Tailoring the Mechanical Properties of Laser Cladding-Deposited Ferrous Alloys with a Mixture of 410L Alloy and Fe–Cr–B–Si–Mo Alloy Powders

The effects of different ratios of 410L alloy and Fe–Cr–B–Si–Mo alloy powders on the microstructure and mechanical properties of laser cladding-deposited ferrous alloys were investigated. The experimental results revealed that the 410L alloy had good strength and excellent ductility due to its microstructure consisting of large elongated ferrite dendrites surrounded by a small number of martensite grains, while the Fe–Cr–B–Si–Mo alloy had high strength and poor ductility because of its eutectic microstructure composed of ferrite and Fe2B/Cr2B. As the concentration of Fe–Cr–B–Si–Mo alloy powder added to the 410L alloy powder increased, the ferrite grains became finer and the volume fraction of the eutectic increased, which eventually improved the strength and reduced the plasticity. Then, 410L + 12.5% Fe–Cr–B–Si–Mo alloy powder was successfully deposited onto AISI 1060 steel substrate via laser cladding deposition, and the mechanical properties met those of the substrate, which verified that tailoring the mechanical properties of the laser cladding-deposited alloys with a mixture of 410L and Fe–Cr–B–Si–Mo alloy powders for steel repairing applications is a feasible solution.


Introduction
Many defective components, which are mis-machined in the manufacturing process or locally worn in the service process, have to be scrapped, resulting in serious resource waste and huge economic losses. Steel is the most commonly used materials for gears, shafts, railway wheels, and so on in many industrial applications, and the market demand for the repairing of such products is huge. Therefore, it is urgently necessary to find an effective repair method to restore the geometry and provide sufficient strength to such components, allowing for their continued use [1].
Laser cladding deposition (LCD), also called laser engineering net shaping (LENS) [2], is a laser additive manufacturing process, which is based on the iterative process of coaxial powder delivery melting/rapid solidification layer-by layer deposition [3]. The deposited layers are metallurgically bonded and exhibit a narrow heat-affected zone and small dilution zones, possessing a high accuracy and outstanding mechanical property [4]. Owing to the manufacturing principle and those significant merits, LCD technique is suitable for the repairing of defective components [5].
Repairing steel parts using LCD has been the subject of much research in recent years. Liu et al. [4,6] presented a feasibility exploration of superalloys for AISI 4140 steel repairing using LENS. However, the tensile strength and hardness value of the specimens did not meet the industrial requirements.  All the alloy samples were deposited using a homemade LCD system (Xi'an Jiaotong University, Xi'an, China) [21]. The schematic diagram of the LCD system is illustrated in Figure 2. The system fundamentally consists of a 1000 W Nd:YAG laser, a coaxial powder feed system, a gas shielded box, and a 3-axis motion control system. Argon was used as the powder carrier gas and shielding gas during the LCD process. The powder was uniformly mixed and dried, and the substrate surface was polished and cleaned by ethanol before the deposition. The optimized process parameters were employed, as shown in Table 2. The hatch path was set to an S shape, and the scanning direction of each layer was perpendicular to the previous layer. A rectangle sample of 15 mm × 9 mm × 5 mm, and 3 cylindrical samples of Φ 8.2 mm × 45 mm for each alloy were built via LCD.    All the alloy samples were deposited using a homemade LCD system (Xi'an Jiaotong University, Xi'an, China) [21]. The schematic diagram of the LCD system is illustrated in Figure 2. The system fundamentally consists of a 1000 W Nd:YAG laser, a coaxial powder feed system, a gas shielded box, and a 3-axis motion control system. Argon was used as the powder carrier gas and shielding gas during the LCD process. The powder was uniformly mixed and dried, and the substrate surface was polished and cleaned by ethanol before the deposition. The optimized process parameters were employed, as shown in Table 2. The hatch path was set to an S shape, and the scanning direction of each layer was perpendicular to the previous layer. A rectangle sample of 15 mm × 9 mm × 5 mm, and 3 cylindrical samples of Φ 8.2 mm × 45 mm for each alloy were built via LCD.  All the alloy samples were deposited using a homemade LCD system (Xi'an Jiaotong University, Xi'an, China) [21]. The schematic diagram of the LCD system is illustrated in Figure 2. The system fundamentally consists of a 1000 W Nd:YAG laser, a coaxial powder feed system, a gas shielded box, and a 3-axis motion control system. Argon was used as the powder carrier gas and shielding gas during the LCD process. The powder was uniformly mixed and dried, and the substrate surface was polished and cleaned by ethanol before the deposition. The optimized process parameters were employed, as shown in Table 2. The hatch path was set to an S shape, and the scanning direction of each layer was perpendicular to the previous layer. A rectangle sample of 15 mm × 9 mm × 5 mm, and 3 cylindrical samples of Φ 8.2 mm × 45 mm for each alloy were built via LCD.    The rectangle samples were sectioned vertically through the middle in length. The sections parallel and perpendicular to the building direction were mounted, grinded, and polished for metallographic observations and phase composition analysis, respectively. The metallographic specimens were then etched with a solution of 5 g CuCl 2 , 100 mL HCl, and 100 mL ethanol. The cylindrical samples were machined into dogbone-shaped tensile specimens with a gauge section of 20 mm (length) × 3 mm (diameter). The tensile tests were performed by an Instron 5985 tensile machine (Instron Corporation, Boston, America) at room temperature (22 • C). The etched metallographic specimens and the fracture surfaces of the tensile specimens were evaluated by a Hitachi SU-8010 scanning electron microscope (SEM, Hitachi, Ltd., Tokyo, Japan). The phase compositions of the sections, which were perpendicular to the building direction and were not etched, were identified by X-ray diffraction (XRD, Bruker AXS GmbH, Karlsruhe, Germany), using a Bruker D8 Diffractometer (Bruker AXS GmbH, Karlsruhe, Germany) with Cu Kα radiation. Figure 3 shows the X-ray diffraction patterns of the deposited alloys with different weight fractions of Fe-Cr-B-Si-Mo powder. From Figure 3, it can be noted that the peaks of ferrite/martensite (F/M) were all recorded in the pattern of the deposited alloys. Only the F/M peaks were observed in the pattern of the 410L alloy, as shown in Figure 3a, and the result is in agreement with the literature [11,12]. Figure 3b-d show the X-ray diffraction patterns of the deposited alloys produced with a mixture of 410L and Fe-Cr-B-Si-Mo alloy powders. Compared with the patterns of 410L alloy, in addition to the peaks of F/M, the peaks of Fe 2 B/Cr 2 B (M 2 B) were also recorded, the peak intensities of M 2 B increased with the weight fraction of Fe-Cr-B-Si-Mo in 410L, which corresponded to the volume fraction of the M 2 B phase increase. Figure 3e shows the X-ray diffraction patterns of the Fe-Cr-B-Si-Mo alloy. From Figure 3e, it can be observed that the peak intensities of M 2 B were prominently higher than those of F/M, which suggests that the volume fraction of the M 2 B phase may be more than that of the F/M phase. Figure 4 shows the microstructural characteristics of the 410L alloy. From Figure 4, it can be seen that there were large, elongated ferrite grains (dark color) and a small quantity of martensite grains (bright color), which were distributed along the ferrite grain boundary. This is due to the fact that during the transformation from austenite to ferrite, the ferrite nuclei form at the austenitic grain boundary and coarsen into the interior; meanwhile, the carbon diffuses into the austenite, which increases the austenitic carbon content and promotes the transformation of austenite to martensite. Although silicon was contained in the 410L alloy, no eutectic microstructure was observed.

Microstructural Evaluation
A hypoeutectic microstructure was detected in the Fe-Cr-B-Si-Mo alloy, as shown in Figure 5. Fine ferrite grains occupy subordinately, while a eutectic microstructure consisting of ferrite and M 2 B (bright color) dominated the alloy, and the volume fraction of the eutectic was greater than 50%. This might be mainly attributed to the boron contained in the Fe-Cr-B-Si-Mo alloy; the boron exists in liquid near the liquid-solid interfaces during the solidification process due to its weak solubility in solid iron, which increases the constitutional undercooling of the remaining liquid, promotes the eutectic reaction [22], and restrains the growth of austenite grains. Meanwhile molybdenum contained  Figure 4 shows the microstructural characteristics of the 410L alloy. From Figure 4, it can be seen that there were large, elongated ferrite grains (dark color) and a small quantity of martensite grains (bright color), which were distributed along the ferrite grain boundary. This is due to the fact that during the transformation from austenite to ferrite, the ferrite nuclei form at the austenitic grain boundary and coarsen into the interior; meanwhile, the carbon diffuses into the austenite, which increases the austenitic carbon content and promotes the transformation of austenite to martensite. Although silicon was contained in the 410L alloy, no eutectic microstructure was observed. A hypoeutectic microstructure was detected in the Fe-Cr-B-Si-Mo alloy, as shown in Figure 5. Fine ferrite grains occupy subordinately, while a eutectic microstructure consisting of ferrite and M2B (bright color) dominated the alloy, and the volume fraction of the eutectic was greater than 50%. This might be mainly attributed to the boron contained in the Fe-Cr-B-Si-Mo alloy; the boron exists in liquid near the liquid-solid interfaces during the solidification process due to its weak solubility in solid iron, which increases the constitutional undercooling of the remaining liquid, promotes the eutectic reaction [22], and restrains the growth of austenite grains. Meanwhile molybdenum contained in the Fe-Cr-B-Si-Mo alloy also acts to refine the austenite grains. Fine austenite grains eventually transform into fine ferrite grains during cooling.    Figure 4, it can be seen that there were large, elongated ferrite grains (dark color) and a small quantity of martensite grains (bright color), which were distributed along the ferrite grain boundary. This is due to the fact that during the transformation from austenite to ferrite, the ferrite nuclei form at the austenitic grain boundary and coarsen into the interior; meanwhile, the carbon diffuses into the austenite, which increases the austenitic carbon content and promotes the transformation of austenite to martensite. Although silicon was contained in the 410L alloy, no eutectic microstructure was observed. A hypoeutectic microstructure was detected in the Fe-Cr-B-Si-Mo alloy, as shown in Figure 5. Fine ferrite grains occupy subordinately, while a eutectic microstructure consisting of ferrite and M2B (bright color) dominated the alloy, and the volume fraction of the eutectic was greater than 50%. This might be mainly attributed to the boron contained in the Fe-Cr-B-Si-Mo alloy; the boron exists in liquid near the liquid-solid interfaces during the solidification process due to its weak solubility in solid iron, which increases the constitutional undercooling of the remaining liquid, promotes the eutectic reaction [22], and restrains the growth of austenite grains. Meanwhile molybdenum contained in the Fe-Cr-B-Si-Mo alloy also acts to refine the austenite grains. Fine austenite grains eventually transform into fine ferrite grains during cooling. Micrographs of a typical cross section of the deposited alloys with different concentrations of Fe-Cr-B-Si-Mo powder are shown in Figure 6. The diameter of the ferrite grains and the volume fraction of the eutectic in Figures 4, 5, and 6 were calculated using ImageJ software, as shown in Figure 7. Fine ferrite grains and a small amount of interdendritic divorced eutectic were observed in the deposited 410L + 6.25% Fe-Cr-B-Si-Mo, as shown in Figure 6a. The size of the ferrite grains  Figure 6. The diameter of the ferrite grains and the volume fraction of the eutectic in Figures 4-6 were calculated using ImageJ software, as shown in Figure 7. Fine ferrite grains and a small amount of interdendritic divorced eutectic were observed in the deposited 410L + 6.25% Fe-Cr-B-Si-Mo, as shown in Figure 6a. The size of the ferrite grains reduced to one-third of that of the 410L alloy (Figure 4). The ferrite grain size decreased, while the volume fraction of the eutectic increased with the increasing weight fraction of Fe-Cr-B-Si-Mo in the 410L alloy, as shown in Figure 7, and similar results were also observed in the literature [22]. This may be due to the fact that the liquid phase composition is closer to the eutectic composition as the boron content increases, so the volume fraction of the eutectic is larger, and the size of ferrite grains transformed from austenite is finer. Micrographs of a typical cross section of the deposited alloys with different concentrations of Fe-Cr-B-Si-Mo powder are shown in Figure 6. The diameter of the ferrite grains and the volume fraction of the eutectic in Figures 4, 5, and 6 were calculated using ImageJ software, as shown in Figure 7. Fine ferrite grains and a small amount of interdendritic divorced eutectic were observed in the deposited 410L + 6.25% Fe-Cr-B-Si-Mo, as shown in Figure 6a. The size of the ferrite grains reduced to one-third of that of the 410L alloy (Figure 4). The ferrite grain size decreased, while the volume fraction of the eutectic increased with the increasing weight fraction of Fe-Cr-B-Si-Mo in the 410L alloy, as shown in Figure 7, and similar results were also observed in the literature [22]. This may be due to the fact that the liquid phase composition is closer to the eutectic composition as the boron content increases, so the volume fraction of the eutectic is larger, and the size of ferrite grains transformed from austenite is finer.  Further, no martensite phase was observed in the deposited alloys containing Fe-Cr-B-Si-Mo alloy, as shown in Figures 5 and 6. To illustrate this phenomenon, the Schaeffler diagram was adopted, as shown in Figure 8. The chemical composition of ferritic stainless-steel elements (except Fe) are simplified by the chromium equivalent (Creq) and nickel equivalent (Nieq), and the Creq and Further, no martensite phase was observed in the deposited alloys containing Fe-Cr-B-Si-Mo alloy, as shown in Figures 5 and 6. To illustrate this phenomenon, the Schaeffler diagram was adopted, as shown in Figure 8. The chemical composition of ferritic stainless-steel elements (except Fe) are simplified by the chromium equivalent (Cr eq ) and nickel equivalent (Ni eq ), and the Cr eq and Ni eq are shown below: Cr eq = Cr + Mo + 1.5Si + 0.5Nb (1) where each chemical element symbol indicates the percentage content [23]. Ferrite and martensite distribution in each alloy can be found in the Schaeffler diagram, except for the 410L alloy (A1); the other alloys (A2-A5) are located in the ferrite region of the Schaeffler diagram due to the content of carbon and manganese decreasing when the Fe-Cr-B-Si-Mo alloy was mixed into the 410L alloy. Further, no martensite phase was observed in the deposited alloys containing Fe-Cr-B-Si-Mo alloy, as shown in Figures 5 and 6. To illustrate this phenomenon, the Schaeffler diagram was adopted, as shown in Figure 8. The chemical composition of ferritic stainless-steel elements (except Fe) are simplified by the chromium equivalent (Creq) and nickel equivalent (Nieq), and the Creq and Nieq are shown below: where each chemical element symbol indicates the percentage content [23]. Ferrite and martensite distribution in each alloy can be found in the Schaeffler diagram, except for the 410L alloy (A1); the other alloys (A2-A5) are located in the ferrite region of the Schaeffler diagram due to the content of carbon and manganese decreasing when the Fe-Cr-B-Si-Mo alloy was mixed into the 410L alloy.  Figure 9 shows the stress-strain curves of the 410L alloy and Fe-Cr-B-Si-Mo alloy. From Figure  9, it can be observed that the yield strength (YS), ultimate tensile strength (UTS), and elongation of  Figure 9 shows the stress-strain curves of the 410L alloy and Fe-Cr-B-Si-Mo alloy. From Figure 9, it can be observed that the yield strength (YS), ultimate tensile strength (UTS), and elongation of 410L alloy were 330 MPa, 545.5 MPa, and 18%, respectively, and the excellent tensile properties were attributed to its microstructure composed of ferrite and martensite. The YS, UTS, and elongation of the Fe-Cr-B-Si-Mo alloy were 841.5 MPa, 1365.5 MPa, and 2%, respectively, and the high strength and low plasticity were due to the eutectic microstructure. The tensile results of the deposited alloys with different weight fractions of Fe-Cr-B-Si-Mo powder are shown in Figure 10. In Figure 10, as the mass fraction of Fe-Cr-B-Si-Mo mixed in the 410L alloy increases, the YS and UTS increases from 282 MPa to 1153.3 MPa and from 565 MPa to 1326.7 MPa, respectively, and the elongation decreases from 22% to 5.5%. This is related to the aforementioned changes in the microstructure of the alloys; the strength of the alloy is improved because of the ferrite grain refinement according to the Hall-Petch strengthening behavior and the increasing volume fraction of the eutectic, while the plasticity is reduced due to the increasing numbers of the eutectic. the mass fraction of Fe-Cr-B-Si-Mo mixed in the 410L alloy increases, the YS and UTS increases from 282 MPa to 1153.3 MPa and from 565 MPa to 1326.7 MPa, respectively, and the elongation decreases from 22% to 5.5%. This is related to the aforementioned changes in the microstructure of the alloys; the strength of the alloy is improved because of the ferrite grain refinement according to the Hall-Petch strengthening behavior and the increasing volume fraction of the eutectic, while the plasticity is reduced due to the increasing numbers of the eutectic.  The fracture surfaces were examined using SEM to investigate the different tensile properties of the alloys (Figure 11). The SEM analysis showed that the tensile fracture of the alloys changed from ductility fracture to cleavage fracture. Many fine dimples and microvoids were observed on the fracture surfaces of the 410L alloy (Figure 11a) and the 410L + 6.25% Fe-Cr-B-Si-Mo alloy ( Figure  11b), which indicated that the fracture surfaces were ductile, the ductile fractures were reasonably consistent with the high elongation of the 410L alloy and the 410L + 6.25% Fe-Cr-B-Si-Mo alloy from 22% to 5.5%. This is related to the aforementioned changes in the microstructure of the alloys; the strength of the alloy is improved because of the ferrite grain refinement according to the Hall-Petch strengthening behavior and the increasing volume fraction of the eutectic, while the plasticity is reduced due to the increasing numbers of the eutectic.  The fracture surfaces were examined using SEM to investigate the different tensile properties of the alloys (Figure 11). The SEM analysis showed that the tensile fracture of the alloys changed from ductility fracture to cleavage fracture. Many fine dimples and microvoids were observed on the fracture surfaces of the 410L alloy (Figure 11a) and the 410L + 6.25% Fe-Cr-B-Si-Mo alloy ( Figure  11b), which indicated that the fracture surfaces were ductile, the ductile fractures were reasonably consistent with the high elongation of the 410L alloy and the 410L + 6.25% Fe-Cr-B-Si-Mo alloy The fracture surfaces were examined using SEM to investigate the different tensile properties of the alloys (Figure 11). The SEM analysis showed that the tensile fracture of the alloys changed from ductility fracture to cleavage fracture. Many fine dimples and microvoids were observed on the fracture surfaces of the 410L alloy (Figure 11a) and the 410L + 6.25% Fe-Cr-B-Si-Mo alloy (Figure 11b), which indicated that the fracture surfaces were ductile, the ductile fractures were reasonably consistent with the high elongation of the 410L alloy and the 410L + 6.25% Fe-Cr-B-Si-Mo alloy ( Figure 10). Figure 11c presents the fracture surface of the 410L + 12.5% Fe-Cr-B-Si-Mo alloy; it can be seen that fewer and shallower dimples existed on the fracture surface of the 410L + 12.5% Fe-Cr-B-Si-Mo alloy compared with that of the 410L alloy and the 410L + 6.25% Fe-Cr-B-Si-Mo alloy. The fracture of the 410L + 25% Fe-Cr-B-Si-Mo alloy was a mixture of quasi-cleavage fracture and ductile fracture (Figure 11d). The fracture of the Fe-Cr-B-Si-Mo alloy was observed to be in quasi-cleavage failure mode (Figure 11e).

Tensile Properties
(Figure10). Figure 11c presents the fracture surface of the 410L + 12.5% Fe-Cr-B-Si-Mo alloy; it can be seen that fewer and shallower dimples existed on the fracture surface of the 410L + 12.5% Fe-Cr-B-Si-Mo alloy compared with that of the 410L alloy and the 410L + 6.25% Fe-Cr-B-Si-Mo alloy. The fracture of the 410L + 25% Fe-Cr-B-Si-Mo alloy was a mixture of quasi-cleavage fracture and ductile fracture (Figure 11d). The fracture of the Fe-Cr-B-Si-Mo alloy was observed to be in quasi-cleavage failure mode (Figure 11e).

A Case Study of the Repair of AISI 1060 Steel
The above research results showed that the mechanical properties of the deposited alloys could be adjusted by adding Fe-Cr-B-Si-Mo powder to the 410L alloy, which matched the mechanical properties of the steel that needed to be repaired. A case study of the repair of AISI 1060 steel (Table  1) was used to verify the feasibility of this method. AISI 1060 steel is a material used for railway wheels, which is usually worn and deformed by the complex contact between the wheels and rails, and the worn wheel is difficult to repair. The mechanical properties of AISI 1060 steel were close to those of the deposited 410L + 12.5% Fe-Cr-B-Si-Mo, so the 410L + 12.5% Fe-Cr-B-Si-Mo powder was chosen as the repair material, and three 410L + 12.5% Fe-Cr-B-Si-Mo pillars (length of 25mm and diameter of 8.2mm) were deposited onto the AISI 1060 steel substrate (dimensions of 75mm ×

A Case Study of the Repair of AISI 1060 Steel
The above research results showed that the mechanical properties of the deposited alloys could be adjusted by adding Fe-Cr-B-Si-Mo powder to the 410L alloy, which matched the mechanical properties of the steel that needed to be repaired. A case study of the repair of AISI 1060 steel (Table 1) was used to verify the feasibility of this method. AISI 1060 steel is a material used for railway wheels, which is usually worn and deformed by the complex contact between the wheels and rails, and the worn wheel is difficult to repair. The mechanical properties of AISI 1060 steel were close to those of the deposited 410L + 12.5% Fe-Cr-B-Si-Mo, so the 410L + 12.5% Fe-Cr-B-Si-Mo powder was chosen as the repair material, and three 410L + 12.5% Fe-Cr-B-Si-Mo pillars (length of 25 mm and diameter of 8.2 mm) were deposited onto the AISI 1060 steel substrate (dimensions of 75 mm × 55 mm × 40 mm) (Figure 12a). Then, the specimen was machined onto the tensile samples. The size of the tensile samples is shown in Figure 12b. The mechanical properties of the AISI 1060 steel substrate samples, deposited 410L + 12.5% Fe-Cr-B-Si-Mo samples, and 410L + 12.5% Fe-Cr-B-Si-Mo for the AISI 1060 steel repairing samples are shown in Figure 13. From Figure 13, it can be noted that a YS of 406 MPa, an UTS of 794 MPa, and an elongation of 16.5% were obtained for the AISI 1060 steel substrate. Compared with the AISI 1060 steel substrate, the YS of the 410L + 12.5% Fe-Cr-B-Si-Mo for AISI 1060 steel repairing was 449 MPa, about 110% of the YS of the substrate, the UTS was 801.5 MPa, slightly higher than that of the substrate, and the elongation was 16%, about 97% of the elongation of the substrate, which indicated that the mechanical properties might meet the requirements for AISI 1060 steel repairing. 55mm × 40mm) (Figure 12a). Then, the specimen was machined onto the tensile samples. The size of the tensile samples is shown in Figure 12b. The mechanical properties of the AISI 1060 steel substrate samples, deposited 410L + 12.5% Fe-Cr-B-Si-Mo samples, and 410L + 12.5% Fe-Cr-B-Si-Mo for the AISI 1060 steel repairing samples are shown in Figure 13. From Figure 13, it can be noted that a YS of 406 MPa, an UTS of 794 MPa, and an elongation of 16.5% were obtained for the AISI 1060 steel substrate. Compared with the AISI 1060 steel substrate, the YS of the 410L + 12.5% Fe-Cr-B-Si-Mo for AISI 1060 steel repairing was 449 MPa, about 110% of the YS of the substrate, the UTS was 801.5 MPa, slightly higher than that of the substrate, and the elongation was 16%, about 97% of the elongation of the substrate, which indicated that the mechanical properties might meet the requirements for AISI 1060 steel repairing.

Conclusions
In this study, the microstructure features and mechanical properties of cladding with a mixture of 410L alloy and Fe-Cr-B-Si-Mo alloy powders were studied, and then, a case study of 410L + 12.5% Fe-Cr-B-Si-Mo repairing of AISI 1060 steel was implemented. The conclusions are as follows: 55mm × 40mm) (Figure 12a). Then, the specimen was machined onto the tensile samples. The size of the tensile samples is shown in Figure 12b. The mechanical properties of the AISI 1060 steel substrate samples, deposited 410L + 12.5% Fe-Cr-B-Si-Mo samples, and 410L + 12.5% Fe-Cr-B-Si-Mo for the AISI 1060 steel repairing samples are shown in Figure 13. From Figure 13, it can be noted that a YS of 406 MPa, an UTS of 794 MPa, and an elongation of 16.5% were obtained for the AISI 1060 steel substrate. Compared with the AISI 1060 steel substrate, the YS of the 410L + 12.5% Fe-Cr-B-Si-Mo for AISI 1060 steel repairing was 449 MPa, about 110% of the YS of the substrate, the UTS was 801.5 MPa, slightly higher than that of the substrate, and the elongation was 16%, about 97% of the elongation of the substrate, which indicated that the mechanical properties might meet the requirements for AISI 1060 steel repairing.

Conclusions
In this study, the microstructure features and mechanical properties of cladding with a mixture of 410L alloy and Fe-Cr-B-Si-Mo alloy powders were studied, and then, a case study of 410L + 12.5% Fe-Cr-B-Si-Mo repairing of AISI 1060 steel was implemented. The conclusions are as follows:

Conclusions
In this study, the microstructure features and mechanical properties of cladding with a mixture of 410L alloy and Fe-Cr-B-Si-Mo alloy powders were studied, and then, a case study of 410L + 12.5% Fe-Cr-B-Si-Mo repairing of AISI 1060 steel was implemented. The conclusions are as follows:

1.
Coatings with several combinations of strength and plasticity were manufactured using LCD by adding different proportions of Fe-Cr-B-Si-Mo powder to 410L powder, which are available for the repair of various kinds of steel parts.

2.
The microstructural morphologies of the deposited 410L alloy chiefly consisted of large, elongated ferrite grains and a small number of martensite grains distributed around the ferrite grain boundary, and it has low strength and good ductility.