冷却速率对Ti3Al合金组织和拉伸性能的影响

王震,曹,磊,刘仁慈,刘冬,崔玉友,杨,锐

doi:10.3724/SP.J.1037.2013.00572

金属学报 >

2013 , Vol. 49 >Issue 11: 1487 - 1492

DOI: https://doi.org/10.3724/SP.J.1037.2013.00572

论文

冷却速率对Ti₃Al合金组织和拉伸性能的影响

展开

1)中国科学院金属研究所, 沈阳 110016
2)东北大学材料与冶金学院, 沈阳 110819

王震, 男, 1985年生, 博士生

收稿日期: 2013-09-09

修回日期: 2013-09-24

网络出版日期: 2013-11-11

收起

EFFECT OF COOLING RATE ON MICROSTRUCTURE AND TENSILE PROPERTIES IN Ti₃Al ALLOY

Expand

1) Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016
2) College of Materials and Metallurgy, Northeastern University, Shenyang 110819

Received date: 2013-09-09

Revised date: 2013-09-24

Online published: 2013-11-11

Fold

摘要

对两相区锻造的Ti₃Al合金棒材分别在1020和1150℃保温30 min,以10, 1.5和0.3℃/s速度冷至室温, 研究了冷速对Ti₃Al合金组织和拉伸性能的影响.结果表明, 在1020℃固溶, 冷速为10℃/s时, 合金主要由B2相和α₂相组成;降低冷速, 基体中均匀析出针状α₂/O相; 冷速为0.3℃/s,等轴α₂/O相体积分数增加, 针状α₂/O相粗化.随着冷速下降, 合金的室温强度先升高后下降, 塑性先降低后提高;600℃拉伸强度逐渐下降, 塑性提高. 在1150℃固溶, 快速冷却时,合金主要由B2相构成, 晶粒尺寸约为440 μm; 降低冷速, 晶内均匀析出α₂/O相,呈网篮状; 冷速0.3℃/s时, 基体中析出的α₂/O相片层呈集束状.随着冷速下降, 室温强度下降, 而塑性先升高后降低; 600℃拉伸强度先升高后降低, 而塑性逐渐上升.结合组织分析表明, Ti₃Al合金的强度取决于晶界和α₂/O片层的尺寸,塑性受B2相体积分数以及α₂/O相的分布及体积分数影响. 冷速为1.5℃/s时,Ti₃Al合金具有良好的综合力学性能.

关键词： Ti₃Al合金; 冷却速率; 显微组织; 拉伸性能

本文引用格式

王震,曹,磊,刘仁慈,刘冬,崔玉友,杨,锐 . 冷却速率对Ti₃Al合金组织和拉伸性能的影响[J]. 金属学报, 2013 , 49(11) : 1487 -1492 . DOI: 10.3724/SP.J.1037.2013.00572

Abstract

The microstructure and tensile properties in Ti₃Al alloy rod by forging in the (B2+α₂) region after heating at 1020 and 1150℃ for 30 min and cooling to room temperature at the cooling rates of 10, 1.5 and 0.3℃/s were investigated. The results showed that Ti₃Al alloy structure was mainly composed of B2 phase and α₂ phase at the cooling rate of 10℃/s after heating at 1020℃. With the decrease of cooling rate, the acicular α₂/O phase homogeneously precipitated in the matrix on slow cooling. The volume fraction of equiaxed α₂/O phase increased and the acicular α₂/O phase was coarsed under the cooling rate of 0.3℃/s. For room temperature tensile tests, the data indicated that the strength initially increased and then decreased and the ductility firstly decreased and then increased with reducing cooling rate. During the 600℃ tensile tests, the strength decreased monotonically and ductility rose as reducing cooling rate. When solid solution temperature was 1150℃, Ti₃Al alloy was mainly composed of B2 phase and the size of grain was 440 $\mu$m by fast cooling. Basketweave structure was obtained in the grain at the cooling rate of 1.5℃/s. The α₂/O phase colony precipitated in the B2 phase with further reducing the cooling rate. With the decrease of cooling rate, the strength decreased gradually and ductility initially increased and then decreased at the room temperature, the 600℃ tensile strength firstly went up and then down and ductility increased. Through microstructure analysis, strength in Ti₃Al alloy is controlled by boundary and the size of α₂/O phase, and ductility is decided by the number of B2 phase and α₂/O phase and the shape of α₂/O phase. The good comprehensive properties were obtained at the cooling rate of 1.5℃/s.

Key words： Ti₃Al alloy; cooling rate; microstructure; tensile property

参考文献

[1] Dimiduk D M, Miracle D B, Ward C H. Mater Sci Technol, 1992; 8: 367

[2] Cao C X, Ma J M, Yan M G. Mater Eng, 1991; (2): 32

(曹春晓, 马济民, 颜鸣皋. 材料工程, 1991; (2): 32)

[3] Williams J C, Starke E A. Acta Mater, 2003; 51: 5775

[4] Li S Q, Zhang J W, Cheng Y J, Liang X B. Rare Met Mater Eng, 2005; 34(suppl. 3): 104

(李世琼, 张建伟, 程云君, 梁晓波. 稀有金属材料与工程, 2005; 34(增刊3): 104)

[5] Si Y F, Chen Z Y, Meng L H, Wang Z W, Chen Y Y. Spec Cast Nonferrous Alloys, 2003; (4): 33

(司玉锋, 陈子勇, 孟丽华, 王肇文, 陈玉勇. 特种铸造及有色合金, 2003; (4): 33

[6] Sagar P K. Mater Sci Eng, 2006; A434: 259

[7] Wang M G, Sun J K, Chen J Q. Rare Met Lett, 2007; 26(11): 8

(王孟光, 孙建科, 陈志强. 稀有金属快报, 2007; 26(11): 8)

[8] Mishra R S, Banerjee D. Scr Metall Mater, 1990; 24: 1477

[9] Dary F C, Thompson A W. In: Froes F H, Caplan I L, eds.,Titanium'92: Science and Technology, Warrendale,PA: The Minerals, Metals and Materials Society, 1993: 375

[10] Huang C, Loretto M H. In: Blenkinsop P A, Evans W J, Flower H M, eds.,Titanium'95: Science and Technology, London: Institute of Materials, 1996: 558

[11] Wu Y, Tang Z X, Yang D Z, Li D M. Mater Sci Technol, 1996; 4(1): 24

(武英, 唐之秀, 杨德庄, 李明道. 材料科学与工艺, 1996; 4(1): 24)

[12] Banerjee D, Gogia A K, Nanay T K. Acta Metall Mater, 1988; 36: 871

[13] Banerjee D, Baligidad R G, Gogia A K. In: Hemker K J, Dimiduk D M, Clemens H,Darolia R, Inui H, Larsen J M, Sikka V K, Thomas M, Whittenberger J D, eds.,Structural Intermetallics 2001, Warrendale, PA: The Minerals, Metals and Materials Society, 2001: 43

[14] Zhang Y G, Han Y F, Chen G L, Guo J T, Wan X J, Feng D. Structure Intermetallics.Beijing: National Defence Industry Press, 2001: 789

(张永刚, 韩雅芳, 陈国良, 郭建亭, 万晓景, 冯涤. 金属间化合物结构材料.北京: 国防工业出版社, 2001: 789)

[15] Cao J X, Xu J W, Huang X. Rare Met, 2006; 30(special issue): 13

(曹京霞, 许剑伟, 黄旭. 稀有金属, 2006; 30(专辑): 13)

[16] Cao J X, Sun Y F, Cao C X. Rare Met, 1997; 21: 490

(曹京霞, 孙育峰, 曹春晓. 稀有金属, 1997; 21: 490)

[17] Cao J X, Xu J W. Titanium Ind Prog, 2008; 25(1): 15

(曹京霞, 许剑伟. 钛工业进展, 2008; 25(1): 15)

[18] Xu J W, Huang X, Gao J X. Rare Met, 2004; 28(1): 50

(许剑伟, 黄旭, 曹京霞. 稀有金属, 2004; 28(1): 50)

[19] Cao J X, He S L, Shi W M, Wang H W, Wang X. Chin J Nonferrous Met,2010; 20(special issue 1): 207

(曹京霞, 何书林, 石为民, 王宏武, 王新. 中国有色金属学报, 2010; 20(专辑1): 207)

[20] Cao J X, Duan R, Li Z X. Rare Met Mater Eng, 2008; 37(suppl. 3): 541

(曹京霞, 段锐, 李臻熙. 稀有金属材料与工程, 2008; 37(增刊3): 541)

[21] Cao J X, Duan R, Li Z X. Rare Met, 2009; 33: 746

(曹京霞, 段锐, 李臻熙. 稀有金属, 2009; 33: 746)

[22] Muraleedharan K, Gogia A K, Nandy T K, Banerjee D, Lele S. Metall Mater Trans,1992; 23A: 401

[23] Wang Y, Ma N, Chen Q, Zhang F, Chen S L, Chang Y A. JOM, 2005; 57: 32

[24] Ward C H. Int Mater Rev, 1993; 38: 79

[25] Gogia A K, Banerjee D, Nandy T K. Metall Trans, 1990; 21A: 609

[26] Wu Y, Tang Z X, Yang D Z, Li D M. Chin J Nonferrous Met, 1996; 6(3): 99

(武英, 唐之秀, 杨德庄, 李道明. 中国有色金属学报, 1996; 6(3): 99)

Options

文章导航

模态框（Modal）标题

摘要

本文引用格式

Abstract

参考文献