journal of mas chemterl ia y trais - pkusz.edu.cn · synthesis of the two polymorphs of lithium...
TRANSCRIPT
This is an Accepted Manuscript, which has been through the Royal Society of Chemistry peer review process and has been accepted for publication.
Accepted Manuscripts are published online shortly after acceptance, before technical editing, formatting and proof reading. Using this free service, authors can make their results available to the community, in citable form, before we publish the edited article. We will replace this Accepted Manuscript with the edited and formatted Advance Article as soon as it is available.
You can find more information about Accepted Manuscripts in the author guidelines.
Please note that technical editing may introduce minor changes to the text and/or graphics, which may alter content. The journal’s standard Terms & Conditions and the ethical guidelines, outlined in our author and reviewer resource centre, still apply. In no event shall the Royal Society of Chemistry be held responsible for any errors or omissions in this Accepted Manuscript or any consequences arising from the use of any information it contains.
Accepted Manuscript
rsc.li/materials-a
Journal of Materials Chemistry AMaterials for energy and sustainabilitywww.rsc.org/MaterialsA
ISSN 2050-7488
Volume 4 Number 1 7 January 2016 Pages 1–330
PAPERKun Chang, Zhaorong Chang et al. Bubble-template-assisted synthesis of hollow fullerene-like MoS
2 nanocages as a lithium ion battery anode material
Journal of Materials Chemistry AMaterials for energy and sustainability
View Article OnlineView Journal
This article can be cited before page numbers have been issued, to do this please use: H. Guo, H. Ping, J.
Hu, X. Song, J. Zheng and F. Pan, J. Mater. Chem. A, 2017, DOI: 10.1039/C7TA03369A.
Journal of Materials Chemistry A
ARTICLE
This journal is © The Royal Society of Chemistry 20xx J. Name., 2013, 00, 1-3 | 1
Please do not adjust margins
Please do not adjust margins
Received 00th January 20xx,
Accepted 00th January 20xx
DOI: 10.1039/x0xx00000x
www.rsc.org/
Controllable synthesis of LiFePO4 in different polymorphs and study of reaction mechanism
Hua Guoa,b,#
, He Pinga,#
, Jiangtao Hua, Xiaohe Song
a, Jiaxin Zheng
a, Feng Pan
a,*
Lithium Iron Phosphate, a widely used cathode material in Lithium Ion Batteries (LIB), crystalizes typically in olivine-type
phase, α-LiFePO4 (aLFP). However, the new phase β-LiFePO4 (bLFP) which can be transformed from aLFP under high
temperature with high pressure, can be produced through simple liquid-phase reaction. The mechanism of controllable
synthesis of the two polymorphs of lithium iron phosphate has not been studied thoroughly. In this paper, with thorough
experiments, we demonstrate that controllable synthesis of LFP with different crystal polymorphs can be obtained by
controlling certain conditions. Phosphate acid ratio in reactants and reaction time play key roles in the controllable
syntheses. Higher phosphate acid ratio and shorter reaction time would result in more bLFP content, while less phosphate
acid and longer reaction time would be beneficial to aLFP formation. To illustrate the mechanism for this phenomenon,
detailed reaction process was researched via X-ray diffraction, from which a possible mechanism associated with evolution
of crystal structures was demonstrated. Solvent content is also important for the process: some water content would lead
to nanoplate-shaped aLFP particles appearing. Their influence on the reaction could be attributed to change of
thermodynamics and kinetics, which leads to different crystal nucleation, growth and phase-change process.
Introduction
Olivine phase Lithium Iron Phosphate1 (LiFePO4, abbreviated
aLFP) has been a quite popular cathode material of Lithium Ion
Batteries (LIB) for its low cost, safety and proper
electrochemical property in ambient environment2, which has
been widely used for large-scale energy storage facilities and
electric vehicles (EV)3. But there are many shortcomings of
aLFP that limits its use in mobile phones, such as low electronic
conductivity and lithium migration efficiency4-9
, which can be
overcome by proper coating10
, ion-doping11
and nano-sizing12-
17. Lithium storage could also be extended by certain
treatment with the formation of certain interface18
.
Manufacture of aLFP is usually conducted in solid-calcine or
carbon-reduction method19
, products aLFP of which are made
in high temperature and suffers from uneven distribution in
size and quality. Nano-sized and well-shaped aLFP particles
could be synthesized by methods in liquid-state, like
hydrothermal or solvothermal method17
. But liquid-state
synthesis methods usually proceed in relatively low
temperature, in which aLFP was made from crystal growth20
.
The crystal growth process was not entirely clear even after
several articles21
exhibit the mechanism of aLFP crystal growth.
It is commonly accepted that hydrated ferrous phosphate
would appear as intermediate because of lower solubility
compared to lithium phosphate in water, which would react
further and produce aLFP with even lower solubility in
hydrothermal condition. While research22
showed a different
intermediate appeared during a reaction starting from ferrous
oxalate in ethanol glycol, which shows similar structure as
aLFP, and changed into aLFP in further reaction, showing
different mechanism of reaction because of reactants and
solvents. On the other hand, it is common acknowledged23
that an amorphous layer forms after hydrothermal or
solvothermal treatment, which shows lower lithium ion
migration efficiency24
compared to aLFP, and decreases during
the process then disappears after calcination, while using
ethanol glycol (EG) as solvent would reduce the crystal defects
efficiently12, 25
.
Beta Lithium Iron Phosphate (abbreviated bLFP) is another
morphology of LFP, in space group of Cmcm, which was found
in 200126
and could only be synthesized with high pressure at
an early stage27
. Liquid synthesis methods in ambient
atmosphere and low temperature of bLFP were reported only
after 201228
, using reactants similar to the ones used for
olivine phase product, with unique solvents as the key for the
controllable synthesis. In some of the research17
about aLFP,
bLFP would appear as an intermediate product during the
reaction, mechanism and influence of which are not
understood properly. Manthiram et al. reported29
the
synthesis of LiMPO4 (M=Mn, Fe, Co and Ni) in the crystal
polymorph of Cmcm, finding out that with proper reaction
condition, bLMP can be synthesized with a facile microwave-
assisted method, which leads to wonder about the key for
controllable synthesis of bLFP and aLFP, which are very
Page 1 of 8 Journal of Materials Chemistry A
Jour
nalo
fMat
eria
lsC
hem
istr
yA
Acc
epte
dM
anus
crip
t
Publ
ishe
d on
08
June
201
7. D
ownl
oade
d by
Uni
vers
ity T
own
Lib
rary
of
Shen
zhen
on
18/0
6/20
17 0
3:32
:56.
View Article OnlineDOI: 10.1039/C7TA03369A
ARTICLE Journal Name
2 | J. Name., 2012, 00, 1-3 This journal is © The Royal Society of Chemistry 20xx
Please do not adjust margins
Please do not adjust margins
important for LFP crystal research and manufacture in large
scale. Considering that product bLFP can be calcined and
changed into aLFP in short time, which can be conducted
during carbon coating and calcination procedure30
, with similar
process time, leading to final products of aLFP with less
defects20, 31
, compared with traditional synthesis procedure.
Research based on the use of bLFP as cathode material of
Lithium-ion has been conducted a lot, mostly focused on the
phase transformation to products in other phases with great
electrochemical properties through calcination32
, or defects
introduction33
. As shown in Figure S1, bLFP particles show little
capacity, which would increase to around 100 mAh/g after
introduced defects or annealed into aLFP, and would further
increase to 160 mAh/g if annealed into aLFP with carbon
coating. More importantly, aLFP with olivine-like structure
shows relatively unstable properties when exposed to air34, 35
,
which makes it difficult for the storage and transportation
under ambient condition (oxygen and humidity would result in
decomposition of aLFP), so usually aLFP should be coated with
thin carbon layer to prevent oxidation or composition
change36
. While bLFP suffers from its low lithium migration
properties37
, making it relatively more difficult to be
delithiated and oxidized (electrochemical properties shown in
Figure S1), which could make the manufacturing process easier
and cheaper, helpful for extent application of the material.
With more and more use of wet-chemical manufacture in
synthesizing LFP, more importance has been drawn into
research about solvothermal synthesis of LFP in different
conditions, which could affect the defects content, particle
morphologies and even crystal polymorphs of products. So it is
very important to study the mechanism and phase evolution
during solvothermal process in LFP synthesis. In this work, LFP
in different crystal polymorphs was synthesized with a facile
solvothermal method, with products controlled by different
aspects. Mechanism of the controllable synthesis was studied,
which would illustrate the process of LFP nucleation and
growth, and find out the key factor for controllable synthesis.
Experimental Methods
Synthesis method of LFP in different morphologies. All
reactants were used as bought without further treatment.
Ferrous sulfate, phosphate acid and lithium hydroxide, in a
ratio of 1: x: 2.7 (x = 1, 1.3, 1.5 and 1.8, products of which
named P1, P1.3, P1.5 and P1.8 respectively), were solute in
ethanol glycol (EG) separately. Ferrous sulfate and phosphate
acid solutions were mixed together first. Then lithium hydrate
solution was added slowly. After continuous stirring for 2 h,
produced gel-like mix was transferred into a Teflon-protected
autoclave inside a sealed stainless steel container and heated
to 180 oC for different time. This whole system was protected
by nitrogen atmosphere. Products were washed by water and
alcohol repeatedly right after cooled to room temperature,
dried in 80 oC vacuum oven overnight
30.
In the experiment of alternative adding sequence, lithium
hydroxide and phosphate acid were add together first, then
ferrous sulfate solution was added into the mixture under
continuous stirring, with other process same as steps
described.
Characterization of product powder. X-ray Diffraction (XRD)
was carried out with a Bruker D8-Advantage powder
diffractometer, of which light source was Cu-Kα radiation.
Scanning Electron Microscopy (SEM, carried out with ZEISS
SURPA 55) was applied to test morphology of the samples.
Differential Scanning Calorimetry (DSC, METTLER TOLEDO) was
applied to test heat flow change during the phase change.
Results and Discussion
Structure and morphology. Lithium Iron Phosphate with
different phases (aLFP and bLFP) was successfully synthesized
by solvothermal method (Figure 1), illustrated by XRD tests.
Particles of aLFP exhibit nanoplate morphology, with size of
about 300×500×30 nm3. The size and morphology are both
uniformly distributed, and every a few particles gathered in
parallelism forming a secondary particle. Particles of bLFP are
in form of nanorods with size of about 20×20×120 nm3,
Page 2 of 8Journal of Materials Chemistry A
Jour
nalo
fMat
eria
lsC
hem
istr
yA
Acc
epte
dM
anus
crip
t
Publ
ishe
d on
08
June
201
7. D
ownl
oade
d by
Uni
vers
ity T
own
Lib
rary
of
Shen
zhen
on
18/0
6/20
17 0
3:32
:56.
View Article OnlineDOI: 10.1039/C7TA03369A
Journal Name ARTICLE
This journal is © The Royal Society of Chemistry 20xx J. Name., 2013, 00, 1-3 | 3
Please do not adjust margins
Please do not adjust margins
hundreds of which gather together end-to-end extending out
from center and form spherical secondary particles with
diameter of about 8 μm, as shown in Figure 1(b, e).
In Figure 1c, XRD result of aLFP is in strict consist of standard
sample result (PDF#40-1499) with no other peaks, meaning
that the acquired material is pure aLFP with no impurity. Same
for bLFP in accord with calculated peaks position from the
structure32
. Through detailed refinement with TOPAS software,
size distribution and crystal lattice parameters of statistic
results (as shown in Table S1) are similar with SEM results and
standard samples.
Influence of acid ratio. In the controllable synthesis process,
in order to obtain products with different polymorphs, acid
ratio in reactants was adjusted. When adjusting phosphate
acid ratio n (mole ratio of phosphate acid to ferrous ion being
n, with lithium hydroxide ratio being 2.7) increased from 1.0 to
2.0 (with pH adjusting from near neutral to lower), gathered
experiment product named Pn, and products changed from
aLFP to bLFP gradually, as shown in XRD results in Figure 2a. As
shown in Figure 2(b-e) respectively, shape of produced
particles changed from nanoparticles to nanorods for sample
P1.3, then to mixing of nanorods and smaller nanoparticles for
sample P1.5, finally becoming spheres consisting of nanorods
attaching to each other in P1.8. It is obvious combined with
XRD results that aLFP particles are in shape of nanoparticles
and then nanorods, while bLFP particles are in shape of
nanorods gathering into spheres, which can be explained by
mechanism of oriented attachment38
.
Influence of reaction time. Whereas in P1.8 experiment, it is
clearly shown that products changed from bLFP to aLFP when
solvothermal reaction time increased. Some content (18.7,
30.8, 60.1 and 81.5 %) of aLFP was obtained for different
reaction time (3, 7, 12 and 21 days respectively), as shown in
Figure 3a. It was obvious that aLFP content increased nearly
linearly to reaction time, as shown in Figure 3b, which was in
accordance with reaction course. The reason bLFP turned into
aLFP was that aLFP was more thermodynamically stable in the
condition, which was illustrated by former reports24
. From
some of the mixed production, morphology of certain particles
(Figure S2) showed strange combination of aLFP and bLFP
particles staggered, illustrating that aLFP was obtained by
dissolving of bLFP and recrystallizing into aLFP, as explained by
some similar papers21
. To further illustrate the argument, a
thermal test was carried (as shown in Figure S3), showing that
only from temperature of about 600 oC can bLFP be
transferred into aLFP under calcination condition, and DSC test
result showed that about 30 J/g of heat was released from the
system during the phase change. Calculation result of reaction
rate observed was much lower than calculated from Gibbs free
energy for same change in 180 oC - proves that direct phase
change from bLFP to aLFP was not the true process for the
reaction, and only dissolution-recrystallization process can
explain such low reaction rate under the
hydrothermal/solvothermal condition39
. (Detailed calculation
was shown in Supplementary Information S1.)
Mechanism for Controllable Synthesis. To illustrate the
mechanism behind different products in different acid ratio,
more detailed tests were conducted to verify the product
structure change during heating process in different
temperature for P1.3 and P1.5 experiments. It is obvious that
during initial crystallization state (around 100 oC), both aLFP
and bLFP nucleation were formed. But when heated to higher
temperature, XRD peaks of aLFP increase and peaks of bLFP
decrease, as labeled in Figure 3(c-d). P1.5 productions are pure
aLFP for 140 oC or 180
oC (different from previous
solvothermal product of aLFP and bLFP mixing, which could be
resulted from the slight difference in heat proved by Figure
S4). In order to make sure the crystal formation temperature
for products of different phases, detailed synthesis process
was tested. As shown in Figure S5, the obtained material was
first crystalized in form of bLFP in about 100 oC, and continued
crystallization process when the temperature was maintained,
illustrated by peaks heightening and sharpening shown in
Figure S5a. When system was heated to 180 oC, almost all
Figure 2. (a) XRD results for products with different phosphate acid ratio (ranging from 1.0 to 2.0), and SEM images showing different particle morphology produced by
different reactant ratio: phosphate acid ratios x is (b) 1, (c) 1.3, (d) 1.5 and (e) 1.8.
Page 3 of 8 Journal of Materials Chemistry A
Jour
nalo
fMat
eria
lsC
hem
istr
yA
Acc
epte
dM
anus
crip
t
Publ
ishe
d on
08
June
201
7. D
ownl
oade
d by
Uni
vers
ity T
own
Lib
rary
of
Shen
zhen
on
18/0
6/20
17 0
3:32
:56.
View Article OnlineDOI: 10.1039/C7TA03369A
ARTICLE Journal Name
4 | J. Name., 2012, 00, 1-3 This journal is © The Royal Society of Chemistry 20xx
Please do not adjust margins
Please do not adjust margins
product was pure aLFP, and remains after heating for 6 h as
shown in Figure S5b, illustrating that aLFP is a very stable form
under the condition.
To explain the reason that bLFP can only be formed in lower
pH environment, reaction mechanism of synthesis process
must be taken into account. First ferrous sulfate was mixed
with phosphate acid, which was source of acid atmosphere.
Then lithium hydroxide was added drop by drop into the
system, reacting with phosphate acid and turning the system
from acid to neutral atmosphere. The original ratio of ferrous
sulfate, phosphate acid and lithium hydroxide was 1: n: 2.7,
produced lithium phosphate precipitating which reacts with
iron immediately and forms amorphous intermediate, and it
has been certificated by experiments. When increasing
phosphate acid ratio, some of the intermediate product
changes from lithium phosphate (Li3PO4) to acidic phosphate
ion (H2PO4-), which was soluble in ethanol glycol, showing less
precipitation being gathered.
In order to explain the mechanism of different product’s
phases in different condition when first crystalized, structures
of lithium phosphate was compared with aLFP shown in Figure
S6 and Table S3. It is clearly shown that some similarity in
space group and similar lattice parameters lies behind the
controllable synthesis. The structure of lithium phosphate is
very similar to the one of aLFP, making the transforming
process more likely through an amorphous phase in which
lithium and ferrous ion co-precipitating with phosphate anion.
While in a system with more phosphate acid and thus lower
pH, the lithium and ferrous ion would dissolve into the ethanol
glycol solvent, instead of precipitating. Dissolved dihydrogen
phosphate and ferrous ion would form a certain structure with
lithium ion, making it easier to form bLFP when crystalized. In
order to prove the assumption, an additional experiment was
carried out, in which the system was heated before lithium
hydroxide was added. It turned out that crystallized
Fe7H4(PO4)6 appeared from the heating (XRD result shown in
Fig. S7), which can react with LiOH later and form bLFP, the
morphology of which in Fig. S8 clearly showed that LiOH from
solution reacted with Fe7H4(PO4)6 bulk particles in micrometer
size and became nano particles gathering together. The
similarity in these two crystal structures lies in form of
combination of Fe-O octahedral: Fe-O octahedral in both
crystal structure linked with each other with a shared edge,
which offers us the conclusion that ferrous oxygen octahedral
would be linked to other through shared edges in the solvent
environment. Thus in heating process, Lithium Phosphate
resulted from higher pH reacting with ferrous solution would
form aLFP preferentially, and in lower pH ferrous hydrogen
phosphate would form seed crystal of bLFP. Then after the first
crystallization, crystal growth and phase change would happen
Figure 3. XRD results of (a) P1.8 in different reaction states, with (b) content analysis. And detailed reaction process (crystallization process) monitor with
XRD for reactions (c) P1.3 and (d) P1.5.
Page 4 of 8Journal of Materials Chemistry A
Jour
nalo
fMat
eria
lsC
hem
istr
yA
Acc
epte
dM
anus
crip
t
Publ
ishe
d on
08
June
201
7. D
ownl
oade
d by
Uni
vers
ity T
own
Lib
rary
of
Shen
zhen
on
18/0
6/20
17 0
3:32
:56.
View Article OnlineDOI: 10.1039/C7TA03369A
Journal Name ARTICLE
This journal is © The Royal Society of Chemistry 20xx J. Name., 2013, 00, 1-3 | 5
Please do not adjust margins
Please do not adjust margins
at the same time, with aLFP remaining and bLFP changing into
aLFP gradually. To further prove the assumption, experiments
with different adding sequence of raw materials were carried:
Lithium hydroxyl and phosphate acid were mixed first,
followed by adding ferrous sulfate drop by drop. It turns out
that similar phenomenon appeared in the system. With
phosphate acid ratio below 2.7, experiment were confirmed to
be aLFP, from relatively more-precipitation-existing precursor.
As shown in Fig. S8, bLFP only can form in a system with more
phosphate acid ratio of 2.7, which showed less precipitation
existing. More importantly, a combination of aLFP and bLFP
was produced from the experiment with phosphate acid ratio
of 2.7, which means that ratio of lithium hydroxyl and
phosphate acid ratio was 1:1, forming H2PO4- instead of PO4
3-
(Li3PO4), resulting in less precipitation in the precursor, and
proved the mechanism illustrated above. In normal adding
sequence, ferric ion could react with phosphate ion before
adding of lithium and heating, while in the new experiment,
phosphate would have to react with lithium hydroxyl first, only
phosphate left able to react with ferric ion to form
intermediate phase and produce bLFP finally.
Solvent effects in the synthesis. To illustrate the effects of
solvents (ethanol glycol) in the reaction, water of different
content was added into the reaction system (P1.8). When
ethanol glycol was used as reaction solvent, bLFP was gathered
as production. When adding certain ratio of water (adjusting
from 0% to 10%) into the reaction system, some content of
aLFP was produced, with content increasing from 0 to 100%,
shown as Figure 4(a-b) and Table S4. Combined with previous
analyze, water content has a significant influence towards the
nucleating and growth of crystals. When water complexing on
the surface of crystal or precursor, the stable energy would be
Figure 4. (a) XRD results for products with different phosphate acid ratio (ranging from 1.0 to 2.0), and SEM images showing different particle morphology produced by
different reactant ratio: phosphate acid ratios x is (b) 1, (c) 1.3, (d) 1.5 and (e) 1.8.
Page 5 of 8 Journal of Materials Chemistry A
Jour
nalo
fMat
eria
lsC
hem
istr
yA
Acc
epte
dM
anus
crip
t
Publ
ishe
d on
08
June
201
7. D
ownl
oade
d by
Uni
vers
ity T
own
Lib
rary
of
Shen
zhen
on
18/0
6/20
17 0
3:32
:56.
View Article OnlineDOI: 10.1039/C7TA03369A
ARTICLE Journal Name
6 | J. Name., 2012, 00, 1-3 This journal is © The Royal Society of Chemistry 20xx
Please do not adjust margins
Please do not adjust margins
totally different from ethanol glycol environment, thus
resulting in different reaction process, and materials with
different polymorphs. As reported in previous paper40
, H2O
would complex on the surface of precursor with ethanol glycol,
forming a unique morphology of nanoplate with thickness of
only 1 or 2 crystal lattices as illustrated by Figure S7, which
probably results in products’ morphology of nanoplates (Figure
4). In order to prove the universality of the phenomenon,
similar experiments were carried out in experiment P1.5. A
reasonable hypothesis based on previous analyze is that water
content in solvent would lead to precipitation of Li3PO4, caused
by relatively smaller the solubility in water than in ethanol
glycol.
The controllable synthesis was actually based on adjusting
crystal nucleating, growth and phase-change, by adjusting
reactants, adding sequence, solvents and reaction time, which
could be explained by formation of certain intermediate
product.
Conclusions
In conclusion, bLFP can be obtained by controllable
synthesized, and the mechanism behind the phenomena was
illustrated by analyzation of reaction condition. To control the
polymorphs of produced lithium iron phosphate, acid ratio in
reactants and reaction time should be controlled strictly,
mechanism of which was controlling the crystal nucleation,
growth and phase-change process. Relatively less phosphate
acid, longer reaction time or some water content in solvent
would lead to precipitation of Li3PO4, which could lead to
production of aLFP, otherwise bLFP would be produced. This
paper showing the key parameters in manufacturing lithium
iron phosphate, combining with the application of lithium iron
phosphate as electrode of lithium ion batteries, would lead to
some great development of commercial manufacture of
electrode materials.
Acknowledgements
This work was financially supported by National Materials
Genome Project (2016YFB0700600), the National Natural Science
Foundation of China (No. 21603007 and 51672012), and Shenzhen
Science and Technology Research Grant (No.
JCYJ20150729111733470, JCYJ20151015162256516).
Notes and references
1. A. K. Padhi, J. Electrochem. Soc., 1997, 144, 1188.
2. Y. Wang, P. He and H. Zhou, Energy Environ. Sci., 2011, 4, 805-817.
3. L. X. Yuan, Z. H. Wang, W. X. Zhang, X. L. Hu, J. T. Chen, Y. H. Huang and J. B.
Goodenough, Energy Environ. Sci., 2011, 4, 269-284.
Illustrate 1. Mechanism for controllable solvothermal synthesis of LFP in different polymorphs.
Page 6 of 8Journal of Materials Chemistry A
Jour
nalo
fMat
eria
lsC
hem
istr
yA
Acc
epte
dM
anus
crip
t
Publ
ishe
d on
08
June
201
7. D
ownl
oade
d by
Uni
vers
ity T
own
Lib
rary
of
Shen
zhen
on
18/0
6/20
17 0
3:32
:56.
View Article OnlineDOI: 10.1039/C7TA03369A
Journal Name ARTICLE
This journal is © The Royal Society of Chemistry 20xx J. Name., 2013, 00, 1-3 | 7
Please do not adjust margins
Please do not adjust margins
4. G. K. P. Dathar, D. Sheppard, K. J. Stevenson and G. Henkelman, Chem. Mater.,
2011, 23, 4032-4037.
5. T. Sasaki, Y. Ukyo and P. Novák, Nat. Mater., 2013, 12, 569-575.
6. F. Zhou, C. A. Marianetti, M. Cococcioni, D. Morgan and G. Ceder, Phys. Rev. B,
2004, 69.
7. C. T. Love, A. Korovina, C. J. Patridge, K. E. Swider-Lyons, M. E. Twigg and D. E.
Ramaker, J. Electrochem. Soc., 2013, 160, A3153-A3161.
8. R. Malik, A. Abdellahi and G. Ceder, J. Electrochem. Soc., 2013, 160, A3179-A3197.
9. S.-i. Nishimura, G. Kobayashi, K. Ohoyama, R. Kanno, M. Yashima and A. Yamada,
Nat. Mater., 2008, 7, 707-711.
10. J. J. Wang and X. L. Sun, Energy Environ. Sci., 2012, 5, 5163-5185.
11. P. S. Herle, B. Ellis, N. Coombs and L. F. Nazar, Nat. Mater., 2004, 3, 147-152.
12. X. Rui, X. Zhao, Z. Lu, H. Tan, D. Sim, H. H. Hng, R. Yazami, T. M. Lim and Q. Yan,
ACS Nano, 2013, 7, 5637-5646.
13. R. Malik, D. Burch, M. Bazant and G. Ceder, Nano Lett., 2010, 10, 4123-4127.
14. M.-S. Song, Y.-M. Kang, Y.-I. Kim, K.-S. Park and H.-S. Kwon, Inorg. Chem., 2009, 48,
8271-8275.
15. H. Liu, F. C. Strobridge, O. J. Borkiewicz, K. M. Wiaderek, K. W. Chapman, P. J.
Chupas and C. P. Grey, Science, 2014, 344, 1252817-1252817.
16. D. B. Ravnsbæk, K. Xiang, W. Xing, O. J. Borkiewicz, K. M. Wiaderek, P. Gionet, K.
W. Chapman, P. J. Chupas and Y. M. Chiang, Nano Lett., 2014, 14, 1484-1491.
17. Y. Zhao, L. Peng, B. Liu and G. Yu, Nano Lett., 2014, 14, 2849-2853.
18. H. Guo, X. H. Song, J. X. Zheng and F. Pan, Funct. Mater. Lett., 2016, 9, 5.
19. C. Masquelier and L. Croguennec, Chem. Rev., 2013, 113, 6552-6591.
20. K. M. Ø. Jensen, M. Christensen, H. P. Gunnlaugsson, N. Lock, E. D. Bøjesen, T.
Proffen and B. B. Iversen, Chem. Mater., 2013, 25, 2282-2290.
21. B. Ellis, W. H. Kan, W. R. M. Makahnouk and L. F. Nazar, J. Mater. Chem., 2007, 17,
3248.
22. J. Bai, J. Hong, H. Chen, J. Graetz and F. Wang, J. Phys. Chem. C, 2015, DOI:
10.1021/jp508600u, 150123095009006.
23. K. Dokko, K. Shiraishi and K. Kanamura, J. Electrochem. Soc., 2005, 152, A2199-
A2202.
24. G. Zeng, R. Caputo, D. Carriazo, L. Luo and M. Niederberger, Chem. Mater., 2013,
25, 3399-3407.
25. K. J. Kreder, G. Assat and A. Manthiram, Chem. Mater., 2015, 27, 5543-5549.
26. O. García-Moreno, M. Alvarez-Vega, J. García-Jaca, J. M. Gallardo-Amores, M. L.
Sanjuán and U. Amador, Chem. Mater., 2001, 13, 1570-1576.
27. U. Amador, J. M. Gallardo-Amores, G. Heymann, H. Huppertz, E. Morán and M. E.
Arroyo y de Dompablo, Solid State Sci., 2009, 11, 343-348.
28. B. Voß, J. Nordmann, A. Kockmann, J. Piezonka, M. Haase, D. H. Taffa and L.
Walder, Chemistry of Materials, 2012, 24, 633-635.
29. G. Assat and A. Manthiram, Inorg. Chem., 2015, 54, 10015-10022.
30. L. Wang, X. He, W. Sun, J. Wang, Y. Li and S. Fan, Nano Letters, 2012, 12, 5632-
5636.
31. K.-Y. Park, I. Park, H. Kim, H.-d. Lim, J. Hong, J. Kim and K. Kang, Chem. Mater.,
2014, 26, 5345-5351.
32. C. Y. Wu, W. Huang, L. F. Liu, H. Wang, Y. W. Zeng, J. Xie, C. H. Jin and Z. Zhang,
Crystengcomm, 2016, 18, 7707-7714.
33. H. Guo, X. H. Song, Z. Q. Zhuo, J. T. Hu, T. C. Liu, Y. D. Duan, J. X. Zheng, Z. H. Chen,
W. L. Yang, K. Amine and F. Pan, Nano Lett., 2016, 16, 601-608.
34. W. Porcher, P. Moreau, B. Lestriez, S. Jouanneau, F. Le Cras and D. Guyomard,
Ionics, 2008, 14, 583-587.
35. J.-F. Martin, M. Cuisinier, N. Dupré, A. Yamada, R. Kanno and D. Guyomard, J.
Power Sources, 2011, 196, 2155-2163.
36. M. Cuisinier, N. Dupré, P. Moreau and D. Guyomard, J. Power Sources, 2013, 243,
682-690.
37. T. E. Ashton, J. V. Laveda, D. A. MacLaren, P. J. Baker, A. Porch, M. O. Jones and S.
A. Corr, J. Mater. Chem. A, 2014, 2, 6238.
38. K. S. Cho, D. V. Talapin, W. Gaschler and C. B. Murray, J. Am. Chem. Soc., 2005,
127, 7140-7147.
39. L. Zhou, W. Z. Wang, L. Zhang, H. L. Xu and W. Zhu, J. Phys. Chem. C, 2007, 111,
13659-13664.
40. T. C. Liu, Y. C. Feng, Y. D. Duan, S. H. Cui, L. P. Lin, J. T. Hu, H. Guo, Z. Q. Zhuo, J. X.
Zheng, Y. Lin, W. L. Yang, K. Amine and F. Pan, Nano Energy, 2015, 18, 187-195.
Page 7 of 8 Journal of Materials Chemistry A
Jour
nalo
fMat
eria
lsC
hem
istr
yA
Acc
epte
dM
anus
crip
t
Publ
ishe
d on
08
June
201
7. D
ownl
oade
d by
Uni
vers
ity T
own
Lib
rary
of
Shen
zhen
on
18/0
6/20
17 0
3:32
:56.
View Article OnlineDOI: 10.1039/C7TA03369A
Table of Contents
Controllable synthesis of LiFePO4 with different crystal polymorphs can be obtained by
controlling certain conditions.
Page 8 of 8Journal of Materials Chemistry A
Jour
nalo
fMat
eria
lsC
hem
istr
yA
Acc
epte
dM
anus
crip
t
Publ
ishe
d on
08
June
201
7. D
ownl
oade
d by
Uni
vers
ity T
own
Lib
rary
of
Shen
zhen
on
18/0
6/20
17 0
3:32
:56.
View Article OnlineDOI: 10.1039/C7TA03369A