BEHAVIOR OF MARTENSITE REVERSE TRANSFORMA- TION IN 18Mn TRIP STEEL DURING WARM DEFORMATION
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- Ανδώνιος Δραγούμης
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1 Ð 46 Ð 10 Vol.46 No Þ Ð Ì ACTA METALLURGICA SINICA Oct pp Mn TRIP Â«É ÓÙÞÔ Â ( «Õ² Û, «100083) Ñ Ò Ê ¼ XRD «EBSD À Æ ³Â «18Mn Ð Ä Â ß. Ð Ï, 300 Ï, TRIP,  Ò, Á ; Æ ± ¼, bcc Â Ì Ä ± «, «² ȵº ; ¼«Á Ä Á Í, ÍÀ  ; Ï, À¾  Á {110} {100}. bcc Â Ü ¼ hcp Â. «ß, hcp  Þ. Ê 18Mn,, TRIP,  РРTG111.5, TG ÄØÒ A Á (2010) BEHAVIOR OF MARTENSITE REVERSE TRANSFORMA- TION IN 18Mn TRIP STEEL DURING WARM DEFORMATION LU Fayun, YANG Ping, MENG Li, MAO Weimin School of Materials Science and Engineering, University of Science and Technology Beijing, Beijing Correspondent: YANG Ping, professor, Tel: (010) , yangp@mater.ustb.edu.cn Supported by National Natural Science Foundation of China (No ) and Specialized Research Fund for the Doctoral Program of Higher Education (No ) Manuscript received , in revised form ABSTRACT High manganese steels show significant potential for industrial application due to their remarkable TRIP/TWIP effects at room temperature. The study on the TRIP behavior during warm deformation is important in controlling microstructures and properties of high manganese steels. In this paper, the microstructures, phase structures and reverse transformation of martensites to austenite in a high manganese steel which is composed of two types of martensites and austenite were investigated under warm deformation ( ) by means of the determination of transformation temperature, calculation of phase diagram, microstructure observation, XRD analysis and EBSD orientation imaging technique. Results show that during compression above 300, TRIP effect disappeared and reverse transformation from martensite to austenite was enhanced. The transformation from bcc martensite to austenite was determined to be diffusive and no nucleation of austenite was needed. The warm deformation of austenite leads to the formation of coarse deformation twins and the mechanical stabilization of austenite, which suppressed the subsequent martensitic transformation during quenching. The austenitic grains in which reverse martensitic transformation completed at the latest, show mainly {110} and {100} orientations. In addition, hcp martensite could hardly be detected around bcc martensite, and the transformation of hcp martensite into austenite is regarded to be reversible and diffusionless. KEY WORDS 18Mn steel, warm deformation, TRIP effect, reverse transformation of martensite * Å Î ³± Ñ ÀÎ ¾ Ø : , Ø : «Ð :,, 1985 ±, ± ± DOI: /SP.J Ê TRIP. ¹, TRIP Ë, ¹ ² ¼ TRIP [1] ; ¹, ¹ Ã, È ¹ µô TRIP [2,3]. Ó½
2 1154 Ð 46 TRIP Ñ ² à ¾Ò Ü M s à ¾Ò Ü M d. Î Ü, TRIP µ ٺر, ± ÎÆ» [4,5]. Ì 2 à ¹, hcp Ã, ; α à Å, ³. Á [6,7] Fe Mn Si ± Ñ ε à ². ÆÖÆ [8 10], 304 ³ ± Ñ Ã 400 Ð ²Ã., ß ¹ à Á. Á à ¼ TRIP µ 18Mn ¹, È ¹ Ü Ý Ü; ε α à ; TRIP ± ±, Ò ; ¹ Ò». 1 Ï Ê 18Mn, Ù ( À, %) : Fe 17.48Mn C 3.04Si 1.80Al S. Ù Ö 1050, 0.5 h Á Þ, ¾ Þ Ü 1050, ²Þ Ü 800, ÞÁ. «ÁÙ 18Mn ÆÐ 6 mm, 10 mm Ú½ Ç, h ÁÁË. Á, ºÅ. CMT4305 Ô Ù Å, 10% 30%, Ç 10 2 s 1. Gleeble /s Ç 100, Á 10%, 20%, 30% Á, ÁË, Ç 10 2 s 1. ÈÚ½ÇÔ Í½ Å. º ËÊ DIL805A È ± Ò. D/MAX RB Æ X à (XRD) Ç Ô± Å; «È D5000 X à ÇÔ Å. Thermo Cal ¾ Ë Ó. 5%( À) É ÍÔĐ ¾Á, Leo 1450 Zeiss SUPRA 55 ÎÔÆ (SEM) HKL Channel 5 Ô Ã (EBSD) ß ÇÔ Å Mn Ú Ä, É ØÙ Ò. Ó 1a 18Mn 1100 Á ËÁ. ÕÌ Ã, Ò±Å Æ hcp Ã, ÍÝÐÆ bcc Ã, ÑÚ. Ó 1b 30% Á, Õà Ð, Ã. EBSD ÔØ 3 Ì S N» {111} γ /{0001}ε, 1 10 / ε Burgers» {0001} ε /{110} α, ε / 1 11 α, Ú³ K S» [11]. 2.2 ÅÃÌÇÍ ÅĐ Û Ó ÜÁ ( ³ Ü), Æ É Đ Å. Ø 18Mn ¹ Ò Ë Õ Ó, ÕÓ 2 Ó 3. Ó 2 ÞÁ ÇÔ» ¹. Õ ¹, ÇÔ ², ß Ô bcc Ã Í Å ; ², ß Ã Í Å. ¹, Ç ÅÒ, Ý 1 18Mn Æ Fig.1 Microstructures of 18Mn steel at room temperature Relative length change (a) undeformed (b) compressed by 30% Heating Temperature, o C 2 18Mn ³Ú Í Ä 2 Cooling Fig.2 Length change of 18Mn steel during heating and cooling (heating at 10 /s and cooling at 5 /s)
3 Ð 10 ß : 18Mn TRIP ¾ Á Þ 1155 Temperature, o C bcc bcc+liquid bcc+fcc+liquid fcc+liquid fcc bcc+fcc bcc+cementite Liquid 400 bcc+m 5 C 2 bcc+cementite bcc+fcc+m 5 C 2 bcc+fcc+cementite Mass fraction of Mn, % 3» Termo Calc Ê 18Mn Ò Fig.3 Phase diagram of 18Mn steel calculated by Termo Calc 600 ÑÅ, ² Å, ß hcp Ã Đ α Ã, ½ Ã, α Ã È hcp à ±² (Ó 1). ¹ Ó, ¹ hcp à ¹ ( Ò À Ë), Đ α à ¹Ì, Õ, Î ÜÛ ºØ, Æ ³ ½. ¹, Ô Ï, hcp Ã ß α Ã Í Å, ¼. 600 α à ŠÁ, «³ à Ò. Ó 3 ¾ Thermo Calc Ë 18Mn Õ Ó. Õ, 18Mn 700 ¾Â bcc, Å,  C, Mn 20% ¹, ³ Ø, 18Mn. Ó 3 Æ, 500 ³ Ø, Å Â, º, Å, ÂÀ³. ¹ ¹, Ì Ã Í Å, Å Þ. 2.3 Å Î Ü Ã ËÅ È Ó 4a  18Mn ³ Ü Á Ø. Õ, Ì ε α à Ð, Ù±» (A); 30% Á (B ), Ó, α à Ç, Ï α à ; 18Mn 100, % Á,, α à Ó, (C, D E). 500 Á,», {110} γ à ÞÝ, Ø (E). Â, Þ Ü, Ã, TRIP µ Ó, Þ Ü ²Ã Intensity a.u. True stress, MPa (a) (100)hcp (111)fcc (110)bcc (101)hcp (200)fcc (102)hcp (200)bcc (220)fcc (211)bcc (311)fcc (222)fcc E D B A , deg (b) True strain 4 18Mn XRD Ö Æ ½ Æ Fig.4 XRD patterns (a) and true stress true strain curves (b) of 18Mn steel (A undeformed at room temperature; B compressed by 30% at room temperature; C compressed by 30% at 100 ; D compressed by 30% at 300 ; E compressed by 30% at 500 ). Ó 4b 18Mn ³ Ü ¾. Õ, Î Ü, 18Mn ÝÜ Å Û, Å ß, Ü, à Ó, TRIP µ ºØ±. 2.4 Å Î Üà ÖÀ Ë Ó 5  18Mn ³ Ü 30% Á. Õ, % ¹, à ÐÀ, Á ³ ; 300 ¹, à Ó, Ç TRIP µ, Â Þ Ü Ç Ã ; % Á, à ΠÓ, Ø ±, Æ α M Ì. Ó 5, α M ÝÙ³ ε (Ó 5c ±Ö ) Î. Æ Â, ¹, hcp à Ù. Ó 3, 500 fcc bcc Đ, ³É Î, bcc Ì, Ã É ÈÊÃ Í Å. C E D C B
4 1156 Ð Mn ² ÛÆ Ï 30% À Fig.5 Microstructures of 18Mn steel compressed by 30% at 100 (a), 300 (b) and 500 (c) Ó 6 18Mn 300, min Á, ÁË Æ. ÇÔ, à Ð. Ó 6a 300 Á, α M, Ù³ à ± ²Ñ È Ê, Æ Ç Å. Ó 6b, 400 Á, ±Â Þ ÐÆ Ã (Ö ), à ÈÊÃ Í Å. Ó 6c, 500 Á, ± ÈÊÃ Í Å ± ( Ö ), ±Æ Þв α M( Ö ), ±» ĐÇÃ, 500 ¹, à ², ÈÊÃ Í Å, ±Ò» Ã, پà Æ. Â, 18Mn 300 ¹, à ² ; 300 Ñ, Ç ¼ ²Ã, 500 ². ¹, Ó Ì, 6 18Mn ² Û Fig.6 Microstructures of 18Mn steel heated for 30 min at 300 (a), 400 (b) and 500 (c) Á³É» à ; Á, ±Â Ã. Æ ±, Ê Ã ; ¹, ± Ì Ò Ã. 2.5 Õ ßÆ Ã Ñ Ã ÒÕ [12]. Ó % EBSD. Ó 7a, ż± µ е ÃÐÆ Þ α M. È α M Ó (Ó 7b c) Â, ż Ø {110}, µ {100} {111} 6 α M, Ù± {100} α M ¹Þ Ø, Ù ² Ù. α M Þ Ä,.  α M Ù³ à ± ³
5 l 10 s ~7 18Mn {g : 18Mn TRIP 27B#I8`b 5z EW 3 30% e EBSD? Fig.7 EBSD orientation maps of 18Mn steel compressed by 30% at 300 (a) orientation map (grey denotes α M, red denotes ε M, other colors denote austenite) (b) pole figures of austenite (c) pole figures of α M f, ~' 7 4 I+ 9 D %* /4 f. 18Mn , x (, 6W ` (, γ α M 8 $^, P~ & α γ f8, $ k+ :b 0%3>"6 α M. o 8 18Mn 500 F X 30% I f EBSD!, q α M b k T C } EBSD M, J X U e C Z. o 1a < B, " α bb f [ ue 7 ε M, v 7 s Z i f :b!,.o 5c 1 8f ~6. < r, 1 8 ZFVf 4 G (o 8b % f O G, o 8c [ oh ), 7 < 4 -~ 1 8 f. G _ k " 6 f hcp K :b (q o 8b % f G & n), G * i f {111}[ 7 hcp K :b {0001}f. N r, " K :b b 4 N Z b O k, Z E o emb (U PRK :b). z f :b _ f! M Z o z g f K :b, J X 4 / Q & :b _. $ > Z 6 α M f :b j Miller H! (Z y 7 {103}), s u G / f {110}! :b _O k K :b T. = ; _ / Q k 1! hcp K :b b; k 4 ( α M b (o 8b? e), " {100}, {111}? 2 ( H!, jo * K :b7 u f, ~8? 18Mn 500 EW 30% He va \ EBSD Fig.8 Microstructure and EBSD orientation maps of 18Mn steel compressed by 30% at 500 (a) microstructure of the steel (b) orientation map (red denotes ε M, grey denotes α M, other colors denote austenite, yellow lines denote twin boundaries) (c) pole figures of austenite (d) pole figures of ε M (e) pole figures of α M - k% + f _. P o 8b % } X &, ~!', ~ α M! :bf8 7& 9D!f&>9D, ~Ok/ :bf4=. α M
6 D o 9 18Mn 500 F X 30% I< V t f!, U ST CZf EBSD M (q o 9b), J X e C Z. o 9b E x :b 0 K {123}!, _ + K :b C "; l x K {317}! f 1158 ~9 500 EW 30% He va \ EBSD? G 18Mn Fig.9 Microstructure and EBSD orientation maps of 18Mn steel compressed by 30% at 500 (a) microstructure (b) orientation map (red denotes ε M, blue denotes α M, other colors denote austenite) (c) pole figures of austenite (d) pole figures of ε M (e) pole figures of α M l 46 :b _K :b z } (o 9b? e), D ^ % +. [13] b S! X, {100}! f :b Fe 2 f G i _ 4 K:b. " d5`f7, sk:b Vvf : b ({223}) 7u :b ({317}) Z fg!, JXu j :b8 α M -G&f*Q8, -S7d8 fu :b!.! EBSD! %, vo k18 VY!f&i- :b, 4 f :bsuz :b 9 b 'Z, N Æ O k J 4 =9 D, ~ 7 J 9K:bUeMbfd!&>. Po 9e f[oh J, T 4 ( α M!, 2 ( {110}? 2 ( {100}. \ 2! EBSD H v! X, α K :b,y J Z 6 M, JX M4 6CZ, [Q7 hcp K:bN7d8 f :bk\ V*. H*Æ, hcp K:b! :b f 8 7 d f$ 7 d z", α K :b! hcp K :bu :b8 7' d f, ^& 9D!f. o 10! Mn ~ 4? 4 I f, L 9D. jo 18Mn u2. Op%7 :b, α M? ε M * T, N ^ \i X # 5 6F1,. o 10a ~ 10 18Mn } 3> 3 H 9a ( Fig.10 Austenitic orientation distribution in undeformed and warmly deformed 18Mn steel (a) austenite orientations in undeformed 18Mn, inverse pole figures (level max=1.2) (b) macrotexture of austenite after compresed at 500 by 30%, ODF φ2 =45 (c) orientations of austenite in 18Mn steel compressed at 500 by 30% inverse pole figures (level max=2.0)
7 Ð 10 ß : 18Mn TRIP ¾ Á Þ 1159 EBSD Ò Ø, 230 ż., Ù¾ 18Mn ± µ ÞÎ, Þ % Á, Ï, Ã, Æ X à fcc, Ó 10b. Õ, Þ² ² Ø {110}, Æ Þ {113}, {110} Å. 500 ½ ÞÉ Å, È {110}. 18Mn 500 Á, Æ Å¼± Ã, ß Ç Å¼, Ù 10c. Õ, 500 Á à żÐß {110} {100}, {110} ÞÐ, ¹ Ø Î. Ù¾ ¹ Þ, 500, Ü, Ï, TRIP µ, ²Ã. ±»É ²Ã Æ ², ƹ ºØ {110} Ù, {100} ± ² ². ÜÍ Å, α M à ² ½, à ºØ Õ ²Í± ; ÈÙ {110} Å ÞÐ, ³ ² ÍÛ, È {110} ±Ã ³. 3 ÝÑ TRIP Á [8 16], Î ÜÍÇ ³, ß, Ë ², Ç ºÓß ½. Á, ºÅ 3 Ò³ : Î ßÓ Á ¹ Ã, Á ß. Đ ßÓ Á Î Ã, ε γ Í α γ, Á 2 Ã Ì ¹,» ± ε Ã. 18Mn ±, ¹ α È ε ±, ½ ε à ; ¹, Þ ½ ε Ã, ÙÙ ¹ ε Ã Þ ; Í ε à Þ, ¹ ², EBSD Å Ò, Ø. ¹ Ì Ï. ¼ Ø 18Mn ± α γ ² ½. Ì«Ã ÌÜ ², Þ Â ε Ã, ½ Á [6,7], ε Ã, ß ³ Ü ÇÔ,  ßà 3 Í : (1) É ² Å, ßß ½ ³º ; Ó ÜÞ, Ï, à Ð, ß ½. Þ Ü (300 ) ¹, bcc à ß, hcp à ¾Ü ÐÀ. Ê ² ½, ¹, 500 à º Ó. ½Ã Ó Ü 500 Û 300. (2) Á ¹ à ; ß 30 min Á, É ²» à (Ó 6). µ Î ßËʳ Ã È TRIP Ü ³. ĐØ, Ø,, ½ ¹ TRIP, Ñ È. (3) Ç ¹, ² ¼ Î Å. 18Mn Ï, ÜÌ Ï, ½ hcp à ÇÜ Ó Å ÇÜ; TRIP ±, Ì«Ó Å, Î ² à Â. Ü Á, ¹Îà ±, à ¼, ²³Đ Ã, ² ¾ Û,»É. Î Å Ë Î Ü Å. Î Å Í Å Mn TWIP (25 30Mn) ¹Ë Ç ½, Æ Ù ± ÔÊ Å» ³ Ã. ÅÆ, ÜÁ ¾Ü, Î ε Ã, µ γ ßßÄ α à ß, ½ ÁË ¹, α à ڳ È ßÅÂ, ε à ; Æ, µ α à ², Â Ê ² ½. 4 Ñ (1) Â, 18Mn 5 /s ¹ Ý 600 ² γ ε α Ã, Ò ²ÐÛ Å, ¹ 200 ² Ô bcc Ã Í Å, 600 ¹Â Å Í (ÈÊ) Ã, ² ¼ Å, α à ² ½. (2) γ, ε α Ì Ù¾, 100 ¹ TRIP µ ; 300 ¹, TRIP µ ±, à Ó. ² Å Ç ² ½ α /α γ, α ε Á ¹ γ ε α à ; ½ ² ¾Î Ü Û, à Ó,  ΠÅ. (3) Ã»É ε à ÈÙ, α à ÈÊÃ Í Å ÁĐ ² Ù, ³». ¹ Ï ³ ¼ % Á, Á α»é
8 1160 Ð 46 ¹ Ø {110}, ÙÇ {100},. ¹ ¹ Ö³ Ü Ý ¾ Ê Ò. Æ [1] Zhang F C, Lei T Q. Wear, 1997; 212: 195 [2] Grässel O, Krüger L, Frommeyer G, Meyer L W. Int J Plast, 2000; 16: 1391 [3] Frommeryer G, Brüx U, Neumann P. ISIJ Int, 2003; 43: 438 [4] Curtze S, Kuokkala V T, Hokka M, Peura P. Mater Sci Eng, 2009; A507: 124 [5] Byun T S, Hashimoto N, Farrell K. Acta Mater, 2004; 52: 3889 [6] Sawaguchi T, Bujoreanu L G, Kikuchi T, Ogawa K, Koyamaa M, Murakamic M. Scr Mater, 2008; 59: 826 [7] Bergeon N, Guenin G, Esnouf C. Mater Sci Eng, 1998; A242: 87 [8] Stalder M, Vogel S, Bourke M A M, Maldonado J G, Thoma D J, Yuan V W. Mater Sci Eng, 2000; A280: 270 [9] Gauzzi F, Montanari R, Principi G, Tata M E. Mater Sci Eng, 2006; A : 202 [10] Tavares S S M, Fruchart D, Miraglia S. J Alloys Compd, 2000; 307: 311 [11] Kundu S, Bhadeshia H K D H. Scr Mater, 2007; 57: 869 [12] Kitahara H, Ueji R, Tsuji N, Minamino Y. Acta Mater, 2006; 54: 1279 [13] Zhang M X, Kelly P M, Gates J D. Mater Sci Eng, 1999; A : 251 [14] Gauzzi F, Montanari R. Mater Sci Eng, 1999; A : 524 [15] Lee Se J, Park Y M, Lee Y K. Mater Sci Eng, 2009; A515: 32 [16] Leem D S, Lee Y D, Jun J H, Choi C S. Scr Mater, 2001; 45: 767
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