Effect of process parameters on the strength of resistance spot welds in 6082-T6 aluminium alloy

In this study the microstructural and mechanical behaviour of resistance spot welds (RSW) done on aluminium alloy 6082-T6 sheets, welded at different welding parameters, is examined. Microstructural examinations and hardness evaluations were carried out in order to determine the influence of welding parameters on the quality of the welds. The welded joints were subjected to static tensile-shear tests in order to determine their strength and failure mode. The increase in weld current and duration increased the nugget size and the weld strength. Beyond a critical nugget diameter the failure mode changed from interfacial to pullout. Taking into consideration the sheet thickness and the mechanical properties of the weld, a simple model is proposed to predict the critical nugget diameter required to produce pull-out failure mode in undermatched welds in heat-treatable aluminium alloys.     

SUS304不锈钢板点焊接头超声成像及力学性能EI北大核心CSCD

利用超声波水浸聚焦入射法,对1mm厚的SUS304奥氏体不锈钢板点焊接头进行超声C扫描成像检测,研究不同焊接工艺参数下接头的C扫描图像特征,检测分析点焊的熔核直径,并对点焊接头进行拉伸-剪切实验。结果表明：超声波水浸聚焦C扫描成像法能够有效检测点焊熔核直径,为4．76～5．25mm,比金相实测值大2．6％～5．3％;随着焊接电流的增加（4-8kA）,接头的失效载荷均值从7116．8N增加到9707．1N,能量吸收均值从66．3J增加到196J,同时反映在C扫描图像上的熔核直径也从4．76mm增加到5．11mm;当焊接电流增加至9kA时,接头的失效载荷均值下降至6799．5N,能量吸收均值下降至41．3J,此时在C扫描图像上反映出飞溅、焊穿等典型的焊接缺陷。     

Conventional and in situ tensile test of friction stir welded steel – Optimization of processing parameters

In the present investigation, steel plates were joined at different tool traversing speed by friction stir welding keeping other parameters same. Microstructural characterization was carried out with optical and scanning electron microscopes. At weld nugget pearlite and bainite were present within ferrite matrix. Thermo‐mechanically and heat affected zones microstructure consisted of pearlite and ferrite. Second phase area fraction and matrix grain size at different regions were varied depending on welding parameters. Weld nugget exhibited substantial improvement in microhardness with respect to base metal. In this respect heat affected zone revealed minimum microhardness and was below base metal value. Tensile tests were carried out on standard and miniature specimens in scanning electron microscope. Highest joint efficiency to the tune of ～82 % and ～120 % of that of base metal obtained for standard and miniature specimens, respectively machined from weld fabricated at lowest welding speed. With increment in welding speed assembly strength was reduced for both types of specimens. Standard specimens failed from heat affected zone and miniature specimens failed through centre of weld nugget. Apart from matrix grain size and second phase area fraction, precipitation of microalloyed carbide / carbonitride was responsible for altering the joint strength.     

Mechanical performance of three thickness resistance spot welded low carbon steel

Abstract

Resistance spot welding is the dominant process for joining sheet metals in automotive industry. Despite the application of three thickness resistance spot welds in this industry, present guidelines and recommendations are limited to two thickness spot welds. Study towards better understanding of weld nugget growth and mechanical properties is the first step to understanding the welding behaviour and developing proper guidelines for the three thickness resistance spot welding. In this paper, weld nugget growth, mechanical performance and failure behaviour of three thickness low carbon steel resistance spot welds are investigated. Macrostrcutural and microstructural investigations, microhardness tests and quasi-static tensile–shear tests were conducted. Mechanical performance of the joint was described in terms of peak load, energy absorption and failure mode. In order to understand the failure mechanism, micrographs of the cross-sections of the spot welded joints during and after tensile–shear are examined by optical microscopy. Unlike two thickness resistance spot welded joint, weld nugget was formed in the geometrical centre of the joint (i.e. centre of the middle sheet). Weld nugget size along sheet/sheet interface was greater than that of along geometrical centre of the joint. Increasing welding time leads to increases in peak load and energy absorption of the joint and transition of interfacial failure mode to pullout failure mode, primarily due to the enlargement of weld nugget size along sheet/sheet interface.     

Resistance spot welding joints of AISI 316L austenitic stainless steel sheets: Phase transformations,mechanical properties and microstructure characterizations

In this paper, we aim to optimize welding parameters namely welding current and time in resistance spot welding (RSW) of the austenitic stainless steel sheets grade AISI 316L. Afterward, effect of optimum welding parameters on the resistance spot welding properties and microstructure of AISI 316L austenitic stainless steel sheets has been investigated. Effect of welding current at constant welding time was considered on the weld properties such as weld nugget size, tensile–shear load bearing capacity of welded materials, failure modes, failure energy, ductility, and microstructure of weld nuggets as well. Phase transformations that took place during weld thermal cycle were analyzed in more details including metallographic studies of welding of the austenitic stainless steels. Metallographic images, mechanical properties, electron microscopy photographs and micro-hardness measurements showed that the region between interfacial to pullout mode transition and expulsion limit is defined as the optimum welding condition. Backscattered electron scanning microscopic images (BE-SEM) showed various types of delta ferrite in weld nuggets. Three delta ferrite morphologies consist of skeletal, acicular and lathy delta ferrite morphologies formed in resistance spot welded regions as a result of non-equilibrium phases which can be attributed to the fast cooling rate in RSW process and consequently, prediction and explanation of the obtained morphologies based on Schaeffler, WRC-1992 and Pseudo-binary phase diagrams would be a difficult task.     

Effects of welding parameters on the characteristics of magnesium alloy joint welded by resistance spot welding with cover plates

Magnesium alloy AZ31B sheets were welded using the technique of resistance spot welding with cover plates. The effects of welding parameters on the characteristics of the joint were investigated. The joint with larger nugget and higher tensile shear load was obtained under relatively low welding current condition. Enhancing electrode force and extending down-sloping time are effective for inhibiting pores formation and increasing the tensile shear strength of the joint under corresponding welding conditions. The results reveal that the technique is feasible to weld magnesium alloy.     

The effects of the welding current on heat input,nugget geometry,and the mechanical and fractural properties of resistance spot welding on Mg/Al dissimilar materials

Investigating the joining capability of magnesium AZ31 alloy sheets and aluminium 1350 alloy sheets with the application of resistance spot welding was the objective of this study. The weld current values used in the welding process of Al–Mg sheets were 22, 23, 25, 27, 29, 31, and 33 kA. The studies examined the nugget geometries of joined specimens, recorded the scanning electron microscopy (SEM) images of the welded zone and the fracture surface, and recorded the energy-dispersive spectroscopy (EDS, semi-quantitative) analyses. The results of the experiment confirmed that nugget geometry was different for the Al and Mg sides. Tensile shear tests carried out on the welded joints determined their strength and failure mode. The increase in the weld current and duration resulted in an increase in the nugget size and the weld strength. According to observations, the tensile load bearing capacity (TLBC) increased up to 29 kA of the weld current value. It was also found that tearing during fracture occurred in two different ways.     

DP590双相钢点焊接头的正交试验及超声检测分析

对DP590双相钢点焊接头进行正交试验,研究不同工艺因素对点焊接头失效载荷和焊核直径的影响,确定最优点焊工艺参数,并探讨点焊接头压痕深度的超声测量方法.采用超声波水浸聚焦入射法对1.5 mm厚的DP590双相钢点焊接头进行超声C扫描,获得接头焊核直径,利用超声A扫信号,计算点焊接头压痕深度,并与实际测量结果对比.研究表明:焊接参数对DP590点焊接头的失效载荷与焊核直径的显著性影响一致,从大到小依次为焊接电流、焊接时间、电极压力;DP590点焊接头最优的焊接工艺参数为:焊接时间70 ms,焊接电流15.0 k A,电极压力6.5 k N,在此参数下接头的抗拉强度为9 521.4 N;超声A扫信号计算得到的点焊接头表面压痕率与实际压痕率的误差在2.5%~9.7%,超声计算所得压痕深度与实际测量压痕率较为接近.     

储能缝焊工艺对304不锈钢接头性能的影响

为研究电容储能缝焊工艺对304不锈钢接头性能的影响规律,对0.5 mm厚304不锈钢板进行了缝焊工艺实验,通过接头拉剪力检测和金相显微组织观察,对比了不同焊接速度、充电电容和放电频率下的缝焊接头组织特点,并分析了各工艺参数对接头拉剪力、熔核宽度、焊缝重叠量和焊透率的影响.结果表明:储能焊焊缝中心晶粒细小,熔合区为柱状晶,重叠部位晶粒粗大,接头组织呈现不均匀性,随着充电电容的增大晶粒变得更细密,组织不均匀程度显著降低,焊接速度和放电频率增大导致晶粒组织粗化并出现缩孔缺陷,提高电极压力可克服缩孔并使组织趋向均匀;充电电容对接头拉剪力的影响较小,焊接速度、充电电压、放电频率和电极压力调到一个合适值后,继续增大参数值对接头拉剪力影响很小;焊接速度的增大引起焊缝熔核宽度和重叠量急剧下降,充电电压增大引起焊缝焊透率下降过多,导致飞溅、过烧、毛刺等焊接缺陷的产生.因此,304不锈钢储能缝焊应采用低的焊接速度、较小的充电电压和较高的电极压力。     

Nucleus geometry and mechanical properties of resistance spot welded coated–uncoated DP automotive steels

In this study, mechanical properties of resistance spot welding of DP450 and DP600, galvanized and ungalvanized automotive sheets have been investigated. The specimens have been joined by resistance spot welding at different weld currents and times. Welded specimens have been examined for their mechanical, macrostructure and microstructure properties. Depending on the weld current and time, effects of zinc coating on tensile properties, microhardness values as well as microstructure nugget geometry and nucleus size ratio have been investigated. X-ray diffraction analysis has been used to investigate the phase that formed at the joint interface. Result of the experiment show that nugget diameter, indentation depth and tensile load-bearing capacity are affected by weld parameters. Coating prevents full joining at low parameters. Microhardness increased in heat-affected zone and weld metal.     

三层板电阻点焊接头界面力学性能

目的为掌握汽车侧撞区域三层板电阻点焊接头不同界面的承载能力,研究三层板接头力学性能。方法以B1500HS-1.4 mm/B1500HS-1.6 mm/DC06-0.8 mm三层板电阻点焊接头为研究对象,通过剪切拉伸试验结果,对比分析不同界面的力学性能,并对焊点熔核区显微组织、界面熔核尺寸、显微硬度以及失效模式进行研究与分析。结果在三层焊中,当上下两侧板材强度相差很大时,不同界面的三层板点焊接头具有不同的峰值载荷和断裂能量,强强界面的剪切承载能力是强弱界面的6倍;熔核区不同板材处的马氏体含量以及界面熔核尺寸均影响点焊接头的力学性能;热成形钢一侧影响区因原始全马氏体组织出现了软化;拉剪试验条件下,B1500HS-1.4 mm/B1500HS-1.6 mm界面点焊接头失效模式为纽扣失效,B1500HS-1.6mm/DC06-0.8 mm界面点焊接头失效模式为先纽扣失效,后母材撕裂。结论在汽车耐撞设计中应通过承载分配,将碰撞结构力传导至强强界面,并通过隔离设计尽量避免强弱界面受到结构力影响,以提高碰撞性能。     

Characterization of magnesium spot welds under tensile and cyclic loadings

Resistance spot welds of a magnesium alloy were characterized in terms of microstructure, hardness and monotonic and cyclic properties. Microstructural features in base metal and different zones in the weld region were discussed and the mechanical behavior of spot welds in tensile–shear configuration was studied. Effects of welding parameters were investigated on the micro- and macro-scale characteristics of magnesium spot welds. To this end, five sets of spot weld specimens were prepared, utilizing different welding parameters. The effect of cyclic loading was studied on microstructure and hardness of the base metal and the weld region, and it was shown that microstructural features do not change remarkably under cyclic loading. Fatigue crack initiation and propagation behavior was discussed for different specimen sets under both low and high cyclic loads. Fatigue cracks under high cyclic loading initiated close to the nugget edge, and decreasing the cyclic load nucleated the cracks farther from the nugget.     

Factors affecting mechanical properties of resistance spot welds

Abstract

The present paper addresses the factors governing the mechanical performance of low carbon resistance spot welds. Correlations among the process parameters (welding current, welding time, electrode force and holding time), physical spot weld attributes and mechanical performance are analysed. Peak load and energy absorption of spot welds during the tensile shear test are used to describe spot welds performance. It is shown that weld nugget size, electrode indentation, failure mode and strength/ductility of the failure location are the main factors affecting peak load and energy absorption of spot welds.     

Influence of weld parameters on the mechanical properties of spot-welded Fe-Mn-Al-Cr alloy

The static weld strength, hardness and microstructure evolution of a Fe-Mn-Al-Cr alloy during spot welding were investigated. A nugget can be formed for weld times as low as 5 cycles at 60 Hz (83 ms). The nugget growth rate is different between the front and the rear of the acceptable weld region. In the acceptable weld region, the tensile-shear strength ranges from 3038 to 3626 N, and the cross-tension strength varies from 2356 to 3136 N. The static weld strength strongly depends on the nugget size, and the dependence of the static weld strength on the electrode force is affected by the weld time and weld current. Evolution of spot-welded nuggets indicates that the hardness in the nuggets is, on average, about 100 H _V higher than that in the base unwelded metal, which is attributed to a cooling effect after welding.     

Ultrasonic spot welding of Al/Mg/Al tri-layered clad sheets

Solid-state ultrasonic spot welding (USW) was used to join Al/Mg/Al tri-layered clad sheets, aiming at exploring weldability and identifying failure mode in relation to the welding energy. It was observed that the application of a low welding energy of 100 J was able to achieve the optimal welding condition during USW at a very short welding time of 0.1 s for the tri-layered clad sheets. The optimal lap shear failure load obtained was equivalent to that of the as-received Al/Mg/Al tri-layered clad sheets. With increasing welding energy, the lap shear failure load initially increased and then decreased after reaching a maximum value. At a welding energy of 25 J, failure occurred in the mode of interfacial failure along the center Al/Al weld interface due to insufficient bonding. At a welding energy of 50 J, 75 J and 100 J, failure was also characterized by the interfacial failure mode, but it occurred along the Al/Mg clad interface rather than the center Al/Al weld interface, suggesting stronger bonding of the Al/Al weld interface than that of the Al/Mg clad interface. The overall weld strength of the Al/Mg/Al tri-layered clad sheets was thus governed by the Al/Mg clad interface strength. At a welding energy of 125 J and 150 J, thinning of weld nugget and extensive deformation at the edge of welding tip caused failure at the edge of nugget region, leading to a lower lap shear failure load.     

Failure analysis of 316L austenitic stainless steel bellows used under dynamic sodium in a creep testing chamber

Failure analysis has been carried out on 316L austenitic stainless steel seamless bellows served as mechanical and environmental isolator in a creep chamber for carrying out creep test under dynamic sodium. A set of 4 seamless bellows welded with a supporting ring by TIG welding process has been used. Visual examination and liquid penetration test revealed that the failure reveal as holes occurring at the bellow convolution which was welded with the supporting ring. Severe loss of material at the failed region due to reaction of leakage liquid sodium with residual oxygen and moisture in argon cover gas was observed. Further, deposition of chromium- and iron-rich oxides was observed in and around the failure location. Microstructure studies revealed the presence of interdendritic porosity in the weld fusion zone and evidences of sensitized grain boundary with extensive precipitation of chromium-rich carbides in the coarse heat affected zone in the bellow. The leakage of sodium through the interdendritic pores and micro-cracks might have facilitated the reaction of sodium with bellows. Improper method for welding of the thin-walled bellow convolution with a supporting ring is considered as the root cause of the failure. Welding technique and method facilitating the formation of equi-axed microstructure with least formation of dendritic structure in the fusion zone and the use of proper cooling arrangement during welding to avoid sensitization have been recommended to avoid the bellow failure during service.     

Failure Analysis of HAZ Cracking in Low C–CrMoV Steel Weldment

This case study describes the failure analysis of steel nozzle in which cracking was observed after a circumferential welding process. The nozzle assembly was made from low C–CrMoV alloy steel that was subsequently single pass butt welded using gas tungsten arc welding. No cracks were found in visual inspection of the welds; however, X-ray radiography showed small discontinuous cracks on the surface in the area adjacent to weld bead, i.e. heat affected zone. The welding of nozzle parts made of same material was a routine process and this type of cracking did not occur in the past. Therefore, it became essential to determine the root cause of the failure. A detailed investigation including visual examination, non-destructive testing, optical microscopy, microhardness measurements and residual stress measurements were carried out to find out the primary cause of failure and to identify actions required to avoid its reoccurrence in future. Results of the investigation revealed that the principal cause of failure was the presence of coarse untempered martensite in the heat affected zone due to localized heating. The localized heating was caused by high welding heat input or low welding speed and resulted in the high transformation stresses. These transformation stresses combined with the thermal stresses and the constraint conditions to cause intergranular brittle fracture.     

7075铝合金高速搅拌摩擦焊材料流动行为及性能研究

目的 针对7075–O铝合金高焊速、高转速搅拌摩擦焊接缺陷多、质量差等问题,研究焊接接头材料流动对焊缝性能的影响。方法 选用焊接速度1 000 mm/min,搅拌转速分别为1 000、1 200、1 600、1 700 r/min的条件对7075–O铝合金板进行搅拌摩擦焊接,分析不同焊接工艺参数下焊接接头的显微组织及力学性能。同时,利用Fluent软件模拟7075–O铝合金搅拌摩擦焊接过程中的材料流动场分布,分析焊接材料流动与缺陷形成的关系。结果 利用7075–O铝合金三维流动模型,预测出高焊速条件下焊缝前进侧形成一个低压区,孔洞等缺陷易出现在此区域,数值模拟预测与试验结果吻合。在高焊接速度1 000 mm/min、焊接转速1 200 r/min时,焊缝表面光滑平整,焊核区域的硬度分布更加均匀。结论 随着搅拌转速从1 000 r/min增大到1 700 r/min,热输入量逐渐增大,孔洞缺陷由隧道型孔洞转变为不连续的小孔。同时,随着搅拌转速的增大,焊缝高硬度区域的宽度先增大而后降低。当搅拌转速为1 200 r/min时得到了优质的焊接接头,焊缝焊核区硬度分布均匀,硬度值最高为176HV。     

Exploring material flow in friction stir welding: Tool eccentricity and formation of banded structures

Surface striations with spacing equal to feed rate per rotation and banded structures in the weld nugget are some of the striking features of friction stir welding. However, their formation is still subject to some debate. This study contributes to comprehend their formation by evaluating the possible role played by the eccentricity of the tool during the welding of an aluminium alloy and using a plasticine as its analogue. The eccentric movement is visualized to generate both surface and bulk striations in plasticine. By voluntarily using non optimized welding conditions on aluminium, the material flow has been deduced and confronted with direct visual observations through high speed camera on plasticine. In the non closed section of the weld, two lobes each with thickness equal to feed rate per rotation were observed. First lobe corresponds to flow induced by the pin and tests on plasticine showed constant volume displacement per rotation for a given tool eccentricity. The second lobe is generated by material flow from under the shoulder back to the rear of the pin. The assembling or not of these two lobs behind the pin can explain some of the characteristic patterns observed in the weld nugget such as onion rings, oxide dispersions and cavities.     

Friction Stir Weldabilities of AA1050-H24 and AA6061-T6 Aluminum Alloys

The friction stir weldabilities of the strain-hardened AA1050-H24 and precipitate-hardened AA6061-T6 aluminum alloys were examined to reveal the effects of material properties on the friction stir welding behavior. The experimental results are obtlained. (1) For AA1050-H24, the weld can possess smoother surface ripples; there is no elliptical weld nugget in the weld; there is no discernible interface between the stir zone and the thermomechanically affected zone; and the internal defect of the weld looks like a long crack and is located in the lower part of the weld. (2) For AA6061-T6, the weld usually possesses slightly rougher surface ripples; an elliptical weld nugget clearly exists in the weld; there are discernible interfaces among the weld nugget, thermomechanically affected zone and heat affected zone; and the internal defect of the weld is similar to that of the AA1050-H24 weld. (3) The effective range of welding parameters for AA1050-H24 is narrow, while the one for AA6061-T6 is very wide. (4) T