ContentslistsavailableatScienceDirect
Optik
j o ur na l h o m e p a g e :w w w . e l s e v i e r . d e / i j l e o
W
doped
SnO
2
growth
via
sol–gel
routes
and
characterization:
Nanocubes
Eyüp
Fahri
Keskenler
a,∗,
Güven
Turgut
b,
Serdar
Aydın
b,
Seydi
Do˘gan
caRecepTayyipErdo˘ganUniversity,FacultyofEngineering,DepartmentofNanotechnology,53100Rize,Turkey
bAtatürkUniversity,KazımKarabekirEducationFaculty,DepartmentofPhysics,25240Erzurum,Turkey
cDepartmentofElectricalandElectronicsEngineering,FacultyofEngineeringandArchitecture,BalikesirUniversity,Balikesir10145,Turkey
a
r
t
i
c
l
e
i
n
f
o
Articlehistory: Received18September2012 Accepted15February2013 Keywords: SnO2 W-doping Nanocube Sol–gel Cubicphasea
b
s
t
r
a
c
t
TheeffectsofWdopingonthecharacteristicalpropertiesofSnO2thinfilmspreparedbysol–gelspin coatingmethodwereinvestigated.TheSnO2thinfilmsweredepositedatvariousWdopingratiosand characterizedbyvariousmeasurements.XRDstudiesindicatedthattheundopedandWdopedSnO2films hadcubicandtetragonalphases.TheSEMimagesofWTOthinfilmsshowedcubicshapednanocubes correspondingtocubicphaseandthesmallerparticlescorrespondingtotetragonalphasewereformed onthefilmsurfaces,andtheirdistributionsandsizesweredependentontheWdopingratio.EDX spec-troscopyanalysesshowedthatthecalculatedandparticipatedatomicratiosofW/(W+Sn)(at.%)inthe startingsolutionandintheWTOthinfilmswerealmostclose.Itwasfoundthatthesheetresistance dependedonWdopingratioand2.0at.%WdopedSnO2(WTO)exhibitedlowestvalueofsheetresistance (7.11×103/cm2).
© 2013 Elsevier GmbH. All rights reserved.
1. Introduction
Tinoxide(SnO2)hasvarious applicationareas[1] duetoits
uniquepropertiessuchaslow electrical resistivity,highoptical transmittanceinthevisibleregion,highinfraredreflectivity, chem-icallyinertandmechanicallyhard[2–5].SomepropertiesofSnO2
thinfilmscanbeimprovedbysuitabledopantelementssuchas antimony(Sb),fluorine(F),vanadium(V),andtungsten(W).Among thesedopants,tungstenhasoxidationstatesapttoW6+ionstate,
andtheradiusofW6+isclosetothatofSn4+(W6+:67pm,Sn4+:
71pm),which makeiteasytoreplacetheSn4+ions.Therefore,
tungsten-dopedtin oxidemaybe expectedtohave a potential prospect[6].
Undopedand dopedSnO2 thinfilmshave beenpreparedby
variousexperimentaltechniquessuchaselectrochemical deposi-tion[7],hydrothermalmethod[8],polymerizing-complexingand sol–gel[9]techniques.However,tothebestofourknowledge,the fabricationofWdopedSnO2thinfilmshavenotbeenreportedup
tonowbysol–gelspincoatingmethod.Therefore,inthisstudy,we aimedtoinvestigatetheeffectofWdopingonstructural, morpho-logical,opticalandelectricalpropertiesofSnO2thinfilmsprepared
bysol–gelspincoatingmethod.
∗ Correspondingauthor.Tel.:+9004642236126x1764;fax:+9005376104849.
E-mailaddress:keskenler@gmail.com(E.F.Keskenler).
2. Experimental
Inthepresentstudy,W-dopedtinoxide(WTO)thinfilmswere preparedbysol–gelspincoatingmethodonglasssubstrateusinga solpreparedwithstannouschloridedihydrate(SnCl2·2H2O),
tung-stenhexachloride(WCl6),monoethanolamine(C2H7NO,MEA)and
2-methoxyethanol(C3H8O2,2-MTE),asstartingmaterial,dopant
source, stabilizer, and solvent, respectively. The molar ratio of MEAtometalsaltswasmaintainedat1:1inallsolutions.Various amountsofthestannouschloridedihydrateandtugsten hexachlo-ridewerecombinedtoachievedifferentW/W+Snatomicratios changingfrom1.0at.%to4.0at.%with1.0at.%step.Theprecursor solwasstirredat80◦Cfor24hinatightlyclosedflasktoobtain aclearandhomogenoussolution.Theglasssubstratesfirstlywere keptinboilingchromicacidsolutionandthentheywererinsed withdeionized water. Finally,they werecleaned withacetone, methanolanddeionizedwaterbyusinganultrasoniccleanerand driedwithnitrogen.Theresultantsolutionbeingdroppedonglass substratewasrotatedataspeedof3000rpmfor30sbyusinga spin-coater.Aftertheglasssubstrateswerecoated,theyweresinteredat 200◦Cfor5mintoevaporatesolventandremovetheorganic sed-imentsandthenspontaneouslycooledtoroomtemperature.This procedurewasrepeatedfor4timesandfinally,thesampleswere annealedinairat450◦Cfor30min.
ThestructuralcharacterizationoftheWTOthinfilmswas car-riedoutbyX-raydiffraction(XRD)measurementsusingaRigaku MiniflexIIdiffractometerwithCuK␣radiation(=1.5418 ˚A).The diffractometerreflections weretaken atroom temperatureand thevaluesof2werealteredbetween15◦ and80◦. Morpholog-icalpropertiesoftheW-dopedSnO2thinfilmsweredetermined
0030-4026/$–seefrontmatter © 2013 Elsevier GmbH. All rights reserved.
Fig.1.XRDspectraforundopedandWdopedSnO2thinfilms.
withJeolNano-SEM.Theopticaltransmittanceofthesampleswas recordedinspectralregionof300–1000nmat300KusingaUV-Vis spectrophotometer(Perkin-Elmer,Lambda40)whichworksinthe rangeof200–1100nm.Thesheetresistancevaluesoffilmswere measuredbymeansoffourpointprobetechnique.
3. Resultsanddiscussion 3.1. X-raydiffractionresults
ThecrystalstructureofWTOthinfilmswasinvestigatedby X-raydiffraction(XRD)patterns.Fig.1showsXRDspectraofWTOthin films.Thesespectraindicatethatthesampleshave(111)plane cor-respondingtoSnO2cubicphase(JPDS50-1429)and(110),(101)
planescorrespondingtoSnO2 tetragonalrutilephase (JPDS
41-1445).Noadditionalpeakwhichimpliesoxidesoftungstenwere notobserved.AsseeninFig.1,thestrongestorientationis(111) lineofcubicstructureand(111)peakintensityvalueofundoped samplehasdecreasedcontinuouslywithincreasingWdopant con-tent.ItcaneasilybeconcludedthatthecrystallineofWTOthin filmsarebeingdeterioratedbyincreasedWcontent.
AlthoughSnO2 crystallizeinthetetragonalrutilecrystal
sys-tem,therearealsoorthorhombicandcubicphasesofSnO2.Asa
mineral,SnO2beingformedattetragonalrutilephaseisalsocalled
Cassiterite[10].Suitoetal.[11]reportedthephasetransitionfrom tetragonaltoorthrombicstructure.Shieh[12],HainesandLegér [13]observedSnO2 cubic phase.Phasetransformations ofSnO2
haveusuallybeenstudiedunderhighpressure.Jiangetal.[14]have foundfluoritecubicphasewithFm3mspacegroupabove18GPa pressure,andOnoetal.[15]haveobservedpeaksof(111),(200), (220),(222)belongingtothecubicstructure underhigh pres-sureandtemperature(about23GPaand1000K).Inrecentyears, cubicandotherphaseshavebeenreportedfromtheexperiments studiesbasedonthesolutionsperformedatatmosphericpressure [16–18].CubicphaseforSnO2thinfilmspreparedbyreactiveradio
frequencymagnetronsputteringwithdifferentsputteringpower (about>100W)havebeenreportedbytheSongetal.[19].
Inthisstudy,SnO2cubicstructurehasbeenobtainedat
atmo-sphericpressure,andtothebestourknowledge,thisisthefirst result obtainedfor SnO2 films grownby thesol gel technique.
Intheliterature,ethanole[20,21],1-propylalcohol[22],mixture ofwaterand alcohol[23,24]aregenerallyusedasasolventfor preparation of SnO2 films via sol–gel route. Huang et al. [25]
havesynthesizedWdopedSnO2 thinfilmfromsol–gelsolution
preparedby mixinga weighed quantityofSnCl2·2H2Owithan
ethanol/water,WCl6solutedinmixture.Thereasonforobtaining
thecubic structureinthis studymay,atfirst,betheusageofa solpreparedwithstannouschloridedihydrate(SnCl2·2H2O),
tung-stenhexachloride(WCl6),monoethanolamine(C2H7NO,MEA)and
2-methoxyethanol(C3H8O2),asstartingmaterial,dopantsource,
stabilizerandsolvent,respectively.
Forthesamples,theobserved‘d’valueswhicharethe inter-planerdistances are presented in Table1 and thesevalues are comparedwiththestandardonesfromtheJPDS50-1429datafiles. Thelatticeconstant‘a’forcubicstructureisdeterminedbyrelation [26]. 1 d2 =
h2+k2+l2 a2 (1) where(hkl)ismillerindices.Thecalculatedandstandardlattice constantsarealsogiveninTable1.Thecalculated‘a’valuesagree withJPCDScardno:50-1429(a=4.87 ˚A).AscanbeseeninTable1, thelatticeconstantvalueforundopedsampleis4.8745 ˚A.Thisvalue decreaseswithWdopingupto2.0at.%,andthenitincreases con-tinuouslywiththeWdopingconcentrationinthefilms.Thiscan beexplainedifitisconsideredthat:Whasmanyoxidationstates suchas+6,+5,+4,+3,+2[27,28]andwithdecreasingtheoxidation numberofW,itsionicradiiincreases[28,29].Atthelowdoping levels,W6+presumablysubstituteswiththeSn4+andcauseslat-ticeconstantdecrease.WiththeincreasingofWdopinglevelin SnO2lattice,W5,4,3,2+oxidationstatesalsosubstitutetoSn4+and
havingincreaseinlatticeconstant.Similarly,inearlierstudies,it wasfoundthatsomeoftheSn4+ionsinthelatticewerereplaced
bySb5+atlowdopinglevel,howeverSb3+substitutedtoSn4+at
highdopinglevel[20]. 3.2. SEMandEDXresults
ThecompositionofWTOthinfilmswasdeterminedbyenergy dispersiveX-rayspectroscopy(EDX).EDXspectraofWTOthinfilms andthecompositionofelementsinSnO2structure aretogether
giveninFig.2.ThesespectraclearlyconfirmtheexistenceofSn andWelementsintheWTOthinfilms.TheSi,Na,MgandCa
ele-Table1
Thestructural,electricalandopticalvaluesofundopedandWTOthinfilms.
Sample Cubic(hkl) Cubic-dst.(Å) Cubic-dobs.(Å) Cubic-a(Å) Rs(×103/cm2) Eg(eV)
UndopedSnO2 (111) 2.8120 2.8143 4.8745 48.22 4.105
1.0at.%WdopedSnO2 (111) 2.8120 2.8140 4.8739 12.96 4.112
2.0at.%WdopedSnO2 (111) 2.8120 2.8236 4.8626 7.11 4.115
3.0at.%WdopedSnO2 (111) 2.8120 2.8146 4.8750 8.24 4.099
Fig.2.EnergydispersivespectroscopyanalysisofWdopedSnO2thinfilms:(a) undoped,(b)1.0at.%Wdoped,(c)2.0at.%Wdoped,(d)3.0at.%Wdoped,(e)4.0at.% Wdoped,(f)elementalconcentrationsinthefilmwithdifferentWdopinglevelsin SnO2lattice.
ments,insolidfilms,areresultedfromtheglasssubstrates.EDX
analysesshowthatthecalculatedandparticipatedatomicratiosof
W/(W+Sn)(at.%)inthestartingsolutionandintheWTOthinfilms
arealmostclose.Theseresultsconfirmthereliabilityofthesol–gel
spincoatingmethodusedinexperiments.Thescanningelectron
microscopy(SEM)imagesofWTOsthinfilmsgiveninFig.3.Itcan
beseenthatthecubicshapednanocubesareformedonsurfaces ofthefilms,andtheirdistributionsandsizesofnanocubesdepend ontheWdopingratio.Fortheundopedsample(Fig.3a),thesizes ofcubicnanoshapevarybetween300and400nm.Forthe1.0at.% WdopedSnO2 (Fig.3b),thesizesofnanocubesdecreasetothe
valueofabout250–350nm.AscanbeseenfromFig.3c,thesizes ofnanocubessharplydecreasetoabout70nmforthe2.0at.%W dopedSnO2anddistributionofnanocubesismorearranged
com-paredtoundopedand1.0at.%WdopedSnO2.Above2.0at.%W
dopinglevel(Fig.3dande),thesizesofnanocubesincreasesharply toabout200–250nmandthefilmsurfaceconsistoflotof non-uniformeddistortednanocubeshapes.Also,fortheallsamples,it shouldbenotedthatthesenanocubescanbeformedbyan aggre-gationofsmallparticlesobservedonglasssubstrates.Theseresults areinharmonywithtendencyoflatticeconstant‘a’calculatedfrom XRDresultsfortheWTOthinfilms.ThesimilarstructuresofSnO2
cubicphaseandcubicshapewereobtainedforthefilmsgrownby hydrothermalmethod[8].
3.3. Electricalandopticalproperties
Electricalpropertiesofthefilmswereinvestigatedbyfourpoint probemethod.AscanbeseeninTable1,there isadecreasein thesheetresistancevaluesupto2.0at.%Wdopinglevels,thenit increaseswithW-dopantconcentrationincrease.Thevariationin thesheetresistanceofSnO2withWdopingcanbeexplainedon
thebasisofthepresenceofdifferentvalancestateofWelement. WhenitisdopedwithW,someoftheSn4+ionsinthelatticecan
Fig.3. SEMimagesundopedandWdopedSnO2thinfilms:(a)undoped,(b)1.0at.%
Wdoped,(c)2.0at.%Wdoped,(d)3.0at.%Wdoped,(e)4.0at.%Wdoped.
bereplacedbyW6+,resultingthesheetresistance[6,25,30].Hence,
areductioninthesheetresistanceisobserveduntiltheWdoping levelreaches2.0at.%.Beyond2.0at.%ofWdoping,apartoftheW6+
ionsarereducedtothelowvalancestatessuchasW4+,W3+,W2+,
resultingintheformationofacceptorstatesandalossofcarriers. Thusanincreasingisobservedatsheetresistance.Inearlierstudies, itwasfoundthat3.0at.%Wdopingreducedthesheetresistanceof SnO2 andWatomswerefullyoxidizedtothevalenceof6+,and
mostofW6+wereincorporatedinsidetheSnO
2 structureatlow
dopingratiofromXPSstudy[6,25,30].
TheopticalpropertiesofWTOthinfilmswereinvestigatedby usingUV-Visspectrophotometer.Transmittancespectraaregiven in Fig. 4. As can be seen, the transmittance values are varied
Fig.5.Thevariationof(˛h)2vs.hforundopedandWdopedSnO
2thinfilms.
between60 and75%invisible region.It isquiteclearfromthe transmittancespectrathattransparencyhasslightlychangedwith Wdoping.Theanalysisofthedependenceofabsorptioncoefficient versusphotonenergyinthehighabsorptionregionsiscarriedout toobtainmoredetailedinformationabouttheenergybandgaps. Theabsorptioncoefficient(˛)isdeterminedbytheequation[31]; ˛= ln(1/T)
d (2)
whereTistransmissionanddisfilmthickness.Theopticalband gapofWTOsisobtainedbyfollowingrelation[32];
˛h=A(h−Eg)1/2 (3)
wherehandAarephotonenergyandtheconstant,respectively.Eg
valuesweredeterminedbyplotting(˛h)2vs.handextrapolating
ofthelinearregionoftheplottozeroabsorption((˛h)2=0).The
bandgapvaluesofundoped,1.0,2.0,3.0and4.0at.%WdopedSnO2
thinfilmswerefoundas4.105,4.112,4.115,4.099,4.097eV, respec-tively.ItisclearlyseeninFig.5thattheincreasingWcontentin theSnO2structuresupto2.0at.%,thebandgapvaluesincreaseand
thencontinuouslydecreasewithfurtherincreasingWdopinglevel. ThereasonforincreasingbandgapwithWcontentmayprobably beexplainedasfollows;SnO2isoneofdegeneratesemiconductors
[10],whichtheFermilevellieswithintheconductionband[27]. Thus,theopticalbandgapsarerelatedtotheexcitationofthe elec-tronsfromthevalancebandtoFermilevels[33,34].Thismeans thatFermilevelisliftedsomemoreintotheconductionbandofthe degeneratesemiconductorduetotheincreaseinthecarrier den-sity.Thisleadstotheenergybandbroadening(shifting)andsomeof theSn4+ionsinthelatticearereplacedbyW6+(orW5+),andthisis
calledMoss–Bursteineffect[35].Adecreaseintheenergybandgaps beyond2.0at.%WdopingcanbecausedthatapartoftheW6+ions
isreducedtolowervalancestatesofWlikeW4+,W3+,W2+,which
canresultintheformationofdefects,impuritiesorcompletelynot substitutionofdopantwithhostatomsorinterstitialandlattice strain[36–39].Thecalculatedlatticeconstantvaluessupportthat W6+arebeingreplacedwithSn4+atlowdopingcontents(for1.0
and2.0at.%). 4. Conclusions
Thisstudypresentscubicphasebeingobtainedforthefirsttime forWdopedSnO2thinfilmsgrownbysol–gelspincoating,using
methanolamine,2-methoxyethanol,stannouschloridedihydrate, andtungstenhexachloridebasedonprecursorsolution.XRD stud-iesindicatethattheundopedandWdopedSnO2 havegrownat
cubicandtetragonalphases.EDXanalysesshowthatthecalculated andparticipatedatomicratiosofW/(W+Sn)(at.%)inthestarting solutionandintheWTOthinfilmsarealmostclose.TheSEMimages
ofWTOsthinfilmsshowedthatthevariousdistributedandsized cubicshapednanocubeswereformedonthesurfacesofthefilms, dependingonWdopingratio.Allresultshadshowedthat2.0at.% WdopedSnO2filmhadthebestoptoelectronicproperty.Thus,the
resultsofthis studyindicatethatthestructural,morphological, electrical,andopticalpropertiesoftheSnO2thinfilmsprepared
bysol–gelmethodcanbestronglyaffectedbytheincorporationof WelementsinSnO2thinfilmsandWTOthinfilmscanbeusefulfor
microandnano-sizedoptoelectronicdeviceapplications.
References
[1]D.Jadsadapattarakul,C.Euvananont,C.Thanachayanont,J.Nukeaw,T.Sooknoi, Tinoxidethinfilmsdepositedbyultrasonicspraypyrolysis,Ceram.Int.34 (2008)1051–1054.
[2]E.Elangovan,S.A.Shivashankar,K.Ramamurthi,Studiesonstructuraland elec-tricalpropertiesofsprayedSnO2:Sbfilms,J.Cryst.Growth276(2005)215–221.
[3]K.S.Kim,S.Y.Yoon,W.J.Lee,K.H.Kim,Surfacemorphologiesandelectrical propertiesofantimony-dopedtinoxidefilmsdepositedbyplasma-enhanced chemicalvapordeposition,Surf.Coat.Technol.138(2001)229–236.
[4]S.Chacko,N.S.Philip,K.G.Gopchandran,P.Koshy,V.K.Vaidyan,Nanostructural andsurfacemorphologicalevolutionofchemicallysprayedSnO2thinfilms,
Appl.Surf.Chem.254(2008)2179–2186.
[5]E.Elangovan,M.P.Singh,K.Ramamurthi,Studiesonstructuralandelectrical propertiesofspraydepositedSnO2:Fthinfilmsasafunctionoffilmthickness,
Mater.Sci.Eng.B113(2004)143–148.
[6]Y.Huang,Q.Zhan,G.Li,Transparentconductivetungsten-dopedtinoxide polycrystallinefilmspreparedonquartzsubstrates,Semicond.Sci.Technol. 24(2009),015003-5.
[7]M.Lai,J.H.Lim,S.Mubeen,Y.Rheem,A.Mulchandani,M.A.Deshusses,N.V. Myung,Size-controlledelectrochemicalsynthesisandpropertiesofSnO2
nano-tubes,Nanotechnology20(2009),185602-6.
[8]L.Shi,K.Bao,J.Cao,Y.Qian,ControlledfabricationofSnO2solidand
hol-lownanocubeswithasimplehydrothermalroute,Appl.Phys.Lett.93(2008) 152511.
[9]M.Bagheri-Mohagheghi, N.Shahtahmasebi,M.R. Alinejad,A.Youssefi, M. Shokooh-Sarem,Theeffectofthepost-annealingtemperatureonthe nano-structureandenergybandgapofSno2semiconductingoxidenano-particles
synthesizedbypolymerizing-complexingsol–gelmethod,PhysicaB403(2008) 2431–2437.
[10]M.Batzill,U.Diebold,Thesurfaceandmaterialsscienceoftinoxide,Prog.Surf. Sci.79(2005)47–154.
[11]K.Suito,N.Kawai,Y.Masuda,HighpressuresynthesisoforthorhombicSnO2,
Mater.Res.Bull.10(1975)677–680.
[12]A.R.Shien,High-pressurephasesinSnO2to117GPa,Phys.Rev.B73(2006),
014105-7.
[13]J.Haines,J.M.Legér,X-raydiffractionstudyofthephasetransitionsand struc-turalevolutionoftindioxideathighpressure:relationshipsbetweenstructure typesandimplicationsforotherrutile-typedioxides,Phys.Rev.B55(1997) 1144–1154.
[14]J.Z.Jiang,L.Gerward,J.S.Olsen,Pressureinducedphasetransformationin nanocrystalSnO2,Scr.Mater.44(2001)1983–1986.
[15]S.Ono,E.Ito,T.Katsura,A.Yoneda,M.J.Walter,S.Urakawa,W.Utsumi,K. Funakoshi,Thermoelasticpropertiesofhigh-pressurephaseofSnO2
deter-minedbyinsituX-rayobservationsupto30GPaand1400K,Phys.Chem.Miner. 27(2000)618–622.
[16]P.S.Patil,R.K.Kawar,S.B.Sadale,P.S.Chigare,Propertiesofspraydepositedtin oxidethinfilmsderivedfromtri-n-butyltinacetate,ThinSolidFilms437(2003) 34–44.
[17]C.Agashe,R.C.Aiyer,High-yieldsynthesisofnanocrystallinetindioxideby thermaldecompositionforuseingassensors,Int.J.Appl.Ceram.Technol.5 (2008)181–187.
[18]B.Hariprakash,A.U.Mane,S.K.Martha,S.A.Gaffoor,S.A.Shivashankar,A.K. Shukla,Alow-cost,highenergy-densitylead-acidbattery,Electrochem.Solid StateLett.7(2004)A66–A69.
[19]J. Song,M.Z.Cai, Q.F.Dong,M.S. Zhen,Q.H.Wu,S.T. Wu,Structuraland electrochemicalcharacterizationofSnOxthinfilmsforLi-ionmicrobattery,
Electrochim.Acta54(2009)2748–2753.
[20]C.Terrier,J.P.Chatelon,J.A.Roger,R.Berjoan,C.Dubois,Analysisofantimony dopingintinoxidethinfilmsobtainedbythesol–gelmethod,J.Sol–GelSci. Technol.10(1997)75–81.
[21]Y.J.Lin,C.J.Wu,Thepropertiesofantimony-dopedtinoxidethinfilmsfromthe sol–gelprocess,Surf.Coat.Technol.88(1997)239–247.
[22]M.Izerrouken,S.Kermadi,N.Souami,A.Sari,M.Boumaour,Influenceofreactor neutronsirradiationonelectrical,opticalandstructuralpropertiesofSnO2film
preparedbysol–gelmethod,Nucl.Instrum.MethodsA611(2009)14–17.
[23]Y.Xiao,S.Ge,L.Xi,Y.Zuo,X.Zhou,B.Zhang,L.Zhang,C.Li,X.Han,Z.Wen, RoomtemperatureferromagnetismofMn-dopedSnO2thinfilmsfabricatedby
sol–gelmethod,Appl.Surf.Sci.254(2008)7459–7463.
[24]L.K.Dua,A.De,S.Chakraborty,P.K.Biswas,Studyofspincoatedhighantimony contentSn–Sboxidefilmsonsilicaglass,Mater.Charact.59(2008)578–586.
[25]Y.Huang,D.Li,J.Feng,G.Li,Q.Zhang,Transparentconductivetungsten-doped tinoxidethinfilmssynthesizedbysol–geltechniqueonquartzglasssubstrates, J.Sol–GelSci.Technol.54(2010)276–281.
[26]R.J.D.Tilley,CrystalandCrystalStructures,Wiley,London,UK,2006.
[27]J.J.Lingane,L.A.Small,Polarographyofthevariousoxidationstatesoftungsten, J.Am.Chem.Soc.71(1949)973–978.
[28]E.Lassner,W.-D.Schubert,Tungsten,KluwerAcademic,NewYork,1999.
[29]N.N.Greenwood,A.Earnsha,ChemistryoftheElements,seconded.,Elseiver, Oxford,UK,1997.
[30]Y.Huang,G.Li,J.Feng,Q.Zhang,Investigationonstructural,electricaland opticalpropertiesoftungsten-dopedtinoxidethinfilms,ThinSolidFilms518 (2010)1892–1896.
[31]T.Serin,N.Serin,S.Karadeniz,H.Sarı,N.Tu˘gluo˘glu,O.Pakma,Electrical, struc-turalandopticalpropertiesofSnO2thinfilmspreparedbyspraypyrolysis,J.
Non-Cryst.Solids352(2006)209–215.
[32]J.Tauc,R.Grigorovici,A.Vancu,Opticalpropertiesandelectronicstructureof amorphousgermanium,Phys.StatusSolidi(b)15(1966)627–637.
[33]A.R.Babar,S.S.Shinde,A.V.Moholkar,C.H.Bhosale,J.H.Kim,K.Y.Rajpure, Struc-turalandoptoelectronicpropertiesofantimonyincorporatedtinoxidethin films,J.AlloysCompd.505(2010)416–422.
[34]A.R.Babar,S.S.Shinde,A.V.Moholkar,C.H.Bhosale,J.H.Kim,K.Y.Rajpure, Sensingpropertiesofsprayedantimonydopedtinoxidethinfilms:solution molarity,J.AlloysCompd.509(2011)3108–3115.
[35]E.Burstein,AnomalousopticalabsorptionlimitinInSb,Phys.Rev.93(1954) 632–633.
[36]F.Yakuphanoglu,Y.Caglar,S.Ilican,M.Caglar,Theeffectsoffluorineonthe structural,surfacemorphologyandopticalpropertiesofZnOthinfilms,Physica B394(2007)86–92.
[37]M.Tomakin,M.Altunbas,E.Bacaksız,I.Polat,Preparationand characteriza-tionofnewwindowmaterialCdSthinfilmsatlowsubstratetemperature (<300K)withvacuumdeposition,Mater.Sci.Semicond.Process.14(2011) 120–127.
[38]L.B.Freund,S.Suresh,ThinFilmMaterials:Stress,DefectFormationandSurface Evolution,CambridgeUniversityPress,Cambridge,2003,pp.192.
[39]Y.H.Lee,W.J.Lee,Y.S.Kwon,G.Y.Yeom,J.K.Yoon,EffectsofCdSsubstrates onthephysicalpropertiesofpolycrystallineCdTefilms,ThinSolidFilms341 (1999)172–175.