时效时间对铸态Fe56.5Ni30Al10.5Nb3形状记忆合金组织与性能的影响

陈朝霞; 彭文屹

doi:10.11868/j.issn.1005-5053.2020.000015

时效时间对铸态Fe_56.5Ni₃₀Al_10.5Nb₃形状记忆合金组织与性能的影响

doi: 10.11868/j.issn.1005-5053.2020.000015

陈朝霞^1,2,
彭文屹^1, ,

1.
南昌大学材料科学与工程学院，南昌 330013
2.
华东交通大学材料科学与工程学院，南昌 330013

基金项目: 国家自然科学基金（51461030）；江西省教育厅科学技术研究项目（GJJ160481）

详细信息

通讯作者:
彭文屹（1968—），女，博士，教授，主要研究方向为金属功能材料、材料表面改性，E-mail：wypengtougao@163.com

中图分类号: TG166
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- 被引次数: 0
出版历程
- 收稿日期: 2020-01-19
- 修回日期: 2020-08-20
- 网络出版日期: 2020-08-20
- 刊出日期: 2020-10-01

Effect of aging time on microstructure and properties of as-cast Fe_56.5Ni₃₀Al_10.5Nb₃ shape memory alloy

Zhaoxia CHEN^1,2,
Wenyi PENG^{1
, ,}

1.
School of Materials Science and Engineering, Nanchang University, Nanchang 330031, China
2.
School of Materials Science and Engineering, East China Jiaotong University, Nanchang 330031, China

摘要

摘要: 研制一种无Co添加的Fe_56.5Ni₃₀Al_10.5Nb₃（atom fraction/%）合金，在制备中直接对铸态合金进行固溶和650 ℃下的时效处理。利用扫描电子显微镜（SEM）和X射线衍射仪（XRD）分析合金的组织和物相，同时对其进行硬度测试、抗压强度测试、超弹性测试及电子背散射衍射（EBSD）测试。结果表明：时效时间处于0~95 h的范围时，合金内均能析出纳米尺寸的γ′相和细小的β相，在室温都展现出超弹性，最大超弹性应变达10.62%；γ′相在晶内析出，在时效时间为70 h时分布最密集，时间超过70 h后进入长大阶段；β相在晶内和晶界都能析出，析出量随时效时间的延长而增加；β相的析出能促进硬度的增加，但其在晶界的生成对强度不利；随着时效时间的延长，合金硬度持续增加，抗压强度和超弹性应变均先增加后减小，且均在时间为70 h时取得最大值；合金内部纳米尺寸的γ′析出相及较强的{100}<001>织构对其超弹性影响较大。
- 形状记忆合金 /
- 时效 /
- 超弹性 /
- Fe-Ni-Al-Nb /
- 织构
Abstract: A Co-free Fe_56.5Ni₃₀Al_10.5Nb₃ (atom fraction/%) alloy was developed. In the preparation, the as-cast alloy was subjected to aging treatment at 650 ℃ and followed solution treatment directly. Scanning electron microscope (SEM) and X-ray diffractometer (XRD) were used to analyze the microstructure and phases of the alloy. At the same time, the hardness test, compressive strength test, superelasticity test and electron backscatter diffraction (EBSD) test were performed. The results show that, when the aging time range from 0 to 95 h, the alloy can exhibit superelasticity at room temperature with the maximum superelastic strain of 10.62%. There are nano-sized γ′ precipitates and fine β precipitates in the alloy. The γ′ phase is formed in the grain interiors and is most densely distributed when the aging time is 70 h. After the aging time exceeds 70 h, the γ′ phase enters the growth stage. The β phase can be formed both in the grain interiors and in the grain boundaries, and the amount of β precipitates increases with the aging time. The precipitation of the β phase can improve the hardness, but its formation in the grain boundaries is detrimental to the strength. With the increase of aging time, the hardness of the alloy increases continuously, and the compressive strength and superelastic strain first increase and then decrease, and reach the maximum value at the time of 70 h. The nano-sized γ′ precipitates and strong {100}<100> texture in the alloy have a great influence on its superelasticity.
- shape memory alloys /
- aging /
- superelasticity /
- Fe-Ni-Al-Nb /
- texture

HTML全文

图 1 Fe_56.5Ni₃₀Al_10.5Nb₃合金经650 ℃时效不同时间后在室温下的SEM图像　（a）20 h；（b）45 h；（c）70 h；（b）90 h

Figure 1. SEM images of Fe_56.5Ni₃₀Al_10.5Nb₃ alloy at room temperature aged at 650 ℃ for different time　（a）20 h；（b）45 h；（c）45 h；（d）90 h

下载: 全尺寸图片幻灯片

图 2 650 ℃时效20 h的合金在低倍下的组织形貌（a）及Nb元素面分布图（b）

Figure 2. Microstructure of the alloy aged at 650 ℃ for 20 h at low magnification （a） and Nb surface distribution diagram （b）

下载: 全尺寸图片幻灯片

图 3 合金经固溶及650 ℃下时效20 h，45 h，70 h，95 h后在室温下的XRD图谱

Figure 3. XRD patterns of the alloy at room temperature after solution treatment and aged at 650 ℃ for 20 h，45 h，70 h and 95 h.

下载: 全尺寸图片幻灯片

图 4 合金硬度（a）和抗压强度（b）随时效时间的变化

Figure 4. Changes of hardness（a） and compressive strength （b） of the alloy with aging time

下载: 全尺寸图片幻灯片

图 5 合金经650 ℃下时效不同时间后在室温下的应力-应变曲线　（a）20 h；（b）45 h；（c）70 h；（b）90 h

Figure 5. Stress-strain curves of the alloy at room temperature aged at 650 ℃ for different time　（a）20 h；（b）45 h；（c）45 h；（d）90 h

下载: 全尺寸图片幻灯片

图 6 650 ℃下时效70 h合金内晶粒的{100}极图（a）、反极图（b）和ODF截面图（c）

Figure 6. {100} pole figure（a），inverse pole figure（b）and ODFs for texture of the alloy aged at aged at 650 ℃ for 70 h

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参考文献(18)

[1]	谭慧俊,王子运,张悦. 形状记忆合金在飞行器进气道中的应用研究进展[J]. 南京航空航天大学学报,2019,51(4):438-448. TAN H J,WANG Z Y,ZHANG Y. Review of applications of shape memory alloy in inlets[J]. Journal of Nanjing University of Aeronautics& Astronautics,2019,51(4):438-448.)
[2]	邹芹,党赏,李艳国,等. Fe-基形状记忆合金的研究进展[J]. 材料导报,2019,33(12):3955-3962. ZOU Q,DANG S,LI Y G,et al. Research progress of iron-based shape memory alloys:a review[J]. Materials Reports,2019,33(12):3955-3962.)
[3]	WAEL A,HUSEYIN S. Superelasticity and functional fatigue of single crystalline FeNiCoAlTi iron-based shape memory alloy[J]. Materials and Design,2018,160:642-651. doi: 10.1016/j.matdes.2018.10.003
[4]	OMORI T,ABE S,TANAKA Y,et al. Thermoelastic martensitic transformation and superelasticity in Fe-Ni-Co-Al-Nb-B polycrystalline alloy[J]. Scripta Materialia,2013,69(11/12):812-815. doi: 10.1016/j.scriptamat.2013.09.006
[5]	TANAKA Y,HIMURO Y,KAINUMA R,et al. Ferrous polycrystalline shape-memory alloy showing huge superelasticity[J]. Science,2010,327:1488-1490. doi: 10.1126/science.1183169
[6]	VOLLMER M,KROOΒ P,KARAMAN I,et al. On the effect of titanium on quenching sensitivity and pseudoelastic response in Fe-Mn-Al-Ni-base shape memory alloy[J]. Scripta Materialia,2017,126:20-23. doi: 10.1016/j.scriptamat.2016.08.002
[7]	VOLLMER M,SEGEL C,KROOΒ P,et al. On the effect of gamma phase formation on the pseudoelastic performance of polycrystalline Fe-Mn-Al-Ni shape memory alloys[J]. Scripta Materialia,2015,108:23-26. doi: 10.1016/j.scriptamat.2015.06.013
[8]	HUADONG F,HUIMIN Z,YIXIONG Z,et al. Enhancement of superelasticity in Fe-Ni-Co-Based shape memory alloys by microstructure and texture control[J]. Procedia Engineering,2017,207:1505-1510. doi: 10.1016/j.proeng.2017.10.1084
[9]	TSENG L W,MA J,VOLLMER M,et al. Effect of grain size on the superelastic response of a FeMnAlNi polycrystalline shape memory alloy[J]. Scripta Materialia,2016,125:68-72. doi: 10.1016/j.scriptamat.2016.07.036
[10]	OMORI T,IWAIZAKO H,KAINUMA R. Abnormal grain growth induced by cyclic heat treatment in Fe-Mn-Al-Ni superelastic alloy[J]. Materials and Design,2016,101:263-269. doi: 10.1016/j.matdes.2016.04.011
[11]	OMORI T,KUSAMA T,KAWATA S,et al. Abnormal grain growth induced by cyclic heat treatment[J]. Science,2013,341:1500-1502. doi: 10.1126/science.1238017
[12]	OZCANA H,MA J,WANG S J,et al. Effects of cyclic heat treatment and aging on superelasticity in oligocrystalline Fe-Mn-Al-Ni shape memory alloy wires[J]. Scripta Materialia,2017,134:66-70. doi: 10.1016/j.scriptamat.2017.02.023
[13]	SAGARADZEN V V,SHABASHOV V A,KATAEVA N V,et al. The anomalous diffusion processes “dissolution-precipitation” of the γ' phase Ni₃Al in an Fe-Ni-Al alloy during low-temperature deformation[J]. Materials Letters,2016,172:207-210. doi: 10.1016/j.matlet.2015.11.078
[14]	渠桂丽,彭文屹,陈朝霞,等. 时效时间对 FeNiCoAlNbB 合金组织和性能的影响[J]. 金属热处理,2015,40(3):109-114. QU G L,PENG W Y,CHEN Z X,et al. Influence of aging time on microstructure and mechanical properties of FeNiCoAlNbB alloy[J]. Heat Treatment of Metals,2015,40(3):109-114.)
[15]	CHEN Z X,PENG W Y. Fe-Ni-Al-Ta polycrystalline shape memory alloys showing excellent superelasticity[J]. Functional Materials Letters,2020,13(1):1950096-1-4.
[16]	BALDAN A. Progress in ostwald ripening theories and their applications to the γ'-precipitates in nickel-base superalloys:Part Ⅱ Nickel-base superalloys[J]. Journal of Materials Science,2002,37(12):2397-2400.
[17]	徐祖耀, 江伯鸿, 杨大智, 等. 形状记忆材料[M]. 上海: 上海交通大学出版社, 2000. XU Z Y, JIANG B H, YANG D Z, et al. Shape memory materials[M]. Shanghai: Shanghai Jiao Tong University Press, 2000.
[18]	MA J,KOCKAR B,EVIRGEN A,et al. Shape memory behavior and tension–compression asymmetry of a FeNiCoAlTa single-crystalline shape memory alloy[J]. Acta Materialia,2012,60(5):2186-2195. doi: 10.1016/j.actamat.2011.12.047