A method for Si element modified high-strength titanium-based amorphous composite material

Abstract

A method for modifying a high-strength titanium-based amorphous composite material with Si element comprises the following steps: 1. selecting raw materials; 2. surface treating the raw materials; 3. batching the raw materials; placing the treated bulk raw materials together in a vacuum arc melting furnace; 4. melting the initial alloy ingot; 5. melting the target alloy ingot; 6. spray casting; cutting, polishing, and cleaning the alloy ingot obtained in step 5 to obtain an alloy material to be placed in a quartz glass tube with a small hole at the bottom; evacuating the spray casting furnace chamber and then filling it with high-purity argon gas; and heating the alloy material in the quartz glass tube by energizing the induction coil of the spray casting furnace to obtain (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9～99.7 Si 0.1～0.3 The amorphous composite material is in a rod shape. The present invention obtains uniform structure, high strength and good plasticity by introducing an appropriate amount of silicon element and controlling its process parameters, thereby solving the problem of unsatisfactory plasticity of amorphous composite materials at room temperature in the prior art.

Description

Technical Field

[0001] The invention belongs to the technical field of high-strength titanium alloy preparation, and particularly relates to a method for preparing a Si element-modified high-strength titanium-based amorphous composite material. Technical Background

[0002] Compared with crystalline alloys, titanium-based amorphous alloys have unique long-range disorder and short-range ordered atomic arrangement characteristics, and there are no defects such as grains, grain boundaries, and dislocations inside the structure. Therefore, they exhibit more excellent mechanical, physical and chemical properties, such as high strength (even up to 5GPa), high hardness, high specific strength, superelasticity (2%) and excellent wear and corrosion resistance. Therefore, they have potential application prospects in structural parts in the fields of aviation, aerospace, etc.

[0003] However, due to the small critical size, room temperature brittleness and strain softening of titanium-based amorphous alloys, their application in the engineering field is greatly limited. In order to solve this problem, researchers have introduced crystal phases for exogenous composite or in-situ self-generation to obtain amorphous composite materials, which can effectively inhibit the single extension of shear bands and promote the initiation of multiple shear bands, thereby improving their plasticity and toughness. Among them, endogenous dendrite-toughened amorphous composite materials have always attracted the attention of domestic and foreign researchers due to their simple preparation and synthesis process, low cost and high stability.

[0004] Since strength and plasticity are a pair of contradictory performance indicators, the challenge faced by amorphous composite materials is to obtain better comprehensive performance by optimizing the strength and plasticity of the glass matrix, crystal phase, and interface precipitation phase. At present, some endogenous dendrite-toughened titanium-based amorphous composite material systems have been developed, such as Ti-Zr-V-Cu-Be, Ti-Zr-Ni-Be-Ta, and Ti-Cu-Ni-Sn-Nb. They all have high yield strength, but their plasticity has not shown a significant breakthrough. Considering that the machinability of amorphous composite materials plays an important role in broadening the application field and development needs of such alloys, the development of a high-strength and high-plasticity titanium-based amorphous composite material has become a key issue that needs to be solved urgently. Summary of the Invention

[0005] To overcome the shortcomings of the prior art, the present invention provides a method for modifying high-strength titanium-based amorphous composite materials with Si. This method achieves uniform microstructure, high strength, and good plasticity by introducing an appropriate amount of Si and controlling the process parameters, thereby resolving the problem of unsatisfactory room-temperature plasticity in prior art amorphous composite materials.

[0006] In order to achieve the above object, the technical solution adopted by the present invention is:

[0007] A method for modifying a high-strength titanium-based amorphous composite material with Si element comprises the following steps:

[0008] Step 1, raw material selection: according to the target product (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9～99.7 Si 0.1～0.3 (at.%) amorphous composite material components, Ti particles, Zr particles, Nb plates, Cu rods, Be particles and Si particles are selected according to atomic percentage;

[0009] Step 2: Surface treatment of raw materials: After polishing the Ti particles, Nb plates, Be particles, and Cu rods, the Cu rods are cleaned again with dilute hydrochloric acid, and all raw materials are cleaned and set aside;

[0010] Step 3, batching: putting the Ti particles, Nb plates, Zr particles and Si particles processed in step 2 into a vacuum arc melting furnace;

[0011] Step 4, melting the initial alloy ingot: evacuate the vacuum consumable arc melting furnace and introduce high-purity argon gas to protect the alloy ingot;

[0012] During the first smelting, slowly increase the smelting current to gradually wrap the particles below; then turn the alloy ingot over, increase the current, and repeat the smelting three times;

[0013] Step 5, smelting of target alloy ingot: put the initial alloy ingot obtained in step 4, Cu rod and Be particles into a crucible, slowly increase the smelting current; repeat the smelting three times to obtain (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9～99.7 Si 0.1～0.3 alloy ingots;

[0014] Step 6, spray casting: the (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9～99.7 Si 0.1～0.3 The alloy material obtained after cutting, grinding and cleaning the alloy ingot is placed in a quartz glass tube with a small hole at the bottom;

[0015] The spray casting furnace chamber is evacuated and then filled with high-purity argon gas, and the alloy material in the quartz glass tube is heated by energizing the induction coil of the spray casting furnace; (Ti 48 Zr 20 Nb 12Cu5Be 15 ) 99.9～99.7 Si 0.1～0.3 The amorphous composite material is rod-shaped.

[0016] In step 1, high-purity particles and bulk materials (≥99%) are selected as raw materials.

[0017] In step 2, all the raw materials are ultrasonically cleaned in alcohol for 20 minutes to prevent the introduction of other impurities.

[0018] In step 3, the atomic percentage of each element is converted into mass percentage, and the mass of each element is calculated according to the mass of the final alloy ingot.

[0019] In step 3, the smaller Si particles are placed at the bottom of the crucible, the Ti and Zr particles are placed in the middle, and the high-melting-point Nb plate is placed on the top. This allows the high-melting-point material to melt first, enveloping the lower-melting-point particles and preventing melt splashing that could cause the composition to deviate from the theoretical value.

[0020] In step 4, the vacuum consumable arc melting furnace is evacuated to 2×10 -3 Pa;

[0021] Slowly increase the melting current to about 280-350A for 1 minute, gradually enveloping the lower particles. Then, flip the alloy ingot over, increase the current to 350-450A, and melt for 1-2 minutes. Repeat this process three times. The purpose of this step is to obtain a high-melting-point alloy ingot with uniform composition.

[0022] In step 5, the Cu rod and Be particles are placed at the bottom and the initial alloy ingot is placed at the top to prevent volatilization and splashing of the low-melting-point material. The smelting current is slowly increased to 350-400 A. The smelting is repeated three times, each smelting for 1-2 minutes.

[0023] In step 6, the obtained alloy material is placed in a quartz glass tube with a 1.2-1.5 mm hole at the bottom; the spray casting furnace chamber is evacuated to 2×10 -3 Pa, and then filled with high-purity argon to -0.04 ~ -0.05MPa, the alloy material in the quartz glass tube is heated by energizing the induction coil of the spray casting furnace; when the heating power is 15 ~ 18kW, the melt is quickly flowed into the water-cooled copper mold through a 1.2 ~ 1.5mm small hole under the pressure of high-purity argon to obtain (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9～99.7 Si 0.1～0.3The amorphous composite material is rod-shaped.

[0024] The (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9～99.7 Si 0.1～0.3 The yield strength of amorphous composite materials is greater than 1400Mpa, and the maximum plastic strain at fracture can reach 63%; many parallel small-spacing and staggered large-spacing shear slip steps are generated at the fracture surface. At the same time, shear slip steps of different directions and scales change the direction of crack propagation.

[0025] Beneficial effects of the present invention:

[0026] In the present invention, the high strength Ti 48 Zr 20 Nb 12 Cu5Be 15 The modified amorphous composite material resulted in a refined original microstructure of the (Ti-Zr-Nb-Cu-Be)-Si amorphous composite material. However, the introduction of Si did not change the types of dendritic and amorphous phases. The yield strength of the composite material was >1400 MPa, and the plastic strain at fracture could reach 63%.

[0027] Many parallel small-spacing and staggered large-spacing shear-slip steps are generated at the fracture surface, such as Figure 3 、 Figure 6 and Figure 9 As shown by the red arrows, shear slip steps of varying orientations and scales alter the direction of crack propagation. In other words, the excellent mechanical properties of titanium-based amorphous composites primarily stem from the interaction between shear bands and dendrites. Under compressive load, the relatively soft dendrite phase deforms by dislocation slip, absorbing most of the elastic energy. This transfers the concentrated stress at the amorphous matrix / dendrite interface from the dendrite phase to the glass matrix, causing some shear bands to initiate and propagate within the amorphous matrix. When shear bands encounter and interact with dendrites, their propagation is hindered by the dendrites. Therefore, the mechanical properties of the (Ti-Zr-Nb-Cu-Be)-Si amorphous composite are the result of the combined effects of shear bands within the glass matrix and dislocations within the dendrite phase, resulting in superior plastic deformation capacity. BRIEF DESCRIPTION OF THE DRAWINGS

[0028] Figure 1 It is provided in Example 1 (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9 Si 0.1 XRD diffraction curves of amorphous composite materials.

[0029] Figure 2 It is provided in Example 1 (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9 Si 0.1 Compressive stress-strain curve of amorphous composite material. The strain rate is 5×10 -4 s -1 .

[0030] Figure 3 It is provided in Example 1 (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9 Si 0.1 Distribution diagram of the fracture slip steps of amorphous composite materials.

[0031] Figure 4 It is provided in Example 2 (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.8 Si 0.2 XRD diffraction curves of amorphous composite materials.

[0032] Figure 5 It is provided in Example 2 (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.8 Si 0.2 Compressive stress-strain curve of amorphous composite material at a strain rate of 5×10 -4 s -1 .

[0033] Figure 6 It is provided in Example 2 (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.8 Si 0.2 Distribution diagram of the fracture slip steps of amorphous composite materials.

[0034] Figure 7 It is provided in Example 3 (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.7 Si 0.3XRD diffraction curves of amorphous composite materials.

[0035] Figure 8 It is provided in Example 3 (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.7 Si 0.3 Compressive stress-strain curve of amorphous composite material. The strain rate is 5×10 -4 s -1 .

[0036] Figure 9 It is provided in Example 3 (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.7 Si 0.3 Distribution diagram of the fracture slip steps of amorphous composite materials. DETAILED DESCRIPTION

[0037] The present invention will be described in further detail below with reference to the accompanying drawings.

[0038] Implementation Case 1

[0039] This embodiment is a (Ti-Zr-Nb-Cu-Be)-Si based amorphous composite material.

[0040] In order to obtain a titanium-based amorphous composite material with excellent performance, the present invention proposes a preparation step of a Si-modified high-strength titanium-based amorphous composite material as follows:

[0041] 1. Raw material selection: According to the target product (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9 Si 0.1 The raw materials for the amorphous composite material are high-purity particles and blocks (≥99%) of Ti, Zr, Nb, Cu, Be, and Si. The total ingot mass is 22g, including 8.881g of Ti, 7.051g of Zr, 4.308g of Nb, 1.228g of Cu, 0.521g of Be, and 0.011g of Si.

[0042] 2. Surface treatment of raw materials: After polishing the Ti particles, Nb plates and Cu rods respectively, clean the Cu rods again with dilute hydrochloric acid. Then, ultrasonically clean the raw materials in alcohol for 20 minutes, blow dry and set aside.

[0043] 3. Batching: Convert the atomic percentage of each element into mass percentage and calculate the mass of each element based on the mass of the ingot. Place the processed bulk raw materials into a vacuum arc melting furnace, with the smaller Si particles at the bottom of the crucible, the Ti and Zr particles in the middle, and the high-melting-point Nb plate at the top.

[0044] 4. Melting of initial alloy ingot: evacuate the vacuum consumable arc melting furnace to 2×10 -3 Pa, high-purity argon gas is introduced to protect the alloy ingot. During the first smelting, the smelting current is slowly increased to about 300A, and the smelting time is 1 minute, gradually enveloping the particles below. Then, the alloy ingot is turned over, the current is increased to 400A, and the smelting time is 2 minutes. Smelt three times to ensure uniform composition of the alloy ingot.

[0045] 5. Melting of target alloy ingot: put the initial alloy ingot obtained in step 3, Cu rod and Be particles into a crucible, with Cu rod and Be particles at the bottom and initial alloy ingot at the top to prevent volatilization and splashing of low melting point materials. Slowly increase the melting current to 400A. Repeat the melting three times, each melting for 1 minute, to obtain (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9 Si 0.1 alloy ingots;

[0046] 6. Spray casting: Spray the (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9 Si 0.1 The alloy ingot was cut, polished and cleaned to obtain 10.5 g of alloy material, which was placed in a quartz glass tube with a 1.2 mm hole at the bottom. The spray casting furnace chamber was vacuumed to 2 × 10 -3 Pa, and then filled with high-purity argon to -0.05MPa. The alloy material in the quartz glass tube is heated by energizing the induction coil of the spray casting furnace. When the heating power reaches 16kW, the melt is quickly flowed into a water-cooled copper mold through a 1.2mm small hole under the pressure of high-purity argon to obtain (TiO2) with a diameter of 3mm and a length of 75mm. 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9 Si 0.1 The amorphous composite material is rod-shaped.

[0047] The obtained (Ti 48 Zr 20Nb 12 Cu5Be 15 ) 99.9 Si 0.1 Amorphous composite material rods cut into The samples were subjected to X-ray diffraction, scanning electron microscopy and uniaxial compression tests. The experimental results are as follows: Figure 1 As shown in the figure, the XRD pattern mainly shows the diffraction peaks of amorphous phase and body-centered cubic β-Ti solid solution. With the introduction of Si element, the types of dendrite phase and amorphous phase have not changed. Figure 2 As shown in the engineering compression stress-strain curve of the amorphous composite material, the yield strength is 1437MPa, the compression fracture strength is 1388MPa, and the plastic strain before fracture is 63%; Figure 3 As shown in the figure, many parallel small-spacing and staggered large-spacing shear slip steps are generated at the fracture surface, showing excellent yield strength and plasticity.

[0048] Implementation Case 2

[0049] This embodiment is a (Ti-Zr-Nb-Cu-Be)-Si based amorphous composite material.

[0050] In order to obtain a titanium-based amorphous composite material with excellent performance, the present invention proposes a preparation step of a Si-modified high-strength titanium-based amorphous composite material as follows:

[0051] 1. Raw material selection: According to the target product (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.8 Si 0.2 The raw materials for the amorphous composite material are high-purity granular and bulk materials (≥99%) of Ti, Zr, Nb, Cu, Be, and Si. The total mass of the ingot is 22g, including 8.877g of Ti, 7.047g of Zr, 4.305g of Nb, 1.228g of Cu, 0.521g of Be, and 0.022g of Si.

[0052] 2. Surface treatment of raw materials: After polishing the Ti particles, Nb plates and Cu rods respectively, clean the Cu rods again with dilute hydrochloric acid. Then, ultrasonically clean the raw materials in alcohol for 20 minutes, blow dry and set aside.

[0053] 3. Batching: Convert the atomic percentage of each element into mass percentage and calculate the mass of each element based on the mass of the ingot. Place the processed bulk raw materials into a vacuum arc melting furnace, with the smaller Si particles at the bottom of the crucible, the Ti and Zr particles in the middle, and the high-melting-point Nb plate at the top.

[0054] 4. Melting of initial alloy ingot: evacuate the vacuum consumable arc melting furnace to 2×10 -3 Pa, high-purity argon gas is introduced to protect the alloy ingot. During the first smelting, the smelting current is slowly increased to about 300A, and the smelting time is 1 minute, gradually enveloping the particles below. Then, the alloy ingot is turned over, the current is increased to 400A, and the smelting time is 2 minutes. Smelt three times to ensure uniform composition of the alloy ingot.

[0055] 5. Melting of target alloy ingot: put the initial alloy ingot obtained in step 3, Cu rod and Be particles into a crucible, with Cu rod and Be particles at the bottom and initial alloy ingot at the top to prevent volatilization and splashing of low melting point materials. Slowly increase the melting current to 400A. Repeat the melting three times, each melting for 1 minute, to obtain (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.8 Si 0.2 alloy ingots;

[0056] 6. Spray casting: Spray the (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.8 Si 0.2 The alloy ingot was cut, polished and cleaned to obtain 9.5 g of alloy material, which was placed in a quartz glass tube with a 1.2 mm hole at the bottom. The spray casting furnace chamber was vacuumed to 2 × 10 -3 Pa, and then filled with high-purity argon to -0.05MPa. The alloy material in the quartz glass tube was heated by energizing the induction coil of the spray casting furnace. When the heating power reached 16kW, the melt was quickly flowed into a water-cooled copper mold through a 1.2mm small hole under the pressure of high-purity argon to obtain (TiO2) with a diameter of 3mm and a length of 71mm. 48 Zr 20 Nb 12 Cu5Be 15 ) 99.8 Si 0.2 The amorphous composite material is rod-shaped.

[0057] The obtained (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.8 Si 0.2 Amorphous composite material rods cut into The samples were subjected to X-ray diffraction, scanning electron microscopy and uniaxial compression tests. The experimental results are as follows: Figure 4 As shown in the figure, the XRD pattern mainly shows the diffraction peaks of amorphous phase and body-centered cubic β-Ti solid solution. With the introduction of Si element, the types of dendrite phase and amorphous phase have not changed. Figure 5 As shown in the engineering compressive stress-strain curve of the amorphous composite material, the yield strength is 1552MPa, the compressive fracture strength is 1516MPa, and the plastic strain before fracture is 61.6%. Figure 6 As shown in the figure, many parallel small-spacing and staggered large-spacing shear slip steps are generated at the fracture surface, showing excellent yield strength and plasticity.

[0058] Implementation Case 3

[0059] This embodiment is a (Ti-Zr-Nb-Cu-Be)-Si based amorphous composite material.

[0060] In order to obtain a titanium-based amorphous composite material with excellent performance, the present invention proposes a preparation step of a Si-modified high-strength titanium-based amorphous composite material as follows:

[0061] 1. Raw material selection: According to the target product (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.7 Si 0.3 The raw materials for the amorphous composite material are high-purity particles and blocks (≥99%) of Ti, Zr, Nb, Cu, Be, and Si. The total mass of the ingot is 22g, including 8.873g of Ti, 7.042g of Zr, 4.303g of Nb, 1.228g of Cu, 0.521g of Be, and 0.033g of Si.

[0062] 2. Surface treatment of raw materials: After polishing the Ti particles, Nb plates and Cu rods respectively, clean the Cu rods again with dilute hydrochloric acid. Then, ultrasonically clean the raw materials in alcohol for 20 minutes, blow dry and set aside.

[0063] 3. Batching: Convert the atomic percentage of each element into mass percentage and calculate the mass of each element based on the mass of the ingot. Place the processed bulk raw materials into a vacuum arc melting furnace, with the smaller Si particles at the bottom of the crucible, the Ti and Zr particles in the middle, and the high-melting-point Nb plate at the top.

[0064] 4. Melting of initial alloy ingot: evacuate the vacuum consumable arc melting furnace to 2×10 -3Pa, high-purity argon gas is introduced to protect the alloy ingot. During the first smelting, the smelting current is slowly increased to 300A for 1 minute to gradually envelop the particles below. The alloy ingot is then turned over and the current is increased to 400A for 2 minutes. This process is repeated three times to ensure uniform composition of the alloy ingot.

[0065] 5. Melting of target alloy ingot: put the initial alloy ingot obtained in step 3, Cu rod and Be particles into a crucible, with Cu rod and Be particles at the bottom and initial alloy ingot at the top to prevent volatilization and splashing of low melting point materials. Slowly increase the melting current to 400A. Repeat the melting three times, each melting for 1 minute, to obtain (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.7 Si 0.3 alloy ingots;

[0066] 6. Spray casting: Spray the (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.7 Si 0.3 The alloy ingot was cut, polished and cleaned to obtain 11.6 g of alloy material, which was placed in a quartz glass tube with a 1.2 mm hole at the bottom. The spray casting furnace chamber was vacuumed to 2 × 10 -3 Pa, and then filled with high-purity argon to -0.05MPa. The alloy material in the quartz glass tube is heated by energizing the induction coil of the spray casting furnace. When the heating power is 16kW, the melt is quickly flowed into a water-cooled copper mold through a 1.2mm small hole under the pressure of high-purity argon to obtain (TiO2) with a diameter of 3mm and a length of 92mm. 48 Zr 20 Nb 12 Cu5Be 15 ) 99.7 Si 0.3 The amorphous composite material is rod-shaped.

[0067] The obtained (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.7 Si 0.3 Amorphous composite material rods cut into The samples were subjected to X-ray diffraction, scanning electron microscopy and uniaxial compression tests. The experimental results are as follows: Figure 7As shown in the figure, the XRD pattern mainly shows the diffraction peaks of amorphous phase and body-centered cubic β-Ti solid solution. With the introduction of Si element, the types of dendrite phase and amorphous phase have not changed. Figure 8 As shown in the engineering compression stress-strain curve of the amorphous composite material, the yield strength is 1446MPa and the compression fracture strength is 1500MPa. The plastic strain before fracture is 43%; as shown in the attached figure, Figure 9 As shown in the figure, many parallel small-spacing and staggered large-spacing shear slip steps are generated at the fracture surface, showing excellent yield strength and plasticity.

Claims

1. A method for modifying a high-strength titanium-based amorphous composite material with Si element, characterized in that: The following steps are included: Step 1, raw material selection: according to the target product (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9～99.7 Si 0.1～0.3 (at.%) amorphous composite material components, Ti particles, Zr particles, Nb plates, Cu rods, Be particles and Si particles are selected according to atomic percentage; Step 2: Surface treatment of raw materials: After polishing the Ti particles, Nb plates, Be particles, and Cu rods, the Cu rods are cleaned again with dilute hydrochloric acid, and then the used bulk raw materials are cleaned and set aside; Step 3, batching: putting the Ti particles, Nb plates, Zr particles and Si particles processed in step 2 into a vacuum arc melting furnace; Step 4, melting the initial alloy ingot: evacuate the vacuum consumable arc melting furnace and introduce high-purity argon gas to protect the alloy ingot; During the first smelting, slowly increase the smelting current to gradually wrap the particles below; then turn the alloy ingot over, increase the current, and repeat the smelting three times; Step 5, smelting of target alloy ingot: put the initial alloy ingot obtained in step 4, Cu rod and Be particles into a crucible, slowly increase the smelting current; repeat the smelting three times to obtain (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9～99.7 Si 0.1～0.3 alloy ingots; Step 6, spray casting: the (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9～99.7 Si 0.1～0.3 The alloy material obtained after cutting, grinding and cleaning the alloy ingot is placed in a quartz glass tube with a small hole at the bottom; The spray casting furnace chamber is evacuated and then filled with high-purity argon gas, and the alloy material in the quartz glass tube is heated by energizing the induction coil of the spray casting furnace; (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9～99.7 Si 0.1～0.3 Amorphous composite materials are rod-shaped; In step 4, the vacuum consumable arc melting furnace is evacuated to 2×10 -3 Pa; Slowly increase the melting current to about 280-350A, melting time is 1 minute, gradually wrapping the particles below; then turn the alloy ingot over, increase the current to 350-450A, melting time is 1-2 minutes, and repeat the melting back and forth three times; In step 5, the Cu rod and Be particles are placed at the bottom, and the initial alloy ingot is placed at the top to prevent volatilization and splashing of the low-melting-point material. The smelting current is slowly increased to 350-400A; the smelting is repeated three times, each smelting for 1-2 minutes; In step 6, the obtained alloy material is placed in a quartz glass tube with a small hole of 1.2 to 1.5 mm at the bottom; the spray casting furnace chamber is evacuated to 2×10 -3 Pa, and then filled with high-purity argon to -0.04 ~ -0.05MPa, the alloy material in the quartz glass tube is heated by energizing the induction coil of the spray casting furnace; when the heating power is 15 ~ 18kW, the melt is quickly flowed into the water-cooled copper mold through a 1.2 ~ 1.5mm small hole under the pressure of high-purity argon to obtain (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9～99.7 Si 0.1～0.3 The amorphous composite material is rod-shaped.

2. The method for modifying a high-strength titanium-based amorphous composite material with Si element according to claim 1, characterized in that: In step 1, high-purity particles and bulk materials (≥99%) are selected as raw materials.

3. The method for modifying a high-strength titanium-based amorphous composite material with Si element according to claim 1, characterized in that: In step 2, all the raw materials are ultrasonically cleaned in alcohol for 20 minutes.

4. The method for modifying a high-strength titanium-based amorphous composite material with Si element according to claim 1, characterized in that: In step 3, the atomic percentage of each element is converted into mass percentage, and the mass of each element is calculated according to the mass of the final alloy ingot.

5. The method for modifying a high-strength titanium-based amorphous composite material with Si element according to claim 1, characterized in that: In step 3, the smaller Si particles are placed at the bottom of the crucible, the Ti particles and the Zr particles are placed in the middle, and the high-melting-point Nb plate is placed on the top.

6. The method according to any one of claims 1 to 5, characterized in that The (Ti 48 Zr 20 Nb 12 Cu5Be 15 ) 99.9 ~99.7Si 0.1 The yield strength of the 0.3 amorphous composite materials is greater than 1400 MPa, and the plastic strain at fracture can reach 63%. Many parallel small-spacing and staggered large-spacing shear slip steps are generated at the fracture surface. At the same time, the shear slip steps of different directions and scales change the direction of crack propagation.

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