High-performance biomedical magnesium alloy and welding process thereof

Abstract

The invention provides a high-performance biomedical magnesium alloy and a welding process thereof, and the welding process comprises the following steps: S1, processing a magnesium alloy plate, and forming a groove in the surface of the magnesium alloy plate; s2, polishing the magnesium alloy welding surface in the step S1, cleaning with alcohol, and blow-drying, so that the surface of the magnesium alloy welding surface is clean and free of oil stains and oxidation layers; s3, the magnesium alloy plate to be welded is placed in the machining area of the machine tool to be assembled; s4, nano-scale hydroxyapatite HA powder is adopted as a reinforcing phase, the grooves in the surface of the magnesium alloy plate are evenly filled with the nano-scale hydroxyapatite HA powder, and a needle-free stirring head is used for powder sealing operation; and S5, the surface of the magnesium alloy plate subjected to powder sealing is subjected to stirring friction machining treatment, and the high-performance biomedical magnesium alloy is obtained. Hydroxyapatite powder is introduced into a magnesium alloy matrix by adopting a stirring friction processing technology, so that the biocompatibility of the magnesium alloy is improved, the corrosion resistance and the antibacterial property of the magnesium alloy are also improved, and finally, the high-performance biomedical magnesium alloy is obtained.

Description

Technical Field

[0001] The present invention belongs to the technical field of biomedical materials, and particularly relates to a high-performance biomedical magnesium alloy and its welding process. Background Art

[0002] Magnesium (Mg) is one of the four major cations in the body and is also a nutrient essential for various life activities of the body. A large amount of magnesium element ingested daily can promote the growth of bone cells and accelerate the repair of bones. Due to the too-fast degradation rate of magnesium alloys and their poor bioactivity, their application in bioengineering is limited. Hydroxyapatite (HA) has been widely studied because of its similar chemical composition to human bones, and its biocompatibility and bioactivity make it an ideal candidate material for enhancing magnesium alloys. However, in the existing technology, defects such as holes and tunnels are likely to appear during the welding process of magnesium alloys, and the agglomeration problem caused by the uneven distribution of hydroxyapatite makes the biological properties of magnesium alloys not ideal. Summary of the Invention

[0003] Aiming at the above technical problems, the present invention provides a high-performance biomedical magnesium alloy and its welding process. The friction stir processing (FSP) process is used to introduce hydroxyapatite powder into the magnesium alloy matrix, which improves its biocompatibility while also enhancing the corrosion resistance and antibacterial properties of the magnesium alloy, and finally obtains the HA / Mg composite material, that is, a high-performance biomedical magnesium alloy.

[0004] The present invention uses the friction stir processing (FSP) process to introduce hydroxyapatite HA powder into the ZK60 magnesium alloy matrix, which can significantly refine the grain size of the magnesium alloy matrix, and during the FSP process, the hydroxyapatite HA particles are evenly distributed in the Mg matrix. Under this process, the Ca / P of the HA / Mg composite material increases to 1.61, which is extremely close to the Ca / P ratio of 1.67 of human bone tissue, indicating its good biocompatibility, and the corrosion resistance of the HA / Mg composite material under the S1500-3 pass process reaches 1898 Ω·cm 2 , and its corrosion resistance is improved by an order of magnitude compared with the magnesium alloy matrix without adding hydroxyapatite.

[0005] Note that the recording of these objectives does not prevent the existence of other objectives. One aspect of the present invention does not need to achieve all the above objectives. Other objectives than the above can be extracted from the descriptions of the specification, drawings, and claims.

[0006] The present invention achieves the above technical objectives through the following technical means.

[0007] A welding process for a high-performance biomedical magnesium alloy includes the following steps:

[0008] Step S1: Process the magnesium alloy sheet and create a groove on the surface of the magnesium alloy sheet.

[0009] Step S2: Polish the welding surface of the magnesium alloy in Step S1, clean it with alcohol and dry it to make its surface clean, free of oil stains and oxide layers.

[0010] Step S3: Place the magnesium alloy sheet to be welded in the machining area of the machine tool for assembly.

[0011] Step S4: Use nano-hydroxyapatite HA powder as the reinforcement phase, evenly fill the nano-hydroxyapatite HA powder into the groove on the surface of the magnesium alloy sheet, and perform powder sealing operation with a needleless stirring head.

[0012] Step S5: Perform friction stir processing on the surface of the powder-sealed magnesium alloy sheet to obtain HA / Mg composite material, namely high-performance biomedical magnesium alloy.

[0013] In the above solution, the grade of the magnesium alloy sheet in Step S1 is ZK60, and the size of the magnesium alloy sheet is 180mm×90mm×6mm.

[0014] Further, in Step S1, a groove with a length of 180mm, a width of 3mm and a depth of 2mm is processed at the center position of the surface of the magnesium alloy sheet.

[0015] In the above solution, the average particle size of the nano-hydroxyapatite HA powder in Step S4 is 3.71±0.38μm.

[0016] In the above solution, the shoulder width of the needleless stirring head in Step S4 is 20mm, and the pressing amount of the stirring head is 0.4mm.

[0017] In the above solution, the rotation speed of the welding tool for friction stir processing in Step S5 is 1300 - 1700rpm / min, the welding speed is 100mm / min, the spindle tilt angle is 2.5°, and the number of welding passes is 3.

[0018] Further, the rotation speed of the welding tool for friction stir processing in Step S5 is 1500rpm / min.

[0019] In the above solution, the welding tool for friction stir processing in Step S5 is a needle stirring head, the shoulder width of the stirring head is 20mm, and the pressing amount of the stirring head is 4mm.

[0020] A high-performance biomedical magnesium alloy is prepared according to the welding process of the high-performance biomedical magnesium alloy.

[0021] In the above solution, the grain size of the high-performance biomedical magnesium alloy is 2.1 μm, the calcium-phosphorus ratio is 1.61, the hardness is 88.2 HV, the tensile strength is 168.77 MPa, the elongation is 5.26%, the elastic modulus is 32.08 GPa, and the corrosion resistance is 1898 Ω·cm 2 .

[0022] Compared with the prior art, the beneficial effects of the present invention are as follows:

[0023] 1. In the present invention, ZK60 magnesium alloy is used as the matrix material, and hydroxyapatite HA powder is introduced into the ZK60 magnesium alloy matrix by friction stir processing. By refining the microstructure and uniformly distributing the hydroxyapatite particles, the mechanical properties and corrosion resistance of the magnesium matrix composite are enhanced. Through 3 passes of FSP process tests, defects such as holes and tunnels that occur during the welding process and the agglomeration problem caused by the uneven distribution of hydroxyapatite are solved, so as to achieve the purpose of uniform structure, densification and high performance, and obtain an HA / Mg composite material with excellent performance, namely a high-performance biomedical magnesium alloy.

[0024] 3. In the present invention, HA particles are reinforced into ZK60 magnesium alloy by FSP, and an HA / Mg composite material with significant antibacterial properties and excellent biocompatibility is successfully prepared. Compared with ZK60 magnesium alloy, FSP significantly refines the grain size, and the grain size is reduced from 15.6 μm to 2.1 μm. The introduced HA particles increase the calcium-phosphorus ratio to 1.61, which is close to 1.67 of human bone. In addition, the biocompatibility and bioactivity of this material make it an ideal choice to replace traditional metal implants, which helps to reduce the incompatibility risk between the implant and the host tissue and avoid the need for secondary surgery to remove the implant, thereby reducing the economic burden and medical risk of patients.

[0025] 3. The antibacterial rate of the high-performance biomedical magnesium alloy prepared by the present invention is 77.2%, and the antibacterial rate is significantly improved, making it an excellent material for orthopedic implants, thereby enhancing its potential as an antibacterial orthopedic implant.

[0026] 4. The high-performance biomedical magnesium alloy prepared by the present invention exhibits optimal mechanical properties. Its microhardness can reach 88.2 HV, the tensile strength is 168.77 MPa, the elongation is 5.26%, and the elastic modulus is 32.08 GPa, which is extremely close to the properties of human bone. The fracture morphology analysis shows that the dimples of the composite material under this process are small, numerous and evenly distributed, indicating its good toughness and plasticity. Moreover, this material has excellent wear resistance. The uniformly distributed HA particles play a lubricating role during the friction process, reducing the wear of the material. The HA powder in the composite material can significantly improve the corrosion resistance in the form of increasing the number of active sites on the material surface. The corrosion resistance of the HA / Mg composite material under the S1500-3 pass process reaches 1898 Ω·cm 2 。

[0027] Note that the description of these effects does not preclude the existence of other effects. One embodiment of the present invention does not necessarily have all of the above effects. Effects other than the above can be obviously seen and extracted from the descriptions in the specification, drawings, claims, etc. Brief Description of the Drawings

[0028] Figure 1 is the welding process flow chart for preparing the high-performance biomedical magnesium alloy of the present invention, where Figure 1 (a) is a schematic diagram of grooving, Figure 1 (b) is a schematic diagram of powder filling, Figure 1 (c) is a schematic diagram of powder sealing, Figure 1 (d) is a schematic diagram of friction stir processing;

[0029] Figure 2 is the macroscopic morphology of the welding process for preparing the high-performance biomedical magnesium alloy in Example 1 of the present invention;

[0030] Figure 3 are the macroscopic morphology structure diagram and the microscopic structure diagram of the weld nugget zone of the HA / Mg composite material prepared in Example 1, where Figure 3 (a) is the macroscopic morphology of the welded joint, Figure 3 (b) is the microscopic morphology of the base metal BM, Figure 3 (c) is the microscopic morphology of the heat affected zone HAZ, Figure 3 (d) is the microscopic morphology of the thermo-mechanically affected zone TMAZ, Figure 3 (e) is the microscopic morphology of the weld nugget zone SZ;

[0031] Figure 4 is the tensile fracture morphology diagram of the HA / Mg composite material prepared in Example 1;

[0032] Figure 5 is the Nyquist diagram of the HA / Mg composite material prepared in Example 1;

[0033] Figure 6 The macroscopic morphology of the HA / Mg composite material prepared in Example 2 and the microstructure of the weld nugget zone, where Figure 6 (a) is the macroscopic morphology of the welded joint, Figure 6 (b) is the microscopic morphology of the base metal BM, Figure 6 (c) is the microscopic morphology of the heat affected zone HAZ, Figure 6 (d) is the microscopic morphology of the thermo-mechanically affected zone TMAZ, Figure 6 (e) is the microscopic morphology of the weld nugget zone SZ;

[0034] Figure 7 is the tensile fracture morphology of the HA / Mg composite material prepared in Example 2;

[0035] Figure 8 The macroscopic morphology of the HA / Mg composite material prepared in Example 3 and the microstructure of the weld nugget zone, where Figure 8 (a) is the macroscopic morphology of the welded joint, Figure 8 (b) is the microscopic morphology of the base metal BM, Figure 8 (c) is the microscopic morphology of the heat affected zone HAZ, Figure 8 (d) is the microscopic morphology of the thermo-mechanically affected zone TMAZ, Figure 8 (e) is the microscopic morphology of the weld nugget zone SZ;

[0036] Figure 9 is the tensile fracture morphology of the HA / Mg composite material prepared in Example 3;

[0037] Figure 10 are the antibacterial test results of the HA / Mg composite material prepared in Example 3, where Figure 10 (a) is the result diagram of the control group, Figure 10 (b) is the result diagram of the 1300-3 antibacterial test. Detailed implementation manners

[0038] To make the above objects, features, and advantages of the present invention more obvious and understandable, the following specifically describes the specific embodiments of the present invention with reference to the accompanying drawings. Without conflict, the features in the embodiments of the present invention can be combined with each other. In addition, in the following embodiments, if there is no special description in the preparation process, they are all conventional means in the prior art, so they will not be described in detail; all raw materials used in the following embodiments are commercially available products.

[0039] Example 1

[0040] Combined with Figure 1 shown, a welding process for preparing a high-performance biomedical magnesium alloy includes the following steps:

[0041] Step S1: Machine a ZK60 magnesium alloy plate with dimensions of 180 mm × 90 mm × 6 mm, and machine a groove with a width of 3 mm, a depth of 2 mm, and a length of 180 mm at the center of the ZK60 magnesium alloy plate;

[0042] Step S2: Grind the welding surface of the magnesium alloy in Step S1, clean it with alcohol and blow it dry to make its surface clean, free of oil and oxidation layer;

[0043] Step S3: Place the base material within the machining area of the machine tool and assemble the magnesium alloy plate to be welded;

[0044] Step S4: Use nano-hydroxyapatite (HA) powder as the reinforcing phase. The average particle size of the nano-hydroxyapatite (HA) powder is 3.71 ± 0.38 μm. Fill the nano-hydroxyapatite powder evenly into the groove on the surface of the magnesium alloy plate, and perform powder sealing operation with a non-pin stirring head. The shoulder of the non-pin stirring head used is 20 mm and the downward pressure is 0.4 mm;

[0045] Step S5: After powder sealing treatment, perform friction stir processing on the surface of the powder-sealed magnesium alloy plate. The shoulder width of the pin stirring head used is 20 mm, the downward pressure of the stirring head is 4 mm, the rotational speed of the pin stirring head is set at 1500 rpm / min, the welding forward speed is 100 mm / min, the spindle tilt angle is 2.5°, and the number of welding passes is 3 to obtain the HA / Mg composite material, i.e., the high-performance biomedical magnesium alloy.

[0046] After Step S5, use a wire cutting device to cut the specimen perpendicular to the weld seam direction. After grinding, polishing, and etching, quickly clean it with clean water, dehydrate it with alcohol, and blow it dry with an electric hair dryer, and then observe its microstructure under an optical microscope and a scanning electron microscope.

[0047] Figure 2 Shown is the macroscopic morphology diagram of the high-performance biomedical magnesium alloy obtained after friction stir processing.

[0048] Figure 3 Shows the macroscopic morphology and the microscopic structure of the weld nugget zone of the HA / Mg composite material under this process, where Figure 3 (a) is the macroscopic morphology of the welded joint, Figure 3 (b) is the microscopic morphology of the base material BM, Figure 3 (c) is the microscopic morphology of the heat-affected zone HAZ, Figure 3 (d) is the microscopic morphology of the thermo-mechanically affected zone TMAZ, Figure 3 (e) is the microscopic morphology of the weld nugget zone SZ. As Figure 3As shown, in the HA / Mg composite material under the S1500-3 pass process, the grain size in the weld nugget zone is the finest and there are few defects, less fine agglomerates, and the grain shape in the weld nugget zone is similar to equiaxed grains. The S1500-3 process uses a higher spindle speed, resulting in stronger mechanical stirring and heat input in the weld nugget zone. This high energy input promotes dynamic recrystallization, significantly refining the grain size, as Figure 3 (e) shows that compared with the ZK60 magnesium alloy, FSP significantly refined the grain size of the HA / Mg, and the grain size decreased from 15.6 μm to 2.1 μm. At the same time, the strong stirring effect made the HA particles more evenly dispersed in the matrix. The grain size in the thermo-mechanically affected zone is slightly larger than that in the weld nugget zone and there are no obvious defects. The thermal and mechanical effects in the thermo-mechanically affected zone are lighter than those in the weld nugget zone, so the grain size is larger. Due to the lower mechanical stirring intensity, the distribution of HA particles in this area is less. The grain size in the heat-affected zone is slightly larger than that in the thermo-mechanically affected zone. The heat-affected zone is mainly affected by the thermal cycle and lacks mechanical stirring, resulting in a slightly larger grain size than the thermo-mechanically affected zone. At this time, the Ca / P ratio of the HA / Mg composite material is 1.61 and the hardness reaches 88.2 HV.

[0049] Figure 4 The tensile fracture morphology of the HA / Mg composite material prepared in Example 1; under the S1500-3 pass process, the dimples of the HA / Mg composite material are small, numerous and evenly distributed, and its toughness is the best. Its tensile strength is relatively high at 168.77 MPa, the elongation is 5.26%, and the elastic modulus is 32.08 GPa, which is extremely close to the elastic modulus of human bone.

[0050] Figure 5 The impedance results of the HA / Mg composite material prepared in Example 1. It can be seen from the figure that the HA powder in the HA / Mg composite material can significantly improve the corrosion resistance in the form of increasing the number of surface active sites of the material. The corrosion resistance of the HA / Mg composite material under the S1500-3 pass process reaches 1898 Ω·cm 2 。

[0051] Example 2

[0052] The specific preparation steps are the same as those in Example 1. The differences between this example and Example 1 are as follows:

[0053] In step S5, the rotation speed is set to 1700 rpm / min, the welding travel speed is 100 mm / min, the spindle tilt angle is 2.5°, and the number of welding passes is 3. Other parameters are the same as those in Example 1.

[0054] Figure 6 The macroscopic morphology and the microscopic structure of the weld nugget zone of the HA / Mg composite material prepared in Example 2, where Figure 6(a) Macroscopic morphology of the welded joint, Figure 6 (b) Microscopic morphology of the base metal BM, Figure 6 (c) Microscopic morphology of the heat affected zone HAZ, Figure 6 (d) Microscopic morphology of the thermo-mechanically affected zone TMAZ, Figure 6 (e) Microscopic morphology of the stir zone SZ. For the HA / Mg composite material under the S1700-3 pass process, the grain size in the stir zone is fine and there are few defects. The grain size in the heat affected zone is slightly larger than that in the stir zone, and the grain size in the thermo-mechanically affected zone is slightly larger than that in the stir zone. The heat affected zone is larger than the thermo-mechanically affected zone. As the spindle speed increases, the heat input correspondingly increases, which will lead to a stronger tendency for recrystallized grains to grow. This is because the increase in spindle speed will increase the frictional heat between the tool and the material, thus increasing the temperature of the material and the heat input. At a higher temperature, the diffusion rate of atoms accelerates, the recrystallization process becomes more active, and the tendency for grain growth is enhanced. The increase in heat input will also affect the distribution and agglomeration of HA particles in the material, and thus affect the microstructure and properties of the material. The Ca / P ratio of the HA / Mg composite material obtained in this example is 1.47, and the hardness reaches 81.9 HV.

[0055] Figure 7 The tensile fracture morphology of the HA / Mg composite material prepared in Example 2 is shown. At this time, the fracture surface of the tensile specimen presents a dimpled shape, and the dimples of the composite material are fine, numerous and evenly distributed. The elongation rate reaches 4.11%, and the tensile strength is 131.19 MPa.

[0056] Example 3

[0057] The specific preparation steps are the same as those in Example 1. The differences between this example and Example 1 are as follows:

[0058] In step S5, the rotation speed is set to 1300 rpm / min, the welding travel speed is 100 mm / min, the spindle tilt angle is 2.5°, the number of welding passes is 3, and other parameters are the same as those in Example 1.

[0059] Figure 8 The macroscopic morphology and the microscopic structure of the stir zone of the HA / Mg composite material prepared in Example 3 are shown. Among them, Figure 8 (a) Macroscopic morphology of the welded joint, Figure 8 (b) Microscopic morphology of the base metal BM, Figure 8 (c) Microscopic morphology of the heat affected zone HAZ, Figure 8 (d) Microscopic morphology of the thermo-mechanically affected zone TMAZ, Figure 8(e) is the microscopic morphology of the weld nugget zone SZ. For the HA / Mg composite material under the S1300-3 pass process, the grains in the weld nugget zone are slightly coarser. The grain size in the thermo-mechanically affected zone is slightly larger than that in the weld nugget zone. The grain size in the heat-affected zone is slightly larger than that in the thermo-mechanically affected zone. The grain size of the base material is the largest among the other three zones. The grains in the weld nugget zone are significantly refined after plastic deformation processing. With the change of the position of friction stir processing, the density of the banded structure formed by material flow is different. Usually, the formation of this structure is due to the formation of texture during the recrystallization of metal recovery in the rolling process, and the original strong texture will be weakened during the friction stir processing. The Ca / P ratio of the HA / Mg composite material obtained in this example is 1.43, and the hardness reaches 79HV.

[0060] Figure 9 Figure 4 shows the tensile fracture morphology of the HA / Mg composite material prepared in Example 3; for the HA / Mg composite material under the S1300-3 pass process, the dimples are small and the number is slightly less. Its tensile strength is 126.93 MPa, and the elastic modulus is 37.01 GPa, which is very close to the elastic modulus of human bone.

[0061] Figure 10 Figure 5 shows the antibacterial experimental results of the HA / Mg composite material prepared in Example 3, where Figure 10 (a) is the result diagram of the control group, Figure 10 (b) is the result diagram of the 1300-3 antibacterial test. As can be seen from Figure 10 (a), in the results of the base material sample without adding nano-hydroxyapatite, the Gram-negative Escherichia coli shows a phenomenon of large-area colony dense cluster growth within the range of the bacterial liquid coating, and the antibacterial rate is 21.5%. As can be seen from Figure 10 (b), for several groups of samples containing HA, the number of colonies is significantly reduced, which indicates that the addition of HA can improve the antibacterial ability of the Mg alloy. The antibacterial rate of the HA / Mg composite material under this process is 77.2%, indicating that the HA / Mg composite material under this process has good antibacterial performance. This is because of the role of the rotation speed and passes in the friction stir processing, which avoids the agglomeration of HA. HA is evenly dispersed in ZK60. The topological structure of HA has tiny pores and cracks, providing adsorption sites for a large number of bacteria colonies, and playing the role of antibacterial and absorbing colonies.

[0062] The welding process of the high-performance biomedical magnesium alloy described in the present invention uses a non-pin stirring head to seal hydroxyapatite powder into the magnesium alloy matrix, and a pin stirring head is used for three-pass friction stir processing, so that the hydroxyapatite powder is evenly dispersed in the magnesium alloy matrix. By means of friction stir processing, the present invention evenly disperses the hydroxyapatite powder in the magnesium alloy matrix, which can greatly improve the biological properties of the magnesium alloy and obtain a biomedical magnesium alloy HA / Mg composite material with excellent performance.

[0063] It should be understood that although this specification is described according to various embodiments, not every embodiment contains only an independent technical solution. This narrative way of the specification is only for clarity. Those skilled in the art should regard the specification as a whole, and the technical solutions in each embodiment can also be appropriately combined to form other embodiments that can be understood by those skilled in the art.

[0064] The series of detailed descriptions listed above are only specific descriptions of the feasible embodiments of the present invention, and they are not intended to limit the protection scope of the present invention. Any equivalent embodiments or changes made without departing from the technical spirit of the present invention should be included in the protection scope of the present invention.

Claims

1. A welding process for high-performance biomedical magnesium alloy, characterized in that: The following steps are involved: Step S1: processing a magnesium alloy plate and forming grooves on the surface of the magnesium alloy plate; Step S2: polish the magnesium alloy welding surface in step S1, clean it with alcohol and blow it dry, so that the surface is clean, free of oil and oxide layer; Step S3: placing the magnesium alloy sheet to be welded in the machining area of ​​the machine tool for assembly; Step S4: using nano-hydroxyapatite HA powder as a reinforcing phase, uniformly filling the nano-hydroxyapatite HA powder into the grooves on the surface of the magnesium alloy plate, and performing a powder sealing operation using a needle-free stirring head; Step S5: performing friction stir processing on the surface of the magnesium alloy plate after powder sealing to obtain a HA / Mg composite material, namely a high-performance biomedical magnesium alloy.

2. The welding process of high-performance biomedical magnesium alloy according to claim 1, characterized in that: In the step S1, the grade of the magnesium alloy plate is ZK60, and the size of the magnesium alloy plate is 180 mm×90 mm×6 mm.

3. The welding process of the high performance biomedical magnesium alloy according to claim 2, characterized in that: In the step S1, a groove with a length of 180 mm, a width of 3 mm and a depth of 2 mm is processed at the center position of the surface of the magnesium alloy plate.

4. The welding process of the high performance biomedical magnesium alloy according to claim 1, characterized in that: The average particle size of the nano-hydroxyapatite HA powder in step S4 is 3.71±0.38 μm.

5. The welding process of high performance biomedical magnesium alloy according to claim 1, characterized in that: In step S4, the shoulder width of the needle-free stirring head is 20 mm, and the downward pressure of the stirring head is 0.4 mm.

6. The welding process of the high performance biomedical magnesium alloy according to claim 1, characterized in that: In the step S5, the rotation speed of the welding tool in the friction stir processing is 1300-1700 rpm / min, the welding speed is 100 mm / min, the spindle inclination angle is 2.5°, and the number of welding passes is 3.

7. The welding process of the high performance biomedical magnesium alloy according to claim 6, characterized in that: The rotation speed of the welding tool in the friction stir processing in step S5 is 1500 rpm / min.

8. The welding process of high performance biomedical magnesium alloy according to claim 1, characterized in that: The welding tool for the friction stir processing in step S5 is a needle stirring head, the shoulder width of the stirring head is 20 mm, and the downward pressure of the stirring head is 4 mm.

9. A high-performance biomedical magnesium alloy, characterized in that: The high-performance biomedical magnesium alloy is prepared by the welding process according to any one of claims 1 to 8.

10. The high performance biomedical magnesium alloy according to claim 9, characterized in that: The high-performance biomedical magnesium alloy has a grain size of 2.1 μm, a calcium-phosphorus ratio of 1.61, a hardness of 88.2 HV, a tensile strength of 168.77 MPa, an elongation of 5.26%, an elastic modulus of 32.08 GPa, and a corrosion resistance of 1898 Ω.cm 2 .

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