大学物理实验报告英文版.docx
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大学物理实验报告英文版
大学物理实验报告
FerroelectricControlofSpinPolarization
ABSTRACT
Acurrentdrawbackofspintronicsisthelargepowerthatisusuallyrequiredformagneticwriting,incontrastwithnanoelectronics,whichrelieson“zero-current,”gate-controlledoperations.Effortshavebeenmadetocontrolthespin-relaxationrate,theCurietemperature,orthemagneticanisotropywithagatevoltage,buttheseeffectsareusuallysmallandvolatile.Weusedferroelectrictunneljunctionswithferromagneticelectrodestodemonstratelocal,large,andnonvolatilecontrolofcarrierspinpolarizationbyelectricallyswitchingferroelectricpolarization.Ourresultsrepresentagianttypeofinterfacialmagnetoelectriccouplingandsuggestalow-powerapproachforspin-basedinformationcontrol.
Controllingthespindegreeoffreedombypurelyelectricalmeansiscurrentlyanimportantchallengeinspintronics(1, 2).Approachesbasedonspin-transfertorque(3)haveprovenverysuccessfulincontrollingthedirectionofmagnetizationinaferromagneticlayer,buttheyrequiretheinjectionofhighcurrentdensities.Anidealsolutionwouldrelyontheapplicationofanelectricfieldacrossaninsulator,asinexistingnanoelectronics.Earlyexperimentshavedemonstratedthevolatilemodulationofspin-basedpropertieswithagatevoltageappliedthroughadielectric.Notableexamplesincludethegatecontrolofthespin-orbitinteractioninIII-Vquantumwells(4),theCurietemperature TC (5),orthemagneticanisotropy(6)inmagneticsemiconductorswithcarrier-mediatedexchangeinteractions;forexample,(Ga,Mn)Asor(In,Mn)As.Electricfield–inducedmodificationsofmagneticanisotropyatroomtemperaturehavealsobeenreportedrecentlyinultrathinFe-basedlayers(7, 8).
Anonvolatileextensionofthisapproachinvolvesreplacingthegatedielectricbyaferroelectricandtakingadvantageofthehystereticresponseofitsorderparameter(polarization)withanelectricfield.Whencombinedwith(Ga,Mn)Aschannels,forinstance,aremanentcontrolof TC overafewkelvinwasachievedthroughpolarization-drivenchargedepletion/accumulation(9, 10),andthemagneticanisotropywasmodifiedbythecouplingofpiezoelectricityandmagnetostriction(11, 12).Indicationsofanelectricalcontrolofmagnetizationhavealsobeenprovidedinmagnetoelectricheterostructuresatroomtemperature(13–17).
Recently,severaltheoreticalstudieshavepredictedthatlargevariationsofmagneticpropertiesmayoccuratinterfacesbetweenferroelectricsandhigh-TC ferromagnetssuchasFe(18–20),Co2MnSi(21),orFe3O4 (22).Changingthedirectionoftheferroelectricpolarizationhasbeenpredictedtoinfluencenotonlytheinterfacialanisotropyandmagnetization,butalsothespinpolarization.Spinpolarization[.,thenormalizeddifferenceinthedensityofstates(DOS)ofmajorityandminorityspincarriersattheFermilevel(EF)]istypicallythekeyparametercontrollingtheresponseofspintronicssystems,epitomizedbymagnetictunneljunctionsinwhichthetunnelmagnetoresistance(TMR)isrelatedtotheelectrodespinpolarizationbytheJullièreformula(23).Thesepredictionssuggestthatthenonvolatilecharacterofferroelectricsattheheartofferroelectricrandomaccessmemorytechnology(24)maybeexploitedinspintronicsdevicessuchasmagneticrandomaccessmemoriesorspinfield-effecttransistors
(2).However,thenonvolatileelectricalcontrolofspinpolarizationhasnotyetbeendemonstrated.
WeaddressthisissueexperimentallybyprobingthespinpolarizationofelectronstunnelingfromanFeelectrodethroughultrathinferroelectricBaTiO3 (BTO)tunnelbarriers(Fig.1A).TheBTOpolarizationcanbeelectricallyswitchedtopointtowardorawayfromtheFeelectrode.Weusedahalf-metallic(25)bottomelectrodeasaspindetectorintheseartificialmultiferroictunneljunctions(26, 27).Magnetotransportexperimentsprovideevidenceforalargeandreversibledependenceofthe TMR onferroelectricpolarizationdirection.
Fig.1
(A)Sketchofthenanojunctiondefinedbyelectricallycontrollednanoindentation.Athinresistisspin-coatedontheBTO(1nm)/LSMO(30nm)bilayer.Thenanoindentationisperformedwithaconductive-tipatomicforcemicroscope,andtheresultingnano-holeisfilledbysputter-depositingAu/CoO/Co/Fe.(B)(Top)PFMphaseimageofaBTO(1nm)/LSMO(30nm)bilayerafterpolingtheBTOalong1-by-4–μmstripeswitheitheranegativeorpositive(tip-LSMO)voltage.(Bottom)CTAFMimageofanunpoledareaofaBTO(1nm)/LSMO(30nm)bilayer.Ω,ohms.(C)X-rayabsorptionspectracollectedatroomtemperatureclosetotheFeL3,2 (top),BaM5,4 (middle),andTiL3,2 (bottom)edgesonanAlOxnm)/Alnm)/Fe(2nm)/BTO(1nm)/LSMO(30nm)(D)HRTEMand(E)HAADFimagesoftheFe/BTOinterfaceinaTa(5nm)/Fe(18nm)/BTO(50nm)/LSMO(30nm)Thewhitearrowheadsin(D)indicatethelatticefringesof{011}planesintheironlayer.[110]and[001]indicatepseudotetragonalcrystallographicaxesoftheBTOperovskite.
ThetunneljunctionsthatweusedinthisstudyarebasedonBTO(1nm)/LSMO(30nm)bilayersgrownepitaxiallyonto(001)-orientedNdGaO3 (NGO)single-crystalsubstrates(28).Thelarge(~180°)andstablepiezoresponseforcemicroscopy(PFM)phasecontrast(28)betweennegativelyandpositivelypoledareas(Fig.1B,top)indicatesthattheultrathinBTOfilmsareferroelectricatroomtemperature(29).ThepersistenceofferroelectricityforsuchultrathinfilmsofBTOarisesfromthelargelatticemismatchwiththeNGOsubstrate(–%),whichisexpectedtodramaticallyenhanceferroelectricpropertiesinthishighlystrainedBTO(30).ThelocaltopographicalandtransportpropertiesoftheBTO(1nm)/LSMO(30nm)bilayerswerecharacterizedbyconductive-tipatomicforcemicroscopy(CTAFM)(28).Thesurfaceisverysmoothwithterracesseparatedbyone-unit-cell–highsteps,visibleinboththetopography(29)andresistancemappings(Fig.1B,bottom).NoanomaliesintheCTAFMdatawereobservedoverlateraldistancesonthemicrometerscale.
WedefinedtunneljunctionsfromthesebilayersbyalithographictechniquebasedonCTAFM(28, 31).Topelectricalcontactsofdiameter~10to30nmcanbepatternedbythisnanofabricationprocess.Thesubsequentsputterdepositionofa5-nm-thickFelayer,cappedbyaAu(100nm)/CoOnm)/Conm)stacktoincreasecoercivity,definedasetofnanojunctions(Fig.1A).ThesameAu/CoO/Co/FestackwasdepositedonanotherBTO(1nm)/LSMO(30nm)sampleformagneticmeasurements.Additionally,aTa(5nm)/Fe(18nm)/BTO(50nm)/LSMO(30nm)sampleandaAlOxnm)/Alnm)/Fe(2nm)/BTO(1nm)/LSMO(30nm)samplewererealizedforstructuralandspectroscopiccharacterizations.
Weusedbothaconventionalhigh-resolutiontransmissionelectronmicroscope(HRTEM)andtheNIONUltraSTEM100scanningtransmissionelectronmicroscope(STEM)toinvestigatetheFe/BTOinterfacepropertiesoftheTa/Fe/BTO/LSMOsample.TheepitaxialgrowthoftheBTO/LSMObilayerontheNGOsubstratewasconfirmedbyHRTEMandhigh-resolutionSTEMimages.Thelow-resolution,high-angleannulardarkfield(HAADF)imageoftheentireheterostructureshowsthesharpnessoftheLSMO/BTOinterfaceoverthestudiedarea(Fig.1E,top). Figure1D revealsasmoothinterfacebetweentheBTOandtheFelayers.WhereastheBTOfilmisepitaxiallygrownontopofLSMO,theFelayerconsistsoftexturednanocrystallites.Fromthein-plane(a)andout-of-plane(c)latticeparametersinthetetragonalBTOlayer,weinferthat c/a =±,ingoodagreementwiththevalueoffoundwiththeuseofx-raydiffraction(29).TheinterplanardistancesforselectedcrystallitesintheFelayer[.,~Å(Fig.1D,whitearrowheads)]areconsistentwiththe{011}planesofbody-centeredcubic(bcc)Fe.
WeinvestigatedtheBTO/FeinterfaceregionmorecloselyintheHAADFmodeoftheSTEM(Fig.1E,bottom).OntheBTOside,theatomicallyresolvedHAADFimageallowsthedistinctionofatomiccolumnswheretheperovskiteA-siteatoms(Ba)appearasbrighterspots.Latticefringeswiththecharacteristic{100}interplanardistancesofbccFe(~Å)canbedistinguishedontheoppositeside.Subtlestructural,chemical,and/orelectronicmodificationsmaybeexpectedtooccurattheinterfacialboundarybetweentheBTOperovskite-typestructureandtheFelayer.TheseeffectsmayleadtointerdiffusionofFe,Ba,andOatomsoverlessthan1nm,orthelocalmodificationoftheFeDOScloseto EF,consistentwithabinitiocalculationsoftheBTO/Feinterface(18–20).
TocharacterizetheoxidationstateofFe,weperformedx-rayabsorptionspectroscopy(XAS)measurementsonaAlOxnm)/Alnm)/Fe(2nm)/BTO(1nm)/LSMO(30nm)sample(28).Theprobedepthwasatleast7nm,asindicatedbythefiniteXASintensityattheLaM4,5 edge(28),sothattheentireFethicknesscontributedsubstantiallytothesignal.Asshownin Fig.1C (top),thespectrumattheFeL2,3 edgecorrespondstothatofmetallicFe(32).TheXASspectrumobtainedattheBaM4,5 edge(Fig.1C,middle)issimilartothatreportedforBa2+ in(33).Despitethepoorsignal-to-noiseratio,theTiL2,3 edgespectrum(Fig.C,bottom)showsthetypicalsignatureexpectedforavalencecloseto4+(34).FromtheXAS,HRTEM,andSTEManalyses,weconcludethattheFe/BTOinterfaceissmoothwithnodetectableoxidationoftheFelayerwithinalimitoflessthan1nm.
Aftercoolinginamagneticfieldof5kOealignedalongthe[110]easyaxisofpseudocubicLSMO(whichisparalleltotheorthorhombic[100]axisofNGO),wecharacterizedthetransportpropertiesofthejunctionsatlowtemperatureK). Figure2A (middle)showsatypicalresistance–versus–magneticfield R(H)cyclerecordedatabiasvoltageof–2mV(positivebiascorrespo