The E ﬀ ect of Laser O ﬀ set Welding on Microstructure and Mechanical Properties of 301L to TA2 with and without Cu Intermediate Layer

: Based on dissimilar materials of 301L / TA2, the e ﬀ ect of laser o ﬀ set and copper intermediate layer on welded joints was investigated. First, the process optimization of laser o ﬀ sets indicated that the tensile strength of welded joint without intermediate layer was reached to the highest value when the laser was applied on the TA2 side. On the other hand, the tensile strength of welded joint with intermediate layer performed well when laser was applied in the middle position. Then, microstructural characterization and mechanical properties of welded joints were observed and tested. Based on eutectic reaction and peritectic reaction: TiFe and TiFe 2 compounds were produced for welded joint without intermediate layer. Cu-Fe solid solutions and Cu-Ti compounds were generated when copper was used as the intermediate layer. The maximum tensile strength of welded joint with and without copper intermediate layer were 396 and 193 MPa, respectively. Finally, fracture mechanism of 301L / TA2 welded joint was studied: Fe-Ti compounds caused brittle fracture of welded joints without intermediate layer; brittle fracture took place in rich copper and Cu-Ti compounds area of welded joints with copper intermediate layer. writing—review and X.L.; visualization, X.Z.; supervision, X.Z.; project administration, X.Z.;


Introduction
Pure titanium and stainless steel are often used in clinical medical field for the high mechanical strength, fatigue resistance, excellent resistance to physiological corrosion, and biocompatibility [1]. At present, the medical implants with stainless steel and titanium-based alloys have been approved. The hip joint prosthesis are made of stainless steel. Industrial pure titanium is also used to make artificial bone, knee, and elbow joints. Besides, they are used as stamping parts and corrosion-resistant structural parts with a working temperature below 360 • C, which are not stressed but require high plasticity, such as: aircraft frame partitions, engine accessories, marine corrosion-resistant pipelines, and heat exchangers in chemical industry. The composite component formed by stainless steel and titanium can fully take advantage of the complementary performance and economic advantages.
Because of the differences in physical and chemical properties of titanium and stainless steel, there are many technical difficulties in the welding process. First of all, the huge difference in the linear expansion coefficient results in a different deformation capacities during welding heating and cooling process. Therefore, a large tensile residual stress will be produced in the welded joint, and it is difficult to be removed. Second, the strong interdiffusion between titanium and iron atoms will occur under the action of high temperature during welding process, so a large amount of brittle and hard intermetallic compounds (TiFe, TiFe 2 , Ti 2 Fe) are formed in the welded joint during cooling process. In addition, titanium is easy to form intermetallic compounds (TiC, TiCr 2 , TiNi, TiNi 2 , TiNi 3 ) with carbon, chromium, and nickel in the stainless steel matrix, which increases the brittleness of welded joints [2][3][4].
In order to obtain the welded joint with excellent performance of pure titanium and stainless steel, it is necessary to adopt appropriate welding methods and welding processes to reduce internal stress and avoid formation of brittle phase. Ridha Mohammed [5] studied the fiber laser welding of dissimilar 2205/304 stainless steel plates. The results suggest that fiber laser welding is effectively employed to produce austenitic-duplex stainless steel weldment. Landowski [6] had investigated the autogenous fiber laser welding of 316L austenitic and 2304 lean duplex stainless steels. Cao [7] experimented on the effect of beam offset on macro defects, microstructure and mechanical behaviors in dissimilar laser beam welds of SDSS2502/Q235. The study reports that a good weld formation could be obtained when a suitable laser beam offset toward the SDSS2507. From the previous investigations, laser welding and laser offset are conducive to the connection of dissimilar materials. In addition, a suitable intermediate layer can greatly affect the interdiffusion of elements and hinder the direct reaction of iron and titanium. As for the selection of intermediate layer, copper is currently the best choice because of its excellent ductility and low cost [8][9][10][11]. Under the action of welding heat source, a part of molten copper reacts with titanium and iron to form compounds, the other part exists in welded seam in the form of solid solution, which hinders the metallurgical reaction of titanium and iron. Therefore, copper as an intermediate layer greatly restrains the formation of brittle compounds [12,13]. In the past 10 years, considerable attention has been paid to Cu intermediate layer. Pardal [14] had performed welding of Ti and stainless by Cu as transition metal using cold metal transfer technology. The results suggest that the intermetallic compounds formed are less and mechanical properties improved are higher. Tomashchuk [11] had performed dissimilar welding of titanium alloy to stainless steel using copper as an interlayer on a Nd:YAG laser. The study showed that the insertion of copper obtained good mechanical properties. Zhang [15] also had performed dissimilar welding of titanium alloy with stainless steel using laser welding technique by Cu intermediate layer. The study shows that a good weld quality was obtained for joints having Cu as a filler material. However, there are a few reports and studies on the effect of laser offset on joints 301L to TA2 with and without Cu intermediate layer.
In this study, the effect of laser offset on welded joints of 301L to TA2 with and without Cu intermediate layer was investigated. Microstructural characterization and mechanical properties of welded joints were observed and tested. The fracture mechanism of welded joints was investigated.

Materials and Methods
Pulsed Nd:YAG laser system (Changchun New Industries Optoelectronics Technology Co. Ltd., Changchun, China) was used in this study. The parameters were laser power of 1.05 kW, wavelength of 1.064 µm, beam spot diameter of 0.1 mm, and focal length of 150 mm. Stainless steel of 301 and pure titanium of TA2 were used. The chemical composition and physical properties are shown in Tables 1-3 [16,17].  The workpieces were machined into 50 mm × 40 mm × 1 mm plates, and then were cleaned mechanically and chemically before welding. The laser beam offset is the distance between laser spot center and 301L/TA2 interface. When the laser beam center was irradiated on 301L side, the offset was recorded as a negative value, on the contrary, the offset was recorded as a positive value. Three kinds of offsets, i.e., −0.3 mm, 0 mm, and +0.3 mm were employed, as shown in Figure 1. Different offsets mean that the heat input and temperature field are different.  The workpieces were machined into 50 mm × 40 mm × 1 mm plates, and then were cleaned mechanically and chemically before welding. The laser beam offset is the distance between laser spot center and 301L/TA2 interface. When the laser beam center was irradiated on 301L side, the offset was recorded as a negative value, on the contrary, the offset was recorded as a positive value. Three kinds of offsets, i.e., −0.3 mm, 0 mm, and +0.3 mm were employed, as shown in Figure 1. Different offsets mean that the heat input and temperature field are different. In the process of setting welding parameters, we not only should ensure the completely melting of intermediate layer, but also control the partial melting of base metal. In this study, the adopted laser welding parameters of TA2/301L is current of 110 A, welding speed of 200 mm/min, pulse width of 9.0 ms, defocus amount of 19.6 mm, pulse frequency of 6.0 Hz and argon (99.99%) gas flow of 15 L/min. Based on the above welding parameters, three kinds of laser offsets (−0.3 mm, 0 mm, 0.3 mm) were applied. In order to better observe the microstructure, the welded joint was etched by corrosive liquid (10 g FeCl3 + 30 mL HCl + 120 mL H2O). Microstructure was observed with OM (Scope Axio ZEISS, Jena, Germany) and SEM (S-3400, HITACHI, Tokyo, Japan). Phase composition was investigated by X-ray diffraction (XRD) analysis (D8 DISCOVER GDDDS, Bruker, Karlsruhe, Germany). Micro-hardness was evaluated by Nano-indentation test (MH-3, Xi'an Minks Testing Equipment Co. Ltd., Xi'an, China). Tensile strength was measured by Electro-hydraulic servo universal testing machine (MIS8/0.22M, MTS Systems Corporation 14000 Technology Drive, Eden Prairie, MN, USA). In the process of setting welding parameters, we not only should ensure the completely melting of intermediate layer, but also control the partial melting of base metal. In this study, the adopted laser welding parameters of TA2/301L is current of 110 A, welding speed of 200 mm/min, pulse width of 9.0 ms, defocus amount of 19.6 mm, pulse frequency of 6.0 Hz and argon (99.99%) gas flow of 15 L/min. Based on the above welding parameters, three kinds of laser offsets (−0.3 mm, 0 mm, 0.3 mm) were applied. In order to better observe the microstructure, the welded joint was etched by corrosive liquid (10 g FeCl 3 + 30 mL HCl + 120 mL H 2 O). Microstructure was observed with OM (Scope Axio ZEISS, Jena, Germany) and SEM (S-3400, HITACHI, Tokyo, Japan). Phase composition was investigated by X-ray diffraction (XRD) analysis (D8 DISCOVER GDDDS, Bruker, Karlsruhe, Germany). Micro-hardness was evaluated by Nano-indentation test (MH-3, Xi'an Minks Testing Equipment Co. Ltd., Xi'an, China). Tensile strength was measured by Electro-hydraulic servo universal testing machine (MIS8/0.22M, MTS Systems Corporation 14000 Technology Drive, Eden Prairie, MN, USA). Figure 2 shows the front and back surfaces morphologies of 301L/TA2 welded joints with different laser offsets. From Figure 2 we can know that laser offsets greatly affected the appearance of welded joints. When the offset was −0.3 mm, there was no obvious metal luster and welding ripples, while the obvious underfill (Figure 2a) exists on the front of welded joint. In addition, the linear expansion coefficient of 301L was greater than that of TA2. When the offset was −0.3 mm, the greater deformation and residual stress were produced because the more heat input was applied to 301L side, so the crack can be observed on the back surface ( Figure 2b). When the offset was 0 mm, there are good welding ripples, but the obvious collapse still exists (Figure 2c). When the offset was +0.3 mm, a favorable morphology (obvious welding ripples and metallic luster) of welding surface without collapse was formed ( Figure 2e). In Figure 2d,f, the obvious welding flaws were not found, and the quality of back welding surface were good.  Figure 2 shows the front and back surfaces morphologies of 301L/TA2 welded joints with different laser offsets. From Figure 2 we can know that laser offsets greatly affected the appearance of welded joints. When the offset was −0.3 mm, there was no obvious metal luster and welding ripples, while the obvious underfill (Figure 2a) exists on the front of welded joint. In addition, the linear expansion coefficient of 301L was greater than that of TA2. When the offset was −0.3 mm, the greater deformation and residual stress were produced because the more heat input was applied to 301L side, so the crack can be observed on the back surface ( Figure 2b). When the offset was 0 mm, there are good welding ripples, but the obvious collapse still exists (Figure 2c). When the offset was +0.3 mm, a favorable morphology (obvious welding ripples and metallic luster) of welding surface without collapse was formed (Figure 2e). In Figure 2d,f, the obvious welding flaws were not found, and the quality of back welding surface were good.

Microstructures and Elements Distribution
The cross-sectional morphologies of 301L/TA2 welded joints are shown in Figure 3. As displayed in Figure 3a-b, welded joints showed full penetration when laser offsets were −0.3 mm and 0 mm because stainless steel has low heat capacity and a high thermal conductivity as compared with TA2 (Table 3). However, welded joint with offset of +0.3 mm showed lack of penetration (Figure 3c). 301L and TA2 form a welded joint through two ways of fusion welding at the top and diffusion bonding at the bottom (red box in Figure 3c). Figure 3d-f show the microstructures of welded joint on 301L side, welding center and TA2 side, respectively. Figure 3d mainly contained gray region A and white

Microstructures and Elements Distribution
The cross-sectional morphologies of 301L/TA2 welded joints are shown in Figure 3. As displayed in Figure 3a,b, welded joints showed full penetration when laser offsets were −0.3 mm and 0 mm because stainless steel has low heat capacity and a high thermal conductivity as compared with TA2 (Table 3). However, welded joint with offset of +0.3 mm showed lack of penetration ( Figure 3c). 301L and TA2 form a welded joint through two ways of fusion welding at the top and diffusion bonding at the bottom (red box in Figure 3c). Figure 3d-f show the microstructures of welded joint on 301L side, welding center and TA2 side, respectively. Figure 3d mainly contained gray region A and white region B. According to the results of Energy Disperse Spectroscopy (EDS) analysis (Table 4), the main element in region A was Fe with a content of approximately 72.18%, and the gray region A was γ-Fe. The Micro-XRD analysis results further confirmed that γ-Fe existed on 301L side (see Figure 4a below). Based on the analysis of EDS and XRD, region B was mainly composed of γ-Fe + FeTi. According to Fe-Ti binary phase diagram [12], the FeTi compound was formed by eutectic reaction (L → β-Ti + FeTi). Figure 3e mainly contains the white region C. According to the results of EDS analysis, the Fe-Ti atomic ratio in the region C was close to the stoichiometric ratio of Fe 2 Ti. Based on the Fe-Ti binary phase diagram, the Fe 2 Ti compound was formed by the eutectic reaction (L → α-Fe+ Fe 2 Ti). Micro-XRD analysis also confirmed the existence of Fe 2 Ti ( Figure 4b). As shown in Figure 3f, region D was close to base metal TA2 and mainly contained Ti. Region D was identified as β-Ti based on the results of Micro-XRD analysis ( Figure 4c) and EDS analysis ( Table 4). Figure 3g shows the enlarged view of red box region in Figure 3c. A thin diffusion layer was observed in Figure 3h,i, indicating that diffusion of Fe in TA2 and existence of Ti in 301L stainless steel. Figure 3j shows the line scanning results of Path 4, the transition of elements is characterized by diffusion welding and the curve overlap at the interface does not exist, which is different from the line scanning results of Path 3 (see Figure 5c), indicating that no intermetallic compounds were formed. In addition, Figure 5a,b also present curve overlap phenomenon. The above results indicate that 301L/TA2 welded joint contains two connection types that is fusion welding at the top and diffusion bonding at the bottom (red box in Figure 3c), which was conducive to enhance tensile strength of 301L/TA2 welded joint [18]. The Micro-XRD analysis results further confirmed that γ-Fe existed on 301L side (see Figure 4a below). Based on the analysis of EDS and XRD, region B was mainly composed of γ-Fe + FeTi. According to Fe-Ti binary phase diagram [12], the FeTi compound was formed by eutectic reaction (L → β-Ti + FeTi). Figure 3e mainly contains the white region C. According to the results of EDS analysis, the Fe-Ti atomic ratio in the region C was close to the stoichiometric ratio of Fe2Ti. Based on the Fe-Ti binary phase diagram, the Fe2Ti compound was formed by the eutectic reaction (L → α-Fe+ Fe2Ti). Micro-XRD analysis also confirmed the existence of Fe2Ti ( Figure 4b). As shown in Figure 3f, region D was close to base metal TA2 and mainly contained Ti. Region D was identified as β-Ti based on the results of Micro-XRD analysis ( Figure 4c) and EDS analysis ( Table 4). Figure 3g shows the enlarged view of red box region in Figure 3c. A thin diffusion layer was observed in Figure 3h-i, indicating that diffusion of Fe in TA2 and existence of Ti in 301L stainless steel. Figure 3j shows the line scanning results of Path 4, the transition of elements is characterized by diffusion welding and the curve overlap at the interface does not exist, which is different from the line scanning results of Path 3 (see Figure 5c), indicating that no intermetallic compounds were formed. In addition, Figure  5a-b also present curve overlap phenomenon. The above results indicate that 301L/TA2 welded joint contains two connection types that is fusion welding at the top and diffusion bonding at the bottom (red box in Figure 3c), which was conducive to enhance tensile strength of 301L/TA2 welded joint [18].      From Figure 5, it is clear that a large fluctuation exists in the Fe and Ti distribution curves. When the offset was +0.3 mm, the peak of Fe curve corresponds with the trough of Ti curve (Figure 5c), indicating that Fe-Ti compound was formed in the welding zone. Little amount of curve overlap means that only a small amount of intermetallic compounds (Fe-Ti) were generated in the welded joints. Owing to the uneven temperature field distribution and little melting amount of 301L when the laser beam was located on TA2 side, the diffusion rate and diffusion amount of Fe element were reduced. Then a small amount of Fe-Ti compounds were generated, which was beneficial to improve the tensile strength of the welded joint. Figure 6 shows the map scanning results of elements distribution on the cross-sections of 301L/TA2 welded joints. It is obvious that both Fe and Ti are evenly distributed. As the offset changes from −0.3 mm to +0.3 mm, the content of Fe decreases, and the content of Ti increases. From Figure 5, it is clear that a large fluctuation exists in the Fe and Ti distribution curves. When the offset was +0.3 mm, the peak of Fe curve corresponds with the trough of Ti curve (Figure 5c), indicating that Fe-Ti compound was formed in the welding zone. Little amount of curve overlap means that only a small amount of intermetallic compounds (Fe-Ti) were generated in the welded joints. Owing to the uneven temperature field distribution and little melting amount of 301L when the laser beam was located on TA2 side, the diffusion rate and diffusion amount of Fe element were reduced. Then a small amount of Fe-Ti compounds were generated, which was beneficial to improve the tensile strength of the welded joint. Figure 6 shows the map scanning results of elements distribution on the cross-sections of 301L/TA2 welded joints. It is obvious that both Fe and Ti are evenly distributed. As the offset changes from −0.3 mm to +0.3 mm, the content of Fe decreases, and the content of Ti increases.

Microhardness
As shown in Figure 7, the hardness value of welding seam was higher than that of base metal. Because of the formation of Fe-Ti intermetallic compounds by element diffusion in the welding process, the hardness of welding seam was enhanced [19].  Figure 8 shows the dimensions of the tensile specimens. In order to ensure the accuracy of the test data, under the same welding parameters, the average value of the tensile test results of three samples is taken as the final tensile strength value. The tensile specimens with different laser offsets are shown in Figure 9. Although offsets were different, the fracture position was always close to 301L side. On the one hand, the linear expansion coefficient of 301L was about twice as that of TA2, which leads to a large deformation of 301L during welding process and a high tensile residual stress in the welded joint. On the other hand, brittle intermetallic compounds (FeTi) were formed in the welded joint near 301L side.

Microhardness
As shown in Figure 7, the hardness value of welding seam was higher than that of base metal. Because of the formation of Fe-Ti intermetallic compounds by element diffusion in the welding process, the hardness of welding seam was enhanced [19].

Microhardness
As shown in Figure 7, the hardness value of welding seam was higher than that of base metal. Because of the formation of Fe-Ti intermetallic compounds by element diffusion in the welding process, the hardness of welding seam was enhanced [19].  Figure 8 shows the dimensions of the tensile specimens. In order to ensure the accuracy of the test data, under the same welding parameters, the average value of the tensile test results of three samples is taken as the final tensile strength value. The tensile specimens with different laser offsets are shown in Figure 9. Although offsets were different, the fracture position was always close to 301L side. On the one hand, the linear expansion coefficient of 301L was about twice as that of TA2, which leads to a large deformation of 301L during welding process and a high tensile residual stress in the welded joint. On the other hand, brittle intermetallic compounds (FeTi) were formed in the welded joint near 301L side.  Figure 8 shows the dimensions of the tensile specimens. In order to ensure the accuracy of the test data, under the same welding parameters, the average value of the tensile test results of three samples is taken as the final tensile strength value. The tensile specimens with different laser offsets are shown in Figure 9. Although offsets were different, the fracture position was always close to 301L side. On the one hand, the linear expansion coefficient of 301L was about twice as that of TA2, which leads to a large deformation of 301L during welding process and a high tensile residual stress in the welded joint. On the other hand, brittle intermetallic compounds (FeTi) were formed in the welded joint near 301L side.   The results of tensile tests are shown in Figure 10, the tensile strength of 301L/TA2 welded joint with offset of +0.3 mm was reached to 193 MPa.  Figure 11 is SEM images of tensile fracture surfaces of 301L/TA2 welded joints. As shown in Figure 11d-f, a relatively smooth fracture surface with a river patterns appears, exhibiting a typical brittle fracture characteristic, attributing to the formation of brittle intermetallic compounds consisting of Fe and Ti. The EDS map scanning results indicated that the phase on fracture surface The results of tensile tests are shown in Figure 10, the tensile strength of 301L/TA2 welded joint with offset of +0.3 mm was reached to 193 MPa.          It is well-known that the tensile strength of welded joint was reduced with the formation of Fe-Ti compounds. In the following research, the effect of laser offset welding on microstructure and mechanical properties of 301L to TA2 with a copper intermediate layer was studied. Figure 13 shows the front and back surfaces of welded joints with copper intermediate layer under the different laser offsets. From Figure 13, the overall welding formation with copper intermediate layer is better than that of weld joints without intermediate layer (Figure 2). When the laser beam was located on 301L side with offset of −0.3 mm, a minor spatter exits on the welding surface. When the laser offset was +0.3 mm on TA2 side, the unmelted copper regions can be observed on the back surface of welded joint (Figure 13f). When the offset was 0 mm, the welding surface is better. It is well-known that the tensile strength of welded joint was reduced with the formation of Fe-Ti compounds. In the following research, the effect of laser offset welding on microstructure and mechanical properties of 301L to TA2 with a copper intermediate layer was studied. Figure 13 shows the front and back surfaces of welded joints with copper intermediate layer under the different laser offsets. From Figure 13, the overall welding formation with copper intermediate layer is better than that of weld joints without intermediate layer (Figure 2). When the laser beam was located on 301L side with offset of −0.3 mm, a minor spatter exits on the welding surface. When the laser offset was +0.3 mm on TA2 side, the unmelted copper regions can be observed on the back surface of welded joint (Figure 13f). When the offset was 0 mm, the welding surface is better.  Figure 14 shows SEM images of pulsed laser welded joints with copper intermediate layer. As displayed in Figure 14a-c, the welded joint was characterized by full penetration. Under the influence of pulsed laser, the molten copper and the partially molten base metal begin to fuse and react. Figure  14d-f show the microstructures on 301L side, welding center and TA2 side, respectively. Figure 13d  Figure 14 shows SEM images of pulsed laser welded joints with copper intermediate layer.

Microstructures and Elements Distribution
As displayed in Figure 14a-c, the welded joint was characterized by full penetration. Under the influence of pulsed laser, the molten copper and the partially molten base metal begin to fuse and react. Figure 14d-f show the microstructures on 301L side, welding center and TA2 side, respectively. Figure 13d mainly includes white region A and gray region B. During welding cooling process, the columnar grain was formed, which can be seen in region A. Table 5 presents EDS results, the content of Fe was 70.10% in white region A, indicating that the microstructure of region A could be solid solution of Fe (γ-Fe). Micro-XRD analysis results (Figure 14a) confirmed the presence of γ-Fe in the welded joints. Table 5 shows that the atomic ratio of Fe-Ti in the region B was close to the stoichiometric ratio of Fe 2 Ti, so the region B may be Fe 2 Ti. According to Fe-Cu binary phase diagram, Cu could not produce brittle intermetallic compounds with Fe [20]. Thus, Fe element here and Ti element will form Fe 2 Ti. Furthermore, Fe 2 Ti embedded in a solid solution of Cu and then formed coarse granule phase (region B). Such distribution pattern reduced the brittleness of Fe-Ti intermetallic compound, enhanced the plasticity of Cu solid solution, and improved the mechanical properties of welded joints [21]. Figure 13e mainly included gray region C and white region D. Combined with the results of EDS analysis, the main microstructure of C region was Cu 2 Ti, the main microstructure of D region was Cu and TiFe 2 . The Micro-XRD results (Figure 15b) demonstrated the presence of phases above in the welded joints. However, it can be seen from C region that Cu 2 Ti was honeycomb-shaped, and its formation can be explained according to Ti-Cu binary phase diagram. First, TiCu was produced (Cu + Ti → TiCu). Then, Cu 4 Ti 3 phase was formed through peritectic reaction (L + TiCu → Cu 4 Ti 3 ). Finally, the generated Cu 4 Ti 3 continues to undergo a peritectic reaction with the liquid phase to form Cu 2 Ti (L + Cu 4 Ti 3 → Cu 2 Ti) [19]. It was worth noting that the brittleness of Cu-Ti intermetallic compound was lower than Fe-Ti [22], so the formation of Cu 2 Ti helps to reduce the brittleness of welded joint [23]. As shown in Figure 14f, we can see a white region E and a gray region F, which was adjacent to base metal of TA2. The content of Ti near base metal of TA2 was higher than that of welding center, combining with EDS results, we can conclude that microstructure of region E was solid solution of Cu and the phase of region F was TiCu compounds. Micro-XRD analysis results (Figure 15c) also confirmed the presence of phases above in the weld joints. Cu4Ti3 → Cu2Ti) [19]. It was worth noting that the brittleness of Cu-Ti intermetallic compound was lower than Fe-Ti [22], so the formation of Cu2Ti helps to reduce the brittleness of welded joint [23]. As shown in Figure 14f, we can see a white region E and a gray region F, which was adjacent to base metal of TA2. The content of Ti near base metal of TA2 was higher than that of welding center, combining with EDS results, we can conclude that microstructure of region E was solid solution of Cu and the phase of region F was TiCu compounds. Micro-XRD analysis results (Figure 15c) also confirmed the presence of phases above in the weld joints. Based on the analysis above, the formation of Cu-Ti is better than that of Ti-Fe in the welded joint, but the formation of Ti-Fe brittle phases cannot be completely eliminated. In other words, the mechanical property of welded joint with copper intermediate layer is better. Figure 14. The cross-sectional morphologies and microstructures of 301L/Cu/TA2 welded joints: (ac) The cross-sectional morphologies of 301L/Cu/TA2 welded joints based on laser offsets of −0.3 mm, 0 mm, +3 mm, respectively; (d-f) microstructures of welded joints on 301L side, welding center, TA2 side, respectively.     Figure 16 shows the line scanning results of elements distribution for welded joints with different offsets. Overall, Ti distribution curve has a lager fluctuation in the seam-titanium interface. When the offset was +0.3 mm, the fluctuation of Ti distribution curve was obvious at the welding seam. In addition, owing to the similar atomic distance between Cu and Fe, the solid solution can be formed easily, more copper atoms would diffuse to 301L side instead of TA2 side (Figure 16c) [22]. Based on the analysis above, the formation of Cu-Ti is better than that of Ti-Fe in the welded joint, but the formation of Ti-Fe brittle phases cannot be completely eliminated. In other words, the mechanical property of welded joint with copper intermediate layer is better. Figure 16 shows the line scanning results of elements distribution for welded joints with different offsets. Overall, Ti distribution curve has a lager fluctuation in the seam-titanium interface. When the offset was +0.3 mm, the fluctuation of Ti distribution curve was obvious at the welding seam. In addition, owing to the similar atomic distance between Cu and Fe, the solid solution can be formed easily, more copper atoms would diffuse to 301L side instead of TA2 side (Figure 16c) [22].  Figure 17 shows the map scanning results of elements distribution on the cross-sections of 301L/Cu/TA2 welded joints. Obviously, Fe and Ti are evenly distributed on both sides of the welding seam. As the offset changes from −0.3 mm to +0.3 mm, the content of Fe is decreased, and Ti is increased in the welded seam.  Figure 17 shows the map scanning results of elements distribution on the cross-sections of 301L/Cu/TA2 welded joints. Obviously, Fe and Ti are evenly distributed on both sides of the welding seam. As the offset changes from −0.3 mm to +0.3 mm, the content of Fe is decreased (Figure 17b,f,j), and Ti is increased in the welded seam (Figure 17d,h,i).

Microhardness
In Figure 18, the hardness value of welding seam was higher than that of base metal, and the fluctuation of hardness value was larger. As discussed above, the composition of welding seam was complex, including copper-iron solid solution, copper-titanium compounds, and a small amount of titanium-iron compounds. In summary, the inhomogeneity of microstructure leads to an uneven distribution of hardness value, which ultimately affects the mechanical properties of welded joint [16].  Figure 8 is the dimension of tensile specimens. As shown in Figure 19, when copper was added as an intermediate layer during welding process, the fracture position of welded joint was close to TA2 side with offset of -0.3 mm and 0 mm. As analyzed above, Ti-Cu compounds formed on TA2 side, resulting in fracture on the TA2 side. When the offset was +0.3 mm, the position of fracture was close to 301L. It is because there is an unmelted copper in the welding seam, which causes the decrease of connecting strength of 301L and Cu.

Microhardness
In Figure 18, the hardness value of welding seam was higher than that of base metal, and the fluctuation of hardness value was larger. As discussed above, the composition of welding seam was complex, including copper-iron solid solution, copper-titanium compounds, and a small amount of titanium-iron compounds. In summary, the inhomogeneity of microstructure leads to an uneven distribution of hardness value, which ultimately affects the mechanical properties of welded joint [16].

Microhardness
In Figure 18, the hardness value of welding seam was higher than that of base metal, and the fluctuation of hardness value was larger. As discussed above, the composition of welding seam was complex, including copper-iron solid solution, copper-titanium compounds, and a small amount of titanium-iron compounds. In summary, the inhomogeneity of microstructure leads to an uneven distribution of hardness value, which ultimately affects the mechanical properties of welded joint [16].  Figure 8 is the dimension of tensile specimens. As shown in Figure 19, when copper was added as an intermediate layer during welding process, the fracture position of welded joint was close to TA2 side with offset of -0.3 mm and 0 mm. As analyzed above, Ti-Cu compounds formed on TA2 side, resulting in fracture on the TA2 side. When the offset was +0.3 mm, the position of fracture was close to 301L. It is because there is an unmelted copper in the welding seam, which causes the decrease of connecting strength of 301L and Cu.  Figure 8 is the dimension of tensile specimens. As shown in Figure 19, when copper was added as an intermediate layer during welding process, the fracture position of welded joint was close to TA2 side with offset of -0.3 mm and 0 mm. As analyzed above, Ti-Cu compounds formed on TA2 side, resulting in fracture on the TA2 side. When the offset was +0.3 mm, the position of fracture was close to 301L. It is because there is an unmelted copper in the welding seam, which causes the decrease of connecting strength of 301L and Cu. Tensile tests results are shown in Figure 20, the tensile strength can reach the maximum value of 396 MPa when the offset was 0 mm with Cu intermediate layer. Tensile tests results are shown in Figure 20, the tensile strength can reach the maximum value of 396 MPa when the offset was 0 mm with Cu intermediate layer. Figure 19. The tensile fracture specimens of 301L/Cu/TA2 welded joints: (a-c) tensile specimen with offset of −0.3 mm, 0 mm and +0.3 mm, respectively.

Tensile Strength and Fracture Surface Observation
Tensile tests results are shown in Figure 20, the tensile strength can reach the maximum value of 396 MPa when the offset was 0 mm with Cu intermediate layer.   Figure 21d-f, a relatively rough fracture surface with river pattern appears, which exhibits a typical brittle fracture characteristic. It is clear that a small number of dimples can be observed on the fracture surface (Figure 21e), the fracture morphology was copper-rich, and XRD analysis results confirmed the presence of Cu ( Figure 22). In addition, when copper was used as the intermediate layer, the EDS map scanning results indicated that the phase on fracture surface was mainly composed of Ti (48.9 at.%) and Cu (46 at.%) (Figure 21e). Fracture occurred at the Ti-Cu compounds. As shown in Figure  22, the XRD analysis results also confirmed the presence of Cu-Ti compounds on the fracture surface.  In Figure 21d-f, a relatively rough fracture surface with river pattern appears, which exhibits a typical brittle fracture characteristic. It is clear that a small number of dimples can be observed on the fracture surface (Figure 21e), the fracture morphology was copper-rich, and XRD analysis results confirmed the presence of Cu ( Figure 22). In addition, when copper was used as the intermediate layer, the EDS map scanning results indicated that the phase on fracture surface was mainly composed of Ti (48.9 at.%) and Cu (46 at.%) (Figure 21e). Fracture occurred at the Ti-Cu compounds. As shown in Figure 22, the XRD analysis results also confirmed the presence of Cu-Ti compounds on the fracture surface.

Conclusions
In conclusion, the joint properties of with and without Cu intermediate layer were actually affected by the laser offset in welding process, and joint with Cu intermediate showed a relatively high strength. Besides, the element diffusion of the dissimilar joint with different laser offsets (−0.3

Conclusions
In conclusion, the joint properties of with and without Cu intermediate layer were actually affected by the laser offset in welding process, and joint with Cu intermediate showed a relatively high strength. Besides, the element diffusion of the dissimilar joint with different laser offsets (−0.3 mm, 0 mm, and +0.3 mm) has been analyzed. The main conclusions can be summarized as follows:

Conclusions
In conclusion, the joint properties of with and without Cu intermediate layer were actually affected by the laser offset in welding process, and joint with Cu intermediate showed a relatively high strength. Besides, the element diffusion of the dissimilar joint with different laser offsets (−0.3 mm, 0 mm, and +0.3 mm) has been analyzed. The main conclusions can be summarized as follows: (1) The process optimization of laser offsets indicated that the tensile strength of welded joints without intermediate layer reached to the highest value of 197 MPa when the laser was applied on TA2 side.
(2) Intermediate layer of Cu restrained the formation of Ti-Fe compounds and it was beneficial to the tensile strength of welded joints. The tensile strength of welded joints with Cu intermediate layer reached to 396 MPa.
(3) Because of the characteristics of fast heat and cooling in the pulse laser welding process, the distributions of hardness were uneven in welding seam. The fluctuation of hardness value was low in welding seam without intermediate layer. On the contrary, the fluctuation of hardness value was obvious in welding seam with Cu intermediate layer.
(4) Element diffusion was actually affected by the laser offset in welding process. In the weld, the content of Fe decreases, and Ti increases, as the offset changes from −0.3 mm to +0.3 mm.
(5) When the Cu was not used as an intermediate layer in the welding process, Fe and Ti formed the Fe-Ti compounds by a eutectic reaction (L → β-Ti + FeTi), which led to brittle fracture of welded joints; brittle fracture took place in the rich copper and Cu-Ti compounds area of welded joints with copper intermediate layer.