OATAO is an open access repository that collects the work of Toulouse
researchers and makes it freely available over the web where possible
Any correspondence concerning this service should be sent
to the repository administrator:
tech-oatao@listes-diff.inp-toulouse.fr
This is an author’s version published in:
http://oatao.univ-toulouse.fr/27622
To cite this version:
Xu, Baolin and Qi, Shihan and Jin, Mengmeng [et al.]. 2020 roadmap on
two-dimensional materials for energy storage and conversion. (2019) Chinese
Chemical Letters, 30 (12). 2053-2064. ISSN 1001-8417
2020 roadmap on two-dimensional materials for energy storage
and conversion
Baolin Xua, Shihan Qia, Mengmeng Jinb, Xiaoyi Caic, Linfei Laib,c,**, Zhouting Sund, Xiaogang Hand ,*, Zifeng Line,*, Hui Shaof,g,***, Peng Pengh, Zhonghua Xiangh,*, Johan E. ten ElshofÏ·*, Rou Tanj, Chen Liuj, Zhaoxi Zhang\ Xiaochuan Duani·*, Jianmin Maa,k,****
asd!ool of Physics and Electronics, Hunan University, Otangsha 410082, China
b Key Laboratory of Flexible Elearonics & lnstitute of Advanœd Materials (1AM), Jiangsu National Synergistic Innovation Center for Advanced Materials (SICAM), Nanjing Tech University, Nanjing 210009, China
cSchool of Physical and Mathematical Sciences, Nanyang Technological University, Singapore 637371, Singapore dState Key Lab of Elearirol Insu lation and Power Equipment, Xi'an Jiaotong University, Xi'an 710049, China e College of Materials Science and Engineering. Sichuan University, Otengdu 610065, China
f Université Paul Sabatier, Laboratoire OR/MAT UMR CNRS 5085, Toulouse 31062, Franœ g Réseau sur le Stockage Elearodlimique de /'Energie (RS2E), CNRS 3459, Amiens, Fmnœ
h State Key Laboratory of Organic-lnorganic C omposites, Beijing University of Otemical Ted!nology, Beijing 100029, Otina 1 University of Twente, AE Enschede 7500, the Netherlands
J Pen-Tung Sah lnstitute of Micro-Nana Scienœ and Technology, Xiamen University, Xiamen 361005, China
k Key Laboratory of Materials Processing and Mold (Zhengzhou University), Ministry of Education, Zhengzhou University, Zhengzhou 450002, China
A RTI CLE I NFO
Keywords: Graphene Black phosphorus
MXenes
Covalent organic frameworks Oxides Chalcogenides Metal-air batteries Metal-sulfur batteries Metal-ion batteries Electrochemical capacitors • Corresponding authors. AB STR ACT
Energy storage and conversion have attained significant interest owing to its important applications that
reduce COi emission through employing green energy. Sorne promising technologies are included metal air batteries, metal sulfur batteries, metal ion batteries, electrochemical capacitors, etc. Here, metal
elements are involved with lithium, sodium, and magnesium For these devices, electrode materials are
of importance to obtain high performance. Two dimensional (2D) materials are a large kind of layered
structured materials with promising future as energy storage materials, which include graphene, black
phosporus, MXenes, covalent organic frameworks ( COFs ), 2D oxides, 2D chalcogenides, and others. Great
progress has been achieved to go ahead for 2D materials in energy storage and conversion. More
researchers willjoin in this research field. Under the background, it has motivated us to contribute with a
roadmap on 'two dimensional materials for energy storage and conversion.
© 2019 Chinese Chemical Society and Institute ofMateria Medica, Chinese Academy ofMedical Sciences.
1. Graphene and graphene-composites for energy storage applications
•• Corresponding author at Key Laboratory of Flexible Electronics & lnstitute of Advanced Materials (1AM}, Jiangsu National Synergistic Innovation Center for Advanced Materials (SICAM}, Nanjing Tech University, Nanjing 2 10009, China.
Mengmeng Jin, Xiaoyi Cai, Linfei Lai**
1.1. Status••• Corresponding author at: Université Paul Sabatier, Laboratoire CIRJMAT UMR CNRS 5085, Toulouse 31062, France.
•••• Corresponding author at: School of Pbysics and Electronics, Hunan University, Changsha 410082, China.
E-mai l addresses: iamlflai@njtech.edu.cn (L. Lai} xiaogang.han@xjtu.edu.cn
(X Han}, linzifeng@scu.edu.cn (Z. Lin}, shao@chimie-ups-tlse.fr (H. Shao },
xiangzh@mail.buct.edu.cn (Z. Xiang}, j.e.tenelshof@utwente.nl O .E. ten Elshof),
xcduan@xmu.edu.cn (X. Duan}, nanoelechem@hnu.edu.cn
u.
Ma).Graphene is a one atom thick two dimensional sheet corn
posed of sp
2bonded carbon atoms that are densely packed in a
honeycomb crystal lattice. The 2D planar structure of single
layer graphene ensures high utilization of carbon atoms for the
electron transfer, high surface area, and tlexibility. Graphene and
https: / /doi.org/ 10.1016/j.cclet.2019.10.028graphene based composites have been demonstrated to have
enhancedperformanceinvariousenergystorageandconversion
systems (Fig. 1), such as Li/Na ion batteries, supercapacitors,
electrocatalysis,Li Sbatteries.
1.2.Currentandfuturechallenges
1.2.1.Li/Na ionbatteries
Asexcellent2Dcarbonmaterials,thehybridizationofgraphene
withelectroactivematerialsforbothcathodeandanodeofLi/Na
ionbatterieshavebeenvastlyreported,andsignificantlyimproved
capacity,rateperformanceandcyclabilityhavebeenachieved[1].
Theultrathingraphenecanformastableconductingnetworkwith
low percolation threshold and enhanced the electrochemical
performanceofelectrodewitheventraceamountandisregarded
asapromisingconductiveadditiveforbothcathodeandanodein
Li ionbatteries.Forexample,0.2at%graphenewith1%superP(SP)
wasreportedtohavebetterelectrodeconductivitywithmicrom
eter sizedLiCoO2than3wt%ofSP[2].Grapheneasanodehasa
theoreticalcapacityoftwicethatofgraphite.However,mostofthe
capacityofgraphenemaybecontributedbytheadsorptionofLi+
on edges, defects, and pores, together with the fast surface
reactionsongraphene,which maynot bebeneficialfor battery
applicationsincetheycanleadtoalargeirreversiblecapacityloss
initially.All graphene basedelectrodeshavehighcapacity,high
rate,andlongcyclelife,however,thecapacitylossintheinitial
cycleis commonlyover50%,makingthemimpracticalin Li ion
batteryfullcells.The2Dfeatureofgraphenemakesitanexcellent
candidateas a protectivecoating layerof Alfoil torestrictthe
electrolytecorrosion during high rate cycling. The coating also
enhances the adhesion of electroactive materials with current
collector and assists in electron transportation. The excellent
mechanicalpropertiesofgraphenemakeitapplicabletoprepare
free standingelectrodeseitherwithorwithoutcompositingwith
otherelectroactivematerials.
1.2.2.Supercapacitors
Supercapacitorsareahighlypromisingclassofenergystorage
devices due to their high power density and long life cycle.
Supercapacitorscanbebroadlyclassifiedintotwotypesbasedon
thedifferentmechanismsofenergystorage:electricdoublelayer
capacitors(EDLCs)andpseudocapacitors.Thespecificcapacitance
ofEDLCsisdeterminedbysurfacearea,porestructureandpore
sizedistribution ofcarbonaceous materials.Graphenestructure
modulationbyKOHactivationtogeneratemicroporesorin plane
poreopeningofgraphenebytemplate directedetchingtocreate
holey graphene with pore size from a few to hundreds of
nanometers are highly desirable for not only supercapacitors
but also batteries and electrocatalysis. As the energy storage
mechanismofpseudocapacitorsreliesonthefastandreversible
Faradaicredoxreactionsintheinterfacebetweenelectrolyteand
electrode, grapheneis usually combined withpseudocapacitive
materials,suchas transitionmetaloxides/sulphides/hydroxides,
conductingpolymers,etc.Comparedwithothertypesofcarbon,
suchasactivatedcarbonnanoparticles,rGOandGOfabricatedvia
wetchemicalmethodshavethehighaccessiblesurfaceareaand
variety of surface functional groups for efficient loading of
pseudocapacitive materials. The graphene composites based
supercapacitive materials generally show excellent capacitance
whichincludestheredoxchargeprovidedbypseudocapacitancein
additiontotheEDLCchargeprovidedbyhighsurfacearearGO.The
surface functional groups of graphene contribute capacitance
valueundercharge accumulation,therationalsurfacemodified
graphenecanchargeanddischargefastandresultinasignificant
increaseinpseudocapacitance.
1.2.3.Electrocatalysis
Typical energy conversion devices, i.e., metal air batteries
and fuel cell rely on the efficiency of oxygen reduction (ORR)
and evolution reaction (OER), while electrolysis involves
hydrogenevolutionand OER.Holeygraphenewithin planpore
size in meso/macro pore range could further facilitate mass
diffusion of reactants. Graphene based materials can induce
favorablecatalyst supportinteractionandactivityenhancements
forpreciousmetalcatalysts nanoparticles,thereby,leadingtoa
reduced loading mass, thus saving cost. Graphene with heter
oatomsdopingorcompositingwithothernanostructuredcarbon
arealsoeffectivestrategiestoachieveexcellentcatalyticperfor
mance. As planar ultrathin 2D carbon materials with tunable
surfacechemistryandhighconductivity,italsoaffordsastrong
backbonetoearth abundantmetalbasednanoparticlestomini
mize the agglomerations of these nonprecious metal catalyst
and enhance the stability [3]. Free standing graphene and
graphene composites as catalysts, gas diffusion, and current
collector integrated air electrodes are promising for energy
conversion devices. The pore volume density, pore diameter,
and thenumber of defectsin the graphenenanoplateletshave
critical effects on the electrochemical performance of these
devices.Forexample,althoughZn airbatteriesandLi O2batteries
havedifferentreactionmechanismstowardOER,thebi/trimodal
porous graphene are reported to effectively accommodate
intermediate products and facilitate the electrolyte and ions
diffusion. Graphene show superior performance not only in
fundamental electrocatalysis measurement but also in some
energyconversiondevicesdue totherationalizedstructureand
composition. N doped graphene has a slightly lower kinetic
activityin fast forced convectiveelectrolyte but a much larger
rate capability(nearly 1.5 timesof powerdensity)inquiescent
electrolytethanthat ofcommercial20%Pt/CcatalystforZn air
batteries[4].
1.2.4.Li Sbatteries
Li S batteries are promising alternative for next generation
energy storage system due to the preferred high theoretical
capacities of Li (3861mAh/g) and sulfur (1675mAh/g) [5].
Heteroatoms doped graphene or compositing with selected
transition metals/carbon nanomaterials may lead to a strong
bindingstrengthwithpolysulfidewhichcanbetterrestricttheloss
ofsulfurduringcyclingandensureshighsulfurloading.Graphene
has been applied as a sulfur wrapping substrate to restrict
polysulfideshuttling. Graphenethin layercoating eitheronthe
membrane or cathode side efficiently barrier the diffusion of
polysulfides.
1.2.5.Solarcells
Graphenehasshowngreatpotentialintransparentelectrodes
forsolarcells.Ultrathin andflexiblesolarcells canbeachieved
withgraphene’sgoodconductivity,transparency,andmechanical
strength.Currentresearchmainlyfocusesonfunctionalizationand
doping to improve the efficiency of graphene containing solar
cells.
1.3.Advancesinscienceandtechnologytomeetchallenges
Among the mass production of graphene in mechanical
exfoliationmethods includingballmilling,ultrasonication,fluid
dynamics,supercriticalfluids,etc.,supercriticalfluidsmethodhas
shown advantages in terms of high yield and environmental
friendliness.However,howtoimprovetheyieldofmono/fewlayer
grapheneandenhanceexfoliationefficiencyremainsahottopic
[6,7]. Theprelithiationofgraphene basedLielectrodestooffset
theirlow initialcycleefficiencyhavebeenexplored,yetnotbeen
developedforindustrialproduction.Athigherconcentrationsover
5 10mg/mL,thechemicallyreducedgrapheneslurryturnsviscous
for processing, and its high porosity makes the electroactive
materialseasily detachfrom thecurrent collectorunless more
insulatingbinder isapplied.Therestackingofgrapheneleadsto
lowcross planediffusivityofLiorNaionsstericeffectresultin
increasedpolarizationathighcharge/dischargeratesfornanosized
electrodematerials.Structuremodulationbyetchingtogenerate
in planeholes, orusingunconventional dryingprocess,suchas
spraydrying,freezedryingareeffectivetorestricttherestacking.
Thelowdensityandporousstructureofgraphenecouldlowerthe
volumetricpowerandenergydensitiesofenergystoragedevices,
theinterfacialmodulationofgrapheneandelectroactivematerials
need to be explored. The residual of O containing functional
groups ofgrapheneand theiradsorbedwatermayleadtohigh
leakage current and gas evolution for EDLC type nonaquoues
supercapacitors [8]. Recent research has developed plenty of
graphene basedhigh performancecatalystbutstillfailtoreplace
the noble metal based catalysts. Therefore, rational control of
synthesisconditioniscriticaltoachievenotonlyreasonablehigh
capacitancevaluebutalsoultralongdurationcyclelife.Moreover,
most of the OERand ORR electrocatalysts function only under
alkaline conditions [9], graphene based catalyst for all pH
electrocatalysts are highly desirable. The catalytic mechanisms
for some of the catalysts are well known, but the synergistic
mechanismbetweencatalystsandgraphenesubstratearestillnot
fully understandable. Despite the excellentbarrier effect of 2D
graphene,thelowdensityandhighsurfaceareaofgraphenelimit
thearealloadingofsulfurandbringchallengestotheelectrolyte
control.Itisalsoworthtonotethatwhenprocessedintoelectrode
films via various methods, graphene layers tend to stack and
aggregate inhibiting electrolyte access. The packing density of
grapheneelectrodepreparedinconventionalwetcastingproce
dureislow,andnewprocessingtechnology,suchasspraydrying,
in situ sintering, vacuum filtration. The residual O containing
functionalgroupsonthelong durationcyclabilityofbatteriesneed
toberevisitedastheundefinedfunctionalgroupscouldaffectthe
agingproperties.Therefore,adjustmentofgrapheneporestructure
and surface chemistry to construct a fast ion and electron
conductingnetworkifofhighsignificance.
1.4.Concludingremarksandprospects
Graphenehasthepotentialtogreatlyenhancemanyofcurrent
energyapplications.However,thecurrentlyavailablegraphenecan
possess variousproperties,suchasporosity,purityandamount
and typeof dopants,whichneedstobeclearly investigatedfor
eachapplication.Manyofgraphene’sproblemsintheapplication
come from their porosity and low density. Development of
methods toimprovegrapheneelectrode’s densityandcolumbic
efficiencyonthefirstcyclewillgreatlyimprovetheapplicationof
grapheneinenergydevices.
2.Blackphosphorousforenergystorage
ZhoutingSun,XiaogangHan*
2.1.Status
A 2D material black phosphorous (BP) is one of the most
promisingmaterialforenergystoragearea:(1)Itsintrinsicbad
gap(0.34eV),reasonabledensity(2.69g/cm3)andhightheoreti
cal capacity (2596mAh/g for lithium ion batteries) are also
advantageous for achieving high energy density and power
density [10]. (2)Its largelateral size andultra thinproperties
provide an ultra high specific surface area.Combined with its
excellent electronic conductivity (102 S/m), the content of
conductiveagentintheelectrodecouldbedecreased.Environ
mentalfriendliness and theabundance ofphosphorus are also
importantreasonsforitbeinganimportantcandidatematerial
2.2.Currentandfuturechallenges
BP is considered anexcellent active materialin lithium ion
batteries,sodiumionbatteries,magnesiumionbatteriesandsuper
capacitors(Fig.2).AlthoughBPhasattractedgreatattentioninthe
fieldof energy storage,it still hasmanychallengesin practical
applications.
TheBPusedinthecurrentenergystoragefieldispeelofffrom
bulk BP. Conventional preparation methods include "top down
methods" (mechanical cleavage, liquid exfoliation, etc.) and
"bottom up methods" (e.g., chemical vapor deposition (CVD)
andwet chemistry).Thesemethodsaregenerallyexpensiveand
timeconsuming. Thisproduction challengepartiallyoffsetsthe
superiority of black phosphorus performance. In addition,
phosphorene,anatomic thicknessBP,degradesunderair,which
preventsitsuseinenergystoragedevices.
BPcanreactwiththreelithiumatomstoformaLi3Pcompound,
correspondingtoaveryhightheoreticalspecificcapacity (2596
mAh/g).AlthoughBPisanimportantcandidateforanodematerials
in lithium ion batteries, it still has several shortcomings. For
example,layered BPwillre stack due tovander Waalsforces,
which will result in additional electrolyte consumption. And,
volumeexpansionfromamorphousLi3.3PtocrystallineLi3Pduring
thedischargingprocessleadstopulverizationoftheanode.The
lossofelectricalcontactcausedbyelectrodecrackingandthelow
electron conductivity of Li3P all make the reversibility of the
discharge process worse, further resulting in low Coulombic
efficiencyandcapacityretentionofthefirstcycle[11].
Sodiumionswithalargerionicradius(0.106nm)havedifferent
embeddingbehaviorthanlithiumions(0.076nm).BPhasalarger
interlayerchannelsize(3.08Åvs.1.86Åofgraphite),whichmeans
thatsodiumismoreeasilystoredbetweenthe2DBPlayers.In
addition,the2DBPexhibitsextremelyhighcapacityandfastion
diffussionchannelsduring sodiumalloying. However,therapid
declineincapacitycausedbythelargevolumechange(300%)
duringchargingand dischargingstill hinders theapplicationof
blackphosphorusinsodiumionbatteries.
The current applicationof blackphosphorus incapacitors is
limitedbycapacitiveperformance.Thespecificsurfaceareaand
poresizedistributionstillsignificantlyaffecttheperformanceof
theelectrodematerial.Inaddition,blackphosphorusisalsousedin
magnesiumionbatteriesandpotassiumionbatteries.
2.3.Advancesinscienceandtechnologytomeetchallenges
Highmaterialcostsandlimitedproductioncapacitypreventthe
applicationofblackphosphorus.BPthatissimpletoprepareand
scalable is urgently needed. Recently, a technique of applying
pressure to synthesize BP at a normal temperature has been
reportedforuseinanopticaldevice[12].However,theanisotropic
volume expansion of 2D BPduring the reactionrequires other
conductivetwo dimensional materials(suchas redoxgraphene
GO)forbuffering.Liuetal.developedasimpleandscalablemethod
for synthesizing BP/GO composites by pressurizing at room
temperature[13]. Ata currentdensity of1A/g, thecapacityof
thecompositestabilizedat1250mAh/gafter500deepcycles.
Enhancing the stability of the electrode structure is an
important meanstosolve thevolume changeand thecapacity
attenuationcausedbytheelectricalcontactloss.Thisstrategyis
usually achieved by couplingconductive carbon (carbon black,
carbonnanotubes,graphene,etc.)withBPtoformaphosphorus
carbonbond.Sunetal.proposeastrategyforformingstrongP C
bondsbetweenBPandgraphene,whichisachievedbyHEMMinan
argon atmosphere of 1.2MPa [14]. The P C bond effectively
decreasesthevolumechangeduringlithiationanddelithiationand
increasesthecoulombicefficiencyofthecycle.
Whenappliedtoacapacitor,2DBPisstilllimitedbyitslower
capacitance.Duetothelargespecificsurfacearea,there stacking
of 2D BP is inevitable, and its electronic conductivity is also
impaired due to the absorption of impurities and defects. The
constructionof3DBPcaneffectivelyavoidthere stackingof2DBP
and promote theeffective diffusionof electrolyte. Atthe same
time,closecontactbetweenthe2DBPlayerscanprovideafastand
continuous electron transport path. Wu et al. proposed a
heterostructuredBP/CNTs hybrid material.The CNTsembedded
in the BP layer can promote interlayer electron conduction,
reducethestacking of BPnanosheets,and enhancemechanical
stability[15].
The mechanical flexibility of phosphorene and graphene
compositespowers wearable electronics[16]. Thehighpacking
densityisduetotheclosecontactofphosphorenewithgraphene,
buttheBPinphosphorene graphenecompositesiseasilyoxidized.
Therefore,atpresent,therearefewreportsonphosphoreandBP
basedstrategiesasanode.
The interlayer distanceof black phosphorus (5.4Å)is larger
than thatof graphite(3.4Å),meaningthat it iseasier toinsert
larger ions between them, so the feasibility of BP applied to
magnesiumionbatteriesandpotassiumionbatteriesisalsowidely
reported. BP hasbeenproven tohave a capacity over graphite
materialsforuseinpotassiumionbatteries.Sultanaetal.proposed
a potassiumion batteryanodematerialthat encapsulatesblack
phosphorus in a carbon based material and measured a high
capacityof600mAh/g[17].BasedontheBPalloyformedbythe
expectedalloyingmechanism,thetheoreticalcapacityofBPcanbe
ashighas843mAh/g.Moresimulationresultshaveconfirmedthat
BP can be used as an electrode material for magnesium ion
batteries,whichcanstoremagnesiumatomsinMg2P.Thesingle
layerofphosphorenemaintainsitsstructuralstabilityintheform
ofMg0.5P[18].
2.4.Concludingremarksandprospects
With its intrinsic superior performance, BP is one of the
promisingmaterialsinthefieldofenergystorage.Theinterfacial
interactionbetweenBPandothermaterialsisanimportantfactor
Fig.2.2DBPusedforelectrochemicalenergystorage.Copiedwithpermission[10].
inimproving theelectrical performanceof batteriesand super
capacitors. But at present, BP still faces many challenges.
ImpuritiesanddefectsintroducedduringBPpreparationadversely
affectelectrochemicalproperties.Inaddition,theelectrochemical
propertiesof2DBParehighlydependentonthenumberoflayers,
sothemanufactureof2DBPwithadjustablelayercountisvery
important. The current complex and expensive manufacturing
processisalsoanimportantfactorhinderingBP'sexpansionand
furtherapplication.Therefore,competitiveprocessingtechnology
shouldbedevelopedtoimproveproductquality,reduceproduc
tioncosts,andpromoteBP'sapplicationinenergystorage.Inthe
field of energy storage, most of the research focuses on the
preparationandcharacterizationofelectrodematerials,andthere
isstillinsufficientresearchonthemechanismofactionofblack
phosphorusto improvechemical properties. Fullystudying the
mechanismanddevelopingthefullpotentialofblackphosphorus
isatoppriority.
Blackphosphorus is a very attractivenew two dimensional
material, but it still facesmany challenges. A large number of
theoretical calculations and experimental studies have been
reported,hopingtomakeevengreaterbreakthroughsinthefuture.
2.5.Acknowledgment
Thisworkis supportedby KeyResearchProgramofShaanxi
Province(No.2017ZDXM GY 035).
3. MXenematerialsforelectrochemicalenergystorage
ZifengLin,HuiShao***
3.1.Status
2Dtransitionmetalcarbides,carbonitrides,andnitrides,known
asMXenes,areproducedbyselectiveremovalofaatomlayersfrom
MAX phaseprecursorsusing aqueousfluoride containing acidic
solutions astheetchants.MAXphases areternarycarbidesand
nitrides,withageneralformulaofMn+1AXn(n=1 3),whereMisa
transition metal (such as Sc, Ti, Zr, Hf, V, Nb, Ta, Cr, Mo), A
representselementsfromthegroup13and14oftheperiodictable
andXiscarbonand/ornitrogen.ThemetallicM Abondsofthe
MAXphasescanbebreakbytheetchant,resultinginmultilayered
Mn+1XnTxmaterials,and Txrepresentssurfacefunctional groups
(suchashydroxyl,oxygenandfluorine)thatareobtainedfromthe
etchingprocess.Afterward,multilayeredMXenescanbedelami
nated into single flakes via intercalation of organic molecules
and/or metal ions, followed with mechanical vibration or
sonication inwater. Since 2011,Gogotsi etal. reportedthefirst
MXene material Ti3C2Txthat was synthesizedby removingAl
atomsfromTi3AlC2MAXphaseinconcentratedHF(Fig.3),todate,
morethan20differentMXenematerialsaresuccessfullyprepared,
anddozensofmoreMXeneshavebeentheoreticallypredicted[19].
MXenescanhaveatleastthreedifferentformulas:M2X,M3X2
andM4X3,whereMisanearlytransitionmetalandXiscarbon
and/ornitrogen.Theycanbemadeinthreedifferentforms:mono
Melements(forexample,Ti2CandNb4C3);asolidsolutionofat
least two different M elements (for example, (Ti,V)3C2 and
(Cr,V)3C2);orordereddouble Melements,inwhichonetransition
metaloccupiestheperimeterlayers,andanotherfillsthecentralM
layers(forexample,Mo2TiC2andMo2Ti2C3,inwhichtheouterM
layersareMoandthecentralMlayersareTi).Solidsolutionsonthe
Xsiteproducecarbonitrides.NA,notavailable[19].
Withthemeritsofmetallicconductivity,uniquetwo dimen
sional structure and rich chemistry, MXenes have attracted
significant attention as electrode materials of rechargeable
batteriesandelectrochemicalcapacitors.Thecalculatedtheoreti
calcapacities ofLi,Na,KandCaionsbatteriesbasiconvarious
oxygenterminatedMXenenanosheetsare447.8,351.8,191.8and
319.8mAh/g, respectively [20]. Experimentally, MXene film
electrodes typically deliver capacities less than 200mAh/g for
Li+ storageand even less for Na+ and othermetal ion storage.
MXenecomposite or surface functionalized electrodeis able to
enhancetheelectrochemicalperformance greatly. Ontheother
hand,MXenesexhibitoutstandingcapacitiveorpseudocapacitive
performance,especiallyinaqueouselectrolytes.Highgravimetric
capacitance up to 350F/g as well as the high volumetric
capacitanceof 1500F/cm3 can be obtainedfrom a Ti
3C2Txfilm
electrodein3mol/LH2SO4electrolyte;theredoxpeaksidentified
inFig.4aindicatesapseudocapacitivecontributionthathasbeen
wellconfirmedbyX rayabsorptionanalysis[21].
3.2.Currentandfuturechallenges
TopushforwardtheapplicationofMXenesinenergystorage,
severalchallengesneedtobeaddressed.Alargenumberofnovel
MXene compositions with interesting properties have been
theoreticallypredicted,andmoreexperimentaleffortsshouldbe
takentoremovethegaps.Anotherconcernisthatthehazardous
aqueousfluoride containingacidicsolutions,suchashydrofluoric
acidorlithiumfluoridemixedinhydrochloricacid,arethemost
commonusedetchantstoprepare MXenes.Asafeandefficient
route for MXene synthesis is important to further practical
applications.Inaddition,thestabilityofMXenesremainsanother
challenge.MXenessufferfromeasyoxidation,thusbringdifficul
tiestothelong termreservation.Ithasbeendemonstratedthatthe
oxidation of MXene flakes starts from the edges, and the
manufacturing procedure can affect the stability. Restacking is
oneofthemainchallengesnotonlyexistinMXenesbutalsoother
2Dmaterialswhenfilteredasfilmelectrodes,whichwillimpede
electrolytemigration andlimitpowerperformanceasshownin
Fig.4b[22].Onepossibleapproachtopreventtherestackingissue
istoincorporatepolymerswithpolarfunctionalgroupswithinthe
interlayers. Although MXene electrodes demonstrated a high
capacitanceinaqueouselectrolytes,performancesinnon aqueous
systemsareinadequate.Itiscrucial toincreaseMXenescapaci
tanceinnon aqueouselectrolytessincenon aqueoussystemscan
offeralargervoltagewindow(>2.5V),thusleadtohighenergy
density. Besides, in the battery applications of MXenes, the
irreversiblecapacityoftheinitialcycleshouldbeminimizedfrom
thepracticalpointofview.
3.3.Advancesinscienceandtechnologytomeetchallenges
LotsofeffortsarededicatedtothesynthesisofnovelMAXphase
precursorsandMXenecompositionsinthelastfewyears.Ti4N3Tx
MXenewaspreparedbyheatingTi4AlN4inamoltenfluoridesalt,
makingitaninterestingHF freeapproachtoprepareMXenes[23].
Very recently, a new series of Zn based MAX phases (Ti3ZnC2,
Ti2ZnC,Ti2ZnN,and V2ZnC)weresynthesizedbya replacement
reaction[24].ThenaLewisacidicmoltensaltwasusedtoextract
Znatom of theas preparedMAX phases,resulting inthe first
reportedCl terminatedMXenes.Ithasbeenconfirmedthatsurface
terminationsplayacrucialroleinenergystorageapplications[25].
SomerecentstudieshaveindicatedthatClfunctionalizedgroups
canenhancetheelectrochemicalbehavior[24].
Thearchitecturaldesignoftheelectrodeisaneffectivemethod
to address the restacking issue. Xia et al. reported a vertical
alignmentTi3C2Txelectrode(Fig.4c),whichexhibitsanoutstand
ingthickness independentrateperformanceinaqueouselectro
lyte[22].Over200F/gisretainedatahighscanrateof2000mV/s
with electrode thickness even up to 200
m
m. Moreover, 3DmacroporousMXene film (Fig.4d) werefabricated to enhance
theiontransport.Byusingthismacroporousdesign,Ti3C2Tx,V2CTx,
and Mo2CTxelectrode deliver high rate electrochemical perfor
manceandlongcyclingstabilityinNa ionstorage[26].
Correctly coupling organic electrolytes with electrodes can
furtherpush forward theelectrochemical performance in non
aqueoussystems[27].Therecentreportprovedsolventisthekey
factorincontrollingthechargestoragemechanismintheTi3C2Tx
electrode.AspresentedinFigs.4eandf,thefulldesolvationofLi+
inpropylenecarbonatesolventleadstomuchbetterelectrochem
icalperformancethaninothersolventswithlessdesolvation.
Fig.4.(a)Cyclicvoltammetryprofilesofper-intercalatedTi3C2Txfilmin3mol/LH2SO4atscanratesfrom2mV/sto200mV/s.Copiedwithpermission[21].Copyright2017, NaturePublishingGroup.(b,c)SchematicillustrationofiontransportinTi3C2TxMXenefilms.(b)Iontransportinhorizontallystackedand(c)verticallyalignedTi3C2TxMXene
films.Thebluelinesindicateiontransportpathways.Copiedwithpermission[22].Copyright2018,NaturePublishingGroup.(d)SEMimageofmacroporoustemplated
Ti3C2Txelectrodecross-section.Scalebars:5mm.Insetsshowsschematicallytheioniccurrentpathwayinelectrodes.Copiedwithpermission[21].Copyright2017,Nature PublishingGroup.(e)CVcurvesofmacroporousTi3C2Txelectrodewith1mol/LLiT-FSIinDMSO,ACNandPCorganicelectrolytesand(f)schematicofasupercapacitorusing2D MXeneasanegativeelectrodewithsolvatedordesolvatedstatues.TheOCVs(markedbyarrows)are 0.13V(black), 0.32V(blue)and 0.12V(red)versusAgforDMSO,ACN andPC-basedelectrolytes,respectively.Copiedwithpermission[27].Copyright2019,NaturePublishingGroup.
3.4.Concludingremarksandprospects
MXenes with advantages of metallic conductivity and 2D
structure are emerging as excellent electrode materials for
batteriesandelectrochemicalcapacitors.Breakthroughsinmate
rialssynthesis, electrode structure design, and a better under
standingofchargestoragemechanismhavegreatlyimprovedthe
electrochemical performance of MXene electrodes. Despite the
remained challenges, it can be provisioned that MXenes will
becomecompetitiveelectrodematerialsfromthepracticalpointof
viewandwilldevelopfastinenergystorageapplications.
3.5.Acknowledgments
Z.LinissupportedbytheFundamentalResearchFundsforthe
CentralUniversities(No.YJ201886).H.Shaowassupportedbya
grantfromtheChinaScholarshipCouncil.
4.2Dcovalentorganicframeworksforenergyconversionand
storage
PengPeng,ZhonghuaXiang*
4.1.Status
SinceYaghiandco workersdiscoveredthetopologicalframe
worksin2005[28],adiversityof2Dcovalentorganicframeworks
(COFs) have emerged towards versatile applications. With
preciselycontrollable capacitiessuchaswell defined structures
androbust tailoringheteroatoms[29],2D COFshavepresented
superior potentials for energy storage and conversion devices.
Through hightemperature treatment, COFs are widely used to
prepare hetero doped catalysts for oxygen reduction reaction
(ORR), oxygenevolution reaction(OER)etc.,which arevital for
clean and renewable energy technologies such as metal air
batteries and fuel cells [30]. To date, numerous COFs derived
highlyefficient energy electrocatalystshave been reported. For
example,benefitedfromwell defined2Dstructuresandcomplex
ation of non noble metals (such as Fe, Co, Mn), carbon based
catalystsaredevelopedwithoutstandingcatalyticperformancefor
oxygenreductioninbothalkalineandacidmedia[31].
4.2.Currentandfuturechallenges
Eventherapiddevelopmentof2DCOFshaspredictedabright
future,challengesofCOFstowardsenergyapplicationsstillexist.
Toaddressthepracticalapplicationsof2DCOFsinenergydevices,
researchersinthefieldshouldfocusonthesechallengesoutlined
in (Fig.5).Firstly, theinsufficient stability orlimited durability
remainsagrandchallenge.FornotonlyCOFs derivedcatalysts,but
also most carbon based catalysts, significant performance loss
(50%)occuroverafewhundredsofhoursinthepresenceofO2at
more practical potentials (>0.6V) [32]. In both aqueous acidic
electrolyteandsolid stateelectrolyte basedMEAs,carbonstruc
tureswouldbecorrodedunderthechemicalattackofH2O2and
radicalsthroughtheFentonreaction,whichcouldalsodrivethe
demetallation of the active sites. Besides, collapse of carbon
structures generates additional barriers for mass transfer and
charge transport, leading to limited performance in practical
scenarios.
Anotherissuethatprecludesthewideapplicationof2DCOFsis
their poor processing ability. The inherent cross linked frame
worksorreticularnetworksresultintoinsolublenatureandpoor
three phaseinterfaces,incurringdifficultiesforthepreparationof
electrodesandunstablefactorssuchasstripingoff.Asinsoluble
powders,COFs cannot bereliably interfacedonto electrodes or
incorporatedintodevices.Forthefabricationof electrodeswith
insolubleCOFs,extracomponents(bindersorconductiveagents)
arealwaysnecessary,whichalsohinderthechargetransportand
masstransfer.
Last but not the least, the pyrolysis free construction of
functional2DCOFswithintrinsiccatalyticpropertyisimperative.
Inordertopromotethepracticallyusefulperformancelevelsof2D
COFstowardsenergydevices,itisveryimportanttoilluminatethe
catalystdegradationmechanismsandelucidatetherolesofeach
components.Nevertheless,pyrolysistreatmentisalwaysneeded
toimprovetheconductivityandstabilityofCOFs basedprecursors,
which unfortunately bring unpredictable and undetectable
changestothestructures.Onthecontrary,pyrolysis freederived
2D COFs would provide valuable information for the optimal
structures and components in a predictive manner. Thus, the
developmentofpyrolysis freesynthesiswouldbeinstructivefor
translating the experimental activity and stability into device
performance.
4.3.Advancesinscienceandtechnology
Recentyearshavewitnessednumerouseffortsinexplorationof
2DCOFsforfunctionalapplicationsandseveralapproacheshave
been made tomeet those challenges. In terms of the stability,
researchershavefoundthatFentonreactionsinvolvingmanganese
ionsarenearlynegligibleandthusMn basedcatalystsmayprovide
anewopportunitytoachieveenhancedstability[33].Meanwhile,
increasingtheratioofhighlygraphitizedcarbonalsobenefitsthe
durability byenhancingcorrosion resistance in electrochemical
oxidativeenvironments.However,highergraphitizationmakesit
hardertoaccommodateactivesitessuchastransitionmetalandN
dopants.Itremainsachallengetofindthebalancebetweenactivity
andstability.
Interms oftheprocessability,evennumerousattemptshave
beenutilizedtoprepareprocessableCOFnanosheetsorfilms,only
limitedachievementshavebeenobtained.Thematuresynthesisof
solution processable COFs still remains a grand challenge. For
example, physical approaches, including ultrasonication, ball
milling,andmechanicaldelaminationusuallybreaktheCOFsinto
small pieces with decreasing properties. Chemical approaches
suchasinterfacialpolymerizationallowstheformationoffilm like
2DCOFs,butitistoodifficulttoscaleup.Recentlydevelopedionic
Fig.5.Challengesfor2DCOFsintheareaofenergydevices:insufficientstability, poorprocessingabilityandunpredictablestructurescausedbypyrolysis.
COFswhich couldbeexfoliatedintonanosheetsuponmixingin
special solvent still demonstrate rather limited solubility with
smallsizesoftheexfoliatednanosheets.Althoughissuesstillexist,
thesedevelopmentshavepavedpathwaysforrealizingprocess
able 2D COFs. It should be noted that researchers have also
developedmethodstowithstandtheinter layer
p p
stackingortheinter layer interactionsof2D COFlayersviaencodinghigh
densityelectrostaticrepulsionintotheskeletonorsimplein situ
chargeexfoliationpathway.Bythismeans,highlysoluble2DCOFs
andstabletruesolutionsof2DCOFshavebeenreported[34].
In terms of thedevelopment of COFs based electrocatalysts
withoutpyrolysis,consideringthecombinationofactivesitesand
conductive backbone, several possible approaches have been
explored.Onewayis todesign and synthesizeCOFscombining
fully conjugatedstructureswithactivecenters.Researchershave
reporteda2DCOFswithdelocalizedconnectionsandactiveknots,
which demonstrate outstanding performance for ORR catalysis
[35].Anotherpromisingwayisformingthehybridelectrocatalysts
byself assemblingpristine COFswithmatrixthat containlarge
conjugatedsystemandhighchargemobility.Forexample,ithas
beenreportedthataftercombiningwithreducedgrapheneoxide
(rGO),electricalconductivityofthehybridizedmaterialssignifi
cantlyincreasebymore thansevenordersofmagnitude, along
with the enhanced ORR activities [36]. Very recently, by
constructing the intermolecular conjugatedstructures, carbon
basedcatalystswithnitrogen coordinatedsingleatomshavealso
beenachievedviapyrolysis freepathway(Fig.6),demonstrating
superioractivities and long termstabilities when assembled in
zinc air batteries [37]. As one can expect, thedevelopment of
pyrolysis free approach not only paves a new and promising
avenuetoatomicallyoptimizethecatalysts,but alsoprovides a
platformfortheaccuratetheoreticalpredictioncalculations.Based
onthewell definedstructuresof2DCOFs,thistechniquemakesit
possibletodevelop moreexcellent catalysts forvarious energy
conversionandstoragedevicesbesidesoxygenreduction.
4.4.Concludingremarksandprospects
2D COFs represent a newsynthetic era of the catalysts for
energy applications. Their unique features, such as flexible
moleculardesign and diverse buildingblocks provide 2D COFs
with promising potentials in further applications for energy
storageandconversiondevices.Therapiddevelopmentinthisarea
has, therefore, attracted increasing interest from scientific
researchers. The 2D COFs combining with the pyrolysis free
techniquesallowresearcherstomodulateactivesitesandcontrol
thedensityofactivestiesatthemolecularlevel,offeringpiratical
possibilitiestostudytheoptimalstructures,degradationmecha
nisms and kinetics of energy electrocatalysis. 2D COFs with
enhancedstabilityandprocessabilityholdgreatpromiseforthe
bettersolution for energy and environmental issues. Although
currently2D COFstowards energyapplicationsarein itsinfant
stages,thenewadvancesinscienceandtechnologyencouragethat
itwillgrowintoarichandbroadareaofgreatimportance.
4.5.Acknowledgments
WeacknowledgethefinancialsupportfromtheNaturalScience
FoundationofChina(No.21676020);theBeijingNaturalScience
Foundation(No.17L20060);theYoungEliteScientistsSponsorship
ProgrambyCAST(No.2017QNRC001);theTalentCultivationand
Open Project (No. OIC 201801007) of State Key Laboratory of
Organic Inorganic Composites; the Distinguished Scientist Pro
gramatBUCT(No.buctylkxj02);Double First ClassConstruction
Projects(Nos.XK180301,XK1804 02)andthe111ProjectofChina
(No.B14004).
5. 2Dmetaloxidenanosheet-basedelectrodesforcharge
storagedevices
JohanE.tenElshof*
Fig.6. Constructionofnitrogen-coordinatedsingleatomcatalystthroughpyrolysis-freepath.(a)Atomicallyrivetthewell-designedCOFnetworkscontainingFe-N-Ccenters ontographenematrixviaintermolecularvanderWallsinteractions;(b)as-obtainedcatalystswithplentifulFeatoms(brightdots)anchoredonthegraphenematrix.Copied
withpermission[37].Copyright2019,AmericanAssociationfortheAdvancementofScience.
Fig.7.Threeexamples ofoxidenanosheets. Copiedwithpermission[38–40].
5.1.Status
The high specific surface areas and well defined surface
terminationsoftwo dimensionaloxideandhydroxidenanosheets,
combined with their semiconducting nature, makes these
materialsattractiveasbuildingblocksforconstructionofultrathin
porous electrode architectures for future generation faradaic
supercapacitorsandlithium ionbatteries.Techniquestochemi
callyexfoliatelayeredmetaloxidesandlayereddoublehydroxides
(LDH)intocolloidalunilamellar,single crystallineplateletswith
thicknessesinthe0.5 3nmnanometer rangeandlateraldimen
sionsof50nm 50
m
mhavebeenoptimizedandgeneralizedoverthepastyears.Examplesofwell knownnanosheetcompositions
areTi1-xO2,Ca2Nb3O10,MnO2,V2O5,TaWO6,Ni(OH)2andCo(OH)2
[38 40],asshowninFig.7.Dozensofothercompositionshavealso
beenrealized,dependingonlyontheavailabilityoflayeredparent
compoundsthatcanbechemicallyexfoliated.
Owingtotheir2Dnature,nanosheetstendtorestackduring
electrodeformation,therebyreducingtheireffectivesurfacearea
and generating slit shaped porosity. The in plane orientational
disorderofelectrodesmadefromrestacked2Dcrystallitescanhelp
tosuppress phase transformations during charging/discharging
andthusimprovecyclelife.Theionstoragecapacityisdetermined
byboth thespecificsurface areaand thepore sizeswithin the
electrodes.Inprinciple,largeporesizesfacilitatefastlithiumion
transportation and yield high rate capacities. Pillaring, i.e.,
incorporationofadditionalentitiessuchasnanoparticles,nano
wiresandnanoplateletsbetweenrestackednanosheets,hasbeen
shownavalidapproachtopreventorslowdowntheirstructural
collapseandtorealizestructurallystableelectrodearchitectures
withdischargecapacitiesevenupto860mAh/g[41].
Mostofthemetaloxidenanosheetcompositionsmadesofarby
exfoliationmethodsarebasedonoxidescontainingTi,Taand/or
Nb.Theyaretypicallywidebandgapsemiconductorsexhibiting
poorconductivity[38]. Pillaringphasesarethereforepreferably
highlyconductive,e.g.,Agnanoparticles,(reduced)grapheneoxide
(rGO) or carbon nanotubes. Synergistic phenomena have been
observed in some of these nanocomposites, e.g., spontaneous
electroncharge transfer fromgrapheneintoTi1-xO2 nanosheets
resultinginoverallconductivityenhancement,orfavorablecharge
separation atthe interface betweentwo suchphases,i.e., a Li+
accepting phase and an electron accepting phase, thereby
providingadditionallithiumstoragesites[42].
Faradaic pseudocapacitors based on 2D transition metal
hydroxides utilize (surface) redoxreactions to chemicallybind
andstoreions.Onlysurfaceatomsplayaroleinpseudo capacitive
processes.ThebestcandidatematerialisRuO2(700F/g),butsince
itisrareandexpensive,researchhasbeenfocusingonmorereadily
available cheaperalternativessuchas2DNi(OH)2,Co(OH)2 and
MnO2.Specificcapacitancesupto1100 1300F/g(at1A/g)have
beenreported[38].
Ithasalsobeendemonstratedthatthefractionofelectrochem
icallyactiveatoms inmonolayer andmultilayer nanosheetthin
film electrodes is higher than in precipitated nanosheet based
powders. Use of nanosheets as thin film electrodes in small
(flexible)devicesisthereforeoneofthepotentiallymostpromising
areasofapplicationofthese2Dmaterials.Multilayerarchitectures
ofoxidenanosheetsandoptionallyothermaterialscanberealized
withanunsurpasseddegreeofcontrolovertheassemblyprocess
using layer by layer (LbL) Langmuir Blodgett deposition [43].
Heterostructures made by sandwiching metal oxide or LDH
derivednanosheetswithe.g.,GO,rGOandCoOOHnanowireshave
shown reasonable togoodperformances when testedas Li ion
batteryorpseudocapacitorelectrodes.LbLassemblyisalsouseful
forthinfilmdevicefabricationonsoftsubstrates,inparticularfor
devices consisting of a limited number of layers. Interestingly,
flexiblepaper likenanocompositesconsistingoflithiatedTi1-xO2
nanosheetsandcarbon,withacapacityof150mAh/ghavealso
beendemonstrated[44],asshowninFigs.8aandb.
5.2.Currentandfuturechallenges
Oneofthemaincurrentchallengesconcernsthesynthesisof
nanosheetsonlargescale.Becauseofthemicron sizedradiusof
gyrationofnanosheets,colloidalnanosheetdispersionsarevery
dilute,typicallyintherangeof1 10g/L.Largereactionvolumesare
thusrequiredtoproducerelativelysmallamountsof2Dmaterial.
Under more concentrated conditions, non ideal separation of
sheetsandrestackedclusterswilldominatethestructureofthe
colloidaldispersions.
Otherchallengesincludegettingmorecontroloverthesizeof
the intergallery spaces, and further increasing the structural
stabilityoftheelectrodes.Inmanycases,restackedhostmaterials
oftensufferfromslowkineticsresultingfromtheincompatibility
betweenthesizeoftheintercalatingionsandthelimitedlattice
spaceavailableintheintergalleryspace.Moreover,theelectrode
architectures that are essentially composed of loose stacks of
isolated sheets, appear to degrade relatively quickly as a
consequence of repeated electrochemical exchange reactions.
Thestructuralcoherencythereforeneedstobeimproved,ideally
withoutoveralllossofelectrodeflexibility.
Whilehybridizationofoxidenanosheetsandmoreconductive
second phases as a route to getting materials with improved
electricalconductivityhasbeenstudiedinsomedepth,theuseof
controlleddefectengineeringstrategies,e.g.,aliovalentdopingin
2Doxidelattices,asatooltoimprovethelateralconductivityof
nanosheets as well as their surface redox properties, and
consequently alsotheir performance, has been explored much
less[46].Asystematicunderstandingoftheinfluenceoftransition
metal ion doping into 2D nanosheets on their conductivity,
electrontransfer(redox)propertiesandcapacitytoelectrochemi
callystoreLi+,willhelptoboosttheperformanceofnanosheet
basedelectrodesinbatteriesandsupercapacitors.
5.3.Advancesinscienceandtechnologytomeetchallenges
The prospect of massive scale production of nanosheets as
would be required for their commercial application in larger
energy storage systems seems unlikely on the short and
intermediate term.Their mostlikelyapplication is therefore in
theareaof(flexible)thinfilmbatteriesandsupercapacitorswith
Fig.8.(a)Opticalimageofaself-standinglithiumtitanatenanosheetelectrode
underbending.(b)Cross-sectionofthesamefilm.Copiedwithpermission[44].
Copyright 2013, WILEY-VCH. (c) Optical images of MnO2 nanosheet-based
microsupercapacitoronpolyimidesubstrateunderdifferentbendingangles.The
centimeter to micrometer sized lateral dimensions. Industrial
scalefabricationofthinfilmstoragedevicesrequiresmuchfaster
electrodeassemblymethodsthantheLangmuir Blodgettmethod.
Takingtheabove mentionedchallengesinmind,researchintothe
useof inkjetprintingof oxidenanosheetsand 2Dmaterialsin
general is currently ongoing and shows good prospects [47].
Devicesofsomewhatlargedimensionscouldbemadeviascreen
printing. Given the ability to mass produce layered thin film
devices via screen printing, the application of this production
methodseemslikely.
An advantageof employingnanosheets incombination with
wet chemicalprocessingmethodsisthatnohightemperaturesare
requiredintheelectrodeformationprocess.Theprecursorinkcan
thuscontainorganicandothersensitivecomponentsthatremain
in the as dried films and can serve a specific purpose. More
importantly,italsoimpliesthattemperature sensitivesubstrates
suchasflexibleplasticsubstratescanbealsousedasaplatformfor
deviceconstructdeviceson(Fig.8c)[45].Paralleltothefurther
development of nanosheet based electrodes, there is a more
general needfor saferelectrolytesin next generation batteries.
Replacementof liquid and gel electrolytesby solid electrolytes
wouldbeamajorstepforward.Thedevelopment ofnovel thin
solidelectrolytes,includingoptimizationoftheelectrolyte nano
sheetelectrodeinterface,isthereforeneeded.
5.4.Concludingremarksandprospects
Oxide nanosheetsarepromisingcandidatematerialsfor thin
film charge storage device electrodes. Various scalable low
temperaturedepositiontechniquesforthinandthickfilmdevice
fabricationlike inkjet and screenprinting are available. While
showingreasonableperformance intermsofenergyand power
density,thenanosheet basedelectrodearchitecturesneedfurther
structural improvements to extend their cycling lifetime, and
improvedcontrolovertheporesizesinthematerialinorderto
improveion diffusionand storagecapacity. Hybridization with
conductivesecondphasestoimproveconductivityhasshowntobe
successful, in particular a systematic exploration of aliovalent
dopingstrategies canhelptoenhance both theconductivityin
nanosheets,andimprovetheirelectrontransferandsurfaceredox
properties.
6.Verticallyalignednanosheetsaselectrodematerialsfor
high-performancerechargeablebatteries
RouTan,ChenLiu,ZhaoxiZhang,XiaochuanDuan*
6.1.Status
The developmentof electrode materialswith well designed
architecturespromiseshigh performancerechargeablebatteries.
Inpursuitofbetterelectrodekineticsandmasstransportation,3D
nanostructuredelectrodescomposedbyverticallyalignednano
sheets(VANS) havebeen receivingincreasingresearchinterest.
Combined witha highlyconductive carbon basedsubstrate(or
metallic thin film), VANS electrodes areendowed with several
merits,suchaslargesurfacearea,superiorelectroncapability,and
excellent mechanical strength. In this roadmap, various VANS
electrodeswithdifferentcomposition thatcanbeused asfree
standing electrodes for the high performance rechargeable
batteries are highlighted. Recent advances regarding the novel
synthetic method for VANS electrodes and the speculative
mechanism for the enhanced electrochemical properties are
reviewed. In addition, the emerging challenges and some
perspectivesontheprogressofVANSelectrodesforrechargeable
batteriesareincluded.
6.2.Currentandfuturechallenges
ThestudyofVANSoriginatedfromtheriseoftheapplicationof
2Delectrodematerialsinthefieldofenergystorage.Compared
withthebulkelectrodematerials,theultra thinstructureof2D
electrode materials thoroughly facilitates the electrochemical
reaction,whilebeingabletominimizeoreliminatethevolume
changeoftheelectrodematerialsinthecharge/dischargecycles.
Therefore,2Delectrodematerialscangenerallyexhibithighactual
specific capacity and structural stability. Previous studies have
provided that 2D electrode materials tend tohave a reversible
capacityexceedingthetheoreticalcapacityduetotheirsmallsizes
andlargenumberofexposedsurfaces.Inaddition,theultra thin
structure of 2D electrode materialsfacilitatethe rapidand full
immersion of theelectrolyte,which caneffectively shortenthe
electrontransport andion diffusiondistance,therebyachieving
fastchargeanddischargeforrechargeablebatteries[48].
Itiswell knownthattherearesizeeffectandstrongvander
Waals force in the nanomaterials, making the nanostructured
electrodesextremelyeasytoformirreversiblestackedaggregates
[22].Inparticular,theultra highspecificsurfaceareaandstrong
interlayerforcesof2Dnanomaterialspromotetheoccurrenceof
agglomeration,whichgreatlyreducesthestructuraladvantagesof
2D nanomaterials. This stacked structure is detrimental to the
rapid transfer of electrons and ions when used as electrode
materialsforenergystorage.AsshowninFig.9a,theclosestacking
ofactivematerialsformsaparallelelectrodestructure,resultingin
poor wettability of the electrolyte, which in turn leads to an
increase in ion transport distance [49]. However, if the 2D
nanomaterials canbedesigned a verticallyaligned structure as
showninFig.9b,thereisa largeamountofporesbetweenthe
open ended nanosheets. This vertical structure expands the
contactareabetweentheactivematerialsandelectrolyte,which
isbeneficialtoachieve rapidextractionandembeddingofions.
Therefore, controlling the vertical orientation assembly of 2D
materialsisanimportantmeanstopromotetheirelectrochemical
energystorageapplications.
Fig.9.Schematicdepictionofthestackedgeometry(a)andtheverticallyaligned
structure(b).Copiedwithpermission[49].Copyright2011,AmericanChemical
6.3.Advancesinscienceandtechnologytomeetchallenges
Carbon basedmaterialsareusuallyadoptedasthesubstratefor
theconfigurationofVANS.Inthepasttwodecades,carbon based
materialsandtheirhybridnanocompositeshavebeenthefocusof
considerableeffortsinenergyconversionandstoragebecauseof
their unique properties, featured by unique porous structures,
superiorelectricalproperties,fastionandelectrontransportation,
etc. In pursuit of optimal performance, various well designed
architectures have been developed for carbon based materials,
includingsomeinterestingsurfacemultilevelstructures(branched
nanorodsor nanosheets) and inner multilevel structures (core/
shell or multichannel nanostructures). However, traditional
preparation processes for carbon based materialsor electrodes
often lead to random restacking of loading materials, which
reducesactive sites and limits ion transport. This shortcoming
keepsthemawayfromtheoriginalintentionofdesign,oftenfails
to achieve the desired performances. To this end, vertical
alignment of 2D nanostructures on carbon based substrate
guaranteeseffectiveactivesitesanddirectionaliontransportthat
canleadtosuperiorperformances.Nevertheless,owingtothebad
compatibilityofcarbon basedmaterialswithothersubstancesand
strict synthesis conditions for 2D nanostructures, only limited
successinvolvingcomplexsynthesis methodhasbeenreported
heretofore.Asaproofofconcept,Xieetal.proposedahierarchical
electrode structure consisting of MoS2 nanosheets vertically
aligned on carbon paper, as shown in Fig.10 [50]. This VANS
structureisconducivetosufficientelectrode/electrolyteinterac
tionandfastelectrontransmission,enablinghighinitialCoulombic
efficiency,highratecapability,andlongcyclelifeforsodium ion
batteries.
Despite VANS electrodes demonstrate exhilarating perfor
manceforenergystoragedevices, theirprecisesynthesisisstill
a huge challenge. In most cases, the VANS electrodes were
prepared by chemical vapor deposition with relatively high
technicalrequirements(i.e.,PECVD)ormultistepprocesses[51].
InordertopromotetheapplicationofVANSelectrodesforhigh
performance rechargeablebatteries, more convenient synthesis
methodswillbethefocusofresearchinthisfield.Encouragingly,
someconcisesyntheticmethodsprovedtobeabletosynthesize
well designedVANSstructures,presentingnewopportunitiesfor
futureresearch.
6.3.1.Salt templatingmethod
Fellinger and co workers successfully prepared vertically
alignedgraphiticcarbonnanosheets(CNS)andmetalcarbide@CNS
compositesusing afacilesalttemplatinginduced self assembly
[52].Theresultingelectrodesmanifestultralowthickness,excel
lent structural tobustness,and porous structure,which enables
large contact between electrode and electrolyte and shortens
electron/iondiffusionpathways,renderingtheirexcellentelectro
chemicalperformanceswhenusedaselectrodematerialsforLi ion
batteries.
6.3.2.Electrochemicalassemblymethod
Lietal.adoptedatunablecyclicvoltammetry(CV)processto
fabricateverticallyalignedsulfur graphene(S G)nanowallsonto
electrically conductive substrates [53]. The S G VANS with
hierarchicalandmacroporousstructuresenablethefastdiffusion
bothoflithiumandelectron,therebyachievingsuperiorelectro
chemicalperformancesincludinghighreversiblecapacity,excel
lent rate capability, and outstanding cyclability when used as
electrodesforlithium sulfurbatteries.
6.3.3.Hydrothermalandsolvothermalmethod
Wangetal.patternedverticallyalignedMoS2nanosheetsonto
exfoliatedgraphenenanosheetsviaascalablesolutionsynthesis
strategy[54].Thisuniquearchitecturecombinestheadvantagesof
vertically aligned structure and 2D geometry, endowing the
features of good mechanical stability, highutilization of active
materials, andfastcapacitive energystoragebehavior. Liuet al.
reportedanelectrostatic attractionstrategytopreparethefew
layered ReS2 nanosheets vertically aligned on rGOsurfaces via
hydrothermal method [55]. By mean of the synergistic effect
betweenfew layeredReS2nanosheetsandthegraphenesubstrate
with the sandwich like structure, the outstanding excellent
sodiumstorageperformancecanbeobtained.
6.4.Concludingremarksandprospects
Here,wegiveabriefreviewofthestructure,synthesismethods
and electrochemical properties of VANS electrode materials.
Compared to other 2D material architecture, VANS electrode
materialswithinterconnectednetworkandeffectiveexposureof
active materials enable high mechanical integrity and fast
chargetransportkinetics.Althoughsomemeaningfulprogresses
achieved, there are great challenge still remaining for VANS
electrode materials. First, the controllable synthesis of
VANS electrode materials withdesired composition, as wellas
facile and scale up synthesis methods, still need to befurther
explored. Second, the relationship between the structures of
VANSelectrodesandtheirrelatedelectrochemicalperformances
or electrochemistry mechanism, is yet be fully understood in
depth.Astheresearchprogresses,theunexploredadvantagesof
VANSstructureswillbemoredeveloped.Theuniqueandversatile
electrochemicalpropertiesofVANShavemadeitagreatpromise
aselectrodematerialsforenergystorageinthefuture.
6.5.Acknowledgments
This study was supported by the National Natural Science
Foundation of China (No. 21601148) and the Natural Science
FoundationofFujianProvince(No.2017J05090).
Declarationofcompetinginterest
Theauthorsdeclarethatthereisnointerestforthismanuscript.
Fig.10.Schematic illustrationof thepaths for thesodium-ion diffusionand
electrontransmissioninVANSstructure.Copiedwithpermission[50].Copyright
References
[1]X.Cai,L.Lai,Z.Shen,J.Lin,J.Mater.Chem.A5(2017)15423–15446. [2]R.Tang,Q.Yun,W.Lv,etal.,Carbon103(2016)356–362.
[3]N.Suen,S.Hung,Q.Quan,etal.,Chem.Soc.Rev.46(2017)337–365. [4]L.Tian,J.Yang,M.Weng,etal.,ACSAppl.Mater.Interfaces9(2017)7125–7130. [5]M.Rana,S.A.Ahad,M.Li,etal.,EnergyStorageMater.18(2019)289–310. [6]M.Yi,Z.Shen,J.Mater.Chem.A3(2015)11700–11715.
[7]N.Pu,C.Wang,Y.Sung,Y.Liu,M.Ger,Mater.Lett.63(2009)1987–1989. [8]C.Yang,Q.Nguyen,T.Chen,etal.,ACSSustainable.Chem.Eng.6(2017)1208–
1214.
[9]M.Tahir,L.Pan,F.Idrees,etal.,NanoEnergy37(2017)136–157. [10]S.Wu,K.Hui,K.Hui,Adv.Sci.5(2018)1700491.
[11]S.Jung,Y.Han,J.Phys.Chem.C119(2015)12130–12137. [12]X.Li,B.Deng,X.Wang,etal.,2DMater.2(2015)031002. [13]Y.Liu,Q.Liu,A.Zhang,etal.,ACSNano12(2018)8323–8329. [14]J.Sun,G.Zheng,H.Lee,NanoLett.14(2014)4573–4580. [15]X.Wu,Y.Xu,Y.Hu,etal.,Nat.Commun.9(2018)4573.
[16]P.Li,D.Zhang,J.Wu,Y.Cao,Z.Wu,Sensor.Actuat.B-Chem.273(2018)358– 364.
[17]I.Sultana,M.Rahman,T.Ramireddy,Y.Chen,A.Glushenkov,J.Mater.Chem.A5 (2017)23506–23512.
[18]K.Hembram,H.Jung,B.Yeo,etal.,Phys.Chem.Chem.Phys.18(2016)21391– 21397.
[19]B.Anasori,M.Lukatskaya,Y.Gogotsi,Nat.Rev.Mater.2(2017)16098. [20]D.Er,J.Li,M.Naguib,Y.Gogotsi,V.Shenoy,ACSAppl.Mater.Interfaces6(2014)
11173–11179.
[21]M.Lukatskaya,S.Kota,Z.Lin,etal.,Nat.Energy2(2017)17105. [22]Y.Xia,T.S.Mathis,M.Zhao,etal.,Nature557(2018)409–412.
[23]P.Urbankowski,B.Anasori,T.Makaryan,etal.,Nanoscale8(2016)11385– 11391.
[24]M.Li,J.Lu,K.Luo,etal.,J.Am.Chem.Soc.141(2019)4730–4737. [25]Y.Xie,M.Naguib,V.N.Mochalin,etal.,J.Am.Chem.Soc. 136(2014)6385–6394.
[38]J.E.tenElshof,H.Yuan,P.GonzalezRodriguez,Adv.EnergyMater.6(2016) 1600355.
[39]H.Tan,W.Sun,L.Wang,Q.Yan,Chem.NanoMat.2(2016)562–577. [40]J.Mei,T.Liao,L.Kou,Z.Sun,Adv.Mater.29(2017)1700176. [41]J.Kang,S.Paek,J.Choy,Chem.Commun.48(2012)458–460. [42]Q.Wu,J.Xu,X.Yang,etal.,Adv.EnergyMater.5(2015)1401756. [43]T.Yamaki,K.Asai,Langmuir17(2001)2564–2567.
[44]N.Li,G.Zhou,F.Li,L.Wen,H.Cheng,Adv.Funct.Mater.23(2013)5429– 5435.
[45]Y.Wang,Y.Zhang,D.Dubbink,J.E.tenElshof,NanoEnergy49(2018)481–488. [46]S.Kim,I.Kim,S.Patil,etal.,Chem.Eur.J.20(2014)5132–5140.
[47]J.E.tenElshof,Y.Wang,SmallMethods3(2019)1800318. [48]X.Duan,J.Xu,Z.Wei,etal.,SmallMethods1(2017)1700156. [49]J.Yoo,K.Balakrishnan,J.Huang,NanoLett.11(2011)1423–1427. [50]X.Xie,T.Makaryan,M.Zhao,etal.,Adv.EnergyMater.6(2016)1502161. [51]Z.Zhang,C.Lee,W.Zhang,Adv.EnergyMater.7(2017)170678. [52]J.Zhu,K.Sakaushi,G.Clavel,J.Am.Chem.Soc.137(2015)5480–5485. [53]B.Li,S.Li,J.Liu,B.Wang,S.Yang,NanoLett.15(2015)3073–3079. [54]G.Wang,J.Zhang,S.Yang,etal.,Adv.EnergyMater.8(2018)1702254. [55]S.Liu,Y.Liu,W.Lei,etal.,J.Mater.Chem.A6(2018)20267–20276.
[26]M.Zhao,X.Xie,C.Ren,etal.,Adv.Mater.29(2017)1702410. [27]X.Wang,T.Mathis,K.Li,etal.,Nat.Energy4(2019)241–248. [28]A.Cote,A.Benin,N.Ockwig,etal.,Science310(2005)1166–1170. [29]B.Zhang,H.Mao,R.Matheu,etal.,J.Am.Chem.Soc.141(2019)11420–
11424.
[30]P.Peng,Z.Zhou,J.Guo,Z.Xiang,ACSEnergyLett.2(2017)1308–1314. [31]Z.Xiang,Y.Xue,D.Cao,etal.,Angew.Chem.Int.Ed.53(2014)2433–2437. [32]X.Wang,M.Swihart,G.Wu,Nat.Catal.2(2019)578–589.
[33]J.Li,M.Chen,D.Cullen,etal.,Nat.Catal.1(2018)935–945. [34]L.Wang,C.Zeng,H.Xu,etal.,Chem.Sci.10(2019)1023–1028. [35]P.Peng,L.Shi,F.Huo,etal.,ACSNano13(2019)878–884.
[36]J.Guo,C.Lin,Z.Xia,Z.Xiang,Angew.Chem.Int.Ed.57(2018)12567– 12572.