# Microstructural and Mechanical Characteristics of Pure-Cu/brass Dissimilar Joints Welded by Friction Stir Welding Using Various Process Parameters

Authors: Ramesh C; Mohammed Tharwan; P. Manoj Kumar; Dawit Tafesse Gebreyohannes
Journal: Advances in Materials Science and Engineering
 (2022)

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## Abstract

FSW (friction stir welding) is a solid-state joining method that attracts interest from all industries. The influence of various tool rotational speeds on the microstructure and mechanical characteristics of dissimilar pure Cu-brass joints has been investigated. The travel speed and vertical load were kept constant in the welding trials, at 40 mm/min and 10 kN, respectively, while the tool rotational speed varied from 1000 to 1400 rpm. The increase of the rotational speed to 1400 rpm resulted in degradation of the mechanical properties. The stir zone grain structure was refined; however, the grain size was irregular. Grain refining occurs due to a continuous and discontinuous dynamic recrystallization mechanism. In the grain interior, there were many large dislocations, identifying that incomplete recrystallization took part within the SZ. Instead, the lower rotational speed, i.e., 1000 rpm, led to more uniform grain refinement in the SZ. Moreover, in contrast to the welded zone where very fine grains exist, the base metal and thermomechanically heat-affected zone display coarser grains. Because of the microstructural modification, the stir zone’s mechanical characteristics were higher than the base materials, and the mechanical strength and plasticity were simultaneously upgraded. These results indicate that the size of the grains is independent of rotational speed. And mechanical properties like hardness and impact strength decreased as the rotational speed increased.


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## Body

## 1. Introduction

In earlier days, the FSW process was only used to join aluminium alloy materials for structural applications, and the FSWed joints of Al-alloys exhibited much better joint performance than the fusion welded joints [1]. Later it has been used to process materials like steels, nickel alloys [2–4], magnesium alloys [5, 6], titanium alloys [7, 8], aluminum alloys [9, 10], copper and copper alloys [11–14]. Among them, copper has superior properties like high thermal and electrical conductivity, ductility, and corrosion resistance [15–17]. Due to copper’s high oxidation and heat diffusivity, fusion welding high oxidation and heat diffusivity make fusion welding difficult [18, 19]. High heat input helps to reduce defeats in copper joining. To produce defect-free joints, high heat input is necessary during copper joining. Reference [20].An alloy of copper and zinc is called brass. Its high thermal and electrical conductivity, high strength, and corrosion resistance make it useful in different industries. It has various applications such as electrical, radiators, heat exchangers, and power plants. The copper melts at 1083/2590°C and the zinc at 419/907°C zinc [21, 22]. The results identify the existence of two different zones inside the SZ, one largely filled with Al2Cu intermetallic near the aluminium sheet and the other mostly filled with Al4Cu9 intermetallic near the brass sheet. FSW and the Taguchi approach were used to improve the process parameters and tool design [23]. In the conventional welding process, the electrode may reach 4200°C during joining, while the workpiece reaches 3200°C. When the process reaches its high melting point, materials such as zinc and copper evaporate. Hence, it is essential to apply a novel welding technique to overcome the difficulties. The FSW process has potential benefits in the evolution of the enhancement of microstructure and mechanical properties. The produced weld joint refined the grain size without any gas porosity. The weldments are characterized by four zones: (a) Heat Affected Zone (HAZ); (b) Material zone (base/parent/unaffected); (c) Weld or Stir Zone (WZ/SZ); and (d) Thermomechanical Affected Zone (TMAZ).The weldability study of copper alloys used in FSW is limited. The mechanical properties and microstructure of different rotating speeds were studied by several researchers. They concluded that the SZ's grain size was too small, based on optimizing rotational speeds. As mentioned above, usually the ultrafine grain structure of the welded joints has a high dislocation density. It shows that the various rotational speeds are achievable to obtain the high strength of Cu-Br weld joints. The microstructure examination was explored by optical microscope, electron backscatter diffraction, scanning electron microscope, as well as transmission electron microscopy in this investigation, in order to study the Cu-Br dissimilar joint made through the FSW process. Further, the mechanical properties have been investigated. In addition, the heat generation during Cu/Brass FSP was analyzed and process parameters on temperature distribution were also experimented with. To simulate the heat transfer of copper during FSP, a 3D, transient, non-linear thermal model with a moving heat source was developed using the ANSYS 11.0 software. To verify the accuracy of the computer simulation, results from numerical simulations are compared with experimental data.


## 2. Selection of Materials and Parameters

### 2.1. Material Selection

By joining dissimilar copper and bronze metals by friction stir welding, hybrid materials can be produced. Copper has a high thermal conductivity as well as a high electrical conductivity. The bronze plate is made of copper and zinc alloys and is easily formed. It has high strength, good electrical conductivity, and excellent forming and drawing characteristics. Fusion welding has some difficulties such as evaporation of zinc and welded metal having pores.


### 2.2. Composition of the Material

The following lists the composition of H13 tool steel, brass, and copper (Tables1 and 2).Table 1
Composition of H13 tool steel.
MaterialPercentage (%)Carbon0.33–0.46Chromium4.63–5.45Manganese0.30–0.65Molybdenum1.20–1.88Phosphorus0.45 max.Silicon0.80–1.20Sulphur0.03 max.Vanadium1.80–2.20Table 2
Cu and Br materials exhibit different chemical compositions.
MaterialZnSnPbFeSPAlNiTiCuCopper0.060.15........0.100.040.040.030.02BalanceBrass39.660.403.460.20............0.03....Balance


### 2.3. Process Parameters

The pressure, rotational, travel speed, tool design, and also the properties of the material being joined. Thus, all impacts of the microstructure of a welded joint performance are measured by the following parameters:(1)
Traverse speed(2)
The rotational speed of the tool(3)
Axial load(4)
The tilt angle of the tool


### 2.4. Design of the Tool

The tool's design has an important impact on the welded joint’s uniformity and heat generation. On the shoulder, a lot of heat is produced; the plasticized material cannot escape the workpiece. The shoulder and the tool–pin restrict the material flow and attain a hardness of 58HRC.


## 2.1. Material Selection

By joining dissimilar copper and bronze metals by friction stir welding, hybrid materials can be produced. Copper has a high thermal conductivity as well as a high electrical conductivity. The bronze plate is made of copper and zinc alloys and is easily formed. It has high strength, good electrical conductivity, and excellent forming and drawing characteristics. Fusion welding has some difficulties such as evaporation of zinc and welded metal having pores.


## 2.2. Composition of the Material

The following lists the composition of H13 tool steel, brass, and copper (Tables1 and 2).Table 1
Composition of H13 tool steel.
MaterialPercentage (%)Carbon0.33–0.46Chromium4.63–5.45Manganese0.30–0.65Molybdenum1.20–1.88Phosphorus0.45 max.Silicon0.80–1.20Sulphur0.03 max.Vanadium1.80–2.20Table 2
Cu and Br materials exhibit different chemical compositions.
MaterialZnSnPbFeSPAlNiTiCuCopper0.060.15........0.100.040.040.030.02BalanceBrass39.660.403.460.20............0.03....Balance


## 2.3. Process Parameters

The pressure, rotational, travel speed, tool design, and also the properties of the material being joined. Thus, all impacts of the microstructure of a welded joint performance are measured by the following parameters:(1)
Traverse speed(2)
The rotational speed of the tool(3)
Axial load(4)
The tilt angle of the tool


## 2.4. Design of the Tool

The tool's design has an important impact on the welded joint’s uniformity and heat generation. On the shoulder, a lot of heat is produced; the plasticized material cannot escape the workpiece. The shoulder and the tool–pin restrict the material flow and attain a hardness of 58HRC.


## 3. Experimental Procedure

For this work, 100 × 50 × 6 mm sizes of copper and brass materials were used. FSW was carried out on the Cu-Br butt joint in a dissimilar configuration by the FSW machine. The H13 tool steel is used with dimensions of ɸ24 mm shoulder diameter. The profile pin is straight cylindrical of 4.5 mm length as shown in (Figure1). The traverse and rotational speeds are the major process parameters for good weld quality. Tool geometry and different pin profiles creates impacts on the microstructure and mechanical characteristics of the weld joint. Compared with various pin profiles, the cylindrical pin profile was good in terms of the quality of the weld. Process parameters such as rotational speeds of 1000, 1200, and 1400 rpms, and 40 mm/min travel speed with a load of 10 kN were used. Experiments were conducted by keeping constant travel speed and axial load with varying rotational speeds.Figure 1
FSW H13 tool steel.For microstructural analyses, the samples were cut in a perpendicular direction after welding. The microstructural characterization sample prepared by the procedure of metallographic standard and etched using FeCl3 + HCl + H2O solution. The analysis was carried out on friction stir welded dissimilar joints using OM and SEM (Model: LEO 1450 VT) observations. EBSD was used in combination with a field emission scanning electron microscope (FESEM) to characterize the base material and SZ microstructure. The electropolishing EBSD sample preparation was done with 250 ml H3PO4 solution, 250 ml ethanol, and 500 ml distilled water with 20 V applied at −30°C for one minute. The 200 nm scanning step was selected for the EBSD. While evaluating the EBSD data mis-orientation angle, the cut-off angle was 2°. The welded structures were described by TEM with an accelerating voltage of 200 kV. Samples for TEM made by (∼50) mm electropolishing was repeated on thin polished samples at −30°C and 10 V. A hardness value was measured in the welded area of the samples using a Wolpert microhardness tester at 10 grams to 1 Kg Load. The impact tests were carried out in conformity with ASTM E 23-02a. Tensile testing is carried out by a universal tensile testing machine (ZWICK 250 kN) to ASTM E 8 M-98 standards.


## 4. Results and Discussion

Friction stir welded samples were evidenced at several rotational speeds of (a) 1000 rpm (b) 1200 rpm and (c) 1400 rpm, as shown in (Figure2). The welded joints at 1000 and 1200 rpm are found without any defects on visual inspection. The formation of cracks is observed on the weld joint at 1400 rpm rotational speed due to a lack of thermoplastic material flow during stirring action.Figure 2
FSW samples after (a) 1000 rpm, (b) 1200 rpm, and (c) 1400 rpm.


### 4.1. Microstructure Evaluation

Figure3(a) displays the optical micrograph (OM) of friction stir welded Cu-Br of the SZ at 1000 rpm. It is observed that SZ attained equated, recrystallized, finely distributed grains compared with the base metals. However, the HAZ is negligible in all situations. Larger and small size grains are also found in TMAZ. The interaction with the base metal (Figure 3(b)). A similar kind of observation is noted in (Figure 4(a) and 4(b)) for the rotational speed of 1200 rpm. With the higher rotational speed of 1400 rpm in (Figure 5) high heat input generation, the excess plastic flow of material generation produces thermal effects.Figure 3
OM image at the rotational speed of 1000 rpm (a) Stir zone (b) TMAZ.Figure 4
OM image at the rotational speed of 1200 rpm (a) Stir zone (b) TMAZ.Figure 5
OM image at the rotational speed of 1400 rpm (a) TMAZ (b) Stir zone.Figure6(a) displays the SEM microstructure of the SZ of the Cu-Br metal interface at 1000 rpm. The grains are equiaxed with good bonding and recrystallized in the SZ region. Figure 6(b) displays the SEM analysis of the stir zone at 1200 rpm. The dark points and microholes are found in the zone. SEM micrograph at 1400 rpm shows the mixture of round particles formed in grains due to the high rotational speed of the welding process (Figure 6(c)).Figure 6
SEM image of samples after (a) 1000 rpm, (b) 1200 rpm, and (c) 1400 rpm.The base material EBSD microstructural features is shown in Figure7(a). High angle grain boundary (HAGB) stands for 94% of the total and twin boundary (TB) stands for 38%. The BM showed microstructure characteristics were completely annealed. Figure 7(b) displays the SZ microstructure obtained by 1400 rpm rotational speed conditions. The welded joint of the SZ displayed a combination of the grain structure with (0.7 mm) small grains and (8.4 mm) large grains because the high dynamic recrystallization presented by 1400 rpm was extremely high recrystallization. The HAGB was 62% amount fraction and the TB was 5%. Figure 7(c) shows the SZ of the 1000 rpm grain structure was very fine compared with 1400 rpm welded joint, and its observed that average grain size is 1.8 mm. For further grain refinement the number of fractions of 84% HAGBs and 28% TBs increased.Figure 7
EDSD of (a) the base metal, (b) the SZ of 1400 rpm, and (c) the SZ of 1000 rpm.Figure8(a) shows the TEM image of FSW joints. It is seen in the SZ the number of dislocations that have developed at 1400 rpm, which corresponds to the EBSD results as a low angle grain boundary. But, the 1000 rpm welded joint of the SZ decreased the dislocation density visibly and generated several micron-scale twins (Figure 8(b)). As a result, there were more than 28% of TBs in SZ at 1000 rpm. In addition, regionally observable twins on the nano- and submicron sizes, which are not seen by EBSD can be seen in Figure 8(c).Figure 8
SZ (a) dislocation structure, (b) twin structure, and (c) nano-twin.The following grain refining methods were found based on EBSD and TEM observations: Dynamic recrystallization was produced during the welding process by the 1400 rpm rotational speed of the tool. The material undergoes plastic deformation due to this huge number of dislocations induced in the SZ. An increase in the action of stress ensures dislocation slips are formed. While the dislocations moved to the original grain boundary, a dislocation collision occurred, resulting in an enlarged region. At a certain level of dislocation, the dislocation cells are formed. By absorbing dislocations on a continuous basis, the cell structures enhanced their mis-orientation. The subgrains are reconverted into equiaxed recrystallization grains [24]. The FSW technique helps to improve the grain refinement mechanism. Therefore, as welding speed increased, the SZ also changed to refine the grains’ structure. As a result, the SZ formed had a notable microstructural variation at 1000 rpm and 1400 rpm. This can affect the welded joints' mechanical characteristics.


### 4.2. Hardness Properties

The samples are subjected to a hardness test using the Wilson Wolpert Microhardness tester. Every sample had been tested at four different locations with the stir zone location applied to a 0.5 kg load and 10 seconds for dwell time. At all rotational speeds, it was found that the stir zone's hardness was significantly higher than base metals. The different stir zone hardness values are presented in (Figure9). The SZ was not found to have a low-hardness value in each of the 1000 to 1400 rpm joints which eliminated the HAZ. The BM hardness value was observed at 64 HV. The density of dislocations increased as the grains were refined [25]. The maximum hardness of 126.2 HV was found at 1000 rpm due to good bonding, showing that the entire welded joints have been strengthened. The hardness strongly depends upon the frictional tool speed. The desired surface hardness on the brass-copper weld zone is 1000 rpm. Compared with other samples at 1000 rpm, maximum hardness was reached. In particular, at 1200 and 1400 rpm hardness was gradually reduced due to irregular bonding molecules as shown in the SEM figure.Figure 9
The hardness of the Cu-Br welded joint at various rotational speeds.


### 4.3. Impact Test

The ASTME 23-02a standard was used when conducting the impact test. The specimens were prepared as per the dimensions shown in Figure 10(a). Three samples of the copper-brass friction stir weld were refined to 55 mm in length and 10 × 10 mm in cross section, having a V-notch with an angle of 45° and a depth of 2 mm. Figure 10(b) presents a decreased trend of impact strength for 1000 to 1400 rpm, increasing the rotational speed. It has a decreasing impact on strength due to stir zone density variations. In the weld zone, the maximum impact energy attained by 32.4 J at the tool rotational speed of 1000 rpm due to this fine grain structure.Figure 10
(a) The dimensions of Impact test specimen, (b) impact strength of Cu-Br welded joint at various speeds.
(a)(b)While dimples in the brass structure indicate a ductile fracture, brittle fracture forms in the microsized Br reinforcements indicate a brittle fracture. Low impact toughness is caused by coarse, micron-sized silicon carbide particles that function as stress concentration sites and facilitate easy fracture initiation. The impact strength is more influenced by grain refinement during processing, more uniform dispersion of reinforcing particles, and better interaction between the matrix and particles.


### 4.4. Tensile Properties

Figure11(a) presents the dimensions of prepared tensile specimens from welded joints. The tensile strength of the welded joint at various rotational speeds is shown in Figure 11(b). The maximum tensile strength is observed at 1200 rpm. It should be due to the width variation of the stir zone. It has the potential to act as a strengthening structure and improve material density; it has appropriately increased the weld zone strength. It has properly improved the weld zone's strength. The tensile strength enhancement at 1200 rpm welded joint is produced by the following two important causes: First, the grain's low dislocation density leads to a greater area for similarly dislocated dislocation storage [26, 27]. Noticeably, the 1200 rpm welded joint had low dislocation density, so dislocations can additionally collect tensile properties to stimulate plasticity enhancement and strain hardening. Second, nano-scale twins have been shaped within the SZ joint. When compared to incoherent HAGB, coherent TB structural material is a strengthening process. The mirror symmetry of the crystal lattice on each side of TB makes it a unique low-energy coherent grain boundary similar to the traditional dislocation motion region, which now not only allows for easier plastic deformation modification but also improves plasticity strain and hardening [28, 29]. Since HAGB and TB effectively limit dislocation movement, the material is reinforced [30].Figure 11
(a) The dimensions of tensile test specimen, (b) tensile strength of Cu-Br welded joint at various rotational speeds.
(a)(b)Nonetheless, the strengthening result was not significant for the micro twin or submicro twin. While refining the twin to nanoscale, perform the toughening and strengthening effects trigger. Another technique to enhance weld strength without losing ductility is to refine the grain or introduce a twin structure into the grain interior [31]. The nano twin’s existence proves to be adequate. As an outcome, ductility and strength were both improved at the same time. However, the UTS value decreased at a rotational speed of 1400 rpm due to the formation of defects.The maximum tensile strength of 74 MPa is the result of the Br-Cu joint, which is 86.36% of the parent metal Br and 40.6% of parent metal Cu. The fine Cu particles distributed in the Br matrix weld region make the weld region a composite-like system. This Cu reinforcement makes a pinning effect for the dislocation motion during the tensile loading. Since the Br-Cu joint has a defect at the weld region, it acts as the fracture initiation site. Thus, it yields poorer mechanical properties than the Br-Cu joint. The SEM fractography for both joint configurations is shown in Figure11(b). A flat featureless fracture surface was observed for the Br-Cu joint. Initially, the fracture started from the tunnel defect and then followed the interface of Br and Cu materials. Thus, due to the clear separation of Br and Cu materials, a flat featureless surface was observed. Fine populated dimples were observed for the Br-Cu joint which resembles the joint that has undergone a ductile mode of failure.


### 4.5. Corrosion Test

The corrosion properties of the welded samples produced at varying rotational speeds are shown in Figure12. The Cu-Br welded sample density was 7.740 g/cm3, the initial weight of the samples was 19 grams, and the final weight was measured as 18.99 grams after 24 hours. The effects of the samples were 0.010 grams of weight loss at 1000 rpm. Hence, it is inferred that the high corrosion resistance is observed at 1000 rpm compared to other rotational speeds.Figure 12
Corrosion resistance of the Cu-Br welded zone at various rotational speeds.


### 4.6. Numerical Analysis

In finite element modelling, the characteristics of pure copper 28°C at room temperature are used: (8930 Kg/m3) density, (0.385 KJ/KgK), specific heat, and (400 W/mK) thermal conductivity. Surface loads were used to specify boundary conditions in ANSYS programs. The transient, nonlinear equations were solved by full Newton-Raphson to make the ANSYS program's movement tool on the workpiece sheet easier to understand. The ANSYS software is used to investigate the distributions of temperature on welded samples, as shown in Figure 13. When the rotating tool makes contact with the plates, the temperature rises to the point where it reaches the recrystallization temperature. The process moves heated material away from the tool from behind it, while cold material enters the tool from the front. The maximum temperature obtained for welding, according to the ANSYS analysis, is significantly lower than the copper and bronze plate melting points. Along the weld axis, the increase temperature values as the time duration increases. According to the results of the experiment, temperature values decrease as distance increases and increase as time duration increases perpendicular to the weld axis.Figure 13
Temperature distribution during FSW using the ANSYS model.
(a)(b)(c)(d)


## 4.1. Microstructure Evaluation

Figure3(a) displays the optical micrograph (OM) of friction stir welded Cu-Br of the SZ at 1000 rpm. It is observed that SZ attained equated, recrystallized, finely distributed grains compared with the base metals. However, the HAZ is negligible in all situations. Larger and small size grains are also found in TMAZ. The interaction with the base metal (Figure 3(b)). A similar kind of observation is noted in (Figure 4(a) and 4(b)) for the rotational speed of 1200 rpm. With the higher rotational speed of 1400 rpm in (Figure 5) high heat input generation, the excess plastic flow of material generation produces thermal effects.Figure 3
OM image at the rotational speed of 1000 rpm (a) Stir zone (b) TMAZ.Figure 4
OM image at the rotational speed of 1200 rpm (a) Stir zone (b) TMAZ.Figure 5
OM image at the rotational speed of 1400 rpm (a) TMAZ (b) Stir zone.Figure6(a) displays the SEM microstructure of the SZ of the Cu-Br metal interface at 1000 rpm. The grains are equiaxed with good bonding and recrystallized in the SZ region. Figure 6(b) displays the SEM analysis of the stir zone at 1200 rpm. The dark points and microholes are found in the zone. SEM micrograph at 1400 rpm shows the mixture of round particles formed in grains due to the high rotational speed of the welding process (Figure 6(c)).Figure 6
SEM image of samples after (a) 1000 rpm, (b) 1200 rpm, and (c) 1400 rpm.The base material EBSD microstructural features is shown in Figure7(a). High angle grain boundary (HAGB) stands for 94% of the total and twin boundary (TB) stands for 38%. The BM showed microstructure characteristics were completely annealed. Figure 7(b) displays the SZ microstructure obtained by 1400 rpm rotational speed conditions. The welded joint of the SZ displayed a combination of the grain structure with (0.7 mm) small grains and (8.4 mm) large grains because the high dynamic recrystallization presented by 1400 rpm was extremely high recrystallization. The HAGB was 62% amount fraction and the TB was 5%. Figure 7(c) shows the SZ of the 1000 rpm grain structure was very fine compared with 1400 rpm welded joint, and its observed that average grain size is 1.8 mm. For further grain refinement the number of fractions of 84% HAGBs and 28% TBs increased.Figure 7
EDSD of (a) the base metal, (b) the SZ of 1400 rpm, and (c) the SZ of 1000 rpm.Figure8(a) shows the TEM image of FSW joints. It is seen in the SZ the number of dislocations that have developed at 1400 rpm, which corresponds to the EBSD results as a low angle grain boundary. But, the 1000 rpm welded joint of the SZ decreased the dislocation density visibly and generated several micron-scale twins (Figure 8(b)). As a result, there were more than 28% of TBs in SZ at 1000 rpm. In addition, regionally observable twins on the nano- and submicron sizes, which are not seen by EBSD can be seen in Figure 8(c).Figure 8
SZ (a) dislocation structure, (b) twin structure, and (c) nano-twin.The following grain refining methods were found based on EBSD and TEM observations: Dynamic recrystallization was produced during the welding process by the 1400 rpm rotational speed of the tool. The material undergoes plastic deformation due to this huge number of dislocations induced in the SZ. An increase in the action of stress ensures dislocation slips are formed. While the dislocations moved to the original grain boundary, a dislocation collision occurred, resulting in an enlarged region. At a certain level of dislocation, the dislocation cells are formed. By absorbing dislocations on a continuous basis, the cell structures enhanced their mis-orientation. The subgrains are reconverted into equiaxed recrystallization grains [24]. The FSW technique helps to improve the grain refinement mechanism. Therefore, as welding speed increased, the SZ also changed to refine the grains’ structure. As a result, the SZ formed had a notable microstructural variation at 1000 rpm and 1400 rpm. This can affect the welded joints' mechanical characteristics.


## 4.2. Hardness Properties

The samples are subjected to a hardness test using the Wilson Wolpert Microhardness tester. Every sample had been tested at four different locations with the stir zone location applied to a 0.5 kg load and 10 seconds for dwell time. At all rotational speeds, it was found that the stir zone's hardness was significantly higher than base metals. The different stir zone hardness values are presented in (Figure9). The SZ was not found to have a low-hardness value in each of the 1000 to 1400 rpm joints which eliminated the HAZ. The BM hardness value was observed at 64 HV. The density of dislocations increased as the grains were refined [25]. The maximum hardness of 126.2 HV was found at 1000 rpm due to good bonding, showing that the entire welded joints have been strengthened. The hardness strongly depends upon the frictional tool speed. The desired surface hardness on the brass-copper weld zone is 1000 rpm. Compared with other samples at 1000 rpm, maximum hardness was reached. In particular, at 1200 and 1400 rpm hardness was gradually reduced due to irregular bonding molecules as shown in the SEM figure.Figure 9
The hardness of the Cu-Br welded joint at various rotational speeds.


## 4.3. Impact Test

The ASTME 23-02a standard was used when conducting the impact test. The specimens were prepared as per the dimensions shown in Figure 10(a). Three samples of the copper-brass friction stir weld were refined to 55 mm in length and 10 × 10 mm in cross section, having a V-notch with an angle of 45° and a depth of 2 mm. Figure 10(b) presents a decreased trend of impact strength for 1000 to 1400 rpm, increasing the rotational speed. It has a decreasing impact on strength due to stir zone density variations. In the weld zone, the maximum impact energy attained by 32.4 J at the tool rotational speed of 1000 rpm due to this fine grain structure.Figure 10
(a) The dimensions of Impact test specimen, (b) impact strength of Cu-Br welded joint at various speeds.
(a)(b)While dimples in the brass structure indicate a ductile fracture, brittle fracture forms in the microsized Br reinforcements indicate a brittle fracture. Low impact toughness is caused by coarse, micron-sized silicon carbide particles that function as stress concentration sites and facilitate easy fracture initiation. The impact strength is more influenced by grain refinement during processing, more uniform dispersion of reinforcing particles, and better interaction between the matrix and particles.


## 4.4. Tensile Properties

Figure11(a) presents the dimensions of prepared tensile specimens from welded joints. The tensile strength of the welded joint at various rotational speeds is shown in Figure 11(b). The maximum tensile strength is observed at 1200 rpm. It should be due to the width variation of the stir zone. It has the potential to act as a strengthening structure and improve material density; it has appropriately increased the weld zone strength. It has properly improved the weld zone's strength. The tensile strength enhancement at 1200 rpm welded joint is produced by the following two important causes: First, the grain's low dislocation density leads to a greater area for similarly dislocated dislocation storage [26, 27]. Noticeably, the 1200 rpm welded joint had low dislocation density, so dislocations can additionally collect tensile properties to stimulate plasticity enhancement and strain hardening. Second, nano-scale twins have been shaped within the SZ joint. When compared to incoherent HAGB, coherent TB structural material is a strengthening process. The mirror symmetry of the crystal lattice on each side of TB makes it a unique low-energy coherent grain boundary similar to the traditional dislocation motion region, which now not only allows for easier plastic deformation modification but also improves plasticity strain and hardening [28, 29]. Since HAGB and TB effectively limit dislocation movement, the material is reinforced [30].Figure 11
(a) The dimensions of tensile test specimen, (b) tensile strength of Cu-Br welded joint at various rotational speeds.
(a)(b)Nonetheless, the strengthening result was not significant for the micro twin or submicro twin. While refining the twin to nanoscale, perform the toughening and strengthening effects trigger. Another technique to enhance weld strength without losing ductility is to refine the grain or introduce a twin structure into the grain interior [31]. The nano twin’s existence proves to be adequate. As an outcome, ductility and strength were both improved at the same time. However, the UTS value decreased at a rotational speed of 1400 rpm due to the formation of defects.The maximum tensile strength of 74 MPa is the result of the Br-Cu joint, which is 86.36% of the parent metal Br and 40.6% of parent metal Cu. The fine Cu particles distributed in the Br matrix weld region make the weld region a composite-like system. This Cu reinforcement makes a pinning effect for the dislocation motion during the tensile loading. Since the Br-Cu joint has a defect at the weld region, it acts as the fracture initiation site. Thus, it yields poorer mechanical properties than the Br-Cu joint. The SEM fractography for both joint configurations is shown in Figure11(b). A flat featureless fracture surface was observed for the Br-Cu joint. Initially, the fracture started from the tunnel defect and then followed the interface of Br and Cu materials. Thus, due to the clear separation of Br and Cu materials, a flat featureless surface was observed. Fine populated dimples were observed for the Br-Cu joint which resembles the joint that has undergone a ductile mode of failure.


## 4.5. Corrosion Test

The corrosion properties of the welded samples produced at varying rotational speeds are shown in Figure12. The Cu-Br welded sample density was 7.740 g/cm3, the initial weight of the samples was 19 grams, and the final weight was measured as 18.99 grams after 24 hours. The effects of the samples were 0.010 grams of weight loss at 1000 rpm. Hence, it is inferred that the high corrosion resistance is observed at 1000 rpm compared to other rotational speeds.Figure 12
Corrosion resistance of the Cu-Br welded zone at various rotational speeds.


## 4.6. Numerical Analysis

In finite element modelling, the characteristics of pure copper 28°C at room temperature are used: (8930 Kg/m3) density, (0.385 KJ/KgK), specific heat, and (400 W/mK) thermal conductivity. Surface loads were used to specify boundary conditions in ANSYS programs. The transient, nonlinear equations were solved by full Newton-Raphson to make the ANSYS program's movement tool on the workpiece sheet easier to understand. The ANSYS software is used to investigate the distributions of temperature on welded samples, as shown in Figure 13. When the rotating tool makes contact with the plates, the temperature rises to the point where it reaches the recrystallization temperature. The process moves heated material away from the tool from behind it, while cold material enters the tool from the front. The maximum temperature obtained for welding, according to the ANSYS analysis, is significantly lower than the copper and bronze plate melting points. Along the weld axis, the increase temperature values as the time duration increases. According to the results of the experiment, temperature values decrease as distance increases and increase as time duration increases perpendicular to the weld axis.Figure 13
Temperature distribution during FSW using the ANSYS model.
(a)(b)(c)(d)


## 5. Conclusion

The friction stir welding of Cu-Br dissimilar joint configurations is studied at different rotational speeds. The good feasibility of making a joint on Cu with Br is observed while looking at the microstructure. The improved mechanical properties are observed at 1000 rpm rather than 1400 rpm. The leading conclusions are summarized as follows: the Cu-Br dissimilar joint formation of grains was equiaxed, recrystallized, and well distributed in the SZ. SEM observed a unique deformation form with the ultra-fine grains mixed in the SZ region. EBSD perceived in the SZ had shown a kind of grain structure at 1000 rpm, which was very fine compared with the 1400 rpm welded joint, and it was observed that it had a 1.8 mm average grain size. More than 28% of TBs were found in the SZ at 1000 rpm FSW joint, according to TEM. The hardness and impact strength have been observed to be decreased due to the increasing of rotational speed. High corrosion resistance was observed at 1000 rpm compared to other rotational speeds. ANSYS software was used to investigate the formation of energy heat distribution in copper and bronze during friction stir welding. It can be perceived that the plates had displayed the lower melting point, compared to their parent materials during the welding.



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