Joint performance in laser welding Al alloy with filler wire

CO2 laser welding aluminum alloy with filler wire was studied. The results indicate that the problems in CO2 laser welding of Al alloy, such as bad appearance of weld, easily excessive penetration and low strength, can be improved effectively by using laser welding with filler wire, and the maximum tensile strength of weld can reach 94% for the base metal. It also can be found that, the linear energy have great influence on the microstructure and mechanical properties of the joint. As the heat input increases, the cellular fir-tree crystals in the weld zone become sparse and the form of tensile fracture transforms from gliding fracture to brittle fracture.

Microstructure and Mechanical Property of Al-Cu-Li Alloy Joint by Laser Welding with Filler Wire

The Al-Cu-Li alloy is welded by using laser beam welding,and the welding wire ER4043 is used as filler metal. The microstructure and mechanical property of welded joints are systematically investigated. Microstructure analyses show that the fusion zone is mainly composed of α-Al matrix phase and some strengthening phases including T,δ’,θ’,β’ and T1,etc. During welding,the weld formation and joint quality are obviously improved by the addition of Al-Si filler wire. The measurements of mechanical property indicate that,compared with that of the base metal(BM), the microhardness in the weld zone is decreased to a certain extent. Under the appropriate welding parameters,the tensile strength of welded joint reaches 369.4 MPa,which is 67.8% of that of the BM. There are many dimples on the joint fracture surface,and it mainly presents the fracture characteristic of dimple aggregation.

Effect of filler wire on the joint properties of AZ31 magnesium alloys using CO_2 laser welding

Laser welding with filler wire of AZ31 magnesium alloys is investigated using a CO2 laser experimental system. The effect of three different filler wires on the joint properties is researched. The results show that the weld appearance can be effectively improved when using laser welding with filler wire. The microhardness and tensile strength of joints are almost the same us those of the base metal when ER AZ31 or ER AZ61 wire is adopted. However, when the filler wire of ER 5356 aluminum alloy is used, the mechanical properties of flints become worse. For ER AZ31 and ER AZ61 filler wires, the microstructure of weld zone slws small dendrite grains. In comparison, for ER 5356 filler wire, the weld shows a structure of snowy dendrites and many intermetallic compounds and eutectic phases distribute in the dendrites. These intermetallic constituents with low melting point increase the tendency of hot crack and result in fiagile joint properties. Therefore, ER AZ31 and ER AZ61 wire are more suitable filler material than ER 5356 for CO2 laser welding of AZ31 magnesium alloys.

Prediction of wire transfer behaviors in laser hot wire welding

With preheating wire by resistance heat, laser hot wire welding improves process stability and wire deposition efficiency, which gives broad potential applications in sugracing and narrow gap welding. It is a critical issue to control the temperature of preheated wire in this process. The temperature which is so high that the wire fuses outside molten pool or so low that the wire cannot melt timely in the molten pool, results in poor wire transfer stability and bad weld formation. This paper is purposed to calculate the wire temperature for the prediction of wire transfer behavior under various welding parameters. A heat conduction model is set up. Heat sources of the wire include resistance heat and reflected laser, and the heat source of molten pool is laser. The calculated temperature of wire part outside the molten pool is verified by infrared ratio temperature measurement. The calculated temperature of wire part in the molten pool is verified by measurement of the molten pool size. Analyzing the wire temperature and welding process observed by the high speed video imaging, the temperature criteria of wire transfer behaviors are obtained. Thus, numerical simulation of the wire temperature can be used to predict wire transfer behaviors in laser hot wire welding.

Characteristics of Joint Welded by Laser Welding of Aluminium-Lithium Alloy with Filler Wire

The characteristics of weld shape,microstructure,mechanical properties and defects of 5A90 Al-Li alloy joint by laser welding (LBW) and laser welding with filler wire (LWFW) were studied and analyzed.The results indicated that the microstructure of joint by LWFW was fine-grained layer and the equiaxed grain in most of seams,which were similar to the joint by LBW.Compared with the joint by LBW,the microstructure of joint by LWFW tended to fine,and the range of the columnar crystals zone was prone to decrease.The Microhardness of the joint by LWFW (92.57HV0.2) was lower than that by LBW (95.65HV0.2),but the uniformity was better.The ultimate tensile strength of the joint by LWFW was lower than that by LBW slightly,which reached to 73.03% and 79.22% of the base metal respectively.However,the elongation of the LWFW joint was higher than that of the LBW joint significantly,which reached to 38.65% and 20.38% of the base metal respectively.The microstructure and mechanical properties of 5A90 Al-Li alloy by LWFW were better than that by LBW.The defects of joint were mainly forming defects which were caused by improper parameters and porosity inside the joint,which was caused by uncleaned surface and incomplete penetration.

Mg-Al-Zn合金激光填丝焊接接头的显微组织与力学性能

采用激光填丝焊方法对4 mm厚的Mg-Al-Zn系镁合金进行焊接,采用金相显微镜、扫描电镜、透射电镜和X射线衍射仪对接头的微观组织进行分析,并对接头的拉伸性能和显微硬度进行测试。结果表明,接头焊缝区主要由α-Mg基体相和β-Mg17Al_(12)强化相组成。与母材区相比,接头热影响区的硬度有所降低,与该区域的晶粒粗化有关。在激光功率3.0 kW,焊接速度1.5 m/min,送丝速度2.1 m/min的工艺条件下获得的接头,焊缝成形良好,其抗拉强度为315 MPa,与母材的抗拉强度接近。接头拉伸断口上分布着一定数量的韧窝和河流花样,总体呈韧-脆混合型断裂特征。

Dendritic Boundary Corrosion of AA2198 Weld Using Fiber Laser Welding with Al–Cu Filler Wire

The microstructures and corrosion behaviors of AA2198-T851 alloy and weld were analyzed under corrosive conditions. Weld was formed using an innovative fiber laser welding process with AA2319 Al-Cu filler wire. The metallurgic morphology and distribution of the chemical compositions were determined using imaging techniques such as optical micrograph, scanning electron micrograph, high-resolution transmission electron microscopy, energy-dispersive X-ray spectrometry and X-ray diffraction. Corrosion was evaluated using an immersion test and electrochemical impedance spectroscopy in 3.5% NaC1 solution at room temperature. Results indicate that the parent alloy suffered from pitting corrosion during the initial 4-h immersion which was caused by the inhomogeneous distribution of its chemical compo- nents and the different intermetallics formed during the rolling process. The weld experienced dendritic boundary corrosion under the same conditions due to the addition of the Al-Cu filler and rapid solidification during laser welding, which led to the precipitates Cu enrichment along the grain boundary. When a welding joint was immersed in the solution for 5 days, a big crack was observed across the center of the weld. In comparison, there was good corrosion resistance in the heat- affected zone with a compact protective film.

磁场辅助窄间隙激光填丝焊焊接工艺研究

采用磁场辅助窄间隙激光填丝焊工艺对25 mm厚S32101双相不锈钢板进行多层焊接,并对其焊接性能进行了研究。观察对比了有无磁场辅助窄间隙激光填丝焊的焊缝成形,并重点分析了磁场辅助焊接接头的力学性能、金相组织。结果表明:有无磁场辅助得到的焊缝表面均平滑均匀,基本无飞溅。无磁场辅助的焊缝出现气孔及未熔合缺陷,施加磁场后焊缝无此缺陷。磁场辅助焊接的拉伸试样均断裂于母材位置,焊接接头的抗拉强度高于母材。各焊层焊缝的平均硬度高于母材。焊缝组织为奥氏体和铁素体,组织细密均匀,两相比例均匀稳定,约为1:1。

薄镀层热成形钢激光填丝焊的焊缝特征及性能

为降低镀覆在钢板表面的铝硅镀层对激光接头的不利影响,采用薄镀层热成形钢材料配合激光填丝焊技术,获得了焊缝内铝质量分数小于1%的激光填丝焊接头。对该接头进行了宏观及微观组织分析,发现热成形后焊接接头组织被全马氏体组织取代,避免了软化现象。力学性能分析表明,热成形前后试样的抗拉强度从约570 MPa提高到约1 500 MPa,接头的薄弱环节位于母材,高速拉伸对接头的抗拉强度没有不良影响,而断裂伸长率受影响较大。

钛合金激光填药芯焊丝接头组织性能

通过激光填丝焊接方法并采用自主开发设计的钛合金药芯焊丝,进行TC4钛合金板的焊接,对获得的焊接接头进行850℃保温2 h后随炉冷却退火工艺处理,并与焊态焊接接头的组织性能进行比对分析,结果表明,热处理态焊接接头焊缝中由α_(p)相、α_(s)相集束及点状分布的残留β相构成,没有发现焊态焊缝中的α’马氏体组织;热处理态焊接接头强度降低但断后伸长率和常温冲击韧性增加;热处理态焊接接头拉伸断口由大量撕裂唇包围,韧窝深且均匀,呈微孔聚合韧性断裂.通过XRD测试发现焊态焊缝中主要由α’马氏体组成,还有少量极弱的多角度α相衍射峰,而热处理态焊缝中α相衍射峰中心角度位置与焊态焊缝中α’马氏体一致,另外还发现了较为明显且尖锐的β相(110)衍射峰.

Al-Si镀层热成形钢热填丝激光焊接接头的性能研究

利用热填丝激光焊接技术实现Al-Si镀层热成形钢的焊接,在模具内热成形、淬火,对焊接接头的显微组织、Al元素分布和力学性能进行了研究。结果表明,基材的显微组织为马氏体组织,而熔核区的显微组织为马氏体、铁素体和贝氏体的混合组织;熔入到焊缝中的铝元素分布均匀,无局部聚集,平均含量约为0.87%;熔核区、基材的硬度分别为475、501 HV;焊接接头和两侧基材的强度基本相同,但断后伸长率存在一定差异,主要是由于焊缝和基材二者在拉伸过程中变形的不均匀所致。

镀锌钢板激光填丝焊接工艺与接头力学性能研究

车身用镀锌钢板的厚度较薄,采用其他方法焊接制造容易产生较大变形,开发厚度较薄的镀锌钢板激光填丝焊接工艺具有重要工程实践意义。针对车身用0.7 mm厚异种镀锌钢板,开展激光填丝焊接工艺试验,系统研究关键工艺参数(激光功率、焊接速度、离焦量和送丝速度)对焊缝表面和横截面的影响规律,分析焊接接头的微观组织特征和力学性能。结果表明,激光功率、焊接速度、离焦量和送丝速度有较好匹配时,可以获得焊接飞溅少、表面光滑的焊缝;焊接接头拉伸试样在强度较弱的母材发生断裂。

热轧态HiB钢冷轧穿带激光填丝焊接试验研究

针对热轧态HiB钢冷轧穿带激光焊缝杯突检测不合格的问题,采用高功率光纤激光器开展了两种填充材料50C-6和307Si在不同填充速度下的焊接试验。结果表明:当激光焊接速度为3m/min时,填丝50C-6的速度≥1.5m/min时焊缝杯突合格;填丝307Si的速度为1.5 m/min时焊缝杯突合格,为4m/min时焊缝杯突不合格,对导致焊缝杯突不合格的原因进行了探讨。

Al-Si涂层22MnB5钢激光拼焊焊缝性能研究

利用激光填丝焊技术对Al-Si涂层22MnB5热成型钢进行拼焊,并对焊缝性能进行研究。采用金相显微镜观察焊缝微观形貌,结果表明,焊缝未出现裂纹、气孔等焊接缺陷,组织为马氏体;通过杯突试验对焊缝进行检测,发现开裂方向均与焊缝方向垂直;通过拉伸试验发现断裂位置均在母材区域;通过维氏硬度计检测发现母材及焊缝硬度差异在±50 HV以内。上述试验结果表明,该焊接工艺获得的焊缝性能满足汽车行业的要求。

5A06铝合金激光填丝焊工艺研究

针对1.2mm厚5A06铝合金薄板YAG激光焊接工艺范围窄和对间隙要求严格等问题,较系统地研究了该铝合金激光填丝焊接工艺。试验中采用ER5356焊丝作为填充金属,对光丝间距、送丝速度、激光功率和焊接速度等影响焊缝成形的各种焊接工艺参数进行了优化分析。研究结果表明:优化工艺参数可以显著改善焊缝成形;与激光焊相比,激光填丝焊接工艺范围明显扩大;激光填丝焊的最大容许间隙裕度可以提高至0.6～0.9mm。表明了YAG激光填丝焊工艺是实现5A06铝合金薄板焊接的有效方法。

焊接参数对铝合金激光填丝焊缝成形的影响

采用ER5356焊丝对1.2mm厚5A06铝合金和3mm厚5A90铝锂合金进行激光填丝焊接实验,探讨了焊接参数包括光丝间距、送丝速率、激光功率和焊接速率等对焊缝成形的影响。结果表明:光丝间距必须控制在一定范围内才能获得成形较好的焊缝,且其优化范围受焊接速率的影响显著;母材板厚较小有利于激光填丝焊优化送丝速率的提高及其范围的扩大;焊接速率对焊缝成形的影响较大,随着焊接速率的增加,激光功率应随之增加与其匹配;激光填丝焊时在保证熔透性且较好成形的基础上,应尽量采用较小的焊接热输入。

采用填充焊丝激光焊接工艺的研究

分析了采用填充焊丝激光焊接的加工原理、工艺特点和技术关键。工艺研究表明，采用填充焊丝激光焊接可以大为改善焊缝的冶金性能，提高焊缝质量，降低激光焊接工艺对工件坡口加工精度的要求，并可以实现大厚度板的窄间隙激光焊接。

激光-MIG复合焊接304不锈钢工艺研究

为了研究304不锈钢光纤激光-MIG(metal inert-gas welding)复合焊接性能,采用正离焦的方法进行了大量的焊接实验。分析了送丝速率、弧长、激光功率、光丝距离、焊接方向和不同对接接头等参量对焊接成形的影响。结果表明,在焊丝的干伸长度为15mm、光丝距离为2mm、采用前送丝时,通过适当调节送丝速率、弧长可以实现较好的焊接效果;小直径焊丝有利于形成较小熔宽和余高的焊缝,而通过加入引弧板可以解决初始位置焊缝成形较差的问题。因此,采用合适的激光-MIG复合焊接工艺可以实现304不锈钢较好的焊接效果。

铝合金激光焊新技术

介绍了铝合金激光焊接的四种新技术:激光-GMA复合焊、激光填丝焊、双光束激光焊接和激光辅助搅拌摩擦焊的原理及其工艺特点。在此基础上重点阐述了用这四种激光焊接方法焊接铝合金的研究进展。

钛合金激光填丝焊缝晶粒生长及相变原位观察

采用高温激光共聚焦显微镜原位观察方法,研究TC4钛合金激光填药芯焊丝焊缝区在模拟焊接热循环作用下冷却过程中组织形成特征及相变规律。结果表明:当焊缝区分别以0.5℃/s、5℃/s、20℃/s和80℃/s的冷却速率降温到889.5℃、864.2℃、835.5℃和818.9℃时,在相界位置开始出现新相的微观组织形貌;当焊缝区分别降温到725.7℃、749.3℃、769.4℃和789.2℃时,新相完成转变,即相变的温度区间随着冷却速率的增大而逐渐变窄。随着冷却速率的增加,新相的片层间距逐渐减小;随着冷却速率的增大,冷却到室温的试样硬度逐渐增大,由339 HV10增大到368 HV10;试样全部由密排六方(HCP)晶体结构组成,没有斜方晶格和体心立方的晶体结构产生。