Evolution of Microstructure and Mechanical Properties in a Single-Stage Aged 7075 Aluminum Alloy Pulse Variable Polarity Plasma Arc Welded Joint

A 7075 aluminum alloy was successfully welded by pulsed variable polarity plasma arc welding (PVPPAW) and the single-stage aging behavior of the 7075 aluminum alloy PVPPAW joint was systematically investigated. The results demonstrated that the tensile strength of the welded joints initially increased and then decreased with the increase of the single-stage aging temperature and time. After single-stage aging at 490 ◦C for 80 min and at 130 ◦C for 24 h, the tensile strength of the welded joint was 551 MPa, which was increased by 38.5% compared to the as-welded joint. Moreover, the conductivity was 25% international annealed copper standard (IACS) at room temperature, and the resistance to stress corrosion was improved. The main strengthening phases of the weld center were η′ and η phase. The average precipitate size slightly increased with the increase of the single-stage aging temperature, but no obvious change was observed with the increase of the single-stage aging time. The area fraction was initially increased and then decreased with the increase of the single-stage aging temperature and time.


Introduction
Due to their excellent mechanical properties, 7××× series high-strength aluminum alloys are widely used in aerospace, national defense, navigation, automobile, and other fields [1][2][3][4][5][6].A proper welding method is often needed in practical applications, and achieving high-quality welding has been a hot and challenging research topic [7,8].Compared to other traditional fusion welding techniques, PVPPAW technology has significant advantages in welding aluminum alloys [9][10][11], such as the small deformation, energy concentration, absence of a need for groove preparation, narrow weld bead, one-sided welding, and both sides formation.However, there are some limitations, including the strength loss and poor corrosion resistance of welded joints [12,13], which affect, to a certain extent, the further development and application of the Al-Zn-Mg-Cu aluminum alloy.
Methods for improving the softening and corrosion resistance of welded joints have been the research focus of many researchers.In general, heat treatment is a key process to improve the mechanical properties of 7××× series high-strength aluminum alloys [14][15][16][17][18][19].Single-stage aging treatment is one of the main methods used to enhance the mechanical properties of aluminum alloys [20].Several researchers [21][22][23] have found that single-stage aging treatment can not only enhance the strength of 7××× series aluminum alloys, but also improve the performance of 7××× series aluminum alloy welded joints.Kumar et al. [24] found that the strength and hardness of an AA7075 aluminum alloy friction stir welded joint were significantly improved after T6 heat treatment, but the welds demonstrated poor corrosion resistance.Moreover, the resistance to pitting corrosion was improved by retrogression and re-aging treatment with minimum loss of weld strength.Wang et al. [25] investigated the effects of heat treatment on high-strength aluminum alloy friction stir welded joints.The tensile strength reached 415 MPa, which was nearly 89.5% of that of the base metal, the microhardness of the joints was significantly increased, and a more uniform hardness distribution was achieved after heat treatment.Chen et al. [26] investigated the one-step aging behavior of a 7A52 aluminum alloy laser welded joint.The age hardening speed of the joint was significantly accelerated, and the time to peak hardness was significantly reduced when the aging temperature increased from 120 • C to 160 • C. Aging at 140 • C for 16 h was considered as a reasonable one-step aging process.Yan et al. [27] investigated the influence of heat treatment on the microstructure and mechanical properties of a spray formed 7××× series aluminum alloy tungsten inert gas (TIG) welded joint.Their results demonstrated that the microstructure of the weld was homogenous without overburning, the grain size increased slightly after solution treatment, and the strength of the welded joint was improved by about 70% after heat treatment.Therefore, single-stage aging treatment should be an effective way to improve the mechanical properties of 7××× series aluminum alloy welded joints.
In this study, the optimized PVPPAW process was used to weld 7075 aluminum alloy sheets.After solution treatment, the samples were quenched by water and then treated by single-stage aging.The effect of solution treatment on the microstructure and mechanical properties has been investigated in our previous work [28], where the solution treatment process was optimized, and the variation of the size and number of T phases were analyzed.In the present study, the changes in the microstructure and mechanical properties of welds with different applied single-stage aging processes were investigated, and the effects of single-stage aging treatment on the structure and mechanical properties of the 7075 aluminum alloy PVPPAW joint were systematically analyzed.

Materials and Methods
The material used in the present study was sheets of 7075-T651 aluminum alloy produced by Southwest Aluminum Company Co., Ltd.(Chongqing, China), with a chemical composition of (wt.%) 5.1-6.1 Zn, 2.1-2.9Mg, 1.2-2.0Cu, 0.3 Mn, 0.2 Ti, 0.18-0.28Cr, 0.5 Fe, 0.4 Si, and balance Al.ER5183 (Al-Mg alloy) with a diameter of 1.2 mm and chemical composition of (wt.%) 0.25 Zn, 4.3-5.2Mg, 0.1 Cu, 0.5-1.0Mn, 0.15 Ti, 0.05-0.25 Cr, 0.4 Fe, 0.4 Si, and balance Al was used as the filler wire.The mechanical properties of the 7075 aluminum alloy and ER5183 welding wire are shown in Table 1.A VPPA-300 welding power supply and a PMW-300 plasma arc welding torch were used in the experiments, the welding equipment is shown in Figure 1, while 99.9% argon gas was used as both plasma and shielding gas.The joint weld type was butt welding, and the welding parameters [28] of PVPPA are shown in Table 2.The welding sample dimensions were 100 × 80 × 10 mm 3 , and the edge of the specimens were welded along the longitudinal direction.The mechanical properties were tested at room temperature using a SHT-4605 universal testing machine (Shanghai SANS Measuring instrument manufacturing Co., Ltd., Shanghai, China), under a loading speed of 1 mm/min.The tensile tests were performed according to the Chinese GB/T 2651-2008 standard.A schematic illustration of the welded joint is shown in Figure 2. The mechanical properties of the samples were measured perpendicular to the axial direction of the weld, and the weld reinforcement of the front and back surface of the specimens was removed to reduce the stress concentration.The initial gauge length of each sample was 60 × 12 × 10 mm 3 .To ensure the reliability of the measured data, at least three specimens were tested for each condition.The macroscopic structure was observed using optical microscopy (Carl Zeiss AG, Oberkochen, German) after being treated by mechanical and electrical polishing, and then etching by the Keller solution of HNO3:HCl:HF:H2O = 2.5:1.5:1:95(vol.%).The micro-area composition was observed by a Tecnai G2 F20 transmission electron microscope (TEM, FEI Company, Hillsboro, OR, USA).TEM specimens with a thickness of 1 mm were cut by wire cutting and mechanically polished to thick disks of approximately 60 μm.The final thinning was prepared by twin-jet electro-polishing in a mixture solution of 75% methanol and 25% nitric acid (vol.%) at approximately −25 °C and 15 V.The resistivity was measured at room temperature by a SIGMASCOPE SMP 10 conductometer (Linseis Messgeräte GmbH, Vielitzer, German), and electrical conductivity is the reciprocal of resistivity.The sample thickness was 3 mm and the diameter was 12 mm.The Vickers micro-hardness was measured using an HXD-1000TM microhardness tester (Shanghai Taiming Optical Instrument Co., Ltd., Shanghai, China) with an applied load of 200 g for 15 s.The welding sample dimensions were 100 × 80 × 10 mm 3 , and the edge of the specimens were welded along the longitudinal direction.The mechanical properties were tested at room temperature using a SHT-4605 universal testing machine (Shanghai SANS Measuring instrument manufacturing Co., Ltd., Shanghai, China), under a loading speed of 1 mm/min.The tensile tests were performed according to the Chinese GB/T 2651-2008 standard.A schematic illustration of the welded joint is shown in Figure 2. The mechanical properties of the samples were measured perpendicular to the axial direction of the weld, and the weld reinforcement of the front and back surface of the specimens was removed to reduce the stress concentration.The initial gauge length of each sample was 60 × 12 × 10 mm 3 .To ensure the reliability of the measured data, at least three specimens were tested for each condition.The macroscopic structure was observed using optical microscopy (Carl Zeiss AG, Oberkochen, Germany) after being treated by mechanical and electrical polishing, and then etching by the Keller solution of HNO 3 :HCl:HF:H 2 O = 2.5:1.5:1:95(vol.%).The micro-area composition was observed by a Tecnai G2 F20 transmission electron microscope (TEM, FEI Company, Hillsboro, OR, USA).TEM specimens with a thickness of 1 mm were cut by wire cutting and mechanically polished to thick disks of approximately 60 µm.The final thinning was prepared by twin-jet electro-polishing in a mixture solution of 75% methanol and 25% nitric acid (vol.%) at approximately −25 • C and 15 V.The resistivity was measured at room temperature by a SIGMASCOPE SMP 10 conductometer (Linseis Messgeräte GmbH, Vielitzer, Germany), and electrical conductivity is the reciprocal of resistivity.The sample thickness was 3 mm and the diameter was 12 mm.The Vickers micro-hardness was measured using an HXD-1000TM microhardness tester (Shanghai Taiming Optical Instrument Co., Ltd., Shanghai, China) with an applied load of 200 g for 15 s.In order to study the evolution of microstructure and mechanical properties in the single-stage aged 7075 aluminum alloy PVPPAW joints, the welded joint was solution-treated at 490 °C for 80 min, and was subsequently quenched in water at 25 °C.Then, it was aged at 100 °C, 110 °C, 120 °C, 130 °C, and 140 °C for 24 h.After the optimum temperature was determined, different aging times of 12 h, 16 h, 20 h, 24 h, and 28 h were investigated.

Microstructure of the 7075 Aluminum PVPPAW Joint
The optical microstructures of the 7075 aluminum alloy PVPPAW joint can be seen in Figure 3.As it can be observed from Figure 2, the welded joint consists of a base metal (BM) zone, a heat affected zone (HAZ), and a weld metal zone (WMZ).As shown in Figure 3, the BM exhibited a typical rolling microstructure, the HAZ showed an equiaxed grain shape, and the WMZ consisted of coarse dendrites.The morphology of the microstructure is closely related to the heating state and physical characteristics of the aluminum alloy during welding.The PVPPAW method has a high energy density and fast welding speed.The WMZ is the center of the heat input, leading to a small temperature gradient.The fact that the duration at high temperature was longer and the grain growth time was abundant resulted in the formation of a dendritic structure in the WMZ.The temperature of HAZ was increased by the heat dissipation, which reached the recrystallization temperature of the BM, and thus partially equiaxed grains were formed by recrystallization of the rolled structure.The microstructure of the BM was unchanged.In order to study the evolution of microstructure and mechanical properties in the single-stage aged 7075 aluminum alloy PVPPAW joints, the welded joint was solution-treated at 490 • C for 80 min, and was subsequently quenched in water at 25 • C.Then, it was aged at 100 • C, 110 • C, 120 • C, 130 • C, and 140 • C for 24 h.After the optimum temperature was determined, different aging times of 12 h, 16 h, 20 h, 24 h, and 28 h were investigated.

Microstructure of the 7075 Aluminum PVPPAW Joint
The optical microstructures of the 7075 aluminum alloy PVPPAW joint can be seen in Figure 3.As it can be observed from Figure 2, the welded joint consists of a base metal (BM) zone, a heat affected zone (HAZ), and a weld metal zone (WMZ).As shown in Figure 3, the BM exhibited a typical rolling microstructure, the HAZ showed an equiaxed grain shape, and the WMZ consisted of coarse dendrites.The morphology of the microstructure is closely related to the heating state and physical characteristics of the aluminum alloy during welding.The PVPPAW method has a high energy density and fast welding speed.The WMZ is the center of the heat input, leading to a small temperature gradient.The fact that the duration at high temperature was longer and the grain growth time was abundant resulted in the formation of a dendritic structure in the WMZ.The temperature of HAZ was increased by the heat dissipation, which reached the recrystallization temperature of the BM, and thus partially equiaxed grains were formed by recrystallization of the rolled structure.The microstructure of the BM was unchanged.In order to study the evolution of microstructure and mechanical properties in the single-stage aged 7075 aluminum alloy PVPPAW joints, the welded joint was solution-treated at 490 °C for 80 min, and was subsequently quenched in water at 25 °C.Then, it was aged at 100 °C, 110 °C, 120 °C, 130 °C, and 140 °C for 24 h.After the optimum temperature was determined, different aging times of 12 h, 16 h, 20 h, 24 h, and 28 h were investigated.

Microstructure of the 7075 Aluminum PVPPAW Joint
The optical microstructures of the 7075 aluminum alloy PVPPAW joint can be seen in Figure 3.As it can be observed from Figure 2, the welded joint consists of a base metal (BM) zone, a heat affected zone (HAZ), and a weld metal zone (WMZ).As shown in Figure 3, the BM exhibited a typical rolling microstructure, the HAZ showed an equiaxed grain shape, and the WMZ consisted of coarse dendrites.The morphology of the microstructure is closely related to the heating state and physical characteristics of the aluminum alloy during welding.The PVPPAW method has a high energy density and fast welding speed.The WMZ is the center of the heat input, leading to a small temperature gradient.The fact that the duration at high temperature was longer and the grain growth time was abundant resulted in the formation of a dendritic structure in the WMZ.The temperature of HAZ was increased by the heat dissipation, which reached the recrystallization temperature of the BM, and thus partially equiaxed grains were formed by recrystallization of the rolled structure.The microstructure of the BM was unchanged.

Effect of Single-Stage Aging Temperature on the Mechanical Properties
The influence of the single-stage aging temperature on the mechanical properties of welded joints was investigated.Figure 4 shows the change trend of tensile strength and electrical conductivity of welded joints at different single-stage aging temperatures for 24 h.The fracture of the welded joints occurred in the WMZ.The tensile strength of the as-welded joint was 398 MPa, which was about 67.5% of that of the base metal.After solution treatment and single-stage aging, the tensile strength increased to a peak value, and then decreased with the increase of the single-stage aging temperature.The tensile strength of the welded joint at 100 • C was 497 MPa, which was nearly 84.3% of that of the BM.As the single-stage aging temperature increased, the tensile strength of the welded joint was gradually improved.The highest tensile strength of 551 MPa was achieved at 130 • C, which was nearly 93.5% of that of the BM, and it was increased by 38.5% compared to the as-welded joint.

Effect of Single-Stage Aging Temperature on the Mechanical Properties
The influence of the single-stage aging temperature on the mechanical properties of welded joints was investigated.Figure 4 shows the change trend of tensile strength and electrical conductivity of welded joints at different single-stage aging temperatures for 24 h.The fracture of the welded joints occurred in the WMZ.The tensile strength of the as-welded joint was 398 MPa, which was about 67.5% of that of the base metal.After solution treatment and single-stage aging, the tensile strength increased to a peak value, and then decreased with the increase of the single-stage aging temperature.The tensile strength of the welded joint at 100 °C was 497 MPa, which was nearly 84.3% of that of the BM.As the single-stage aging temperature increased, the tensile strength of the welded joint was gradually improved.The highest tensile strength of 551 MPa was achieved at 130 °C, which was nearly 93.5% of that of the BM, and it was increased by 38.5% compared to the as-welded joint.However, the tensile strength of the welded joint at 140 °C decreased slightly compared to that at 130 °C.According to Figure 4, the tensile strength of the welded joint was evidently improved by single-stage aging.Moreover, the electrical conductivity increased slowly when the temperature was between 100 °C and 120 °C, but increased rapidly when the temperature was further increased.The electrical conductivity of the as-welded joint was 17% IACS at room temperature, and it increased from 22% IACS at 110 °C to 26% IACS at 140 °C.It can be seen that the stress corrosion resistance of the welded joints increased with the increase of the single-stage aging temperature [29].Based on the tensile strength results, the optimum aging temperature was 130 °C.The same trend was also observed in the results of the welded joints microhardness.
Figure 5 shows the microhardness distribution of the welded joints at different temperatures for 24 h with a load of 200 g for 15 s.As it can be observed, the microhardness initially increased, and then, as the temperatures increased, it decreased.The microhardness of the weld center increased from 127 HV of the as-welded joint to 145 HV of the joint heat-treated at 130 °C.After single-stage aging, the microhardness of the weld center was still the smallest, much lower than that of the BM, and the microhardness of the HAZ was significantly enhanced.The highest microhardness values of the weld center and the HAZ were obtained when the temperature was 130 °C.However, the tensile strength of the welded joint at 140 • C decreased slightly compared to that at 130 • C. According to Figure 4, the tensile strength of the welded joint was evidently improved by single-stage aging.Moreover, the electrical conductivity increased slowly when the temperature was between 100 • C and 120 • C, but increased rapidly when the temperature was further increased.The electrical conductivity of the as-welded joint was 17% IACS at room temperature, and it increased from 22% IACS at 110 • C to 26% IACS at 140 • C. It can be seen that the stress corrosion resistance of the welded joints increased with the increase of the single-stage aging temperature [29].Based on the tensile strength results, the optimum aging temperature was 130 • C. The same trend was also observed in the results of the welded joints microhardness.
Figure 5 shows the microhardness distribution of the welded joints at different temperatures for 24 h with a load of 200 g for 15 s.As it can be observed, the microhardness initially increased, and then, as the temperatures increased, it decreased.The microhardness of the weld center increased from 127 HV of the as-welded joint to 145 HV of the joint heat-treated at 130 • C.After single-stage aging, the microhardness of the weld center was still the smallest, much lower than that of the BM, and the microhardness of the HAZ was significantly enhanced.The highest microhardness values of the weld center and the HAZ were obtained when the temperature was 130 • C.

Effect of Single-Stage Aging Time on the Mechanical Properties
The variation of tensile strength and electrical conductivity of welded joints at 130 °C for different single-stage aging times can be seen in Figure 6.With the increase of the single-stage aging time, the tensile strength of the welded joint initially increased and then decreased.The tensile strength of the welded joint was 482 MPa after being aged for 12 h, while the maximum tensile strength was 551 MPa after 24 h.The electrical conductivity of the welded joints increased with the increase of aging time.After 24 h, the electrical conductivity reached 24% IACS, and then, after 28 h, increased to 26% IACS.Based on the tensile strength results, the optimum single-stage aging time was 24 h. Figure 7 shows the microhardness distribution of the welded joints at 130 °C for different times with a load of 200 g for 15 s.As it can be observed, the microhardness of welded joints initially increased, and then, as the aging time increased, it decreased.The microhardness of the weld center was 138 HV after 12 h and increased to 145 HV after 24 h of aging.As the aging time increased, the microhardness decreased to 143 HV.After single-stage aging treatment, the microhardness of the weld center was higher than that of the as-welded joint.The microhardness of the HAZ was evidently improved, but it was still lower than that of the BM.The highest microhardness values of the weld center and HAZ were obtained after 24 h of aging.

Effect of Single-Stage Aging Time on the Mechanical Properties
The variation of tensile strength and electrical conductivity of welded joints at 130 • C for different single-stage aging times can be seen in Figure 6.With the increase of the single-stage aging time, the tensile strength of the welded joint initially increased and then decreased.The tensile strength of the welded joint was 482 MPa after being aged for 12 h, while the maximum tensile strength was 551 MPa after 24 h.The electrical conductivity of the welded joints increased with the increase of aging time.After 24 h, the electrical conductivity reached 24% IACS, and then, after 28 h, increased to 26% IACS.Based on the tensile strength results, the optimum single-stage aging time was 24 h.

Effect of Single-Stage Aging Time on the Mechanical Properties
The variation of tensile strength and electrical conductivity of welded joints at 130 °C for different single-stage aging times can be seen in Figure 6.With the increase of the single-stage aging time, the tensile strength of the welded joint initially increased and then decreased.The tensile strength of the welded joint was 482 MPa after being aged for 12 h, while the maximum tensile strength was 551 MPa after 24 h.The electrical conductivity of the welded joints increased with the increase of aging time.After 24 h, the electrical conductivity reached 24% IACS, and then, after 28 h, increased to 26% IACS.Based on the tensile strength results, the optimum single-stage aging time was 24 h. Figure 7 shows the microhardness distribution of the welded joints at 130 °C for different times with a load of 200 g for 15 s.As it can be observed, the microhardness of welded joints initially increased, and then, as the aging time increased, it decreased.The microhardness of the weld center was 138 HV after 12 h and increased to 145 HV after 24 h of aging.As the aging time increased, the microhardness decreased to 143 HV.After single-stage aging treatment, the microhardness of the weld center was higher than that of the as-welded joint.The microhardness of the HAZ was evidently improved, but it was still lower than that of the BM.The highest microhardness values of the weld center and HAZ were obtained after 24 h of aging.Figure 7 shows the microhardness distribution of the welded joints at 130 C for different times with a load of 200 g for 15 s.As it can be observed, the microhardness of welded joints initially increased, and then, as the aging time increased, it decreased.The microhardness of the weld center was 138 HV after 12 h and increased to 145 HV after 24 h of aging.As the aging time increased, the microhardness decreased to 143 HV.After single-stage aging treatment, the microhardness of the weld center was higher than that of the as-welded joint.The microhardness of the HAZ was evidently improved, but it was still lower than that of the BM.The highest microhardness values of the weld center and HAZ were obtained after 24 h of aging.

Effect of Single-Stage Aging Temperature on the Microstructure
In Figure 8, TEM images of the welded joints at different single-stage aging temperatures for 24 h are demonstrated.As it can be seen in Figure 8, the precipitation phase was formed in the grain interior at different temperatures.In addition, typical TEM images with corresponding selected area electron diffraction (SAED) patterns of precipitates are displayed in Figure 9. Based on the analyses, a kind of weak spot appeared at the 1/3 {022 -} position in the diffraction pattern taken along the [011] zone axis and at the 2/3 {2 -20} position in the diffraction pattern taken along the [001] zone axis.These spots were identified as η′ and η phases, the chemical composition of MgZn2 [30][31][32].There were no extra spots other than those in the α-Al matrix, suggesting the presence of fine precipitates in the aged specimen, which can be seen in Figure 8a, where the Guinier-Preston (GP) zone precipitates have the same crystal structure as the matrix [33].As it can be observed in Figure 8a, the particle size of the η′ phase was very small and its distribution was uniform.Furthermore, in Figure 8b, the size of the η' phase increased slightly at 130 °C for 24 h, while its density increased significantly.

Effect of Single-Stage Aging Temperature on the Microstructure
In Figure 8, TEM images of the welded joints at different single-stage aging temperatures for 24 h are demonstrated.As it can be seen in Figure 8, the precipitation phase was formed in the grain interior at different temperatures.In addition, typical TEM images with corresponding selected area electron diffraction (SAED) patterns of precipitates are displayed in Figure 9. Based on the analyses, a kind of weak spot appeared at the 1/3 {022} position in the diffraction pattern taken along the [011] zone axis and at the 2/3 {220} position in the diffraction pattern taken along the [001] zone axis.These spots were identified as η and η phases, the chemical composition of MgZn 2 [30][31][32].There were no extra spots other than those in the α-Al matrix, suggesting the presence of fine precipitates in the aged specimen, which can be seen in Figure 8a, where the Guinier-Preston (GP) zone precipitates have the same crystal structure as the matrix [33].As it can be observed in Figure 8a, the particle size of the η phase was very small and its distribution was uniform.Furthermore, in Figure 8b, the size of the η phase increased slightly at 130 • C for 24 h, while its density increased significantly.

Effect of Single-Stage Aging Temperature on the Microstructure
In Figure 8, TEM images of the welded joints at different single-stage aging temperatures for 24 h are demonstrated.As it can be seen in Figure 8, the precipitation phase was formed in the grain interior at different temperatures.In addition, typical TEM images with corresponding selected area electron diffraction (SAED) patterns of precipitates are displayed in Figure 9. Based on the analyses, a kind of weak spot appeared at the 1/3 {022 -} position in the diffraction pattern taken along the [011] zone axis and at the 2/3 {2 -20} position in the diffraction pattern taken along the [001] zone axis.These spots were identified as η′ and η phases, the chemical composition of MgZn2 [30][31][32].There were no extra spots other than those in the α-Al matrix, suggesting the presence of fine precipitates in the aged specimen, which can be seen in Figure 8a, where the Guinier-Preston (GP) zone precipitates have the same crystal structure as the matrix [33].As it can be observed in Figure 8a, the particle size of the η′ phase was very small and its distribution was uniform.Furthermore, in Figure 8b, the size of the η' phase increased slightly at 130 °C for 24 h, while its density increased significantly.

Effect of Single-Stage Aging Temperature on the Microstructure
In Figure 8, TEM images of the welded joints at different single-stage aging temperatures for 24 h are demonstrated.As it can be seen in Figure 8, the precipitation phase was formed in the grain interior at different temperatures.In addition, typical TEM images with corresponding selected area electron diffraction (SAED) patterns of precipitates are displayed in Figure 9. Based on the analyses, a kind of weak spot appeared at the 1/3 {022 -} position in the diffraction pattern taken along the [011] zone axis and at the 2/3 {2 -20} position in the diffraction pattern taken along the [001] zone axis.These spots were identified as η′ and η phases, the chemical composition of MgZn2 [30][31][32].There were no extra spots other than those in the α-Al matrix, suggesting the presence of fine precipitates in the aged specimen, which can be seen in Figure 8a, where the Guinier-Preston (GP) zone precipitates have the same crystal structure as the matrix [33].As it can be observed in Figure 8a, the particle size of the η′ phase was very small and its distribution was uniform.Furthermore, in Figure 8b, the size of the η' phase increased slightly at 130 °C for 24 h, while its density increased significantly.After aging at 140 • C for 24 h, the density of the precipitated phase was smaller than that at 130 • C. As it can be seen in Figure 8c, the η and η phase in the grains' interior were coarsened remarkably.Moreover, in the analysis of the diffraction pattern taken along the [011] zone axis by the schematic diffraction pattern of Refs.[30,34], the η phase was found to transform to η phase after aging at 140 • C. Due to the difficulty in quantitatively measuring the accurate precipitate size and area fraction from Figure 8, the average precipitate size and area fraction under three different aging temperatures were semi-quantitatively measured [14] and the results are presented in Figure 10.The qualitative comparison of these results indicated that the average precipitate size and area fraction of the precipitates at 130 • C appeared to be smaller and higher than those at the other two temperatures, respectively.The shape of the precipitates was spherical and plate-like, while the average precipitate size was approximated from the average measurements on the long and short axes of the precipitates.As it can be seen in Figure 10, at 120 • C, the fine precipitates were in the size range of 4-6 nm, with an average precipitate size of 5 nm and an area fraction of 18.3%.With the increase of temperature to 130 • C, the average precipitate size remained in the range of 4-6 nm, with an average precipitate size of 5 nm, while the area fraction increased to 34.6%.Then, at 140 • C, the average precipitate size increased to a size range of 5-8 nm and the area fraction decreased to 19.6%.
After aging at 140 °C for 24 h, the density of the precipitated phase was smaller than that at 130 °C.As it can be seen in Figure 8c, the η′ and η phase in the grains' interior were coarsened remarkably.Moreover, in the analysis of the diffraction pattern taken along the [011] zone axis by the schematic diffraction pattern of Refs.[30,34], the η′ phase was found to transform to η phase after aging at 140 °C.Due to the difficulty in quantitatively measuring the accurate precipitate size and area fraction from Figure 8, the average precipitate size and area fraction under three different aging temperatures were semi-quantitatively measured [14] and the results are presented in Figure 10.The qualitative comparison of these results indicated that the average precipitate size and area fraction of the precipitates at 130 °C appeared to be smaller and higher than those at the other two temperatures, respectively.The shape of the precipitates was spherical and plate-like, while the average precipitate size was approximated from the average measurements on the long and short axes of the precipitates.As it can be seen in Figure 10, at 120 °C, the fine precipitates were in the size range of 4-6 nm, with an average precipitate size of 5 nm and an area fraction of 18.3%.With the increase of temperature to 130 °C, the average precipitate size remained in the range of 4-6 nm, with an average precipitate size of 5 nm, while the area fraction increased to 34.6%.Then, at 140°C, the average precipitate size increased to a size range of 5-8 nm and the area fraction decreased to 19.6%.

Effect of Single-Stage Aging Time on the Microstructure
In Figure 11, TEM images of the welded joints aged at 130 °C for different times are demonstrated.As it can be seen in Figure 11, there is no obvious change in the average precipitate size.Initially, the density of the precipitates increased, and then, as the aging time increased, it decreased.Figure 12 shows the SAED analysis of TEM images, where the precipitates were identified as η′ and η phases.The average precipitate size and area fraction of the precipitates at different aging times are shown in Figure 13.As it can be observed, after 12 h, the fine precipitates were in the size range of 4-6 nm, with an average precipitate size of 5 nm and an area fraction of 12.6%.With the increase of time to 24 h, the average precipitate size was in the range of 4-6 nm, with an average precipitate size of 5 nm, and the area fraction increased to 34.6%.After 28 h, the average precipitate size was still in the range of 4-6 nm and the area fraction decreased slightly to 32.6%.As it can be seen in Figure 11, there is no obvious change in the average precipitate size.Initially, the density of the precipitates increased, and then, as the aging time increased, it decreased.Figure 12 shows the SAED analysis of TEM images, where the precipitates were identified as η and η phases.The average precipitate size and area fraction of the precipitates at different aging times are shown in Figure 13.As it can be observed, after 12 h, the fine precipitates were in the size range of 4-6 nm, with an average precipitate size of 5 nm and an area fraction of 12.6%.With the increase of time to 24 h, the average precipitate size was in the range of 4-6 nm, with an average precipitate size of 5 nm, and the area fraction increased to 34.6%.After 28 h, the average precipitate size was still in the range of 4-6 nm and the area fraction decreased slightly to 32.6%.

Discussion
In this study, a 7075 aluminum alloy was welded by PVPPAW using ER5183 (Al-Mg alloy) filler wire, and the effect of single-stage aging on the welded joint was systematically investigated.The tensile strength and the microhardness were enhanced by single-stage aging treatment, as shown in Figure 4; Figure 5. Single-stage aging was an effective method for improving the mechanical properties of welded joints.The improvement of the mechanical properties of the welded joint was due to the precipitation strengthening [14,15,35].The main alloying elements (Zn, Mg, and Cu elements) in the 7075 aluminum alloy PVPPAW joint were the same as in the 7075 aluminum alloy.Consequently, the precipitation sequence in the welded joint would be the same as in an A1-Zn-Mg-Cu alloy.The most common precipitation process that occurs during aging treatment in Al-Zn-Mg-Cu alloys is as follows: supersaturated solid solution state-coherent GP zones-semi-coherent η' phase-incoherent η phase [23].The GP zone and η' phase play an important role in strengthening the alloy, while the strengthening effect of the η phase is weak.

Discussion
In this study, a 7075 aluminum alloy was welded by PVPPAW using ER5183 (Al-Mg alloy) filler wire, and the effect of single-stage aging on the welded joint was systematically investigated.The tensile strength and the microhardness were enhanced by single-stage aging treatment, as shown in Figure 4; Figure 5. Single-stage aging was an effective method for improving the mechanical properties of welded joints.The improvement of the mechanical properties of the welded joint was due to the precipitation strengthening [14,15,35].The main alloying elements (Zn, Mg, and Cu elements) in the 7075 aluminum alloy PVPPAW joint were the same as in the 7075 aluminum alloy.Consequently, the precipitation sequence in the welded joint would be the same as in an A1-Zn-Mg-Cu alloy.The most common precipitation process that occurs during aging treatment in Al-Zn-Mg-Cu alloys is as follows: supersaturated solid solution state-coherent GP zones-semi-coherent η' phase-incoherent η phase [23].The GP zone and η' phase play an important role in strengthening the alloy, while the strengthening effect of the η phase is weak.

Discussion
In this study, a 7075 aluminum alloy was welded by PVPPAW using ER5183 (Al-Mg alloy) filler wire, and the effect of single-stage aging on the welded joint was systematically investigated.The tensile strength and the microhardness were enhanced by single-stage aging treatment, as shown in Figure 4; Figure 5. Single-stage aging was an effective method for improving the mechanical properties of welded joints.The improvement of the mechanical properties of the welded joint was due to the precipitation strengthening [14,15,35].The main alloying elements (Zn, Mg, and Cu elements) in the 7075 aluminum alloy PVPPAW joint were the same as in the 7075 aluminum alloy.Consequently, the precipitation sequence in the welded joint would be the same as in an A1-Zn-Mg-Cu alloy.The most common precipitation process that occurs during aging treatment in Al-Zn-Mg-Cu alloys is as follows: supersaturated solid solution state-coherent GP zones-semi-coherent η' phase-incoherent η phase [23].The GP zone and η' phase play an important role in strengthening the alloy, while the strengthening effect of the η phase is weak.

Discussion
In this study, a 7075 aluminum alloy was welded by PVPPAW using ER5183 (Al-Mg alloy) filler wire, and the effect of single-stage aging on the welded joint was systematically investigated.The tensile strength and the microhardness were enhanced by single-stage aging treatment, as shown in Figure 4 and Figure 5. Single-stage aging was an effective method for improving the mechanical properties of welded joints.The improvement of the mechanical properties of the welded joint was due to the precipitation strengthening [14,15,35].The main alloying elements (Zn, Mg, and Cu elements) in the 7075 aluminum alloy PVPPAW joint were the same as in the 7075 aluminum alloy.Consequently, the precipitation sequence in the welded joint would be the same as in an A1-Zn-Mg-Cu alloy.The most common precipitation process that occurs during aging treatment in Al-Zn-Mg-Cu alloys is as follows: supersaturated solid solution state-coherent GP zones-semi-coherent η phase-incoherent η phase [23].The GP zone and η phase play an important role in strengthening the alloy, while the strengthening effect of the η phase is weak.During aging, the size, quantity, and distribution of precipitates such as GP zones, and η and η phases determine the mechanical properties of welded joints.The final mechanical properties of welded joints are determined by the size of the particles, the interfacial relationship of particles with the matrix, and the grain boundary characteristics [36].
According to the results, the precipitate phase of the 7075 aluminum alloy PVPPAW joint mainly consists of a few GP zones and η phase after an aging time of 12 h, and thus the tensile strength of the welded joint is low.Moreover, the precipitation phases of the welded joints are mainly η phase and η phase under aging at 140 • C, and thus the tensile strength of the welded joint is slightly higher than after 12 h.Under aging at 130 • C, the tensile strength is the highest due to the fact that the precipitated phases are mainly GP zones and an abundance of η phase.According to the dislocation theory, Gleiter and Ashby [37] analyzed the shearing and bypassing mechanisms in detail, and the following equations were obtained: where τ G and τ A are the strengths of the material under the shearing and bypassing mechanisms, respectively; k 1 and k 2 are constants; G is the shear modulus; f is the volume fraction of particles; r is the radius of particles; b is the Bernoulli vector; τ 0 is the strength of the matrix; γ A is the antiphase domain boundary energy; and r 0 is the radius of the dislocation core.From Equations ( 1) and ( 2), it can be deduced that the strengthening effect of the shearing mechanism increases with the increase of the volume fraction and the size of the particles, while the strengthening effect of the bypassing mechanism decreases decrease of the volume fraction and the increase of the particle size.The present work can be reasonably explained by means of shearing and bypassing mechanisms [38][39][40].The volume fraction and the average precipitate size are smaller at 120 • C, as shown in Figure 8a.The tensile strength of the welded joint is lower owing to the fact that the dislocation cuts the GP zone and η phases by moving dislocations [39].When the temperature is 140 • C, the volume fraction of the precipitates decreases and the size of some precipitates increases compared to that aged at 130 • C. The hardness and the tensile strength would be decreased due to the coarsening of precipitate dispersion and the decrease of volume fraction [14], which could be explained by η or η precipitate bypassing mechanisms [40].Our results are consistent with this theory; the dislocation bypassed η phase and η phase particles during deformation, the strengthening effect decreases, and the tensile strength of the welded joint at 140 • C is lower than under an aging temperature of 130 • C, as shown in Figures 4, 5 and 8.
At 130 • C, the precipitated phases are mainly GP zones and η phase.The volume fraction of the precipitated phases is much larger than that at 120 • C and 140 • C. In addition, the precipitate size is similar to that at 120 • C, but smaller than that at 140 • C. The tensile strength of the welded joint is higher according to the precipitation shearing mechanism [38].The volume fraction of the precipitated phase initially increases, and then, as the aging time increases, it decreases.Therefore, the tensile strength of the welded joint initially increases, and then decreases, after reaching the peak value under the combined action of the shearing and bypassing mechanism, as the increase of both the aging temperature and time.
Aging treatment has a certain effect on electrical conductivity.The precipitated amount of solute atoms in the matrix increased with the aging process.At the beginning of aging, a large amount of solute atoms precipitate within the matrix, leading to a poor solid solution, and this results in the rapid increase of electrical conductivity.The total conductivity increases, since the effect of the poor solid solution is greater than the additional scattering effect of the precipitating electrons.The higher the aging temperature, the more solute atoms will precipitate from the matrix, which results in a higher conductivity.With an increase of the aging time, the η and η phases are continuously precipitated within the matrix, and the electrical conductivity increases monotonously.It is advantageous to improve the electrical conductivity by increasing the aging temperature and prolonging the aging

Figure 2 .
Figure 2. Schematic illustration of the welded joint and an indication of various zones across the weld.BM: base metal, HAZ: heat affected zone, WMZ: weld metal zone.

Figure 2 .
Figure 2. Schematic illustration of the welded joint and an indication of various zones across the weld.BM: base metal, HAZ: heat affected zone, WMZ: weld metal zone.

Figure 2 .
Figure 2. Schematic illustration of the welded joint and an indication of various zones across the weld.BM: base metal, HAZ: heat affected zone, WMZ: weld metal zone.

Figure 4 .
Figure 4. Tensile properties and electrical conductivities of welded joints aged at different temperatures for 24 h.

Figure 4 .
Figure 4. Tensile properties and electrical conductivities of welded joints aged at different temperatures for 24 h.

Figure 5 .
Figure 5. Microhardness distributions of welded joints aged at different temperatures for 24 h.

Figure 6 .
Figure 6.Tensile properties and electrical conductivities of welded joints aged at 130 °C for different times.

Figure 5 .
Figure 5. Microhardness distributions of welded joints aged at different temperatures for 24 h.

Figure 5 .
Figure 5. Microhardness distributions of welded joints aged at different temperatures for 24 h.

Figure 6 .
Figure 6.Tensile properties and electrical conductivities of welded joints aged at 130 °C for different times.

Figure 6 .
Figure 6.Tensile properties and electrical conductivities of welded joints aged at 130 • C for different times.

Figure 7 .
Figure 7. Microhardness distributions of welded joints aged at 130 °C for different times.

Figure 7 .
Figure 7. Microhardness distributions of welded joints aged at 130 • C for different times.

Figure 7 .
Figure 7. Microhardness distributions of welded joints aged at 130 °C for different times.

Figure 7 .
Figure 7. Microhardness distributions of welded joints aged at 130 °C for different times.

Figure 10 .
Figure 10.Area fraction of precipitates and average precipitate sizes aged at different temperatures for 24 h.

Figure 10 .
Figure 10.Area fraction of precipitates and average precipitate sizes aged at different temperatures for 24 h.

3. 5 .
Effect of Single-Stage Aging Time on the Microstructure In Figure 11, TEM images of the welded aged at 130 • C for different times are demonstrated.

Figure 11 .
Figure 11.TEM images of the weld center aged at 130 °C for different times (a) 12 h; (b) 24 h; (c) 28 h.

Figure 13 .
Figure 13.Area fraction of precipitates and average precipitate sizes aged at 130 °C for different times.

Figure 11 .
Figure 11.TEM images of the weld center aged at 130 • C for different times (a) 12 h; (b) 24 h; (c) 28 h.

Figure 11 .
Figure 11.TEM images of the weld center aged at 130 °C for different times (a) 12 h; (b) 24 h; (c) 28 h.

Figure 13 .
Figure 13.Area fraction of precipitates and average precipitate sizes aged at 130 °C for different times.

Figure 11 .
Figure 11.TEM images of the weld center aged at 130 °C for different times (a) 12 h; (b) 24 h; (c) 28 h.

Figure 13 .
Figure 13.Area fraction of precipitates and average precipitate sizes aged at 130 °C for different times.

Figure 13 .
Figure 13.Area fraction of precipitates and average precipitate sizes aged at 130 • C for different times.

Table 1 .
Mechanical properties of 7075 aluminum alloy and ER5183 welding wire.