Mechanical Strengthening of Lightweight Aluminium Alloys through Friction Stir Process

Yogesh, P.; Shinde, Santaji Krishna; C, Shyamlal.; Suresh kumar, R.; Rinawa, Moti Lal; Puthilibai, G.; Sudhakar, M.; Negash, Kassu; S, Rajesh

doi:https://doi.org/10.1155/2022/8907250

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Volume 2022 | Article ID 8907250 | https://doi.org/10.1155/2022/8907250

Mechanical Strengthening of Lightweight Aluminium Alloys through Friction Stir Process

P. Yogesh,¹Santaji Krishna Shinde,²Shyamlal. C,³R. Suresh kumar,⁴Moti Lal Rinawa,⁵G. Puthilibai,⁶M. Sudhakar,⁷Kassu Negash,⁸and Rajesh S⁹

Academic Editor: Chang Chuan Lee

Received11 Dec 2021

Revised23 Feb 2022

Accepted17 Mar 2022

Published06 Apr 2022

Abstract

The aerospace industries are focused on lightweighting with alloys having good tensile strength, fracture toughness, fatigue resistance, and corrosion resistance. The friction stir welding technology is one of the productive techniques in the aerospace industry to join such alloys with little ease. This paper deals with the composition of alloying elements that makes the structure lightweight and the impact of the precipitates evolved out of the selected alloying elements on the mechanical properties such as tensile strength and hardness of the joint in the aerospace alloys such as AA2xxx conventional aluminium alloys, AA2xxx lithium-based aluminium alloys, and AA7xxx aluminium alloys.

1. Introduction

The effective use of friction stir welding (FSW) technology, which is invented by TWI (The Welding Institute) [1–6], in the aerospace structures reduced the million number of rivets used in the aerospace structures that resulted in better joint tightness and reduced vibration along with reduction of several kilograms of weight. In addition to the above, by providing a leak proof joint, this welding technique improves the mechanical properties of the end product. The finer grains produced by FSW technique withstands heavy impact and is tough enough to handle heavy loads (very useful for ballistic applications). The welding parameters such as rotation speed (N) (heating effect), traversing speed (V) (cooling effect), the distribution of coherent precipitates (including sheared precipitates), and wt.% of alloying elements play a major role in deciding the hardness and tensile strength in the weld joint. In FSW, strengthening mechanism can be divided as precipitation strengthening (more pronounced in base metal (BM)), solid solution strengthening, dislocation strengthening, and fine grain strengthening (particularly in stir zone (SZ)).

However, the precipitate formation, temper selected, and dislocation hindrance are considered to be the major mechanisms to increase the strength of the joint and base material. At the outset, the equiaxed grains in the stir zone (SZ) impedes more dislocations by the increased grain boundary area. Hence, the synergetic effect of precipitate formation (less influence) [7] and equiaxed grains (more grain boundary area and higher influence) in the stir zone and thermo-mechanically affected zone make FSW joint efficiency superior than fusion welding and other allied welding processes. FSW joint efficiency is defined by the hardness in the weakest area of the weld commonly referred as low hardness distribution region (LHDR). The LHDR may be either in the heat affected zone (HAZ) (W hardness distribution), at the interface between HAZ and thermo-mechanically affected zone (TMAZ) (W hardness distribution), or even at stir zone (V hardness distribution), as discussed by Mishra et al. [8]. The LHDR is decided by the density of precipitates and the density of dislocations and the heterogeneous nucleation of precipitates in the dislocations. Hence, the precipitates and dislocations play a major role in increasing the hardness of the structure [9, 10]. When the speed is increased, from low rpm to high rpm, the precipitates grow, which led to its dissolution in the stir zone that in turn leads to decreasing trend in the hardness in the stir zone [11]. Further, Yadav et al. [12] discussed about the rotational speed of the tool. It was observed that the disappearance of hard precipitates during friction stir welding in the stir zone and reappearance of the hardened precipitate (Al-Cu) in the stir zone after PWHT while welding AA2024 - T3. The disappearance of the precipitate is due to the higher rotational speed of the tool. The reformation of precipitates is also influenced by the alloying elements present, the aging time, and temperature. The base metal mechanical properties (tensile strength, hardness, fracture toughness, fatigue resistance) are considered as the important parameters for end use.

Furthermore, the addition of alloying elements enhances the strength, corrosion, and ductility of the parent metal. For example, the addition of lithium to aluminium enhances the elastic modulus of the material and also decreased the density of the metal, which is used in aerospace application. A minor addition of scandium (Sc) resulted in major increase in the strength of the order of 50 to 100 MPa per 0.1 wt. % due to Al₃Sc dispersoids as told by Sauvage et al. [13]. The addition of scandium in the aluminium matrix restricts the grain growth and stops the movement of grain boundary. In addition to that, vacancies play a crucial role in developing and maintaining the strength of the metal. The vacancies are responsible for the enhanced diffusion of atoms of alloying elements. For example, face-centered cubic structure (FCC) has more vacancy creating structure than body-centered cubic structure (BCC). Hence, the solute atoms will be absorbed more easily in FCC than in BCC. During rotation of the tool, in the case of AA2024 alloy where Cu is more (up to 4.5%), a large number of precipitates will be broken up (more intermetallic Al₂Cu–BCT structure) and block the movement of dislocations, which increase the hardness and tensile strength of the workpiece. Conversely, the coarsening of the precipitates may induce ductility of the joint in some cases. Hence, the shape of the precipitates and its density influence the hardness of the joint. The needle-shaped precipitates are coherent with matrix than rod-shaped precipitates. Hence, mechanical properties depend on the density of the needle-shaped precipitates as told by Sato et al. (AA6063-T5) [14]. Moreover, the temper of the material also increases the base metal hardness. When the base metal has more hardness, eventually, the joint also exhibits better efficiency. The tool breaks the precipitates and nucleates more precipitates, which act as barriers for dislocation motion thereby increasing the hardness and tensile strength. Further, if the difference between ultimate tensile strength and yield strength value is more for an alloy, then it can be said that the crack tolerance will be good for the particular structure. Initially, this technology was adopted to weld light metals such as monolithic aluminium and magnesium alloys. But after the invention of Al-Li alloy series, this technology has been adopted as a unique technique for joining aerospace alloys. Also, aluminium alloys are considered as the chief alternative [15] to steel in automobile industries because of its better specific strength, better specific stiffness, and its better corrosion resistance [16, 17]. Moreover, the low density of aluminium alloys makes it the suitable candidate for designing complex products than steel allowing better design freedom and also allows designers to build structures with more thickness (more safety in case of accidents in automobiles than steels due to excellent ductility). The addition of aluminium alloy in the aerospace industry leads to the reduction in emission by reducing the weight of the airplane. Particularly, the lithium-based aluminium alloys are the preferable candidate alloy for the above purpose of lightweighting. The lithium-based aluminium alloys have been invented to replace the AA7xxx and AA2xxx aluminium alloys to offer more strength, stiffness, and elongation than conventional aluminium alloys. But there exists a disadvantage in lithium-based aluminium alloys that is anisotropy behavior and the formation of coherent but shearable Al₃Li precipitate. In order to mitigate this effect, Cu and Mg are added in these alloys for the formation of precipitates such as Al₂CuLi and Al₂CuMg. These precipitates increase the hardness, tensile strength, and fracture toughness of the aerospace structure (for example, cryogenic fuel tank in rockets) but with reduced density to achieve better specific stiffness. These lithium-based aluminium alloys are used as the replacement of AA2024 and AA7075 alloy in the aerospace industry.

This paper deals with the tensile strength and hardness of the lightweight aerospace alloys such as AA2050, AA2060, AA2198, AA7475, AA7050, AA7055, AA2024, and AA7075. The aforementioned properties are essential for aerospace alloys to prevent crack propagation in higher altitudes.

2. Types of Precipitation Hardening Aluminium Alloys and Their Tempers

2.1. Types of Precipitation Hardening Aluminium Alloys and Their Precipitates

This subsection deals with types of precipitation hardening aluminium alloys. Generally, the temper designation refers to the degree of hardness of the aluminium alloy material. The aging time also influences the hardness of the aluminium alloys. The aluminium alloys that belong to the above category are AA2xxx, AA6xxx, and AA7xxx alloys. In AA2xxx alloys, the major alloying element is copper (Cu), which increases the tensile strength of the component but retard corrosion resistance; Li is another alloying element that forms the precipitate Al₃Li (a coherent precipitate); it also forms other type of precipitates with Cu and Mg such as Al₂CuLi and Al₂CuMg to enhance tensile strength and increase elongation. In AA6xxx alloys, the major alloying elements are magnesium and silicon (Mg and Si). The Mg adds strengthening effect to the alloy; it also increases micro hardness of the alloy due to HCP crystal structure and Si induces fluidity for the alloy. The precipitate formed by Mg and Si is -Mg₂Si having FCC crystal structure. In AA7xxx alloys, the major alloying elements are magnesium and zinc (Mg and Zn). The precipitate formed between Mg and Zn is MgZn₂ (magnesium di zinc) and Al₃Zr (a dispersoid) having HCP crystal structure (6 atoms per unit cell), which impart better hardness than FCC structure (4 atoms per unit cell). In all the above-said alloys, Fe is an insoluble impurity that must be controlled to avoid brittle fracture, which initiates in the grain boundary.

2.2. Temper Designations Applicable for Aerospace Alloys

This subsection analyses the temper designations applicable for aerospace alloys. During solutionizing, single solid solution comprising primarily aluminium and solute forms either as substitutional or interstitial in solution state. After solutionizing, the metal will be quenched to a room temperature. When the solvus line is touched in the phase diagram and during aging much below the solvus line, guinier preston zones are generated. At this stage, vacancies created above the solvus line will be supersaturated in room temperature. The aging performed after quenching accelerates the diffusion of atoms in the generated vacancies and vacancy loops to produce strong and ductile structure. Moreover, the tensile strength and hardness of the base metal for the joint will change based on the temper as discussed by Chen et al. [18]. The selection of the temper is based on the application of the material. For example, A class surfaces can be produced in automobiles using the aluminium alloy having T651 temper and for better corrosion resistance, peak-aged temper (T7, T87) will be chosen. The following subsection deals with the types of tempers used in industries.

2.2.1. Underaging Tempers

T3. Solution heat treatment, cold work, and natural aging. It is used for the aerospace alloy AA2024. T6. The O tempered aluminium billet is heated to about 990˚F and then quenched in water followed by aging at about 350˚F for around 8 hours. This temper will increase the yield strength of the base material. This temper is used with AA6061 aluminium alloy. This temper designation is for artificial aging. This temper can be used to achieve better flatness. Solution is heat treated and artificially aged to attain maximum strength. T651. In this temper along with T6 treatment, 1% to 3% straightening is done to relieve the residual stresses and to increase the dislocations. This temper is a very stable temper.

2.2.2. Peak-Aging Tempers

T7. Better crash resistance. Slightly decreased strength and improved ductility. This temper is used to achieve better dimensional stability. But this temper will consume other small precipitates leading to decrease in strength of the alloy. This temper also increases corrosion resistance but degrade mechanical properties as suggested by Pagalia et al. [19]. T7451. This temper is used along with AA7050 for aerospace applications. It combines high strength with good exfoliation corrosion resistance and average stress corrosion cracking resistance. T76. It provides highest strength with exfoliation corrosion resistance and stress corrosion cracking resistance. T7651. It provides better exfoliation corrosion resistance and stress corrosion resistance with average strength. T8. Solution heat treated, cold worked, then artificially aged. The cold working increases the number of dislocations that aid for heterogeneous nucleation of precipitates and hence better mechanical properties will be obtained. This temper is used for AA2050 and AA2060 aluminium lithium alloy. T87. This is one of the standard temper for AA8090 alloy, 7% cold work (by rolling and stretching) with age hardening to increase the dislocations and to produce flatness. Solution treatment with water quenching, 7% cold work and peak aging. This temper is used for AA8090 aluminium lithium alloy.

3. Overview of Precipitation

Generally, the precipitate evolution is the desirable phenomenon in aluminium alloys. Precipitation is favored by the process of artificial aging. In precipitation hardening alloys, the precipitation sequence occurs as ϴ” (GP zones-coherent) ⟶ ϴ’ (semicoherent) ⟶ ϴ (stable precipitate) ⟶ precipitate coarsening (over-aging) [20–22]. ϴ’’ are the cluster of precipitates of few tens of nm size, ϴ′ are the precipitates of few hundreds of nm size (larger size than ϴ”) and ϴ is the stable size of the precipitate (larger than previous two versions of precipitates) and beyond the stable size, more precipitate coarsening (phenomenon of overaging) occurs which led to the decrease in hardness in the stir zone (SZ) when the temperature favors for the growth of the precipitate. The precipitates are of three type’s, namely, Coherent, semi coherent and incoherent. During the formation of precipitate, coherency with a solution (aluminium and solute component) is very important. The coherent precipitate will slowly change to semi-coherent precipitate when the precipitate grows (lessening of fine precipitates start). The coherent precipitate (quasi-unstable) will have higher strain energy. In the stage of semi coherency, the dislocation will start to form when the temperature is further increased, the semi coherent precipitate (metastable) changes to very few large incoherent precipitate (stable). The incoherent precipitate is defined as stable precipitate [23] due to the extra ordinary growth which will consume small finer precipitate as suggested by Anderson et al. [24]. During the transition from coherent to incoherent precipitation, the maximum hardness and tensile strength will be attained. Hence, more number of coherent and incoherent precipitate induces better hardness than incoherent precipitate. The precipitate is grown to the specified size and composition (morphology).

If the precipitate is larger, the dislocation adopts the looping mechanism (Orowan strengthening mechanism) [25, 26] to by-pass large precipitate. The hardness will be better in the stage of coherency. There is a relation between precipitates and dislocation initiation. The semi coherent precipitates introduce dislocation in the matrix due to elastic straining around the precipitate (solute). Grain boundaries also play a significant role in increasing the strength of the alloy. When the grain boundary restricts the movement of dislocations, it increases the strength of the structure. If the dislocations are introduced in the grain boundary (heterogeneous nucleation), the yield strength decreases. There is also a possibility of precipitate-free zones (PFZ’s) near the grain boundary where hardness is very lesser. The PFZ is created due to the large size of precipitates consuming equi-axed or small precipitates near grain boundary making the vicinity of grain boundary completely free of precipitates. The hardness is a main concern when dislocations nucleate at precipitate free zone (PFZ). This will decrease the yield strength makes the area prone to failure as discussed by Thorsten Krol et al. [27]. Liu et al. [28] detailed about the formation of different size of precipitates and its influence on hardness and microstructure. It is told that the base metal and heat affected zone (HAZ) has similar density of dislocations. After the workpiece is placed in welding fixture, there will be no cold work or plastic deformation takes place in the base metal and in the HAZ. The deformation takes place only in the stir zone creating more number of equi-axed grains thereby enhancing the strength of the joint. But, HAZ receives strength only from solution treatment and aging. Hence, it is told that stir zone exhibits higher hardness than HAZ [29–31].

It is also understood that whenever the tool rotation speed increases, the precipitate size is increased due to the change of coherent to stable precipitate. The stable precipitate has little influence in increasing the hardness in the joint and elsewhere in the workpiece. The coherency will be lost when precipitates begin to grow due to temperature increase. In the stir zone, more temperature is created near to solidus temperature. Hence, more number of undissolved precipitates will reappear in the stir zone.

3.1. Possible Combination of Precipitates

The major alloying elements added in the aluminium series are copper (Cu), magnesium (Mg), manganese (Mn), silicon (Si), zinc (Zn), titanium (Ti), and lithium (Li) (aerospace). In general, the precipitates formed are Al₂Cu (a precipitate of aluminium and copper but rich in aluminium in the aluminium side of binary phase diagram-FCC structure), Mg₂Si (magnesium silicide rich in magnesium), and MgZn₂ (di zinc magnesium rich in Zn-HCP structure). Zn and Cu are added to aluminium alloys to increase the strength along with Al, but it will reduce the ductility. Si (an impurity) is added to the alloy to increase the fluidity of the alloy. Si with Mg produces the intermetallic compound that has better mechanical properties. Ti is added to the alloy as the grain refiner. Zr is added to the alloy to produce fine precipitates and forms precipitate with aluminium-Al₃Zr, which has the role of restricting the movement of grain boundary. Fe and Si are impurities in the alloy. Ni is added to enhance the high temperature strength. Li is added to the alloy to enhance the ductility (through modulus of elasticity) and to reduce the density of the alloy. As lithium is expensive than other alloying elements, it is extensively used only in aerospace applications. The main aim of adding Li is to reduce the density of aluminium making the aircraft fuel efficient [32]. The final aim of the heat treatment procedure (artificial aging) that starts from the base metal temper to postweld heat treatment (PWHT) of FSWed alloy is to achieve fine precipitates to attain sufficient tensile strength to resist deformation and fracture in the stir zone and in other zones of the weld.

3.2. Morphology of Precipitates

The precipitates take the shape of sphere (coherent precipitate) to plate and disc morphology (semi-coherent/incoherent precipitate). The spherical GP zones (precipitate zones) will be formed, whenever the atom size between the matrix and solute is the same. The GP zones will deviate from the spherical shape (disk shape) when the atoms of matrix and solute are of different sizes [33]. The shape of the precipitates is governed by Gibb’s free energy, G, and is given asHere, P = pressure, bar, and V = volume, m³.

In precipitation, after FSW internal energy, U (may be responsible for internal stress generation) dominates the enthalpy, H. Hence, Gibb’s free energy is directly proportional to internal energy. The term TS (combined effect of temperature, T and entropy, S) can be neglected as friction stir welding is a solid state welding process (disorderliness of atoms is lesser). Hence, Gibbs free energy equals internal energy. When atoms start to vibrate, it expands the grain boundary. Lowest free energy (∆G < 0) is the state of thermal equilibrium that leads to in-coherency [34] in precipitation development. The spontaneous reaction (natural reaction) takes place from coherent to incoherent phase. Many elements inside the alloy show metastable (semi-coherent) phases that are compounds formed along with the matrix (Al) and also with other alloying elements being added.

Generally, it is assumed that the matrix phase is infinite phase and the precipitate phase is finite phase. The basic concept behind the changing shape of precipitates is the agglomeration (accumulation) of solute atoms (Figures 1 and 2) in the combined form. Initially, the precipitate will be in the form of a sphere. When the solute atoms start to accumulate, then the shape changes to disc and plate shape thereby becoming incoherent having lowest strain energy up on experiencing heat. The morphology of the precipitate changes from sphere to plates or disks depends on the temperature involved. The sphere morphology [10, 35, 36] (GP zones at room temperature) is an unstable morphology. Hence, the precipitate grows until it attains stable morphology (lower strain energy). The precipitates also nucleate and grow when the dislocations shear the precipitate.

4. Influence of Chemical Composition on the Precipitate Formation and Its Effect on Mechanical Properties

Figure 3 and Table 1 present the chemical composition of alloys that is recommended for lightweight applications in aerospace industry such as AA2024, AA2060, and AA7075. From the above table, it can be clearly seen that Cu, Mg, Zn, and Li have more wt. % elements. In the above-mentioned alloys, the Li-based aluminium alloy has been invented to replace the conventionally used AA2xxx and AA7xxx series alloys. Cu and Mg are intentionally added to Li-based alloys to the formation of S phase (Al₂CuMg) and T1 phase (Al₂CuLi). These element additions will reduce the anisotropy and increases the elongation of the alloy and also impart better properties. Compared to a conventional alloy, every 1% lithium presence increases the elastic modulus by 3%, while decreasing the density by 6%. It is a quaternary alloy capable of ensuring, in addition to the aforesaid form and density effects, a high response to aging treatment, thanks to the formation of the metastable phase δ’ (Al₃Li) coherent with the matrix and other magnesium and copper phases. Zirconium presence allows it to control the grain structure and also plays a beneficial nucleating effect on the δ′ particles.

Hence, the intermetallic precipitates will be more involving Cu, Mg, Zn, and Li. In Li-based alloys to impart ductility to the alloy, which is clearly indicated in Cu/Li ratio. Also Mg is intentionally added to other alloys as an alloying element to increase the hardness of the alloy, since it has HCP structure. In the above-mentioned alloys, Cu dominates Mg except for AA7xxx series where Mg dominates Cu, which is clearly indicated in the above table. Cu is added to aluminium alloy to increase tensile strength by forming precipitates such as Al₂Cu, Al2CuLi, and Al2CuMg, which will precipitate up on reaching the solvus line in the Al-Cu phase diagram and fatigue strength to AA2xxx alloy and Zn is added to AA7xxx alloys along with magnesium and copper to form MgZn₂ precipitate. Generally, Zn, Cu, and Mg are added to influence natural aging and artificial aging. In AA2060 alloy, Zr (0.1%) is intentionally added to increase the dispersoids (Al₃Zr), which will strengthen the grain boundary and to inhibit recrystallization as told by Xie et al. [45]. In all the above-mentioned compositions, Ti (trace element) was added to intentionally control the grain size (to approach finer size) by forming Al₃Ti compound. Hence, the precipitates involving Zn, Cu, Mg, and Li content will appear as the precipitate after aging treatment as mentioned in Figure 3.

In Figure 4, two types of temper are presented, namely, T6-underaged temper and T7 and T8-peak-aged temper. Both types of temper are used in aerospace industries. It is observed that the strength of 2024 is lesser than 7075. In 7075, MgZn₂ exhibits HCP structure (fewer slip systems), but in 2024, Al₂Cu exhibits FCC structure (Figure 5) (more slip systems). In HCP structure, deformation takes place by twinning that makes the material stronger than AA2xxx category. In AA7075, in addition to Cu, Zn is also present that also contribute to increase in the strength of the alloy as told by Ipekoglu et al. [46] Further, Zinc dissolves more in aluminium during solution stage and make the material stronger that reappear at room temperature creating more number of precipitates, which makes the material suitable for high-temperature applications.

From Figure 6, it is ascertained that Cu content in AA2024 aluminium alloy produces higher tensile strength and hence hardness. The coarse precipitates in AA7075 with T7 temper and in AA2024 with T8 temper produce lesser hardness than AA7075 with T6 temper due to the absence of solid solution hardening and the disappearance of precipitates. But, hardness can be recovered to some extent using PWHT as suggested by El. Danaf and El-Rayes [47].

Figure 7 indicates hardness of the FSW joint that is 140 VHN for AA7075 T7, which is 87.5% of the base metal hardness [19], and 123 VHN for AA7075 T6 [48], which is 68.33% of the base metal hardness. The reason for the decrease in hardness in AA7075 T6 compared to the base metal is due to the presence of dynamic recrystallization [49–52] in the stir zone that might have fragmented [53] many incoherent precipitates to coherent precipitate that allow more dislocation to pass through and also reduces dislocation density.

Figure 8 displays the base metal with tempers. In the peak-aged temper (T7, T8), the elongation at break increased compared to its underaged temper before processing in friction stir welding due to more number of coarsened stable precipitates. As coarsening of precipitates induces ductility, elongation at break % is higher for peak-aged tempers but can be reduced by PWHT (postweld heat treatment) as suggested by Sivaraj et al. [54].

Cabrini et al. [48] investigated the SEM of FSW joint and found that wt. % Zn (8.4%) is rich in pct, as compared to Cu and Mg due to the fact that Zn dissolves more in aluminium than other two elements mentioned above in the solutionizing stage. Hence, coherent MgZn₂ precipitate is developed inside the grain and in the grain boundaries due to dynamic recrystallization. When compared with base metal AA7075-T6 composition (Figure 1), Wt. % Zn 8.48 is in upper hand that introduces better strength to the joint. As seen from Figure 9, Zn has more atoms than Mg and Cu. Hence, the hardness value of 124 VHN compared to base metal hardness of 180 VHN as seen from Figure 7 is appreciable. This hardness is attained due to the precipitation of MgZn₂ and equi-axed fine grain structure after FSW in the weld joint. Hao et al. [55] discussed about the precipitation behavior of AA7075-T6 alloy with 6 mm thickness. It was found that the distribution of precipitates varied with rotational speed. It was found that the strengthening to the weld zone was provided by strain hardening effect and Cu-containing precipitate, which is in agreement with Behzadi et al. [56] and Xu et al. [57]. Furthermore, Hernandez et al. [58] discussed about the ratio of Cu and Mg in AA2024 alloy. Combined effects of chemical composition and plastic deformation influence strengthening behavior and precipitate mechanism. It was suggested that strength can be increased by solid solution, strain hardening, and precipitate hardening. Hardness is influenced mainly by precipitation formation but is modified by plastic deformation and Cu/Mg ratio.

5. Conclusions

In this work, mechanical properties such as tensile strength and hardness of the alloy in the context of alloying elements present in the alloy are covered in greater detail. The following observations were made:(i)The importance of alloying elements and its contribution in the precipitate formation that led to the improvement in mechanical properties has been discussed(ii)Mechanical properties such as tensile strength and hardness of the alloy have been discussed(iii)The significance of temper in improving the mechanical properties has also been discussed(iv)The effect of free energy of the system in the precipitate growth has been briefed(v)The contribution of welding parameters in improving the mechanical properties of the stir zone has been detailed

Abbreviations

U:	Internal energy, J
H:	Enthalpy, J/Kg
P:	Pressure, bar
V:	Volume, m³
T:	Temperature, deg. Celsius
S:	Entropy, J/K
GP:	Guinier preston zones
BCC:	Body-centered cubic structure
FCC:	Face-centered cubic structure
HCP:	Hexagonal close packed structure.

Data Availability

The data used to support the findings of this study are included in the article. Should further data or information be required, they will be available from the corresponding author upon request.

Disclosure

It was performed as a part of the Employment Hawassa University, Ethiopia.

Conflicts of Interest

The authors declare that there are no conflicts of interest regarding the publication of this paper.

Acknowledgments

The authors appreciate the technical assistance to complete this experimental work from Department of Mechanical Engineering, Sri Sai Ram Engineering College, Chennai 600100, Tamil Nadu, India.

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