深过冷液态Al-Ni合金中枝晶与共晶生长机理

杨尚京; 王伟丽; 魏炳波

doi:10.7498/aps.64.056401

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摘要

在自由落体条件下实现了液态Al-4 wt.%Ni亚共晶、Al-5.69 wt.%Ni共晶和Al-8 wt.%Ni过共晶合金的深过冷与快速凝固. 计算表明, (Al+Al3Ni)规则纤维状共晶的共生区是4.8–15 wt.%Ni成分范围内不闭合区域, 且强烈偏向Al3Ni相一侧. 实验发现, 随液滴直径的减小, 合金熔体冷却速率和过冷度增大, (Al)和Al3Ni相枝晶与其共晶的竞争生长引发了Al-Ni 共晶型合金微观组织演化. 在快速凝固过程中, Al-4 wt.%Ni亚共晶合金发生完全溶质截留效应, 从而形成亚稳单相固溶体. 当过冷度超过58K时, Al-5.69 wt.%Ni 共晶合金呈现从纤维状共晶向初生(Al) 枝晶为主的亚共晶组织演变. 若过冷度连续增大, Al-8 wt.%Ni过共晶合金可以形成全部纤维状共晶组织, 并且最终演变为粒状共晶.

关键词:

作者及机构信息

1.
西北工业大学应用物理系, 西安 710072

基金项目: 国家自然科学基金(批准号: 51371150, 51271150, 51101123)资助的课题.

参考文献

[1]	Clopet C R, Cochrane R F, Mullis A M 2013 Appl. Phys. Lett. 102 031906
[2]	Matthews T S, Sawyer C, Ogletree D F, Liliental-Weber Z, Chrzan D C, Wu J Q 2012 Phy. Rev. Lett. 108 096102
[3]	Wu M W, Xiong S M 2011 Acta Phys. Sin. 60 058103 (in Chinese) [吴孟武, 熊守美 2011 物理学报 60 058103]
[4]	Pasturel A, Tasci E S, Sluiter M H F, Jakse N 2010 Phys. Rev. B 81
[5]	Yang Y J, Wang J C, Zhang Y X, Zhu Y C, Yang G C 2009 Acta Phys. Sin. 2797 [杨玉娟, 王锦程, 张玉祥, 朱耀产, 杨根仓 2009 物理学报 58 2797]
[6]	Park J M, Sohn S W, Kim D H, Kim K B, Kim W T, Eckert J 2008 Appl. Phys. Lett. 92 091910
[7]	Lu Y P, Lin X, Yang G C, Li J J, Zhou Y H 2008 J. Appl. Phys. 104 013535
[8]	Zhou S, Li J F, Liu L, Zhou Y H 2009 Chin. Phys. B 18 1674
[9]	Zhu Y C, Wang J C, Yang G C, Zhao D W 2007 Chin. Phys. 16 805
[10]	Lv Y J, Wei B B 2003 Chin. Phys. Lett. 20 1379
[11]	Yang T Y, Wu S K, Shiue R K 2001 Intermetallics 9 341
[12]	Chrifi-Alaoui F Z, Nassik M, Mahdouk K, Gachon J C 2004 J. Alloy. Compd. 364 121
[13]	Silva B L, Araujo J C, Silva W S, Goulart P R, Garcia A, Spinelli J E 2011 Phil. Mag. Lett. 91 337
[14]	Chang J, Wang H P, Wei B 2008 Phil. Mag. Lett. 88 821
[15]	Nishiyama N, Takenaka, Inoue A 2006 Appl. Phys. Lett. 88 121908
[16]	Liu J, Zhao J Z, Hu Z Q 2006 Appl. Phys. Lett. 89 031903
[17]	Trivedi R, Magnin P, Kurz W 1987 Acta Metall. 35 971
[18]	Lipton J, Kurz W, Trivedi R 1987 Acta Metall. 35 957
[19]	Boetinger W J, Coriell S R, Trivedi R 1987 in: R. Mehrabian (Eds.), Proceedings of the Fourth Conference on Rapid Solidification Processing, Principles and Technologies, Claitors, Baton Rouge p13
[20]	Yan N, Wang W L, Dai F P, Wei B 2011 Acta Phys. Sin. 60 034602 (in Chinese) [闫娜, 王伟丽, 代富平, 魏炳波 2011 物理学报 60 034602]
[21]	Tournier S, Vinet B, Pasturel A, Ansara I, Desre P J 1998 Phys. Rev. B 57 3340
[22]	Cortella L, Vinet B, Desre P J, Pasturel A, Paxton A T, Vanschilfgaarde M 1993 Phy. Rev. Lett. 70 1469
[23]	Levi C G, Mehrabian R 1990 Metall. Trans. 21 59
[24]	Aziz M J 1982 J. Appl. Phys. 53 1158

施引文献

[1]	Clopet C R, Cochrane R F, Mullis A M 2013 Appl. Phys. Lett. 102 031906
[2]	Matthews T S, Sawyer C, Ogletree D F, Liliental-Weber Z, Chrzan D C, Wu J Q 2012 Phy. Rev. Lett. 108 096102
[3]	Wu M W, Xiong S M 2011 Acta Phys. Sin. 60 058103 (in Chinese) [吴孟武, 熊守美 2011 物理学报 60 058103]
[4]	Pasturel A, Tasci E S, Sluiter M H F, Jakse N 2010 Phys. Rev. B 81
[5]	Yang Y J, Wang J C, Zhang Y X, Zhu Y C, Yang G C 2009 Acta Phys. Sin. 2797 [杨玉娟, 王锦程, 张玉祥, 朱耀产, 杨根仓 2009 物理学报 58 2797]
[6]	Park J M, Sohn S W, Kim D H, Kim K B, Kim W T, Eckert J 2008 Appl. Phys. Lett. 92 091910
[7]	Lu Y P, Lin X, Yang G C, Li J J, Zhou Y H 2008 J. Appl. Phys. 104 013535
[8]	Zhou S, Li J F, Liu L, Zhou Y H 2009 Chin. Phys. B 18 1674
[9]	Zhu Y C, Wang J C, Yang G C, Zhao D W 2007 Chin. Phys. 16 805
[10]	Lv Y J, Wei B B 2003 Chin. Phys. Lett. 20 1379
[11]	Yang T Y, Wu S K, Shiue R K 2001 Intermetallics 9 341
[12]	Chrifi-Alaoui F Z, Nassik M, Mahdouk K, Gachon J C 2004 J. Alloy. Compd. 364 121
[13]	Silva B L, Araujo J C, Silva W S, Goulart P R, Garcia A, Spinelli J E 2011 Phil. Mag. Lett. 91 337
[14]	Chang J, Wang H P, Wei B 2008 Phil. Mag. Lett. 88 821
[15]	Nishiyama N, Takenaka, Inoue A 2006 Appl. Phys. Lett. 88 121908
[16]	Liu J, Zhao J Z, Hu Z Q 2006 Appl. Phys. Lett. 89 031903
[17]	Trivedi R, Magnin P, Kurz W 1987 Acta Metall. 35 971
[18]	Lipton J, Kurz W, Trivedi R 1987 Acta Metall. 35 957
[19]	Boetinger W J, Coriell S R, Trivedi R 1987 in: R. Mehrabian (Eds.), Proceedings of the Fourth Conference on Rapid Solidification Processing, Principles and Technologies, Claitors, Baton Rouge p13
[20]	Yan N, Wang W L, Dai F P, Wei B 2011 Acta Phys. Sin. 60 034602 (in Chinese) [闫娜, 王伟丽, 代富平, 魏炳波 2011 物理学报 60 034602]
[21]	Tournier S, Vinet B, Pasturel A, Ansara I, Desre P J 1998 Phys. Rev. B 57 3340
[22]	Cortella L, Vinet B, Desre P J, Pasturel A, Paxton A T, Vanschilfgaarde M 1993 Phy. Rev. Lett. 70 1469
[23]	Levi C G, Mehrabian R 1990 Metall. Trans. 21 59
[24]	Aziz M J 1982 J. Appl. Phys. 53 1158

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深过冷液态Al-Ni合金中枝晶与共晶生长机理

1. 西北工业大学应用物理系, 西安 710072

基金项目:

国家自然科学基金(批准号: 51371150, 51271150, 51101123)资助的课题.

收稿日期: 2014-07-21

修回日期: 2014-10-02

刊出日期: 2015-03-05

摘要: 在自由落体条件下实现了液态Al-4 wt.%Ni亚共晶、Al-5.69 wt.%Ni共晶和Al-8 wt.%Ni过共晶合金的深过冷与快速凝固. 计算表明, (Al+Al3Ni)规则纤维状共晶的共生区是4.8–15 wt.%Ni成分范围内不闭合区域, 且强烈偏向Al3Ni相一侧. 实验发现, 随液滴直径的减小, 合金熔体冷却速率和过冷度增大, (Al)和Al3Ni相枝晶与其共晶的竞争生长引发了Al-Ni 共晶型合金微观组织演化. 在快速凝固过程中, Al-4 wt.%Ni亚共晶合金发生完全溶质截留效应, 从而形成亚稳单相固溶体. 当过冷度超过58K时, Al-5.69 wt.%Ni 共晶合金呈现从纤维状共晶向初生(Al) 枝晶为主的亚共晶组织演变. 若过冷度连续增大, Al-8 wt.%Ni过共晶合金可以形成全部纤维状共晶组织, 并且最终演变为粒状共晶.

关键词:

Growth mechanisms of dendrites and eutectics within undercooled liquid Al-Ni alloys

1.
Department of Applied Physics, Northwestern Polytechnical University, Xi'an 710072, China

Fund Project:

Project supported by the National Natural Science Foundation of China (Grant Nos. 51271150, 51371150, 51101123).

Received Date: 21 July 2014

Accepted Date: 02 October 2014

Published Online: 05 March 2015

Abstract: Al-4 wt.%Ni (hypoeutectic), Al-5.69 wt.%Ni (eutectic) and Al-8 wt.%Ni (hypereutectic) liquid alloys are highly undercooled and rapidly solidified under free fall condition. Theoretical calculations indicate that the coupled zone of (Al+Al3 Ni) fibrous eutectic is an unclosed region in the composition range from 4.8 to 15 wt.% Ni, which is strongly skewed towards the Al3 Ni phase side. It is found that the cooling rate and undercooling of liquid alloys would increase as the droplet size decreases. Then the microstructural evolution of Al-Ni alloys will be induced by the competitive growth of (Al) dendrite, Al3 Ni dendrite, and (Al+Al3 Ni) eutectic. During the rapid solidification of Al-4 wt.%Ni hypoeutectic alloy, complete solute trapping effect occurs and then causes the formation of metastable segregationless (Al) solid solution phase. When the droplet undercooling exceeds 58 K, the structural morphology of Al-5.69 wt.%Ni eutectic alloy shows a transition from (Al+Al3 Ni) fibrous eutectic to primary phase (Al)-dominated hypoeutectic structure. As the undercooling increases further, the fibrous eutectic becomes the unique microstructure of Al-8 wt.%Ni hypereutectic alloy, and finally evolves into a kind of granular eutectic.

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