改良型9Cr-1Mo擁有高的硬化能及高的麻田散鐵轉換起始溫度Ms，本實驗主要是針對不同的冷速、熱機處理及回火等不同的熱處理方式，觀察顯微組織的變化。在過去的觀念，一直認為麻田散鐵的變態起始溫度Ms為一特定的溫度。可是根據本實驗室熱膨脹儀在固溶化處理後，再以不同的冷卻速率冷卻，膨脹儀所紀錄的膨脹儀曲線所得的結果顯示，當冷卻速率越快，麻田散鐵的成長有被抑制到低溫的趨勢。反而不同沃斯田鐵化溫度所得的不同沃斯田鐵晶粒大小卻對Ms溫度沒有明顯可辨識的影響。
由光學顯微組織及TEM顯微組織的觀察顯示，本材料固溶化處理後，以0.5oC/s或100oC/s的冷卻速率冷卻至室溫，都可以得到完全的麻田散鐵組織。當此材料在固溶化處理後，在800oC施以不同的塑性變形，結果顯示塑性變形會造成機械穩定作用而抑制麻田散鐵相變態的成長。
當對此合金鋼固溶化處理後進行回火熱處理，當回火溫度650oC時有M3C沿雙晶界面及殘留沃斯田鐵界面析出，當回火溫度達到700oC以上，有M23C6在晶界及板條間析出，當回火溫度750oC回火兩小時，可以鑑定到VC的蹤跡。

Modified 9Cr-1Mo steel has a high hardenability and possesses a range of Ms temperature during continuous cooling at different cooling rates. The purpose of this work was to investigate the effect of different cooling rates, thermomechanical treatment and tempering on microstructural evolution. It is usually considered that the Ms temperature is constant, but the results of dilatomteric curves show that the Ms temperature decreases with the increase of cooling rate. This also found that the Ms temperature is not sensitive to the austenitization temperature.
The modified 9Cr-1Mo steel can virtually full transform to dislocated lath martensite even at a very slow cooling rate (0.5oC/s). Micro-twinning is generally detected in the martensite laths when the adjacent variants of martensite form in a twin-related manner. These twins extended partially across the martensite units and their features are different from those in twinned plate martensite. The prior deformation of austenite at 800oC is found to bring about the mechanical stabilization of austenite against the martensitic transformation.
Tempering at 650oCfor 30 min leads to the M3C precipitation along the interface of twins and the boundaries of austensite-martensite . As tempering temperature is over 700oC, the precipitates of coarse M23C6 can be found on grain boundary and martensitic lath boundary. The fine distribution of VC particles can be observed when the specimen tempered at 750 ℃ for 2h.

目錄
摘要……………………………………………………………………..
第一章前言……………………………………………………………1
第二章文獻回顧………………………………………………………2
2-0簡介……………………………………………………………2
2.1 9-12Cr合金鋼的背景…………………………………………3
2.2 鉻鉬鋼及9Cr-1Mo合金鋼…………………………………...4
2.2.1 9Cr-1Mo合金鋼之組成及相變化………………………..4
2.2.2合金元素對9Cr合金鋼的影響…………………………..5
2.2.3回火碳化物………………………………………………..9
2.2.4鉻鉬鋼的碳化物…………………………………………..10
2.3麻田散鐵相變化……………………………………………….13
2.3.1麻田散鐵的特徵…………………………………………..13
2.3.2麻田散鐵的晶體結構……………………………………..15
2.3.3麻田散鐵的結晶學………………………………………..15
2.3.4麻田散鐵的形態學………………………………………..16
2.3.4.1板條狀麻田散鐵……………………………………...17
2.3.4.2板片狀麻田散鐵……………………………………...18
2.3.4.3自動回火麻田散鐵…………………………………...19
2.3.5.初始沃斯田鐵塑性變形對後續對後續麻相
變態的影響……………………………………………..20
第三章材料準備及儀器的使用………………………………………31
3.1實驗材料……………………………………………………….31
3.2成分分析所使用之儀器……………………………………….31
3.3熱處理儀器…………………………………………………….31
3.4金相之觀察…………………………………………………….32
3.5 TEM試片製作及觀察………………………………………...32
第四章改良型9Cr-1Mo相變化之研究………………………………34
4.1簡介……………………………………………………………34.
4.2實驗方法……………………………………………………….35
4.3原材顯微組織觀察…………………………………………..35
4.4均質化顯微組織之觀察……………………………………….36
4.5不同沃斯田鐵化溫度及不同冷速連續冷卻相變態之
顯微組織…………………………………………………….37
4.5.1不同沃斯田鐵化溫度及不同冷速對相變態的影響……37
4.5.2不同沃斯田化溫度之顯微組織………………………….38
4.5.3不同冷速之顯微組織…………………………………….38
4.6結論……………………………………………………………43
第五章沃斯田鐵塑性變形對改良型9Cr-1Mo相變態之影響………67
5.1簡介…………………………………………………………….67
5.2實驗方法……………………………………………………….68
5.3沃斯田鐵塑性變形後相變態顯微組織之觀察……………….69
5.3.1光學顯微鏡顯微組織之觀察……………………………..69
5.3.2TEM顯微鏡顯微組織之觀察…………………………….69
5.4結論……………………………………………………………70
第六章改良型9Cr-1Mo回火相變態之研究…………………………78
6.1簡介…………………………………………………………….78
6.2實驗方法………………………………………………………79
6.3不同回火溫度持溫不同時間之顯微組織……………………79
6.3.1 在1050oC固溶化處理3分鐘後以5oC/s冷卻之
顯微組織………………………………………………..78
6.3.2不同回火溫度之OM……………………………………..80
6.3.3 650oC回火30分鐘………………………………………80
6.3.4 700oC回火30分鐘……………………………………….81
3.3.5 750oC回火30分鐘……………………………………….82
6.3.6 750 oC回火2小時………………………………………..83
6.4結論…………………………………………………………….84
建議未來工作…………………………………………………………100
參考文獻……………………………………………………………....101

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