Thorium effect on the oxidation of uranium: Photoelectron spectroscopy (XPS/UPS) and
cyclic voltammetry (CV) investigation on (U1 − xThx)O2 (x = 0 to 1) thin films
Cakir, P.; Eloirdi, R; Huber, F.; Konings, R. J.M.; Gouder, T
DOI
10.1016/j.apsusc.2016.10.010
Publication date
2017
Document Version
Final published version
Published in
Applied Surface Science
Citation (APA)
Cakir, P., Eloirdi, R., Huber, F., Konings, R. J. M., & Gouder, T. (2017). Thorium effect on the oxidation of
uranium: Photoelectron spectroscopy (XPS/UPS) and cyclic voltammetry (CV) investigation on (U1 −
xThx)O2 (x = 0 to 1) thin films. Applied Surface Science, 393, 204-211.
https://doi.org/10.1016/j.apsusc.2016.10.010
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ContentslistsavailableatScienceDirect
Applied
Surface
Science
j o u r n a l ho me p ag e :w w w . e l s e v i e r . c o m / l o c a t e / a p s u s c
Full
Length
Article
Thorium
effect
on
the
oxidation
of
uranium:
Photoelectron
spectroscopy
(XPS/UPS)
and
cyclic
voltammetry
(CV)
investigation
on
(U
1
−
x
Th
x
)O
2
(x
=
0
to
1)
thin
films
P.
Cakir
a,b,∗,
R.
Eloirdi
a,
F.
Huber
a,
R.J.M.
Konings
a,b,
T.
Gouder
aaEuropeanCommission,JointResearchCentre,P.O.Box2340,D-76125,Karlsruhe,Germany
bDepartmentofRadiationScienceandTechnology,DelftUniversityofTechnology,Mekelweg15,2629,JBDelft,TheNetherlands
a
r
t
i
c
l
e
i
n
f
o
Articlehistory:
Received17August2016 Receivedinrevisedform 27September2016 Accepted3October2016 Availableonline4October2016 Keywords: Thinfilm Mixedoxide Electrochemistry Corrosion Actinideoxide
a
b
s
t
r
a
c
t
ThinfilmsofU1−xThxO2(x=0to1)havebeendepositedviareactiveDCsputtertechniqueand
charac-terizedbyX-ray/Ultra-violetPhotoelectronSpectroscopy(XPS/UPS),X-rayPowderDiffractometer(XRD) andCyclicVoltammetry(CV)inordertounderstandtheeffectofThoriumontheoxidationmechanism. Duringthedeposition,thecompetitionbetweenuraniumandthoriumforoxidationshowedthat tho-riumhasamuchhigheraffinityforoxygen.Depositionconditions,timeandtemperaturewerealsothe subjectofthisstudy,tolookatthehomogeneityandthestabilityofthefilms.Whilecoreleveland valencebandspectrawerenotalteredbythetimeofdeposition,temperaturewasaffectingtheoxidation stateofuraniumandthevalencebandduetothemobilityincreaseofoxygenthroughthefilm.X-ray diffractionpatterns,corelevelspectraobtainedforU1−xThxO2versusthecompositionshowedthat
lat-ticeparametersfollowtheVegard’slawandtogetherwiththebindingenergiesofU-4fandTh-4fare ingoodagreementwithliteraturedataobtainedonbulkcompounds.Tostudytheeffectofthoriumon theoxidationofU1−xThxO2films,weusedCVexperimentsatneutralpHofaNaClsolutionincontact
withair.Theresultsindicatedthatthoriumhasaneffectontheuraniumoxidationasdemonstratedby thedecreaseofthecurrentoftheoxidationpeakofuranium.XPSmeasurementsmadebeforeandafter theCV,showedarelativeenrichmentofthoriumattheextentofuraniumatthesurfacesupportingthe formationatalongertermofathoriumprotectivelayeratthesurfaceofuranium-thoriummixedoxide. ©2016TheAuthors.PublishedbyElsevierB.V.ThisisanopenaccessarticleundertheCCBY-NC-ND license(http://creativecommons.org/licenses/by-nc-nd/4.0/).
1. Introduction
Thorium-Uranium mixed oxides are interesting nuclear fuel materials. Compared to uranium- plutonium mixed oxide, the higherthermalstabilityandmeltingtemperatureresultsinalarger margintomelting[1].TheuseofThorium-Uraniummixedoxide resultsin theproduction ofsmallerquantitiesofTransuranium elements[2].
Duringthegeologicalstorageofusednuclearfuel,the radionu-clidesembeddedintheuraniumfuelmatrix,whichareproduced duringthereactorirradiation,canbereleasedviathedissolutionof thefuelmatrix.Uraniumhastwostableoxidationstates,(IV)and (VI),andseveralmixedvalencephases(i.e.U3O7,U4O9,U3O8).The
solubilityofuraniumincreasesseveralmagnitudesasthe oxida-tionstateincreasesfromU(IV)toU(VI)inthematrix[3].Onthe
∗ Correspondingauthorat:EuropeanCommission,JointResearchCentre,P.O.Box 2340,D-76125,Karlsruhe,Germany.
E-mailaddress:pelincakir@outlook.com(P.Cakir).
otherhand,ThO2ischemicallystable,havingoneoxidationstate
(IV),anditsdissolutionisreportedtobeextremelydifficult[4]. Sincethefirst contactof thematerialwiththeenvironment happensonthesurface,ourinterestistoobservechangesandthe evolutionoftheoxidelayerformingattheinterface.Inthiswork, thinfilmsof(U, Th)mixedoxidesformedbysputter deposition technique[5]areusedinsteadofusingbulkmaterial[6–9].The useofthinfilmstosimulatethesurfaceofbulkcompoundsresults inahighflexibilityforcompositionalchanges(O/(U+Th)orU/Th ratios).Moreover,itallowsdepositionoflayersofdifferent thick-nessontovariablesubstrates,withdifferentmicrostructurewhen changingthetemperatureandgaspressureduringthedeposition. Materialssuchas uranium− thoriumoxides,aredifficultto studybyphotoelectronspectroscopy[10],which isduetotheir semiconductorpropertiesasaresultofwhichtheflowofcurrent cannotbeachievedproperlyalongthebulksamplethickness.This aspectcanbelimitedoravoidedbytheuseofthinfilmsbecause thelowthicknessresultsinalowresistanceandthevoltagedrop canbeneglected[11,12].
http://dx.doi.org/10.1016/j.apsusc.2016.10.010
0169-4332/©2016TheAuthors.PublishedbyElsevierB.V.ThisisanopenaccessarticleundertheCCBY-NC-NDlicense(http://creativecommons.org/licenses/by-nc-nd/4. 0/).
Themaingoalofthisstudyistounderstandtheeffectofthe sta-bletetravalentactinideTh(IV)ontouraniumdioxideandtofollow theelectronicstructure,oxidationstateandredoxreactionsonthe surface.
Thepaperisdividedintothreesections.Thefirstpart investi-gatestherelativeoxygenaffinitybetweenuraniumandthorium, bybringingthemintocompetition.Thesecondpartexaminesthe effectofhightemperatureandlowtemperaturedepositiononthe surfacepropertiessuchasoxygendiffusionandatomic segrega-tion.Alsoin this part,we compare U1-xThxO2 (x=0 to1) thin
filmstobulkmaterialstoconfirmtheiruseasmodel,byanalysing theirelectronicstructureandlatticeparametersversustheir com-position. The third part consists of electrochemical studies on U1-xThxO2 films(X=0 to 1). Electrochemistry, especially cyclic
voltammetry(CV)ofUO2sampleshasbeenintensivelyemployed
[13–18]howevertothebestofourknowledge,therehasbeenno CVrecordonuranium-thoriummixedoxides,probablyduetothe semiconductorproperties.TheobjectiveofthecurrentCVstudies istoexaminetheoxidationofU1-xThxO2beforeandaftertheCV
usingXPS,lookingatthecompositionandtheoxidationstate.
2. Experimental
ThethinfilmsofU1−xThxO2(x=0to1)werepreparedin-situ
bydirectcurrentreactiveco-sputteringfromthoriumanduranium metaltargetsinagasmixtureofAr(6N)andO2(6N).Theoxygen
concentrationinthefilmswasadjustedbychangingtheO2partial
pressure(10−8mbar–6×10−6mbar),whiletheArpartialpressure wasmaintainedat5×10−7mbar.Thecompositionofthefilmsis controlledbychangingtherespectivetarget voltagesfor Uand Thtarget.Thethinfilmsweredepositedontosiliconwafer(111) substrates,whichwerecleanedbyAr ionsputtering (4keV) for 1min.Theplasmainthediodesourcewasmaintainedbyinjection ofelectronsof50–100eVenergy(triodesetup),allowingworking atlowArpressureinabsenceofstabilizingmagneticfields.After deposition,thethinfilmsweretransferredtotheXPS-UPSanalysis chamberwithoutexposingthemtoair.
Photoelectronspectroscopydatawererecordedusinga hemi-sphericalanalyserfromOmicron(EA125U5).Thespectrawere taken using Mg K␣ (1253.6eV) radiation with an approximate energyresolutionof1eV.UPSmeasurementsweremadeusingHeII (40.81eV)excitationradiationproducedbyahighintensity win-dowlessUVraregasdischargesource(SPECSUVS300).Thetotal resolutioninUPSwas0.1–0.05eVforthehighresolutionscans.The backgroundpressureintheanalysischamberwas2×10−10mbar. ThespectrometerwascalibratedbyusingAu-4f7/2lineofmetalto
giveavalueat83.9eVBEandCu-2p3/2lineofmetalat932.7eV
BEforXPS,andonHeIandHeIIFermi-edgesforUPS. Photoemis-sionspectraweretakenatroomtemperature.Quantificationofthe spectrawasdoneusingCasaXPSsoftware(version2.3.13Dev50).As RelativeSensitivityFactors,Scofieldcross-sectionsforMg-K␣ radi-ation[19]weretaken.Anexampleofpeaksdeconvolutionwiththe CasaXPSsoftwareisreportedinFig.1.
Fortheelectrochemicalstudy,astandard3-electrodesetupwas usedwithaworkingelectrodecomposedofU1−xThxO2 (x=0.00,
0.10,0.44,0.84,1.00)thinfilmsdepositedontogoldfoilsurface; thereferenceelectrodewasanAg/AgCl(3MKCl)electrode and aPtwireascounterelectrode.Goldfoilswerefirstcleanedwith Ethanol/1NH2SO4/H2Othen heatedtill300◦C underultra-high
vacuum(UHV).Asadhesionlayer,aninterfacecomposedofa(U,Th) metallayerwasdepositedat300◦Cbetweenthegoldfoilandthe U1-xThxO2film.AllpotentialvaluesinthispaperareversusAg/AgCl.
Themeasurementswerecarriedoutwithastationaryelectrodein anunstirredsolution.Theelectrolytewasa0.01MNaClsolution atneutralpHincontactwithair.Experimentswerecarriedout atroomtemperature(22±3◦C)inaclosedTeflonelectrochemical
Table1
Bindingenergyof4f5/2corelevelpeakforThmetal,Umetal,ThO2andUO2.
Substance 4f5/2(eV) satellite
Thmetal 342.3[20,43] –
Umetal 388.40[44] –
ThO2 346.8[20,45] 7.3
UO2 390.95[11,46] 6.7
cellwithanelectrolytevolumeof3ml.Appliedpotentialswerenot correctedforvoltagedropbecauseofthenegligibleelectrode resis-tanceofthefilmelectrodes[11].Beforethescans,theelectrodes werepreconditionedatthemostcathodicpotentialfor5minto reduceanyhigheroxidesformedduringthetransportation.The cyclovoltammetry(CV)measurementswererecordedinpotential sweepcyclesinafirstseries(15cycles)from−1.000VAg/AgClupto
+0.600VAg/AgCl,andbackto−1.000VAg/AgClandtheninasecond
series(15cycles)from−1VAg/AgClto0.8VAg/AgClatascanrateof
0.010Vs−1.UltrapurewaterfromaMilliQ-system(>18M)was used.Chemicalswereallp.a.grade(Merck,Darmstadt).
TheX-raydiffractionanalysesweremadeona conventional Phillips PW3830 powder diffractometer with a Cu X-ray tube (40kV,30mA,K␣1=0.1540560nm).Filmsofabout360nm(1Å/s) thicknessesweredepositedat100◦ConaSi(111)wafer.The pat-ternswererecordedatroomtemperatureinastepscanmodeover a2rangeof[10–100]◦,withastepsizeof0.01◦andacounttime of5sperstep.
3. Resultsanddiscussion
3.1. Relativeoxygenaffinity
Tomeasuretherelativeoxygenaffinityofthoriumanduranium, aseriesofthinfilmsweredepositedsuccessivelybyincreasingthe oxygenpartialpressurewithalowincrementandanalysingthem in-situbyXPS.TheU-4fandTh-4fcorelevelspectraenableto inves-tigatetheoxidationofuraniumandthoriumthroughtheirbinding energy(BE)peak,theirshapeandtheirsatellites.Asreference val-ues,Table1reportsthe4f5/2BEofthoriumanduraniumpresentin
themetalandinthedioxide,aswellasthecorrespondingsatellite. Fig.2reportsU-4f5/2andTh-4f5/2corelevelspectraof(U,Th)Ox
(x<2) thin films obtained successively by co-deposition under slightincrease ofoxygenpartialpressureand (U,Th)metalfilm spectraareusedasreference(redplots).Itshouldbenotedthatthe oxygenpartialpressuresusedinthisexperimentarenotuniversal values,butvaryaccordingtotheexperimentalset-up.TheBEand thepeakshapesobtainedfor(U,Th)metalareinagreementwith thosereportedinliteratureforsingleandbulkelementofuranium andthorium[20,21].
Theinitialaddingofoxygenduringdepositionaffectsfirstthe thoriumasshownbytherelativeincreaseofthed-screenedpeak whereastheuraniumpeakkeepsconstantinshapeandinbinding energy.Thequickeroxidation ofthoriumrelativetouraniumis confirmedbythefurtherandnearlycompleteoxidationofthorium (greencurves)whileforuraniumthef-screenedpeakisstillthe mainpeak.Thissimpleexperimentdemonstratesanobviousand much strongeraffinityofoxygenforthoriumthanforuranium, asshownbytheoxidationofuraniumstartingonlyoncethorium isnearlycompletelyoxidised.Thisisinagreementwiththehigher stability(lowerGibbsenergyofformation)ofTh4+relativelytoU4+.
TheshifttolowerbindingenergyofTh-4fandU-4fpeaksistaking placeduetothedecreaseofFermi-energylinkedtochargecarrier depletion[22,23]inthesample,asreportedinapreviousstudyon ThO2[20].Itisacoherentshift,occurringforallphotoemissionlines
(includingO-1s).Thethicknessoftheoxidelayerissmallenough toallowelectronstotunnelthrough.Thisavoidsthechargingupon photoemissionandstillpermitsawell-definedFermi-level[24].
Fig.1. PeaksDeconvolutionofTh-4f5/2andU-4f5/2,withpeakspositions,FWHM,peaksareaandquantificationobtainedwithCasaXPSsoftware.
Fig.2. Th-4f7/2line(left)U-4f7/2line(right)corelevelspectraforco-deposited(U,Th)filmsversustherelativeincreaseofpartialpressureofoxygen(PO2).
3.2. Influenceofdepositionconditionsandcomparisonwithbulk data
3.2.1. Influenceofdepositiontimeandtemperatureon U0.50Th0.50O2thinfilms
Inthefollowingsection,wecomparetheeffectofdeposition timeoffilmsatroomtemperatureonthecorelevelandvalence bandspectra.Theideabehindistoinvestigatethereproducibility andthehomogeneityofthefilmsurfaceasafunctionofthefilm
thickness,goingfromatomictobulkproperties.WhileXPSprobes adepthofabout100Å,XRDislookingintoasampledepthofthe orderofam.Sinceweshowedthatthecompositionalongthe thicknessofthefilm(i.e.depositiontime)isconstant,weconsider thatthecompositionofthesurfaceisrepresentativeofthatofthe bulk.
AfilmcompositionofU0.50Th0.50O2 hasbeenchosenforthis
experimentsseries.Thedepositionrateisabout1Å/s.Fig.3shows thecorelevelspectraU-4fandTh-4f(A),thevalenceband(B)and
Fig.3. TheinfluenceofthedepositiontimeontheU-4fandTh-4fcorelevelspectra(A)andonHeIIvalencebandspectra(B)forU0.50Th0.50O2.
Fig.4. TheinfluenceofthedepositiontemperatureontheU-4fandTh-4fcorelevelspectra(A)andontheHeIIvalencebandspectra(B)foraU0.50Th0.50O2.
thecorrespondingO–1s(middle)ofU0.50Th0.50O2filmdeposited
during5minand25mincorrespondingto30and150nm, respec-tively.Thedepositionconditionswerekeptrigorously thesame despite a small differencefor theoxygen partialpressure. The Fig.3Ashowsthespin-orbitsplitsofuraniumandthorium4f5/2
and4f7/2.Thebindingenergiesof4f7/2 inuraniumandthorium
are380.3eVand334.3eVrespectively,correspondingtouranium (IV)andthorium(IV)oxidationstates.Thesatellitepeaksandthe peakpositionshavebeenextensivelystudiedinpreviouspapers bothonThO2[20]andUO2[11].Thepositionandtheintensityof
thesatellitepeaksarecharacteristicfortheoxidationstatesofthe materialsandarelinkedtothefinalstateoccupation.Thesatellite peakpositionsforU-Thmixedoxides(6.7eVforU-4f7/2and7.3eV forTh-4f7/2)arealsothoseexpectedforthe+IVoxidationstate[25]. Withintheuncertaintythequantificationofthespectrallines,using CasaXPSsoftware,doesnotindicateanyatomicsegregationatthe surfaceforbothdepositions,andthisisalsoemphasizedbythe
con-stantfullwidthathalfmaximum(FWHM)andbindingenergies. Thisshowsthestabilityofthedepositiontechnique.
TheHeIIvalencebandspectra(Fig.3B)aremoresensitiveto5f statescomparedtoHeI(notreportedhere)andduetotheshort rangeoftheemittedphotoelectrons,UPSismoresensitivetothe surfacethanXPS.Asthoriumdoesnothavea 5fstate,thepeak at1.3eVbelowEFis duetotheU-5f2.Thepeakbetween3and
9eVisattributedtoO-2pbandemission.WhileXPSspectradid notshowquantitativedifferences,UPSshowsdifferentO-2pband intensityandthusdifferentratioO-2p/U-5f,goingfrom5.7to7.0 for5.1×10−6and6.1×10−6mbarpartialoxygenpressure, respec-tively.
Withthesamegoalasthepreviousexperiments,wecompared theelectronicstructureofU0.50Th0.50O2filmspreparedwiththe
sametimeofdepositionatroomtemperatureandat390◦C.Fig.4A reportstheU-4fandTh-4fcorelevelstatesandtheO–1sspectra (insetFig.4),whileFig.4BshowsthecorrespondingHeIIvalence bandofU0.50Th0.50O2.Firstweobservedaclearsuperpositionofthe
Fig.5.LatticeparameterofU1-xThxO2filmsversusxobtainedinthisworkand
comparedtoliteraturedataobtainedonbulkcompounds(A).Th-4f7/2andU-4f7/2
BindingenergyinU1-xThxO2filmsobtainedinthisworkandcomparedtoliterature
obtainedonbulkcompounds(B).
Th-4fcorelevelpeaksforbothtemperatures,whileasmall differ-enceappearsfortheintensityoftheU-4fpeaksandfortheshapeof theirsatellites.Thisshowsthattemperaturedoesnothaveaneffect onthethoriumstatesoncethisiscompletelyoxidised,whereasit influencestheuraniumstatesduetothediffusionoftheoxygenin thefilm,leadingtofurtheroxidationofU.Thisisalsoshowninthe magnifiedsatelliteintensities(insetFig.4A)andbytheslightshift towardshigherBEobservedininsetO–1sfigure.Thecomposition ofthefilmdepositedat390◦CcouldbequantifiedasU0.51Th0.49O2
whichiswithintheuncertaintyofthetechniquesimilartothe com-positionofthefilmdepositedatroomtemperature.InFig.4B,the HeIIvalencespectrashowamaineffectofthetemperatureonthe O-2pbandwhoseintensityandFWHMdecrease,whilethe5f2peak
shiftsslightlytohigherBE.Thediffusionoftheoxygenfromthetop surfacetotheinnerofthefilmcanexplainthiseffect.
3.2.2. Electronicstructureandlatticeparameterversus compositionofU1-xThxO2filmsandbulkmaterials
Tovalidatetheuseofthinfilmsasmodel,weproceededwiththe depositionofaseriesofU1−xThxO2(x=0to1)filmsmonitoringthe
U-4fandTh-4fbindingenergiesin-situandalsothelattice param-eterversusthecompositioninex-situbyXRD.Thecorresponding datareportedinFig.5Aarecomparedtothedataobtainedonbulk samples[25–29].Thelatticeparametersobservedforourthinfilms areclosetotheonesreportedonbulksample,followingVegard’s lawexpectedforthissolidsolution.Theinterceptofthelinearfit ofourworkandofAnthonysamyetal.[25]studyforUO2are5.448
and5.465Å,respectively.Thesmallerlatticeparameterfoundfor ourfilmcanbeexplainedbythepresenceofthestressinthefilms andwiththesmallcrystallitesizeasshownbythebroadeningof theXRDpeaks[30].Anotherparameterwhichmayinfluencethe evolutionofthelatticeparameteristheoxygencontentwhich com-paredtobulkcompoundsmightbeslightlydifferentfromourfilms producedin-situ.However,XPSresultsshowedthatthefilmsare stoichiometric.
Fig.5BshowstheBEofU-4f7/2andtheTh-4f7/2inU1−xThxO2
(x=0to1)versusthecompositionsandcompareswiththedata obtainedon bulk samples [25,31]. Vael et al. [32] pointed out thatthebindingenergyofU-4f7/2forU(IV)rangesfrom379.9to
380.9eV.Ourresultsstayinthereportedrangewhichshowsthat UandThmixedoxidearestoichiometric.Bindingenergiesof Th-4f7/2arealsostableina0.6eVrangeandinagoodagreementwith
Fig.6. CyclicvoltammetryonU1-xThxO2(x=0,0.10,0.44,0.84,1)filmsforthefırst
twocycles.
dataobtainedbyAllenetal.[31]butdifferentby1eVrelativelyto theonereportedbyAnthonysamyetal.[25].
Tosummarize,U1−xThxO2(x=0to1)mixedoxidesfilmsfollow
Vegard’slawandthebindingenergiesareingoodrelationwiththe onesobtainedforbulkmaterials.Itisapparentfromtheseresults thatourthinfilmscanbeusedasmodelforactinideoxidebulk samples,despitethemicrostructurewhichcanbedifferent(stress, preferentialorientation,...).
3.3. Electrochemicalstudies
Manystudieshavebeenreportedonchemical,physical proper-tiesandleachingexperimentsof(U,Th)mixedoxides[6,9,33,34]. Sunderetal.[9]showedthattheoxidationprocesstakingplace atthesurfaceof(U,Th)mixedoxidesamplesaresimilartopure UO2.However,comparedtoUO2theleachingexperimentsshowed
thatthedecreaseoftheuraniumdissolutionrateandthishasbeen linkedtotheloweruraniumcontentpresentinmixedoxideandin contactwithsolution.Thisstatementhasbeensupportedby Heis-bourgetal.[6,33]whostudiedthekineticsofdissolutionof(U,Th) mixedoxidesboththorium-anduranium-richsamples.Also,XPS analysesofsamplesobtainedafterleachingexperiment demon-strateasurface enrichedin thorium,formingaprotective layer disablingfurtherdissolutionoftheuranium[6].Demkowiczetal. [34]alsoreportedthattheuraniumdissolutionrateinfresh sam-plesof(U,Th)O2 was10to40timeslowerthanforconventional
UO2fuel.
Thuscompared topureUO2,thereisa clearindicationfor a
lowerdissolutionrateofuraniumin(U,Th)mixedoxide,however theoxidationandreductionprocessisnotclearyet.Sunderetal. [9]pointedoutthatduetothehighelectricalresistivity,working withelectrochemicaltechniquesonsuchasystemasbulk mate-rialwasnotpossible.Toovercomethisdifficulty,thinfilmscanbe agoodalternativeasdemonstratedbyMiserqueetal.[11],who reportedcyclicvoltammetryonUO2thinfilms.BycomparingCV
measurementsonUO2thinfilm(1m)andbulkUO2(1mm),itwas
confirmedthatthefilmsmadebyDCsputteringtechniquehave muchlowerresistancethanthebulkelectrodesandtheIRdropfor cyclicvoltammetryisnegligible.
Fig.6showsthefirsttwocyclesofU1−xThxO2 (x=0.10,0.44,
0.84,1.00)electrodesscannedbetween−1Vto0.6V(vs.Ag/AgCl) in0.01MNaCl.Thefirstcyclesareindicatedwithsolidlines,the secondonesareindicatedwithdashedlines.Romannumberson thegraphsindicatethepeakpositionsofthesuggestedreactions basedonliterature[17,35],Duringthefirstcycle,theUO2electrode
win-Fig.7. CyclicvoltammetryforU1-xThxO2(x=0,0.10,0.44,0.84,1)filmsfromthe3rduptothe15thcycleintherangeof−1Vto0.6V(A).CyclicvoltammetryforU1-xThxO2
(x=0,0.10,0.44,0.84,1)filmsforhigherpotentialwindowupto0.8V(vs.Ag/AgCl)andgoldsubstratecycles(yellowlines)(B).(Forinterpretationofthereferencestocolour inthisfigurelegend,thereaderisreferredtothewebversionofthisarticle.)
dowitisthermodynamicallyimpossibletooxidisehomogeneous UO2andthepreviousstudiesattributedthecurrentchangetothe
differentenergysitesorinhomogeneitysuchasgrainboundaries andhyperstoichiometry(e.gUO2+x)onthesurfaceoftheelectrode
[17,35].ThefirstcyclefortheUO2,U0.90Th0.10O2,U0.56Th0.44O2and
U0.16Th0.84O2electrodesdoesnotshowanysignificantpeaks,
how-ever,thesecondcyclesofUO2andU0.90Th0.10O2electrodesshowa
slightcurrentincrease.Ontheotherhand,atlowercontentof ura-nium(i.e.U0.56Th0.44O2andU0.16Th0.84O2 electrodes)wedonot
observetheincreaseofthecurrent,whichcanbeexplainedbya loweroxidationonthesurfaceinthefirstcycles.
InregionII,theoxidationofUO2toUO2+xstartsandinthe
sub-sequentregionIII,UO2+xincreasestoUO2.33byO2−incorporation
intothelattice.Athigherpotentials,theoxidationprocessmight leadeithertoitsdissolutionasUO22+orrecrystallizationasUO2.5
andUO2.66 (duetotheadsorbedUO22+).However,inneutralto
slightlyalkalineelectrolytes,UO22+insolutionmightre-precipitate
ontheelectrodeeitherasschoepite(UO3·H2O)orasmetaschoepite
(UO3·2H2O)[17,35].
InregionIII,afastincreaseofthecurrentisobservedforboth UO2andU0.90Th0.10O2electrodesindicatingtheonsetof
dissolu-tion,whichisnot tosuchextentthecase forU0.56Th0.44O2 and
U0.16Th0.84O2 films. Thisprocesswasstudiedbymonitoringthe
masslossfromtheUO2electrodeinsolutionsofpH=5topH=8
usingEQCMbySeibertetal.[12].
Region IV and V are thereduction peaks of oxidised layers observed on cathodic potentials. These peaks are usually cou-pledwiththeanodicoxidationpeaks.Thepotentialsofthepeaks arerelatedtothethicknessoftheoxidelayerformedduringthe anodicscansatthesurface[36].Inneutralelectrolytes,regionIV is observedand attributed toreduction of UO3·nH2O toUO2+x.
UO3·nH2O phases are insulators and thought to precipitate as
porouslayeranddonotinterferewiththereductionofthe under-lyingoxides [37,38]. RegionV is associated tothereduction of underlyingoxidessuchasUO2.33/UO2+xorUO2.5,UO2.67 created
inregionIII,asstatedabove[35].StartingfromregionIVandgoing toregionV,UO2andU0.90Th0.10O2electrodesshowhighercathodic
currentsindicatingthereductionofU(VI)toU(IV).Thisisnotthe case for U0.56Th0.44O2 and U0.16Th0.84O2. Thisbehaviouris also
reflectedinregionVwhileUO2 andU90Th10O2 electrodesshow
reductiontostoichiometricUO2,theothertwoelectrodesdoesnot
indicateanycompellingcurrentactivity.Thelowcurrentobserved atthispotentialwindowontheU0.56Th0.44O2 and U0.16Th0.84O2
electrodescanbeattributedtothelowercontentofuraniumin
con-tactwiththesolution.Alsothesubstitutionofuraniumbythorium inUO2latticeleadstothealterationoftheelectricproperties(from
semi-conductorUO2toinsulatorThO2)ofmixedoxidesamples.It
decreasestheelectricalconductivityandthusthedissolutionrate ofuraniumasreportedinliterature[9,39].
Fig.7Arepresentsthecyclesfrom3rdtill15thCVintherange
of−1Vto0.6VAgCl/Ag.InFig.7A,inregionV,wedoobservethat
thecathodiccurrentincreaseswiththeuraniumcontent.While U0.90Th0.10O2and,toalesserextent,U0.56Th0.44O2behaveina
simi-larwayaspureUO2,showingashiftingtohighercathodicpotential
alongthesuccessivecycle,U0.16Th0.84O2remainsconstantcurrent
inthis region.Theshiftingtolowerpotentialseemstoindicate theformationofathickeroxidelayerincreasingalongthe succes-sivecycles(indicatedwiththearrows).Uncompletedreductionin domainVleadstoanincreaseofoxidationonregionIofthecurrent gettinghigherandhigherineachcycle.Thesamephenomenonis notobservedforU0.56Th0.44O2andU0.16Th0.84O2electrodesdueto
theloweramountofuranium.InregionIIandIII,whereoxidation ofUO2 andUO2+x istakingplace,thecurrentincreaseswiththe
contentoftheuraniumpresentintheelectrodes.
Whenthe scans continued upto 0.8VAg/AgCl for another 15
cycles,differenceswereobservedasshowninFig.7B.Lookingat thepeaksinregionVandregionI,wedoobserveanoppositetrend comparedtoFig.7A.Thebroaderscanwindowtohigheranodic potentialleadsashiftingtolowercathodicpotentialofregionV andtoadecreaseofcurrentalongthecyclesinregionsVandI. Thismightbeduetofactthathigherdissolutionratesareachieved athigheranodicpotentials.Thisdecreaseinintensityofpeaksin regionVandImayberelatedtothedecreaseofthethicknessof thehyperstoichiometricoxidelayers(regionV),thusleadingtoless differentenergysitesorgrainboundariesonthesurface(regionI). Thereasonwhythisishappeninginthisbiggerpotentialwindow isnottotallyclear.
Goldusedassubstrateandconsideredasnoblemetaldoesnot interferestronglyintheworkingpotentialwindowchoseninthis study,asshowninFig.7Binyellowlines.Inthepotentialwindows upto0.6V(notreportedhere)ithasnoeffectasdemonstrated bythelowcurrentvalue,butwhenmeasuredupto0.8Vapeak markedasX onthecathodicpotentials isobserved.Thismight beattributedtotheelectrolytereduction.Thefilmshaveacertain porosityenablingthecontactofthesolutionwithgoldsubstrate. TheintensitypeakXincreasealongthesuccessivecyclesandcan berelatedtotheoxidelayergettingmoreandmoreporouswhile thegoldsurfaceincreasestogetherwithitsrelatedcurrent.
Table2
CompositionandU-4f5/2,Th-4f5/2andO–1soffilmsbeforeandafter30cyclesofCVin[NaCl]=0.01M.
Sample BeforeCV AfterCV
Composition BindingEnergy,eV Composition BindingEnergy,eV
U-4f5/2 Th-4f5/2 O-1s U-4f5/2 Th-4f5/2 O-1s
1 U0.67Th0.33O2 380.5 334.0 529.8 U0.57Th0.43O2+x 381.3 334.1 529.7/531.2
2 U0.56Th0.44O2 380.5 333.9 529.8 U0.40Th0.60O2+x 381 333.9 529.8/531.2
3 U0.16Th0.84O2 380.5 333.9 529.8 U0.14Th0.86O2+x 380.9 333.8 529.7/531.3
Fig.8. U-4fandTh-4fofU0.67Th0.33oxidefilmbeforeandafter15cycles,insetgraph
representsthecorrespondingO–1sspectra.
ThecurrentcountsfortheU0.56Th0.44O2andU0.16Th0.84O2
elec-trodes throughout their consecutive CVs have about the same values,whichcanbeexplainedbytheloweramountofuranium atthesurface.TheU0.16Th0.84O2electrodeisratherbehavingasthe
goldsubstrateitself.Ithasahighercurrentthangoldsubstratedue tothesmallamountofuraniumonthesurface.Nonethelessthe currentactivityshouldberelatedtotheelectrolyteinterference becauseThoriumisnotexpectedtoshowanyoxidationonthese potentialwindow[40].
Fig.8comparestheU-4fandTh-4fspectraofU0.67Th0.33O2film
obtainedbeforeandafterCVasanexamplethegeneral observa-tions.FirsttheU-4fpeaksshifttohigherbindingenergyindicating furtheroxidationasUO2+x,unliketheTh-4fpeaksthatkeepa
con-stantbindingenergybecausenofurtheroxidationthanTh(IV)can takeplace.We alsoobservedthechangeintheintensitypeaks. WhenthetwospectrabeforeandaftertheCVexperimentare nor-malizedtoTh-4f,theU-4fintensitypeaksdecreasedaftertheCV cycles,indicatingaloweruraniumcontentatthesurfacecompared totheinitial,asdepositedfilmcomposition.AlsotheshiftofU-4f tohigherbindingenergyafterCVexperimentindicatesahigher oxidationstateforuraniumatthesurface.Thequantificationusing CasaXPSshowsthatthecompositionchangesfromU0.67Th0.33O2
toU0.57Th0.43O2+x.IntheinsetofFig.8weobservethebroadening
ofthepeakO–1swhichcanbedeconvolutedintwocomponents, atlowBEandoneathigherBE,correspondingtoO2−andtoOH− respectively[33,41].TheO–1sshiftismorepronouncedonthefilms thatcontainhigheramountofuraniumonthecomposition.
TosummarizetheCVexperiment onthemixed oxidefilms, Table2reportsthecompositionsandtheBEofU-4f5/2,Th-4f5/2and O–1scorelevelpeaksforthedifferentsamplesbeforeandafterCV cycles.Theresultsshowastrongdecreaseofuraniumcontent rela-tivetothorium,decreasingbyabout30at%(sample2)comparedto theinitialcomposition.Thepreferentialdissolutionofuraniumat thesurfaceenablestoexplainthisresultleadingtoanenrichment ofthoriumatthesurfacewhichalongoxidationanddissolutionof U(VI)providesaprotectionlayerinhibitingthefurtheroxidation oftheuraniumpresentdeeperinthefilm.Thethoriumeffecthas
beendiscussedinliterature[6,9,33]reportingitsroletopassivate thesurface,limitingfurtheroxidationofuraniumanddecreasing thedissolutionrateofuranium.Ourresultsenabletoconfirmthis processtakingplaceatthesurfaceofthesampleincontactwitha neutralsolution.
4. Conclusionandsummary
ThinfilmsofU1−xThxO2(x=0to1)mixedoxideswere
investi-gatedbyXPS/UPS,XRDandCVtoestablishthepossibleinfluence ofthoriumontheoxidation/dissolutionprocess.
WefirstinvestigatedtherelativeoxygenaffinityofThandUand oxidationofuraniumstartedonlyoncethoriumwascompletely oxidized.Thisobservationisconsistentwiththehigherstability ofThO2 (fG0 (298K):−1170kJmol−1)comparedtoUO2 (fG0
(298K):−1031kJmol−1[42]).
Basedoncorelevelandvalencebandspectra,homogeneityof thefilmscouldbeshowedalongthedeposition.Alsodeposition temperature(from25◦Ctoabout400◦C)hadnoinfluenceon tho-riumoxidationstatewhileuraniumundergoesfurtheroxidation, seenbyashiftoftheU-4fsatelliteandtheU-5f2 peak,andbya
changeoftheO-2p/U-5f2intensityratio.
Todeterminethesuitabilityofthinfilmsasmodelsystemfor nuclearfuelwecomparedthelatticeparametersandtheU-4fand Th-4fcorelevelbindingenergyoffilmstobulkcompounds,fora seriesofcompositionsofU1−xThxO2(x=0to1).Thelattice
param-etersfollowedtheVegard´ıslaw,withaslightdeviationattributed tostresspresentinthefilms.AlsothebindingenergiesofU-4fand Th-4fcorelevelswereinagreementwiththosereportedonbulk compounds.
Cyclicvoltammetrywasusedtofollowthesurfaceredox reac-tionsfordifferentcompositions.Inthepotentialwindowof[−1 to0.6]V(vsAg/AgCl),oxidativedissolutionofuraniuminneutral pHsolutionsuggeststheformationofa layerofhigheroxideat thesurface.Shiftofthepeakstothehighernegativepotentialsare observedinthecathodicregionVatabout−0.9V(vsAg/AgCl), aswell asin current intensityincrease in theanodic regionat about−0.5V(vsAg/AgCl)inregionI,indicatingformationofthicker layershyperstoichiometricoxidesoneachcycleperformed.The intensity and the positionof the peaks showed a proportional relationwiththethoriumcontentinUO2 matrix.However,ona
largerpotentialwindow[-1to0.8]V (vsAg/AgCl),an opposite behaviourisobserved,suchaslowerintensityandadverse direc-tionshiftsoneachcycles.Thischangeinbehaviourshowedthat thesuccessivecyclesresultinthinnerlayersof hyperstoichiomet-ricoxidesonthesurface.Ontheotherhand,inthehigherpotential windowweobservedhighercurrentcountsforbothanodicand cathodicpotentialsforfilmswithhigherthoriumcontent(going fromU0.56Th0.44O2andU0.16Th0.84O2).Thiscanbeexplainedbythe
factthatahigherthoriumconcentrationrequireshigherpotentials tooxidiseuranium.
TheXPSspectraobtainedonsamples,beforeandafterCV exper-iments,indicatedclearlyenrichmentinthoriumatthesurfaceand ahigheroxidationstateofuranium.Theresultsalsoindicatedthat ahigherinitialuraniumcontentonthesurfaceleadstoahigher
shiftofU-4fbindingenergies,suggestingahigheroxidationstate ofuranium.Thiswassupportedbytheshapeofthecorresponding O–1sspectrumshowinghighercontributionofoxygenfromOH− groups.
Acknowledgments
WethankD.WegenandA.Seibertforfruitfuldiscussionsand alsotoS.StumpfandZ.BaofortheXRDmeasurements.P.Cakir acknowledgestheEuropeanCommissionandJointResearch Cen-tre.
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