Method for improving work hardening capacity of TiZrVNbAl series light high-entropy alloy

Abstract

The invention relates to a method for improving the work hardening capacity of a TiZrVNbAl series light high-entropy alloy, and belongs to the technical field of metal material additive manufacturing. The method comprises the steps that firstly, a high-entropy alloy bar is obtained through smelting, then high-entropy alloy powder is prepared through a plasma rotating electrode atomization method, then two different laser additive manufacturing parameters are adopted for alternate switching printing, a heterostructure with coarse grain layers and fine grain layers arranged alternately is obtained, and finally solution treatment is conducted. Due to the fact that the mechanical properties of the two adjacent layers are different, uneven plastic strain can be generated during deformation, then strain gradient is formed near an interface, a large number of geometric necessary dislocations are generated, the remarkable heterogeneous strengthening effect is achieved, the strong plasticity of the TiZrVNbAl series light-weight high-entropy alloy is effectively improved, and meanwhile the work hardening capacity of the TiZrVNbAl series light-weight high-entropy alloy can be obviously improved.

Description

Technical Field

[0001] This invention relates to a method for improving the work hardening capability of TiZrVNbAl-based lightweight high-entropy alloys, belonging to the field of additive manufacturing technology for metallic materials. Background Technology

[0002] TiZrVNbAl alloys are typical lightweight high-entropy alloys composed of various highly active elements, exhibiting excellent energy release characteristics, strong plasticity, high-temperature resistance, and corrosion resistance, showing broad application prospects in aerospace, defense, and shipbuilding. However, due to insufficient work hardening capacity, TiZrVNbAl lightweight high-entropy alloys are prone to localized deformation during deformation, which may lead to fracture failure under high overload, severely hindering their engineering applications. To improve their work hardening capacity, researchers typically employ deformation heat treatment to refine grains or incomplete recrystallization to introduce heterogeneous structures, but the practical results are not ideal. On the one hand, TiZrVNbAl lightweight high-entropy alloys have high grain deformation resistance and rapid growth rate at high temperatures, making grain refinement difficult for large-sized components, while also incurring the problem of increased costs due to multi-heat forging; on the other hand, the uneven cooling rate and deformation degree in different parts of large-sized components make it difficult to control heterogeneous structures.

[0003] In recent years, the development of laser additive manufacturing technology has provided a new approach to improve the work hardening capability of TiZrVNbAl-based lightweight high-entropy alloys. Laser additive manufacturing boasts extremely high cooling rates, enabling significant grain refinement. Furthermore, through multi-material delivery systems, in-situ alloying, and process parameter control, it can prepare various heterogeneous structural materials ranging from macroscopic to microscopic, and from continuous gradients to discrete mosaics. However, for single-component powders, constructing heterogeneous structural materials requires establishing a precise relationship model between "process parameters, melt pool kinetics, microstructure, and mechanical properties," making process control extremely complex and posing a significant challenge. Summary of the Invention

[0004] In view of this, the purpose of this invention is to provide a method for improving the work hardening capability of TiZrVNbAl-based lightweight high-entropy alloys. This method employs direct laser deposition technology, using TiZrVNbAl-based lightweight high-entropy alloys as the deposition object. By using alternating laser process parameters to control the grain size and morphology of different deposition layers, grain refinement and heterogeneous deformation-induced strengthening are achieved, significantly improving the alloy's uniform deformation capability and work hardening capability, demonstrating promising application prospects.

[0005] To achieve the above objectives, the technical solution of the present invention is as follows.

[0006] A method for improving the work hardening ability of TiZrVNbAl-based lightweight high-entropy alloys, the method comprising the following steps: (1) Weigh the raw materials of each element in metal blocks according to the composition and proportion of the TiZrVNbAl system lightweight high-entropy alloy; (2) The raw materials are added to a suspended melting water-cooled copper crucible for melting to obtain alloy ingots and process them into high-entropy alloy rods; (3) The high-entropy alloy rod is made into a consumable electrode, and the high-entropy alloy powder is prepared by plasma rotating electrode atomization method and the printing powder is obtained by sieving. (4) After drying the printing powder, laser additive manufacturing printing is performed to obtain a high-entropy alloy block; (5) The high-entropy alloy block was subjected to solid solution treatment to obtain a TiZrVNbAl system lightweight high-entropy alloy with high work hardening ability; In step (4), two different laser additive manufacturing parameters are used alternately for printing to obtain a heterostructure with alternating coarse and fine grain layers. The average grain size of the coarse grain layer is 40~80 μm, and the thickness of each layer is 250~1500 μm. The average grain size of the fine grain layer is 10~20 μm, and the thickness of each layer is 250~1500 μm. Preferably, in step (1), the TiZrVNbAl lightweight high-entropy alloy is denoted as Ti by atomic ratio. a Zr b V c Nb d Al e M f M is one or more of Al, Hf, Cr, Fe, Mg, Be, Li, Mo, Co, Ni, Si, B, O, and N; wherein 25 < a < 65, 0 < b ≤ 55, 0 < c < 25, 0 < d < 35, 0 < e < 20, 0 < f < 10, and a + b + c + d + e + f = 100. More preferably, 50 ≤ a ≤ 60, 15 ≤ b ≤ 25, 15 ≤ c ≤ 20, 15 ≤ d ≤ 25, 3 ≤ e ≤ 7, and 4 ≤ f ≤ 8.

[0007] Preferably, in step (2), the arc melting current during melting is 200~1000 A and the magnetic stirring current is 2~10 A.

[0008] Preferably, in step (2), the number of melting times is more than 5.

[0009] Preferably, in step (2), the diameter of the high-entropy alloy rod is 30~70 mm.

[0010] Preferably, in step (3), the rotational speed of the electrode rod in the plasma rotating electrode atomization method is 10,000 to 30,000 revolutions per minute.

[0011] Preferably, in step (3), the particle size of the printing powder is 45~75 μm and 75~150 μm.

[0012] Preferably, in step (4), the first laser additive manufacturing parameters are: laser power of 1000~1200 W, scanning speed of 12~15 mm / s, powder feeding rate of 10~15 g / min, overlap distance of 1.2~1.4 mm, layer height of 0.2~0.4 mm, and powder particle size of 75~150 μm used for printing; the second laser additive manufacturing parameters are: laser power of 1200~1500 W, scanning speed of 5~8 mm / s, powder feeding rate of 10~15 g / min, overlap distance of 0.8~1 mm, layer height of 0.2~0.4 mm, and powder particle size of 45~75 μm used for printing. More preferably, the laser energy density of the first laser additive manufacturing parameters is 120~250 J / mm². 3 The laser energy density for the second type of laser additive manufacturing parameters is 400~1000 J / mm². 3 ·s.

[0013] Preferably, in step (4), the thickness of each layer of the coarse grain layer is 250~350 μm, and the thickness of each layer of the fine grain layer is 250~350 μm.

[0014] Preferably, in step (4), a high-entropy alloy block with a size of 30~50×30~50×30~50 mm is printed on a TC4 titanium alloy substrate whose surface has been polished.

[0015] Preferably, in step (5), the solution treatment allows the precipitated phase during the printing process to dissolve back without affecting the grain size. More preferably, the solution treatment temperature is 900~1000℃ and the time is 0.5~2 h.

[0016] A TiZrVNbAl-based lightweight high-entropy alloy with high work hardening capability was prepared by the above method.

[0017] Beneficial effects This invention provides a method for improving the work hardening capability of TiZrVNbAl-based lightweight high-entropy alloys. The method first involves melting a high-entropy alloy rod, then preparing high-entropy alloy powder using a plasma rotating electrode atomization method. Next, two different laser additive manufacturing parameters are alternately switched during printing to obtain a heterogeneous structure with alternating coarse and fine grain layers. Finally, a solution treatment is performed to eliminate grain boundary precipitates caused by in-situ heat treatment during printing, thereby improving the alloy's plasticity. Because the mechanical properties of adjacent layers differ, uneven plastic strain is generated during deformation, leading to a strain gradient near the interface and the formation of numerous geometrically necessary dislocations. This results in a significant heterogeneous strengthening effect, effectively improving the strength and plasticity of TiZrVNbAl-based lightweight high-entropy alloys while significantly enhancing their work hardening capability.

[0018] This invention employs laser additive manufacturing to improve the work hardening capability of TiZrVNbAl-based lightweight high-entropy alloys. This method ensures that the heterogeneous structures in different parts of the formed part are identical, thereby overcoming the difficulty of constructing heterogeneous structures in large-sized components and promoting the engineering application of TiZrVNbAl-based lightweight high-entropy alloys. Furthermore, the laser additive manufacturing method used in this invention to prepare TiZrVNbAl-based lightweight high-entropy alloys with heterogeneous structures can meet the requirements for fabricating complex-shaped parts, while reducing material waste and shortening the material processing cycle. Attached Figure Description

[0019] Figure 1 Ti, as described in Embodiment 1 of the present invention 48 Zr 13 V 13 Nb 13 SEM image of Al5Mo8 alloy powder.

[0020] Figure 2 Ti, as described in Embodiment 1 of the present invention 48 Zr 13 V 13 Nb 13 SEM image of Al5Mo8 alloy.

[0021] Figure 3 The solution-treated Ti of Example 1 of this invention 48 Zr 13 V 13 Nb 13 SEM image of Al5Mo8 alloy.

[0022] Figure 4 Ti, as described in Embodiment 1 of the present invention 48 Zr 13 V 13 Nb 13 Stress-strain curves of Al5Mo8 alloy and alloy printed using uniform laser process parameters.

[0023] Figure 5 Ti, as described in Embodiment 2 of the present invention 48 Zr 13 V 13 Nb 13 Stress-strain curves of Al5Mo8 alloy and alloy printed using uniform laser process parameters.

[0024] Figure 6 Ti, as described in Embodiment 3 of the present invention 48 Zr 13 V 13 Nb 13 Stress-strain curves of Al5Mo8 alloy and alloy printed using uniform laser process parameters. Detailed Implementation

[0025] The present invention will be further described in detail below with reference to specific embodiments.

[0026] In the following examples and comparative examples, the tensile tests were conducted according to standard GB / T228.1-2021, using a CMT4305 microcomputer-controlled universal testing machine for room temperature axial quasi-static tensile tests, with a strain rate of 10. -3 s -1 The test specimen was a non-standard I-shaped part, 1.0 mm thick, 3.14 mm wide, with a parallel section length of 10 mm and a gauge length of 7 mm.

[0027] Example 1 Select Ti alloy 48 Zr 13 V 13 Nb 13 Using Al5Mo8 as the research object, metal blocks of each element were weighed according to the specific alloy composition and proportion. The surface of the raw material was polished and cleaned, and then added to a water-cooled copper crucible for smelting. The arc melting current was 600 A, and the magnetic stirring current was 5 A. Each alloy ingot was smelted at least five times to ensure the uniformity of the composition. After smelting, the ingot was solidified and processed into alloy rods with a diameter of 30 mm. The alloy rods were made into consumable electrodes, and the alloy rods were powdered using a plasma rotating electrode atomization method at a rotation speed of 20,000 rpm. To ensure good powder flowability, powders with particle sizes of 45–75 μm and 75–150 μm were selected by sieving for subsequent experiments. Figure 1 Ti of Example 1 48 Zr 13 V 13 Nb 13SEM images of Al5Mo8 alloy powder show a full powder surface with no obvious defects. Before printing, the alloy powder was dried in a drying oven at 125℃ for 4 hours to remove moisture. TC4 alloy was selected as the substrate for the experiment; its surface was polished to remove the oxide layer and cleaned with alcohol.

[0028] Laser additive manufacturing was used to print on a TC4 titanium alloy substrate. The laser process parameters were set as follows: (1) laser power 1000 W, scanning speed 12 mm / s, powder feed rate 10 g / min, overlap distance 1.2 mm, layer height 0.3 mm, and laser energy density 231.5 J / mm². 3 •s, the powder particle size used for printing is 75~150 μm. (2) Laser power 1500 W, scanning speed 8 mm / s, powder feeding rate 10 g / min, overlap distance 1 mm, layer height 0.3 mm, laser energy density is 625 J / mm 3 The powder used for printing had a particle size of 45–75 μm. Two laser process parameters were used alternately for printing, switching to the other laser process parameter after each deposition layer was completed. The final printed sample was a block-shaped sample with dimensions of 30 × 30 × 30 mm. After printing, the sample was cut from the substrate using a wire EDM machine, and the microstructure of the alloy was observed using SEM. Figure 2 Ti prepared in Example 1 48 Zr 13 V 13 Nb 13 The SEM image of the Al5Mo8 alloy shows a dense microstructure with no obvious defects or pores. The grains are fine, exhibiting a layered heterostructure composed of alternating coarse and fine grains. The coarse grains have a grain size of 40 μm and a thickness of 260 μm, while the fine grains have a grain size of 10 μm and a thickness of 330 μm. Discontinuous precipitates are present at the grain boundaries in both layers.

[0029] Since precipitates at grain boundaries can easily cause alloy brittleness, the alloy is subjected to a solution treatment at 980℃ for 1 h to dissolve the precipitates back, followed by water quenching. Figure 3 The solution-treated Ti from Example 1 48 Zr 13 V 13 Nb 13 The SEM image of the Al5Mo8 alloy shows that after solution treatment, the grain size of the alloy remains unchanged, and the precipitates at the grain boundaries are completely dissolved back.

[0030] The Ti prepared in this embodiment 48 Zr 13 V 13 Nb 13Tensile property tests were conducted on the Al5Mo8 alloy. Using alternating laser processing parameters, the alloy exhibited a yield strength of 1172 MPa, an elongation of 30%, and a maximum work hardening rate of 1094 MPa. Figure 4 As shown.

[0031] Comparative Example 1 Other conditions are the same as in Example 1, except that: laser additive manufacturing process parameters (1) and (2) are used separately for printing with uniform laser process parameters to obtain Ti. 48 Zr 13 V 13 Nb 13 Al5Mo8 alloy bulk samples were obtained by printing using two uniform laser process parameters. The alloy microstructure was entirely equiaxed, with grain sizes of 45 μm and 15 μm, respectively, without layered heterostructure, and discontinuous precipitates appeared at the grain boundaries. The alloy was subjected to solution treatment at 980℃ for 1 h to dissolve the precipitates, followed by water quenching. After solution treatment, the grain size of the alloy remained unchanged, and the precipitates at the grain boundaries were completely dissolved.

[0032] The Ti prepared in this comparative example 48 Zr 13 V 13 Nb 13 Tensile properties tests were conducted on the Al5Mo8 alloy, and its yield strengths were 1107 MPa and 1174 MPa, its elongation was 24% and 27%, and its maximum work hardening rates were 713 MPa and 640 MPa, respectively.

[0033] The results show that, compared with Comparative Example 1, the alloy printed in Example 1 is superior in terms of strength and plasticity matching, and has a stronger work hardening ability. For details of the comparison results, please refer to Table 1.

[0034] Table 1

[0035] Example 2: Select Ti alloy 48 Zr 13 V 13 Nb 13Using Al5Mo8 as the research object, metal blocks of each element were weighed according to the specific alloy composition and proportion, and then added to a water-cooled copper crucible for smelting under suspension melting conditions. The arc melting current was 600 A, and the magnetic stirring current was 5 A. Each alloy ingot was melted at least five times to ensure the uniformity of the composition. After melting, the ingot was condensed to obtain an alloy ingot, which was then processed into an alloy rod with a diameter of 50 mm. The alloy rod was made into a consumable electrode, and the alloy rod was powdered using a plasma rotating electrode atomization method at a rotation speed of 20,000 rpm. To ensure good powder flowability, powders with particle sizes of 45–75 μm and 75–150 μm were selected by sieving for subsequent experiments. Before printing, the powder was dried in a drying oven at 125°C for 4 h to remove moisture. TC4 alloy was selected as the substrate for the experiment. Its surface was polished to remove the oxide layer and cleaned with alcohol.

[0036] Laser additive manufacturing was used to print on a TC4 titanium alloy substrate. The laser process parameters were set as follows: (1) laser power 1200 W, scanning speed 15 mm / s, powder feed rate 10 g / min, overlap distance 1.4 mm, layer height 0.3 mm, and laser energy density 190.5 J / mm². 3 •s, the powder particle size used for printing is 75~150 μm. (2) Laser power 1200 W, scanning speed 5 mm / s, powder feeding rate 10 g / min, overlap distance 0.8 mm, layer height 0.3 mm, laser energy density is 1000 J / mm 3 The powder used for printing had a particle size of 45–75 μm. Two laser process parameters were used alternately for printing, switching to the other laser process parameter after each deposition layer was printed. The final printed block sample had dimensions of 30 × 30 × 30 mm. After printing, the sample was cut from the substrate using a wire EDM machine, and the microstructure of the alloy was observed using SEM. SEM observation revealed that the alloy microstructure was a layered heterostructure composed of alternating coarse and fine grain layers. The coarse grain layer had a grain size of 60 μm and a layer thickness of 275 μm, while the fine grain layer had a grain size of 15 μm and a layer thickness of 320 μm. Discontinuous precipitates were observed at the grain boundaries in both layers.

[0037] Since precipitates at grain boundaries can easily cause alloy brittleness, the alloy was subjected to a solution treatment at 980℃ for 1 h to dissolve the precipitates back, followed by water quenching. After the solution treatment, the grain size of the alloy remained unchanged, and the precipitates at the grain boundaries were completely dissolved back.

[0038] The Ti prepared in this embodiment 48 Zr 13 V 13 Nb 13Tensile property tests were conducted on the Al5Mo8 alloy, revealing a yield strength of 1177 MPa, an elongation of 27%, and a maximum work hardening rate of 953 MPa. Figure 5 As shown.

[0039] Comparative Example 2 Other conditions are the same as in Example 2, except that: laser additive manufacturing process parameters (1) and (2) are used separately for printing with uniform laser process parameters to obtain Ti. 48 Zr 13 V 13 Nb 13 Al5Mo8 alloy bulk samples were obtained. The alloy microstructure obtained by printing with two uniform laser process parameters was entirely equiaxed, with grain sizes of 75 μm and 18 μm, respectively, exhibiting no layered heterostructure and discontinuous precipitates at grain boundaries. The alloy was subjected to a solution treatment at 980℃ for 1 h to dissolve the precipitates, followed by water quenching. After the solution treatment, the grain size of the alloy remained unchanged, and the precipitates at the grain boundaries were completely dissolved.

[0040] The Ti prepared in this comparative example 48 Zr 13 V 13 Nb 13 Tensile properties tests were conducted on the Al5Mo8 alloy, and its yield strengths were 1105 MPa and 1114 MPa, its elongation was 17% and 19%, and its maximum work hardening rates were 591 MPa and 524 MPa, respectively.

[0041] The results show that, compared with Comparative Example 2, the alloy printed in Example 2 is superior in terms of strength and plasticity matching, and has a stronger work hardening ability. For detailed comparison results, please refer to Table 2.

[0042] Table 2

[0043] Example 3: Select Ti alloy 48 Zr 13 V 13 Nb 13Using Al5Mo8 as the research object, metal blocks of each element were weighed according to the specific alloy composition and proportion, and then added to a water-cooled copper crucible for smelting under suspension melting conditions. The arc melting current was 600 A, and the magnetic stirring current was 5 A. Each alloy ingot was melted at least five times to ensure the uniformity of the composition. After melting, the ingot was condensed to obtain an alloy ingot, which was then processed into an alloy rod with a diameter of 50 mm. The alloy rod was made into a consumable electrode, and the alloy rod was powdered using a plasma rotating electrode atomization method at a rotation speed of 20,000 rpm. To ensure good powder flowability, powders with particle sizes of 45–75 μm and 75–150 μm were selected by sieving for subsequent experiments. Before printing, the powder was dried in a drying oven at 125°C for 4 h to remove moisture. TC4 alloy was selected as the substrate for the experiment. Its surface was polished to remove the oxide layer and cleaned with alcohol.

[0044] Laser additive manufacturing was used to print on a TC4 titanium alloy substrate. The laser process parameters were set as follows: (1) laser power 1000 W, scanning speed 12 mm / s, powder feed rate 10 g / min, overlap distance 1.2 mm, layer height 0.3 mm, and laser energy density 231.5 J / mm². 3 •s, the powder particle size used for printing is 75~150 μm. (2) Laser power 1500 W, scanning speed 8 mm / s, powder feeding rate 10 g / min, overlap distance 1 mm, layer height 0.3 mm, laser energy density is 625 J / mm 3 The powder used for printing had a particle size of 45–75 μm. Two laser process parameters were used alternately for printing, switching to the other laser process parameter after printing three deposition layers. The final printed block sample had dimensions of 30 × 30 × 30 mm. After printing, the sample was cut from the substrate using a wire cutter, and the microstructure of the alloy was observed using SEM. SEM observation revealed that the alloy microstructure was a layered heterostructure composed of alternating coarse and fine grain layers. The coarse grain layer had a grain size of 45 μm and a thickness of 800 μm, while the fine grain layer had a grain size of 12 μm and a thickness of 950 μm. Discontinuous precipitates were observed at the grain boundaries in both layers.

[0045] Since precipitates at grain boundaries can easily cause alloy brittleness, the alloy was subjected to a solution treatment at 980℃ for 1 hour to dissolve the precipitates back, followed by water quenching. After the solution treatment, the grain size of the alloy remained unchanged, and the precipitates at the grain boundaries were completely dissolved back.

[0046] The Ti prepared in this embodiment 48 Zr 13 V 13 Nb 13Tensile properties of Al5Mo8 alloy were tested and compared with those of two Ti alloys printed using uniform laser process parameters. 48 Zr 13 V 13 Nb 13 Compared with Al5Mo8 alloy, the tensile stress-strain curves are as follows: Figure 6 The alloy obtained using alternating laser process parameters has a yield strength of 1213 MPa, an elongation of 29%, and a maximum work hardening rate of 1057 MPa.

[0047] Comparative Example 3 The other conditions are the same as in Example 3, except that: laser additive manufacturing process parameters (1) and (2) are used separately for printing with uniform laser process parameters to obtain Ti. 48 Zr 13 V 13 Nb 13 Al5Mo8 alloy bulk samples were obtained by printing using two uniform laser process parameters. The alloy microstructure was entirely equiaxed, with grain sizes of 40 μm and 15 μm, respectively, without layered heterostructure, and discontinuous precipitates appeared at the grain boundaries. The alloy was subjected to solution treatment at 980℃ for 1 h to dissolve the precipitates, followed by water quenching. After solution treatment, the grain size of the alloy remained unchanged, and the precipitates at the grain boundaries were completely dissolved.

[0048] The Ti prepared in this comparative example 48 Zr 13 V 13 Nb 13 Tensile properties tests were conducted on the Al5Mo8 alloy, and its yield strengths were 1107 MPa and 1164 MPa, its elongation was 24% and 27%, and its maximum work hardening rates were 713 MPa and 640 MPa, respectively.

[0049] The results show that, compared with Comparative Example 3, the alloy printed in Example 3 is superior in terms of strength and plasticity matching, and has stronger work hardening ability. For detailed comparison results, please refer to Table 3.

[0050] Table 3

[0051] In summary, the invention includes, but is not limited to, the above embodiments. Any equivalent substitutions or partial improvements made under the spirit and principles of this invention shall be considered to be within the protection scope of this invention.

Claims

1. A method for improving the work hardening capacity of a TiZrVNbAl-based light-weight high-entropy alloy, characterized in that: The method steps include: (1) according to the composition and proportion of the TiZrVNbAl light-weight high-entropy alloy, the metal block raw materials of each element are weighed; (2) the raw materials are added into a suspension smelting water-cooled copper crucible for smelting, an alloy ingot is obtained, and a high-entropy alloy rod is processed; (3) the high-entropy alloy rod is made into a consumable electrode, a high-entropy alloy powder is prepared by a plasma rotating electrode atomization method, and a printing powder obtained by screening is obtained; (4) after the printing powder is dried, laser additive manufacturing printing is performed, and a high-entropy alloy block is obtained; (5) the high-entropy alloy block is subjected to solid solution treatment, and a TiZrVNbAl light-weight high-entropy alloy with high work hardening capacity is obtained. In step (4), two different laser additive manufacturing parameters are alternately switched to print, and a heterogeneous structure with alternating arrangement of coarse grain layers and fine grain layers is obtained; the average grain size of the coarse grain layer is 40-80 μm, the thickness of each layer is 250-1500 μm, and the average grain size of the fine grain layer is 10-20 μm, the thickness of each layer is 250-1500 μm.

2. The method for improving work hardening capacity of TiZrVNbAl light weight high-entropy alloy according to claim 1, characterized in that: In step (1), the TiZrVNbAl-based light-weight high-entropy alloy is denoted as Ti a Zr b V c Nb d Al e M f , M is one or more of Al, Hf, Cr, Fe, Mg, Be, Li, Mo, Co, Ni, Si, B, O and N; wherein 25 < a < 65, 0 < b ≤ 55, 0 < c < 25, 0 < d < 35, 0 < e < 20, 0 < f < 10, and a + b + c + d + e + f = 100.

3. The method for improving work hardening capacity of TiZrVNbAl light weight high-entropy alloy according to claim 2, characterized in that: 50≤a≤60, 15≤b≤25, 15≤c≤20, 15≤d≤25, 3≤e≤7, 4≤f≤8.

4. The method for improving work hardening capacity of TiZrVNbAl light weight high-entropy alloy according to claim 1, characterized in that: In step (2), the arc smelting current during smelting is 200-1000 A, the magnetic stirring current is 2-10 A, and the smelting frequency is more than 5 times; And / or, the diameter of the high-entropy alloy rod is 30-70 mm.

5. The method for improving work hardening capacity of TiZrVNbAl light weight high-entropy alloy according to claim 1, characterized in that: In step (3), in the plasma rotating electrode atomization method, the rotating speed of the electrode rod is 10,000-30,000 revolutions / minute; And / or, the particle size of the printing powder is 45-75 μm and 75-150 μm.

6. The method for improving work hardening capacity of TiZrVNbAl light weight high-entropy alloy according to claim 1, characterized in that: In step (4), the first laser additive manufacturing parameter is: the laser power is 1,000-1,200 W, the scanning speed is 12-15 mm / s, the powder feeding rate is 10-15 g / min, the overlapping distance is 1.2-1.4 mm, the layer height is 0.2-0.4 mm, and the powder particle size used for printing is 75-150 μm; the second laser additive manufacturing parameter is: the laser power is 1,200-1,500 W, the scanning speed is 5-8 mm / s, the powder feeding rate is 10-15 g / min, the overlapping distance is 0.8-1 mm, the layer height is 0.2-0.4 mm, and the powder particle size used for printing is 45-75 μm.

7. The method for improving work hardening capacity of TiZrVNbAl light weight high-entropy alloy according to claim 6, characterized in that: The laser energy density of the first laser additive manufacturing parameter is 120-250 J / mm 3 • s, the laser energy density of the second laser additive manufacturing parameter is 400-1000 J / mm 3 • s.

8. The method for improving work hardening capacity of TiZrVNbAl light weight high-entropy alloy according to claim 1, characterized in that: The thickness of each layer of the coarse grain layer is 250-350 μm, and the thickness of each layer of the fine grain layer is 250-350 μm; And / or, a high-entropy alloy block with a size of 30-50×30-50×30-50 mm is printed on a TC4 titanium alloy substrate that has been polished on the surface.

9. The method for improving work hardening capacity of TiZrVNbAl light weight high-entropy alloy according to claim 1, characterized in that: In step (5), the solid solution treatment causes the precipitated phase in the printing process to dissolve back while not affecting the grain size; preferably, the solid solution treatment temperature is 900-1,000°C, and the time is 0.5-2 h.

10. A TiZrVNbAl-based light-weight high-entropy alloy having high work hardening capacity, characterized in that: Prepared by the method of any one of claims 1-9.

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