本論文探討四元鐵-13錳-2.8鋁-1.2碳合金鋼在不同溫度下之相變化情形。合金先經1100℃固溶處理，再進行溫度為850℃以下的恆溫處理。利用分析儀器觀察後，確認本合金鋼於1100℃至850℃的溫度區間為單一的沃斯田體相，並無任何二次相的出現。在800℃時，於沃斯田體的晶界處發現M3C碳化物(C)以顆粒狀或條狀的形式析出，故形成M3C碳化物的上限溫度應介於850℃至800℃之間。當恆溫處理的溫度為700℃時，於合金鋼內發現由層狀M3C晶粒與肥粒體()晶粒所組成的波來體出現於沃斯田體基地內；所以，當溫度低於750℃時，於本合金內會有→(M3C+的共析反應發生。由於750℃以上生成的M3C碳化物為初析碳化物，故本合金鋼是屬於過共析鋼，而共析反應的最高溫度應介於750℃至700℃之間。經不同恆溫處理條件的觀察，判定波來體組織的恆溫變態曲線的鼻部溫度應介於575℃至550℃之間。

We have studied the phase transformation of an Fe-13.4 Mn-2.84 Al-1.22 C steel. The steel was solution heat treated at 1100℃. We found the steel is single austenite at 1100℃ and in the as-quenched condition. After the solution heat treatment, the steel underwent the following annealing condition at temperatures ranging from 850℃ to 500℃. At the annealing temperature of 850℃, single austenite was discovered. We found M3C carbide appears at the austenite grain boundaries at temperatures below 800℃. Thus, the upper temperature limit for the appearance M3C carbide is between 850℃ and 800℃. The pearlite comprising of lamellae of ferrite and M3C carbide appears in the austenite matrix at annealing temperatures below 750℃. The pearlite formed as a result of a eutectoid reaction:   + M3C. The upper temperature limit for the eutectoid reaction is between 750℃ and 700℃. The nose temperature for the time-temperature-transformation curve is between 575℃ and 550℃.

01.H.V. Lawrence, Elements of Materials Science and Engineering, 6th ed., Addison Wesley(1995).
02.R.E. Reed-Hill, Physical Metallurgy Principles, 3rd ed., pp.538-585 (1992).
03.W.F. Smith, Structure and Properties of Engineering Alloys, 2/e, pp1-25 (1993).
04.D.A. Porter, K. Easterling and David A. Porter, “Phase Transformations in Metals and Alloys”, 3/e (2008).
05.C.J. Wang and Y.C. Chang, Mater. Chem. Phys., 76, 151 (2002).
06.W.C. Cheng and H.Y. Lin, Mater. Sci. Eng., A323, 462 (2002).
07.S.K. Chen, K.W. Chour, W.B. Lee, C.M. Wan and J.G. Byrne, Mater. Res. Bull., 25, 1115 (1990).
08.D.S. Zhou and G.J. Shiflet, Scripta Metall., 27, 1215 (1992).
09.C.R. Hutchinson and G.J. Shiflet, Scripta Mater., 50, 1 (2004).
10.Y.L. Lin and C.P. Chou, Scripta Metall., 27, 67 (1992).
11.H. Huang, D. Gan and P.W. Kao, Scripta Metall., 30, 499 (1994).
12.M.C. Li, H. Chang, P.W. Kao and D. Gan, Mater. Chem. Phys., 59, 96 (1999).
13.T.F. Liu and C.M. Wan, Scripta Metall., 19, 727 (1985).
14.T.F. Liu and J.C. Tasy, Scripta Metall., 21, 1213 (1987).
15.J.W. Lee, C.C. Wu and T.F. Liu, Scripta Mater., 50, 1389 (2004).
16.C.M. Liu, H.C. Cheng, C.Y. Chao and K.L. Ou, J. All. Comp., 488, 52 (2009).
17.T.F. Liu and C.C. Wu, Scripta Meatll., 23, 1087 (1989).
18.T.F. Liu and C.C. Wu, Scripta Metall., 23, 1243 (1989).
19.許中杰，“鐵-20錳-4鋁-0.5碳合金鋼之時效相變化研究”，國立台灣科技大學，碩士論文 (2008)。
20.陳崧豪，“鐵-20錳-2鋁合金鋼之相變化研究”，國立台灣科技大學機械工程研究所，碩士論文 (2008)。
21.劉柏言，“錳鋁鋼層狀組織的-碳化物旁沃斯田體雙晶層之研究”，國立台灣科技大學機械工程研究所，碩士論文。
22.M.C. Li, H. Chang, P.W. Kao, Mat. Chem. Phys., 5996 (1999).
23.K.H. Han, J.C. Yoon, W.K. Choo, Scripta Metall., 20, 33 (1986).
24.Y.G. Kim, Y.S. Park and J.K. Han, Metall. Trans. A, 16, 1689 (1985).
25.Y.G. Kim, J.K. Han and E.W. Lee, Metall. Trans. A, 17, 2097 (1986).
26.W.F. Smith, “Structure and Properties of Engineering Alloys”, 2/e (1993).
27.C.R. Hutchinson, R.E. Hackenberg and G.J. Shiflet, Acta Mater., 52, 3565 (2004).
28.R.J. Dippenaar and R.W.K. Honeycombe, Proc. R. Soc. Lond., A, 333, 455 (1973).
29.D.N. Shackleton and P.M. Kelly, Acta Metall., 15, 979 (1967).
30.G.Spanos and H.I. Aaronson, Scripta Metall., 22, 1537 (1988).
31.R.E. Reed-Hill, “Physical Metallurgy Principle”, 3/e (1992).
32.G. Krauss, Principles of Heat Treatment of Steel, ASM, pp.17-41, (1980).
33.E.C. Bain and H.W. Paxton, Alloying Elements in steel, 2nd ed., American Society for Metals, pp. 18 (1966).
34.張容，“10錳高錳鋼低溫相變化研究”，國立台灣科技大學機械工程研究所，碩士論文。
35.李育誠，“20錳-1.6鋁1碳錳鋁鋼之低溫相變化研究”，國立台灣科技大學機械工程研究所，碩士論文。
36.宋元聖，“錳鋁鋼中形成波來體的共析反應研究”，國立台灣科技大學機械工程研究所，碩士論文。
37.胡廷菁，“錳鋁鋼合金的層狀反應相變化研究”，國立台灣科技大學機械工程研究所，碩士論文。
38.M.C. Li, H. Chang and P.W. Kao, Mater. Chem. Phys., 5996 (1999)。