Refill Friction Stir Spot Welding Al Alloy to Copper via Pure Metallurgical Joining Mechanism

Abstract

The current investigation of refill friction stir spot welding (refill FSSW) Al alloy to copper primarily involved plunging the tool into bottom copper sheet to achieve both metallurgical and mechanical interfacial bonding. Compared to conventional FSSW and pinless FSSW, weld strength can be significantly improved by using this method. Nevertheless, tool wear is a critical issue during refill FSSW. In this study, defect-free Al/copper dissimilar welds were successfully fabricated using refill FSSW by only plunging the tool into top Al alloy sheet. Overall, two types of continuous and ultra-thin intermetallic compounds (IMCs) layers were identified at the whole Al/copper interface. Also, strong evidence of melting and resolidification was observed in the localized region. The peak temperature obtained at the center of Al/copper interface was 591 °C, and the heating rate reached up to 916 °C/s during the sleeve penetration phase. A softened weld region was produced via refill FSSW process, the hardness profile exhibited a W-shaped appearance along middle thickness of top Al alloy. The weld lap shear load was insensitive to the welding condition, whose scatter was rather small. The fracture path exclusively propagated along the IMCs layer of Cu₉Al₄ under the external lap shear loadings, both CuAl₂ and Cu₉Al₄ were detected on the fractured surface on the copper side. This research indicated that acceptable weld strength can be achieved via pure metallurgical joining mechanism, which has significant potential for the industrial applications.

Introduction

In order to obtain technical and economic advantages, joining of dissimilar materials is gaining wide popularity in the industries [1,2,3,4]. For instance, Al and copper alloys are useful for electrical and thermal applications, since they have excellent electrical and thermal conductivities [5]. However, it is a critical issue to fusion join Al alloy to copper since they can produce thick and continuous intermetallic compounds (IMCs) [6, 7]. Mechanical joining approaches such as self-piercing riveting can result in poor work environment, low work efficiency and weight increment of structures [8]. It is inspiring that solid phase joining technique such as explosive welding [9], ultrasonic welding [10], friction welding [11], friction stir welding (FSW) [12,13,14,15,16], and conventional friction stir spot welding (FSSW) are feasible approaches to join dissimilar metals [17], since they could avoid solidification, liquation cracking and porosity which are common occurred during fusion welding.

Compared to conventional and pinless FSSW, mechanical performance of refill FSSWed joint can be dramatically improved by increasing the weld effective bonded volume and integrity [18]. As presented in Figure 1, a tool comprises a clamping ring, a sleeve and a pin is applied during refill FSSW, the weld is fabricated by plasticizing, and displacing the material in a process similar to back extrusion and forging, whose detailed joining processes were provided elsewhere [18,19,20,21]. Role of the stational clamping ring is to steadily hold the workpieces, prevent the coupons from separating, and avoid overflow the softened material from the stirring area [20]. The sleeve and pin can rotate in the same direction by using the same motor, and move up and down independently by using two actuators [19]. Refill FSSW provides a number of benefits compared to fusion welding and mechanical joining methods, since it can minimize IMCs layer thickness by suppressing the temperature rise, providing many virtues for joining lightweight materials and dissimilar combinations [22,23,24,25,26,27,28].

Figure 1

Refill FSSW process: (a) preheating before penetration, (b) sleeve penetration, (c) stirring after penetration, (d) sleeve retraction, and (e) flatten weld surface after retraction

Currently, joining Al alloys to copper by FSW and conventional FSSW has been extensively studied, in which the bonding mechanism includes both metallurgical bonding and mechanical interlocking by plunging the tool pin into the bottom hard copper materials [26, 29, 30]. Compared to that in FSW, tool wear could be much more excessive in FSSW, because severe tool wear primarily takes place during the plunging phase [17]. The three-components tool utilized in refill FSSW was always made of tool steel due to that the tool design was very complicated. Hence, it can be expected that the tool threads could be severely worn off, if it was plunged into the copper sheet material to obtain the mechanical interlocking joining mechanism by displacing the bottom copper material into to Al alloy [30,31,32]. Under the circumstances, IMCs layer formation is indispensable to achieve metallurgical bonding at the interface. Nevertheless, the weld strength will be seriously deteriorated once the IMCs layer exceeds a critical thickness. Previous literatures revealed that tool sleeve penetration depth is the decisive factor determines the interfacial reaction, IMCs layer growth and thus mechanical properties [24, 26, 27, 31]. Therefore, purpose of the present investigation is to clarify the function of tool sleeve penetration depth on interfacial reaction and mechanical performance of refill friction stir spot welded Al/copper welds, in terms of interfacial microstructure, hardness profile, weld lap shear load and failure mechanism based on the experimental examination.

Experimental Procedure

The as-received materials utilized in this investigation were 2.0 mm thick Al 6061-T4 and 0.5 mm thick commercial pure copper, respectively. Chemical component of Al 6061-T4 is 0.04‒0.35Cr, 0.15‒0.4Cu, 0.8‒1.2Mg, 0.4‒0.8Si, < 0.7Fe, < 0.15Ti, < 0.25Zn, Al bal. (wt-%). The welding operation was conducted using a Harms & Wende RPS100 refill friction stir spot welding machine provided by Coldwater Machine Company. The threaded tool was made of H13 tool steel, function of the threads machined on the sleeve surface was to enhance the material flow performance and facilitate chip removal. Geometries of the clamping ring, sleeve and pin were schematically shown Figure 2, whose diameters were 14.5, 9.0 and 6.4 mm, respectively [21].

Figure 2

Geometrical feature of (a) clamping ring, (b) sleeve and (c) pin

In order to minimize tool wear, Al 6061 sheet material was set as the top coupon (Figure 1), and the welds were manufactured in the center of the 25 mm × 25 mm overlapped area of two 25 mm × 100 mm overlapped coupons. Industrial alcohol was used to clean impurities on the coupon surfaces such as dirt and oil before welding operation. Then, the Al/copper dissimilar spot welds were manufactured using a rotational rate of 1800 r/min, a surface dwell time of 0.5 s (before plunging), a plunging time of 0.5 s, a dwell time of 3 s, a retreating time of 0.5 s and a surface dwell time of 0.5 s (after retreating). Role of surface dwell time before the plunging and after retreating was to preheat and platen the materials to be joined [21]. The above-mentioned welding variants remain constant, while the tool sleeve penetration depth varies from 1.2 mm to 1.8 mm. In order to prevent steel sleeve is plugged into bottom of the copper sheet material and thus damaging the thermocouple, one 0.1 mm deep groove and hole (0.1 mm diameter) were machined on the bottom copper sheet, and a 0.1 diameter K-type thermocouple was inserted into the Al/copper interface center to record the temperatures (see Figure 1e).

After joining process, the weld was cut along weld center using wire-electrode cutting, and then prepared using standard metallographic techniques such as grinding and polishing. Afterwards, weld microstructures were examined by using an OLYMPUS NTB 3558 optical microscope after the sample was chemically etched by Keller’s reagent for 15 s. The Al/copper weld interfacial microstructure and the fractured surfaces morphology were examined using a JEOL JSM-6460 scanning electron microscope. All of the chemical compositions measured by energy dispersive X-ray (EDX) spectroscopy were reported as wt%. The weld lap shear load was performed on a CHANGCHUN CSS-44100 electronic universal testing machine provided by China Machine Testing Equipment Co. LTD, using a constant cross head speed of 10 mm/min, which was reported as the average of three individual testing samples. The hardness measurement was conducted along mid-thickness of to Al alloy using a LECO AMH 43 hardness tester produced by Leco Corporation, with a load of 5 gf and a dwell time of 10 s. X-ray diffraction (XRD) was used to identify the IMCs phases at the fractured surfaces on the copper side.

Results and Discussion

Interfacial Bonding

Cross sectional view of the weld fabricated utilizing a sleeve penetration depth of 1.8 mm was selected to investigate the weld macrostructure and interfacial microstructure (see Figure 3), where the sleeve plunging and retreating path was labeled by blue dotted lines. The weld top surface was uniform to that of the Al alloy coupon, suggesting no softened material was squeezed out of the stirring area during the entire joining process. The Al/copper interface was rather flat, and no micro-level plastic deformation or hooking feature can be observed due to that the tool sleeve did not penetrate into the bottom copper sheet material. Also, macroscopic defects such as lack of or no mixing, incomplete refill or bonding ligament were not formed in the weld, since a relatively longer dwell time was applied after the plunging phase. It is worth noting that previous studies indicated that the top sheet material microstructure did not influence the weld performance, since the weld failure always propagated along the weld interface [24,25,26,27], and the refill FSSWed Al 6061 microstructures have been extensively investigated [33]. Thus, the present investigation primarily focused on the Al/copper interfacial microstructure.

Figure 3

Cross sectional view of the weld manufactured using a 1.8 mm penetration depth

With the purpose of clarifying the interfacial microstructure and material flow pattern at the Al/copper faying interface, enlarged views in the rectangles I-IV in Figure 3 were presented in Figures 4, 5, 6, respectively. As shown in Figures 4 and 5, intimate bonding was achieved, and no microdefects such as voids, poles or cracking can be observed at the entire Al/copper interface. As presented in Figure 4 and Table 1, two different types of continuous IMCs layers were produced at the weld center. The IMCs layer adjacent to top Al sheet material was approximately 1.5 μm thick, where the average chemical component was 56.5%Al and 43.5%Cu (locations 4, 5 and 6), which was consistent with that of CuAl₂. While the thickness of the IMCs layer attached to the bottom copper sheet was approximate 0.5 μm thick, where the average chemical component was 27.7%Al and 72.3%Cu (locations 2 and 3), consistent with that of Cu₉Al₄ according to Al-Cu phase diagram.

Figure 4

(a) SEM image of region I in Figure 3, and element maps for (b) Al and (c) Cu

Figure 5

(a) SEM image of region II in Figure 3, and element maps for (b) Al and (c) Cu

Figure 6

SEM image of regions (a) IV and (b) III in Figure 3

Table 1 EDX quantification results (wt%) indicated in Figure 4

As shown in Figure 5, the IMCs layer was slightly thicker at the weld edge (approximate 3.0 μm) compared to that in the weld center, where more frictional heat can be generated due to the higher linear velocity of the rotating sleeve. The IMCs layer adjacent to the top Al 6061 sheet material was approximately 2.7 μm thick, where the average chemical component was 43.8%Al and 56.2%Cu (see Table 2, locations 3, 4 and 5), consistent with that of CuAl₂. It is interesting to be noted that the IMCs layer adjacent to the bottom copper sheet was extremely thin (approximate 0.3 μm) where the heat can be readily dissipated to the surroundings, and the average chemical component was 19.8%Al and 80.2%Cu (see Table 2, locations 1 and 2) and consistent with that of Cu₉Al₄. As shown in Figures 4b, 4c and Figures 5b, 5c, interdiffusion can be clearly identified between the top IMC layers and Al alloy stir zone (SZ), since fine grain size produced by dynamic recrystallization is beneficial to the mutual diffusion. A maximum temperature of 591 °C (with a temperature rising rate of 916 °C/s during the plunging phase) was obtained at the weld center (see Figure 7), which readily explained the interfacial microstructure formation. Encouragingly, the IMCs thickness was much thinner than those formed in fusion welding, and thus beneficial to the weld strength.

Table 2 EDX quantification results (wt%) indicated in Figure 5

Figure 7

Thermal cycle measured at the weld interface center

As shown in Figure 6a, it is interesting to be noted that evidence of resolidification and relatively thick IMCs layer can be observed in the localized region at the Al/copper interface, which can be attributed to high temperature exposure and mutual diffusion promoted by the refill FSSW process [26]. Furthermore, through-interface material flow pattern can be clearly identified around the weld edge (see Figures 3 and 6b), a fraction of Cu content was displaced upwards into the top Al sheet (see Table 3). Such a material flow pattern has been reported during refill friction stir spot welded Mg/steel [31], Al/steel and Al/Mg dissimilar welds [25, 28]. This material flow pattern has been identified to be formed during the sleeve plunging phase and further propagated to the weld top surface during the sleeve retreating phase [28].

Table 3 EDX quantification results (wt%) indicated in Figure 6b

Mechanical Properties

Hardness

Hardness profile conducted along middle thickness of the top Al 6061 sheet of the weld fabricated under a 1.8 mm penetration depth was shown in Figure 8. It can be observed that a softened welded zone was produced by the combination of frictional heat and plastic deformation derived from refill FSSW process, which is consistent with the previous research [33]. Overall, the hardness profile presented a W-shaped appearance since Al 6061 was a precipitation-hardened alloy, whose hardness was primarily governed by the state and distribution of precipitates (Mg₂Si) and scarcely affected by grain size [21]. The minimum hardness was measured at the junction of thermo-mechanically affected zone (TMAZ) and heat affected zone (HAZ), where the material experienced the highest temperatures besides SZ, resulting in coarsening or dissolution of the precipitate particles. However, the hardness gradually increased in the TMAZ and reached a plateau in the SZ due to reprecipitation of Mg₂Si during the following natural aging [34].

Figure 8

Hardness profile along mid-thickness of Al 6061 sheet

Lap Shear Strength

Relationship between tool sleeve penetration depth and weld lap shear load was presented in Figure 9a. Overall, the weld lap shear load was insensitive to the welding condition, because the frictional heat can be immediately dissipated to the steel anvil through the bottom copper sheet material, although higher penetration depth/rate could generate more heat. The weld lap shear load slightly increased to a maximum value of 2.19 kN when the penetration improved from 1.2 mm to 1.4 mm, which further slightly reduced to 2.10 kN when the sleeve penetration depth improved from 1.4 to 1.8 mm. As indicated in Figure 10, compared to the lap shear load of FSSWed Al/copper dissimilar welds derived from both metallurgical bonding and mechanical inter-locking mechanisms, it can be concluded that acceptable weld strength can be achieved via pure metallurgical joining mechanism. Figure 9b shows a typical lap shear load/displacement curve of the weld fabricated using a penetration depth of 1.8 mm, it is clearly that the weld failed in a brittle manner, because the fracture exclusively propagated through the IMCs layer (see Figure 11).

Figure 9

(a) relation between sleeve penetration depth and weld lap shear strength, (b) typical lap shear load/displacement curve of Al/copper weld

Figure 10

Summary of published workpiece thickness versus Al/copper spot welds lap shear strength [35,36,37,38,39,40,41,42,43]

Figure 11

(a) Interfacial fractured surface on the cupper side of the weld fabricated using a sleeve penetration depth of 1.8 mm, (b) XRD patterns obtained from the fracture surfaces

Failure Mode

Figure 11a presents a typical fractured surface of the Al/copper weld on the copper side of a fractured weld fabricated using a sleeve penetration depth of 1.8 mm. It should be noted that only interfacial failure mode was observed when the welds were evaluated under external lap shear loadings. The fracture area was consistent with the diameter of the rotating sleeve, which was really flat and no macroscopic or microscopic deformation can be observed. The fracture initiated at the weld edge (Cu₉Al₄ layer) and then propagated towards the weld center and along the weld edge. The chemical component distribution and XRD patterns obtained from the fractured surfaces were shown in Table 4 and Figure 11b, respectively. The fracture exclusively propagated long the Cu₉Al₄ IMCs layer, both CuAl₂ and Cu₉Al₄ were detected on the fractured surfaces.

Table 4 EDX quantification results (wt%) indicated in Figure 11a

Conclusions

In this investigation, interfacial microstructure and mechanical performance of Al/copper dissimilar refill friction stir spot welds were systematically evaluated in terms of interfacial microstructure, hardness profile, lap shear load and failure mechanism. The following conclusions can be drawn based on the experimental observations:

• (1) Defect-free Al/copper welds were manufactured by refill FSSW using a standard sleeve tool under all welding conditions applied in the present study. Two different types of thin and continuous IMCs layers were produced at the Al/copper interface, which was thicker at the weld edge and thin at the weld interface center. Evidence of resolidification was identified at the localized region and upwards material flow pattern was observed around the weld edge.

• (2) A softened welded zone was produced in the top Al 6061 sheet material, and the hardness profile presented a W-shaped appearance. The minimum hardness was identified at the junction of TMAZ and HAZ.

• (3) The weld lap shear load was relatively repeatable and insensitive to the welding condition. Acceptable weld strength can be achieved through pure metallurgical joining mechanism. The fracture exclusively propagated along the IMCs layer of Cu₉A_l4 under the external lap shear loads, both CuAl₂ and Cu₉Al₄ were detected on the fractured surfaces.