狄长江
,
戴晓江
,
王孝东
,
刘佶林
,
宇文巍
黄金
doi:10.11792/hj20151108
对于露天金属矿山的开采规划模型,会有不同的变量参数且每个参数对模型的影响程度不同. 以某露天铜矿为工程背景,利用3 Dmine软件在不同的变量参数组合作用下得出其开采规划模型和相应的优化方案,将正交设计与方差分析有机结合,通过对优化方案当年净现值的分析来求解模型中每一个参数的灵敏度. 结果显示,精矿价格对开采规划模型的影响最大.
关键词:
露天开采
,
开采规划模型
,
变量参数
,
3Dmine软件
,
方差分析
,
灵敏度分析
宇文巍
,
戴晓江
,
狄长江
,
毕春杰
黄金
doi:10.11792/hj20160819
柴油设备在现代矿山中被广泛使用,其排出的碳烟、氮氧化物等污染物严重影响了井下的生产环境,甚至对井下工作人员的身体健康造成了威胁.该文在实验室环境下通过对柴油机进行富氧燃烧试验来研究柴油机的排放特性,寻找降低柴油机污染物排放的途径.该研究根据柴油机富氧燃烧的机理,设计了柴油机在不同工况下的富氧燃烧试验,对其在各不同工况下排出的碳烟、氮氧化物和一氧化碳进行了对比分析.试验结果表明:柴油机不论在何种工况下的富氧燃烧均可降低碳烟的排放;氮氧化物的排放会随着氧气的增加而上升;一氧化碳的排放也会有所降低,但降低的幅度不大.
关键词:
富氧燃烧
,
柴油机
,
碳烟
,
氮氧化物
狄长江
,
戴晓江
,
宇文巍
黄金
doi:10.11792/hj20150808
境界优化是露天矿山开采设计的主要内容之一。对于多金属矿山露天开采境界圈定时，会有不同的境界圈定方法。以某锡锌多金属矿为工程背景，利用3 DMine软件分别以不同的方法进行境界圈定，并综合考虑矿山资源状况、开采技术条件、矿产品销售价格、矿石开采及处理成本等多种因素，得出实现经济效益最大化的境界。结果显示，对于矿石品位已知的矿山，利用以品位计算价值比以矿石类型计算价值更合理；对于多金属主元素含量与伴生有益组含量差距比较大时，利用当量品位计算价值比以多金属品位单独赋值计算价值更合理。
关键词:
3Dmine软件
,
多金属矿床
,
境界优化
,
当量品位
,
圈定方法
工程热物理学报
根据《吴仲华奖励基金章程》（吴奖[2008]01号），经各高等院校、中国工程热物理学会和中国科学院工程热物理研究所认真评选和推荐，吴仲华奖励基金理事会评审并确定授予青年学者戴巍、罗坤、唐桂华“吴仲华优秀青年学者奖”，授予程雪涛等10位同学“吴仲华优秀学生奖”。
关键词:
基金
,
奖励
,
评选
,
获奖者
,
中国科学院
,
青年学者
,
物理研究所
,
高等院校
金属学报(英文版)
桑危郑牛樱裕桑牵粒裕桑希巍。希啤。龋伲模遥希牵牛巍。桑危模眨茫牛摹。模眨茫裕桑蹋拧。拢遥桑裕裕蹋拧。裕遥粒危樱桑裕桑希巍。桑巍。罚保罚怠。粒蹋眨停桑危眨汀。粒蹋蹋希?##2##3##4##5INVESTIGATIONOFHYDROGENINDUCEDDUCTILEBRITTLETRANSITIONIN7175ALUMINUMALLOY$R.G.Seng:B.JZhong,MG.ZengandP.Geng(DepartmentofMaterialsScierce,ScienceCollege,NorthearsternUniveisity,Shenyang110006,ChinaMaruscriptreceived4September1995inrevisedform20April1996)Abstrac:Effectsofhydrogenonthemechanicalpropertiesofdifferentlyaged7175aluminumalloyswereinvestigatedbyusingcathodicH-permeation,slowstrainratetensionandsoon.Theresultsindicatethatboththeyieldstressandthepercentagereductionofareadecreasewithincreasinghydrogenchargingtime,andthedegreeofreductiondecreasesasagingtimeincreasesforthesamehydrogenchargingtime.Keywords:hydrogeninducedductile-brittletransition,7175aluminumalloy,mechanicalproperty,cathodicH-permeation1.IntroductionForalongtimehydrogenembrittlementproblemwasthoughttobeabsentinhighstrengthaluminiumalloybecausethesolutiondegreeofhydrogeninaluminumatcommontemperatureandpressureisverysmall.However,hydrogenembrittlementphenomenonwasfoundinaluminumalloyduringtheinvestigationofstresscorrosionandcorrosionfatigue[1-5].Therehavebeenonlyafewreportsofhydrogeninducedsofteningandhardening.Inthispaper,theeffectsofhydrogenonmechanicalpropertiesof7175aluminumalloywereinvestigatedbyusingcathodicalchargingwithhydrogenandslowtensiontests.2.ExperimentalProcedureTheexperimentalmaterialwas7175aluminumalloyforgingintheformofa43mminthicknessandwithcomposition(wt%).5.41Zn,2.54Mg.1.49Cu,0.22Cr,0.1Mn.0.1Ti,0.16Fe.0.11Si,balancedbyA1.Alloyplateof1.5mminthicknesswasobtainedbyhot(465℃)andtoldrollingto83%reductioninthickness.Thelongaxisofhydrogenchargedspecimensisalongtherollingdirection.Allspecimensweresolidsolutionedat480℃for70min,followedtyimmediatequenchinginwaterandthenagedat140℃for6h(A),16h(B)and98h(C).Thetreatmentof6hiscorrespondingtotheunderagedstate.16hthefirstpeak-agedstateand98hthesecondpeak-agedstate.Thespecimenswerepolishedsuccessivelyusingemerypaperbeforehydrogencharging.Thetensilespecimenswerecathodicallychargedina2NH_2SO_4solutionwithasmallamountofAs_2O_3forpromotinghydrogenabsorption,andwithacurrentdensityof20±1mA/cm￣2atroomtemperature.ThehydrogencontentanalysiswascarriedoutonanLT-1Amodelionmassmicroprobeafterthesputteringdepthreached8nm.Theioncurrentsofhydrogenandaluminuminvariousagedstateswererecordedunderthesamecondition.ThetensiletestswereperformedonanAG-10TAmodeltestmachinewhichwascontrolledbycomputer.3.ExperimentalResultsTheratioofioncurrentstrengthofhydrogentoaluminumisrelatedtohydrogenconcentrationinhydrogenchargedspecimen.TheresultswereshowninTable1Thehydrogencontentincreaseswiththeincreaseincharingtime.Ofthethreeagedstates,theunderagedspecimenhasthehighesthydrogencontent.Theratioofyieldstrengthofhydrogenchargedandunchargedspecimenschangeswithhydrogenchargingtime,asshowninFig.1Itcanbeseenthattheyieldstrengthofhydrogenchargedspecimendecreasewithincreasinghydrogenchargingtime.Atthesamechargingtime,theyieldstressdecreasestheleastinthesecondpeak-agedstate,anddecreasesthemostintheunderagedstate.Itindicatesthattheunderagedspecimenismostsensitivetohydrogeninducedsoftening,whichisconsistentwiththeresultsofanotherhighstrengthaluminumalloy[6].TherelativechangesoftheradioofreductionofareawithhydrogenchargingtimearesummarizedinFig.2,whereΨ￣0andΨ￣Harethepercentagereductionofareaofthesamplewithoutandwithhydrogenchargingrespectively.Theradioofreductionofareareduceswhenhydrogenchargingtimeincreases,andthedecreasingdegreeofreductionofareaincreaseswithincreasingagingtime,ie,,theunderagedstateisthemostsensitivetohydrogenembrittlement.4.DiscussionItisknownfromtheresultsabovethatcathodicalchargingwithhydrogenleadstotheobviousdecreaseinthetensilestrengthandplasticityThisisbecausealargeamountofsolidsolutionhydrogenentersthespecimenintheprocessofhydrogenchargingSolidsolutionhydrogenisliabletoenterthecentreofdislocationundertheactionofdislocationtrap,henceraisingthemovabilityofdislocation.Thereforethedislocationsinhydrogenchargedspecimenmoveeasierthaninunchargedspecimen.soresultinginthereductionofyieldstrength[7].Whendislocationstartstomove,thecrystallatticeresistance(P-Nforce)whichitmustovercomeisgivenby:whereμismodulusofshear,visPoissonratio,aisspanofslipplane,bisatomspanofslipdirection.Moreover.theotherresistanceofdislocationmotionmayarisefromtheelasticinteractionofdislocation,theactionwithtreedislocationandetc.,itcanbeexpressedasfollows:whereαisconstant,XisdislocationspanSotheresistanceofdislocationmotioncanbewrittenasfollows:Becausehydrogenatomsreducetheatombondingstrengthafterhydrogencharging,shearmodulusμdecreasesandresultsinthereductionoff,therebytheyieldstressdecreases.Asthecentreofdislocationistheseriousdistortionzoneoflattice.thestresscanberelaxedafterhydrogenatomstuffing,andthesystemenergydecreases.Thusthecentreofdislocationisastrongtrapofhydrogen[8].Therefore,amovabledislocationcaptureshydrogenandmigratestograinboundaries.phaseboundariesorsurfaceofthespecimen,promotingthecrackiesformationandgrowth,thuscausingthelossofplasticity.Sincethelocalenrichmentofhydrogenisrealizedbydislocationtransporting(inthestageofdeformation),thelargerthereductionofyieldstress.theearlierarehydrogenatomstransportedtotheplaceofenrichment.Inaddition,thedamageofatombondingstrengthinducedbyhydrogenmakesthefracturestressdecrease[9]:whereCHishydrogenconcentration.σ_thisfracturestrengthbeforehydrogenchargingandisfracturestrengthafterhydrogencharging.Eq.(4)showsthatthematerialsmaybefracturedatalowerstraini.e.,brittlefractureoccurs.5.Conclusions(1)Hydrogencontentofdifferentlyagedspecimensincreaseswithincreasinghydrogenchargingtimethecapabilityofthealloytoabsorbhydrogeninunderagedstateisthestrongest.(2)Theyieldstressaswellasthepercentagereductionofareaof7175aluminumalloydecreaseashydrogenchargingtimeincreasesundervariousagedstates.(3)Underagedstateismostsensitivetohydrogeninducedsofteningandhardening.(4)Anexplanationwasofferedforthephenomenonofhydrogeninducedsofteninginthestageofdeformation,andhardeninginthestageoffracture.REFERENCES｜｜1G.KKock,Corrosion35(1979)73.2M.K.TsengandH.LMarcus,Scr.Metall.15(1981)427.3PSFao.M.GaoandR.P.Wei,Scr.Metall.19(1985)265.4R.G.SongandM.K.TsengJ.NortheasternUniversity15(1994)5(inChinese).5R.K.Viswanadham,T.S.sunandJ.A.S.Green,Metall.Trans.11A(1980)85.6J.Liu,M.KTsengandB.R.Liu.NonferrousMiningandMetallrgy5(1989)33(inChinese).7LChen,WXChen,ZHLiuandZ.Q.Hu,InFrocofthe1stNationalConfonAl-LiAlloys(Sheryang.China,1991)p.328(inChinese).8Z.HLiuL.ChenW.XChenY.X.ShaoandZ.Q.Hu,InProc.ofthe1stNationalConfonAl-LiAlloys(Shenyang,China,1991)p.334(inChinese).9R.A.OrianiandF.H.Josephic,ActaMetall.22(1974)1065.##61G.KKock,Corrosion35(1979)73.2M.K.TsengandH.LMarcus,Scr.Metall.15(1981)427.3PSFao.M.GaoandR.P.Wei,Scr.Metall.19(1985)265.4R.G.SongandM.K.TsengJ.NortheasternUniversity15(1994)5(inChinese).5R.K.Viswanadham,T.S.sunandJ.A.S.Green,Metall.Trans.11A(1980)85.6J.Liu,M.KTsengandB.R.Liu.NonferrousMiningandMetallrgy5(1989)33(inChinese).7LChen,WXChen,ZHLiuandZ.Q.Hu,InFrocofthe1stNationalConfonAl-LiAlloys(Sheryang.China,1991)p.328(inChinese).8Z.HLiuL.ChenW.XChenY.X.ShaoandZ.Q.Hu,InProc.ofthe1stNationalConfonAl-LiAlloys(Shenyang,China,1991)p.334(inChinese).9R.A.OrianiandF.H.Josephic,ActaMetall.22(1974)1065.##A##BINVESTIGATION OF HYDROGEN INDUCED DUCTILE BRITTLE TRANSITION IN 7175 ALUMINUM ALLOY$$$$R.G.Seng: B.J Zhong, MG. Zeng and P. Geng(Department of Materials Scierce, Science College,Northearstern Univeisity, Shenyang 110006, China Maruscript received 4 September 1995 in revised form 20 April 1996)Abstrac:Effects of hydrogen on the mechanical properties of differently aged 7175 aluminum alloys were investigated by using cathodic H-permeation, slow strain rate tension and so on. The results indicate that both the yield stress and the percentage reduction of area decrease with increasing hydrogen charging time, and the degree of reduction decreases as aging time increases for the same hydrogen charging time.
关键词:
:hydrogen induced ductile-brittle transition
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null
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null
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null
金属学报(英文版)
粒裕希停桑谩。疲希遥茫拧。停桑茫遥希樱茫希校佟。希拢樱牛遥郑粒裕桑希巍。希啤。停粒牵危牛裕遥希巍。樱校眨裕裕牛遥牛摹。粒蹋眨停桑危眨停樱桑蹋桑茫希巍。粒蹋蹋希佟。疲桑蹋停?##2##3##4##5ATOMICFORCEMICROSCOPYOBSERVATIONOFMAGNETRONSPUTTEREDALUMINUM-SILICONALLOYFILMSJ.W.Wu,J.H.FangandZ.H.Lu(NationalLaboratoryofMoleculeandBiomoleculeElectronics,SoutheastUniversity,Nanjing210096,ChinaManuscriptreceived27October1995)Abstrcat:Twodifferentsurfacemorphologycharacteristicsofmagnetronsputteredaluminumsilicon(Al-Si)alloyfilmsdepositedat0and200℃wereobservedbyatomicforcemicroscopy(AFM).Oneisirregularlyshapedgrainsputtogtheronaplane.TheotherisirregularlyshapedgrainsPiledupinspace.Nanometer-sizedparticleswithheightsfrom1.6to2.9nmwerefirstobserved.Onthebasisoftheseobservationsthegrowthmechanismofmagnetronsputteredfilmsisdiscussed.Keywords:magnetronsputtering,Al-Sialloy,surfacemorphology,atomicforcemicroscopy,filmgrowthmechanism1.IntroductionTheuseofaluminumalloys[1,2],inparticularAl-Si,isacommonfeatureinmanysinglelevelandmultilevelinterconnectionschemesadoptedinthemanufactureofmicroelectronicdevicesbecauseofseveraldesirableproperties.TheAl-Sigrainmorphology(size.geometryanddistributionofgrainsisassociatedwithstepcoverage[3],electromigration[4]andinterconnectsresistivity[5]etc..Thus,characterizationofAl-Sialloysurfacemorphologyisveryimportant,especiallywhenintegratedintensityincreasesandlinewidthsof0.3to0.5μmbecomecommon.Inthepasttwentyyears,theAl-Sialloysurfacemorphologywhichaffectsthereliabilityofmicroelectronicdeviceshasbeenwidelyinvestigatedbyscanningelectronmicroscopy(SEM),transmissionelectronmicroscopy(TEM)etc.[5-7].However,SEMandTEMhavetheirlimitationorinconvenience,forexample,theverticalresolutionofSEMisnothighandTEMneedscomplexsamplepreparation.Recently,anewgrainboundaryetchingmethodwasproposed￣[8]whichalsoneedstroublesomechemicaletching.Atomicforcemicroscopy(AFM),sinceitsemerging,hasbecomemoreandmoreusefulinphysics,chemistry,materialsscienceandsurfacescience,becauseofitshighresolution,easeofsamplepreparationandrealsurfacetopography.Recently,discussion[9,10]waspresentedonhowAFMwillplayaroleinsemiconductorindustry.Asaresponsetothisdiscussion,weusedAFMtoinvestigateAl-SialloysurfacemorphologyandhaveobtainedsomeresultswhichcannotberevealedbySEMorTEM.ThisindicatesthatAFMisagoodcharacterizationtoolinsemiconductorindustry.2.SamplePreparationInourexperiments,aluminumwith30ppmsiliconwassputteredonsiliconsubstrateinbatchdepositionmodeAllthreefilmswiththicknessof1.6μmweredepositedusinganargonsputteringpressureof4.2×10￣-3Pa.TheotherdepositionparametersaredescribedinTable1.Thesubstratewascleanedusingstandardpremetallizationcleaningtechniquespriortofilmdeposition.3.ExperimentalResultsandDiscussionTheAFMmeasurementswereperformedonacommercialsystem(NanoscopeIII,DigitalInstruments,SantaBarbara).Thetipismadeofmicrofabricatedsiliconnitride(Si_3N_4)Itisattachedtoa200μmcantileverwithaforceconstantofabout0.12N/m.Beforethesurfaceofsamplewasexamined.agoodtipwithananometer-sizedprotrusionatitsendwasselectedbeforehand,whichcanbeobtainedbyimagingtheatomicstructureofmicasubstrateandagoldgrid.AtypicaloperatingforcebetweenthetipandAl-Sisamplesurfaceisoftheorderof10￣-8Nandallimagesweretakenatroomtemperatureinair.AtypicaltopographicviewoftheAl-SifilmsisshowninFig.1(allimagescansizeis5by5μma,bandcarerespectivelyforsample1,2,and3).FromFig.la,itcanbeseenthatirregularlyshapedgrainstiltinginvaryingdegreespileupinspace,andgroovesamongtheirregularlyshapedgrainsaredifficulttodecideatacertainarea(wedefineitascharacteristicA).Toourknowledge,onreportsonthesurfacemorphologyhavebeenpresentedbefore.InFig1b,however,irregularlyshapedgrainsassembleonaPlaneandgroovesamongtheirregularlyshapedgrainsareeasytodecide(wedefineitascharacteristicB),whichisinagreementwithmanypreviousreports[5-7].InFig.1c,bothcharacteristicA(arrowA)andcharacteristicB(arrowB)wereobserved.IndoingAFMexperiments,weselectedfivedifferentscanareastobeimagedforeachsampleandfoundthatallimagesofeachsamplearerespectivelysimilartoFig.1a,bandc.Also,wenotedthatthesurfaceofinFig.1a.WethinkthatdepositionparameterswillinfluenceAl-Sisurfacemorphology,andthetiltedgrainsmaybesusceptibletomicrocracking.Byreducingthescansizeareato2by2μm(Fig.2aandb).Weobtainedmanyidenticalresultsasdescribedabove,suchasirregularlyshapedgrainsetc.Forthefirsttime,wefoundnanometersizedparticlesonirregularlyshapedgrainsurfacewhichcannotberevealedbySEMbecausethediameterofthesenanoparticlesisabout10nmandtheheightofthesenanoparticlesisintherangeof1.6to2.9nm.Inimaging,wenotedthatrotatingthescandirectionandchangingthescanfrequencydidnotaffectthestructureofthesegrainsasshowninFig.2aandb,rulingoutthepossibilitythatscanninginfluencedtheshapeoftheseparticlesorcausedsomesimilarimagingartifacts.Also,wenotedthatthenanoparticleswerenotobservedontheslopesofthegrooves(Fig.2aandb).Thisphenomenoncanbeexplainedasfollows:thepotentialenergyattheslopeislargerthanthatelsewhere,sotheparticlesseemmorelikelytobedepositedontheseareaswithlowerpotentialenergy.Fig.2c,scansize250by250nm,isazoomtopographicimage(whiteoutlineinb).Itshowsunevendistributionofthenanoparticles.Andtheheightdifferenceofthenanoparticlesindicatesdifferentgrowingspeed.Wethinkbasedonthemorphologyofnanoparticles,thattheheightdifferenceandunevendistributionofthesenanoparticlesshowdifferentgrowingadvantageandindicatethatatomshaveenoughenergytomovetoasuitablegrowingspot.Theenergymaybefromthefollowingsources:surfacetemperaturefluctuation,stressdifferenceorcollisionbetweenhighspeedsputteredatoms.Thesenanoparticlesgoongrowingandformmanyirregularlyshapedgrains.AndtheseirregularlyshapedgrainsfurtherconnecteachotheraccordingtocharacteristicAorB,finallyformingtheAl-Sisurfacemorphology.4.ConclusionWecandrawthefollowingconclusionsfromtheabove.First,theexperimentalresultsshowedthatAFMisapowerfultooltoinvestigatethedetailsofAl-Sisurfacemorphologywhichcangreatlyenrichourknowledgeofthefilmgrowthmechanism.Second,depositionconditionsplayanimportantroleindeterminingtheAl-Sisurfacemorphology.Third,thetwoAl-Sisurfacemorphologycharacteristicsarethatirregularlyshapedgrainsassembleonaplaneandirregularlyshapedgrainstiltinginvaryingdegreespileupinspace.Fourth,forthefirsttime,nanoparticleswereobservedonirregularlyshapedgrainsurfacewhichsuggestedthatthefilmgrowthmechanismwasbyinhomogeneousnucleation.Acknowledgements-BeneficialdiscussionswereheldwithDr.ZhenandMr.Zhu.ThisworkwaspartiallysupportedbytheNationalNaturalScienceFoundationofChina.RFFERENCES｜｜1D.pramanikandA.N.Saxena,SolidStateTechnol.26(1983)127.2D.pramanikandA.N.Saxena,SolidStateTechnol.26(1983)131.3D.pramanikandA.N.Saxena,SolidStateTechnol.33(1990)73.4S.S.IyerandC.Y.Worg,J.Appl.phys.57(1985)4594.5J.F.Smith,SolidStateTechnol.27(1984)135.6D.GerthandD.Katzer,ThinSolidFilm208(1992)67.7R.J.WilsonandB.L.Weiss,ThinSolidFilm207(1991)291.8E.G.Solley,J.H.Linn,R.W.BelcherandM.G.Shlepr,SolidStateTechnol33(1990)409I.SmithandRHowland,SolidStateTechnol.33(1990)53.10L.Peters,SemiconductorInternational16(1993)62.##61D.pramanikandA.N.Saxena,SolidStateTechnol.26(1983)127.2D.pramanikandA.N.Saxena,SolidStateTechnol.26(1983)131.3D.pramanikandA.N.Saxena,SolidStateTechnol.33(1990)73.4S.S.IyerandC.Y.Worg,J.Appl.phys.57(1985)4594.5J.F.Smith,SolidStateTechnol.27(1984)135.6D.GerthandD.Katzer,ThinSolidFilm208(1992)67.7R.J.WilsonandB.L.Weiss,ThinSolidFilm207(1991)291.8E.G.Solley,J.H.Linn,R.W.BelcherandM.G.Shlepr,SolidStateTechnol33(1990)409I.SmithandRHowland,SolidStateTechnol.33(1990)53.10L.Peters,SemiconductorInternational16(1993)62.##A##BATOMIC FORCE MICROSCOPY OBSERVATION OF MAGNETRON SPUTTERED ALUMINUM-SILICON ALLOY FILMS$$$$J.W.Wu,J.H. Fang and Z.H.Lu (National Laboratory of Molecule and Biomolecule Electronics,Southeast University,Nanjing 210096, China Manuscript received 27 October 1995)Abstrcat:Two different surface morphology characteristics of magnetron sputtered aluminumsilicon(Al-Si)alloy films deposited at 0 and 200℃ were observed by atomic force microscopy(AFM).One is irregularly shaped grains put togther on a plane.The other is irregularly shaped grains Piled up in space. Nanometer-sized particles with heights from 1.6 to 2.9 nm were first observed. On the basis of these observations the growth mechanism of magnetron sputtered films is discussed.
关键词:
:magnetron sputtering
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null
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null
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null
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null
金属学报(英文版)
茫遥伲樱裕粒蹋蹋桑冢粒裕桑希巍。希啤。疲錩(38)Ni_(39)Si_(10)B_(13) METALLIC GLASS UNDER HELIUM ION IRRADIATION##2##3##4##5CRYSTALLIZATIONOFFe_(38)Ni_(39)Si_(10)B_(13)METALLICGLASSUNDERHELIUMIONIRRADIATION$YANGQifa(ChinaInstituteofAtomicEnergy,Beijing)ZHANGGuoguang;SHENWanshui(UniversityofScienceandTechnologyBeijing)Manuscriptreceived20February1995ThecrystallizationfeaturesofFe38Hi39Si10B13metallicglassunder100keVand6μA/cm2heliumionirradiationwithdifferentdosesarereported.ItisfoundthattheFe38Ni39Si10B13metallicglasscrystallizedundertheheliumionirradiationatthetemperaturelowerthantheordinarythermalcrystallizationtemperature.ThepreferentialprecipitationphaseisFeSi,andfollowedbytheeutecticphaseα-Fe.Thecriticaldosefortheformationofheliumbubblesinthematerialisaround5x10￣16/cm2.Thesensitivityofcrystallizationduetothetemperaturerisingunderheliumionirradiationandthemechanismofthesequenceofprecipitatedphasearebrieflydiscussed.Keywords:Fe38Ni39Si10B13,metallicglass,crystallization,helium,ionirradiationTheblisteringorflakingoffirstwallmaterialsinducedbyheliumionbombardment,whichisrelevanttothefirstwallsurfaceerosionandplasmacontamination,isacriticalproblemtobeconsideredinfusionengineering.Becauseofthefavourablyphysical,chemicalandotherproperties,especially,thebetterresistanceofblistering,metallicglassesareexpectedtobeapromisingcandidatematerialforthefirstwall.TyagiandNanderkarstudiedsystematicallytheblisteringphenomenaofsomemetallicglassmaterialsunderheliumionandprotonbombardmentwithvariousionenergy,ioncurrentdensityanddose,andfoundthecriticaldoseforblisteringofthesematerials[1-3].However,itisverysuspiciousthatmetallicglasseswillcrystallizeunderheliumionirradiationtolosetheiramorphouscharacter,whichwilldeterioratetheirproperties.GusevaandGordeevareportedthatFe40Ni40B20metallicglassbombardedbyheliumionwithenergyof40keVandionbeamcurrentdensitiesof5-40μA/cm2partiallycrystallizedbelowitsordinarythermalcrystallizationtemperature[4].ByusingXRDexamination,itwasfoundthatα-FeandM3B,M2BandMBwereprecipitated(whereM=FeandNi)underheliumionbombardmentwith5μA/cm2and100μA/cm2ioncurrentdensitiesrespectively.Nevertheless,TyagiandNanderkarfoundthatsomemetallicglassescrystallizedandsomedidnotundersameirradiatedparameters[1-3].Consequently,itisnecessarytoinvestigatetheirradiation-assisted-crystallizationfeatureofmetallicglassesbyheliumionirradiationfortheirapplicationinfusionengineering.Inpresentexperiment,thecrystallizationfeatureofFe38Ni39Si10B13metallicglassunderheliumionirradiationwithenergy100keVandvariousdosesintherangeof5×1016/cm2to1×1018/cm2,andthedistributionofheliumbubblesinmaterialaremeasuredbyusingtransmissionelectronmicroscope(TEM)andX-raydiffraction(XRD).1.ExperimentalApproachTheas-receivedFe-Ni-Si-Bmetallicglassribbonswith10mminwidthand0.2mminthicknessweresuppliedbyBeijingInstituteofMetallurgy.Thenominalcomposition(wt%)ofthematerialisNi47.37,Fe43.91,Si5.81andB2.91fromthechemicalanalysisandthecalculatedconstituentisFe38Ni39Si10B13.TheX-raydiffractogramofas-receivedmaterialdemonstratedthattheas-receivedmaterialhasagoodamoophouscharacter.Thetheimalcrystallizationprocessoftheas-receivedmaterialwastestedbydifferentialthermalanalysis(DTA).Theordinarythermalcrystallizationtemperaturewasdeterminedtobeabout490℃.Rectangularsampleswithanareaof1×2cmanddiscsampleswith3mmindiameterwereemployedrespectivelyforXRDandTEMexperiments.ThesamplesforXRDweremechanicallypolishedtomirrorsurfaee.Ontheotherhand,formakingTEMsamples,thepiecescutfromtheribbonwerethinnedto30μmthicknessfirst,thenpunchedout3mmdiscs,electrothinnedinamixedsolutionof10%perchloricacidand90%ethanolandfinally,thediscswereionmilledtoextendthethinarea.HeliumionirradiationofsampleswascarriedoutonTS51-200/ZKionimplanterinChinaInstituteofAtomicEnergy.ThesampleswerefixedonacopperholderwhichwascooledbyF-113coolant.Thevacuumintargetwasbetterthan3×10-3Paandthescanningareaofionbeamwasabout3×7cm.Thetemperatureridingofthesamplescausedbyionbeambombardmentwasmeasuredbythermalcouple.Undertheirradiationparametersofionbeamenergy100keVandionbeamcurrentdensity6μA/cm2,thetemperaturerisingofsampleswaslowerthan200℃.Theiondosesofimplantedsampleswerechosenfrom5×10￣16/cm2to1×10￣18/cm2inpresentexperiment.AJEOL-100CXTEMoperatedat100kVwasused.Thecalculatedmeanprojectrangeandrangestragghngofheliumionwithenergy100keVinthematerialwere306.9nmand85.5nmrespectively,whichwassimulatedbycodeTRIM86.2.Results2.1CrystallizationunderionirradiationTheselectedareadiffraction(SAD)patternsofun-irradiatedandirradiatedsamplesareshowninFig.l.Fortheun-irradiatedsample,thepatterniscomposedoftwoconcentricringswhichexhibitatypicalamorphousdiffractionfeature(Fig.la).Ontheotherhand,forirradiatedsamples,agroupofnewconcentricringsappearsonthebaseofamorphousdiffractionrings,whichmeanstheoccurrenceofpartialcrystallizationandtheformationofsomenewprecipitationphasesinoriginalamorphousmaterialsbyionirradiation.Withtheincreaseofiondose,theinitialamorpohousdiffractionringsbecomefainterandtheintensitiesofdiffractionringsprodueedbyprecipitatesdevelopehigher.Itisexpectedthatthecrystallizationinsamplesincreaseswiththeincreaseiniondose.Moreover,iftheiondoseislowerthan5×10￣17/cm2,thepatternsshowtypicalpolycrystallinediffractionfeaturewithrandomorientationandveryfinegrains(Figs.lbandlc),butfor1×10￣18/cm2iondose,somebrightspotsarise(Fig.ld),thismeansthatsomerelativelargegrainsformedinsampleunderirradiation.FromtheX-raydiffractogramofthesampleirradiatedbyheliumiontodoseof5×10￣17/cm2,thediffractionpoaksarestillamorpohousfeatureandnonewpeaks.Itispredictedthatthecrystallizationonlyoccursintheprojectedrangeofions.2.2AnalysisofprecipitationphaseFromindexingofdiffractionringsinFig.lbandFig.lc,theprecipitatephaseisanfcccrystallinestructure.InFig.ld,anadditionalbccphaseisfound(ring3,ring5andring8).Thecalculatedlatticeparametersforprecipitatephasesundervariousiondosesareasfollows:5×1016/cm2a=0.412nm(fcc)l×1017/cm2a=0.42lnm(fcc)5×1017/cm2a=0.428nm(fcc)l×1018/cm2a=0.478nm(fcc)a=0.292nm(bcc)UsingASTMindex,itisidentifiedthatthebccphaseisα-Fe(a=0.2866nm).Todeterminethefccprecipitatephase,weinspectedallcompoundswithfcccrystallinestructurecomposedofelementsFe,Ni,SiandB,foundthatthreecompoundsFeSi(a=0.446nm),FeNi3(a=0.353nm)andFe3Si(a=0.564nm),butthemostfavourablecompoundwasFeSi.Therefore,itisassumedthatthepreferentialprecipitatephaseisFeSi,andisfollowedbytheeutectcphaseα-Feundertheheliumionirradiation.2.3HeliumbubbledistributionThemorphologiesofheliumbubblesformedbyagglomerationofimplantedheliumionsareshowninFig.2.Thesmallblackdotspresentbubblesunderbrightfieldwiththeunderfocusingoperation.FromFig.2,itisrevealedthatbubbleslowerthedensity,butinflateinthedimensionwiththeincreaseiniondose.Moreover,underthehigherdosethebubblesjoinedtogether.Fig.3plotsthechangesofdensitiesanddiametersofbubbleswiththeiondose.ItisevidentthatthecriticaldosetoformbubblesinFe38Ni39Si10B13islowerthan5×1016/cm2,whichisslightdifferentfrom1×1017/cm2reportedbyTyagi[1].3.DiscussionAstheresultsreportedbyGusevaandGordeeva[4],theheliumirradiationcantrulybringonthepartialcrystallizationinmetallicglassFe38Ni39Si10B13belowitsordinarythermalcrystallizationtemperature.GusevaandGordeevaconfirmedthattheprecipitatesinFe40Ni40B20wasα-Fephaseunderheliumionirradiationof40keVenergyand5μA/cm2currentdensity,inwhichthetemperaturerisingofthesampleswaslowerthan200℃.Howerve,inpresentexperiment,thoughα-Fephaseisdetermined,notraceofM3B,M2BandMBprecipitatephaseisobserved,whichwasreportedbyaboveauthorsunderirradiationwithenergyof40keVandioncurrentdensityof30μA/cm2.Inaddition,theprecipitationprocessinpresentexperimentissomewhatdifferentfromtheprecipitationprocessreportedbyaboveauthors,thepreferentialprecipitationphaseisFeSi,andfollowedbytheeutecticphaseα-Fe.CrystallizationofamorphousFe40Ni40B20wasnotobservedbyTyagi,whichwasthesamematerialasthatusedbyGusevaandGordeeva,undertheirradiationwith100keVionenergyand30μA/cm2ioncurrentdensity[3].Itmayrelatetothetemperaturerisingofsamplesorsomethingelse.Accordingtothecomparisonandanalysis,itmaybeconcludedthatthecrystallizationofmetallicglassesisverysensitivetothetemperaturerisinginsamplescausedbyionbeamirradiation.ThereasonofthepreferentialphasetobeFeSiandfollowedα-Femaybethatinanamorphousmaterial,themetalloidelementsshouldkeepatthetotalcontentsabove20at%,otherwisesomeelementsorcompoundswillprecipitatetoremainthebalanceofchemicalcomposition.Therefore,astheprecipitationofFeSianddeclineofSicontentsinasample,FeandNimayprecipitateasaneutecticphaseaccordingtoaboveidea.Inthisexperiment,Feprecipitatedfirstly.ThedifferenceoflatticeparametersbetweenexperimentaldataandASTMstandarddatamayresultsintheexistencesofNiandBetcandincompletecrystallizationinsample.Thegeneralviewpointforirradiation-assisted-crystallizationofmetallicglassbelowtheirthermalcrystallizationtemperatureisthedisplacementdamagesinducedbycollosion-cascadebetweenincidentionsandtargetatoms.Thedisplacementdamagesprovidethenucleatingcentresandtheirradiation-assistedmigrationincreasesthecrystallizeddrivingforce,butnodirectrelationshipbetweenheliumandcrystallization.Thegrowthofagrainiscloselyattributedtothediffusionofneighbouringatomstothegrowingnucleus,whichisreliedonthetemperatureextremely,accordingly,thecrystallizationofmetallicglassisverysensitivetothetemperaturerisingfromionbeambombardmentinanirradiatedsample.4.Summary(l)TheFe38Ni39Si10B13metallicglasswillcrystallizebelowitsordinarythermalcrystallizationtemperatureunderheliumionirradiationwith100keVenergyand6μA/cm2ionbeamcurrentdensity.(2)ThepreferentialprecipitationphaseofthemetallicglassisFeSi,andfollowedbyaneutecticphaseα-Fe.(3)Thecriticaldoseformingheliumbubblesinthemetallicglassisabout5×1016/cm2,whichisslightlylowerthanthedosereportedbyTyagi.(4)Theirradiation-assisted-crystallizaofametallicglassesisverysensitivetothetemperaturerisingcausedbyionbeambombardmentinanirradiatedsample.Acknowledgements─TheauthorswouldliketothankthecolleaguesofIonImplantationGroupinChinaInstituteof.AtomicEnergy.forhelpinginsampleirradiation,alsotoProfe
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: Fe38Ni39Si10B13
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