Investigation of strengthening mechanism of commercially pure titanium joints fabricated by autogenously laser beam welding and laser-MIG hybrid welding processes

In this study, in order to achieve a better understanding of the strengthening mechanism in the commercially pure (CP) Ti welds, autogenously laser beam and laser-MIG hybrid welding of 4.2 mm thick CP-Ti plates were performed and the correlation between microstructure, texture distribution and the mechanical properties were systematically investigated. Microstructural coarsening and increase in microhardness were observed in the HAZ and WZ. The tensile test results suggested the base metal was the weak point of the joint for both welding conditions. The EBSD observations confirmed that a large number of 101¯2\documentclass[12pt]{minimal} \usepackage{amsmath} \usepackage{wasysym} \usepackage{amsfonts} \usepackage{amssymb} \usepackage{amsbsy} \usepackage{mathrsfs} \usepackage{upgreek} \setlength{\oddsidemargin}{-69pt} \begin{document}$$ \left\{10\overline{1}2\right\} $$\end{document} and 112¯2\documentclass[12pt]{minimal} \usepackage{amsmath} \usepackage{wasysym} \usepackage{amsfonts} \usepackage{amssymb} \usepackage{amsbsy} \usepackage{mathrsfs} \usepackage{upgreek} \setlength{\oddsidemargin}{-69pt} \begin{document}$$ \left\{11\overline{2}2\right\} $$\end{document} twin grains occurred in the HAZ and WZ of both welded joints, while a higher concentration of these twin grains were found in the laser-MIG hybrid joints. High concentration of the twin grain boundaries can act as barrier to stop dislocation slip during deformation and therefore contribute to the strengthening of the welds. The existence of very small twin grains and acicular α phase in HAZ and WZ would equivalently reduce the averaged grain size and therefore induce an increase in strength based on Hall-Petch’s law. In addition, the averaged Schmid factor of BM is higher than that of the WZ and HAZ in both welding joints suggesting that the grain boundary sliding will take place preferably in BM during deformation so that the necking and fracture occurred in base metal during tensile tests of both welding joint specimens.


Introduction
Commercially pure titanium (CP-Ti) has been widely used in many industries, such as aerospace, defense, petrol-chemical, nuclear energy and medical applications, due to its high specific strength, excellent corrosion resistance, high temperature performance and excellent biocompatibility [1][2][3]. With increased usage, joining of titanium has become necessary and more and more important in many circumstances [4][5][6]. In fusion welding of pure titanium and its alloys, it is very easy to have defects such oxidation of surface and gas inclusion. This is because titanium is a relatively active metal and has a strong tendency to absorb oxygen, hydrogen and nitrogen at high temperature. So, the weld zone needs to be well protected to prevent titanium from absorbing these gas elements resulting in interstitial hardening which is harmful for the mechanical performance of the welds [7][8][9][10]. Autogenously laser beam welding of engineering components is receiving great attention as it offers advantages of smaller distortions and lower residual stresses due to lower heat input comparing to arc welding. However, it has negative issues such as gap bridging and brittle phase formation due to high cooling rate [11][12][13].
To overcome these problems, laser-arc hybrid welding was developed by combining the benefits of arc and laser that can offer excellent gap adaptability, large penetration and moderate cooling rate [14][15][16].
The strengthening mechanism of the welded CP-Ti joint is very complicated and still not fully understood yet despite significant research efforts have been made on this topic by many researchers previously. Figure 1 shows the crosssectional view of a typical CP-Ti weld [17]. It can be seen that the grain size of the weld zone (WZ) and heat affected zone (HAZ) in the joint is larger than that of the base metal (BM). According to the Hall-Petch relationship, as described in Eq.
(1) below, a decrease in grain size usually leads to an increase in hardness and yield strength [18]: where σ is the yield stress, σ 0 is the resistance to dislocation movement, k 0 is the hardening contribution from the grain boundary and d grain is the averaged grain size. However, most studies showed that the hardness and strength of the laser welded CP-Ti joints, which comprises of relatively larger grained WZ and HAZ zones, were higher than that of the BM, which consists of relatively smaller grains [5,11,12,14,17]. This is controversial to the Hall-Petch's law and stimulated plenty of research interests. A well-known theory was from H. Liu that the strengthen increased in the HAZ was due to the substructure strengthening effect while the WZ combines the substructure and the solute solution strengthening [19]. C. Li compared joints made by 1.5 mm CP-Ti plates using laser and laser-MIG hybrid processes and pointed out that the interaction of cooling rate with the oxygen and nitrogen concentration played a significant role in the microhardness improvement [20]. M. Y. Wu obtained a sound thick CP-Ti joint by electron beam welding and found that the strengthening was mainly due to the suppression of prismatic slip in the WZ [5].
A. Karpagaraj studied the mechanical properties and microstructural characterization of automated TIG welding of thin CP-Ti sheets and suggested that the increase in weld metal strength was mainly due to the fine grained acicular α grains and solid-solution strengthening by TiCN in the WZ [21]. A study on linear friction welded CP-Ti by X.Y. Wang revealed that it was the grain orientation, rather than microstructure, actually affecting the microhardness distribution of the welded joint and a correlation between mechanical properties and texture was also pointed out [22]. Therefore, it can be seen in the literature that there is no general agreement on the strengthening mechanism of CP-Ti welds and further study is still needed. In this paper, a systematic investigation on laser and laser-arc hybrid welding of CP-Ti will be carried out and a comprehensive analysis of the strengthening in the joints will be conducted. The autogenously fiber laser beam welding and laser-MIG hybrid welding of CP-Ti will be performed and the mechanical properties, microstructure and texture of the joint will be characterized. A correlation between microstructure, texture distribution and mechanical properties will be attempted and the strengthening mechanisms in the two welding processes will be proposed as well. The influences of minor elements, such as oxygen and nitrogen, on the weld properties were not taken into account in this study.

Material and methods
The base metal (BM) was grade 2 hot rolled commercially pure titanium plates in a dimension of 120 mm × 60 mm × 4.2 mm. Autogenously laser beam and laser-MIG hybrid butt welding were carried out. ERTA2ELI filler wire with 1.0 mm diameter was used in the laser-MIG hybrid welding process. The chemical compositions of the base metal and the filler wire are given in Table 1.
A YLS-6000 IPG high-brightness multi-mode ytterbiumdoped (Yb-fiber) continuous wave (CW) laser system was employed for both laser beam and laser-MIG hybrid welding in this study. It operated at a wavelength of 1070 ± 10 nm with a maximum power output of 6 kW. A TPS-4000 Fronius welding machine was used for laser-MIG hybrid welding. Schematics of the laser beam welding process and laser-MIG hybrid welding setups are depicted in Fig. 2. For laser beam welding, a trailing nozzle with four copper pipes were positioned behind the weld pool to deliver sufficient shielding gas (Fig. 2a). For laser-hybrid welding, a wider gas shielding zone was needed and therefore a trailing nozzle cluster covering an area of 120 mm × 50 mm was attached to the back of the MIG welding torch, as shown in Fig. 2b, which can ensure adequate protection of the weld surface during welding.
The parameters for both welding processes are given in Table 2. These parameters were optimized results based on a large number of experiments that would produce defect-free weld, i.e. no lack of fusion, hot cracking, gas inclusion,  Butt joint gap (mm) 0 0 The face gas flow rate (L/min) 50 50 The back gas flow rate (L/min) 20 20 undercut or oxidation etc. The current in Table 2 for MIG welding was consistent and the voltage was the corresponding value recorded during the process. The wire feeding was smooth and steady resulted in minimum spatter and appropriate reinforcement. In this study, RD denotes the rolling direction of the base plate, TD is the transverse direction perpendicular to the RD and ND is the normal direction vertical to the titanium plate surface. The microstructure and texture of the two types of welds were analyzed with optical microscopy (OM), scann i n g e l e c t r o n m i c r o s c o p e ( S E M ) a n d e l e c t r o n backscattered diffraction (EBSD). The EBSD data was processed by using Oxford Instruments HKL Channel 5 software to illustrate the textural information. Meanwhile, X-ray diffraction (XRD) was used to identify the phases in welded zones. The X-ray diffraction was carried out in a Shimadzu XRD-6000 system with 40 kV voltage, Cu target, scanning within 30°-80°range at 4°/min speed and 0.02°step size. The samples were firstly ground by using a series of SiC paper up to 4000 grit, polished using diamond paste down to 1 μm and finished with OPS colloidal silica suspension to remove the mechanically deformed layer. For OM observations, the samples were etched for 50~60 s with Kroll's reagent (5% HNO 3 , 5% HF and 90% H 2 O) after grinding and polishing. To assess the efficiency of the joints, Vickers microhardness was measured at a load of 300 g with 10s dwelling time by using a KB30S automated hardness tester. The hardness tests were carried out through three lines which were 1 mm, 2.1 mm and 3.2 mm away from the top surface, respectively, and the indents had 250 μm interval along each line. The results were statistically averaged between three tests conducted on three different cross-sectional views of same specimen. The strength of the welds were examined by uniaxial tensile tests at room temperature with a 5 mm/min speed on a SANS CMT5205 automated testing system. The experiments were set up according to ISO 4136:2012 "Destructive tests on welds in metallic materials -Transverse tensile test" and ISO 6892-1:2016 "Metallic materials -Tensile testing -Part 1: Method of test at room temperature." Finally, the fracture surfaces were investigated by SEM.

Macro-and microstructure
The macrographs of the laser beam and laser-MIG hybrid welded CP-Ti butt joints are shown in Fig. 3. Spatter-free, uniform and silvery white colored weld beads were observed in all specimens which indicated an excellent shielding effect of the trailing nozzle setup for both welding processes. Figure 4a shows a low-magnification macrograph of the cross-sectional view of laser beam welded joint after etching. The WZ exhibits a typical "V" shape and no porosity or other defects was visible at this scale. A clear boundary can be drawn between the BM and HAZ, but the fusion line can hardly be distinguished between the HAZ and WZ from the microstructural point of view. However, an estimated fusion line can be drawn between the weld toe and root, as the dotted lines indicated in Fig. 4a. Hence, a narrow HAZ with an averaged width of approximate 0.71 mm can be extracted on the crosssectional view. Figure 4b-e illustrates the grain structure of laser beam weld revealed under polarized light. An equiaxed grain structure could be found in BM, as shown in Fig. 4b, while a mixture of large columnar, irregular serrated and acicular α grains were observed in WZ (Fig. 4d). Elongated grains perpendicular to the fusion line, which was formed by preferential growth along the thermal gradient direction, could be found in both left and right HAZ zones, as shown in Fig. 4c, e. The HAZ also contains finer serrated α grains indicating a higher cooling rate than WZ.
The cross-sectional view of laser-MIG hybrid welded CP-Ti joint is shown in Fig. 5. No pores, cracks or undercuts defects were found in the weld zone. The laser-MIG hybrid weld has relatively wider HAZ, i.e. approximate 2.90 mm, due to the larger heat input. As shown in Fig. 5d, the WZ consists of coarse columnar α grains, irregularly jagged α grains, and a small amount of relatively finer equiaxed α grains. Unlike the laser beam welding situation, almost no needle-like α grain structure was spotted in WZ of laser-MIG hybrid circumstance. This can be explained that the laser-MIG hybrid welding has a larger heat input and slower solidification speed comparing with laser beam welding, so that the needle-like α grain nuclei have more time to grow and coarsen thereafter. In addition, as seen in Fig. 5d-f, the HAZ features coarser grains than that of the laser beam welded joint.

EBSD analysis
The crystalline orientation colored map at different regions of laser beam welded joint is shown in Fig. 6. It can be seen that the <0001> orientation of the majority of the grains in BM are aligned along the TD direction indicating a strong texture (Fig. 6a). In comparison, the orientations of the grains in the HAZ and WZ are randomly mixed, as shown in Fig. 6b, c, respectively. Figure 7 illustrates the crystallographic orientation colored map at different regions of laser-MIG hybrid welded joint. It shows that all the HAZ and WZ regions consist of a mixture of acicular and large grains with a randomly distributed orientation. Unlike the base material, no obvious texture can be observed in the HAZ and WZ regions. However, the colored maps indicate a grain coarsening effect from HAZ to WZ, as shown in Fig. 7a-c. Figure 8 shows the inverse pole figure corresponding to three regions of the laser beam welded joint as shown in Fig. 5. In Fig. 8a, it can be found that in the BM, the direction of <0001> is parallel to ND while the direction of < 0110 > is nearly parallel to TD, which has a maximum polar density of 7.05 along the ND. This is a typical characteristic of bimodal texture that is usually obtained in hot rolled titanium [23]. In Fig. 8b, c, the textures were significantly weakened in the HAZ and WZ after the laser beam welding process. In HAZ, the maximum polar density is 2.51 and only a few grains with the direction of <0001> parallel to RD can be spotted. In WZ, the maximum polar density is 3.52 and some grains with the direction of <0001> parallel to the ND are present. Figure 9 illustrates the inverse pole figure corresponding to different regions of the laser-MIG hybrid welded joint shown in Fig. 7. The inverse pole diagram of the BM of the hybrid welding, as shown in Fig. 9a, is the same as that of laser beam welded joint. At the HAZ close to BM, the maximum polar density is 2.24 and there is no obvious texture. The orientation of grains between the <0001> and < 0  Fig. 9a. However, in Fig. 9b, the maximum density of HAZ close to weld zone increased to 7.20 and the majority of the grains < 1210 > orientation is parallel to the ND. In Fig. 9c, the inverse pole figure of the WZ indicates a maximum density value of 6.35. The < 1210 > orientations of the majority of the grains align with the ND direction and the grains between <0001> and < 0110 > are also parallel to the ND. These findings agree well with that in Fig. 7. In addition, for CP-Ti, previous studies have shown that the plastic deformation in ND will be more difficult to occur than in other directions, leading to a higher microhardness value [22].
In order to identify twin grains in the two types of welded joints, the grain boundaries were outlined on the EBSD maps by the Tango package in Channel 5, as shown in Figs. 10 and 11. It is known that in the coarse α phase, there are mainly 1122 È É compressive twins and 1012 È É / 1121 È É tensile twins. Thus, the high-angle grain boundaries (˃ 15°) are outlined in black, whereas the grain boundaries of 1012 È É and 1122 È É twins observed in this study are outlined in red and blue, respectively. Figure 10 indicates that there are a large number of twin grains formed after the laser beam welding process due to the large welding residual stress in the joint. In Fig. 11, it can be found that an extremely high concentration of 1012 È É tensile twins occurred in the HAZ close to BM in the laser-MIG hybrid welded joint. It has been known that the formation of twin grains will change the mechanical performance of the joints resulting in a hardening process [24,25]. In addition, the introduction of twin boundaries can reduce the free path for dislocation to move, which in turn leads to an improvement in joint strength [26,27].
The grain size, with and without twin grains in consideration, in different regions of the laser beam welded and laser-MIG hybrid welded joints are calculated in Table 3. The average grain diameter of the WZ is significantly larger than that of the BM and the HAZ in the laser beam welded joints. It is noted that the average grain size at WZ reaches 41.11 μm without counting twin grains. For hybrid welded joints, the average grain size excluding twin grains in the WZ is 50.13 μm, which is larger than that of laser beam welded joint, due to a higher thermal input from the laser and arc heating. As listed in Table 3, in the two welding situations, the averaged grain size was significantly reduced when twin grains were included in the statistics. According to Hall-Petch equation, i.e. the yield strength is reversely proportional to the grain size, therefore, the formation of twins will improve the strength of the welded joint.
Slip is one of the major deformation modes in the plastic deformation process of pure titanium, including 1010 È É < 1 210 > prismatic slip (dominates), 0002 f g< 1120 > basal slip, 1012 È É < 1210 > and 1011 È É < 1210 > pyramidal plane slip [28,29]. For the welded titanium plates, residual strain always exists due to the non-uniform heating and cooling. The energy accumulated from the strain would act as the driving force during the slip deformation process, directing the grain towards a preferred rotation and movement following the Schmid's law. In this study, the Schmid factor distributions and the averaged value in the two types of joints are shown in Figs. 12 and 13.
The average Schmid factor for BM, WZ and HAZ in the laser beam welded joint were 0.37, 0.33, and 0.32, respectively (Fig. 12). Figure 13 shows that the average Schmid factor for the HAZ close to BM, HAZ close to WZ, and WZ in laser-   The above Schmid factor analysis indicated that the average Schmid factor of the prismatic slip was the highest (0.37) for BM in the two types of joints. It is known that large Schmid factor always promote deformation, due to the migration of grain boundary and grain rotation. The higher the Schmid factor, the easier it is to slip in the slip system obeying the Schmid's law [30,31]. So, it can be deduced that the grain boundary sliding will take place firstly at BM during slip deformation for both joints. Therefore, although the BM has smaller grain size, which is supposed to have higher strength according to the Hall-Petch's law, the higher tendency of deformation under load compromises the grain size strengthening effect and results in relatively weaker BM comparing with the coarsened HAZ and WZ.

X-ray diffraction
X-ray diffraction analysis in the BM and WZ of the two types of joints was carried out and the results are depicted in Fig. 14 by comparing with the PDF standard peaks of Ti (ICDD: 441294). The intensity ratios of crystallographic planes of base metal, laser beam and laser-MIG welds related to matrix are listed in Table 4. The diffraction peaks are all hexagonal α phase in BM and the WZ of the two types of joints. The grains in the WZ of the laser beam welded joint have stronger diffraction peaks and smaller half-width in the crystal index of 1012 À Á , 1110 À Á and 1013 À Á indicating a coarser grain size. Meanwhile, the diffraction peaks of the laser-MIG hybrid welds slightly shifted to the right, suggesting that there was a considerable extent of internal stress or lattice distortion in the joint [32]. This large stress or lattice distortion can be related to the formation of twins in the welded joints. Furthermore, the smaller half-width indicates the formation of much larger grains in the hybrid welded joint. Figure 15 shows the microhardness distribution in the two types of titanium welds. The hardness testing of "top" and "bottom" were carried out with traverses at 1 mm below the top surface and over the bottom surface of the plate respectively where the "middle" is at the half thickness of the plate. Because the joint can be seen as symmetric, for simplicity, only the data on the right half is plotted here. Figure 15a indicates that the peak microhardness occurs in the WZ and successively decreases towards HAZ and BM of the laser beam welded joint. Similarly, in the laser-MIG hybrid welded joint, the microhardness of the WZ and the HAZ are also both higher than that of BM. This can be attributed to the formation of the twin gains in WZ and HAZ in both welds. It should be noted that the microhardness exhibits a fluctuate distribution in the WZ and HAZ due to the significant difference in the grain size in different sub-regions. In addition, the laser-MIG hybrid joint features a larger fluctuation of microhardness in WZ than that of the laser beam welded joint, which agrees well with the different distribution of twin grains demonstrated in Figs. 10 and 11. In other words, the twin grains may play a more important role in the laser-MIG hybrid joint strengthening than that in the laser beam welded joint.

Tensile strength and fracture morphology
Tensile tests of both weld samples and base metal were carried out at 5 mm/min testing rate and the fractured specimens are shown in Fig. 16. As shown in Fig. 16a, the fracture position of the BM samples was near the centerline. However, as shown in Fig. 16b, c, the fracture positions of the two types of welded samples were all in the BM zone indicating the base metal was the weak point of the joints.
Due to a failure of equipment and limited access of resources, it was unable to use an extensometer during the tensile tests. Therefore, Fig. 17 plots the loaddisplacement curves of the two types of welded samples and BM samples. The tensile strength and strain were worked out by dividing the load with cross-sectional area and comparing the overall length before and after tests. However, it should be noted that the calculation may not be accurate because of the necking phenomena and human error, but it is comparable between specimens tested under same conditions. The calculations are summarized in Table 5 and it can be seen that the averaged tensile strength of the laser beam welded joint and the laser-MIG hybrid welded joint were 421.4 MPa and 432.6 MPa, respectively, which were both higher than the BM only situation (410 MPa), while the two average elongations (44% and 40%) were lower than the BM only  situation (47.5%). The increase in the tensile strength of two welds is due to the reinforced weld zones in the presence of large number of twin grains. However, improvement on the strength of the welds slightly compromised the ductility resulting in relatively lower elongations. In addition, it should be noted that the MIG-laser weld zone has excessive material brought in by the filler wire that may also contribute to the increase of strength [33]. Compared with BM samples, the stress in the laser-MIG hybrid welded joint samples reached the maximum value faster, and then the sample fractured with a relatively smaller strain, as shown in the enlarged upper-left corner figure in Fig. 17. This is due to that, as previously reported in literature [34,35], the twin boundaries can lead to strain hardening in titanium and generally contribute to the slight decrease in the strain. In addition, the MIG-laser weld zone had excessive material that limited the ability of deformation during tensile tests and therefore resulted in a relatively small strain. One can also calculate the absorbed energy during tensile tests that can provide additional information about how the welds deform. The amount of energy that a weld can absorb before final fracture can be obtained by measuring the area underneath the stress-strain curve [36,37]. However, based on Fig. 17, the difference of absorbed energy between the laser beam and laser-MIG hybrid weld specimens was trivial. Moreover, the fractured samples showed evident convex shapes in WZ and HAZ of the welded samples, as shown in Fig. 16. Although there are also some twin boundaries in the laser beam welded joint, the strain hardening phenomenon is not so obvious due to its narrower width of WZ and HAZ, as shown in Fig. 4. Figure 18 shows the fracture surface morphology of base metal and both welds tensile specimens. Large number of dimples on the fracture surfaces indicates that all samples are subjected to plastic deformation prior to failure. By combing the large strain shown in Fig. 17, it can be concluded that the failure of BM and the two types of welded joint were all due to ductile fracture.
In summary, both laser beam and laser-MIG hybrid welded joints exhibited reinforced weld zone resulted in higher tensile strength of the overall joints. However, different strengthening mechanisms can be drawn from the microstructure and texture analysis in this study. For the laser beam welded joint, on the one hand, the grain size is relatively finer and some acicular type α grains can be formed due to its high cooling rate in the weld zone; on the other hand, the formation of twin grains reduces the average grain size and prevents the generation and movement of dislocations including slipping during plastic deformation. For the laser-MIG hybrid joint, firstly, twined grains played a significant role in the strengthening of the

Conclusions
In this study, autogenously laser beam welding and laser-MIG hybrid welding of CP-Ti were carried out and the microstructure, texture and mechanical properties of both joints were investigated to further understand the strengthening mechanisms in the welds. Both welding processes can produce high quality, defect-free joints. It was found that the heat affected zone (HAZ) and the weld zone (WZ) contain very complicated microstructure which typically is a mixture of coarsened and elongated α grains, acicular α phase and twined grains in both welded joints. A high concentration of 1012 È É and 1122 È É twin boundaries was found in the HAZ and WZ of the laser-MIG hybrid welded joint. The average Schmid factor for base metal (BM) showed a higher value than that of the WZ and HAZ in the welded joints. Greater microhardness was observed in WZ and HAZ and the laser beam welded joints featured a higher tensile strength. For the laser beam welded joints, the strengthening effect could be attributed to the formation of relatively smaller grains, acicular α grains and twined grains. In contrary, in the laser-MIG hybrid welded joint, the strengthening effect could be attributed to the formation of a higher concentration of twined grains and its typical grain texture along with ND in the HAZ and WZ.