, 239.98, 29.61]	Kalyani, P.; Chitra, S.; Mohan, T.; Gopukumar, S. Lithium Metal Rechargeable Cells Using Li 2 MnO3 as the Positive Electrode. J. Power Sources 1999 , 80 , 103 -106.	Kalyani, P.; Chitra, S.; Mohan, T.; Gopukumar, S. Lithium Metal Rechargeable Cells Using Li 2 MnO3 as the Positive Electrode. J. Power Sources 1999 , 80 , 103 -106.	Kalyani, P.; Chitra, S.; Mohan, T.; Gopukumar, S. Lithium Metal Rechargeable Cells Using Li 2 MnO3 as the Positive Electrode. J. Power Sources 1999 , 80 , 103 -106.	Kalyani, P.; Chitra, S.; Mohan, T.; Gopukumar, S. Lithium Metal Rechargeable Cells Using Li 2 MnO3 as the Positive Electrode. J. Power Sources 1999 , 80 , 103 -106.
12	8	7	150	#/texts/133	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p12:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 255.79, 240.0, 29.61]	Ammundsen, B.; Paulsen, J. Novel Lithium-Ion Cathode Materials Based on Layered Manganese Oxides. Adv. Mater. 2001 , 13 , 943 -956.	Ammundsen, B.; Paulsen, J. Novel Lithium-Ion Cathode Materials Based on Layered Manganese Oxides. Adv. Mater. 2001 , 13 , 943 -956.	Ammundsen, B.; Paulsen, J. Novel Lithium-Ion Cathode Materials Based on Layered Manganese Oxides. Adv. Mater. 2001 , 13 , 943 -956.	Ammundsen, B.; Paulsen, J. Novel Lithium-Ion Cathode Materials Based on Layered Manganese Oxides. Adv. Mater. 2001 , 13 , 943 -956.
12	9	8	151	#/texts/134	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p12:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 286.8, 239.98, 40.15]	Ammundsen, B.; Paulsen, J.; Davidson, I.; Liu, R. S.; Shen, C. H.; Chen, J. M.; Jang, L. Y.; Lee, J. F. Local Structure and First Cycle Redox Mechanism of Layered Li1.2Cr0.4Mn0.4O2 Cathode Material. J. Electrochem. Soc.…	Ammundsen, B.; Paulsen, J.; Davidson, I.; Liu, R. S.; Shen, C. H.; Chen, J. M.; Jang, L. Y.; Lee, J. F. Local Structure and First Cycle Redox Mechanism of Layered Li1.2Cr0.4Mn0.4O2 Cathode Material. J. Electrochem. Soc.…	Ammundsen, B.; Paulsen, J.; Davidson, I.; Liu, R. S.; Shen, C. H.; Chen, J. M.; Jang, L. Y.; Lee, J. F. Local Structure and First Cycle Redox Mechanism of Layered Li1.2Cr0.4Mn0.4O2 Cathode Material. J. Electrochem. Soc. 2002 , 149 , A431 -A436.	Ammundsen, B.; Paulsen, J.; Davidson, I.; Liu, R. S.; Shen, C. H.; Chen, J. M.; Jang, L. Y.; Lee, J. F. Local Structure and First Cycle Redox Mechanism of Layered Li1.2Cr0.4Mn0.4O2 Cathode Material. J. Electrochem. Soc. 2002 , 149 , A431 -A436.
12	10	9	152	#/texts/135	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p12:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 328.36, 239.97, 40.16]	Kikkawa, J.; Akita, T.; Tabuchi, M.; Shikano, M.; Tatsumi, K.; Kohyama, M. Fe-Rich and Mn-Rich Nanodomains in Li1.2Mn0.4Fe0.4O2 Positive Electrode Materials for Lithium-Ion Batteries. Appl. Phys. Lett. 2007 , 91 , 05410…	Kikkawa, J.; Akita, T.; Tabuchi, M.; Shikano, M.; Tatsumi, K.; Kohyama, M. Fe-Rich and Mn-Rich Nanodomains in Li1.2Mn0.4Fe0.4O2 Positive Electrode Materials for Lithium-Ion Batteries. Appl. Phys. Lett. 2007 , 91 , 05410…	Kikkawa, J.; Akita, T.; Tabuchi, M.; Shikano, M.; Tatsumi, K.; Kohyama, M. Fe-Rich and Mn-Rich Nanodomains in Li1.2Mn0.4Fe0.4O2 Positive Electrode Materials for Lithium-Ion Batteries. Appl. Phys. Lett. 2007 , 91 , 054103(1) -054103(3).	Kikkawa, J.; Akita, T.; Tabuchi, M.; Shikano, M.; Tatsumi, K.; Kohyama, M. Fe-Rich and Mn-Rich Nanodomains in Li1.2Mn0.4Fe0.4O2 Positive Electrode Materials for Lithium-Ion Batteries. Appl. Phys. Lett. 2007 , 91 , 054103(1) -054103(3).
12	11	10	153	#/texts/136	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p12:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 369.91, 240.0, 50.7]	Kikkawa, J.; Akita, T.; Tabuchi, M.; Shikano, M.; Tatsumi, K.; Kohyama, M. Coexistence of Layered and Cubic Rocksalt Structures with a Common Oxygen Sublattice in Li1.2Mn0.4Fe0.4O2 Particles: A Transmission Electron Mic…	Kikkawa, J.; Akita, T.; Tabuchi, M.; Shikano, M.; Tatsumi, K.; Kohyama, M. Coexistence of Layered and Cubic Rocksalt Structures with a Common Oxygen Sublattice in Li1.2Mn0.4Fe0.4O2 Particles: A Transmission Electron Mic…	Kikkawa, J.; Akita, T.; Tabuchi, M.; Shikano, M.; Tatsumi, K.; Kohyama, M. Coexistence of Layered and Cubic Rocksalt Structures with a Common Oxygen Sublattice in Li1.2Mn0.4Fe0.4O2 Particles: A Transmission Electron Microscopy Study. J. Appl. Phys. 2008 , 103 , 104911(1) -104911(10).	Kikkawa, J.; Akita, T.; Tabuchi, M.; Shikano, M.; Tatsumi, K.; Kohyama, M. Coexistence of Layered and Cubic Rocksalt Structures with a Common Oxygen Sublattice in Li1.2Mn0.4Fe0.4O2 Particles: A Transmission Electron Microscopy Study. J. Appl. Phys. 2008 , 103 , 104911(1) -104911(10).
12	12	11	154	#/texts/137	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p12:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 422.01, 239.97, 40.16]	Kikkawa, J.; Akita, T.; Tabuchi, M.; Shikano, M.; Tatsumi, K.; Kohyama, M. Formation and Disappearance of Spinel Nanograins in Li 1.2 -x Mn0.4Fe0.4O2 (0 ≤ x ≤ 0.99) during Extraction and Insertion of Li Ions. J. Electro…	Kikkawa, J.; Akita, T.; Tabuchi, M.; Shikano, M.; Tatsumi, K.; Kohyama, M. Formation and Disappearance of Spinel Nanograins in Li 1.2 -x Mn0.4Fe0.4O2 (0 ≤ x ≤ 0.99) during Extraction and Insertion of Li Ions. J. Electro…	Kikkawa, J.; Akita, T.; Tabuchi, M.; Shikano, M.; Tatsumi, K.; Kohyama, M. Formation and Disappearance of Spinel Nanograins in Li 1.2 -x Mn0.4Fe0.4O2 (0 ≤ x ≤ 0.99) during Extraction and Insertion of Li Ions. J. Electrochem. Soc. 2009 , 156 , A839 -A845.	Kikkawa, J.; Akita, T.; Tabuchi, M.; Shikano, M.; Tatsumi, K.; Kohyama, M. Formation and Disappearance of Spinel Nanograins in Li 1.2 -x Mn0.4Fe0.4O2 (0 ≤ x ≤ 0.99) during Extraction and Insertion of Li Ions. J. Electrochem. Soc. 2009 , 156 , A839 -A845.
12	13	12	155	#/texts/138	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p12:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 463.57, 239.99, 40.15]	Kikkawa, J.; Akita, T.; Tabuchi, M.; Tatsumi, K.; Kohyama, M. Participation of Oxygen in Charge/Discharge Reactions in Li 1.2 Mn0.4Fe0.4O2: Evidence of Removal/Reinsertion of Oxide Ions. J. Electrochem. Soc. 2011 , 158 …	Kikkawa, J.; Akita, T.; Tabuchi, M.; Tatsumi, K.; Kohyama, M. Participation of Oxygen in Charge/Discharge Reactions in Li 1.2 Mn0.4Fe0.4O2: Evidence of Removal/Reinsertion of Oxide Ions. J. Electrochem. Soc. 2011 , 158 …	Kikkawa, J.; Akita, T.; Tabuchi, M.; Tatsumi, K.; Kohyama, M. Participation of Oxygen in Charge/Discharge Reactions in Li 1.2 Mn0.4Fe0.4O2: Evidence of Removal/Reinsertion of Oxide Ions. J. Electrochem. Soc. 2011 , 158 , A760 -A768.	Kikkawa, J.; Akita, T.; Tabuchi, M.; Tatsumi, K.; Kohyama, M. Participation of Oxygen in Charge/Discharge Reactions in Li 1.2 Mn0.4Fe0.4O2: Evidence of Removal/Reinsertion of Oxide Ions. J. Electrochem. Soc. 2011 , 158 , A760 -A768.
12	14	13	156	#/texts/139	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p12:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 505.12, 239.96, 40.15]	Kim, J. S.; Johnson, C. S.; Vaughey, J. T.; Thackeray, M. M.; Hackney, S. A. Electrochemical and Structural Properties of x Li2M ′ O3 · (1 -x )LiMn0.5 Ni0.5O2 Electrodes for Lithium Batteries (M ′ = Ti, Mn, Zr; 0 ≤ x ≤ …	Kim, J. S.; Johnson, C. S.; Vaughey, J. T.; Thackeray, M. M.; Hackney, S. A. Electrochemical and Structural Properties of x Li2M ′ O3 · (1 -x )LiMn0.5 Ni0.5O2 Electrodes for Lithium Batteries (M ′ = Ti, Mn, Zr; 0 ≤ x ≤ …	Kim, J. S.; Johnson, C. S.; Vaughey, J. T.; Thackeray, M. M.; Hackney, S. A. Electrochemical and Structural Properties of x Li2M ′ O3 · (1 -x )LiMn0.5 Ni0.5O2 Electrodes for Lithium Batteries (M ′ = Ti, Mn, Zr; 0 ≤ x ≤ 0.3). Chem. Mater. 2004 , 16 , 1996 -2006.	Kim, J. S.; Johnson, C. S.; Vaughey, J. T.; Thackeray, M. M.; Hackney, S. A. Electrochemical and Structural Properties of x Li2M ′ O3 · (1 -x )LiMn0.5 Ni0.5O2 Electrodes for Lithium Batteries (M ′ = Ti, Mn, Zr; 0 ≤ x ≤ 0.3). Chem. Mater. 2004 , 16 , 1996 -2006.
12	15	14	157	#/texts/140	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p12:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 546.68, 239.99, 40.16]	Cabana, J.; Johnson, C. S.; Yang, X. Q.; Chung, K. Y.; Yoon, W. S.; Kang, S. H.; Thackeray, M. M.; Grey, C. P. Structural Complexity of Layered-Spinel Composite Electrodes for Li-ion Batteries. J. Mater. Res. 2010 , 25 …	Cabana, J.; Johnson, C. S.; Yang, X. Q.; Chung, K. Y.; Yoon, W. S.; Kang, S. H.; Thackeray, M. M.; Grey, C. P. Structural Complexity of Layered-Spinel Composite Electrodes for Li-ion Batteries. J. Mater. Res. 2010 , 25 …	Cabana, J.; Johnson, C. S.; Yang, X. Q.; Chung, K. Y.; Yoon, W. S.; Kang, S. H.; Thackeray, M. M.; Grey, C. P. Structural Complexity of Layered-Spinel Composite Electrodes for Li-ion Batteries. J. Mater. Res. 2010 , 25 , 1601 -1616.	Cabana, J.; Johnson, C. S.; Yang, X. Q.; Chung, K. Y.; Yoon, W. S.; Kang, S. H.; Thackeray, M. M.; Grey, C. P. Structural Complexity of Layered-Spinel Composite Electrodes for Li-ion Batteries. J. Mater. Res. 2010 , 25 , 1601 -1616.
12	16	15	158	#/texts/141	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p12:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 588.24, 239.98, 49.99]	Pan, C. J.; Lee, Y. J.; Ammundsen, B.; Grey, C. P. Li-6 MAS NMR Studies of the Local Structure and Electrochemical Properties of Cr-Doped Lithium Manganese and Lithium Cobalt Oxide Cathode Materials for Lithium-Ion Batt…	Pan, C. J.; Lee, Y. J.; Ammundsen, B.; Grey, C. P. Li-6 MAS NMR Studies of the Local Structure and Electrochemical Properties of Cr-Doped Lithium Manganese and Lithium Cobalt Oxide Cathode Materials for Lithium-Ion Batt…	Pan, C. J.; Lee, Y. J.; Ammundsen, B.; Grey, C. P. Li-6 MAS NMR Studies of the Local Structure and Electrochemical Properties of Cr-Doped Lithium Manganese and Lithium Cobalt Oxide Cathode Materials for Lithium-Ion Batteries. Chem. Mater. 2002 , 14 , 2289 -2299.	Pan, C. J.; Lee, Y. J.; Ammundsen, B.; Grey, C. P. Li-6 MAS NMR Studies of the Local Structure and Electrochemical Properties of Cr-Doped Lithium Manganese and Lithium Cobalt Oxide Cathode Materials for Lithium-Ion Batteries. Chem. Mater. 2002 , 14 , 2289 -2299.
12	17	16	159	#/texts/142	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p12:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 640.34, 239.94, 40.16]	Park, S. H.; Kang, S. H.; Johnson, C. S.; Amine, K.; Thackeray, M. M. Lithium-Manganese-Nickel-Oxide Electrodes with Integrated Layered-Spinel Structures for Lithium Batteries. Electrochem. Commun. 2007 , 9 , 262 -268.	Park, S. H.; Kang, S. H.; Johnson, C. S.; Amine, K.; Thackeray, M. M. Lithium-Manganese-Nickel-Oxide Electrodes with Integrated Layered-Spinel Structures for Lithium Batteries. Electrochem. Commun. 2007 , 9 , 262 -268.	Park, S. H.; Kang, S. H.; Johnson, C. S.; Amine, K.; Thackeray, M. M. Lithium-Manganese-Nickel-Oxide Electrodes with Integrated Layered-Spinel Structures for Lithium Batteries. Electrochem. Commun. 2007 , 9 , 262 -268.	Park, S. H.; Kang, S. H.; Johnson, C. S.; Amine, K.; Thackeray, M. M. Lithium-Manganese-Nickel-Oxide Electrodes with Integrated Layered-Spinel Structures for Lithium Batteries. Electrochem. Commun. 2007 , 9 , 262 -268.
12	18	17	160	#/texts/143	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p12:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 681.9, 240.0, 40.15]	Bareno, J.; Balasubramanian, M.; Kang, S. H.; Wen, J. G.; Lei, C. H.; Pol, S. V.; Petrov, I.; Abraham, D. P. Long-Range and Local Structure in the Layered Oxide Li 1.2 Co0.4Mn0.4O2. Chem. Mater. 2011 , 23 , 2039 -2050.	Bareno, J.; Balasubramanian, M.; Kang, S. H.; Wen, J. G.; Lei, C. H.; Pol, S. V.; Petrov, I.; Abraham, D. P. Long-Range and Local Structure in the Layered Oxide Li 1.2 Co0.4Mn0.4O2. Chem. Mater. 2011 , 23 , 2039 -2050.	Bareno, J.; Balasubramanian, M.; Kang, S. H.; Wen, J. G.; Lei, C. H.; Pol, S. V.; Petrov, I.; Abraham, D. P. Long-Range and Local Structure in the Layered Oxide Li 1.2 Co0.4Mn0.4O2. Chem. Mater. 2011 , 23 , 2039 -2050.	Bareno, J.; Balasubramanian, M.; Kang, S. H.; Wen, J. G.; Lei, C. H.; Pol, S. V.; Petrov, I.; Abraham, D. P. Long-Range and Local Structure in the Layered Oxide Li 1.2 Co0.4Mn0.4O2. Chem. Mater. 2011 , 23 , 2039 -2050.
12	19	18	161	#/texts/144	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	bottom_margin	column_1_of_2	1	2	p12:bottom_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 723.45, 240.0, 40.16]	Lei, C. H.; Bareno, J.; Wen, J. G.; Petrov, I.; Kang, S. H.; Abraham, D. P. Local Structure and Composition Studies of Li 1.2 Ni0.2Mn0.6O2 by Analytical Electron Microscopy. J. Power Sources 2008 , 178 , 422 -433.	Lei, C. H.; Bareno, J.; Wen, J. G.; Petrov, I.; Kang, S. H.; Abraham, D. P. Local Structure and Composition Studies of Li 1.2 Ni0.2Mn0.6O2 by Analytical Electron Microscopy. J. Power Sources 2008 , 178 , 422 -433.	Lei, C. H.; Bareno, J.; Wen, J. G.; Petrov, I.; Kang, S. H.; Abraham, D. P. Local Structure and Composition Studies of Li 1.2 Ni0.2Mn0.6O2 by Analytical Electron Microscopy. J. Power Sources 2008 , 178 , 422 -433.	Lei, C. H.; Bareno, J.; Wen, J. G.; Petrov, I.; Kang, S. H.; Abraham, D. P. Local Structure and Composition Studies of Li 1.2 Ni0.2Mn0.6O2 by Analytical Electron Microscopy. J. Power Sources 2008 , 178 , 422 -433.
12	2	19	162	#/texts/127	page_header	page_header	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	top_margin	column_2_of_2	2	2	p12:top_margin:column_2_of_2:colored	[125, 168, 209]	colored	False	True	[519.14, 50.28, 38.3, 6.98]	Perspective	Perspective	Perspective	Perspective
12	20	20	163	#/texts/145	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p12:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.46, 68.99, 239.99, 28.82]	Bareno, J.; Lei, C. H.; Wen, J. G.; Kang, S. H.; Petrov, I.; Abraham, D. P. Local Structure of Layered Oxide Electrode Materials for Lithium-Ion Batteries. Adv. Mater. 2010 , 22 , 1122 -1127.	Bareno, J.; Lei, C. H.; Wen, J. G.; Kang, S. H.; Petrov, I.; Abraham, D. P. Local Structure of Layered Oxide Electrode Materials for Lithium-Ion Batteries. Adv. Mater. 2010 , 22 , 1122 -1127.	Bareno, J.; Lei, C. H.; Wen, J. G.; Kang, S. H.; Petrov, I.; Abraham, D. P. Local Structure of Layered Oxide Electrode Materials for Lithium-Ion Batteries. Adv. Mater. 2010 , 22 , 1122 -1127.	Bareno, J.; Lei, C. H.; Wen, J. G.; Kang, S. H.; Petrov, I.; Abraham, D. P. Local Structure of Layered Oxide Electrode Materials for Lithium-Ion Batteries. Adv. Mater. 2010 , 22 , 1122 -1127.
12	21	21	164	#/texts/146	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p12:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.46, 99.26, 240.02, 38.91]	Gu, M.; Belharouak, I.; Genc, A.; Wang, Z. G.; Wang, D. P.; Amine, K.; Gao, F.; Zhou, G. W.; Thevuthasan, S.; Baer, D. R.; et al. Conflicting Roles of Nickel in Controlling Cathode Performance in Lithium Ion Batteries. …	Gu, M.; Belharouak, I.; Genc, A.; Wang, Z. G.; Wang, D. P.; Amine, K.; Gao, F.; Zhou, G. W.; Thevuthasan, S.; Baer, D. R.; et al. Conflicting Roles of Nickel in Controlling Cathode Performance in Lithium Ion Batteries. …	Gu, M.; Belharouak, I.; Genc, A.; Wang, Z. G.; Wang, D. P.; Amine, K.; Gao, F.; Zhou, G. W.; Thevuthasan, S.; Baer, D. R.; et al. Conflicting Roles of Nickel in Controlling Cathode Performance in Lithium Ion Batteries. Nano Lett. 2012 , 12 , 5186 -5191.	Gu, M.; Belharouak, I.; Genc, A.; Wang, Z. G.; Wang, D. P.; Amine, K.; Gao, F.; Zhou, G. W.; Thevuthasan, S.; Baer, D. R.; et al. Conflicting Roles of Nickel in Controlling Cathode Performance in Lithium Ion Batteries. Nano Lett. 2012 , 12 , 5186 -5191.
12	22	22	165	#/texts/147	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p12:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 139.63, 240.0, 38.91]	Boulineau, A.; Simonin, L.; Colin, J. F.; Canevet, E.; Daniel, L.; Patoux, S. Evolutions of Li 1.2 Mn0.61 Ni0.18Mg0.01O2 during the Initial Charge/Discharge Cycle Studied by Advanced Electron Microscopy. Chem. Mater. 20…	Boulineau, A.; Simonin, L.; Colin, J. F.; Canevet, E.; Daniel, L.; Patoux, S. Evolutions of Li 1.2 Mn0.61 Ni0.18Mg0.01O2 during the Initial Charge/Discharge Cycle Studied by Advanced Electron Microscopy. Chem. Mater. 20…	Boulineau, A.; Simonin, L.; Colin, J. F.; Canevet, E.; Daniel, L.; Patoux, S. Evolutions of Li 1.2 Mn0.61 Ni0.18Mg0.01O2 during the Initial Charge/Discharge Cycle Studied by Advanced Electron Microscopy. Chem. Mater. 2012 , 24 , 3558 -3566.	Boulineau, A.; Simonin, L.; Colin, J. F.; Canevet, E.; Daniel, L.; Patoux, S. Evolutions of Li 1.2 Mn0.61 Ni0.18Mg0.01O2 during the Initial Charge/Discharge Cycle Studied by Advanced Electron Microscopy. Chem. Mater. 2012 , 24 , 3558 -3566.
12	23	23	166	#/texts/148	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p12:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 179.93, 240.02, 38.97]	Xu, B.; Fell, C. R.; Chi, M. F.; Meng, Y. S. Identifying Surface Structural Changes in Layered Li-Excess Nickel Manganese Oxides in High Voltage Lithium Ion Batteries: A Joint Experimental and Theoretical Study. Energ. …	Xu, B.; Fell, C. R.; Chi, M. F.; Meng, Y. S. Identifying Surface Structural Changes in Layered Li-Excess Nickel Manganese Oxides in High Voltage Lithium Ion Batteries: A Joint Experimental and Theoretical Study. Energ. …	Xu, B.; Fell, C. R.; Chi, M. F.; Meng, Y. S. Identifying Surface Structural Changes in Layered Li-Excess Nickel Manganese Oxides in High Voltage Lithium Ion Batteries: A Joint Experimental and Theoretical Study. Energ. Environ. Sci. 2011 , 4 , 2223 -2233.	Xu, B.; Fell, C. R.; Chi, M. F.; Meng, Y. S. Identifying Surface Structural Changes in Layered Li-Excess Nickel Manganese Oxides in High Voltage Lithium Ion Batteries: A Joint Experimental and Theoretical Study. Energ. Environ. Sci. 2011 , 4 , 2223 -2233.
12	24	24	167	#/texts/149	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p12:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 220.3, 240.01, 49.05]	Koga, H.; Croguennec, L.; Mannessiez, P.; Menetrier, M.; Weill, F.; Bourgeois, L.; Duttine, M.; Suard, E.; Delmas, C. Li 1.20 Mn0.54 Co0.13 Ni0.13O2 with Different Particle Sizes as Attractive Positive Electrode Materia…	Koga, H.; Croguennec, L.; Mannessiez, P.; Menetrier, M.; Weill, F.; Bourgeois, L.; Duttine, M.; Suard, E.; Delmas, C. Li 1.20 Mn0.54 Co0.13 Ni0.13O2 with Different Particle Sizes as Attractive Positive Electrode Materia…	Koga, H.; Croguennec, L.; Mannessiez, P.; Menetrier, M.; Weill, F.; Bourgeois, L.; Duttine, M.; Suard, E.; Delmas, C. Li 1.20 Mn0.54 Co0.13 Ni0.13O2 with Different Particle Sizes as Attractive Positive Electrode Materials for Lithium-Ion Batteries: Insights into Their Structure. J. Phys. Chem. C 2012 , 116 , 13497 -13506.	Koga, H.; Croguennec, L.; Mannessiez, P.; Menetrier, M.; Weill, F.; Bourgeois, L.; Duttine, M.; Suard, E.; Delmas, C. Li 1.20 Mn0.54 Co0.13 Ni0.13O2 with Different Particle Sizes as Attractive Positive Electrode Materials for Lithium-Ion Batteries: Insights into Their Structure. J. Phys. Chem. C 2012 , 116 , 13497 -13506.
12	25	25	168	#/texts/150	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p12:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 270.76, 240.03, 38.96]	Wen, J. G.; Bareno, J.; Lei, C. H.; Kang, S. H.; Balasubramanian, M.; Petrov, I.; Abraham, D. P. Analytical Electron Microscopy of Li 1.2Co0.4Mn0.4O2 for Lithium-Ion Batteries. Solid State Ionics 2011 , 182 , 98 -107.	Wen, J. G.; Bareno, J.; Lei, C. H.; Kang, S. H.; Balasubramanian, M.; Petrov, I.; Abraham, D. P. Analytical Electron Microscopy of Li 1.2Co0.4Mn0.4O2 for Lithium-Ion Batteries. Solid State Ionics 2011 , 182 , 98 -107.	Wen, J. G.; Bareno, J.; Lei, C. H.; Kang, S. H.; Balasubramanian, M.; Petrov, I.; Abraham, D. P. Analytical Electron Microscopy of Li 1.2Co0.4Mn0.4O2 for Lithium-Ion Batteries. Solid State Ionics 2011 , 182 , 98 -107.	Wen, J. G.; Bareno, J.; Lei, C. H.; Kang, S. H.; Balasubramanian, M.; Petrov, I.; Abraham, D. P. Analytical Electron Microscopy of Li 1.2Co0.4Mn0.4O2 for Lithium-Ion Batteries. Solid State Ionics 2011 , 182 , 98 -107.
12	26	26	169	#/texts/151	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p12:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 311.12, 240.0, 38.91]	Jarvis, K. A.; Deng, Z. Q.; Allard, L. F.; Manthiram, A.; Ferreira, P. J. Atomic Structure of a Lithium-Rich Layered Oxide Material for Lithium-Ion Batteries: Evidence of A Solid Solution. Chem. Mater. 2011 , 23 , 3614 …	Jarvis, K. A.; Deng, Z. Q.; Allard, L. F.; Manthiram, A.; Ferreira, P. J. Atomic Structure of a Lithium-Rich Layered Oxide Material for Lithium-Ion Batteries: Evidence of A Solid Solution. Chem. Mater. 2011 , 23 , 3614 …	Jarvis, K. A.; Deng, Z. Q.; Allard, L. F.; Manthiram, A.; Ferreira, P. J. Atomic Structure of a Lithium-Rich Layered Oxide Material for Lithium-Ion Batteries: Evidence of A Solid Solution. Chem. Mater. 2011 , 23 , 3614 -3621.	Jarvis, K. A.; Deng, Z. Q.; Allard, L. F.; Manthiram, A.; Ferreira, P. J. Atomic Structure of a Lithium-Rich Layered Oxide Material for Lithium-Ion Batteries: Evidence of A Solid Solution. Chem. Mater. 2011 , 23 , 3614 -3621.
12	27	27	170	#/texts/152	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p12:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 351.49, 239.99, 28.82]	Yoon, W. S.; Kim, N.; Yang, X. Q.; McBreen, J.; Grey, C. P. Li-6 MAS NMR and in Situ X-Ray Studies of Lithium Nickel Manganese Oxides. J. Power Sources 2003 , 119 , 649 -653.	Yoon, W. S.; Kim, N.; Yang, X. Q.; McBreen, J.; Grey, C. P. Li-6 MAS NMR and in Situ X-Ray Studies of Lithium Nickel Manganese Oxides. J. Power Sources 2003 , 119 , 649 -653.	Yoon, W. S.; Kim, N.; Yang, X. Q.; McBreen, J.; Grey, C. P. Li-6 MAS NMR and in Situ X-Ray Studies of Lithium Nickel Manganese Oxides. J. Power Sources 2003 , 119 , 649 -653.	Yoon, W. S.; Kim, N.; Yang, X. Q.; McBreen, J.; Grey, C. P. Li-6 MAS NMR and in Situ X-Ray Studies of Lithium Nickel Manganese Oxides. J. Power Sources 2003 , 119 , 649 -653.
12	28	28	171	#/texts/153	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p12:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 381.71, 240.03, 49.05]	Breger, J.; Jiang, M.; Dupre, N.; Meng, Y. S.; Shao-Horn, Y.; Ceder, G.; Grey, C. P. High-Resolution X-ray Diffraction, DIFFaX, NMR and First Principles Study of Disorder in the Li2MnO3Li[Ni1/2Mn1/2]O2 Solid Solution. J…	Breger, J.; Jiang, M.; Dupre, N.; Meng, Y. S.; Shao-Horn, Y.; Ceder, G.; Grey, C. P. High-Resolution X-ray Diffraction, DIFFaX, NMR and First Principles Study of Disorder in the Li2MnO3Li[Ni1/2Mn1/2]O2 Solid Solution. J…	Breger, J.; Jiang, M.; Dupre, N.; Meng, Y. S.; Shao-Horn, Y.; Ceder, G.; Grey, C. P. High-Resolution X-ray Diffraction, DIFFaX, NMR and First Principles Study of Disorder in the Li2MnO3Li[Ni1/2Mn1/2]O2 Solid Solution. J. Solid State Chem. 2005 , 178 , 2575 -2585.	Breger, J.; Jiang, M.; Dupre, N.; Meng, Y. S.; Shao-Horn, Y.; Ceder, G.; Grey, C. P. High-Resolution X-ray Diffraction, DIFFaX, NMR and First Principles Study of Disorder in the Li2MnO3Li[Ni1/2Mn1/2]O2 Solid Solution. J. Solid State Chem. 2005 , 178 , 2575 -2585.
12	29	29	172	#/texts/154	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p12:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 432.16, 240.01, 48.4]	Ohzuku, T.; Nagayama, M.; Tsuji, K.; Ariyoshi, K. HighCapacity Lithium Insertion Materials of Lithium Nickel Manganese Oxides for Advanced Lithium-ion Batteries: Toward Rechargeable Capacity More Than 300 mA h g -1 . J.…	Ohzuku, T.; Nagayama, M.; Tsuji, K.; Ariyoshi, K. HighCapacity Lithium Insertion Materials of Lithium Nickel Manganese Oxides for Advanced Lithium-ion Batteries: Toward Rechargeable Capacity More Than 300 mA h g -1 . J.…	Ohzuku, T.; Nagayama, M.; Tsuji, K.; Ariyoshi, K. HighCapacity Lithium Insertion Materials of Lithium Nickel Manganese Oxides for Advanced Lithium-ion Batteries: Toward Rechargeable Capacity More Than 300 mA h g -1 . J. Mater. Chem. 2011 , 21 , 10179 -10188.	Ohzuku, T.; Nagayama, M.; Tsuji, K.; Ariyoshi, K. HighCapacity Lithium Insertion Materials of Lithium Nickel Manganese Oxides for Advanced Lithium-ion Batteries: Toward Rechargeable Capacity More Than 300 mA h g -1 . J. Mater. Chem. 2011 , 21 , 10179 -10188.
12	30	30	173	#/texts/155	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p12:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 482.67, 240.0, 38.91]	Thackeray, M. M.; Kang, S. H.; Johnson, C. S.; Vaughey, J. T.; Hackney, S. A. Comments on the Structural Complexity of LithiumRich Li1+xM1 -x O2 Electrodes (M = Mn, Ni, Co) for Lithium Batteries. Electrochem. Commun. 20…	Thackeray, M. M.; Kang, S. H.; Johnson, C. S.; Vaughey, J. T.; Hackney, S. A. Comments on the Structural Complexity of LithiumRich Li1+xM1 -x O2 Electrodes (M = Mn, Ni, Co) for Lithium Batteries. Electrochem. Commun. 20…	Thackeray, M. M.; Kang, S. H.; Johnson, C. S.; Vaughey, J. T.; Hackney, S. A. Comments on the Structural Complexity of LithiumRich Li1+xM1 -x O2 Electrodes (M = Mn, Ni, Co) for Lithium Batteries. Electrochem. Commun. 2006 , 8 , 1531 -1538.	Thackeray, M. M.; Kang, S. H.; Johnson, C. S.; Vaughey, J. T.; Hackney, S. A. Comments on the Structural Complexity of LithiumRich Li1+xM1 -x O2 Electrodes (M = Mn, Ni, Co) for Lithium Batteries. Electrochem. Commun. 2006 , 8 , 1531 -1538.
12	31	31	174	#/texts/156	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p12:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 522.98, 240.0, 49.06]	Kang, S. H.; Kempgens, P.; Greenbaum, S.; Kropf, A. J.; Amine, K.; Thackeray, M. M. Interpreting the Structural and Electrochemical Complexity of 0.5Li2MnO3 · 0.5LiMO2 Electrodes for Lithium Batteries (M = Mn0.5 -x Ni0.…	Kang, S. H.; Kempgens, P.; Greenbaum, S.; Kropf, A. J.; Amine, K.; Thackeray, M. M. Interpreting the Structural and Electrochemical Complexity of 0.5Li2MnO3 · 0.5LiMO2 Electrodes for Lithium Batteries (M = Mn0.5 -x Ni0.…	Kang, S. H.; Kempgens, P.; Greenbaum, S.; Kropf, A. J.; Amine, K.; Thackeray, M. M. Interpreting the Structural and Electrochemical Complexity of 0.5Li2MnO3 · 0.5LiMO2 Electrodes for Lithium Batteries (M = Mn0.5 -x Ni0.5 -x Co2 x , 0 ≤ x ≤ 0.5). J. Mater. Chem. 2007 , 17 , 2069 -2077.	Kang, S. H.; Kempgens, P.; Greenbaum, S.; Kropf, A. J.; Amine, K.; Thackeray, M. M. Interpreting the Structural and Electrochemical Complexity of 0.5Li2MnO3 · 0.5LiMO2 Electrodes for Lithium Batteries (M = Mn0.5 -x Ni0.5 -x Co2 x , 0 ≤ x ≤ 0.5). J. Mater. Chem. 2007 , 17 , 2069 -2077.
12	32	32	175	#/texts/157	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p12:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 573.5, 240.02, 38.91]	Kikkawa, J.; Akita, T.; Tabuchi, M.; Shikano, M.; Tatsumi, K.; Kohyama, M. Real-Space Observation of Li Extraction/Insertion in Li 1.2Mn0.4Fe0.4O2 Positive Electrode Material for Li-Ion Batteries. Electrochem. Solid-Sta…	Kikkawa, J.; Akita, T.; Tabuchi, M.; Shikano, M.; Tatsumi, K.; Kohyama, M. Real-Space Observation of Li Extraction/Insertion in Li 1.2Mn0.4Fe0.4O2 Positive Electrode Material for Li-Ion Batteries. Electrochem. Solid-Sta…	Kikkawa, J.; Akita, T.; Tabuchi, M.; Shikano, M.; Tatsumi, K.; Kohyama, M. Real-Space Observation of Li Extraction/Insertion in Li 1.2Mn0.4Fe0.4O2 Positive Electrode Material for Li-Ion Batteries. Electrochem. Solid-State Lett. 2008 , 11 , A183 -A186.	Kikkawa, J.; Akita, T.; Tabuchi, M.; Shikano, M.; Tatsumi, K.; Kohyama, M. Real-Space Observation of Li Extraction/Insertion in Li 1.2Mn0.4Fe0.4O2 Positive Electrode Material for Li-Ion Batteries. Electrochem. Solid-State Lett. 2008 , 11 , A183 -A186.
12	33	33	176	#/texts/158	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p12:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 613.81, 240.0, 28.82]	Grinberg, I.; Cooper, V. R.; Rappe, A. M. Relationship Between Local Structure and Phase Transitions of A Disordered Solid Solution. Nature 2002 , 419 , 909 -911.	Grinberg, I.; Cooper, V. R.; Rappe, A. M. Relationship Between Local Structure and Phase Transitions of A Disordered Solid Solution. Nature 2002 , 419 , 909 -911.	Grinberg, I.; Cooper, V. R.; Rappe, A. M. Relationship Between Local Structure and Phase Transitions of A Disordered Solid Solution. Nature 2002 , 419 , 909 -911.	Grinberg, I.; Cooper, V. R.; Rappe, A. M. Relationship Between Local Structure and Phase Transitions of A Disordered Solid Solution. Nature 2002 , 419 , 909 -911.
12	34	34	177	#/texts/159	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p12:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 644.08, 239.99, 28.82]	Frenkel, A.; Stern, E. A.; Voronel, A.; Qian, M.; Newville, M. Buckled Crystalline-Structure of Mixed Ionic Salts. Phys. Rev. Lett. 1993 , 71 , 3485 -3488.	Frenkel, A.; Stern, E. A.; Voronel, A.; Qian, M.; Newville, M. Buckled Crystalline-Structure of Mixed Ionic Salts. Phys. Rev. Lett. 1993 , 71 , 3485 -3488.	Frenkel, A.; Stern, E. A.; Voronel, A.; Qian, M.; Newville, M. Buckled Crystalline-Structure of Mixed Ionic Salts. Phys. Rev. Lett. 1993 , 71 , 3485 -3488.	Frenkel, A.; Stern, E. A.; Voronel, A.; Qian, M.; Newville, M. Buckled Crystalline-Structure of Mixed Ionic Salts. Phys. Rev. Lett. 1993 , 71 , 3485 -3488.
12	35	35	178	#/texts/160	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p12:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 674.3, 240.01, 28.81]	Lei, C. H.; Wen, J. G.; Sardela, M.; Bareno, J.; Petrov, I.; Kang, S. H.; Abraham, D. P. Structural Study of Li2MnO3 by Electron Microscopy. J. Mater. Sci. 2009 , 44 , 5579 -5587.	Lei, C. H.; Wen, J. G.; Sardela, M.; Bareno, J.; Petrov, I.; Kang, S. H.; Abraham, D. P. Structural Study of Li2MnO3 by Electron Microscopy. J. Mater. Sci. 2009 , 44 , 5579 -5587.	Lei, C. H.; Wen, J. G.; Sardela, M.; Bareno, J.; Petrov, I.; Kang, S. H.; Abraham, D. P. Structural Study of Li2MnO3 by Electron Microscopy. J. Mater. Sci. 2009 , 44 , 5579 -5587.	Lei, C. H.; Wen, J. G.; Sardela, M.; Bareno, J.; Petrov, I.; Kang, S. H.; Abraham, D. P. Structural Study of Li2MnO3 by Electron Microscopy. J. Mater. Sci. 2009 , 44 , 5579 -5587.
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12	39	38	181	#/texts/164	page_footer	page_footer	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	bottom_margin	column_2_of_2	2	2	p12:bottom_margin:column_2_of_2:white	[255, 255, 255]	white	False	False	[387.33, 773.27, 177.16, 7.74]	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280	dx.doi.org/10.1021/jz400032v | J. Phys. Chem. Lett. 2013, 4, 1268 -1280
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13	1	1	183	#/texts/165	page_header	page_header	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	top_margin	column_1_of_2	1	2	p13:top_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 48.93, 181.19, 8.72]	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters	The Journal of Physical Chemistry Letters
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13	4	3	185	#/texts/168	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p13:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 109.35, 240.07, 38.91]	Yabuuchi, N.; Yoshii, K.; Myung, S. T.; Nakai, I.; Komaba, S. Detailed Studies of a High-Capacity Electrode Material for Rechargeable Batteries, Li2MnO3 -LiCo1/3Ni1/3Mn1/3O2. J. Am. Chem. Soc. 2011 , 133 , 4404 -4419.	Yabuuchi, N.; Yoshii, K.; Myung, S. T.; Nakai, I.; Komaba, S. Detailed Studies of a High-Capacity Electrode Material for Rechargeable Batteries, Li2MnO3 -LiCo1/3Ni1/3Mn1/3O2. J. Am. Chem. Soc. 2011 , 133 , 4404 -4419.	Yabuuchi, N.; Yoshii, K.; Myung, S. T.; Nakai, I.; Komaba, S. Detailed Studies of a High-Capacity Electrode Material for Rechargeable Batteries, Li2MnO3 -LiCo1/3Ni1/3Mn1/3O2. J. Am. Chem. Soc. 2011 , 133 , 4404 -4419.	Yabuuchi, N.; Yoshii, K.; Myung, S. T.; Nakai, I.; Komaba, S. Detailed Studies of a High-Capacity Electrode Material for Rechargeable Batteries, Li2MnO3 -LiCo1/3Ni1/3Mn1/3O2. J. Am. Chem. Soc. 2011 , 133 , 4404 -4419.
13	5	4	186	#/texts/169	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p13:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 149.72, 239.97, 38.91]	Johnson, C. S.; Kim, J. S.; Lefief, C.; Li, N.; Vaughey, J. T.; Thackeray, M. M. The Significance of the Li2MnO3 Component in ' Composite ' x Li2MnO3 · (1 -x )LiMn0.5Ni0.5O2 Electrodes. Electrochem. Commun. 2004 , 6 , 1…	Johnson, C. S.; Kim, J. S.; Lefief, C.; Li, N.; Vaughey, J. T.; Thackeray, M. M. The Significance of the Li2MnO3 Component in ' Composite ' x Li2MnO3 · (1 -x )LiMn0.5Ni0.5O2 Electrodes. Electrochem. Commun. 2004 , 6 , 1…	Johnson, C. S.; Kim, J. S.; Lefief, C.; Li, N.; Vaughey, J. T.; Thackeray, M. M. The Significance of the Li2MnO3 Component in ' Composite ' x Li2MnO3 · (1 -x )LiMn0.5Ni0.5O2 Electrodes. Electrochem. Commun. 2004 , 6 , 1085 -1091.	Johnson, C. S.; Kim, J. S.; Lefief, C.; Li, N.; Vaughey, J. T.; Thackeray, M. M. The Significance of the Li2MnO3 Component in ' Composite ' x Li2MnO3 · (1 -x )LiMn0.5Ni0.5O2 Electrodes. Electrochem. Commun. 2004 , 6 , 1085 -1091.
13	6	5	187	#/texts/170	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p13:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 190.03, 239.96, 48.4]	Armstrong, A. R.; Holzapfel, M.; Novak, P.; Johnson, C. S.; Kang, S. H.; Thackeray, M. M.; Bruce, P. G. Demonstrating Oxygen Loss and Associated Structural Reorganization in the Lithium Battery Cathode Li[Ni0.2Li0.2Mn0.…	Armstrong, A. R.; Holzapfel, M.; Novak, P.; Johnson, C. S.; Kang, S. H.; Thackeray, M. M.; Bruce, P. G. Demonstrating Oxygen Loss and Associated Structural Reorganization in the Lithium Battery Cathode Li[Ni0.2Li0.2Mn0.…	Armstrong, A. R.; Holzapfel, M.; Novak, P.; Johnson, C. S.; Kang, S. H.; Thackeray, M. M.; Bruce, P. G. Demonstrating Oxygen Loss and Associated Structural Reorganization in the Lithium Battery Cathode Li[Ni0.2Li0.2Mn0.6]O2. J. Am. Chem. Soc. 2006 , 128 , 8694 -8698.	Armstrong, A. R.; Holzapfel, M.; Novak, P.; Johnson, C. S.; Kang, S. H.; Thackeray, M. M.; Bruce, P. G. Demonstrating Oxygen Loss and Associated Structural Reorganization in the Lithium Battery Cathode Li[Ni0.2Li0.2Mn0.6]O2. J. Am. Chem. Soc. 2006 , 128 , 8694 -8698.
13	7	6	188	#/texts/171	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p13:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 240.48, 239.94, 38.96]	Kang, S. H.; Johnson, C. S.; Vaughey, J. T.; Amine, K.; Thackeray, M. M. The Effects of Acid Treatment on the Electrochemical Properties of 0.5Li2MnO3 · 0.5LiNi 0.44 Co0.25 Mn0.31 O2 Electrodes in Lithium Cells. J. Elec…	Kang, S. H.; Johnson, C. S.; Vaughey, J. T.; Amine, K.; Thackeray, M. M. The Effects of Acid Treatment on the Electrochemical Properties of 0.5Li2MnO3 · 0.5LiNi 0.44 Co0.25 Mn0.31 O2 Electrodes in Lithium Cells. J. Elec…	Kang, S. H.; Johnson, C. S.; Vaughey, J. T.; Amine, K.; Thackeray, M. M. The Effects of Acid Treatment on the Electrochemical Properties of 0.5Li2MnO3 · 0.5LiNi 0.44 Co0.25 Mn0.31 O2 Electrodes in Lithium Cells. J. Electrochem. Soc. 2006 , 153 , A1186 -A1192.	Kang, S. H.; Johnson, C. S.; Vaughey, J. T.; Amine, K.; Thackeray, M. M. The Effects of Acid Treatment on the Electrochemical Properties of 0.5Li2MnO3 · 0.5LiNi 0.44 Co0.25 Mn0.31 O2 Electrodes in Lithium Cells. J. Electrochem. Soc. 2006 , 153 , A1186 -A1192.
13	8	7	189	#/texts/172	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p13:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 280.85, 239.99, 38.91]	Johnson, C. S.; Li, N. C.; Lefief, C.; Thackeray, M. M. Anomalous Capacity and Cycling Stability of x Li2MnO3 · (1 -x )LiMO2 Electrodes (M = Mn, Ni, Co) in Lithium Batteries at 50 ° C. Electrochem. Commun. 2007 , 9 , 78…	Johnson, C. S.; Li, N. C.; Lefief, C.; Thackeray, M. M. Anomalous Capacity and Cycling Stability of x Li2MnO3 · (1 -x )LiMO2 Electrodes (M = Mn, Ni, Co) in Lithium Batteries at 50 ° C. Electrochem. Commun. 2007 , 9 , 78…	Johnson, C. S.; Li, N. C.; Lefief, C.; Thackeray, M. M. Anomalous Capacity and Cycling Stability of x Li2MnO3 · (1 -x )LiMO2 Electrodes (M = Mn, Ni, Co) in Lithium Batteries at 50 ° C. Electrochem. Commun. 2007 , 9 , 787 -795.	Johnson, C. S.; Li, N. C.; Lefief, C.; Thackeray, M. M. Anomalous Capacity and Cycling Stability of x Li2MnO3 · (1 -x )LiMO2 Electrodes (M = Mn, Ni, Co) in Lithium Batteries at 50 ° C. Electrochem. Commun. 2007 , 9 , 787 -795.
13	9	8	190	#/texts/173	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p13:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 321.21, 239.98, 28.82]	Hy, S.; Su, W. N.; Chen, J. M.; Hwang, B. J. Soft X-ray Absorption Spectroscopic and Raman Studies on Li1.2 Ni0.2Mn0.6O2 for Lithium-Ion Batteries. J. Phys. Chem. C 2012 , 116 , 25242 -25247.	Hy, S.; Su, W. N.; Chen, J. M.; Hwang, B. J. Soft X-ray Absorption Spectroscopic and Raman Studies on Li1.2 Ni0.2Mn0.6O2 for Lithium-Ion Batteries. J. Phys. Chem. C 2012 , 116 , 25242 -25247.	Hy, S.; Su, W. N.; Chen, J. M.; Hwang, B. J. Soft X-ray Absorption Spectroscopic and Raman Studies on Li1.2 Ni0.2Mn0.6O2 for Lithium-Ion Batteries. J. Phys. Chem. C 2012 , 116 , 25242 -25247.	Hy, S.; Su, W. N.; Chen, J. M.; Hwang, B. J. Soft X-ray Absorption Spectroscopic and Raman Studies on Li1.2 Ni0.2Mn0.6O2 for Lithium-Ion Batteries. J. Phys. Chem. C 2012 , 116 , 25242 -25247.
13	10	9	191	#/texts/174	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p13:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 351.43, 240.0, 38.91]	Lu, Z. H.; Dahn, J. R. Understanding the Anomalous Capacity of Li/Li[Ni x Li (1/3 -2 x /3)Mn(2/3 -x /3)]O2 Cells Using in Situ X-ray Diffraction and Electrochemical Studies. J. Electrochem. Soc. 2002 , 149 , A815 -A822.	Lu, Z. H.; Dahn, J. R. Understanding the Anomalous Capacity of Li/Li[Ni x Li (1/3 -2 x /3)Mn(2/3 -x /3)]O2 Cells Using in Situ X-ray Diffraction and Electrochemical Studies. J. Electrochem. Soc. 2002 , 149 , A815 -A822.	Lu, Z. H.; Dahn, J. R. Understanding the Anomalous Capacity of Li/Li[Ni x Li (1/3 -2 x /3)Mn(2/3 -x /3)]O2 Cells Using in Situ X-ray Diffraction and Electrochemical Studies. J. Electrochem. Soc. 2002 , 149 , A815 -A822.	Lu, Z. H.; Dahn, J. R. Understanding the Anomalous Capacity of Li/Li[Ni x Li (1/3 -2 x /3)Mn(2/3 -x /3)]O2 Cells Using in Situ X-ray Diffraction and Electrochemical Studies. J. Electrochem. Soc. 2002 , 149 , A815 -A822.
13	11	10	192	#/texts/175	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p13:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 391.8, 239.97, 38.91]	Simonin, L.; Colin, J. F.; Ranieri, V.; Canevet, E.; Martin, J. F.; Bourbon, C.; Baehtz, C.; Strobel, P.; Daniel, L.; Patoux, S. In Situ Investigations of A Li-Rich Mn-Ni Layered Oxide for Li-Ion Batteries. J. Mater. Ch…	Simonin, L.; Colin, J. F.; Ranieri, V.; Canevet, E.; Martin, J. F.; Bourbon, C.; Baehtz, C.; Strobel, P.; Daniel, L.; Patoux, S. In Situ Investigations of A Li-Rich Mn-Ni Layered Oxide for Li-Ion Batteries. J. Mater. Ch…	Simonin, L.; Colin, J. F.; Ranieri, V.; Canevet, E.; Martin, J. F.; Bourbon, C.; Baehtz, C.; Strobel, P.; Daniel, L.; Patoux, S. In Situ Investigations of A Li-Rich Mn-Ni Layered Oxide for Li-Ion Batteries. J. Mater. Chem. 2012 , 22 , 11316 -11322.	Simonin, L.; Colin, J. F.; Ranieri, V.; Canevet, E.; Martin, J. F.; Bourbon, C.; Baehtz, C.; Strobel, P.; Daniel, L.; Patoux, S. In Situ Investigations of A Li-Rich Mn-Ni Layered Oxide for Li-Ion Batteries. J. Mater. Chem. 2012 , 22 , 11316 -11322.
13	12	11	193	#/texts/176	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p13:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 432.11, 240.0, 38.96]	Jiang, M.; Key, B.; Meng, Y. S.; Grey, C. P. Electrochemical and Structural Study of the Layered, ' Li-Excess ' Lithium-Ion Battery Electrode Material Li[Li 1/9Ni1/3Mn5/9]O2. Chem. Mater. 2009 , 21 , 2733 -2745.	Jiang, M.; Key, B.; Meng, Y. S.; Grey, C. P. Electrochemical and Structural Study of the Layered, ' Li-Excess ' Lithium-Ion Battery Electrode Material Li[Li 1/9Ni1/3Mn5/9]O2. Chem. Mater. 2009 , 21 , 2733 -2745.	Jiang, M.; Key, B.; Meng, Y. S.; Grey, C. P. Electrochemical and Structural Study of the Layered, ' Li-Excess ' Lithium-Ion Battery Electrode Material Li[Li 1/9Ni1/3Mn5/9]O2. Chem. Mater. 2009 , 21 , 2733 -2745.	Jiang, M.; Key, B.; Meng, Y. S.; Grey, C. P. Electrochemical and Structural Study of the Layered, ' Li-Excess ' Lithium-Ion Battery Electrode Material Li[Li 1/9Ni1/3Mn5/9]O2. Chem. Mater. 2009 , 21 , 2733 -2745.
13	13	12	194	#/texts/177	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p13:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 472.47, 239.98, 38.91]	Johnson, C. S.; Li, N. C.; Lefief, C.; Vaughey, J. T.; Thackeray, M. M. Synthesis, Characterization and Electrochemistry of Lithium Battery Electrodes: x Li2MnO3 · (1 -x )LiMn0.333 Ni0.333 Co0.333O2 (0 ≤ x ≤ 0.7). Chem.…	Johnson, C. S.; Li, N. C.; Lefief, C.; Vaughey, J. T.; Thackeray, M. M. Synthesis, Characterization and Electrochemistry of Lithium Battery Electrodes: x Li2MnO3 · (1 -x )LiMn0.333 Ni0.333 Co0.333O2 (0 ≤ x ≤ 0.7). Chem.…	Johnson, C. S.; Li, N. C.; Lefief, C.; Vaughey, J. T.; Thackeray, M. M. Synthesis, Characterization and Electrochemistry of Lithium Battery Electrodes: x Li2MnO3 · (1 -x )LiMn0.333 Ni0.333 Co0.333O2 (0 ≤ x ≤ 0.7). Chem. Mater. 2008 , 20 , 6095 -6106.	Johnson, C. S.; Li, N. C.; Lefief, C.; Vaughey, J. T.; Thackeray, M. M. Synthesis, Characterization and Electrochemistry of Lithium Battery Electrodes: x Li2MnO3 · (1 -x )LiMn0.333 Ni0.333 Co0.333O2 (0 ≤ x ≤ 0.7). Chem. Mater. 2008 , 20 , 6095 -6106.
13	14	13	195	#/texts/178	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p13:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 512.83, 239.98, 49.0]	Amalraj, F.; Kovacheva, D.; Talianker, M.; Zeiri, L.; Grinblat, J.; Leifer, N.; Goobes, G.; Markovsky, B.; Aurbach, D. Synthesis of Integrated Cathode Materials x Li2MnO3 · (1 -x )LiMn1/3Ni1/3Co1/3O2 ( x = 0.3, 0.5, 0.7…	Amalraj, F.; Kovacheva, D.; Talianker, M.; Zeiri, L.; Grinblat, J.; Leifer, N.; Goobes, G.; Markovsky, B.; Aurbach, D. Synthesis of Integrated Cathode Materials x Li2MnO3 · (1 -x )LiMn1/3Ni1/3Co1/3O2 ( x = 0.3, 0.5, 0.7…	Amalraj, F.; Kovacheva, D.; Talianker, M.; Zeiri, L.; Grinblat, J.; Leifer, N.; Goobes, G.; Markovsky, B.; Aurbach, D. Synthesis of Integrated Cathode Materials x Li2MnO3 · (1 -x )LiMn1/3Ni1/3Co1/3O2 ( x = 0.3, 0.5, 0.7) and Studies of Their Electrochemical Behavior. J. Electrochem. Soc. 2010 , 157 , A1121 -A1130.	Amalraj, F.; Kovacheva, D.; Talianker, M.; Zeiri, L.; Grinblat, J.; Leifer, N.; Goobes, G.; Markovsky, B.; Aurbach, D. Synthesis of Integrated Cathode Materials x Li2MnO3 · (1 -x )LiMn1/3Ni1/3Co1/3O2 ( x = 0.3, 0.5, 0.7) and Studies of Their Electrochemical Behavior. J. Electrochem. Soc. 2010 , 157 , A1121 -A1130.
13	15	14	196	#/texts/179	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p13:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 563.29, 239.97, 38.91]	Zheng, J. M.; Wu, X. B.; Yang, Y. A Comparison of Preparation Method on the Electrochemical Performance of Cathode Material Li[Li 0.2 Mn0.54 Ni0.13 Co0.13]O2 for Lithium Ion Battery. Electrochim. Acta 2011 , 56 , 3071 -…	Zheng, J. M.; Wu, X. B.; Yang, Y. A Comparison of Preparation Method on the Electrochemical Performance of Cathode Material Li[Li 0.2 Mn0.54 Ni0.13 Co0.13]O2 for Lithium Ion Battery. Electrochim. Acta 2011 , 56 , 3071 -…	Zheng, J. M.; Wu, X. B.; Yang, Y. A Comparison of Preparation Method on the Electrochemical Performance of Cathode Material Li[Li 0.2 Mn0.54 Ni0.13 Co0.13]O2 for Lithium Ion Battery. Electrochim. Acta 2011 , 56 , 3071 -3078.	Zheng, J. M.; Wu, X. B.; Yang, Y. A Comparison of Preparation Method on the Electrochemical Performance of Cathode Material Li[Li 0.2 Mn0.54 Ni0.13 Co0.13]O2 for Lithium Ion Battery. Electrochim. Acta 2011 , 56 , 3071 -3078.
13	16	15	197	#/texts/180	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p13:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 603.6, 239.96, 38.97]	Van Bommel, A.; Dahn, J. R. Kinetics Study of the High Potential Range of Lithium-Rich Transition-Metal Oxides for LithiumIon Batteries by Electrochemical Methods. Electrochem. Solid-State Lett. 2010 , 13 , A62 -A64.	Van Bommel, A.; Dahn, J. R. Kinetics Study of the High Potential Range of Lithium-Rich Transition-Metal Oxides for LithiumIon Batteries by Electrochemical Methods. Electrochem. Solid-State Lett. 2010 , 13 , A62 -A64.	Van Bommel, A.; Dahn, J. R. Kinetics Study of the High Potential Range of Lithium-Rich Transition-Metal Oxides for LithiumIon Batteries by Electrochemical Methods. Electrochem. Solid-State Lett. 2010 , 13 , A62 -A64.	Van Bommel, A.; Dahn, J. R. Kinetics Study of the High Potential Range of Lithium-Rich Transition-Metal Oxides for LithiumIon Batteries by Electrochemical Methods. Electrochem. Solid-State Lett. 2010 , 13 , A62 -A64.
13	17	16	198	#/texts/181	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p13:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 643.97, 239.98, 38.91]	Lim, J. H.; Bang, H.; Lee, K. S.; Amine, K.; Sun, Y. K. Electrochemical Characterization of Li2MnO3 -Li[Ni1/3Co1/3Mn1/3]O2 -LiNiO2 Cathode Synthesized via Co-precipitation for Lithium Secondary Batteries. J. Power Sourc…	Lim, J. H.; Bang, H.; Lee, K. S.; Amine, K.; Sun, Y. K. Electrochemical Characterization of Li2MnO3 -Li[Ni1/3Co1/3Mn1/3]O2 -LiNiO2 Cathode Synthesized via Co-precipitation for Lithium Secondary Batteries. J. Power Sourc…	Lim, J. H.; Bang, H.; Lee, K. S.; Amine, K.; Sun, Y. K. Electrochemical Characterization of Li2MnO3 -Li[Ni1/3Co1/3Mn1/3]O2 -LiNiO2 Cathode Synthesized via Co-precipitation for Lithium Secondary Batteries. J. Power Sources 2009 , 189 , 571 -575.	Lim, J. H.; Bang, H.; Lee, K. S.; Amine, K.; Sun, Y. K. Electrochemical Characterization of Li2MnO3 -Li[Ni1/3Co1/3Mn1/3]O2 -LiNiO2 Cathode Synthesized via Co-precipitation for Lithium Secondary Batteries. J. Power Sources 2009 , 189 , 571 -575.
13	18	17	199	#/texts/182	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_1_of_2	1	2	p13:page_body:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 684.33, 239.97, 38.26]	Mangani, I. R.; Park, C. W.; Yoon, Y. K.; Beom, J. H.; Kim, J. Synthesis and Characterization of Li[Li 0.27 Cr0.15 Al0.05Mn0.53]O2 Cathode for Lithium-Ion Batteries. J. Electrochem. Soc. 2007 , 154 , A359 -A363.	Mangani, I. R.; Park, C. W.; Yoon, Y. K.; Beom, J. H.; Kim, J. Synthesis and Characterization of Li[Li 0.27 Cr0.15 Al0.05Mn0.53]O2 Cathode for Lithium-Ion Batteries. J. Electrochem. Soc. 2007 , 154 , A359 -A363.	Mangani, I. R.; Park, C. W.; Yoon, Y. K.; Beom, J. H.; Kim, J. Synthesis and Characterization of Li[Li 0.27 Cr0.15 Al0.05Mn0.53]O2 Cathode for Lithium-Ion Batteries. J. Electrochem. Soc. 2007 , 154 , A359 -A363.	Mangani, I. R.; Park, C. W.; Yoon, Y. K.; Beom, J. H.; Kim, J. Synthesis and Characterization of Li[Li 0.27 Cr0.15 Al0.05Mn0.53]O2 Cathode for Lithium-Ion Batteries. J. Electrochem. Soc. 2007 , 154 , A359 -A363.
13	19	18	200	#/texts/183	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	bottom_margin	column_1_of_2	1	2	p13:bottom_margin:column_1_of_2:white	[255, 255, 255]	white	False	False	[60.49, 724.64, 240.0, 38.96]	Park, C. W.; Kim, S. H.; Mangani, I. R.; Lee, J. H.; Boo, S.; Kim, J. Synthesis and Materials Characterization of Li2MnO3-LiCrO2 System Nanocomposite Electrode Materials. Mater. Res. Bull. 2007 , 42 , 1374 -1383.	Park, C. W.; Kim, S. H.; Mangani, I. R.; Lee, J. H.; Boo, S.; Kim, J. Synthesis and Materials Characterization of Li2MnO3-LiCrO2 System Nanocomposite Electrode Materials. Mater. Res. Bull. 2007 , 42 , 1374 -1383.	Park, C. W.; Kim, S. H.; Mangani, I. R.; Lee, J. H.; Boo, S.; Kim, J. Synthesis and Materials Characterization of Li2MnO3-LiCrO2 System Nanocomposite Electrode Materials. Mater. Res. Bull. 2007 , 42 , 1374 -1383.	Park, C. W.; Kim, S. H.; Mangani, I. R.; Lee, J. H.; Boo, S.; Kim, J. Synthesis and Materials Characterization of Li2MnO3-LiCrO2 System Nanocomposite Electrode Materials. Mater. Res. Bull. 2007 , 42 , 1374 -1383.
13	2	19	201	#/texts/166	page_header	page_header	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	top_margin	column_2_of_2	2	2	p13:top_margin:column_2_of_2:colored	[125, 168, 209]	colored	False	True	[519.14, 50.28, 38.3, 6.98]	Perspective	Perspective	Perspective	Perspective
13	20	20	202	#/texts/184	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p13:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 68.99, 240.0, 48.6]	Tabuchi, M.; Nakashima, A.; Ado, K.; Sakaebe, H.; Kobayashi, H.; Kageyama, H.; Tatsumi, K.; Kobayashi, Y.; Seki, S.; Yamanaka, A. The Effects of Preparation Condition and Dopant on the Electrochemical Property for Fe-Su…	Tabuchi, M.; Nakashima, A.; Ado, K.; Sakaebe, H.; Kobayashi, H.; Kageyama, H.; Tatsumi, K.; Kobayashi, Y.; Seki, S.; Yamanaka, A. The Effects of Preparation Condition and Dopant on the Electrochemical Property for Fe-Su…	Tabuchi, M.; Nakashima, A.; Ado, K.; Sakaebe, H.; Kobayashi, H.; Kageyama, H.; Tatsumi, K.; Kobayashi, Y.; Seki, S.; Yamanaka, A. The Effects of Preparation Condition and Dopant on the Electrochemical Property for Fe-Substituted Li2MnO3. J. Power Sources 2005 , 146 , 287 -293.	Tabuchi, M.; Nakashima, A.; Ado, K.; Sakaebe, H.; Kobayashi, H.; Kageyama, H.; Tatsumi, K.; Kobayashi, Y.; Seki, S.; Yamanaka, A. The Effects of Preparation Condition and Dopant on the Electrochemical Property for Fe-Substituted Li2MnO3. J. Power Sources 2005 , 146 , 287 -293.
13	21	21	203	#/texts/185	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p13:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 118.99, 240.02, 38.62]	Tabuchi, M.; Nakashima, A.; Ado, K.; Kageyarna, H.; Tatsumi, K. Heat-Treatment Effect on Phase Stability, Cation Distribution, Chemical Composition, and Electrochemical Behavior for FeSubstituted Li2MnO3. Chem. Mater. 2…	Tabuchi, M.; Nakashima, A.; Ado, K.; Kageyarna, H.; Tatsumi, K. Heat-Treatment Effect on Phase Stability, Cation Distribution, Chemical Composition, and Electrochemical Behavior for FeSubstituted Li2MnO3. Chem. Mater. 2…	Tabuchi, M.; Nakashima, A.; Ado, K.; Kageyarna, H.; Tatsumi, K. Heat-Treatment Effect on Phase Stability, Cation Distribution, Chemical Composition, and Electrochemical Behavior for FeSubstituted Li2MnO3. Chem. Mater. 2005 , 17 , 4668 -4677.	Tabuchi, M.; Nakashima, A.; Ado, K.; Kageyarna, H.; Tatsumi, K. Heat-Treatment Effect on Phase Stability, Cation Distribution, Chemical Composition, and Electrochemical Behavior for FeSubstituted Li2MnO3. Chem. Mater. 2005 , 17 , 4668 -4677.
13	22	22	204	#/texts/186	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p13:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 159.01, 240.08, 28.95]	Van Bommel, A.; Krause, L. J.; Dahn, J. R. Investigation of the Irreversible Capacity Loss in the Lithium-Rich Oxide Li[Li 1/5Ni1/5Mn3/5]O2. J. Electrochem. Soc. 2011 , 158 , A731 -A735.	Van Bommel, A.; Krause, L. J.; Dahn, J. R. Investigation of the Irreversible Capacity Loss in the Lithium-Rich Oxide Li[Li 1/5Ni1/5Mn3/5]O2. J. Electrochem. Soc. 2011 , 158 , A731 -A735.	Van Bommel, A.; Krause, L. J.; Dahn, J. R. Investigation of the Irreversible Capacity Loss in the Lithium-Rich Oxide Li[Li 1/5Ni1/5Mn3/5]O2. J. Electrochem. Soc. 2011 , 158 , A731 -A735.	Van Bommel, A.; Krause, L. J.; Dahn, J. R. Investigation of the Irreversible Capacity Loss in the Lithium-Rich Oxide Li[Li 1/5Ni1/5Mn3/5]O2. J. Electrochem. Soc. 2011 , 158 , A731 -A735.
13	23	23	205	#/texts/187	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p13:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 185.97, 240.01, 31.62]	Kang, S. H.; Thackeray, M. M. Stabilization of x Li2MnO3 · (1 -x )LiMO2 Electrode Surfaces (M = Mn, Ni, Co) with Mildly Acidic, Fluorinated Solutions. J. Electrochem. Soc. 2008 , 155 , A269 -A275.	Kang, S. H.; Thackeray, M. M. Stabilization of x Li2MnO3 · (1 -x )LiMO2 Electrode Surfaces (M = Mn, Ni, Co) with Mildly Acidic, Fluorinated Solutions. J. Electrochem. Soc. 2008 , 155 , A269 -A275.	Kang, S. H.; Thackeray, M. M. Stabilization of x Li2MnO3 · (1 -x )LiMO2 Electrode Surfaces (M = Mn, Ni, Co) with Mildly Acidic, Fluorinated Solutions. J. Electrochem. Soc. 2008 , 155 , A269 -A275.	Kang, S. H.; Thackeray, M. M. Stabilization of x Li2MnO3 · (1 -x )LiMO2 Electrode Surfaces (M = Mn, Ni, Co) with Mildly Acidic, Fluorinated Solutions. J. Electrochem. Soc. 2008 , 155 , A269 -A275.
13	24	24	206	#/texts/188	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p13:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 219.0, 240.03, 18.61]	Manthiram, A. Materials Challenges and Opportunities of Lithium Ion Batteries. J. Phys. Chem. Lett. 2011 , 2 , 176 -184.	Manthiram, A. Materials Challenges and Opportunities of Lithium Ion Batteries. J. Phys. Chem. Lett. 2011 , 2 , 176 -184.	Manthiram, A. Materials Challenges and Opportunities of Lithium Ion Batteries. J. Phys. Chem. Lett. 2011 , 2 , 176 -184.	Manthiram, A. Materials Challenges and Opportunities of Lithium Ion Batteries. J. Phys. Chem. Lett. 2011 , 2 , 176 -184.
13	25	25	207	#/texts/189	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p13:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 239.01, 240.02, 38.57]	Croy, J. R.; Kim, D.; Balasubramanian, M.; Gallagher, K.; Kang, S. H.; Thackeray, M. M. Countering the Voltage Decay in High Capacity x Li2MnO3 · (1 -x )LiMO2 Electrodes (M = Mn, Ni, Co) for Li + Ion Batteries. J. Elect…	Croy, J. R.; Kim, D.; Balasubramanian, M.; Gallagher, K.; Kang, S. H.; Thackeray, M. M. Countering the Voltage Decay in High Capacity x Li2MnO3 · (1 -x )LiMO2 Electrodes (M = Mn, Ni, Co) for Li + Ion Batteries. J. Elect…	Croy, J. R.; Kim, D.; Balasubramanian, M.; Gallagher, K.; Kang, S. H.; Thackeray, M. M. Countering the Voltage Decay in High Capacity x Li2MnO3 · (1 -x )LiMO2 Electrodes (M = Mn, Ni, Co) for Li + Ion Batteries. J. Electrochem. Soc. 2012 , 159 , A781 -A790.	Croy, J. R.; Kim, D.; Balasubramanian, M.; Gallagher, K.; Kang, S. H.; Thackeray, M. M. Countering the Voltage Decay in High Capacity x Li2MnO3 · (1 -x )LiMO2 Electrodes (M = Mn, Ni, Co) for Li + Ion Batteries. J. Electrochem. Soc. 2012 , 159 , A781 -A790.
13	26	26	208	#/texts/190	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p13:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 279.03, 240.03, 37.92]	Song, B. H.; Liu, Z. W.; Lai, M. O.; Lu, L. Structural Evolution and the Capacity Fade Mechanism upon Long-Term Cycling in LiRich Cathode Material. Phys. Chem. Chem. Phys. 2012 , 14 , 12875 -12883.	Song, B. H.; Liu, Z. W.; Lai, M. O.; Lu, L. Structural Evolution and the Capacity Fade Mechanism upon Long-Term Cycling in LiRich Cathode Material. Phys. Chem. Chem. Phys. 2012 , 14 , 12875 -12883.	Song, B. H.; Liu, Z. W.; Lai, M. O.; Lu, L. Structural Evolution and the Capacity Fade Mechanism upon Long-Term Cycling in LiRich Cathode Material. Phys. Chem. Chem. Phys. 2012 , 14 , 12875 -12883.	Song, B. H.; Liu, Z. W.; Lai, M. O.; Lu, L. Structural Evolution and the Capacity Fade Mechanism upon Long-Term Cycling in LiRich Cathode Material. Phys. Chem. Chem. Phys. 2012 , 14 , 12875 -12883.
13	27	27	209	#/texts/191	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p13:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 319.0, 240.02, 38.57]	Wu, Y.; Manthiram, A. High Capacity, Surface-Modified Layered Li[Li (1 -x )/3Mn(2 -x )/3Ni x /3Co x /3]O2 Cathodes with Low Irreversible Capacity Loss. Electrochem. Solid-State Lett. 2006 , 9 , A221 -A224.	Wu, Y.; Manthiram, A. High Capacity, Surface-Modified Layered Li[Li (1 -x )/3Mn(2 -x )/3Ni x /3Co x /3]O2 Cathodes with Low Irreversible Capacity Loss. Electrochem. Solid-State Lett. 2006 , 9 , A221 -A224.	Wu, Y.; Manthiram, A. High Capacity, Surface-Modified Layered Li[Li (1 -x )/3Mn(2 -x )/3Ni x /3Co x /3]O2 Cathodes with Low Irreversible Capacity Loss. Electrochem. Solid-State Lett. 2006 , 9 , A221 -A224.	Wu, Y.; Manthiram, A. High Capacity, Surface-Modified Layered Li[Li (1 -x )/3Mn(2 -x )/3Ni x /3Co x /3]O2 Cathodes with Low Irreversible Capacity Loss. Electrochem. Solid-State Lett. 2006 , 9 , A221 -A224.
13	28	28	210	#/texts/192	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p13:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 359.03, 240.03, 48.54]	Shin, D.; Wolverton, C.; Croy, J. R.; Balasubramanian, M.; Kang, S. H.; Rivera, C. M. L.; Thackeray, M. M. First-Principles Calculations, Electrochemical and X-ray Absorption Studies of Li-Ni-PO4 SurfaceTreated x Li2MnO…	Shin, D.; Wolverton, C.; Croy, J. R.; Balasubramanian, M.; Kang, S. H.; Rivera, C. M. L.; Thackeray, M. M. First-Principles Calculations, Electrochemical and X-ray Absorption Studies of Li-Ni-PO4 SurfaceTreated x Li2MnO…	Shin, D.; Wolverton, C.; Croy, J. R.; Balasubramanian, M.; Kang, S. H.; Rivera, C. M. L.; Thackeray, M. M. First-Principles Calculations, Electrochemical and X-ray Absorption Studies of Li-Ni-PO4 SurfaceTreated x Li2MnO3 · (1 -x )LiMO2 (M = Mn, Ni, Co) Electrodes for LiIon Batteries. J. Electrochem. Soc. 2012 , 159 , A121 -A127.	Shin, D.; Wolverton, C.; Croy, J. R.; Balasubramanian, M.; Kang, S. H.; Rivera, C. M. L.; Thackeray, M. M. First-Principles Calculations, Electrochemical and X-ray Absorption Studies of Li-Ni-PO4 SurfaceTreated x Li2MnO3 · (1 -x )LiMO2 (M = Mn, Ni, Co) Electrodes for LiIon Batteries. J. Electrochem. Soc. 2012 , 159 , A121 -A127.
13	29	29	211	#/texts/193	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p13:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 409.03, 240.01, 27.88]	Reed, J.; Ceder, G.; Van der Ven, A. Layered-to-Spinel Phase Transition in Li x MnO2. Electrochem. Solid-State Lett. 2001 , 4 , A78 -A81.	Reed, J.; Ceder, G.; Van der Ven, A. Layered-to-Spinel Phase Transition in Li x MnO2. Electrochem. Solid-State Lett. 2001 , 4 , A78 -A81.	Reed, J.; Ceder, G.; Van der Ven, A. Layered-to-Spinel Phase Transition in Li x MnO2. Electrochem. Solid-State Lett. 2001 , 4 , A78 -A81.	Reed, J.; Ceder, G.; Van der Ven, A. Layered-to-Spinel Phase Transition in Li x MnO2. Electrochem. Solid-State Lett. 2001 , 4 , A78 -A81.
13	30	30	212	#/texts/194	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p13:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 439.02, 240.04, 38.57]	Ito, A.; Li, D. C.; Sato, Y.; Arao, M.; Watanabe, M.; Hatano, M.; Horie, H.; Ohsawa, Y. Cyclic Deterioration and Its Improvement for Li-Rich Layered Cathode Material Li[Ni0.17 Li 0.2 Co0.07Mn0.56]O2. J. Power Sources 20…	Ito, A.; Li, D. C.; Sato, Y.; Arao, M.; Watanabe, M.; Hatano, M.; Horie, H.; Ohsawa, Y. Cyclic Deterioration and Its Improvement for Li-Rich Layered Cathode Material Li[Ni0.17 Li 0.2 Co0.07Mn0.56]O2. J. Power Sources 20…	Ito, A.; Li, D. C.; Sato, Y.; Arao, M.; Watanabe, M.; Hatano, M.; Horie, H.; Ohsawa, Y. Cyclic Deterioration and Its Improvement for Li-Rich Layered Cathode Material Li[Ni0.17 Li 0.2 Co0.07Mn0.56]O2. J. Power Sources 2010 , 195 , 567 -573.	Ito, A.; Li, D. C.; Sato, Y.; Arao, M.; Watanabe, M.; Hatano, M.; Horie, H.; Ohsawa, Y. Cyclic Deterioration and Its Improvement for Li-Rich Layered Cathode Material Li[Ni0.17 Li 0.2 Co0.07Mn0.56]O2. J. Power Sources 2010 , 195 , 567 -573.
13	31	31	213	#/texts/195	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p13:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 478.99, 239.98, 28.59]	Kim, M. G.; Jo, M.; Hong, Y. S.; Cho, J. Template-Free Synthesis of Li[Ni 0.25 Li 0.15Mn0.6]O-2 Nanowires for High Performance Lithium Battery Cathode. Chem. Commun. 2009 , 218 -220.	Kim, M. G.; Jo, M.; Hong, Y. S.; Cho, J. Template-Free Synthesis of Li[Ni 0.25 Li 0.15Mn0.6]O-2 Nanowires for High Performance Lithium Battery Cathode. Chem. Commun. 2009 , 218 -220.	Kim, M. G.; Jo, M.; Hong, Y. S.; Cho, J. Template-Free Synthesis of Li[Ni 0.25 Li 0.15Mn0.6]O-2 Nanowires for High Performance Lithium Battery Cathode. Chem. Commun. 2009 , 218 -220.	Kim, M. G.; Jo, M.; Hong, Y. S.; Cho, J. Template-Free Synthesis of Li[Ni 0.25 Li 0.15Mn0.6]O-2 Nanowires for High Performance Lithium Battery Cathode. Chem. Commun. 2009 , 218 -220.
13	32	32	214	#/texts/196	list_item	reference	False	low	after_back_matter_stop	after_back_matter_stop					after_stop	False	None	page_body	column_2_of_2	2	2	p13:page_body:column_2_of_2:white	[255, 255, 255]	white	False	False	[324.45, 509.04, 240.03, 38.57]	Wei, G. Z.; Lu, X.; Ke, F. S.; Huang, L.; Li, J. T.; Wang, Z. X.; Zhou, Z. Y.; Sun, S. G. Crystal Habit-Tuned Nanoplate Material of Li[Li 1/3 -2 x /3Ni x Mn2/3 -x /3]O2 for High-Rate Performance Lithium-Ion Batteries. A…	Wei, G. Z.; Lu, X.; Ke, F. S.; Huang, L.; Li, J. T.; Wang, Z. X.; Zhou, Z. Y.; Sun, S. G. Crystal Habit-Tuned Nanoplate Material of Li[Li 1/3 -2 x /3Ni x Mn2/3 -x /3]O2 for High-Rate Performance Lithium-Ion Batteries. A…	Wei, G. Z.; Lu, X.; Ke, F. S.; Huang, L.; Li, J. T.; Wang, Z. X.; Zhou, Z. Y.; Sun, S. G. Crystal Habit-Tuned Nanoplate Material of Li[Li 1/3 -2 x /3Ni x Mn2/3 -x /3]O2 for High-Rate Performance Lithium-Ion Batteries. Adv. Mater. 2010 , 22 , 4364 -4367.	Wei, G. Z.; Lu, X.; Ke, F. S.; Huang, L.; Li, J. T.; Wang, Z. X.; Zhou, Z. Y.; Sun, S. G. Crystal Habit-Tuned Nanoplate Material of Li[Li 1/3 -2 x /3Ni x Mn2/3 -x /3]O2 for High-Rate Performance Lithium-Ion Batteries. Adv. Mater. 2010 , 22 , 4364 -4367.
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