合金經970℃和1050℃固溶1小時後，其顯微結構為板狀α及殘留沃斯田鐵，溫度越高殘留沃斯田鐵含量越多，此板狀α(或稱麻田散鐵，c/a≒1)結構為體心立方結構(B.C.C.)，其晶格常數為a=0.289nm，而殘留沃斯田鐵結構為面心立方結構(F.C.C.)，晶格常數a=0.360nm。於-80℃/8H深冷處理後，將固溶時之殘留沃斯田鐵完全轉變為板狀α結構，此時之晶格常數為a=0.289nm。
經時效(450℃、550℃及650℃)處理，在450℃時可發現α相及沃斯田鐵相之產生，其α相之晶格常數為a=0.289nm。而在550℃和650℃時可發現L12 (Ni3Al)結構之析出物於基地內整合析出，此時之結構為板狀α與沃斯田鐵，並且有L12(面心立方結構)之析出物，其晶格常數為a=0.375nm。並且可以觀察出時效溫度550℃提高至650℃時，其Ni3Al之析出物由微粒狀轉變為顆粒狀，沃斯田鐵含量大量增加。與其他學者比較，固溶溫度提高至980-1050℃後，其B2相(NiAl)之析出物並未被發現。

Being solution heat treatment(SHT) on 970℃/1H or 1050/1H, and quenching room-temperature the microstructure of the alloy is the α phase and retained austenite. The higher SHT temperature would posses the higher retained austenite. This plate-α(called matensite)belong to the body-centered cubic(B.C.C.) structure with the lattice parameter a=0.289nm. The retained austenite belongs the face-centered cubic(F.C.C.) structure with lattice parameter a=0.360nm. After -80℃/8H subzero heat treatment. The retained austenite would transform into plate-α.
During the 450℃ aging processes, the α-plate martensite would be decompose to α + austenite phase, increasing the aging temperature to 550-650℃.The L12-phase(Ni3Al) particles would be found within the matrix . The lattice parameter of the L12-phase is a=0.375nm. Compared with the other workers studies , increasing the SHT temperature to 980-1050℃, the precipitation of the B2-phase(NiAl) will be inhibited.

目錄
摘要 I
Abstract II
謝誌 III
目錄 IV
表目錄 VI
圖目錄 VII
第1章 前言 1
第2章 文獻探討 2
2.1 不銹鋼凝固過程及型態 2
2.2 鉻-鎳沃斯田鐵系中的碳化鉻 3
2.3 麻田散鐵的相變化 4
2.4 麻田散鐵的結晶學 5
2.5 優選織構 6
2.6 17-4PH 析出硬化型不銹鋼 6
2-7 PH 13-8 Mo 析出硬化型不銹鋼之材料性質 7
2-8 Custom 475析出硬化型不銹鋼 8
第3章 實驗方法 12
3.1 材料製備 12
3.2 熱處理條件分析 12
3.3 顯微組織觀察 12
3.3.1 光學顯微鏡觀察 12
3.3.2 掃描式電子顯微鏡觀察 13
3.3.3 X光繞射分析儀 13
3.3.4 穿透式電子顯微鏡觀察 13
3.4 拉伸與硬度實驗 13
3.5 銲接外力及冷卻外力對皺褶之影響 14
第4章 結果與討論 19
4.1固溶處理 19
4.3時效處理 20
4.3.1 450℃時效後顯微結構與性質分析 20
4.3.2 550℃時效後顯微結構與性質分析 20
4.3.3 650℃時效後顯微結構與性質分析 21
4.4討論 21
4.5皺褶分析 23
第5章 結論 52
參考文獻 53
作者簡介 56

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