高熵合金在焊接领域的应用研究现状

张秉刚; 于涛; 王厚勤; 韩柯

doi:10.11868/j.issn.1005-5053.2022.000046

高熵合金在焊接领域的应用研究现状

doi: 10.11868/j.issn.1005-5053.2022.000046

张秉刚^1, ,,
于涛¹,
王厚勤¹,
韩柯^{1, 2}

1.
哈尔滨工业大学先进焊接与连接国家重点实验室, 哈尔滨 150001
2.
江苏大学材料科学与工程学院, 江苏镇江 212013

基金项目: 先进焊接与连接国家重点实验室开放课题基金（AWJ-22M19）

详细信息

通讯作者:
张秉刚（1971—），男，博士，教授，研究方向为新材料及异种材料电子束焊接，联系地址：黑龙江省哈尔滨市南岗区西大直街92号哈尔滨工业大学（150001），E-mail: zhangbg@hit.edu.cn

中图分类号: TG42⁺4
计量
- 文章访问数: 242
- HTML全文浏览量: 81
- PDF下载量: 90
- 被引次数: 0
出版历程
- 收稿日期: 2022-03-21
- 修回日期: 2022-04-27
- 刊出日期: 2022-10-11

Application research status of high-entropy alloys in welding field

ZHANG Binggang^{1
, ,},
YU Tao¹,
WANG Houqin¹,
HAN Ke^{1, 2}

1.
State Key Laboratory of Advanced Welding and Joining, Harbin Institute of Technology, Harbin 150001, China
2.
School of Materials Science and Engineering, Jiangsu University, Zhenjiang 212013, Jiangsu, China

摘要

摘要: 高熵合金由于其新颖的设计理念及特殊性能，成为材料科学领域内新的研究热点。目前高熵合金的研究与应用还主要局限在材料的制备与合成方面，随着其在工业领域的广泛应用，必然涉及高熵合金在焊接领域的研究。本文从高熵合金同种材料的焊接、高熵合金和异种材料之间的焊接以及高熵合金作为填充材料进行异种材料之间的焊接三个方面展开叙述，重点分析焊接方法、高熵合金组分、焊接初始状态及焊接参数等因素对接头组织和性能的影响，特别在高熵合金作为填充材料时，利用高熵效应和迟滞扩散效应进行的界面调控尤为重要；对不同制备方法下的高熵合金涂层进行细致分析，介绍熔覆工艺、添加微量元素以及后热处理的影响，着重对比激光熔覆工艺下高熵合金涂层的耐磨性；通过对高熵合金在焊接领域的研究与应用进行总结，提出目前存在的问题主要是尚未建立高熵合金体系和焊接工艺间的对应标准及阐明缺陷的形成机理；并对未来高熵合金在焊接领域的重点研究方向进行了展望。
- 高熵合金 /
- 高熵效应 /
- 焊接 /
- 填充材料 /
- 涂层
Abstract: Owing to novel design concepts and their unique properties, high-entropy alloy (HEA) has become a hot topic in material science. At present, the studies and applications of high-entropy alloy are still mainly limited to the preparation and synthesis of materials. With its wide application in industry, it must involve the research of high-entropy alloy in welding field. This paper describes the welding of high-entropy alloy with the same material, welding between high-entropy alloy and dissimilar material, and welding between dissimilar material with high-entropy alloy as filler material. The paper focuses on analyzing the welding method, high entropy alloy components, the initial state of welding and welding parameters, and other factors on the joint organization and properties. While the high-entropy alloy is mainly applied as filler material, the high entropy effect and hysteresis diffusion effect for interface controlling are particularly important. Finally, the high-entropy alloy coatings under different preparation methods are analyzed in detail, introducing the cladding process, the addition of microelements, the effect of post-heat treatment, and comparing the wear resistance high-entropy alloy coatings under the laser melting process. By summarizing the research and application of high-entropy alloy in the welding field, it is pointed out that the current problems are that the corresponding standard between high-entropy alloy system and welding process has not been established and the formation mechanism of defects has not been clarified. The future research directions of high entropy alloy in welding field are proposed.
- high-entropy alloy /
- high-entropy effect /
- welding /
- filling material /
- coating

HTML全文

图 1 2016-2021年Web of Science中高熵合金焊接相关论文的出版数和引用数

Figure 1. Numbers of publication and citation of papers related to welding of high-entropy alloys in Web of Science from 2016 to 2021

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图 2 Al_0.3CoCrCu_0.3FeNi高熵合金组织EBSD分析^[17]　 (a) 焊后SZ的核心平均取向差；(b)SZ中心区域的晶粒平均取向差；(c) , (d) SZ和BM的反极图；(e) , (f) SZ和BM在法向-横向-焊接方向的极图

Figure 2. EBSD analysis of the microstructure of Al_0.3CoCrCu_0.3FeNi high-entropy alloy^[17] 　(a) Kernel average misorientation (KAM) map of SZ on AS; (b) grain average misorientation (GAM) map at center of SZ; (c) , (d) inverse pole figures of SZ and BM; (e) , (f) pole figures in ND-TD-WD frame of SZ and BM

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图 3 不同温度下Al₅(TiZrHfNb)₉₅/Ti₂AlNb接头的微观组织及形貌^[22]　 (a) 970 ℃; (b) 1010 ℃; (c) 1050 ℃; (d)1100℃

Figure 3. Morphology and microstructure of Al₅(TiZrHfNb)₉₅/Ti₂AlNb joints at different temperatures^[22] 　(a) 970 ℃; (b) 1010 ℃; (c) 1050 ℃; (d) 1100 ℃

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图 4 母材和接头应力-应变曲线 ^[25] 　(a) 室温；(b) 低温 (LN₂)

Figure 4. Stress-strain curves for base metals and welded joints ^[25]　 (a) at room temperature (RT); (b) at low temperature (LN₂)

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图 5 304SS和Q235钢的激光沉积焊接中添加不同填充层焊缝区的胞状晶组织^[31] 　(a) (CrMnFe)₁(CoNi)₉；(b) (CrMnFe)₅(CoNi)₅； (c) (CrMnFe)₉(CoNi)₁；(d) 异种接头的硬度分布； (e) 三点弯曲实验中母材和异种接头的典型应力-应变曲线

Figure 5. Cellular crystal microstrctures of weld zone in laser deposition welding of 304SS and Q235 steel with different filler layers^[31]　 (a) (CrMnFe)₁(CoNi)₉; (b) (CrMnFe)₅(CoNi)₅; (c) (CrMnFe)₉(CoNi)₁; (d) hardness distributions of dissimilar joints; (e) typical stress-strain curves of BM and dissimilar joints in three-point bending tests

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图 6 高熵合金涂层表面SEM形貌^[51]　 (a) 无Nb元素涂层；(b) 含Nb元素涂层

Figure 6. SEM images of the surface of CoCrCuFeNi high-entropy alloy coatings ^[51]　 (a) coating without Nb; (b) coating with Nb

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表 1 高熵合金焊接的接头力学性能^{[8-9,13,15,17-18,20,23-24,31-32,36,38]}

Table 1. Mechanical properties of welding joints of HEA^{[8-9,13,15,17-18,20,23-24,31-32,36,38]}

Base metal	Filler material	Welding method	Optimum properties	References
Al_0.2CoCrFeNiMo_0.5	—	Gas tungsten arc welding (GTAW)	Yield strength: 300 MPa Tensile strength: 762 MPa Fracture strain: 15.5%	[8]
CrMnFeCoNi	—	Electron beam welding (EBW)	Tensile strength: 77 K：985 MPa 293 K：565 MPa	[9]
AlCoCrFeNi_2.1	—	Laser beam welding (LBW)	Tensile strength: 1201 MPa	[13]
AlCoCrFeNi	Ni-based	Brazing	Shear strength: (687.2±23.2) MPa	[15]
Al_0.3CoCrCu_0.3FeNi	—	Friction stir welding (FSW)	Yield strength: 920 MPa Elongation rate: 37%	[17]
Al_0.1CoCrFeNi and AISI304 stainless steel	—	Electron beam welding (EBW)	Yield strength: (310±10) MPa Tensile strength: (560±15) MPa	[18]
CoCrFeMnNi and 316 stainless steel	—	Laser beam welding (LBW)	Tensile strength: 450 MPa	[20]
AlCoCrFeNi and FGH98	BNi-2	Brazing	Shear strength: 454 MPa	[23]
Fe₃₉Mn₂₀Co₂₀Cr₁₅Si₅Al₁ and Al-7050	—	Friction stir welding (FSW)	Tensile strength: 400 MPa Elongation rate: 10%	[24]
304SS and Q235	(CrMnFe)₅(CoNi)₅ powders	Laser deposition welding	Bending strength: (983±15) MPa	[31]
TC4 titanium and 6082 aluminum	CoNiCuNb_0.5V_1.5	Laser beam welding (LBW)	Tensile strength: 190 MPa	[32]
ZSC ceramic and GH99 superalloy	Ti/FeCoNiCrCu composite filler layer	Brazing	Shear strength: 71 MPa	[36]
ZrB₂-20vol%SiC and pure Nb	CoFeCrNiCu	Brazing	Shear strength: 216 MPa	[38]

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表 2 激光熔敷制备的具有高硬度和高耐磨性高熵合金涂层研究报道^[55-66]

Table 2. Literatures of HEA coating prepared by laser cladding with high microhardness and wear resistance^[55-66]

Substrate	Composition of high-entropy alloy coatings	Hardness and wear resistance	References
304 stainless steel	AlCoCrFeNiNb_x (x=0-1)	When x is 0.75, the wear resistance of the coating is optimal, and the Vickers hardness increases with increasing Nb content. The changes of microstructure are quiaxed crystal to hypoeutectic and to hypereutectic in AlCoCrFeNiNb_x alloy coatings	[55]
45 steel	FeNiCoCrTi_0.5Nb_x (x=0.25-1)	FeNiCoCrTi0.5Nb_0.5 coating has the highest average hardness of 766.62HV, with the best wear resistance and the lowest wear rate, and all coatings are with abrasive wear mechanisms	[56]
M2 tool steel	MoFe_1.5CrTiWAlNb_x (x=1.5-2.5,3)	The hardness and wear resistance of the coatings increase as Nb content increases, with the best performance at x=3	[57]
4Cr5MoSiV steel	FeCoCrNiMnAl_x (x=0-0.75)	Addition of Al can promote the formation of BCC phase and refine the grain. With the increase of Al content, the microhardness and frictional-mass-loss of room temperature show that the increasing and decreasing trend is from 224.4 HV_0.5 to 344.2 HV_0.5 and 6.0 mg to 1.1 mg respectively	[58]
Q235	Al_xMo_0.5NbFeTiMn₂ (x=1-2)	Addition of Al can form BCC and (Nb,Ti)C carbide phases, which promotes solid solution strengthening. As Al content increases, the properties of the coating increase, with the hardness of 1098.5HV_0.2 at x=2 is five times than that of substrate	[59]
45 steel	AlCrCoNiFeCTa_x (x=0-1)	Addition of Ta increases the wear resistance of AlCrCoNiFeCTa_x high-entropy coating in both air and NaCl solutions. At x = 0.5 and 1.0, the wear rates of the coatings in NaCl solution are reduced by 17% and 12% compared to air. Solid solution strengthening, diffuse strengthening of Ta and Fe and the presence of TaC are the main factors of the enhancement of hardness	[60]
ASTM 4140	FeCoCrNi-WC	Compared to plasma beam cladding, laser cladding has a greater ability to retain WC particles, resulting in coatings with twice the microhardness and better wear resistance. This is because plasma coating causes decarburization and oxidation of WC particles, which deteriorates the properties	[61]
Q235	AlCoCrFeNi-xNbC	Addition of NbC ceramic particles can reduce the content of FCC phases in the original high-entropy coating and inhibits grain growth. The hardness and wear resistance of AlCoCrFeNi-xNbC coating are significantly improved and it is optimal at x=20% with the hardness of 525HV	[62]
304 stainless steel	CoCrCuFeNiSi_0.2(Ti,C)_x (x=0-1.5)	Addition of Ti and C elements can lead to in-situ synthesis of TiC ceramic phases at the grain boundaries of the high entropy mircrostrcture, which enhances the microhardness and wear resistance of the coatings. At x = 1.0, the average hardness and wear volume of the coating are 498.5HV_0.2 and 0.42 mm³ respectively	[63]
40Cr	Al₃CoCrCu_1/2FeMoNiTi	The high-entropy alloy coatings have an obvious age-hardening effect, and the best age-hardening effect can be obtained under annealing at 700 °C, with a maximum hardness of 924HV	[64]
AISI 1045	AlCoCrFeNiTi_0.8	As the heat treatment temperature increases, coarsening and Ostwald ripening of the precipitated phase occur, which reduces the wear resistance of the high-entropy coatings	[65]
Q245R	CrFeMoNbTiW	The wear resistance and microhardness of the coatings are significantly increased under post heat treatment conditions of 800-1000 °C/10 h, with a maximum hardness of 1176HV_0.2, which is an increase of 72.5% compared to the unheated coatings	[66]

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