Lightweight high-damping Ti6Al4V alloy and preparation method thereof

Abstract

The invention discloses a lightweight high-damping Ti6Al4V alloy and a preparation method thereof. Ti6Al4V powder and Er powder are subjected to hot pressing sintering molding in a vacuum environment. According to the method, alloy powder vacuum hot pressing sintering is adopted, rapid rearrangement of powder particles can be promoted, the diffusion process is accelerated, the sintered material is more compact, the density of the material can reach 100%, the temperature needed by sintering can be reduced, grain growth can be controlled easily, and the damping performance of the material is improved.

Description

Technical Field

[0001] This invention belongs to the field of alloy materials technology, specifically relating to a lightweight, high-damping Ti6Al4V alloy and its preparation method. Background Technology

[0002] Ti6Al4V titanium alloy (TC4) is an α+β type titanium alloy, whose main components include titanium, aluminum, vanadium, and small amounts of other elements (usually iron, carbon, oxygen, etc.). Ti6Al4V titanium alloy possesses excellent mechanical properties and corrosion resistance. It exhibits high strength and hardness while maintaining the excellent specific strength and specific gravity ratio of titanium alloys. Furthermore, Ti6Al4V titanium alloy also possesses good heat resistance, wear resistance, and fatigue resistance. Ti6Al4V alloy has wide applications in aerospace, medical devices, automotive manufacturing, and shipbuilding. Its high specific strength, good machinability, and adaptability to high-temperature environments make it an indispensable material in modern engineering. Summary of the Invention

[0003] The purpose of this invention is to provide a lightweight, high-damping Ti6Al4V alloy and its preparation method, so as to obtain a lightweight, uniform, and dense high-damping Ti6Al4V alloy.

[0004] This invention is achieved through the following technical solution:

[0005] A method for preparing lightweight, high-damping Ti6Al4V alloy involves hot-pressing and sintering Ti6Al4V powder and Er powder in a vacuum environment.

[0006] In some embodiments of the present invention, the Ti6Al4V powder comprises 99%-95.5% by weight, and the Er powder comprises 0.5%-1%.

[0007] In some embodiments of the present invention, by weight, Ti6Al4V powder is 99% and Er powder is 1%.

[0008] In some embodiments of the present invention, the sintering temperature used in hot pressing sintering is 900℃-1100℃, and the sintering pressure is 20-40MPa.

[0009] In some embodiments of the present invention, the sintering temperature used in hot pressing sintering is 950°C and the sintering pressure is 30 MPa.

[0010] In some embodiments of the present invention, the following steps are included:

[0011] Screening for Ti6Al4V powder and Er powder with a particle size of less than 50 micrometers;

[0012] The screened Ti6Al4V powder and Er powder were mechanically ball-milled and mixed.

[0013] The powder that has undergone mixing is freeze-dried.

[0014] The freeze-dried powder is then hot-pressed and sintered under vacuum.

[0015] In some embodiments of the present invention, the vacuum degree of hot pressing sintering is 0.01-0.1 Pa, the hot pressing sintering temperature is 900-1100℃, the heating rate is 10℃ / min, the hot pressing sintering pressure is 20-40 MPa, and the hot pressing sintering holding time is 1-3 hours.

[0016] On the other hand, the present invention also provides a lightweight, high-damping Ti6Al4V alloy prepared by the aforementioned preparation method.

[0017] In some embodiments of the present invention, the peak damping of the alloy can reach 0.0110.

[0018] Compared with the prior art, the present invention has the following advantages and beneficial effects:

[0019] This invention employs vacuum hot pressing sintering of alloy powder, which can promote rapid rearrangement of powder particles, accelerate the diffusion process, and make the sintered material more compact, achieving a density of 100%. It can also reduce the sintering temperature, which is beneficial for controlling grain growth and improving the damping performance of the material.

[0020] This invention uses alloyed Ti6Al4V powder, which, compared to preparation methods using single elements, is less prone to oxidation during the preparation process and can effectively control the oxygen content of the alloy, thereby ensuring the alloy's performance.

[0021] The Er used in this invention is a heavy rare earth element with a melting point much higher than that of hot pressing sintering. During the sintering process, Er exists in the form of solid particles, which promotes sintering and forming through a solid-solid diffusion mechanism, avoiding the problem of compositional segregation. This is beneficial for forming fine and uniform grains and further improving the damping performance of titanium alloys.

[0022] This invention employs a vacuum hot-pressing furnace for vacuum hot-pressing sintering to sinter rare earth element Er with Ti6Al4V alloy powder, resulting in a lightweight, dense, and high-damping titanium alloy. Er doping of Ti6Al4V helps refine the grain size, regulate the crystal structure, and improve the alloy's mechanical properties. Simultaneously, the vacuum hot-pressing process eliminates oxidation reactions, reduces residual gas, and prevents oxidation of the Ti6Al4V matrix when exposed to high temperatures. This also further improves the density and uniformity of the titanium alloy, effectively enhancing the damping performance of the Ti6Al4V alloy. The peak damping value of the doped Ti6Al4V alloy reaches 0.0110, which is more than three times higher than the peak damping value of 0.0036 for the traditionally melted and cast Ti6Al4V alloy. The peak damping value of the undoped alloy is 0.0086, which is more than 2.3 times higher than the peak damping value of 0.0036 for the traditionally melted and cast alloy. Attached Figure Description

[0023] To more clearly illustrate the technical solutions of the embodiments of the present invention, the accompanying drawings in the embodiments will be briefly described below. It should be understood that the following drawings only show some embodiments of the present invention and should not be regarded as a limitation on the scope. For those skilled in the art, other related drawings can be obtained based on these drawings without creative effort.

[0024] Figure 1 shows the SEM image and EDS spectrum of the Ti6Al4V alloy prepared in Example 1 of the present invention; wherein, a) is the SEM image of the rare earth element Er-doped Ti6Al4V titanium alloy, and b) is the EDS spectrum of the white network precipitate phase.

[0025] Figure 2 is a SEM image of the Ti6Al4V alloy prepared in Example 1 of the present invention; wherein, a) is a SEM image of the rare earth element Er-doped Ti6Al4V titanium alloy, and b) is an EDS surface scan distribution map of rare earth element Er in Ti6Al4V alloy.

[0026] Figure 3 This is the internal friction spectrum of the rare earth element Er-doped Ti6Al4V alloy in Example 1 of the present invention as a function of strain amplitude.

[0027] Figure 4 This is the internal friction spectrum of the Ti6Al4V alloy without rare earth elements in Example 2 of the present invention as a function of strain amplitude.

[0028] Figure 5 The image shows the internal friction spectrum of the Ti6Al4V alloy in Comparative Example 1 of this invention as a function of strain amplitude.

[0029] Figure 6 The image shows the internal friction spectrum of Ti6Al4V alloy as a function of strain amplitude in the embodiments and comparative examples of the present invention. Detailed Implementation

[0030] To make the objectives, technical solutions, and advantages of the embodiments of the present invention clearer, the technical solutions of the embodiments of the present invention will be clearly and completely described below with reference to the accompanying drawings. Obviously, the described embodiments are some embodiments of the present invention, but not all embodiments.

[0031] Current research focuses on improving the strength, corrosion resistance, and fatigue resistance of Ti6Al4V titanium alloys, but research on their damping properties is relatively limited. This invention proposes a method for preparing high-damping titanium alloys using rare-earth element Er-doped Ti6Al4V via vacuum hot pressing.

[0032] In some embodiments of the present invention, the preparation method of Ti6Al4V alloy includes the following steps:

[0033] 1) Use a sieve with a mesh size of not less than 300 to screen Ti6Al4V powder and Er powder respectively, and retain Ti6Al4V powder and Er powder with a particle size of less than 50 micrometers.

[0034] 2) The Ti6Al4V powder obtained by screening was mixed with Er powder by mechanical ball milling;

[0035] Using agate balls and an agate jar, add 20–70 ml of tert-butanol as the dispersion medium, add 1% wt of Er powder, and the remainder is Ti6Al4V powder. Mill at 200–300 rpm and 10–15 degrees Celsius per minute for 1–2 hours.

[0036] (3) The treated powder is placed in a vacuum freeze dryer for 24 hours for drying. The vacuum degree is 0.1 to 10 Pa and the freezing temperature can be reduced to -20 to -50 degrees Celsius.

[0037] (4) The processed powder is vacuum hot-pressed and sintered into a block.

[0038] The vacuum degree of vacuum hot pressing sintering reaches 0.01 to 0.1 Pa, the temperature of vacuum hot pressing sintering is 900 to 1100℃, the heating rate is controlled at 10℃ / min, the pressure of vacuum hot pressing sintering is 20 to 40 MPa, and the holding time of vacuum hot pressing sintering is 1 to 3 hours.

[0039] Doping with the rare earth element Er can act as an active site for crystal nucleation or as an inhibitor of crystal growth, increasing the nucleus density and growth rate. Er doping promotes grain refinement in Ti6Al4V alloys. As grain size decreases, the number of grain boundaries increases, and the total volume of grain boundaries also increases, thereby increasing the material's damping. Furthermore, the addition of Er enriches near grain boundaries, forming a network of precipitates that are intergranular, which is beneficial for energy dissipation at the interface. After grain refinement, the number of interactions between dislocations and grain boundaries increases. When dislocations encounter grain boundaries, dislocation pile-up, reactions, or rearrangements occur, significantly improving the alloy's damping performance.

[0040] The Ti6Al4V alloy prepared by this invention uses Ti6Al4V titanium alloy powder as raw material. The chemical composition of Ti6Al4V titanium alloy powder is shown in Table 1.

[0041] Table 1 Chemical composition of Ti6Al4V powder

[0042]

[0043] The added rare earth metal Er powder has a purity of up to 99.9% and a particle size of ≥300 mesh.

[0044] The preparation method of the present invention and the Ti6Al4V titanium alloy prepared by the preparation method of the present invention will be described in detail below with reference to specific embodiments.

[0045] Example 1

[0046] 1) Pretreatment of Ti6Al4V powder and Er powder;

[0047] Ti6Al4V powder and Er powder were screened using a 300-mesh sieve to obtain Ti6Al4V powder and Er powder with a particle size of less than 48 micrometers. The sieved Ti6Al4V and Er powders had relatively uniform particle size and no obvious impurities or agglomerated particles.

[0048] 2) Prepare mixed powder;

[0049] The sieved Ti6Al4V powder and Er powder were ball-milled using agate balls and an agate ball mill jar. The ball milling media was tert-butanol, the milling speed was 300 rpm, the rotation angle was 15° / min, the milling time was 1 h, and the ball-to-powder ratio was 4:1. After ball milling, the mixture was freeze-dried under vacuum at a vacuum of 10 Pa and a freezing temperature of -20°C for 24 h. The resulting mixed powder was then removed.

[0050] 3) Preparation of rare earth metal Er-doped Ti6Al4V alloy materials

[0051] The freeze-dried mixed powder is then subjected to vacuum hot pressing sintering. The specific process is as follows:

[0052] The mixed powder was placed into a graphite mold with an inner diameter of 55 mm and sintered under the conditions of sintering pressure of 30 MPa, sintering temperature of 950 ℃, heating rate of 10 ℃ / min and holding time of 1 h. Then it was cooled in the furnace and the alloy blank with a diameter of 55 mm and a thickness of about 10 mm was obtained. The sample was named #1.

[0053] Example 2

[0054] The difference between this embodiment and Embodiment 1 is that the Ti6Al4V alloy material prepared in this embodiment is undoped with rare earth metal Er.

[0055] The preparation process used is as follows:

[0056] Take the sieved Ti6Al4V powder from Example 1, ball mill the Ti6Al4V powder for the same time according to the ball milling settings of Example 1, and then freeze it for 24 hours using the same freeze-drying parameters to obtain the processed Ti6Al4V powder.

[0057] Then, vacuum hot pressing was performed, with the specific process being the same as in Example 1. The treated Ti6Al4V powder was placed into a graphite mold with an inner diameter of 55mm, and sintered under the conditions of sintering pressure of 30MPa, sintering temperature of 950℃, heating rate of 10℃ / min, and holding time of 1h. Then, it was cooled in the furnace, and a Ti6Al4V blank with a diameter of 55mm and a thickness of about 10mm without rare earth metal Er was obtained. The sample was named #2.

[0058] Example 3

[0059] The difference between this embodiment and Embodiment 1 is that a different sintering temperature was used during vacuum hot pressing sintering. The specific preparation process used is as follows:

[0060] The freeze-dried mixed powder from Example 1 was subjected to vacuum hot pressing sintering. The specific process was as follows: the mixed powder was placed into a graphite mold with an inner diameter of 55 mm, and sintering was carried out under the conditions of sintering pressure of 30 MPa, sintering temperature of 900 °C, heating rate of 10 °C / min, and holding time of 1 h. Then, it was cooled with the furnace and an alloy blank with a diameter of 55 mm and a thickness of about 10 mm was obtained. The sample was named #3.

[0061] Example 4

[0062] The difference between this embodiment and Embodiment 1 is that a different sintering temperature was used during vacuum hot pressing sintering. The specific preparation process used is as follows:

[0063] The freeze-dried mixed powder from Example 1 was subjected to vacuum hot pressing sintering. The specific process was as follows: the mixed powder was placed into a graphite mold with an inner diameter of 55 mm, and sintering was carried out under the conditions of sintering pressure of 30 MPa, sintering temperature of 1000℃, heating rate of 10℃ / min, and holding time of 1 h. Then, it was cooled with the furnace and an alloy blank with a diameter of 55 mm and a thickness of about 10 mm was obtained. The sample was named #4.

[0064] Example 5

[0065] The difference between this embodiment and Embodiment 1 is that a different sintering temperature was used during vacuum hot pressing sintering. The specific preparation process used is as follows:

[0066] The freeze-dried mixed powder from Example 1 was subjected to vacuum hot pressing sintering. The specific process was as follows: the mixed powder was placed into a graphite mold with an inner diameter of 55 mm, and sintering was carried out under the conditions of sintering pressure of 30 MPa, sintering temperature of 1050 °C, heating rate of 10 °C / min, and holding time of 1 h. Then, it was cooled with the furnace and an alloy blank with a diameter of 55 mm and a thickness of about 10 mm was obtained. The sample was named #5.

[0067] Example 6

[0068] The difference between this embodiment and Embodiment 1 is that a different sintering temperature was used during vacuum hot pressing sintering. The specific preparation process used is as follows:

[0069] The freeze-dried mixed powder from Example 1 was subjected to vacuum hot pressing sintering. The specific process was as follows: the mixed powder was placed into a graphite mold with an inner diameter of 55 mm, and sintering was carried out under the conditions of sintering pressure of 30 MPa, sintering temperature of 1100℃, heating rate of 10℃ / min, and holding time of 1 h. Then, it was cooled with the furnace and an alloy blank with a diameter of 55 mm and a thickness of about 10 mm was obtained. The sample was named #6.

[0070] Example 7

[0071] The difference between this embodiment and Embodiment 1 is that a different sintering pressure was used during vacuum hot pressing sintering. The specific preparation process used is as follows:

[0072] The freeze-dried mixed powder from Example 1 was subjected to vacuum hot pressing sintering. The specific process was as follows: the mixed powder was placed into a graphite mold with an inner diameter of 55 mm, and sintering was carried out under the conditions of sintering pressure of 20 MPa, sintering temperature of 950 °C, heating rate of 10 °C / min, and holding time of 1 h. Then, it was cooled with the furnace and an alloy blank with a diameter of 55 mm and a thickness of about 10 mm was obtained. The sample was named #7.

[0073] Example 8

[0074] The difference between this embodiment and Embodiment 1 is that a different sintering pressure was used during vacuum hot pressing sintering. The specific preparation process used is as follows:

[0075] The freeze-dried mixed powder from Example 2 was subjected to vacuum hot pressing sintering. The specific process was as follows: the mixed powder was placed into a graphite mold with an inner diameter of 55 mm, and sintering was carried out under the conditions of sintering pressure of 40 MPa, sintering temperature of 950 °C, heating rate of 10 °C / min, and holding time of 1 h. Then, it was cooled with the furnace and an alloy blank with a diameter of 55 mm and a thickness of about 10 mm was obtained. The sample was named #8.

[0076] Comparative Example 1

[0077] Ti6Al4V plates were prepared using traditional smelting and forging processes.

[0078] Appropriate amounts of titanium, aluminum, and other alloying elements are mixed according to a specific formula and smelted in a high-temperature melting furnace. The smelting process requires strict control of temperature and atmosphere to ensure uniform mixing of the alloy components and the occurrence of chemical reactions. The smelted alloy block is typically formed into sheet metal using processing methods such as forging or rolling. In the forging process, the smelted alloy block is heated to a suitable temperature and then deformed using forging machinery or hydraulic pressure equipment. Finally, subsequent processing methods such as heat treatment yield the Ti6Al4V titanium alloy produced using traditional processes.

[0079] Comparative Example 1 was obtained from Ti6Al4V (titanium alloy) sheet produced in Baoji, Shaanxi Province. The Ti6Al4V blank with a diameter of 55mm and a thickness of about 10mm was obtained by wire cutting, and the sample was named #9.

[0080] The performance of the Ti6Al4V samples prepared in the above examples and comparative examples was tested, including:

[0081] 1) Density test

[0082] Density is tested using Archimedes' displacement method, and the theoretical density of the sample is calculated based on the content ratio of each component. Density is the ratio of the sample's actual density to its theoretical density.

[0083] The density of Ti6Al4V prepared in Comparative Example 1 and Examples 1-8 was measured using the Archimedes method. The test results are shown in Table 2. The density of Ti6Al4V material prepared by doping and vacuum hot pressing is close to 100%. The density of the sample in Example 1 is 99.70%, and the density of the sample in Example 2 is 99.16%, which is close to 100% of Comparative Example 1, and basically achieves the same densification performance as that of smelting and forging.

[0084] The mechanism by which this invention can prepare high-density Ti6Al4V alloy materials is as follows:

[0085] Firstly, the vacuum environment used in vacuum hot pressing effectively removes gas pores from the material. By applying external force under high temperature and high pressure, the gas pores are squeezed and compacted, thereby reducing the gas content in the alloy and increasing its density.

[0086] Secondly, hot pressing in a vacuum environment promotes atomic diffusion in the alloy. At high temperatures, atoms are highly mobile, and a vacuum environment reduces the impact of surface oxidation and other contaminants, thus accelerating atomic diffusion and improving grain boundary bonding, which is beneficial for increasing alloy density. Furthermore, increasing temperature and pressure in a vacuum environment reduces the impact of gas agglomeration. Under normal atmospheric conditions, gas molecules may aggregate on the alloy surface, forming bubbles and affecting density. In a vacuum environment, this gas agglomeration is significantly reduced, contributing to higher alloy density.

[0087] 2) Scanning Electron Microscopy (SEM) Testing

[0088] The microstructure of the Ti6Al4V alloy materials prepared in Comparative Example 1 and Examples 1-8 was measured and observed using a German ZEISS Sigma 300 microscope to characterize its microstructure.

[0089] The morphology of the Ti6Al4V alloy materials prepared in Comparative Example 1 and Examples 1-8 of the invention was observed, and it was found that the Ti6Al4V alloy materials prepared in Examples 1-8 were dense and had no pores.

[0090] In addition, a white, network-distributed precipitate phase was found in the rare-earth Er-doped Ti6Al4V alloy in Example 1, as shown in Figure 1(a). EDS analysis revealed that this phase was a rare-earth phase, as shown in Figure 1(b). This phase was not found in Example 2 and Comparative Example 1.

[0091] 3) Damping performance test

[0092] Ti6Al4V alloy materials prepared in Comparative Example 1 and Examples 1-8 were cut into strips with dimensions of 30×10×2mm using a wire EDM machine. After cutting, the surface of the specimens was polished with 400-grit and 800-grit sandpaper respectively to ensure uniform surface roughness. Dynamic thermomechanical analyzers (DMA: model TAQ800) were used for testing using a single cantilever fixture. The peak values ​​of sample damping tests are shown in Table 2. The internal friction spectra of the alloys prepared in Comparative Example 1 and Examples 1 and 2 as a function of strain amplitude are shown in Table 2. Figures 3-6 As shown.

[0093] The testing principle involves applying a periodic load to excite the material, measuring its deformation response, and analyzing the data to evaluate the material's damping performance, including loss modulus and storage modulus.

[0094] In Example 1, the damping peak value of the rare earth element Er-doped Ti6Al4V alloy reached 0.0110, which is more than 3 times higher than the damping peak value of 0.0036 of the traditional smelting and casting. The damping peak value of the undoped Ti6Al4V alloy was 0.0086, which is more than 2.3 times higher than the damping peak value of 0.0036 of the traditional smelting and casting.

[0095] In Ti6Al4V alloy, doping with the rare earth element Er results in a damping mechanism involving grain boundary damping and dislocation damping. By appropriately adjusting the doping concentration and distribution of rare earth elements, the size, shape, and orientation of the grains can be controlled, thereby altering the microstructure of the material. Er doping can act as an active site for crystal nucleation or an inhibitor of crystal growth, increasing the crystal nucleus density and growth rate. Er doping leads to grain refinement in the Ti6Al4V alloy. As the grain size decreases, the number of grain boundaries increases, and the total volume of grain boundaries also increases, thus increasing the material's damping. Furthermore, the addition of Er enriches near the grain boundaries, forming a precipitate phase between the grains. A network precipitate phase is observed in the SEM image of Example 1, which is beneficial for energy dissipation at the interface. After grain refinement, the number of interactions between dislocations and grain boundaries increases. When dislocations encounter grain boundaries, dislocation pile-up, reactions, or rearrangements occur, thus increasing the material's damping performance.

[0096] Table 2. Test data of density and peak damping of Ti6Al4V alloy in the examples and comparative examples.

[0097]

[0098]

[0099] As can be seen from Table 2, the hot pressing temperature and pressure have a certain impact on the density and damping peak of the material when using hot pressing molding process. When the hot pressing temperature is 950℃ and the hot pressing pressure is 30MPa, better density and damping performance can be achieved.

[0100] Certain terms are used in the specification and claims to refer to specific components. Those skilled in the art will understand that hardware manufacturers may use different names to refer to the same component. This specification and claims do not distinguish components based on differences in name, but rather on differences in function. The terms "comprising" and "including" used throughout the specification and claims are open-ended and should be interpreted as "comprising / including but not limited to". "Approximately" means that within an acceptable margin of error, those skilled in the art can solve the technical problem and substantially achieve the technical effect within a certain margin of error. The following descriptions in the specification are preferred embodiments for carrying out this application; however, these descriptions are for the purpose of illustrating the general principles of this application and are not intended to limit the scope of this application. The scope of protection of this application shall be determined by the appended claims.

[0101] It should also be noted that the terms "comprising," "including," or any other variations thereof are intended to cover non-exclusive inclusion, such that a product or system comprising a list of elements includes not only those elements but also other elements not expressly listed, or elements inherent to such a product or system. Without further limitation, an element defined by the phrase "comprising one..." does not exclude the presence of other identical elements in the product or system that includes said element.

[0102] It should be understood that the term "and / or" used in this article is merely a description of the relationship between related objects, indicating that three relationships can exist. For example, A and / or B can represent: A existing alone, A and B existing simultaneously, and B existing alone. Additionally, the character " / " in this article generally indicates that the preceding and following related objects have an "or" relationship.

[0103] The above description is merely a preferred embodiment of the present invention and is not intended to limit the present invention in any way. Any simple modifications or equivalent changes made to the above embodiments based on the technical essence of the present invention shall fall within the protection scope of the present invention.

Claims

1. A method for preparing a lightweight, high-damping Ti6Al4V alloy, characterized in that, Ti6Al4V powder and Er powder were hot-pressed and sintered in a vacuum environment.

2. The method for preparing lightweight, high-damping Ti6Al4V alloy according to claim 1, characterized in that, By weight, Ti6Al4V powder accounts for 99%-95.5%, and Er powder accounts for 0.5%-1%.

3. The method for preparing lightweight, high-damping Ti6Al4V alloy according to claim 1, characterized in that, By weight, Ti6Al4V powder accounts for 99% and Er powder accounts for 1%.

4. The method for preparing lightweight, high-damping Ti6Al4V alloy according to claim 1, characterized in that, The sintering temperature used in hot pressing sintering is 900℃-1100℃, and the sintering pressure is 20-40MPa.

5. The method for preparing lightweight, high-damping Ti6Al4V alloy according to claim 4, characterized in that, The sintering temperature used in hot pressing sintering is 950℃, and the sintering pressure is 30MPa.

6. The method for preparing lightweight, high-damping Ti6Al4V alloy according to claim 1, characterized in that, Includes the following steps: Screening for Ti6Al4V powder and Er powder with a particle size of less than 50 micrometers; The screened Ti6Al4V powder and Er powder were mechanically ball-milled and mixed. The powder that has undergone mixing is freeze-dried. The freeze-dried powder is then hot-pressed and sintered under vacuum.

7. The method for preparing lightweight, high-damping Ti6Al4V alloy according to claim 6, characterized in that, The vacuum degree of hot pressing sintering is 0.01-0.1 Pa, the hot pressing sintering temperature is 900~1100℃, the heating rate is 10℃ / min, the hot pressing sintering pressure is 20~40MPa, and the hot pressing sintering holding time is 1-3 hours.

8. A lightweight, high-damping Ti6Al4V alloy prepared by any one of the preparation methods described in claims 1-7.

9. The lightweight, high-damping Ti6Al4V alloy according to claim 8, characterized in that, The peak damping of the alloy can reach 0.0110.

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