A high-damping zirconium-based amorphous composite material and a preparation method thereof

Abstract

The application relates to a high-damping zirconium-based amorphous composite material and a preparation method thereof, and belongs to the field of functional material research and preparation. 63.5‑ a M a Al9Cu 23 Fe 4.5 ) 100‑b X b , M=Nb, Ti or Hf, X=O, C or B, wherein 0.5<=a<=4.5, 0.1<=b<=0.5. In the preparation process, industrial pure Zr, M, Fe, Al, Cu and N are used as raw materials, vacuum arc melting technology is used to melt and prepare alloy ingots, and the required alloy material is obtained through copper mold casting technology, and the damping performance Q ‑1 value of the material is 0.011-0.015. The amorphous composite material of the application has the performance advantages of the material itself, high damping performance, and expanded application fields and ranges of the amorphous material; the material has more excellent room-temperature plastic deformation capacity and fracture strength; the Snoek relaxation peak value temperature of the material is lower than the glass transition temperature of the amorphous matrix, the material is used at the optimal damping temperature, the alloy has excellent structure stability, and is not prone to glass transition or crystallization instability.

Description

TECHNICAL FIELD

[0001] The present application relates to a high-damping zirconium-based amorphous composite material and a preparation method thereof, and belongs to the field of metal functional material research and preparation. BACKGROUND

[0002] Damping alloy is a kind of functional alloy which depends on its structure or physical properties to consume energy under periodic load, thereby achieving the effect of vibration reduction. The use of damping alloy in mechanical equipment can effectively solve the problem of vibration, thereby improving the precision, service stability and safety of mechanical parts.

[0003] Recently, a new type of damping alloy with body-centered cubic structure has been found, which can consume energy (i.e. Snoek relaxation mechanism) by the reciprocating motion of small atoms such as O, C and B at interstitial sites under load, thereby achieving the function of vibration reduction. Since the reciprocating motion of small atoms hardly damages the alloy matrix, the damping alloy based on Snoek relaxation mechanism has a long service life.

[0004] Amorphous alloy is a special alloy with short-range order and long-range disorder in structure. Compared with crystalline alloy, it often has better mechanical, physical and chemical properties, and has shown broad application prospects in the fields of machinery, medicine, chemical industry and aviation.

[0005] However, so far there has been no study on the damping performance of amorphous alloy materials based on Snoek relaxation mechanism. We noticed that there are a large number of tetrahedral and octahedral interstitial sites in the short-range structure of amorphous alloy and the structure of its corresponding crystallized phase, which can provide small atoms such as O, C and B with solid solution and migration, making it possible to carry the Snoek relaxation mechanism. Therefore, by combining the performance advantages of amorphous materials such as high strength and high corrosion resistance, we developed an alloy with high damping performance based on amorphous alloy, which will further expand the application fields and range of amorphous alloy materials.

[0006] Since amorphous alloy is extremely sensitive to impurity elements (such as O), the presence of impurity elements will generally sharply reduce the amorphous forming ability of the alloy, so the purity of the alloy raw materials and the preparation conditions are strictly controlled to avoid their introduction. The present patent applicant takes a Zr-based alloy with high oxygen solubility and high amorphous forming ability as the matrix, controls the composition and structure to make the endogenously dispersed body-centered cubic structure second phase form an amorphous-based composite material, and intentionally dissolves a certain amount of small atoms such as O, C and B into the composite material. On this basis, the effect of coupling the body-centered cubic structure second phase with the amorphous matrix to induce the Snoek relaxation mechanism is achieved, realizing the development of a new amorphous-based alloy material with high damping (Q -1 >0.01) performance. This provides a new idea and approach for the development and application of amorphous-based composite materials in the damping field. SUMMARY

[0007] The purpose of the present application is to broaden the application field and range of amorphous materials, develop a new type of zirconium-based amorphous composite material with high damping performance, and provide a candidate system for high-strength and high-toughness damping alloy materials.

[0008] In order to achieve the above-mentioned purpose, the technical scheme adopted by the present application is:

[0009] A high-damping zirconium-based amorphous composite material, specifically a Snoek-type high-damping zirconium-based amorphous composite material containing a body-centered cubic structure second phase. The constituent elements include Zr, M, Fe, Al, Cu, and X. The atomic percentage composition of the material is generally represented as: (Zr 63.5-a M a Al9Cu 23 Fe 4.5 ) 100-b X b , M = Nb, Ti or Hf, X = O, C or B, wherein 0.5 ≤ a ≤ 4.5 and 0.1 ≤ b ≤ 0.5. The damping performance Q -1 of the high-damping amorphous-based composite material is 0.011-0.015.

[0010] A preparation method of a high-damping zirconium-based amorphous composite material. The preparation method uses commercial industrial pure Zr, M, Fe, Al, Cu, and N as raw materials (wherein M is Nb, Ti or Hf, and N is C, B or ZrO2, wherein ZrO2 provides O in the constituent elements). The target alloy is prepared with atomic percentage composition (Zr 63.5-a M a Al9Cu 23 Fe 4.5 ) 100-b X b . First, vacuum arc melting technology is used to melt and cast the alloy ingot. Then, copper mold casting technology is used to obtain the required alloy material plate. The specific process includes the following steps:

[0011] Step 1: Melting of alloy ingot

[0012] Commercial industrial pure Zr, M, Fe, Al, Cu, and N are used as raw materials to prepare the target alloy with atomic percentage composition (Zr 63.5- a M a Al9Cu 23 Fe 4.5 ) 100-b X bThe target alloy is weighed and placed in a water-cooled copper crucible of an arc melting furnace, then vacuumized to 1-10 Pa, and filled with 0.01-0.10 MPa of industrial pure argon for melting; the working current of the arc melting is 260-290 A, and the alloy ingot is repeatedly melted for multiple times to obtain an alloy ingot with uniform composition.

[0013] Step two: suction casting of the alloy plate

[0014] The target alloy ingot obtained in step one is placed in a water-cooled copper crucible for negative pressure suction casting, vacuumized to 1-10 Pa, and filled with 0.01-0.10 MPa of industrial pure argon as a protective gas; the target alloy ingot is melted and suctioned into a water-cooled copper mold chamber under an arc with a working current of 360-380 A, and the mold is cooled to room temperature to obtain a plate-shaped sample; and the sample is characterized and tested for phase composition, microstructure, thermal performance and internal friction performance at room temperature by using an X-ray diffractometer, a scanning electron microscope, a thermal analyzer and a dynamic mechanical analyzer.

[0015] The principle of the application is as follows:

[0016] The low-cost Zr 63.5 Al9Cu 23 Fe 4.5 The alloy is based on the introduction of alloying elements Ti, Nb or Hf and interstitial elements O, C or B into the alloy, and the microstructure is controlled to form an amorphous-based composite material with an endogenous and dispersed body-centered cubic second phase in the amorphous alloy, so that the Snoek relaxation mechanism is triggered by the coupling of the body-centered cubic second phase and the amorphous matrix, so that the alloy has high damping performance, and also has the advantages of high strength and high corrosion resistance of the amorphous alloy itself. The effects of alloying elements and interstitial elements on the microstructure and performance of the alloy are analyzed as follows:

[0017] There are at least one set of positive mixing enthalpy (or mixing enthalpy is 0) atomic pairs between Ti, Nb or Hf elements and Zr, Cu elements, which makes the addition of Ti, Nb or Hf elements conducive to the preferential precipitation of the body-centered cubic solid solution β-Zr phase in the alloy melt, but when the addition amount is too high, it will affect the formation of the amorphous matrix, so the addition amount is controlled between 0.5-4.5 at. %.

[0018] The main role of O, C or B elements in the alloy is to carry the Snoek relaxation mechanism, which is dissolved into the interstitial position of the body-centered cubic second phase and the amorphous matrix component, and will undergo reciprocating motion under stress induction, so that the amorphous-based composite material exhibits high damping performance, but excessive addition will cause the amorphous forming ability of the alloy matrix to decrease sharply, so the content is controlled in the range of 0.1-0.5 at. %.

[0019] The advantages and beneficial effects of the present application are:

[0020] (1) The present application has high damping performance while maintaining the performance advantages of the amorphous matrix composite material due to the coupling of the body-centered cubic structure second phase and the Snoek relaxation mechanism, which expands the application field and range of amorphous materials.

[0021] (2) The material has excellent room temperature plastic deformation ability and fracture strength due to the presence of body-centered cubic structure solid solution ductile phase particles in the amorphous matrix.

[0022] (3) The Snoek relaxation peak temperature of the material is lower than the glass transition temperature of the amorphous matrix, so the material is used at the optimal damping temperature, and the alloy has excellent microstructure stability and is not prone to glass transition or crystallization instability. BRIEF DESCRIPTION OF DRAWINGS

[0023] Figure 1 is the X-ray diffraction spectrum (a) of the alloy material of Example 1 and the backscattered electron image (b) of its microstructure.

[0024] Figure 2 is the DSC curve of the alloy material of Example 1.

[0025] Figure 3 is the internal friction-temperature spectrum of the alloy material of Example 1. DETAILED DESCRIPTION

[0026] The preparation process and implementation effects of the material of the present application are further described below in combination with six specific examples.

[0027] Example 1 (Zr 63 Nb 0.5 Al9Cu 23 Fe 4.5 ) 99.5 O 0.5

[0028] Commercial Zr, Nb, Fe, Al, Cu and ZrO2 were used as raw materials to prepare the target alloy with atomic percentage composition of (Zr 63 Nb 0.5 Al9Cu 23 Fe 4.5 ) 99.5 O 0.5 The weighed raw materials were placed in a water-cooled copper crucible of an arc melting furnace, then vacuumized to 6 Pa, and then filled with 0.05 MPa of industrial pure argon for melting; the working current of the arc melting was 260 A, and the repeated melting was performed 4 times to obtain a uniform (Zr 63 Nb 0.5 Al9Cu23 Fe 4.5 ) 99.5 O 0.5 The alloy ingot has a mass loss rate of 2 parts per thousand before and after melting.

[0029] Step two: suction casting of alloy plate

[0030] (Zr 63 Nb 0.5 Al9Cu 23 Fe 4.5 ) 99.5 O 0.5 The alloy ingot is placed in a water-cooled copper crucible for negative pressure suction casting, vacuumized to 5 Pa, filled with 0.05 MPa of industrial pure argon as a protective gas, and then melted by using arc melting and copper mold suction casting technology. After the target alloy ingot is melted under an arc with a working current of 360 A, the molten alloy is suctioned into a water-cooled copper mold chamber, the mold is cooled to room temperature, and then a plate-shaped sample is obtained.

[0031] The X-ray diffraction test result of the alloy material is shown in FIG. a of Figure 1 , indicating that the sample is an amorphous-based composite material having a β-Zr phase and an amorphous matrix. The backscattered electron image is shown in FIG. b of Figure 1 , and irregularly shaped second phases distributed on the amorphous matrix can be observed. Thermal analysis shows that the glass transition temperature is 385 ℃ Figure 2 . As shown in FIG. Figure 3 , the internal friction peak value Q -1 of the sample is 0.015 (0.1 Hz)

[0032] Example 2 (Zr 60.5 Nb3Al9Cu 23 Fe 4.5 ) 99.7 O 0.3

[0033] Commercial Zr, Nb, Fe, Al, Cu and ZrO2 are used as raw materials to prepare a target alloy with atomic percentage components of (Zr 60.5 Nb3Al9Cu 23 Fe 4.5 ) 99.7 O 0.3 The weighed raw materials are placed in a water-cooled copper crucible of an arc melting furnace, then vacuumized to 6 Pa, and filled with 0.05 MPa of industrial pure argon for melting. The working current of the arc melting is 260 A, and the alloy is repeatedly melted for 4 times to obtain a (Zr 60.5 Nb3Al9Cu 23 Fe 4.5 ) 99.7 O 0.3Alloy ingot. The mass loss rate of the alloy ingot before and after melting is 4 parts per thousand.

[0034] Step two: suction casting of alloy plate

[0035] (Zr 60.5 Nb3Al9Cu 23 Fe 4.5 ) 99.7 O 0.3 The alloy ingot is placed in a water-cooled copper crucible for negative pressure suction casting, vacuumized to 5 Pa, filled with 0.05 MPa of industrial pure argon as a protective gas, and then melted by using arc melting and copper mold suction casting technology. The target alloy ingot is melted under an arc with a working current of 360 A and then sucked into a water-cooled copper mold chamber. The mold is cooled to room temperature, and a plate-shaped sample is obtained.

[0036] The X-ray diffraction test result of the alloy material shows that the plate-shaped sample is an amorphous-based composite material with a β-Zr phase and an amorphous matrix. The backscattered electron image can observe that the amorphous matrix is distributed with irregular-shaped second phases. Thermal analysis shows that the glass transition temperature is 390°C; the internal friction peak value Q -1 is 0.012 (0.1 Hz)

[0037] Example 3 (Zr 59 Nb 4.5 Al9Cu 23 Fe 4.5 ) 99.9 O 0.1

[0038] Commercial Zr, Nb, Fe, Al, Cu and ZrO2 are used as raw materials to prepare a target alloy with atomic percentage components of (Zr 59 Nb 4.5 Al9Cu 23 Fe 4.5 ) 99.9 O 0.1 The weighed raw materials are placed in a water-cooled copper crucible of an arc melting furnace, and then vacuumized to 6 Pa and filled with 0.01-0.10 MPa of industrial pure argon for melting. The working current of the arc melting is 290 A, and the alloy is repeatedly melted for 4 times to obtain a (Zr 59 Nb 4.5 Al9Cu 23 Fe 4.5 ) 99.9 O 0.1 alloy ingot. The mass loss rate of the alloy ingot before and after melting is 3 parts per thousand.

[0039] Step two: suction casting of alloy plate

[0040] (Zr 59 Nb4.5 Al9Cu 23 Fe 4.5 ) 99.9 O 0.1 The alloy ingot was placed in a water-cooled copper crucible for negative pressure suction casting, and the vacuum was drawn to 7 Pa. 0.05 MPa of industrial pure argon gas was filled in as a protective gas. Using electric arc melting and copper mold suction casting technology, the target alloy ingot was melted and sucked into the water-cooled copper mold cavity under an electric arc with a working current of 380 A. The mold was cooled to room temperature and then taken out to obtain a plate-shaped sample.

[0041] X-ray diffraction results of the alloy material indicate that the plate-shaped sample is an amorphous matrix composite material with a β-Zr phase and an amorphous matrix. Backscattered electron microscopy reveals an irregularly shaped second phase distributed on the amorphous matrix. Thermal analysis shows that its glass transition temperature is 405℃. The peak internal friction Q0 was measured using the secondary resonance method. -1 0.011 (at 0.1Hz)

[0042] Example 3 (Zr) 63 Hf 0.5 Al9Cu 23 Fe 4.5 ) 99.9 C 0.1

[0043] Using commercially available Zr, Hf, Fe, Al, Cu, and C as raw materials, an atomic percentage composition of (Zr) was prepared. 63 Hf 0.5 Al9Cu 23 Fe 4.5 ) 99.9 C 0.1 To obtain the target alloy, the weighed raw materials were placed in a water-cooled copper crucible in an electric arc melting furnace. The furnace was then evacuated to 6 Pa and filled with 0.05 MPa of industrial pure argon gas for melting. The working current for the electric arc melting was 290 A, and the melting was repeated four times to obtain a homogeneous (Zr) alloy. 63 Hf 0.5 Al9Cu 23 Fe 4.5 ) 99.9 C 0.1 Alloy ingots. The mass loss rate of alloy ingots before and after smelting is three per thousand.

[0044] Step 2: Suction casting of alloy plates

[0045] (Zr) 63 Hf 0.5 Al9Cu 23 Fe 4.5 ) 99.9 C 0.1The alloy ingot is placed in a water-cooled copper crucible for negative pressure suction casting, vacuumized to 7 Pa, filled with 0.05 MPa of industrial pure argon as a protective gas, and then melted by using arc melting and copper mold suction casting technology. The target alloy ingot is melted under an arc with a working current of 380 A and then sucked into a water-cooled copper mold chamber. The mold is cooled to room temperature, and a plate-shaped sample is obtained.

[0046] The X-ray diffraction test result of the alloy material shows that the plate-shaped sample is an amorphous-based composite material with a β-Zr phase and an amorphous matrix. The backscattered electron image can observe that the amorphous matrix is distributed with irregular-shaped second phases. The thermal analysis shows that the glass transition temperature is 386 ℃, and the internal friction peak value Q -1 is 0.012 (under 0.1 Hz)

[0047] Example 4 (Zr 59 Hf 4.5 Al9Cu 23 Fe 4.5 ) 99.5 C 0.5

[0048] Commercial Zr, Hf, Fe, Al, Cu and C are used as raw materials to prepare a target alloy with an atomic percentage composition of (Zr 59 Hf 4.5 Al9Cu 23 Fe 4.5 ) 99.5 C 0.5 . The weighed raw materials are placed in a water-cooled copper crucible of an arc melting furnace, and then vacuumized to 6 Pa and filled with 0.05 MPa of industrial pure argon for melting. The working current of the arc melting is 290 A, and the alloy is repeatedly melted for 4 times to obtain a (Zr 59 Hf 4.5 Al9Cu 23 Fe 4.5 ) 99.5 C 0.5 alloy ingot with uniform composition. The mass loss rate of the alloy ingot before and after melting is 3 parts per thousand.

[0049] Step two: suction casting of alloy plate

[0050] The (Zr 59 Hf 4.5 Al9Cu 23 Fe 4.5 ) 99.5 C 0.5The alloy ingot is placed in a water-cooled copper crucible for negative pressure suction casting, vacuumized to 7 Pa, filled with 0.05 MPa of industrial pure argon as a protective gas, and then melted by using arc melting and copper mold suction casting technology. The target alloy ingot is melted under an arc with a working current of 380 A and then sucked into a water-cooled copper mold chamber. The mold is cooled to room temperature, and a plate-shaped sample is obtained.

[0051] The X-ray diffraction test result of the alloy material shows that the plate-shaped sample is an amorphous-based composite material with a β-Zr phase and an amorphous matrix. The backscattered electron image can observe that the amorphous matrix is distributed with irregular-shaped second phases. The thermal analysis shows that the glass transition temperature is 388 ℃, and the internal friction peak value Q -1 is 0.014 (under 0.1 Hz)

[0052] Example 5 (Zr 63 Ti 0.5 Al9Cu 23 Fe 4.5 ) 99.9 B 0.1

[0053] Commercial Zr, Ti, Fe, Al, Cu and B are used as raw materials to prepare a target alloy with an atomic percentage composition of (Zr 63 Ti 0.5 Al9Cu 23 Fe 4.5 ) 99.9 B 0.1 . The weighed raw materials are placed in a water-cooled copper crucible of an arc melting furnace, and then vacuumized to 6 Pa and filled with 0.05 MPa of industrial pure argon for melting. The working current of the arc melting is 290 A, and the alloy is repeatedly melted for 4 times to obtain a (Zr 63 Ti 0.5 Al9Cu 23 Fe 4.5 ) 99.9 B 0.1 alloy ingot with uniform composition. The mass loss rate of the alloy ingot before and after melting is 3 parts per thousand.

[0054] Step two: suction casting of alloy plate

[0055] The (Zr 63 Ti 0.5 Al9Cu 23 Fe 4.5 ) 99.9 B 0.1The alloy ingot is placed in a water-cooled copper crucible for negative pressure suction casting, vacuumized to 6 Pa, filled with 0.05 MPa of industrial pure argon as a protective gas, and then melted by electric arc and suction cast in a copper mold under an electric arc with a working current of 380 A. The alloy ingot is melted and then suctioned into the water-cooled copper mold chamber, and the mold is cooled to room temperature. The plate-shaped sample is obtained.

[0056] The X-ray diffraction test result of the alloy material shows that the plate-shaped sample is an amorphous-based composite material with a β-Zr phase and an amorphous matrix. The backscattered electron image can observe that the amorphous matrix is distributed with irregular-shaped second phases. The thermal analysis shows that the glass transition temperature is 390°C, and the internal friction peak value Q -1 is 0.011 (0.1 Hz)

[0057] Example 6 (Zr 59 Ti 4.5 Al9Cu 23 Fe 4.5 ) 99.5 B 0.5

[0058] Commercial Zr, Ti, Fe, Al, Cu and B are used as raw materials to prepare a target alloy with an atomic percentage composition of (Zr 59 Ti 4.5 Al9Cu 23 Fe 4.5 ) 99.5 B 0.5 . The weighed raw materials are placed in a water-cooled copper crucible of an electric arc melting furnace, and then vacuumized to 6 Pa and filled with 0.05 MPa of industrial pure argon for melting. The working current of the electric arc melting is 290 A, and the alloy ingot is repeatedly melted for 4 times to obtain a (Zr 59 Ti 4.5 Al9Cu 23 Fe 4.5 ) 99.5 B 0.5 alloy ingot with uniform composition. The mass loss rate of the alloy ingot before and after melting is 3 parts per thousand.

[0059] Step two: suction casting of alloy plate

[0060] The (Zr 59 Ti 4.5 Al9Cu 23 Fe 4.5 ) 99.5 B 0.5The alloy ingot is placed in a water-cooled copper crucible of negative pressure suction casting, vacuumized to 6 Pa, filled with 0.05 MPa of industrial pure argon as a protective gas, and then melted by using arc melting and copper mold suction casting technology, and then sucked into a water-cooled copper mold chamber under an arc with a working current of 380 A, and then cooled to room temperature to obtain a plate-shaped sample.

[0061] The X-ray diffraction test result of the alloy material shows that the plate-shaped sample is an amorphous-based composite material with a β-Zr phase and an amorphous matrix, and the backscattered electron image can observe that the second phase with irregular shape is distributed on the amorphous matrix, the thermal analysis shows that the glass transition temperature is 389 ℃, and the internal friction peak value Q -1 is 0.015 (0.1 Hz)

[0062] The above-described embodiments only express the implementation manners of the present application, and cannot be understood as the limitation of the scope of the patent of the present application. 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 damping zirconium-based amorphous composite material, characterized in that, The high-damping zirconium-based amorphous composite is a Snoek-type high-damping zirconium-based amorphous composite containing a second phase of a body-centered cubic structure; The constituent elements include Zr, M, Fe, Al, Cu and X; Characterized in that the atomic percentage composition general formula of the high damping zirconium-based amorphous composite material is: (Zr 63.5- a M a Al9Cu 23 Fe 4.5 ) 100-b X b , M=Nb, Ti or Hf, X=O, C or B, wherein 0.5≤a≤4.5, 0.1≤b≤0.

5.

2. The high damping zirconium-based amorphous composite material of claim 1, wherein, The high damping zirconium-based amorphous composite material has a damping performance Q -1 value is 0.011~0.

015.

3. A method of producing the high damping zirconium-based amorphous composite material according to claim 1 or 2, characterized by, The preparation method uses commercial industrial pure Zr, M, Fe, Al, Cu, N as raw materials, wherein M is Nb, Ti or Hf, N is C, B or ZrO2, and the atomic percentage components are formulated as (Zr 63.5-a M a Al9Cu 23 Fe 4.5 ) 100-b X b The target alloy, then the alloy ingot is melted by using a vacuum arc melting technique, and finally the required alloy material plate is obtained through a copper mold casting technique.

4. The method of claim 3, wherein the zirconium-based amorphous composite material has a damping capacity of 0.5 or more. The method comprises the following steps: Step one: melting of the alloy ingot The target alloy with the atomic percentage composition of (Zr 63.5- a M a Al9Cu 23 Fe 4.5 ) 100-b X b The target alloy with the atomic percentage composition of (Zr 63.5- a M a Al9Cu 23 Fe 4.5 ) 100-b X b The target alloy with the atomic percentage composition of (Zr 63.5- a M a Al9Cu 23 Fe 4.5 ) 100-b X b The target alloy with the atomic percentage composition of (Zr 63.5- a M a Al9Cu 23 Fe 4.5 ) 100-b X b The target alloy with the atomic percentage composition of (Zr 63.5- a M a Al9Cu 23 Fe 4.5 ) 100-b X b The target alloy with the atomic percentage composition of (Zr <000 Step two: suction casting of the alloy plate The target alloy ingot obtained in step one is placed in a water-cooled copper crucible for negative pressure suction casting, vacuum is drawn, and then industrial pure argon is filled as a protective gas; under an arc with a working current of 360-380 A, the target alloy ingot is melted and then sucked into a water-cooled copper mold chamber, the mold is cooled to room temperature, and then the plate-shaped sample is taken out.

5. The method of claim 4, wherein the zirconium-based amorphous composite material has a damping capacity of at least 0.5% at 20°C. In step one, the mass loss rate of the alloy ingot before and after melting is controlled to be less than 10 parts per thousand.

6. The method of claim 4, wherein the zirconium-based amorphous composite material has a damping capacity of 0.5 to 1.

5. In step one, vacuum is drawn to 1-10 Pa, and 0.01-0.10 MPa of industrial pure argon is filled for melting.

7. The method of claim 4, wherein the zirconium-based amorphous composite material has a damping capacity of 0.5 to 1.

5. In step two, vacuum is drawn to 1-10 Pa, and 0.01-0.10 MPa of industrial pure argon is filled as a protective gas.

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