High-strength and high-damping titanium-based eutectic alloy and preparation method thereof

Abstract

The application provides a high-strength and high-damping titanium-based eutectic alloy, and belongs to the field of new material research and preparation. 70‑x‑y Nb x Zr y Fe 30 ) 100‑a‑b Sn a O b Wherein, 0.1<=x<=5, 0.1<=y<=5, 0.1<=a<=5, 0.1<=b<=1. Commercial industrial pure Ti, Fe, Nb, Zr, Sn and TiO2 are used as raw materials to prepare the target alloy, vacuum arc melting technology is used to melt and prepare the alloy ingot, and then copper mold casting technology is used to obtain the required alloy plate. The alloy of the application is (near) eutectic composition, the alloy melt has good fluidity and excellent casting performance; the eutectic structure formed by the alloy can have Snoek relaxation coupling effect, so that the material has better damping performance (Q ‑1 >0.03), the room temperature compression yield strength of the material is more than 2GPa, and in addition, the addition of a small amount of Nb, Zr and Sn elements can refine the alloy structure, and the mechanical properties and damping performance of the alloy are obviously improved.

Description

TECHNICAL FIELD

[0001] The present application relates to a high-strength and high-damping titanium-based eutectic alloy material and a preparation method thereof, and belongs to the field of new material research and preparation. BACKGROUND

[0002] Reasonable use of damping materials can effectively solve the problems of vibration and noise generated during the operation of mechanical equipment. Damping alloys generally have good structural stability, high strength and high damping performance. In particular, titanium-based damping alloys have high damping, light weight and corrosion resistance, and have broad application prospects in the fields of aviation, aerospace, vehicles and marine engineering.

[0003] Titanium-based damping alloys can be divided into three categories: phase transition type, twinning type and Snoek type. Among them, the first two types are basically Ti-Ni-based series alloys based on thermal elastic martensitic phase transition, and their yield strength is generally low (<500 MPa) due to the easy occurrence of deformation-induced martensitic phase transition; while the Snoek type damping alloy is mainly Ti-Nb-based alloy with body-centered cubic structure, which relies on the reciprocating motion of interstitial atoms in octahedral positions in the structure under stress-induced, consumes energy, and achieves the effect of vibration and noise reduction. People generally believe that Snoek-type titanium-based alloys with high damping performance should have a stable body-centered cubic single-phase structure, so a large amount of high-cost and high-melting-point β-Ti stabilizing elements such as Nb, Mo and Ta are introduced into the alloy. For example, the Ti-25Nb-1.5O damping alloy, in which the content of Nb is as high as 25at.%. This will cause high raw material cost and difficult melting and preparation of the alloy; at the same time, the strength of β-Ti single-phase titanium alloy is generally low, and the room temperature yield strength is usually less than 800 MPa, which is difficult to meet the development needs of high-strength and high-damping alloys in the fields of aerospace, ships and other fields, and it is necessary to develop low-cost, easy-to-prepare and high-strength Snoek-type titanium-based damping alloys with excellent comprehensive performance.

[0004] In view of this, people have made various attempts, but have not achieved satisfactory results. For example, Xie Zhifeng et al. (CN104109778B) prepared Ti-Nb-Fe-O alloy by replacing Nb with base metal Fe, which to some extent reduces the raw material cost of the alloy, but the body-centered cubic single-phase structure is still maintained in the alloy structure, so the content of Fe must be strictly controlled below 25wt.%, to avoid the precipitation of TiFe ordered phase in the alloy; at the same time, in order to ensure the stability of the body-centered cubic phase in the alloy, the content of Nb element is higher than 10wt.%, which leads to the presence of high content of high-cost metal Nb in the alloy. And its preparation process includes: alloy ingot casting, alloy homogenization treatment, rolling deformation, recrystallization annealing, surface grinding and polishing, surface oxidation / diffusion, etc., the preparation process is complicated, the parameters are many, and the preparation cost is high. It is particularly important to note that the alloy prepared by this method is still a single-phase structure, and the problem of low strength has not been solved.

[0005] The patent applicant notes that: Ti 70 Fe 30 (at.%) alloy is a kind of high-strength eutectic titanium alloy, and the yield strength is generally higher than 1.5GPa; at the same time, Fe is an effective β-Ti stabilizing element, and B2-TiFe phase has similar body-centered cubic atomic arrangement characteristics with β-Ti, and the two-phase eutectic structure may induce Snoek relaxation coupling effect, so that the alloy shows high damping performance. Therefore, the patent introduces oxygen element in Ti 70 Fe 30 eutectic alloy, and prepares O-containing eutectic alloy composed of B2-TiFe ordered phase and β-Ti by melting and casting method; further through Sn, Zr, Nb and other elements micro-alloying, the morphology of eutectic structure is controlled, so as to obtain titanium-based eutectic alloy with high yield strength (σ>2GPa) and high damping value (Q -1 >0.03). The present application provides a new way for the research and development of low-cost, high-strength Snoek-type titanium-based high-damping new alloy. SUMMARY

[0006] The purpose of the present application is to overcome the common problems of Snoek-type titanium-based damping alloy materials, such as low strength, difficult preparation and high raw material cost.

[0007] In order to achieve the above-mentioned purpose, the technical scheme adopted by the present application is:

[0008] A high-strength and high-damping titanium-based eutectic alloy mainly comprises Ti, Fe, and a small amount of Nb, Zr, Sn and O components, and the atomic percentage composition general formula is (Ti 70-x-y Nb x Zr y Fe 30 ) 100-a-bSn a O b wherein 0.1≤x≤5, 0.1≤y≤5, 0.1≤a≤5, 0.1≤b≤1, the damping performance Q -1 value of the alloy is 0.030-0.035; the compression yield strength at room temperature is above 2 GPa.

[0009] A preparation method of a high-strength and high-damping titanium-based eutectic alloy, the preparation method taking commercial industrial pure Ti, Fe, Nb, Zr, Sn and TiO2 as raw materials, and preparing the target alloy with the atomic percentage composition of (Ti 70-x-y Nb x Zr y Fe 30 ) 100-a-b Sn a O b First, the vacuum arc melting technology is used to melt the alloy ingot, and then the copper mold casting technology is used to obtain the required alloy plate. The specific process includes the following steps:

[0010] Step one: alloy ingot melting

[0011] Commercial industrial pure Ti, Fe, Nb, Zr, Sn and TiO2 are taken as raw materials, and the target alloy with the atomic percentage composition of (Ti 70-x-y Nb x Zr y Fe 30 ) 100-a-b Sn a O b is converted, weighed and prepared; first, the raw materials are placed in the water-cooled copper crucible of the arc melting furnace, then vacuumized to 1-10 Pa, and 0.01-0.10 MPa of industrial pure Ar gas is filled for melting; the working current of the arc melting is 250-290 A, and the target alloy ingot with uniform composition is obtained after repeated melting for multiple times. The mass loss rate of the alloy ingot before and after melting is controlled within 10 per thousand.

[0012] Step two: alloy plate casting

[0013] The target alloy ingot obtained in the above step is placed in the melting crucible of the copper mold casting, vacuumized to 1-10 Pa, and 0.01-0.10 MPa of industrial pure argon gas is filled as the protective gas; the arc melting and copper mold casting technology are used to melt the alloy ingot under the arc with a working current of 380-400 A, and then pour it into the water-cooled copper mold chamber, and the mold is cooled to room temperature, and the plate-shaped sample is taken out. The X-ray diffractometer, scanning electron microscope, dynamic mechanical analyzer and universal mechanical testing machine are used to characterize and test the phase composition, microstructure, internal friction and mechanical properties of the alloy plate at room temperature.

[0014] The principle of the present invention is that the Snoek relaxation mechanism is based on the reciprocating motion of small atoms (such as O, C, N, etc.) in the octahedral interstitial position in the body-centered cubic structure under stress induction, consuming energy and showing a damping effect; and Fe is the most effective β-stabilizing element in titanium alloys. 70 Fe 30 The composition of the alloy is close to that of the B2-TiFe alloy, enabling the stable coexistence of the eutectic β-Ti and B2-TiFe phases. Both the ordered β-Ti and B2-TiFe phases are based on a body-centered cubic atomic arrangement, and their eutectic alloys contain interstitial sites similar to those in single-phase body-centered cubic alloys. Solid solution of a certain amount of atomic oxygen can trigger the Snoek relaxation coupling effect, resulting in high damping properties. The interstitial solid solution strengthening effect of oxygen further enhances the alloy's strength. However, excessive oxygen content can lead to the formation of a complex TiFeO phase, degrading the alloy's damping properties. Therefore, the oxygen content is controlled to 0.1-1.0 at.%. In terms of mechanical properties, the eutectic structure of the β-Ti and B2-TiFe phases exhibits higher strength than that of the single-phase β phase. The introduction of Sn effectively refines the eutectic lamellar structure, further enhancing the alloy's strength. Sn and Zr both have large atomic radii (0.155 nm for Sn and 0.160 nm for Zr, respectively, while Ti and Fe have atomic radii of 0.146 nm and 0.126 nm, respectively). These elements exhibit a strong solid solution strengthening effect in the alloy, effectively increasing its strength. However, excessive Sn addition can produce a Ti3Sn phase, reducing the alloy's internal friction. Excessive Zr addition can disrupt the alloy's eutectic coupling structure, generating other phases. Therefore, their contents are controlled between 0.1% and 5.0 at.%. Nb is an effective β-stabilizing element in titanium alloys. Its addition can further stabilize the β-Ti phase in the eutectic structure and improve the alloy's structural stability. However, Nb's melting point is nearly 800°C higher than Ti's. High Nb additions can complicate arc melting and preparation. Furthermore, Nb is a high-cost metal, and increasing its content significantly increases the cost of the alloy's raw materials. Therefore, its addition level is controlled between 0.1% and 5.0 at.%.

[0015] The advantages and beneficial effects of the present invention are:

[0016] (1) The alloy is a (near) eutectic composition, with a base metal Fe content of approximately 30 at.%. The alloy melt has good fluidity and excellent casting properties. A Snoek-type titanium-based eutectic alloy with high strength and high damping properties can be directly obtained through arc melting and copper mold casting technology. This can effectively reduce the raw material cost and preparation difficulty of the material.

[0017] (2) Since both β-Ti and B2-TiFe ordered phases are based on body-centered cubic atomic arrangement, satisfying the structural basis of Snoek-type relaxation mechanism, the eutectic structure formed thereby can have Snoek relaxation coupling effect, thus making the material have better damping performance (Q -1 >0.03).

[0018] (3) The introduction of Fe leads to the formation of β-Ti and B2-TiFe eutectic structure, and the fine lamellar structure makes the alloy have high mechanical strength. Meanwhile, the solid solution of Fe in β-Ti can further stabilize the body-centered cubic structure and induce solid solution strengthening effect, and the room temperature compressive yield strength is more than 2 GPa. In addition, the addition of a small amount of Nb, Zr and Sn elements can also improve the structural stability of β phase and refine the alloy structure. Finally, the submicron scale lamellar eutectic structure with excellent structure stability is obtained, and the mechanical and damping properties of the alloy are obviously improved. BRIEF DESCRIPTION OF DRAWINGS

[0019] Figure 1 X-ray diffraction spectrum (a) of the alloy of Example 3 and secondary electron morphology (b) of the lamellar eutectic structure thereof.

[0020] Figure 2 The internal friction-temperature spectrum of the alloy material of Example 3.

[0021] Figure 3 The room temperature compressive stress-strain curve of the alloy material of Example 3. DETAILED DESCRIPTION

[0022] The preparation process and implementation effect of the material of the present application will be further described below in combination with six specific examples.

[0023] Example 1 (Ti 69.8 Nb 0.1 Zr 0.1 Fe 30 ) 99.8 Sn 0.1 O 0.1 alloy

[0024] Step one: melting of the alloy ingot

[0025] Commercial industrial pure Ti, Fe, Nb, Zr, Sn and TiO2 are used as raw materials, and the atomic percentage composition (Ti 69.8 Nb 0.1 Zr 0.1 Fe 30 ) 99.8 Sn 0.1 O 0.1Convert, weigh, prepare 100 g of target alloy; first, the raw materials are placed in the water-cooled copper crucible of the arc melting furnace, then vacuumed to 7 Pa, filled with 0.05 MPa of industrial pure argon for melting; the working current of the arc melting is 250 A, and the repeated melting is 4 times, so that the (Ti 69.8 Nb 0.1 Zr 0.1 Fe 30 ) 99.8 Sn 0.1 O 0.1 alloy ingot. The mass loss rate of the alloy ingot before and after melting is 5 parts per thousand.

[0026] Step two: casting of alloy plate

[0027] The (Ti 69.8 Nb 0.1 Zr 0.1 Fe 30 ) 99.8 Sn 0.1 O 0.1 alloy ingot is placed in a water-cooled copper crucible for copper mold casting, vacuumed to 5 Pa, and then filled with 0.05 MPa of industrial pure argon as a protective gas. Under the arc with a working current of 380 A, the alloy ingot is melted and poured into the water-cooled copper mold chamber, and after the mold is cooled to room temperature, the plate-shaped sample is obtained.

[0028] The X-ray diffraction test results of the alloy material show that the plate-shaped sample is a dual-phase alloy with β-Ti phase and B2-TiFe phase, the eutectic structure lamella thickness is about 2 μm, and the internal friction peak value Q -1 of the material is 0.031 (0.1 Hz), and the compression yield strength of the alloy is 2.07 GPa and the elongation is 7.5% in the room temperature uniaxial compression experiment.

[0029] Example 2 (Ti 69.8 Nb 0.1 Zr 0.1 Fe 30 ) 94 Sn5O1 alloy

[0030] Step one: melting of alloy ingot

[0031] Commercial industrial pure Ti, Fe, Nb, Zr, Sn and TiO2 are used as raw materials, and the atomic percentage composition (Ti 69.8 Nb 0.1 Zr 0.1 Fe 30 ) 94Sn5O1 alloy ingot. The mass loss rate of the alloy ingot before and after melting is 3 parts per thousand. 69.8 Nb 0.1 Zr 0.1 Fe 30 ) 94 Sn5O1 alloy ingot. The mass loss rate of the alloy ingot before and after melting is 3 parts per thousand.

[0032] Step two: Casting of alloy plate

[0033] The (Ti 69.8 Nb 0.1 Zr 0.1 Fe 30 ) 94 Sn5O1 alloy ingot is placed in a water-cooled copper crucible for copper mold casting, vacuumed to 6 Pa, and then filled with 0.05 MPa of industrial pure argon as a protective gas. Under an electric arc with a working current of 380 A, the alloy ingot is melted and poured into a water-cooled copper mold chamber. After the mold cools to room temperature, the plate-shaped sample is obtained.

[0034] The X-ray diffraction test results of the alloy material show that the plate-shaped sample is a dual-phase alloy with β-Ti phase and B2-TiFe phase. The eutectic structure lamella thickness is about 0.5 μm. The internal friction peak value Q -1 of the material is 0.031 (0.1 Hz), and the compression yield strength of the alloy is 2.13 GPa and the elongation is 9.0% in the room temperature uniaxial compression experiment.

[0035] Example 3 (Ti 64.9 Nb5Zr 0.1 Fe 30 ) 97.5 Sn2O 0.5 alloy

[0036] Step one: Melting of alloy ingot

[0037] Commercially available industrial pure Ti, Fe, Nb, Zr, Sn and TiO2 are used as raw materials, and the atomic percentage composition (Ti 64.9 Nb5Zr 0.1 Fe 30 ) 97.5 Sn2O 0.5Convert, weigh, prepare 100 g of target alloy; first, place the raw materials in the water-cooled copper crucible of the arc melting furnace, then vacuumize to 7 Pa, fill in 0.05 MPa of industrial pure argon for melting; the working current of the arc melting is 280 A, repeatedly melt for 4 times, and obtain the (Ti 64.9 Nb5Zr 0.1 Fe 30 ) 97.5 Sn2O 0.5 alloy ingot. The mass loss rate of the alloy ingot before and after melting is 6 parts per thousand.

[0038] Step two: casting of alloy plate

[0039] Place the (Ti 64.9 Nb5Zr 0.1 Fe 30 ) 97.5 Sn2O 0.5 alloy ingot in the water-cooled copper crucible of the copper mold casting, vacuumize to 6 Pa, then fill in 0.05 MPa of industrial pure argon as the protective gas, under the arc with a working current of 400 A, use the arc melting and copper mold casting technology, melt the alloy ingot and pour it into the water-cooled copper mold chamber, after the mold cools to room temperature, take out the plate-shaped sample.

[0040] The X-ray diffraction test of the alloy material is shown in Fig. a of the accompanying drawings, Figure 1 The sample presents the diffraction peak characteristics of β-Ti phase and B2-TiFe phase, the morphology observed by scanning electron microscope is shown in Fig. b of the accompanying drawings, Figure 1 The eutectic structure lamella thickness is about 0.2 μm, the internal friction peak value Q -1 of the material at 0.1 Hz is 0.032 (Fig. of the accompanying drawings, Figure 2 ), the compression yield strength of the alloy is 2.21 GPa and the elongation is 7.6% (Fig. of the accompanying drawings, Figure 3 ) in the room temperature uniaxial compression experiment.

[0041] Example 4 (Ti 64.9 Nb 0.1 Zr5Fe 30 ) 97.5 Sn2O 0.5 alloy

[0042] Step one: melting of alloy ingot

[0043] Use commercial industrial pure Ti, Fe, Nb, Zr, Sn and TiO2 as raw materials, and the atomic percentage composition (Ti 64.9 Nb 0.1 Zr5Fe 30 ) 97.5 Sn2O 0.5Convert, weigh, and prepare 100 g of the target alloy; first, place the raw materials in the water-cooled copper crucible of the arc melting furnace, then vacuumize to 7 Pa, and fill in 0.05 MPa of industrial pure argon for melting; the working current of the arc melting is 260 A, and the repeated melting is 4 times, to obtain a (Ti 64.9 Nb 0.1 Zr5Fe 30 ) 97.5 Sn2O 0.5 alloy ingot. The mass loss rate of the alloy ingot before and after melting is 5 parts per thousand.

[0044] Step two: casting of the alloy plate

[0045] Place the (Ti 64.9 Nb 0.1 Zr5Fe 30 ) 97.5 Sn2O 0.5 alloy ingot in the water-cooled copper crucible of the copper mold casting, vacuumize to 7 Pa, and then fill in 0.05 MPa of industrial pure argon as the protective gas; under the arc with a working current of 390 A, the alloy ingot is melted and poured into the water-cooled copper mold chamber, and the mold is cooled to room temperature, and then the plate-shaped sample is obtained.

[0046] The X-ray diffraction test result of the alloy material shows that the plate-shaped sample is a dual-phase alloy with β-Ti phase and B2-TiFe phase, the eutectic structure lamella thickness is about 1.2 μm, the internal friction peak value Q -1 of the material is 0.033 (0.1 Hz) measured by the secondary resonance method, and the compression yield strength of the alloy is 2.01 GPa and the elongation is 10.3% measured by the room temperature uniaxial compression experiment.

[0047] Example 5 (Ti 60 Nb5Zr5Fe 30 ) 97 Sn2O1 alloy

[0048] Step one: melting of the alloy ingot

[0049] Commercially available industrial pure Ti, Fe, Nb, Zr, Sn, and TiO2 are used as raw materials, and 100 g of the target alloy is prepared according to the atomic percentage composition (Ti 60 Nb5Zr5Fe 30 ) 97 Sn2O1; first, place the raw materials in the water-cooled copper crucible of the arc melting furnace, then vacuumize to 6 Pa, and fill in 0.05 MPa of industrial pure argon for melting; the working current of the arc melting is 290 A, and the repeated melting is 4 times, to obtain a (Ti 60 Nb5Zr5Fe30 ) 97 Sn2O1 alloy ingot. The mass loss rate of the alloy ingot before and after smelting is 0.5%.

[0050] Step 2: Casting of alloy sheet

[0051] (Ti 60 Nb5Zr5Fe 30 ) 97 The Sn2O1 alloy ingot was placed in a water-cooled copper crucible cast in a copper mold, evacuated to 7Pa, and then filled with 0.05MPa of industrial pure argon as a protective gas. Under an arc working current of 400A, arc melting and copper mold casting technology were used to melt the alloy ingot and pour it into the water-cooled copper mold cavity. After the mold cooled to room temperature, it was taken out to obtain a plate-shaped sample.

[0052] The X-ray diffraction test results of the alloy material show that the plate sample is a dual-phase alloy with β-Ti phase and B2-TiFe phase. The thickness of the eutectic layer observed by scanning electron microscopy is about 0.5μm. The internal friction peak Q of the material measured by the sub-resonance method is -1 The compressive yield strength of the alloy measured by uniaxial compression test at room temperature is 2.32 GPa and the elongation is 6.5%.

[0053] Example 6 (Ti 65 Nb3Zr2Fe 30 ) 97 Sn2O1 alloy

[0054] Step 1: Melting of alloy ingots

[0055] Commercial industrial pure Ti, Fe, Nb, Zr, Sn and TiO2 are used as raw materials, and the atomic percentage composition (Ti 65 Nb3Zr2Fe 30 ) 97 Sn2O1 was converted, weighed, and 100g of the target alloy was prepared; the raw materials were first placed in a water-cooled copper crucible in an arc melting furnace, then vacuumed to 6Pa and filled with 0.05MPa industrial pure argon for melting; the arc melting current was 280A, and the melting was repeated 4 times to obtain a uniform composition (Ti 65 Nb3Zr2Fe 30 ) 97 Sn2O1 alloy ingot. The mass loss rate of the alloy ingot before and after smelting is 0.5%.

[0056] Step 2: Casting of alloy sheet

[0057] (Ti 65 Nb3Zr2Fe 30 ) 97The Sn2O1 alloy ingot is placed in a water-cooled copper crucible cast by copper mold, vacuumized to 7 Pa, then filled with 0.05 MPa of industrial pure argon as a protective gas, under an arc with a working current of 400 A, the alloy ingot is melted and poured into a water-cooled copper mold chamber by using arc melting and copper mold casting technology, after the mold is cooled to room temperature, a plate-shaped sample is obtained.

[0058] The X-ray diffraction test result of the alloy material shows that the plate-shaped sample is a dual-phase alloy with β-Ti phase and B2-TiFe phase, the eutectic structure lamella thickness is about 0.9 μm observed by a scanning electron microscope, the internal friction peak value Q -1 of the material is 0.034 (under 0.1 Hz), the compression yield strength of the alloy is 2.16 GPa and the elongation is 7.9% measured by a room temperature uniaxial compression experiment.

[0059] The above-mentioned examples only express the embodiments of the present application, but cannot be understood as the limitation of the scope of the present application patent, it should be noted that, for those skilled in the art, without departing from the concept of the present application, a number of modifications and improvements can be made, which all belong to the protection scope of the present application.

Claims

1. A high-strength, high-damping titanium-based eutectic alloy, characterized by, The high-strength and high-damping titanium-based eutectic alloy mainly comprises Ti, Fe, and a small amount of Nb, Zr, Sn, and O components; the atomic percentage component general formula of the high-strength and high-damping titanium-based eutectic alloy is (Ti 70-x-y Nb x Zr y Fe 30 ) 100-a-b Sn a O b , wherein 0.1≤x≤5, 0.1≤y≤5, 0.1≤a≤5, and 0.1≤b≤1.

2. The high-strength, high-damping titanium-based eutectic alloy of claim 1, wherein, The damping performance Q of the high-strength high-damping titanium-based eutectic alloy -1 is 0.030-0.035; the room temperature compression yield strength is above 2 GPa.

3. A method of producing the high-strength, high-damping titanium-based eutectic alloy according to any one of claims 1 to 2, characterized by, The preparation method uses commercial industrial pure Ti, Fe, Nb, Zr, Sn and TiO2 as raw materials, and prepares the target alloy with the atomic percentage components of (Ti 70-x-y Nb x Zr y Fe 30 ) 100-a-b Sn a O b First, the vacuum arc melting technology is used to melt and cast the alloy ingot, and then the copper mold casting technology is used to obtain the required alloy plate.

4. The method of claim 3, wherein the high-strength, high-damping titanium-based eutectic alloy is prepared by the following steps of: The specific process comprises the following steps: ​ Step one: melting alloy ingot Commercially available industrial purity Ti, Fe, Nb, Zr, Sn and TiO2 are used as raw materials, which are converted, weighed and prepared into the target alloy. The raw materials are placed in a water-cooled copper crucible of an electric arc melting furnace, vacuumed to 1-10 Pa, and filled with 0.01-0.10 MPa of industrial pure argon gas for electric arc melting. The alloy ingot is repeatedly melted for multiple times to obtain a target alloy ingot with uniform composition. Step two: casting of alloy plate The target alloy ingot obtained in step one is placed in a melting crucible for copper mold casting, vacuumed to 1-10 Pa, and filled with 0.01-0.10 MPa of industrial pure argon gas as a protective gas. The alloy ingot is melted and poured into a water-cooled copper mold chamber under an electric arc with a working current of 380-400 A. The mold is cooled to room temperature, and the plate-shaped sample is obtained.

5. The method of claim 4, wherein the high-strength, high-damping titanium-based eutectic alloy is prepared by the following steps of: In step one, the working current of the electric arc melting is 250-290 A, and the mass loss rate of the alloy ingot before and after melting is controlled within 10 parts per thousand. ​

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