A Novel Friction Stir Deposition Technique to Refill Keyhole of Friction Stir Spot Welded AA6082-T6 Dissimilar Joints of Different Sheet Thicknesses

Joining dissimilar sheet thicknesses of AA6082-T6 alloys by friction stir spot welding (FSSW) provides many advantages in automotive and aerospace applications. The formed keyhole at the end of the FSSW process is one of the typical features after the welding process, which owns the same size as the rotating pin that remains at the joint center. This keyhole destroys the joint continuity and can stimulate serious stress concentration when the FSSW joint bears an external force. To solve this issue, a novel refilling technique was developed for the FSSW keyholes using a friction stir deposition (FSD) technique. The FSSW joints of AA6082-T6 sheets were welded at various rotation speeds from 400 to 1000 rpm and a constant dwell time of 3 s, where a 2 mm sheet thickness was an upper sheet, and a 1 mm sheet thickness was a lower sheet. All the keyhole refilling processes were achieved using a specially designed AA2011-T6 consumable rod to be used for friction stir deposition of continuous layers at a constant deposition parameter of 400 rpm consumable rod rotation speed and a 1 mm/min feed rate. The heat input energy for both the FSSW and refilled FSSW lap joints was calculated. In addition, the FSSW and the FSD temperatures were measured. Macrostructure, microstructure, and mechanical properties in terms of hardness and tensile shear maximum load were evaluated for both the friction stir spot welded (FSSWed) and the refilled FSSW lap joints. The obtained results showed that the keyhole could be successfully refilled with defect-free continuous multilayers after the refill friction stir spot welding (RFSSW) process. All the RFSSW lap joints showed higher tensile shear loads than that given by the FSSW (before refill) lap joints. The RFSSW joint (welded at 600 rpm/3 s and refilled at 400 rpm/1 mm/min) showed a higher tensile shear load of 5400 N ± 100 compared with that recorded by the unrefilled joint (4300 N ± 80). The fracture location and fracture surface of the FSSW and RFSSW were examined and discussed.


Introduction
Lightweight components are essential in the automotive and aerospace industries for the reduction of CO 2 emissions. The usage of aluminum alloys can reduce the vehicle structure's total weight [1,2]. Different spot joining techniques have been used in the automotive industry, such as riveting and resistance spot welding. Recently, to avoid the drawbacks of these spot welding techniques, alternative joining techniques in terms of friction stir welding (FSW) and its derivative friction stir spot welding (FSSW) processes are used for joining similar [3,4] and dissimilar structural materials [5][6][7][8][9] in engineering

Starting Materials
The starting materials to achieve dissimilar thickness friction stir spot welds were two thin sheets of AA6082-T6 with dimensions of 1 × 1000 × 1000 mm and 2 × 1000 × 1000 mm. Meanwhile, the keyhole filling material was AA2011-T6 rods with initial dimensions of 20 mm diameter and 100 mm length. Both the AA6082-T6 sheets and the AA2011-T6 rods were supplied by the Future Fond Company, Milano, Italy. The chemical compositions of the used AA6082-T6 sheets and the AA2011-T6 rods were performed using Foundry-Master Pro, Oxford Instruments, Abingdon, UK, and are listed in Table 1.

Friction Stir Spot Welding and Friction Stir Deposition Processes
The FSSW joints and the FSD refilled samples were carried out using the friction stir welding/processing machine (EG-FSW-M1) [35]. For the spot welding process, the two AA6082-T6 dissimilar sheets were cut to specimens with dimensions of 30 mm width and 100 mm length. The cut specimens were FSSWed in lap joints at a constant dwell time of 3 s and various rotational speeds of 400, 600, 800, and 1000 rpm, where the two different sheet thicknesses overlapped with a 30 mm length. The other FSSW parameters in terms of plunge rate and plunge depth were kept constant at 0.1 mm/s and 2.6 mm, respectively. The used FSSW tool was made of steel (AISI H13) with dimensions of 20 mm shoulder diameter, 2.6 mm pin length, and 5 mm pin diameter. The tool shoulder was flat, and the pin was cylindrical. The tool features and dimensions are given in Figure 1.
Materials 2022, 15, x FOR PEER REVIEW 3 of 26 1000 rpm. A specially designed consumable rod of AA2011-T6 was suggested. The heat input energy at applied deposition process parameters of 400 rpm consumable rod rotation speed and 1 mm/min feed rate was studied, and a new equation to calculate the heat input energy was suggested. The current work aims also to conduct a comparative study of the FSSW and the RFSSW lap joints in terms of macrostructure, microstructure, hardness, maximum tensile shear, and fracture behaviors.

Starting Materials
The starting materials to achieve dissimilar thickness friction stir spot welds were two thin sheets of AA6082-T6 with dimensions of 1 × 1000 × 1000 mm and 2 × 1000 × 1000 mm. Meanwhile, the keyhole filling material was AA2011-T6 rods with initial dimensions of 20 mm diameter and 100 mm length. Both the AA6082-T6 sheets and the AA2011-T6 rods were supplied by the Future Fond Company, Milano, Italy. The chemical compositions of the used AA6082-T6 sheets and the AA2011-T6 rods were performed using Foundry-Master Pro, Oxford Instruments, Abingdon, UK, and are listed in Table 1.

Friction Stir Spot Welding and Friction Stir Deposition Processes
The FSSW joints and the FSD refilled samples were carried out using the friction stir welding/processing machine (EG-FSW-M1) [35]. For the spot welding process, the two AA6082-T6 dissimilar sheets were cut to specimens with dimensions of 30 mm width and 100 mm length. The cut specimens were FSSWed in lap joints at a constant dwell time of 3 s and various rotational speeds of 400, 600, 800, and 1000 rpm, where the two different sheet thicknesses overlapped with a 30 mm length. The other FSSW parameters in terms of plunge rate and plunge depth were kept constant at 0.1 mm/s and 2.6 mm, respectively. The used FSSW tool was made of steel (AISI H13) with dimensions of 20 mm shoulder diameter, 2.6 mm pin length, and 5 mm pin diameter. The tool shoulder was flat, and the pin was cylindrical. The tool features and dimensions are given in Figure 1.   Figure 2c). Finally, Figure 2d shows the representative spot-welded joint's top view with the formed keyhole. The temperature during the FSSW process at the applied different rotational speeds of 400 to 1000 rpm was recorded using a modern digital multimeter (type-UT61B, Zhejiang, China) with a thermocouple type "K".   Figure 2d shows the representative spot-welded joint's top view with the formed keyhole. The temperature during the FSSW process at the applied different rotational speeds of 400 to 1000 rpm was recorded using a modern digital multimeter (type-UT61B, Zhejiang, China) with a thermocouple type "K". In order to explore the applicability of FSD for refilling the left keyhole after FSSW, an AA2011-T6 consumable rod was machined (according to the keyhole volumetric dimension) to a profile of a flat shoulder of 20 mm diameter and a tapered pin of 5 mm diameter and 3 mm pin length (as shown in Figure 3a) to be tried as a filling material in continuous layers via the FSD process. Figure 3 illustrates the FSD process stages, which involve three steps: fixing the AA 2011-T6 consumable rod in the spindle shank ( Figure  3a) and rotating it at a constant rotation of speed 400 rpm while moving downward to reach the FSSW keyhole of the AA6082-T6 joint ( Figure 3b). Finally, under a continuous feeding speed of 1 mm/min, the rod plastically deformed due to the high friction and the generated heat between the rod and the keyhole substrate, causing the material transfer from the consumable rod to the keyhole to build a material upward yielding refilling. Figure 3e shows the representative top view of the refilled FSSW joint. In order to explore the applicability of FSD for refilling the left keyhole after FSSW, an AA2011-T6 consumable rod was machined (according to the keyhole volumetric dimension) to a profile of a flat shoulder of 20 mm diameter and a tapered pin of 5 mm diameter and 3 mm pin length (as shown in Figure 3a) to be tried as a filling material in continuous layers via the FSD process. Figure 3 illustrates the FSD process stages, which involve three steps: fixing the AA 2011-T6 consumable rod in the spindle shank ( Figure 3a) and rotating it at a constant rotation of speed 400 rpm while moving downward to reach the FSSW keyhole of the AA6082-T6 joint ( Figure 3b). Finally, under a continuous feeding speed of 1 mm/min, the rod plastically deformed due to the high friction and the generated heat between the rod and the keyhole substrate, causing the material transfer from the consumable rod to the keyhole to build a material upward yielding refilling. Figure 3e shows the representative top view of the refilled FSSW joint.
The produced FSSWed and refilled friction stir spot welded (RFSSWed) joints were sectioned for macrostructure investigation, microstructure evaluation, and hardness test. The cross-sectional specimens were ground with SiC papers up to 2400 grit, then polished using a polishing vel-cloth in the presence of alumina paste suspension up to a surface finish of 0.05 µm. A chemical etcher consisting of 2.5 mL nitric acid (HNO 3 ), 1.5 mL hydrochloric acid (HCl), 95 mL distilled water, and 1 mL hydrofluoric (HF) was applied to all the polished specimens before microstructure investigation. The microstructure evaluation was performed using an Olympus optical microscope (OM) (BX41M-LED, Olympus, Tokyo, Japan). The hardness test was carried out along three lines across the transverse sections of the FSSWed and the refill friction stir spot welded (RFSSWed) joints for obtaining hardness profiles (Figure 4). The hardness measurements were carried out using an applied load of 5 N with a dwell time of 15 s using a Vickers hardness tester (model HWDV-75, TTS Unlimited, Osaka, Japan). The distance between every two indentations was set to 0.5 mm along the cross section of the produced FSSWed and RFSSWed joints. The tensile- shear test was performed at room temperature using a 30 ton universal tensile testing machine (Type-WDW-300D, Guangdong, China) at a constant loading rate of 0.1 mm/min. During the tensile-shear test, two backing sheets were used to ensure the application of the axial loading ( Figure 5). After tensile shear testing, the fractured surfaces at the interface between the upper and lower sheets were examined using a scanning electron microscope (SEM-Quanta FEG 250-FEI Company, Hillsboro, OR, USA). For comparison purposes, the as-received materials were examined and tested using the previous described methods.  The produced FSSWed and refilled friction stir spot welded (RFSSWed) joints were sectioned for macrostructure investigation, microstructure evaluation, and hardness test. The cross-sectional specimens were ground with SiC papers up to 2400 grit, then polished using a polishing vel-cloth in the presence of alumina paste suspension up to a surface finish of 0.05 µm. A chemical etcher consisting of 2.5 mL nitric acid (HNO3), 1.5 mL hydrochloric acid (HCl), 95 mL distilled water, and 1 mL hydrofluoric (HF) was applied to all the polished specimens before microstructure investigation. The microstructure evaluation was performed using an Olympus optical microscope (OM) (BX41M-LED, Olympus, Tokyo, Japan). The hardness test was carried out along three lines across the transverse sections of the FSSWed and the refill friction stir spot welded (RFSSWed) joints for obtaining hardness profiles ( Figure 4). The hardness measurements were carried out using an applied load of 5 N with a dwell time of 15 s using a Vickers hardness tester (model mm/min. During the tensile-shear test, two backing sheets were used to ensure the application of the axial loading ( Figure 5). After tensile shear testing, the fractured surfaces at the interface between the upper and lower sheets were examined using a scanning electron microscope (SEM-Quanta FEG 250-FEI Company, Hillsboro, OR, USA). For comparison purposes, the as-received materials were examined and tested using the previous described methods.

FSSWed and RFSSWed Joint Surfaces' Appearance
The top and bottom surfaces of the produced FSSWed AA6082-T6 dissimilar sheet thickness and their RFSSWed joints with AA2011-T6 deposited layers at the applied processing parameters (FSSW and refill processing parameters) are shown in Figure 6. The top and bottom surfaces of the FSSW lap joints welded at different rotation speeds of 400,

FSSWed and RFSSWed Joint Surfaces' Appearance
The top and bottom surfaces of the produced FSSWed AA6082-T6 dissimilar sheet thickness and their RFSSWed joints with AA2011-T6 deposited layers at the applied processing parameters (FSSW and refill processing parameters) are shown in Figure 6. The top and bottom surfaces of the FSSW lap joints welded at different rotation speeds of 400, 600, 800, and 1000 rpm and a constant dwell time of 3 s are represented in Figure 6a. Meanwhile, the top and the bottom surfaces of the RFSSW joints processed at a constant consumable rod rotation speed of 400 rpm and a constant feed rate of 1 mm/min are shown in Figure 6b. It can be remarked that the applied welding parameters for joining the dissimilar thicknesses of the AA6082-T6 thin sheet are appropriate to produce successful spot joints. The circular indentations are shown at the top surface views of the FSSW lap joints, indicating the shoulder projection for all the applied welding parameters. The sizes of the extruded flash materials are also the same (Figure 6a). Furthermore, the bottom surface views of the FSSW lap joints show the affected areas (dark areas) by thermal exposure due to the FSSW process (as shown in Figure 6a). These thermal affected areas become darker by increasing the rotation speeds from 400 to 1000 rpm at a constant dwell time of 3 s due to the increase in heat input generation with increasing rotation speed [6,36], as seen in Figure 6a.  Figure 6b shows the top surface appearance of RFSSWed joints with FSD process parameters of 400 rpm consumable tool rotation speed and 1 mm/min constant feeding rate. Visually, it can be remarked that defect-free refilling using AA2011 material top surfaces was attained for all the processed joints. It can be concluded that the suggested FSD parameters succeeded to refill all the keyholes and the shoulder projections of the FSSW lap joints. In addition, there was no remarkable effect of the exposure thermal cycle during FSD on the bottom surface appearance of the RFSSW lap joints ( Figure 6b) compared to that given by the unrefilled FSSW joints ( Figure 6a).

Heat Input Energy Calculations and Peak Temperature Measurements
The total heat input energy is the summation of the generated heat input energy at the contact shoulder area and the pin surrounding contact area. The generated heat input energy during the FSSW process depends on the tool design, tool material, friction axial downward force, friction coefficient at the interface between the rotating pin and the surrounded stirring material, applied dwell time, and rotation speed [9,37]. The heat input is generated by converting the mechanical energy from the friction of the rotating tool through the joint thickness during the FSSW thermomechanical process. The heat input energy for the FSSW process (Q) can be calculated based on the following equations [9,38]:  Figure 6b shows the top surface appearance of RFSSWed joints with FSD process parameters of 400 rpm consumable tool rotation speed and 1 mm/min constant feeding rate. Visually, it can be remarked that defect-free refilling using AA2011 material top surfaces was attained for all the processed joints. It can be concluded that the suggested FSD parameters succeeded to refill all the keyholes and the shoulder projections of the FSSW lap joints. In addition, there was no remarkable effect of the exposure thermal cycle during FSD on the bottom surface appearance of the RFSSW lap joints (Figure 6b) compared to that given by the unrefilled FSSW joints (Figure 6a).

Heat Input Energy Calculations and Peak Temperature Measurements
The total heat input energy is the summation of the generated heat input energy at the contact shoulder area and the pin surrounding contact area. The generated heat input energy during the FSSW process depends on the tool design, tool material, friction axial downward force, friction coefficient at the interface between the rotating pin and the surrounded stirring material, applied dwell time, and rotation speed [9,37]. The heat input is generated by converting the mechanical energy from the friction of the rotating tool through the joint thickness during the FSSW thermomechanical process. The heat input energy for the FSSW process (Q) can be calculated based on the following equations [9,38]: where µ is the friction coefficient between the steel tool and the aluminum alloy sheet, which equals 0.4 [4]; P is the applied downward force (in N); K A is the ratio of the shoulder contact area to cross-sectional area of the rotating tool; ω is rad/s and equals π 30 n, where n is the applied rotational speed (in rpm); r is the pin radius (in m); and t is the dwell time (in s) during the FSSW process: (shoulder radius of the rotating tool) 2 − (pin radius) 2 (shoulder radius of the rotating tool) 2 (2) where the shoulder radius of the rotating tool and pin radius is equal to 10 and 2.5 mm, respectively. Then K A = 0.9375. From Equations (1) and (2), the calculated heat input energy is as follows: The calculated Q of the FSSW joints is plotted against the applied rotation speed, as given in Figure 7. It can be noted that the increase of the rotation speeds from 400 to 1000 rpm leads to an increase in the generated heat input energy from 1434 to 3351 J during the FSSW process [39]. The FSSW thermal cycle exposure and the measured temperatures of the produced FSSW lap joints are shown in Figure 8.
The thermal cycles of the FSSW AA6082-T6 lap joint in terms of the measured working temperature against the consuming time to yield the spot joint at the applied rotation speeds of 400 to 1000 rpm are given in Figure 8. It can be observed that the experienced thermal cycle for all the processed joints gives the same trends at the welding parameters, with difference in the peak temperatures at each tool rotation speed. Each thermal cycle involves three stages, including rising temperature gradually by inserting the rotating tool pin at a constant feeding rate of 0.1 mm/s through the clamping of two different sheet thicknesses of AA6082-T6 (first stage). The second stage represents the dwell time required to perform the spot weld at near temperature stability. The last stage represents rotating tool retracting at the end of the spot-welding process. Table 2 illustrates the measured peak temperature in the stir zone (SZ) during the FSSW process. It can be noted that the peak temperature increases from to 225 ± 2 to 350 ± 2 with the increasing tool rotation speed from 400 to 1000 rpm, respectively, as a result of frictional heat during the stirring process [39].
The calculated Q of the FSSW joints is plotted against the applied rotation speed, as given in Figure 7. It can be noted that the increase of the rotation speeds from 400 to 1000 rpm leads to an increase in the generated heat input energy from 1434 to 3351 J during the FSSW process [39]. The FSSW thermal cycle exposure and the measured temperatures of the produced FSSW lap joints are shown in Figure 8.   The thermal cycles of the FSSW AA6082-T6 lap joint in terms of the measured working temperature against the consuming time to yield the spot joint at the applied rotation speeds of 400 to 1000 rpm are given in Figure 8. It can be observed that the experienced thermal cycle for all the processed joints gives the same trends at the welding parameters, with difference in the peak temperatures at each tool rotation speed. Each thermal cycle involves three stages, including rising temperature gradually by inserting the rotating tool pin at a constant feeding rate of 0.1 mm/s through the clamping of two different sheet thicknesses of AA6082-T6 (first stage). The second stage represents the dwell time required to perform the spot weld at near temperature stability. The last stage represents rotating tool retracting at the end of the spot-welding process. Table 2 illustrates the measured peak temperature in the stir zone (SZ) during the FSSW process. It can be noted that the peak temperature increases from to 225 ± 2 to 350 ± 2 with the increasing tool rotation  Based on the friction stir processing [40][41][42] and deposition [43,44] concepts, the total heat input (Q t ) to refill the FSSW keyhole via FSD is the summation of the frictional heat generated by the consumable tool shoulder between the rotating consumable pin and the surrounded material in the vicinity of the keyhole and at the consumable pin tip. In general, the heat generation is given as follows: P is the contact pressure at friction interfaces, and it is equal to the axial downward force divided by the projected areas.
The heat input generation under the consumable rod shoulder (Q 1 ) is calculated by integration Equation (4).
The heat input generation between the rotating consumable pin and the surrounded material in the vicinity of the keyhole (Q 2 ) is calculated by integration Equation (4).
The heat input generation at the consumable pin tip (Q 3 ) is calculated by integration Equation (4).
The total heat input energy (Q t ) is calculated by summations of Equations (5)- (8): where Q t is in watt, µ is the friction coefficient between AA6082-T6 keyhole material and AA2011-T6 consumable rod material and equals 1.4 [45], ω is in rad/s and equals π n 30 , n is the rotational speed (in rpm), F is the axial downward force (in N), r s is the consumable rod shoulder radius (in m), r p is the consumable rod pin radius (in m), H p is the consumable rod pin height (in m), and t is the deposition time (in s).
The refilling time of FSD = refill height ×60 = 180 s. The total heat input energy (QE) = Q t × t (in J). The knowledge of the thermal cycle in terms of the heat generation and the temperature history during the FSD process is very important in understanding the thermomechanical interaction occurring during the deposition process in the keyhole of the FSSW joint. The heat generates at the contact area between the consumable rod and the substrate (keyhole bottom) due to the friction during the stirring process. The heat to develop a bond between the keyhole bottom and the deposited material involves transferred heat to the FSD consumable tool, transferred heat to the keyhole bottom, and remaining heat for depositing a material [43]. When the generated peak temperature during the FSD process is below the melting point of the deposition material, the deformation is a solid-state process [43,46]. The thermal cycle to achieve refilling of the FSSW joints of AA6082-T6 is represented as temperature versus time, as given in Figure 9. It can be noted that the deposition peak temperature is 247 • C, which is below the melting point of the AA2011-T6 deposited material. This solid-state process promotes good bonding between the AA2011-T6 deposited material and the keyhole bottom of FSSW dissimilar thickness joints. A similar finding in terms of good bonding between the deposited materials and the substrates is reported by other researchers to build sound continuous layers of as-cast hypoeutectic A356 Al alloy on the AA2024 substrate [30] and also sound continuous layers of AA2011 in two temper conditions on the AA5083 substrate [29] without any defects at the interface. in two temper conditions on the AA5083 substrate [29] without any defects at the interface. Figure 9. The temperature measurements against time during the FSD process. Figure 10 illustrates the transverse macrographs of the FSSW AA6082-T6 dissimilar sheet thickness joints and their RFSSW counterparts. It can be seen that the applied FSSW parameters resulted in defect-free welds at the interface of the overlapped 1 mm and 2 mm AA6082-T6 sheets (Figure 10a-d). In addition, the excessive extruded flash material was eliminated as a result of the FSSW optimization welding parameters based on some experiments and published works [3,6]. The resulting spot welded joint has a characteristic hole in the middle of the joint; this hole is left by the pin after removal. This keyhole (material loss) is the main defect in the FSSW process, and it is a good representative of the pin dimensions and geometry (Figure 10a-d). Figure 10e-h represents the cross-section macrographs of the RFSSW joints. The keyhole refilling process was achieved at the deposition conditions of 400 rpm consumable rod rotation speed and 1 mm/min deposition rate. It can be remarked that the keyhole can be successfully refilled by the FSD process using the deposition material of AA2011-T6. Furthermore, the deposited materials bonded well with the keyhole inner surface without porosity and microcracks for all the refilled joints.  Figure 10 illustrates the transverse macrographs of the FSSW AA6082-T6 dissimilar sheet thickness joints and their RFSSW counterparts. It can be seen that the applied FSSW parameters resulted in defect-free welds at the interface of the overlapped 1 mm and 2 mm AA6082-T6 sheets (Figure 10a-d). In addition, the excessive extruded flash material was eliminated as a result of the FSSW optimization welding parameters based on some experiments and published works [3,6]. The resulting spot welded joint has a characteristic hole in the middle of the joint; this hole is left by the pin after removal. This keyhole (material loss) is the main defect in the FSSW process, and it is a good representative of the pin dimensions and geometry (Figure 10a-d). Figure 10e-h represents the crosssection macrographs of the RFSSW joints. The keyhole refilling process was achieved at the deposition conditions of 400 rpm consumable rod rotation speed and 1 mm/min deposition rate. It can be remarked that the keyhole can be successfully refilled by the FSD process using the deposition material of AA2011-T6. Furthermore, the deposited materials bonded well with the keyhole inner surface without porosity and microcracks for all the refilled joints.  Figure 10. Transverse cross-section macrographs of (a-d) the FSSW lap joints of AA6082-T6 welded at a constant dwell time of 3 s and different rotational speeds of 400 to 1000 rpm [36] and (e-h) RFSSW deposited at a 400 rpm rotation speed and a 1 mm/min deposition rate.

Microstructure Investigation of the Base Materials
The microstructures of the base materials (BMs) for the two AA6082-T6 sheet thicknesses at 1 and 2 mm and the AA2011-T6 rod Al alloys are shown in Figure 11. It can be seen that the microstructures of the AA6082-T6 BMs show coarse and elongated grain structures, indicating the rolling directions. In addition, they contain comparatively coarse (Fe, Mn)3SiAll2 intermetallic and low-density fine dispersed Mg2Si precipitates. These microstructure features are consistent with that reported in other works [2,36,47]. It can be observed also that the AA 6082-T6 sheets of 1 ( Figure 11a) and 2 mm (Figure 11b) Figure 10. Transverse cross-section macrographs of (a-d) the FSSW lap joints of AA6082-T6 welded at a constant dwell time of 3 s and different rotational speeds of 400 to 1000 rpm [36] and (e-h) RFSSW deposited at a 400 rpm rotation speed and a 1 mm/min deposition rate.

Microstructure Investigation of the Base Materials
The microstructures of the base materials (BMs) for the two AA6082-T6 sheet thicknesses at 1 and 2 mm and the AA2011-T6 rod Al alloys are shown in Figure 11. It can be seen that the microstructures of the AA6082-T6 BMs show coarse and elongated grain structures, indicating the rolling directions. In addition, they contain comparatively coarse (Fe, Mn) 3 SiAl l2 intermetallic and low-density fine dispersed Mg 2 Si precipitates. These microstructure features are consistent with that reported in other works [2,36,47]. It can be observed also that the AA 6082-T6 sheets of 1 ( Figure 11a) and 2 mm (Figure 11b) thickness have average grain sizes of 11 ± 2 and 17 ± 1.5 µm, respectively. The variation in the grain size values of the two sheets can be ascribed to imposing different rolling conditions to produce different sheet thicknesses. This reduction in thickness as a result of high accumu-lated plastic deformation promotes high internal strain, which increases the strength [48]. As reported in [28,29], the microstructure of the AA2011-T6 rod alloy shows coarse grains and the intermetallics of Al 7 Cu 2 Fe (rodlike shape) and Al 2 Cu (almost spherical or irregular shapes), as shown in Figure 11c. thickness have average grain sizes of 11 ± 2 and 17 ± 1.5 µm, respectively. The variat the grain size values of the two sheets can be ascribed to imposing different rolling ditions to produce different sheet thicknesses. This reduction in thickness as a res high accumulated plastic deformation promotes high internal strain, which increas strength [48]. As reported in [28,29], the microstructure of the AA2011-T6 rod alloy s coarse grains and the intermetallics of Al7Cu2Fe (rodlike shape) and Al2Cu (almost s ical or irregular shapes), as shown in Figure 11c.

Hardness Results Evaluation
Hardness measurements were carried out on the transverse cross sections of bo AA6082-T6 FSSW joints of the dissimilar sheet thickness and RFSSW joints and plot a hardness profile. Figure 12 shows the hardness profile for the FSSW joints produ a constant dwell time of 3 s and different rotation speeds of 400, 600, 800, and 1000 Meanwhile, Figure 13 represents the hardness profile of the RFSSW joints, refilled AA2011-T6 via the FSD process at a 400 rpm rotation speed and a 1 mm/min feed ra Compared with the different sheet thickness AA6082-T6 BMs, the hardness weld zones, the SZ, thermomechanically affected zone (TMAZ), and the heat-aff zone (HAZ) of the FSSWed joints at the used rotation speeds of 400, 600, 800, and rpm significantly decreased, as shown in Figure 12a-d, respectively, due to anneal the AA6082-T6 BMs during the FSSW process. It was reported that the hardness v across the weld zones of the joints of heat-treatable Al alloys are affected by therm posure during FSW [36,49]. Among the weld zones for each FSSWed joint, the mini hardness values were observed in the HAZ due to the grain structure and overaging [36]. In contrast, the hardness improvement in the SZ is mainly due to the format

Hardness Results Evaluation
Hardness measurements were carried out on the transverse cross sections of both the AA6082-T6 FSSW joints of the dissimilar sheet thickness and RFSSW joints and plotted in a hardness profile. Figure 12 shows the hardness profile for the FSSW joints produced at a constant dwell time of 3 s and different rotation speeds of 400, 600, 800, and 1000 rpm. Meanwhile, Figure 13 represents the hardness profile of the RFSSW joints, refilled with AA2011-T6 via the FSD process at a 400 rpm rotation speed and a 1 mm/min feed rate.   Compared with the different sheet thickness AA6082-T6 BMs, the hardness of the weld zones, the SZ, thermomechanically affected zone (TMAZ), and the heat-affected zone (HAZ) of the FSSWed joints at the used rotation speeds of 400, 600, 800, and 1000 rpm significantly decreased, as shown in Figure 12a-d, respectively, due to annealing of the AA6082-T6 BMs during the FSSW process. It was reported that the hardness values across the weld zones of the joints of heat-treatable Al alloys are affected by thermal exposure during FSW [36,49]. Among the weld zones for each FSSWed joint, the minimum hardness values were observed in the HAZ due to the grain structure and overaging effect [36]. In contrast, the hardness improvement in the SZ is mainly due to the formation of dynamically recrystallized fine grains and the reprecipitation process that might take place during the cooling cycle. The TMAZ hardness gives lower values than the SZ and higher values than the HAZ. The increase in hardness of the TMAZ over the HAZ is likely due to the high dislocation density achieved by plastic deformation during the process of FSSW [14,47]. The highest hardness of the weld zones is achieved for the FSSWed joint at 600 rpm (Figure 12b). Thus, selected areas on the macrostructure of this joint (Figure 14a) were investigated using OM as a representative of the weld zone microstructure features. It can be seen that the welding zones on both sides of the keyhole center line look like a mirror and are arranged as SZ, TMAZ, and HAZ, as given in Figure 14b (left side) and Figure 14c (right side). The keyhole surrounding area is the SZ achieved during the FSSW process of the two AA6082-T6 sheets, and it is characterized by equiaxed refined grains (Figure 14e). Generally, optimizing the FSW [50,51] and the FSSW [3,36] parameters leads to grain refinement in the SZ due to dynamic recrystallization. These variations in microstructure features correspond to the variation in the hardness values in the weld zones (Figure 12b).
Instead of incomplete W-shape hardness profiles of the FSSWed joints (Figure 12), complete W-shape hardness profiles are achieved for the RFSSWed joints ( Figure 13). As mentioned before in the experimental section, the FSD process was performed at the condition of 400 rpm AA2011-T6 consumable rod rotation speed and 1 mm/min feed rate. Thus, it is expected that the deposited material (keyhole refilling material) has the same microstructure feature and mechanical properties. The average measured hardness value of the refilled keyhole is 117 ± 5 HV for all the RFSSW joints, as shown in Figure 13a-d. During the deposition process, the material of the rotating consumable rod is subjected to severe plastic deformation at high homologous temperatures. As a result, the material deposited by the friction stirring process undergoes dynamic recrystallization and develops a very fine grain size [28,29]. El-Sayed Seleman et al. [28] studied utilizing the FSD process to manufacture continuous multilayer high-performance, metal-based AA2011/nano Al 2 O 3 composites using AA2011 in two temper conditions of AA2011-T6 and AA2011-O as a matrix. The results showed that the microstructure of the starting, consumable rods, AA2011-T6 and AA2011-O, was changed from coarse grain to refined equiaxed grain throughout the deposited material. Additionally, the size of precipitates (Al 7 Cu 2 Fe and Al 2 Cu) decreased with the stirring action during FSD for the deposited matrix and the produced composite. The dispersion and fragmentation of these intermetallics in the Al matrix have been detected in other works [29,33]. These microstructure features are gained for the deposited material in the keyholes of the FSSW joints. Figure 14f shows the microstructure of the AA6082-T6 RFSSWed joint welded at 600 rpm and 3 s with keyhole refilling by AA2011-T6 via the FSD conditions of 400 rpm and 1 mm/min. It can be seen that equiaxed refined grains (average grain size 2 ± 0.2 µm) due to the dynamic recrystallization compared with coarse grains AA2011-T6 rod BM (45 ± 8 µm) are detected. In addition, the intermetallics (Al 7 Cu 2 Fe and Al 2 Cu) are highly dispersed and fragmented.

Tensile Shear Test and Fracture Surfaces
The tensile shear test is an important mechanical property for joint efficiency evaluation for vehicles and automotive structure designs. The tensile shear value of the spot welded joint is affected by FSSW process parameters [6,9,21,22]. The maximum tensile shear load of the FSSW and RFSSW lap joints of AA6082-T6 dissimilar sheet thickness is illustrated in Figure 15.

Tensile Shear Test and Fracture Surfaces
The tensile shear test is an important mechanical property for joint efficiency evaluation for vehicles and automotive structure designs. The tensile shear value of the spot welded joint is affected by FSSW process parameters [6,9,21,22]. The maximum tensile shear load of the FSSW and RFSSW lap joints of AA6082-T6 dissimilar sheet thickness is illustrated in Figure 15. It can be noted that the FSSW joint welded at a constant dwell time of 3 s by applying a tool rotation speed of 600 rpm gives the highest tensile shear load of 4300 ± 80 N compared with that obtained by the other welded joints. The two AA6082-T6 sheets of this joint are still connected after the tensile shear testing, as given in Figure 16a-c. This indicates high joint efficiency and may be ascribed to a larger fully bonded section size and a lower hook height [36]. Besides, the enhancement in hardness in the SZ of this joint is over than that noted in the stir zones of the other spot-welded joints. In contrast, the FSSWed joints processed at the same dwell time (3 s) and different tool rotation speeds of 400, 800, and 1000 rpm are completely separated during the tensile shear testing, as given in Figure  17a. On the one hand, the failed joint FSSWed at a relatively lower rotation speed of 400 rpm may be attributed to insufficient heat input, which affects in mixing the dissimilar sheet thicknesses AA6082-T6 during the welding process. On the other hand, the tensile shear loads of the spot welds produced at higher tool rotation speeds of 800 and 1000 rpm illustrate a decrease in the maximum tensile shear load. This decrease in strength for these joints is ascribed to the increase in thermal softening in the SZ with the increasing the heat input and also to the reduced thickness of the upper sheet underneath the shoulder. Ohashi et al. [52] and Xie et al. [53] reported that the mechanical properties of the FSSW joints are mainly governed by both the weld bonded area and the upper sheet underneath the shoulder. In addition, the precipitate-free zones around the grain boundaries due to precipitate coarsening might have reduced the strength of the SZ [36]. From Figure 15, it can be also seen that all the RFSSW lap joints show higher tensile shear loads than that given by the FSSW (unrefilled FSSW) lap joints. The RFSSW joint (welded at 600 rpm/3 s and refilled at 400 rpm/1 mm/min) shows the highest tensile shear load of 5400 N ±100. Its enhancement in the tensile shear load is 25% over that recorded by the unrefilled spot joint. The two sheets of the RFSSW joint are still connected after the tensile shear testing, as given in Figure 16d-f. Furthermore, the other refilled joints show enhancements of 45%, 73%, and 273% over the unrefilled joints processed at 400, 800, and 1000 rpm, respectively. This enhancement for all the refilled joints is ascribed to the repairing of the keyhole defect by depositing high-strength AA 2011-T6 Al alloy via FSD and the strong bonding between the filling deposited material and the key hole interface, in addition to the microstructure features of the filling cavity of the keyhole. Both the deposition process and the good bonding between the keyhole interface and the FSD material filling the cavity are achieved It can be noted that the FSSW joint welded at a constant dwell time of 3 s by applying a tool rotation speed of 600 rpm gives the highest tensile shear load of 4300 ± 80 N compared with that obtained by the other welded joints. The two AA6082-T6 sheets of this joint are still connected after the tensile shear testing, as given in Figure 16a-c. This indicates high joint efficiency and may be ascribed to a larger fully bonded section size and a lower hook height [36]. Besides, the enhancement in hardness in the SZ of this joint is over than that noted in the stir zones of the other spot-welded joints. In contrast, the FSSWed joints processed at the same dwell time (3 s) and different tool rotation speeds of 400, 800, and 1000 rpm are completely separated during the tensile shear testing, as given in Figure 17a. On the one hand, the failed joint FSSWed at a relatively lower rotation speed of 400 rpm may be attributed to insufficient heat input, which affects in mixing the dissimilar sheet thicknesses AA6082-T6 during the welding process. On the other hand, the tensile shear loads of the spot welds produced at higher tool rotation speeds of 800 and 1000 rpm illustrate a decrease in the maximum tensile shear load. This decrease in strength for these joints is ascribed to the increase in thermal softening in the SZ with the increasing the heat input and also to the reduced thickness of the upper sheet underneath the shoulder. Ohashi et al. [52] and Xie et al. [53] reported that the mechanical properties of the FSSW joints are mainly governed by both the weld bonded area and the upper sheet underneath the shoulder. In addition, the precipitate-free zones around the grain boundaries due to precipitate coarsening might have reduced the strength of the SZ [36]. From Figure 15, it can be also seen that all the RFSSW lap joints show higher tensile shear loads than that given by the FSSW (unrefilled FSSW) lap joints. The RFSSW joint (welded at 600 rpm/3 s and refilled at 400 rpm/1 mm/min) shows the highest tensile shear load of 5400 N ±100. Its enhancement in the tensile shear load is 25% over that recorded by the unrefilled spot joint. The two sheets of the RFSSW joint are still connected after the tensile shear testing, as given in Figure 16d-f. Furthermore, the other refilled joints show enhancements of 45%, 73%, and 273% over the unrefilled joints processed at 400, 800, and 1000 rpm, respectively. This enhancement for all the refilled joints is ascribed to the repairing of the keyhole defect by depositing high-strength AA 2011-T6 Al alloy via FSD and the strong bonding between the filling deposited material and the key hole interface, in addition to the microstructure features of the filling cavity of the keyhole. Both the deposition process and the good bonding between the keyhole interface and the FSD material filling the cavity are achieved in a solid-state process. Figure 17 displays the separated tested FSSW and RFSSW lap joint after the tensile shear test. in a solid-state process. Figure 17 displays the separated tested FSSW and RFSSW lap joint after the tensile shear test. Figure 16. Top, side, and bottom photographs show the joint appearance of the AA6082-T6 dissimilar sheet thickness welded at 600 rpm and 3 s after tensile testing, where (a-c) the FSSW joint [36] and (d-f) the RFSSW joint are refilled with AA2011-T6 at 400 rpm and 1 mm/min. Figure 17. Photographs of the joints after tensile shear testing for (a) the FSSW lap joints welded at a dwell time of 3 s and rotation speeds of 400, 800, and 1000 rpm [36] and (b) the RFSSW joints Figure 16. Top, side, and bottom photographs show the joint appearance of the AA6082-T6 dissimilar sheet thickness welded at 600 rpm and 3 s after tensile testing, where (a-c) the FSSW joint [36] and (d-f) the RFSSW joint are refilled with AA2011-T6 at 400 rpm and 1 mm/min. in a solid-state process. Figure 17 displays the separated tested FSSW and RFSSW lap joint after the tensile shear test. Figure 16. Top, side, and bottom photographs show the joint appearance of the AA6082-T6 dissimilar sheet thickness welded at 600 rpm and 3 s after tensile testing, where (a-c) the FSSW joint [36] and (d-f) the RFSSW joint are refilled with AA2011-T6 at 400 rpm and 1 mm/min. Figure 17. Photographs of the joints after tensile shear testing for (a) the FSSW lap joints welded at a dwell time of 3 s and rotation speeds of 400, 800, and 1000 rpm [36] and (b) the RFSSW joints Figure 17. Photographs of the joints after tensile shear testing for (a) the FSSW lap joints welded at a dwell time of 3 s and rotation speeds of 400, 800, and 1000 rpm [36] and (b) the RFSSW joints welded at the same conditions and refilled at a 400 rpm AA2011-T6 consumable rod rotation speed and a 1 mm/min feed rate.
The fracture surfaces of the BMs after tensile testing are given in Figure 18. Two fracture modes in terms of ductile and brittle fractures are detected for both the 1 and 2 mm sheet thicknesses. The Al matrix shows a ductile fracture in terms of different shallow dimple sizes. While the (Fe, Mn) 3 SiAl l2 and Mg 2 Si coarse precipitates show a brittle fracture. Microvoids due to the pullout of the fragmented intermetallics are also noticed on the fracture surface of the two sheets. The dimple size is related to the initial grain structure of the two sheets' materials. ture of the two sheets' materials. Figure 19a illustrates a photograph of the top surface of the lower sheet of the AA6082-T6 FSSW joint welded at a constant dwell time of 3 s and a rotation speed of 400 rpm after tensile shear testing, and Figure 19b-d shows the SEM fracture surface at different magnifications. The spot weld joint is failed by a tensile shear mechanism. Under the tensile shear loading, the crack begins at the tip of the hook of the partially bonded region and propagates preferentially in a horizontal direction at the lap joint interface, shearing the SZ, causing failure. The fracture surface of the failed region shows a typically ductile mode fracture in terms of different sizes of equiaxed deep dimples ( Figure 19d) compared with shallow elongated dimples of the fracture surface of both BMs (Figure 18), indicating the grain refining of the SZ during the FSSW process. Shear cleavage is observed, indicating the direction of the tensile shear mechanism.   Figure 20b,c shows the SEM fracture surface at different magnifications. The refilled joint is failed also by the tensile shear mechanism. Under the tensile shear loading, the crack begins at the tip of the hook of the partially bonded region and propagates at the lap joint interface, shearing the SZ of the welded area and the deposited refilled material, causing failure. The fracture surface of the failed material shows two distinct regions (AA6082-T6 weld sheets and AA2011-T6 deposited material) having a well-bonded interface (Figure 20b). The refilled joint reveals ductile fractures in both regions as they have equiaxed fine grain structures due to the stirring action in both the weld region and the refilled keyhole (Figure 20b).   (Figure 18), indicating the grain refining of the SZ during the FSSW process. Shear cleavage is observed, indicating the direction of the tensile shear mechanism. Figure 20a shows a photograph of the top surface of the lower sheet of the AA6082-T6 RFSSW joint (spot welding conditions of 400 rpm and 3 s and refilled conditions of 400 rpm and 1 mm/min) after tensile shear testing. Figure 20b,c shows the SEM fracture surface at different magnifications. The refilled joint is failed also by the tensile shear mechanism. Under the tensile shear loading, the crack begins at the tip of the hook of the partially bonded region and propagates at the lap joint interface, shearing the SZ of the welded area and the deposited refilled material, causing failure. The fracture surface of the failed material shows two distinct regions (AA6082-T6 weld sheets and AA2011-T6 deposited material) having a well-bonded interface (Figure 20b). The refilled joint reveals ductile fractures in both regions as they have equiaxed fine grain structures due to the stirring action in both the weld region and the refilled keyhole (Figure 20b).

Conclusions
In this study, an innovative technique was developed based on the friction stir deposition and examined to refill the keyhole of the FSSWed aluminum samples. A comparative investigation and evaluation were carried out between the unrefilled FSSWed and RFSSWed samples. Based on that, the following conclusions can be outlined: 1.
The applied FSSW parameters in terms of different rotational speeds of 400 to 1000 rpm and a constant dwell time of 3 s succeeded in spot-welding two different thin sheet thicknesses of AA6082-T6.

2.
The applied FSD parameters in terms of a feed rate of 1 mm/min and an AA2011-T6 consumable rod rotational speed of 400 rpm succeeded in refilling FSSW keyholes and shoulder projections of all the produced AA6082-T6 FSSW lap joints with defect-free continuous multilayers.

3.
All the RFSSW joints show higher bearing tensile shear loads than that given by the as-FSSWed joints.

4.
Among all the RFSSW joints, the RFSSW joint (welded at 600 rpm/3 s and refilled at 400 rpm/1 mm/min) promotes the highest tensile shear load of 5400 N ± 100. Meanwhile, among all the FSSW joints, the FSSW joint (welded at 600 rpm/3 s) gives the highest tensile shear load of 4300 N ± 80. 5.
The suggested FSD technique, including the consumable tool design and the FSD parameters, open new horizons for repairing the FSSW keyhole defect for different welded joints. Data Availability Statement: Data will be available upon request through the corresponding author.