李福泉,李明伟,孟祥旭
(先进焊接与连接国家重点实验室(哈尔滨工业大学),哈尔滨 150001)
摘要:
高速列车车体轻量化制造的迫切需求,使得铝合金结构在车体制造中得到广泛应用,而铝合金焊接也成为高铁车体制造的关键工艺。本文采用激光填丝焊方法焊接6005A-T6铝合金,并对焊接接头进行了固溶/时效热处理。利用扫描电镜、XRD能谱分析及拉伸实验,对焊后热处理的焊接接头组织及性能进行研究。研究发现,与母材相比,由于焊接接头中Mg2Si强化相的消失,使得6005A铝合金激光填丝焊接接头拉伸性能下降。通过对焊接接头进行的固溶/时效焊后热处理,实现了焊接接头中β″相、β′相和Q′相的强化相析出,而强化相的析出有利于焊接接头性能的改善。显微硬度实验表明,焊后经热处理的焊接接头,各区域显微硬度显著提高。随着固溶时间的增加,焊接接头经时效处理达到峰时效状态所需的时间减少。基于焊接接头硬度比较,确定550 ℃固溶1.5 h/175 ℃ 时效8 h为优化的焊后热处理规范。采用优化的焊后热处理规范,焊接接头的拉伸强度增加至340 MPa,高于母材的拉伸强度；热处理后接头延伸率为11.6%,达到母材延伸率的65.2%。采用固溶/时效焊后热处理方式可提高激光焊接接头的性能。
关键词: 6005A铝合金 激光填丝焊 焊后热处理 强化相 拉伸性能
DOI：10.11951/j.issn.1005-0299.20200253
分类号:TG456.7
文献标识码:A
基金项目:国家重点研发计划项目(2016YFB1200506-11).
Effect of heat treatment on microstructure and property of 6005A aluminum alloy laser welding joint
LI Fuquan, LI Mingwei, MENG Xiangxu
(State Key Laboratory of Advanced Welding and Joining (Harbin Institute of Technology), Harbin 150001, China)
Abstract:
To meet the lightweight requirement in high speed train structure, the aluminum structure has been widely utilized in the fabrication of the train body, and welding of aluminum alloy has become the essential process for the fabrication of the train body. In this paper, 6005A-T6 aluminum alloy was laser welded with filler wire. At the same time, the "soild solution/aging" heat treatment was conducted on the welding joint. Based on electron microscopy investigation, XRD analysis and tensile experiment, microstructure and property of welding joint after post-weld heat treatment was studied. After laser welding, tensile property of the welding joint decreased compared with the substrate of 6005A, which was attributed to the disappearance of Mg2Si strengthening phase at the welding joint. After the post-weld heat treatment of "soild solution/aging", β″ phase, β′ phase and Q′ phase precipitated in welding joint, which was beneficial to its property. After the heat treatment, microhardness of the welding joint increased compared with that only treated by laser welding. Microhardness measurement show that aging time of "solid solution/aging" heat treatment needed to reach peak effect decreased with the increase of solid solution time. Based on comparisons of hardness distribution of welding joint, 550 ℃ solid state 1.5 h/175 ℃ aging 8 h was selected as the optimized post-weld heat treatment parameters. Tensile property of the welding joint was increased to 340 MPa under the optimized heat treatment, which was higher than that of the substrate. Meanwhile, the elongation rate was improved to 11.6% after the heat treatment, which was 65.2% of that of the substrate. In conclusion, the property of welding joint was improved by the "soild solution/aging" heat treatment
Key words: 6005A aluminum alloy laser filler wire welding post-weld heat treatment strengthening phase tensile property
李福泉, 李明伟, 孟祥旭. 热处理对6005A铝合金激光焊接头组织和性能的影响[J]. 材料科学与工艺, 2021, 29(2): 44-50. DOI: 10.11951/j.issn.1005-0299.20200253.
LI Fu-quan, LI Ming-wei, MENG Xiang-xu. Effect of heat treatment on microstructure and property of 6005A aluminum alloy laser welding joint[J]. Materials Science and Technology, 2021, 29(2): 44-50. DOI: 10.11951/j.issn.1005-0299.20200253.
基金项目 国家重点研发计划项目(2016YFB1200506-11) 通信作者 李福泉, E-mail: lifuquan@hit.edu.cn 作者简介 李福泉(1972—), 男, 副教授 文章历史 收稿日期: 2020-09-10 网络出版日期: 2020-12-10
Contents Abstract Full text Figures/Tables PDF
热处理对6005A铝合金激光焊接头组织和性能的影响
李福泉
, 李明伟, 孟祥旭 先进焊接与连接国家重点实验室(哈尔滨工业大学), 哈尔滨 150001
收稿日期: 2020-09-10; 网络出版日期: 2020-12-10
基金项目: 国家重点研发计划项目(2016YFB1200506-11)
作者简介: 李福泉(1972—), 男, 副教授.
通信作者: 李福泉, E-mail: lifuquan@hit.edu.cn.
摘要: 高速列车车体轻量化制造的迫切需求, 使得铝合金结构在车体制造中得到广泛应用, 而铝合金焊接也成为高铁车体制造的关键工艺。本文采用激光填丝焊方法焊接6005A-T6铝合金, 并对焊接接头进行了固溶/时效热处理。利用扫描电镜、XRD能谱分析及拉伸实验, 对焊后热处理的焊接接头组织及性能进行研究。研究发现, 与母材相比, 由于焊接接头中Mg2Si强化相的消失, 使得6005A铝合金激光填丝焊接接头拉伸性能下降。通过对焊接接头进行的固溶/时效焊后热处理, 实现了焊接接头中β″相、β′相和Q′相的强化相析出, 而强化相的析出有利于焊接接头性能的改善。显微硬度实验表明, 焊后经热处理的焊接接头, 各区域显微硬度显著提高。随着固溶时间的增加, 焊接接头经时效处理达到峰时效状态所需的时间减少。基于焊接接头硬度比较, 确定550℃固溶1.5 h/175℃时效8 h为优化的焊后热处理规范。采用优化的焊后热处理规范, 焊接接头的拉伸强度增加至340 MPa, 高于母材的拉伸强度; 热处理后接头延伸率为11.6%, 达到母材延伸率的65.2%。采用固溶/时效焊后热处理方式可提高激光焊接接头的性能。
关键词: 6005A铝合金 激光填丝焊 焊后热处理 强化相 拉伸性能
Effect of heat treatment on microstructure and property of 6005A aluminum alloy laser welding joint
LI Fu-quan
, LI Ming-wei, MENG Xiang-xu State Key Laboratory of Advanced Welding and Joining (Harbin Institute of Technology), Harbin 150001, China
Abstract: To meet the lightweight requirement in high speed train structure, the aluminum structure has been widely utilized in the fabrication of the train body, and welding of aluminum alloy has become the essential process for the fabrication of the train body. In this paper, 6005 A-T6 aluminum alloy was laser welded with filler wire. At the same time, the "soild solution/aging" heat treatment was conducted on the welding joint. Based on electron microscopy investigation, XRD analysis and tensile experiment, microstructure and property of welding joint after post-weld heat treatment was studied. After laser welding, tensile property of the welding joint decreased compared with the substrate of 6005 A, which was attributed to the disappearance of Mg2Si strengthening phase at the welding joint. After the post-weld heat treatment of "soild solution/aging", β″ phase, β′ phase and Q′ phase precipitated in welding joint, which was beneficial to its property. After the heat treatment, microhardness of the welding joint increased compared with that only treated by laser welding. Microhardness measurement show that aging time of "solid solution/aging" heat treatment needed to reach peak effect decreased with the increase of solid solution time. Based on comparisons of hardness distribution of welding joint, 550 ℃ solid state 1.5 h/175 ℃ aging 8 h was selected as the optimized post-weld heat treatment parameters. Tensile property of the welding joint was increased to 340 MPa under the optimized heat treatment, which was higher than that of the substrate. Meanwhile, the elongation rate was improved to 11.6% after the heat treatment, which was 65.2% of that of the substrate. In conclusion, the property of welding joint was improved by the "soild solution/aging" heat treatment
Keywords: 6005A aluminum alloy laser filler wire welding post-weld heat treatment strengthening phase tensile property
6005A铝合金是典型6系(Al-Mg-Si)铝合金，由于其轻量化、易成型等特点，适合应用于高速列车车体的铝合金结构制造[1-3], 其主要合金元素为Mg及Si, 并添加有少量的Mn、Cr、Cu等元素[4]。6005A中主要包含有Mg2Si(β)强化相及All3Cu2Mg9Si7(Q)强化相，这些强化相具有自然时效能力[5-6]。单纯Al-Mg-Si合金的时效析出相序列为“SSSS团簇→GP区→β″相→β′相→β相”。与之相比，Cu元素的微量添加使其时效析出相序列发生变化，转变为“SSSS团簇→GP区→β″相→β′相+Q′相→β相+Q相”[7-10]。
激光填丝焊接除具有传统激光焊接的优点外，焊丝的添加提高了激光焊接工艺对装配间隙的适应性，焊丝材料的冶金作用也有利于改善接头组织[11-13]。激光填丝焊接6系铝合金常选用Al-Si焊丝，焊接后Mg、Si等合金元素熔入Al基体中，形成过饱和α-Al固溶体，导致Mg2Si(β)强化相在焊缝区无法形成。同时，焊接热循环作用导致热影响区强化相消融，致使焊接接头出现软化现象[14]。对Al合金焊接接头进行焊后热处理，能够促使焊接接头组织稳定、强化相再沉淀析出，是解决焊接接头软化问题的有效工艺技术[15-16]。
本文基于优化的激光填丝焊工艺焊接6005A铝合金，研究焊后热处理对焊接接头组织及性能的影响。焊后热处理以“固溶/时效”的方式进行，以促进强化相的重新溶解及析出。基于对析出相及接头性能的分析，获得优化的热处理规范，以期为6005A铝合金激光焊接的应用提供基础。
1 试验试验母材采用尺寸为120 mm×60 mm×4 mm的6005A-T6铝合金板。表 1为母材的化学成分，图 1为其SEM微观组织。
表1(Table 1)
表 1 6005A铝合金化学成分(质量分数/%)Table 1 Chemical composition of 6005A aluminum alloy (wt.%)Mg Si Mn Cr Ti Cu Fe Zn Al 0.4~0.6 0.6~0.9 0.10 0.10 0.10 0.10 0.35 0.10 余量
表 1 6005A铝合金化学成分(质量分数/%)Table 1 Chemical composition of 6005A aluminum alloy (wt.%)
图 Figure1(Fig.Figure1)
图 1 6005A铝合金基体微观组织形貌Fig.1 Microstructure of 6005A aluminum alloy substrate激光填丝焊选用Φ1.2 mm的ER5356焊丝，焊丝成分见表 2。焊接过程采用IPG公司(德国)YLR-5000光纤激光器；送丝设备采用FRONIUS公司(奥地利)KD4010送丝机。基于激光工艺实验优化后选用的激光工艺参数为：激光功率4 950 W, 扫描速度0.03 m/s, 送丝速度310 cm/min, 离焦量-4 mm, 保护气流量15 L/min。对获得的激光添丝焊接头进行焊后热处理。焊接接头焊后热处理比较实验步骤如下：1)加热升温固溶：将焊接件以15 ℃/min的加热速率加热至550 ℃固溶温度；2)固溶保温：550 ℃固溶温度下保温0.5、1、1.5、2 h; 3)冷却：将保温后的焊件水冷至室温；4)加热升温时效：以10 ℃/min的速率加热至175 ℃; 5)时效保温：175 ℃时效温度下保温6、8、10、12 h; 6)冷却：时效后空冷至室温。热处理实验采用TSX1400的空气马弗炉进行。
表2(Table 2)
表 2 ER5356焊丝化学成分(质量分数/%)Table 2 Chemical composition of ER5356 (wt.%)Mg Cu Ti Cr Mn Si Fe Zn Al 4.5~5.5 ≤0.1 0.06~0.20 0.05~0.20 0.05~0.20 ≤0.25 ≤0.4 ≤0.1 余量
表 2 ER5356焊丝化学成分(质量分数/%)Table 2 Chemical composition of ER5356 (wt.%)
分别切取焊接态及焊后热处理态金相试样。试样经研磨抛光后进行腐蚀，腐蚀试剂配比为1%HF+1.5%HCl+2.5%HNO3+95%H2O。依据GB/T 3246.2-2000标准对焊接接头进行阳极覆膜以观察晶粒组织。采用Empyrean型射线衍射仪测定物相。用光学显微镜(OLYMPUS GX71)及扫描电镜(Quanta 200FEG)、电子探针(JXA-8230)对试样进行显微组织的观察。利用透射电镜(Talos F200X)进行焊接接头析出相的观测。采用达芬奇D8 ADVANCE型射线衍射仪对焊接接头进行X射线衍射分析(XRD)。用MH-3型硬度计进行焊接接头显微硬度测试，测试中载荷设定为200 g, 保压时长10 s。接头拉伸性能测试采用Instron-5569电子万能试验机，拉伸制样按照GB/T2651-2008标准制备，拉伸速度为2 mm/min。
2 结果与分析2.1 激光填丝焊接头组织分析图 2为获得的6005A铝合金激光填丝焊焊接接头形貌。由图 2(a)和(b)可见，焊接接头的熔合区及焊缝晶粒形态区别明显，其中：熔合区的晶粒尺寸相对粗大、靠近熔合区焊缝区域的晶粒呈柱状晶形态；由靠近熔合区区域向焊缝中心区域，晶粒形态呈现柱状晶向树枝晶，进而焊缝中心等轴晶的变化。图 2(c)显示，焊缝柱状晶的生长具有明显的方向性。由图 2(d)可见，母材有明显的轧制痕迹，晶粒内存在弥散分布颗粒相，其中，尺寸较大的白色颗粒相为杂质相，Mg2Si强化相则相对尺寸较小，呈现颗粒状形态分布于晶内。
图 Figure2(Fig.Figure2)
图 2 激光填丝焊接头各区域金相组织Fig.2 Metallographic structure of welding joint with filler wire: (a) welding joint; (b) fusion zone and weld zone; (c) morphology of weld grain; (d) substrate对焊接接头的焊缝区域及母材区域分别进行X射线衍射分析，结果如图 3及图 4所示，可以看到，焊缝中主要包含的组成相是α-Al相。与母材相比，焊缝中Mg2Si相消失。根据Al-Mg-Si三元相图，平衡凝固条件下，按照其相凝固析出的顺序，α-Al相会先于Mg2Si相析出。激光焊接所形成熔池尺寸小，该熔池凝固具有瞬态快速非平衡凝固的特点，显著不同于平衡凝固。这种非平衡凝固，在析出α-Al相后熔池已经凝固完成，没有足够的熔池停留时间以析出Mg2Si(β)相。焊接后Mg、Si等合金元素熔入Al基体中，形成过饱和α-Al固溶体。Mg2Si(β)强化相在焊缝区无法形成，这必然会对焊接接头部位的性能产生影响。
图 Figure3(Fig.Figure3)
图 3 焊缝区域的XRD谱图Fig.3 XRD pattern of weld zone图 Figure4(Fig.Figure4)
图 4 母材区域的XRD谱图Fig.4 XRD pattern of substrate2.2 焊后热处理焊接接头组织焊后的“固熔/时效”热处理会影响焊接接头的组织形态。固溶1.5 h/时效12 h经焊后热处理的焊接接头金相形貌见图 5。由图 5(a)可见，熔合区附近的焊缝边缘存在沿晶界的灰色链条块状相，靠近熔合区的焊缝内有黑色点状颗粒相析出。由图 5(b)焊缝中心区域的组织形貌可以发现，与熔合区附近相似，在焊缝中心区域沿晶界轮廓方向存在灰色链条块状相，同时在晶内及晶界发现有黑色点状颗粒相弥散分布的情况。
图 Figure5(Fig.Figure5)
图 5 热处理后焊接接头组织(固溶1.5 h/时效12 h)Fig.5 Microstructure of welding joint after heat treatment (solid solution 1.5 h/aging 12 h): (a) area near fusion zone; (b) weld zone图 6为经过固溶1.5 h/时效12 h焊后热处理焊缝及未热处理焊缝的TEM分析图像及其衍射斑点。可以看出，经过热处理的焊缝，存在针状β″相(Mg5Si6)、棒状β′相(Mg9Si5)及块状Q′相(Al3.8Mg8.6Si7.0Cu1.0)等强化相的析出。对比图 6(b)和图 6(d)的焊缝衍射斑点图案发现，当经过焊后热处理导致强化相析出时，会有“十字花样”衍射斑纹出现。
图 Figure6(Fig.Figure6)
图 6 焊缝组织TEM图像及其衍射斑点Fig.6 TEM micrograph and diffraction pattern of weld structure: (a) weld without heat treatment (TEM); (b) diffraction pattern of weld without heat treatment; (c) weld after heat treatment (TEM); (d) diffraction pattern of weld after heat treatment图 7为经焊后热处理的焊缝区域元素面分布。由图 7(a)可见，经焊后热处理的焊缝中有较多片状第二相存在。经过面扫描发现，这些片状第二相区域富含Si、Fe、Cr、Mn元素，同时该区域的Al元素含量保持基本稳定，可以推断这些片状第二相为Al-(Si, Fe, Cr, Mn)杂质相。图 8所示分别为未经焊后热处理的焊缝和焊后热处理焊缝的组织形貌。由图 8可见，激光焊后的焊缝中杂质相尺寸较小，其形状大多为圆形；经过焊后热处理的焊缝中，杂质相尺寸明显变大，且其形态多为块状。
图 Figure7(Fig.Figure7)
图 7 经焊后热处理的焊缝区域元素面分布Fig.7 Element distribution of weld zone after heat treatment图 Figure8(Fig.Figure8)
图 8 未经焊后热处理(a) 及经焊后处理(b) 组织的试样焊缝Fig.8 Microstructure of weld zone: (a) without heat treatment; (b) after heat treatment2.3 焊接接头显微硬度焊接接头的硬度分布取决于组织及相分布，通过测定微观硬度可以反映强化相在焊接接头中的分布情况。图 9为不同热处理规范下焊接接头整体硬度分布曲线，以及未经焊后热处理焊接接头的平均硬度，可以看到，与激光填丝焊焊接接头相比，经焊后热处理后的焊接接头各区域显微硬度显著增加。
图 Figure9(Fig.Figure9)
图 9 不同固溶/时效热处理下的焊接接头硬度曲线Fig.9 Hardness curves of welding joint after heat treatment of different solid state/aging conditions: (a) solid solution 0.5 h/aging; (b) solid solution 1.0 h/aging; (c) solid solution 1.5 h/aging; (d) solid solution 2.0 h/aging比较图 9中的显微硬度曲线变化能够发现，随固溶时间增加，焊后热处理接头硬度达到峰值所需的时效时间缩短。当固溶时间为1.0 h时，如图 9(b)中，随着时效时间的变化，显微硬度达到峰时效需要10 h; 与之相比，当固溶时间为2.0 h时，如图 9(d)中，随着时效时间的变化，显微硬度达到峰时效需要6 h。由此可以认为，固溶时间的增加能够降低焊接接头内部的元素偏析，使其元素分布更均匀；在固溶保温结束进行水淬后，其组织分布达到峰时效所需时间也减少。由图 9中硬度分布可以发现，固溶1.5 h/时效8 h时，焊缝区域平均硬度最高，且波动较小，可以确定其为优化的焊后热处理规范。
2.4 拉伸性能分析图 10为激光填丝焊后未热处理、热处理(固溶1.5 h/时效8 h)以及6005A母材基体的应力-应变曲线。由图 10可以看到，未热处理的激光填丝焊接头抗拉强度为248 MPa, 延伸率6.7%。母材的抗拉强度为333 MPa, 延伸率17.8%。未热处理的激光填丝焊接头抗拉强度及延伸率都远低于母材。与之相比，经焊后热处理后，接头的抗拉强度及延伸率均得到提高：抗拉强度提高到340 MPa, 延伸率提高到11.6%。经焊后热处理焊接接头的抗拉强度略高于母材，延伸率达到母材的65.2%。
图 Figure10(Fig.Figure10)
图 10 焊后热处理试样拉伸曲线Fig.10 Tensile property curves of specimen after post-weld heat treatment图 11为拉伸后的断口形貌图，可以发现：未热处理的激光填丝焊接头断口中韧窝形态平整；而经焊后热处理的焊接接头拉伸断口韧窝相对较深，韧窝中存在强化相及杂质相分布。可见，焊接接头经过热处理，能够促进细小强化相析出及杂质相长大，两者共同作用对焊接接头的力学性能产生影响。
图 Figure11(Fig.Figure11)
图 11 拉伸断口组织形貌Fig.11 Micrographs of tensile fracture: (a) welding joint without heat treatment (low magnification); (b) welding joint without heat treatment (high magnification); (c) welding joint after heat treatment (low magnification); (d) welding joint after heat treatment (high magnification); (e) base material (low magnification); (f) base material (high magnification)与此相比较，如图 11(e)及(f), 在母材断口中为狭长韧窝，且大小均匀，轧制痕迹明显，并且在韧窝内存在第二相粒子的分布。
3 结论1) 本文采用ER5356焊丝进行6005A铝合金激光填丝焊，并对获得的焊接接头进行了固溶/时效热处理。研究发现，未经热处理的激光焊缝中不存在Mg2Si(β)强化相，仅检测到α-Al固溶体。经过焊后热处理，焊接接头中有β"相、β′相和Q′相析出，同时AlFeSiCrMn杂质相增多。
2) 与激光填丝焊焊接接头相比，经固溶/时效焊后热处理后的焊接接头各区域显微硬度显著增加。基于焊接接头硬度比较，确定550 ℃固溶1.5 h/175 ℃时效8 h为优化的焊后热处理规范。
3) 拉伸性能实验表明，经焊后热处理，焊接接头的拉伸强度增加至340 MPa, 高于母材的拉伸强度；热处理后接头延伸率为11.6%, 达到母材延伸率的65.2%。热处理后接头断口韧窝中有弥散分布的析出强化相。可见，焊后热处理有效提升了焊接接头的拉伸性能。
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