Effect of friction stir welding (FSW) parameters on strain hardening behavior of pure copper joints
Highlights
► Strain hardening of friction stir welded (FSWed) copper joints were investigated. ► Base metal (BM) and FSWed samples exhibited stages III and IV of deformation. ► FSWed samples exhibited higher hardening capacity (Hc) relative to BM. ► FSWed samples exhibited lower strain hardening exponent (n∗) relative to BM. ► Increasing rotation rate or decreasing traverse speed led to higher Hc and lower n∗.
Introduction
Special features of copper such as high electrical and thermal conductivities, favorable combinations of strength and ductility, and excellent resistance to corrosion have made it an acceptable material for use in many industrial areas [1], [2], [3]. In contrast with its advantages, fusion welding of copper is difficult because of its high thermal diffusivity and high oxidation rate at melting temperature [4], [5]. One way to overcome these problems is friction stir welding (FSW). FSW is a solid state welding process in which a non-consumable welding tool is used to generate the frictional heat between the tool and the work piece in order to make a solid state joint [6]. While the research and applications of FSW have mainly focused on the aluminum alloys [7], [8], investigations into the FSW of copper and copper alloys is quite limited [9], [10], [11], [12]. This is attributed to the high heat input requirement during FSW of copper to achieve defect-free joints [6].
Xie et al. [11] investigated effect of tool rotation rate on microstructure and properties of friction stir welded (FSWed) copper joints under low heat input condition. They reported the grain size of the stirred zone (SZ) decreased from 9 to 3.5 μm with decreasing rotation rate from 800 to 400 rpm at constant traverse speed of 50 mm/min. They indicated that variations of both microhardness and yield strength of the SZ are related to grain size with the Hall–Petch relationship.
Shen et al. [12] investigated effect of traverse speed on the microstructure and hardness of FSWed copper at constant rotation rate of 600 rpm and traverse speed in the range of 25–150 mm/min. They reported that as the traverse speed increased, the grain size of SZ first increased and then decreased, the thermomechanically affected zone (TMAZ) became narrow and the boundary between these two zones got distinct; the heat affected zone (HAZ) was almost not changed. Hardness values of SZ were considerably lower than that of the base metal (BM) which can be related to the microstructural changes.
Along with the microstructure and mechanical properties, strain hardening behavior of the FSWed joints plays an important role in the material load bearing properties. Strain hardening is one of the most common methods to enhance the mechanical strength of materials through imposing plastic deformations. Additionally, some authors who investigated grain boundary strengthening of polycrystals showed that the major source of such strengthening was also due to the enhanced strain hardening [13]. Strain hardening behavior is greatly influenced by grain size and dislocation density [14], [15], [16]. Therefore, it can play an important role in determining of mechanical properties, due to sever plastic deformation in FSW process.
Afrin et al. [17] investigated strain hardening behavior of FSWed magnesium alloy using two modified equations of hardening capacity and strain hardening exponent where the elastic deformation stage was excluded. Kocks–Mecking type plots were used to show different stages of strain hardening. They reported that the hardening capacity and the strain hardening exponent of the FSWed samples were observed to be about respectively twice and threefold higher than those of the base alloy. They discussed the results by dislocation storage theory. Simar et al. [18] developed a mathematical model for predicting strain hardening of FSWed aluminum alloy 6005A-T6.
Although a few studies can be found in the literatures investigating the effects of FSW parameters on the strain hardening behavior of FSWed aluminum [18] and magnesium alloys [17], no efforts have been devoted to strain hardening behavior of FSWed copper joints. The lack of information in this field promoted the authors to investigate the subject. Therefore, the aim of this paper is to establish a relationship between FSW parameters (tool rotation rate and traverse speed) and strain hardening behavior of FSWed copper joints.
Section snippets
Experimental procedure
Commercial pure copper plate with a thickness of 5 mm was joined by FSW perpendicular to the rolling direction. Two traverse speeds of 25 and 75 mm/min at constant rotation rate of 600 rpm (R600T25 and R600T75 samples) and two rotation rates of 600 and 900 rpm at constant traverse speed of 75 mm/min (R600T75 and R900T75 samples) were conducted to study the effect of traverse speed and rotation rate, respectively. Microstructure features of the FSWed joints were characterized by optical microscopy.
Microstructure characterization
From previous literatures based on microstructural characterizations, four distinct zones, i.e., parent material (PM), SZ, TMAZ and HAZ, were usually identified in FSW joints [6], [20]. Xue et al. [21] investigated effect of heat input conditions on microstructure and mechanical properties of FSWed pure copper and observed the stated four zones at low heat input condition i.e., rotation speed of 400 rpm and traverse speed of 50 mm/min. Fig. 2 shows microstructure of sample R600T75 in which SZ,
Conclusion
In summary, it is declared that FSW parameters such as traverse speed and tool rotation rate affect strain hardening behavior of copper joints as well as microstructure and mechanical properties. FSWed samples have higher hardening capacity and lower strain hardening exponent relative to BM. Decreasing traverse speed and increasing tool rotation rate (increasing heat input to workpiece) results in reduction of dislocation density and grain growth in both of the SZ and HAZ. These all lead to
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