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論文名稱: 高熵合金之高熵效應及緩慢擴散效應探討. 論文名稱(外文):, On High Entropy Effect and Sluggish Diffusion Effect of High-Entropy Alloys. 資料載入處理中... 跳到主要內容 臺灣博碩士論文加值系統 ::: 網站導覽| 首頁| 關於本站| 聯絡我們| 國圖首頁| 常見問題| 操作說明 English |FB專頁 |Mobile 免費會員 登入| 註冊 功能切換導覽列 (167.99.71.17)您好！臺灣時間：2022/01/1207:35 字體大小：       ::: 詳目顯示 recordfocus 第1筆/ 共1筆  /1頁 論文基本資料 摘要 外文摘要 目次 參考文獻 紙本論文 論文連結 QRCode 本論文永久網址: 複製永久網址Twitter研究生:蔡坤佑研究生(外文):Tsai,Kun-Yo論文名稱:高熵合金之高熵效應及緩慢擴散效應探討論文名稱(外文):OnHighEntropyEffectandSluggishDiffusionEffectofHigh-EntropyAlloys指導教授:葉均蔚指導教授(外文):Yeh,Jien-Wei學位類別:博士校院名稱:國立清華大學系所名稱:材料科學工程學系學門:工程學門學類:材料工程學類論文種類:學術論文論文出版年:2013畢業學年度:102語文別:英文論文頁數:177中文關鍵詞:高熵合金、高熵效應、緩慢擴散效應外文關鍵詞:High-entropyalloy、Highentropyeffect、Sluggishdiffusioneffect相關次數: 被引用:1點閱:955評分:下載:0書目收藏:0 高熵合金具有四個核心效應：高熵、嚴重晶格扭曲、緩慢擴散及雞尾酒效應，而本論文主旨在於探討高熵效應及緩慢擴散效應。

由於高熵效應可促進固溶相的形成，但較大的混合焓及原子尺寸差會促進有序相的形成，為瞭解此一競爭，本研究設計兩個參數分析高熵合金的成份與相型態之間的關聯。

其一為熱力學參數ε，代表合金中混合熵與混合焓之間的競爭關係；其二為拓樸學參數δ，代表合金中不同元素原子尺寸的差異。

利用此二參數分析已知的高熵合金，結果發現可清楚界定出形成單純無序固溶相合金及生成有序相的條件。

當δ較小，且混合熵的效應大於混合焓(即ε>1.1)時，會傾向形成無序固溶相。

當混合焓的效應大於混合熵(即ε<1.1)時，合金傾向生成有序中間相。

而當δ超過簡單結構所能承受的極限時，合金即會生成結構較複雜的介金屬相。

此研究結果可提供未來合金設計與開發的參考。

此外，本研究藉由「擬二元擴散偶」實驗量測Co-Cr-Fe-Mn-Ni五元高熵合金中各元素的擴散參數，得到高熵合金緩慢擴散效應的直接證據。

將各項擴散參數與其他FCC金屬比較，可發現隨著合金元數增加，各元素的擴散係數會隨之降低。

而將各元素的活化能除以熔點標準化後，也可發現其值隨著合金元數增加而增加。

本研究對這些趨勢提出理論解釋，採用準化學模型對晶格位能的差異幅度加以計算，結果發現高熵合金因主元素多，晶格屬全溶質晶格，晶格位能的差異幅度較大，因此具有許多位能相對較低的晶格位置形成原子的陷阱，使擴散活化能提高，此一理論可說是高熵合金緩慢擴散效應的主要機制。

High-entropyalloyshavefourcoreeffects:highentropy,sluggishdiffusion,severelatticedistortion,andcocktail.Theaimofthisstudyistodemonstratehighentropyandsluggishdiffusioneffectsinaquantitativeway.Highentropyeffecthasbeenfoundtoenhancetheformationofsolidsolutionswhereaslargeatomicsizedifferenceandlargenegativemixingenthalpybetweenunlikeatompairshavebeenfoundtoenhancetheformationoforderedphases.Inordertogainmoreunderstandingofsuchanorder-disordercompetition,thisstudyproposestwoparameterstoanalyzethecorrelationbetweenalloycompositionsandphasetypes.Oneisthemodifiedthermodynamicparameterεwhichrepresentsthecompetitionbetweenmixingentropyandmixingenthalpy,whiletheotheristhetopologicalparameterδwhichrepresentstheatomicsizedifference.Fromtheanalysesofthesetwoparametersofpublishedhigh-entropyalloys,thewell-definedcriteriafortheformationofrandomsolidsolutionsandorderedphasesareobtained.Whenδissmallandεislarge(i.e.theeffectofmixingentropydominatesoverthatofmixingenthalpy),alloystendtoformrandomsolidsolutions.Ontheotherhands,whenε<1.1(i.e.theeffectofmixingenthalpydominatesoverthatofmixingentropy),alloystendtoformorderedphases.Furthermore,whenδistoohightoretainsimplestructuresalloyswillformintermetallicphaseswithmorecomplexstructures.Thesecriteriacouldprovideausefulguidelineforalloydesignofhigh-entropyalloys.Beside,thisstudydirectlyconfirmsthesluggishdiffusionphenomenonbythemeasurementofdiffusionparametersfortheCo-Cr-Fe-Mn-Nialloysusingaquasi-binarydiffusioncouplemethod.ComparingthediffusionparametersofthefivecomponentelementsmeasuredinthepresentHEAswiththatinthereferenceFCCmetals,itcanbefoundthatthediffusioncoefficientsdecreasewiththenumberofconstituentelementsinthematrix,whereasthenormalizedactivationenergiesQ/Tmincreasewiththenumberofconstituentelements.ThesetendenciesarecertainlythedirectevidencesofthesluggishdiffusioneffectinHEAs.Themechanismbehindsucheffecthasalsobeenproposed.Thefluctuationoflatticepotentialenergy(LPE)wascalculatedusingquasichemicalmodel.ThelargerLPEfluctuationinthewhole-solutematrixofHEAsprovidesabundantsiteswithlowerpotentialenergy,whichbecomethetrapsofatomsandcausehighernormalizedactivationenergiesandlowerdiffusionrate. 摘要iAbstractiii誌謝vContentsviiiListofFiguresxiiListofTablesxviChapter1Introduction1Chapter2Background:High-entropyalloys52.1Alloyconcept52.2Definitionofhigh-entropyalloy62.3Multi-principal-elementeffect122.3.1Highentropyeffect122.3.1Latticedistortioneffect142.3.2Sluggishdiffusioneffect182.3.3Cocktaileffect20Chapter3FormationRulesofSolidSolutionPhasesinHigh-EntropyAlloys21Abstract213.1Introduction223.2Theoreticalbackground253.2.1Mixingenthalpyforbinaryalloys:Miedema’smodel253.2.2Mixingenthalpyformulticomponentalloys283.2.3Mixingentropy303.2.4PredictionofphasesformedinHEAs303.3Analysismethods403.3.1Thermodynamicparameter403.3.2Topologicalparameter493.3.3ClassificationofconstituentphasesofHEAs513.4Resultsanddiscussion573.4.1Statisticdistributionanalysis573.4.2Effectofthethermodynamicparameteronphaseformation793.4.3Effectofthetopologicalparameteronphaseformation803.4.4Advantagesofourmodificationsforpredictionofsolidsolutionformation843.4.4.1Usingabsolutevaluesofbinarymixingenthalpies843.4.4.2Usingsolidstateforcalculationandcorrectphaseclassification873.4.5Otherfactorscontrollingthephaseformation883.5Summary92Chapter4SluggishDiffusioninCo-Cr-Fe-Mn-NiHigh-EntropyAlloys95Abstract954.1Introduction964.2Theoryofdiffusion994.2.1Fick’slaws994.2.2Inversemethod1004.2.2.1Boltzmann-Matanomethod1004.2.2.2Sauer-Freisemethod1034.2.3Multicomponentdiffusion1034.2.4Interdiffusionandintrinsicdiffusion1054.2.5Tracerdiffusion1074.3DeterminationofdiffusioncoefficientsinHEA1084.4Experimentalprocedure1134.4.1Alloysdesign1134.4.2Assemblyanddiffusionannealingofthediffusioncouples1154.4.3Analysisofconcentrationprofiles1174.5Results1184.5.1Concentrationprofilesanddiffusioncoefficients1184.5.2Activationenergiesandpre-exponentialfactors1244.6Discussion1324.6.1Quasichemicalmodelforatomicmigration1324.6.2Calculationofsingle-bondinteractionenergy1354.6.3ProbabilitydistributionsofSBIE1394.6.4ChangeofSBIEduringatomicmigrationanditseffecttodiffusionkinetics1444.6.5Otherpossibleeffecttodiffusionkinetics1484.7Summary149Chapter5Conclusions151AppendixExamplesofalloyidentificationandclassification155References161 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