**1. Introduction**

AA5754 and AA5083 are aluminum magnesium alloys, and their most prominent features are the high corrosion resistance and good formability. Thus, they have been extensively used in pressure vessels, tanks, trucks and shipbuilding [1,2]. AA7020 is a precipitation-hardened aluminum alloy, demonstrating high strength per weight ratio [3]. The use of the dissimilar alloys leads to the sustainable advantages such as overall cost reduction and hybrid properties that are available in the two different alloys. Appropriate joining process and its parameters optimization plays a vital role in the service performance of these alloys. Challenges like solidification cracking, porosity, intermetallic formation and so on are present due to the difference in the chemical and physical properties of the dissimilar alloy's combinations. Recently, the friction stir welding (FSW) of dissimilar

**Citation:** Ahmed, M.M.Z.; Ataya, S.; El-Sayed Seleman, M.M.; Mahdy, A.M.A.; Alsaleh, N.A.; Ahmed, E. Heat Input and Mechanical Properties Investigation of Friction Stir Welded AA5083/AA5754 and AA5083/AA7020. *Metals* **2021**, *11*, 68. https://doi.org/10.3390/met1101 0068

Received: 12 December 2020 Accepted: 26 December 2020 Published: 31 December 2020

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aluminum alloys combinations has been studied extensively, which proved the potential of the process to join these alloy combinations [4–6]. However, improper FSW parameters give rise to the formation of intermetallic compounds and internal and external defects (e.g., tunnel formation, voids, surface grooves and flash) [6–10]. Therefore, the investigation of FSW parameters is very important for obtaining defect-free joints with good mechanical properties. The placement of the higher strength aluminum alloys at the advancing side (AS) or at the retreating side (RS) affects material flow as it strongly influences material the stirring and flow behavior [10,11]. This can be a crucial parameter affecting the final joint microstructure, particularly when the selected combinations of base material (BM) have significant differences in their mechanical properties, microstructure and texture [4,12–16]. Some researchers studied the effect of the placement of BM on the material flow and the resulting FSWed microstructure and the mechanical properties [17,18]. Palanivel et al. [15] revealed that the tool rotational rate and tool pin profiles affected the AA5083- H111/AA6351-T6 joint strength because of the loss of cold work in the heat affected zone (HAZ) of AA5083 side, dissolution and over-aging of precipitates of AA6351 side and macroscopic defects formation in the weld zone. Jannet and Mathews [17] concluded that the AA6061 T6/AA5083 O joints fabricated at tool rotational rate of 900 rpm yielded a higher tensile strength than those fabricated at 750 rpm contributed by the thorough plastic flow and dissolving of dissimilar alloys and due to reduction in heat generated from plastic flow of the metal at 750 rpm. Park et al. [18] showed that the materials were more properly mixed when the AA5052-H32 was in the AS and the AA6061-T6 was in the RS than the reverse case on RS. Leitao et al. [19] reported that the global mechanical behavior of the AA6016-T4/AA5182-H111 welds was a 10–20% strength reduction relative to the base materials and important losses in ductility. Khanna et al. [20] concluded that softer alloy should be placed on AS with tool offset towards it for better FSWed AA6061- T6/AA 8011-H14 qualities. Kailainathan et al. [16] showed that the tensile strength of the 6-mm-thick AA6063/AA8011 joints was increased with the increase in the tool rotational speed due to the uniform temperature distribution at the weld region. However, beyond 1200 rpm, an adverse effect was noticed due to the distortion in the weld region. Abd Elnabi et al. [21] reported that the traverse speed has the highest contribution to the process for ultimate tensile strength of AA5454/AA7075 joints. Cole et al. [22] estimated that the AA6061/AA7075 joint strength was improved with decreasing the power input to the weld because of the sensitivity of alloy to heat input and weld temperature. The work of Ouyang and Kovacevic [23] suggested that the lower-strength alloy should be placed on AS for obtaining a better weld quality. Gerard and Ehrstrom [24] mentioned that the material with the higher solidus temperature should be on the AS not only for joint quality improvement but also for internal defects/porosity elimination. Guo et al. [25] revealed that the material mixing is much more effective when AA6061 alloy was located on the AS for AA6061/AA7075 joints. The ultimate tensile strength of the joints increases with the decrease of the heat input induced by friction. Kim et al. [26] demonstrated that excessive agglomerations and defects generated by joints when the high strength Al alloy on the AS of AA5052/AA5J32 are placed due to limited flow of material. Lee et al. [27] concluded that the mechanical properties of the stir zone showed higher values when AA6061 were positioned at the RS due to the complex microstructure of the stir zone. On the other hand, Jonckheere et al. [28] showed that material flow and joint quality are more dependent on the FSW conditions and their effects on heat input and temperature distribution in weld nugget, regardless of BM placement. Due to the material plastic flow during FSW, the heat generation is controlled by tool rotation and welding speed [29–31]. However, very high rotation speeds lead to macroscopic defects because of the excessive heat input [1,32–34]. To the author's knowledge, the FSW of AA5083/AA5754 and AA5083/AA7020 have not been reported in the open literature. The present work focuses on the influences of FSW parameters more deeply including the traverse speeds (20–80 mm/min) and AS/RS positions of base materials on the quality and the mechanical properties of the dissimilar AA5083/AA5754 and AA5083/AA7020 joints.
