CN114012234B - Vacuum diffusion welding method for dissimilar metals of titanium alloy and magnesium alloy - Google Patents
Vacuum diffusion welding method for dissimilar metals of titanium alloy and magnesium alloy Download PDFInfo
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- CN114012234B CN114012234B CN202111554670.4A CN202111554670A CN114012234B CN 114012234 B CN114012234 B CN 114012234B CN 202111554670 A CN202111554670 A CN 202111554670A CN 114012234 B CN114012234 B CN 114012234B
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- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 68
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- 238000000034 method Methods 0.000 title claims abstract description 34
- 229910052751 metal Inorganic materials 0.000 title claims abstract description 22
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- 150000002739 metals Chemical class 0.000 title claims abstract description 12
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 10
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- 229910052727 yttrium Inorganic materials 0.000 claims description 10
- 229910000914 Mn alloy Inorganic materials 0.000 claims description 8
- 238000010438 heat treatment Methods 0.000 claims description 7
- 238000012360 testing method Methods 0.000 claims description 7
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- 239000006104 solid solution Substances 0.000 claims 1
- 239000000243 solution Substances 0.000 claims 1
- 239000010936 titanium Substances 0.000 abstract description 13
- 230000007704 transition Effects 0.000 abstract description 11
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Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/001—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating by extrusion or drawing
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/14—Preventing or minimising gas access, or using protective gases or vacuum during welding
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/22—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating taking account of the properties of the materials to be welded
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/24—Preliminary treatment
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K2103/00—Materials to be soldered, welded or cut
- B23K2103/18—Dissimilar materials
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Arc Welding In General (AREA)
Abstract
The invention discloses a vacuum diffusion welding method of dissimilar metals of titanium alloy and magnesium alloy, which has the advantages that a certain amount of Mn element is added into the magnesium alloy, tiMn and the like are generated on a diffusion interface of the magnesium alloy and the titanium alloy with Ti, the effect of connecting a transition layer is achieved, and the problem that Mg-Ti atoms are not mutually soluble and can not generate compound phases is solved. The surface to be welded is selected to be perpendicular to the deformation direction of the magnesium alloy, the Mg-RE reinforcing phase in the alloy is stretched along the metal flow direction and distributed in a fiber shape, the end of the similar diffusion interface is enhanced to be tightly riveted into the diffusion transition layer like a rivet, and the connection strength of the magnesium alloy and the diffusion transition layer is improved. The vacuum diffusion welding method has good welding quality, the tensile strength of the vacuum diffusion welding method is as high as 324.15MPa, the elongation is 4.7%, the shear strength of the vacuum diffusion welding method is 121.77MPa, the obtained alloy welding joint has high bonding strength, and the vacuum diffusion welding method can be widely applied to welding between magnesium alloy and titanium alloy.
Description
Technical Field
The invention belongs to the field of metal material welding, and relates to a vacuum diffusion welding method for dissimilar metals of titanium alloy and magnesium alloy.
Background
The lightweight development of weaponry and aerospace equipment is a major strategic requirement of national safety, and the application of lightweight structural members can not only improve the effective load and the maneuvering performance of flight equipment and weaponry, but also produce objective technical and economic benefits. The titanium alloy has the advantages of high strength, good corrosion resistance and good heat resistance. The magnesium alloy has the advantages of low density, high specific strength, good damping effect and the like, and has great application potential in the field of aerospace. Titanium alloy and magnesium alloy play an important role in the light weight manufacturing of weaponry and aerospace equipment, and titanium alloy structural component and magnesium alloy structural component mainly adopt the form of bolted connection in the assembly process of weaponry and aerospace equipment at present, and bolted connection needs trompil, overlap joint each other or add auxiliary connecting plate, not only weakens the component cross-section but also increases the complexity of structure, does not utilize the reliability and the lightweight of structure. The problem can be solved by preparing the titanium/magnesium dissimilar metal integrated (integral) structural component, the key stress part of the structural component is made of titanium alloy, and the non-key part of the structural component is made of magnesium alloy, so that the titanium/magnesium dissimilar metal integrated (integral) structural component can meet the use requirement and can further realize the light weight of the structural component.
Because the difference between the physical and chemical properties of the magnesium alloy and the titanium alloy is large, particularly, the melting point of titanium is almost 3 times of that of magnesium, the magnesium alloy and the titanium alloy cannot be reliably connected by adopting fusion welding. Meanwhile, the two elements of Mg and Ti are not mutually soluble in a liquid phase and a solid phase, and cannot form a compound phase, so that the basic conditions of diffusion welding cannot be met. In addition, the main strengthening forms of the wrought magnesium alloy are fine grain strengthening and work hardening, if the welding temperature is too high, the crystal grains of the magnesium alloy base material are seriously grown in the welding process, and the connection performance of a welding joint is further influenced. Therefore, the direct contact diffusion welding of magnesium alloy and titanium alloy is difficult to realize reliable connection. The method for diffusion welding magnesium alloy and titanium alloy disclosed in the prior art mostly adopts aluminum foil as an intermediate layer to weld magnesium alloy and titanium alloy, but the aluminum foil and the magnesium alloy can be welded at the welding temperature in the processing processEutectic reaction to generate hard and brittle phase Mg 17 Al 12 Hard and brittle metallic compound Mg 17 Al 12 The appearance of phases is not favorable for obtaining a stable welding joint with excellent performance. Therefore, it is important to explore a welding method for dissimilar metals of titanium alloy and magnesium alloy to realize high-strength connection between the titanium alloy and the magnesium alloy.
Disclosure of Invention
In order to overcome the defects of the prior art, one of the purposes of the invention is to provide a vacuum diffusion welding method for dissimilar metals of titanium alloy and magnesium alloy, which can improve the mechanical property of a welding joint of the titanium alloy and the magnesium alloy.
One of the purposes of the invention is realized by adopting the following technical scheme:
a vacuum diffusion welding method for dissimilar metals of titanium alloy and magnesium alloy comprises the following steps:
(1) Polishing, cleaning and drying the surfaces to be welded of the titanium alloy sample and the magnesium alloy sample;
(2) Stacking the surfaces to be welded of the titanium alloy sample and the magnesium alloy sample treated in the step (1) in a mold, then placing the mold between an upper pressure head and a lower pressure head of a hot-pressing furnace, closing the hot-pressing furnace and vacuumizing;
(3) Applying pre-pressure to the sample to be welded in the step (2), heating to a set temperature, boosting to welding pressure, and entering a heat preservation and pressure maintaining stage; and after the pressure is relieved and the temperature is reduced, taking out the die to obtain the titanium alloy and magnesium alloy welded composite structural member.
Further, the heating rate of the step (3) is 5-10 ℃/min, and the set temperature is 430-520 ℃.
Further, the pre-pressure in the step (3) is 1-10 MPa, the welding pressure is 10-30 MPa, and the heat preservation and pressure maintaining time is 30-180 min.
Further, the temperature reduction process in the step (3) is to reduce the temperature to below 100 ℃ at a rate of 1-5 ℃/min.
Further, the vacuum degree in the step (2) is 5 multiplied by 10 -1 Pa or less.
Further, the roughness of the polished in the step (1) is 0.8-3 μm.
Further, the magnesium alloy is a plastic deformation Mg-RE-X-Mn alloy, wherein the content of Mn element accounts for 0.5-1.5 percent by weight of the alloy; RE is selected from one to three of Y, gd, ce, nd and Sc, and the content of RE element is 3-8 times of that of Mn element; x is selected from one or two of Zn and Zr, and the content of X represents element is 0.5-2 times of the content of Mn element.
Further, the preparation of the magnesium alloy sample comprises the following steps: carrying out solution treatment on the Mg-RE-X-Mn alloy, wherein the process comprises the steps of firstly preserving heat for 8-12 h at 500-520 ℃, then preserving heat for 6-10 h at 400-420 ℃, and carrying out water quenching in hot water at 80-100 ℃; heating the Mg-RE-X-Mn alloy subjected to solution treatment to 420-440 ℃, preserving heat for 30min, and performing forging, extrusion or rolling treatment to obtain the deformed Mg-RE-X-Mn alloy.
Further, the surface to be welded in the step (1) is selected to be perpendicular to the deformation direction of the magnesium alloy.
Compared with the prior art, the invention has the beneficial effects that:
the invention provides a vacuum diffusion welding method of dissimilar metals of titanium alloy and magnesium alloy, which is characterized in that a certain amount of Mn element is added into the magnesium alloy to generate TiMn and Ti with Ti on a diffusion interface of the magnesium alloy and the titanium alloy 2 Mn and the like play a role in connecting the transition layer, and the problem that Mg-Ti atoms are not mutually soluble and can not generate compound phases is solved. The surface to be welded is selected to be perpendicular to the deformation direction of the magnesium alloy, the Mg-RE reinforcing phase in the alloy is stretched along the metal flow direction and distributed in a fiber shape, the end of the Mg-RE reinforcing similar diffusion interface is tightly riveted into the diffusion transition layer like a rivet, and the connection strength of the magnesium alloy and the diffusion transition layer is improved. When a sample is welded, the sample to be welded is fixed by the die, so that the thermal expansion deformation of the magnesium alloy can be inhibited, the difference of the thermal expansion sizes of the magnesium alloy and the titanium alloy is reduced, and the interface welding stress is favorably eliminated; after the heat preservation and pressure preservation are finished in the welding process, the sample is cooled at a lower cooling rate, so that the thermal stress caused by uneven expansion caused by heat and contraction caused by cold is reduced, and the mechanical property of the welding joint of the titanium alloy and the magnesium alloy is improved. The vacuum diffusion welding method has good welding quality, and the obtained alloy welding joint has high bonding strength and energyCan be widely applied to the welding between the magnesium alloy and the titanium alloy.
Drawings
FIG. 1 is a schematic view showing an assembly structure for diffusion welding of a titanium alloy and a magnesium alloy in examples 1 to 13 of the present invention;
FIG. 2 is a metallographic structure diagram of a weld joint according to example 3 of the present invention;
FIG. 3 is a TEM element distribution diagram of a diffusion interface in example 3 of the present invention;
FIG. 4 is a scanning electron microscope image of a welded joint in accordance with example 3 of the present invention;
FIG. 5 is a tensile test pattern of a weld joint of the present invention: wherein, 1# is a test sample to be tested by the welding joint of the embodiment 3, 2# is a test sample for completing the tensile test of the welding joint of the embodiment 3, and 3# is a test sample for completing the tensile test of the welding joint of the embodiment 10;
FIG. 6 is a scanning electron microscope topography of tensile fractures of weld joints in accordance with example 3 of the present invention;
in the figure: 1. an upper pressure head; 2. a magnesium alloy; 3. a titanium alloy; 4. a lower gasket; 5. pressing the column upwards; 6. an upper gasket; 7. a mold sleeve; 8. pressing the column downwards; 9. and (4) pressing the head down.
Detailed Description
The present invention is further described with reference to the accompanying drawings and the detailed description, and it should be noted that, in the case of no conflict, any combination between the embodiments or technical features described below may form a new embodiment.
Example 1
A vacuum diffusion welding method of dissimilar metals of titanium alloy and magnesium alloy comprises the following steps;
(1) Pretreatment of a surface to be welded: grinding the surfaces to be welded of the TC4 titanium alloy and the Mg-7Gd-4Y-1Zn-1Mn magnesium alloy (the mass ratio of Gd, Y, zn and Mn is 7.
(2) And (2) orderly stacking the titanium alloy and magnesium alloy to-be-welded surfaces of the samples after the step of cleaning the to-be-welded surfaces, assembling the stacked samples in a high-temperature alloy die, and spraying a boron carbide coating on the contact part of the inner cavity of the die and the samples so as to remove the samples after welding (as shown in figure 1). Placing the mould with the welding sample in the middle of the upper and lower pressure heads of the vacuum hot-pressing furnace, keeping the axial alignment of the mould and the pressure heads, closing the door of the vacuum hot-pressing furnace, and vacuumizing to 5 x 10 -1 And (2) applying 10MPa of pre-pressure to the sample to be welded by an upper pressure head of the vacuum furnace, heating to the welding temperature of 460 ℃ at the heating rate of 10 ℃/min, adjusting the welding pressure to 20MPa, keeping the temperature and the pressure for 120min, releasing the pressure after the heat and the pressure are kept, slowly cooling to the temperature below 100 ℃ along with the furnace at the speed of 3 ℃/min, and taking out the die to obtain the welding composite structural member of the TC4 titanium alloy and the Mg-7Gd-4Y-1Zn-1Mn magnesium alloy.
Example 2
Example 2 differs from example 1 in that: the TC4 titanium alloy obtained in the step (1) was changed to a TA2 titanium alloy, and the procedure was otherwise the same as in example 1.
Example 3
Example 3 differs from example 1 in that: adjusting the Mg-7Gd-4Y-1Zn-1Mn magnesium alloy in the step (1) to Mg-7Gd-4Y-1Zn-0.1Mn magnesium alloy (the mass ratio of Gd, Y, zn and Mn is 7.
Example 4
Example 4 differs from example 1 in that: the Mg-7Gd-4Y-1Zn-1Mn magnesium alloy in step (1) was adjusted to Mg-7Gd-4Y-1Zn-0.5Mn magnesium alloy (Gd, Y, zn, mn in a mass ratio of 7.
Example 5
Example 5 differs from example 1 in that: the welding temperature in the step (2) was adjusted to 490 ℃ and the same as in example 1.
Example 6
Example 6 differs from example 1 in that: the Mg-7Gd-4Y-1Zn-1Mn magnesium alloy in step (1) was adjusted to Mg-7Gd-4Y-1Zn-1.5Mn magnesium alloy (Gd, Y, zn, mn in a mass ratio of 7.
Example 7
Example 7 differs from example 1 in that: the Mg-7Gd-4Y-1Zn-1Mn magnesium alloy in step (1) was adjusted to Mg-8Gd-3Y-0.5Zr-1Mn magnesium alloy (the mass ratio of Gd, Y, zr, mn was 8, 3.
Example 8
Example 8 differs from example 1 in that: the TC4 titanium alloy obtained in the step (1) was adjusted to a TA2 titanium alloy, and the welding temperature in the step (2) was adjusted to 490 ℃ in the same manner as in example 1.
Example 9
Example 9 differs from example 1 in that: the TC4 titanium alloy in the step (1) was adjusted to TA2 titanium alloy, the Mg-7Gd-4Y-1Zn-1Mn magnesium alloy was adjusted to Mg-8Gd-3Y-0.5Zr-1Mn magnesium alloy (Gd, Y, zr, mn mass ratio of 8.
Example 10
Example 10 differs from example 1 in that: the welding temperature in the step (2) was adjusted to 520 ℃ and the same as in example 1 was repeated.
Example 11
Example 11 differs from example 1 in that: the Mg-7Gd-4Y-1Zn-1Mn magnesium alloy in step (1) was adjusted to Mg-8Gd-3Y-0.5Zr-1Mn magnesium alloy (Gd, Y, zr, mn in a mass ratio of 8.
Example 12
Example 12 differs from example 1 in that: the procedure of example 1 was repeated except that the TC4 titanium alloy in step (1) was changed to the TA2 titanium alloy and the welding temperature in step (2) was changed to 520 ℃.
Example 13
Example 13 differs from example 1 in that: the TC4 titanium alloy in the step (1) was adjusted to TA2 titanium alloy, the Mg-7Gd-4Y-1Zn-1Mn magnesium alloy was adjusted to Mg-8Gd-3Y-0.5Zr-1Mn magnesium alloy (Gd, Y, zr, mn mass ratio of 8.
Comparative example 1
Comparative example 1 differs from example 1 in that: and (3) orderly stacking and adjusting the surfaces to be welded of the titanium alloy (TC 4) and the magnesium alloy (AZ 31B) in the step (2) to be aluminum foils as intermediate layers, placing the aluminum foils between the magnesium alloy and the titanium alloy, and stacking and assembling the aluminum foils in a high-temperature alloy die. The rest is the same as in example 1.
Experimental example 1
Mechanical property test of titanium alloy/magnesium alloy welding joint
The welded joints of the titanium alloy/magnesium alloy welded composite structural member obtained in the embodiments 1 to 13 of the invention are subjected to performance tests, and the test process refers to the national standard (GB/T228.1-2010, metal material tensile test: room temperature test method). The results are shown in Table 1.
TABLE 1
As can be seen from Table 1, the welding joints of the titanium/magnesium alloy welding composite structural member obtained in the embodiments 1 to 13 have good mechanical properties, wherein the tensile strength is as high as 258.07-324.15MPa, the elongation is 2.1% -9.1%, the shear strength is 88.3-121.77MPa, and the aluminum foil is adopted as the diffusion intermediate layer for welding in the comparative example 1, so that the mechanical properties of the obtained welding joints are weaker than those of the welding joints obtained in the embodiment 1. The method provided by the invention has the advantage that the welding joint of the titanium alloy and the magnesium alloy has higher bonding strength.
FIG. 2 is a metallographic structure of a weld joint in example 3 of the present invention, and FIGS. 3 and 4 are TEM elements of a diffusion interface in example 3 of the present invention, respectivelyLayout and welding joint scanning electron microscope tissue diagrams, and the diagram shows that Mn element is added into magnesium alloy to enrich at a welding interface and generate TiMn and Ti with Ti 2 Mn and the like play a role in connecting the transition layer, solve the problem that Mg-Ti atoms are not mutually soluble and can not generate a compound phase, and realize the reliable connection of the titanium alloy and the magnesium alloy; meanwhile, the magnesium alloy processed by plastic processing is utilized to lead the Mg-RE strengthening phase in the magnesium alloy to be stretched along the metal flowing direction and distributed in a fiber shape, so as to form a state of being distributed perpendicular to a welding interface, the end of the Mg-RE strengthening similar diffusion interface is tightly riveted into the diffusion transition layer like a rivet, the other end of the Mg-RE strengthening similar diffusion interface is deeply embedded into the magnesium alloy to be tightly combined with the magnesium alloy, the connecting strength of the magnesium alloy and the diffusion transition layer is increased, and the high-strength titanium alloy and magnesium alloy dissimilar metal welding joint is obtained. FIGS. 5 and 6 are respectively a tensile test pattern of a welded joint and a scanning electron microscope image of a tensile fracture of a welded joint in example 3.
The welding method of the invention is adopted for welding, and the result shows that the temperature has great influence on the welding joint. When the temperature is lower, mn element is not sufficiently diffused, the connection performance of a transition layer formed at a welding interface is poorer, when a welding joint is subjected to tensile test, the welding interface is fractured, the tensile strength is about 88 percent of that of a magnesium alloy base metal, and the fracture elongation is lower. When the welding temperature is increased to 490 ℃, more Mn elements are enriched at the welding interface, the formed TiMn transition layer has higher connection strength, the tensile strength of the welding joint is close to the strength of the magnesium alloy base metal, and the fracture is still at the welding interface. But there was a large amount of tear tape in the fracture morphology. When the welding temperature is raised to 520 ℃, the tensile strength of the welding joint is the strength of the magnesium alloy base metal, and tensile fracture occurs on the magnesium alloy base metal, which is caused by the fact that the performance of the magnesium alloy base metal is reduced due to the fact that the magnesium alloy crystal grains grow and the reinforcing phase is coarsened due to overhigh welding temperature.
According to the invention, the titanium alloy and the magnesium alloy are assembled in the high-temperature alloy die after being superposed, the restriction of the die can restrict the thermal expansion size of the magnesium alloy, the difference of the thermal expansion sizes of the magnesium alloy and the titanium alloy is reduced, the interface welding stress is favorably eliminated, and the mechanical property of the welding joint of the titanium alloy and the magnesium alloy is improved. And because the expansion coefficients of the magnesium alloy and the titanium alloy are different, the invention adopts a slower cooling speed, reduces the thermal stress caused by uneven thermal expansion and cold contraction, and realizes the reliability of the welding joint of the magnesium alloy and the titanium alloy under the cooperation of restraining the thermal expansion degree of the magnesium alloy by depending on a high-temperature alloy die with higher thermal stability and rigidity in the adding process.
The above embodiments are only preferred embodiments of the present invention, and the protection scope of the present invention is not limited thereby, and any insubstantial changes and substitutions made by those skilled in the art based on the present invention are within the protection scope of the present invention.
Claims (8)
1. A vacuum diffusion welding method for dissimilar metals of titanium alloy and magnesium alloy is characterized by comprising the following steps:
(1) Polishing, cleaning and drying the surfaces to be welded of the titanium alloy sample and the magnesium alloy sample;
(2) Stacking the titanium alloy test sample treated in the step (1) and the to-be-welded surface of the magnesium alloy test sample in a mold, then placing the mold between an upper pressure head and a lower pressure head of a hot pressing furnace, closing the hot pressing furnace and vacuumizing;
(3) Applying pre-pressure to the sample to be welded in the step (2), heating to a set temperature, boosting to welding pressure, and entering a heat preservation and pressure maintaining stage; releasing the pressure and cooling after the completion, and taking out the die to obtain a welded composite structural member of the titanium alloy and the magnesium alloy;
the magnesium alloy is a plastic deformation Mg-RE-X-Mn alloy, wherein the content of Mn element accounts for 0.5 to 1.5 wt% of the alloy; RE is selected from one to three of Y, gd, ce, nd and Sc, and the content of RE element is 3~8 times of the content of Mn element; x is selected from one or two of Zn and Zr, and the content of the X representing element is 0.5 to 2 times of the content of the Mn element.
2. The vacuum diffusion welding method of a dissimilar metal of a titanium alloy and a magnesium alloy according to claim 1, wherein the temperature rise rate in the step (3) is 5 to 10 ℃/min, and the set temperature is 430 to 520 ℃.
3. The vacuum diffusion welding method of a titanium alloy and a magnesium alloy dissimilar metal according to claim 1, wherein in the step (3), the pre-pressure is 1 to 10MPa, the welding pressure is 10 to 30MPa, and the heat preservation and pressure maintaining time is 30 to 180min.
4. The method for vacuum diffusion welding of dissimilar metals of titanium alloy and magnesium alloy according to claim 1, wherein the step (3) of cooling is carried out at a rate of 1~5 ℃/min to a temperature below 100 ℃.
5. The method for vacuum diffusion welding a dissimilar metal of a titanium alloy and a magnesium alloy according to claim 1, wherein said step (2) is performed with a degree of vacuum of 5 x 10 -1 Pa or less.
6. The vacuum diffusion welding method of a dissimilar metal of a titanium alloy and a magnesium alloy according to claim 1, wherein the roughness of the grinding in the step (1) is 0.8 to 3 μm.
7. The vacuum diffusion welding method of a dissimilar metal of a titanium alloy and a magnesium alloy according to claim 1, wherein the preparation of the magnesium alloy sample comprises the steps of: carrying out solid solution treatment on the Mg-RE-X-Mn alloy, wherein the process comprises the steps of firstly, preserving heat for 8-12h at 500-520 ℃, then preserving heat for 6-10h at 400-420 ℃, and carrying out water quenching in hot water at 80-100 ℃; heating the Mg-RE-X-Mn alloy subjected to the solution treatment to 420-440 ℃, preserving heat for 30min, and performing forging, extrusion or rolling treatment to obtain the variable-form Mg-RE-X-Mn alloy.
8. A vacuum diffusion welding method of dissimilar metals of titanium alloy and magnesium alloy according to claim 1, wherein the welding surfaces in step (1) are selected perpendicular to the deformation direction of the magnesium alloy.
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