Ultrahigh-temperature, ultrahigh-strength and ultrahigh-hardness Re-based amorphous alloy material as well as preparation method and application thereof

Abstract

The invention provides an ultrahigh-temperature, ultrahigh-strength and ultrahigh-hardness Re-based amorphous alloy material as well as a preparation method and application thereof. The specific chemical formula is ReaMbNc; wherein Re is rhenium element, M is boron and / or silicon element, and N comprises at least one element of scandium, yttrium, zirconium, vanadium, niobium, hafnium, tantalum, molybdenum and tungsten; a, b and c are atomic percentage contents of corresponding elements, a is equal to 40-60, b is equal to 20-45, c is equal to 10-30, and a + b + c is equal to 100. According to the invention, the rhenium element is used as a matrix, and metalloid boron and / or silicon elements and specific transition metal elements are added, so that the design and preparation of the ternary or even super-multi-element Re-based amorphous alloy are realized. The performance of the material is far better than that of an existing amorphous alloy material, and the material has the highest glass transition temperature, Vickers microhardness, elasticity modulus, bulk modulus and compression mechanical strength in known amorphous alloy materials. The method can be widely applied to preparation of precise glass forming molds, semiconductor processing choppers, micro drill bits, wear-resistant coatings and films, anti-radiation materials, anti-neutron shielding materials and the like.

Description

Technical Field

[0001] This invention belongs to the field of amorphous alloy material development and preparation technology, specifically relating to a Re-based amorphous alloy material with ultra-high temperature, ultra-high strength, and ultra-high hardness, as well as its preparation method and application. Background Technology

[0002] In the field of materials science, amorphous alloys, due to their lack of long and ordered structures, exhibit high strength, excellent corrosion resistance, and good wear resistance, showing broad application prospects in many fields such as electronics, machinery, and energy.

[0003] However, most traditional amorphous alloy systems, such as common Zr-based and Cu-based alloys, have significant performance limitations. These traditional amorphous alloys have limited environmental thermal stability and are prone to crystallization under high-temperature conditions. After crystallization, the microstructure of the amorphous alloy changes, leading to a significant reduction in its mechanical properties, which cannot meet the requirements for use under high-temperature conditions. This problem severely restricts the expansion of amorphous alloys in high-temperature applications.

[0004] Rhenium (Re), a rare high-melting-point transition metal, has played an important role in many industrial production fields. For example, it is used in Re / Al2O3 and Pt-Re catalysts to participate in reforming reactions; and it is used to make high-temperature thermocouple (W-Re thermocouple) materials. It is expected to become a key element to drive the transformation of amorphous alloys to high-temperature applications.

[0005] High-temperature amorphous alloys (HTMGs) are a class of amorphous metallic materials that maintain high mechanical properties and thermal stability at high temperatures. The operating temperature of traditional amorphous alloys is limited by their glass transition temperature (T0). g ) and crystallization temperature (T) X High-temperature amorphous alloys, typically operating below 700℃, are prone to instability and crystallization at higher temperatures, leading to a sharp decline in performance. Currently, the design philosophy for high-temperature amorphous alloys primarily utilizes high-melting-point refractory elements such as Nb, Mo, Re, Ta, and W as the matrix, increasing the complexity of the constituent elements and precisely controlling atomic size differences and negative mixing enthalpy to improve the alloy's glass-forming ability. Although some progress has been made in existing high-temperature bulk amorphous alloy systems based on high-melting-point refractory elements, such as Ta-based (Ta-Co binary amorphous, Ir-Ni-Ta ternary amorphous, etc.), Os-based (Os-Hf-B ternary amorphous, Os-Zr-B ternary amorphous, etc.), and Mo-based (Mo-Co-B ternary amorphous, Mo-Co-Cr-CB pentagonal amorphous, etc.), there is still room for research and improvement in how to further optimize the overall performance of high-temperature amorphous alloys to better adapt them to diverse high-temperature applications.

[0006] In view of this, the present invention is proposed. Summary of the Invention

[0007] The purpose of this invention is to provide a Re-based ultra-high temperature (T) g A new amorphous alloy material with ultra-high strength (compressive fracture strength above 7 GPa) and ultra-high hardness (Hv above 17 GPa) at ≥1200K. Its specific chemical formula is Re. a M b N c Wherein, Re is rhenium, M is boron and / or silicon, and N includes at least one element selected from Sc (scandium), Y (yttrium), Zr (zirconium), V (vanadium), Nb (niobium), Hf (hafnium), Ta (tantalum), Mo (molybdenum), and W (tungsten); a, b, and c are the atomic percentages (at.%) of the corresponding elements, where a = 40–60, b = 20–45, and c = 10–30, and the sum of the atomic percentages of each element a + b + c = 100.

[0008] In a preferred embodiment, the glass transition temperature of the Re-based amorphous alloy material is above 1200K.

[0009] In a preferred embodiment, the Vickers microhardness of the Re-based amorphous alloy material is above 17 GPa.

[0010] In a preferred embodiment, in the Re-based amorphous alloy material, when M is silicon and N includes at least one element selected from zirconium, hafnium, tantalum, and molybdenum, the atomic percentages of each element are a = 45–55, b = 25–40, and c = 10–25, respectively, and a + b + c = 100; preferably, the composition of the Re-based amorphous alloy material includes Re 45 Si 40 Zr 15 Re 45 Si 40 Ta 15 Re 50 Si 25 Mo 25 Re 45 Si 40 Hf 15 .

[0011] In a preferred embodiment, the Re a Si b Zr c The glass transition temperature of amorphous alloy materials is above 1200K.

[0012] In a preferred embodiment, the Re a Si b Zrc The amorphous alloy material has a Young's modulus of 265 GPa and a Vickers microhardness of over 17 Ga.

[0013] In a preferred embodiment, in the Re-based amorphous alloy material, when M is boron and N includes at least one element selected from zirconium, niobium, yttrium, scandium, and hafnium, the atomic percentages of each element are a = 40–60, b = 20–40, and c = 10–30, respectively, and a + b + c = 100; preferably, the composition of the Re-based amorphous alloy material includes Re 50 B 25 Nb 25 Re 55 B 40 Y 15 Re 55 B 30 Sc 15 Re 50 B 35 Hf 15 .

[0014] In a preferred embodiment, the Re a B b Zr c The glass transition temperature of amorphous alloy materials is above 1300K.

[0015] In a preferred embodiment, the Re a B b Zr c The compressive fracture strength of the amorphous alloy material at room temperature is 7.25 GPa.

[0016] In a preferred embodiment, the Re a B b Zr c The amorphous alloy material has a Young's modulus of 347 GPa and a Vickers microhardness of over 25 Ga.

[0017] Another object of the present invention is to provide a method for preparing any of the above-mentioned Re-based amorphous alloy materials, specifically including the following steps:

[0018] Step 1: According to the chemical formula Re of the Re-based high-temperature amorphous alloy a M b N c Calculate the mass ratio of each element and weigh and mix the ingredients: where Re is rhenium, M is boron and / or silicon, and N includes at least one element selected from scandium, yttrium, zirconium, vanadium, niobium, hafnium, tantalum, molybdenum, and tungsten; a, b, and c are the atomic percentages of the corresponding elements, a = 40–60, b = 20–45, c = 10–30, and the sum of the atomic percentages of each element a + b + c = 100;

[0019] Step 2: Melt the elemental materials weighed in Step 1 in a protective atmosphere until homogeneous to obtain a master alloy ingot;

[0020] Step 3: The master alloy ingot obtained in Step 2 is heated and melted in a protective atmosphere, and Re-based amorphous alloy strips are prepared by melt spin quenching; or the master alloy ingot obtained in Step 2 is heated and melted in a protective atmosphere, and Re-based amorphous alloy bulk is prepared by copper mold casting.

[0021] In a preferred embodiment, in step 2, when M is silicon, the elemental elements in the ReSiN system are melted into a master alloy ingot using an electric arc melting method; specifically, this includes the following steps: according to the designed alloy composition ratio, rhenium elemental raw material, silicon elemental raw material, and N metal elemental raw material are placed in a vacuum electric arc furnace, and a vacuum is drawn to a vacuum degree ≤ 8 × 10⁻⁶. - 3 Pa, fill with 0.05MPa of high-purity Ar gas, and melt the master alloy ingot with an electric arc at 2800-3200℃ for 3-5 minutes under Ar atmosphere, repeat the melting process more than 5 times, and then take it out after cooling.

[0022] In a preferred embodiment, in step 2, when M is boron, induction melting is first used to pre-alloy Re. 58 B 42 (at.%), then add other elemental elements and smelt to form a master alloy ingot; specifically including the following steps:

[0023] S1 places the boron nitride crucible containing rhenium and boron raw materials into a vacuum induction melting furnace and evacuates the furnace to a vacuum level ≤3.0×10⁻⁶. -2 Pa, filled with 0.05 MPa of high-purity Ar gas, melted at 1800–2200 °C for 3–15 min under Ar atmosphere, repeated 2–5 times, and then cooled and removed Re. 58 B 42 Pre-alloyed;

[0024] S2 will obtain Re from induction melting 58 B 42 The pre-alloyed material is placed in a vacuum arc furnace, and rhenium and nitrogen metal raw materials are added according to the designed alloy composition ratio. The furnace is then evacuated to a vacuum degree ≤ 8 × 10⁻⁶. -3 Pa, fill with 0.05MPa of high-purity Ar gas, and melt the master alloy ingot with an electric arc at 2800-3200℃ for 3-5 minutes under Ar atmosphere, repeat the melting process more than 5 times, and then take it out after cooling.

[0025] In a preferred embodiment, step 3 of the melt spin quenching method specifically includes the following steps:

[0026] The master alloy ingot obtained in step 2 is placed in a rapid solidification induction apparatus and evacuated to a vacuum level ≤1×10⁻⁶. -2 Pa, filled with 0.05 MPa of high-purity Ar gas, heated to 1800–2200 °C; the rotation speed of the rapid solidification copper wheel was adjusted to 2000–4000 r / min, the injection pressure was 0.01–0.04 MPa, and after induction heating to melt it for 10–30 s, the molten alloy liquid was sprayed onto the surface of the high-speed rotating copper wheel to obtain Re-based amorphous alloy thin strips.

[0027] In a preferred embodiment, step 3 of the copper mold casting method specifically includes the following steps:

[0028] The master alloy ingot obtained in step 2 is placed in a rapid solidification induction apparatus and evacuated to a vacuum level ≤1×10⁻⁶. -2 Pa, filled with 0.05 MPa of high-purity Ar gas, heated to 1800–2200 °C; copper molds of different diameters are placed under the crucible, sprayed at 0.01–0.04 MPa, and induction heated to melt the master alloy for 10–30 s, then the molten alloy liquid is sprayed into copper molds of different diameters to obtain Re-based amorphous alloy blocks.

[0029] Another object of the present invention is to provide the application of any of the above-mentioned Re-based amorphous alloy materials in the preparation of precision glass forming molds, semiconductor processing cleavers, micro drill bits, wear-resistant coatings and films, radiation-resistant materials and neutron-resistant shielding materials.

[0030] Compared with the prior art, the technical solution of the present invention has the following advantages:

[0031] 1. This invention achieves a compositional innovation in Re-based bulk amorphous alloys, starting from scratch. By using rhenium as the matrix and adding metalloid boron and / or silicon, as well as specific transition metal elements, the design and preparation of ternary or even super-multi-element Re-based amorphous alloys are realized.

[0032] 2. The Re-based amorphous alloy material provided by this invention achieves the performance limits of existing amorphous alloys, possessing the highest glass transition temperature, Vickers microhardness, elastic modulus, and bulk modulus, as well as the highest compressive strength among existing amorphous alloy materials. Its performance far surpasses that of existing Os-based, Ir-based, and Mo-based amorphous alloy materials. Therefore, it can be widely applied in various high-precision technology fields, such as the fabrication of precision glass forming molds, semiconductor processing cleavers, and micro-drill bits.

[0033] 3. The Re-based amorphous alloy material provided by this invention also features multiple components and a wide range of compositional characteristics, allowing for adjustment of the composition of each component within a broad range, which is beneficial for industrial applications. Furthermore, compared to Os- and Ir-based amorphous alloys, the Re-based amorphous alloy of this invention has lower raw material costs and stronger product competitiveness. Simultaneously, the heavy metal element Re in the amorphous alloy material can be used in radiation-resistant coatings and thin films, while element B can achieve excellent neutron shielding effects. Therefore, it can be widely used in the preparation of high-performance wear-resistant coatings and thin films, high-performance radiation-resistant materials, and high-performance neutron shielding materials. Attached Figure Description

[0034] To more clearly illustrate the technical solutions in the specific embodiments of this application or the prior art, the drawings used in the description of the specific embodiments or the prior art will be briefly introduced below. Obviously, the drawings described below are some embodiments of this application. For those skilled in the art, other drawings can be obtained from these drawings without creative effort.

[0035] Figure 1 Re prepared in Example 1 of the present invention 45 Si 40 Zr 15 Re 45 Si 40 Ta 15 Re 50 Si 25 Mo 25 Re 45 Si 40 Hf 15 XRD patterns of amorphous alloy ribbon samples;

[0036] Figure 2 Re prepared in Example 2 of this invention 55 Si 35 Zr 10 XRD pattern of a 1mm amorphous alloy sample;

[0037] Figure 3 Re prepared in Example 2 of this invention 55 Si 35 Zr 10 DSC curve of a 1mm amorphous alloy sample;

[0038] Figure 4 Re prepared in Example 3 of this invention 50 B 25 Nb 25 Re 55 B 40 Y 15 Re55 B 30 Sc 15 Re 50 B 35 Hf 15 XRD patterns of amorphous alloy ribbon samples;

[0039] Figure 5 Re prepared in Example 4 of this invention 55 B 35 Zr 10 XRD pattern of a 1mm amorphous alloy sample;

[0040] Figure 6 Re prepared in Example 4 of this invention 55 B 35 Zr 10 DSC curve of a 1mm amorphous alloy sample;

[0041] Figure 7 Re prepared in Example 4 of this invention 55 B 35 Zr 10 Room temperature compression curve of a 1 mm amorphous alloy sample. Detailed Implementation

[0042] To enable those skilled in the art to better understand the present invention, the present invention will be further described in detail below with reference to the accompanying drawings and specific embodiments. However, it should be understood that the scope of protection of the present invention is not limited to the specific embodiments. Based on the embodiments in this application, all other embodiments obtained by those skilled in the art without creative effort are within the scope of protection of this application.

[0043] Unless otherwise specified, the technical means used in this invention are conventional means well known to those skilled in the art. All raw materials, reagents, instruments, and equipment used in this invention can be purchased commercially or prepared using existing methods. Unless otherwise specified, all reagents used in this invention are of analytical grade. The purity of the elemental substances used in this invention is ≥99.95%. In the embodiments of this invention, the room temperature is 25±5℃.

[0044] Example 1

[0045] Step 1: Re a M b N c The alloy composition is designed with Re representing rhenium, M representing silicon, N representing zirconium, tantalum, molybdenum, and hafnium, and the specific atomic proportions of each element are as follows: Re 45 Si 40 Zr 15 Re 45 Si 40 Ta15 Re 50 Si 25 Mo 25 Re 45 Si 40 Hf 15 .

[0046] Step 2: Based on the alloy composition designed in Step 1, calculate the required mass of each element according to its atomic percentage and relative atomic mass to prepare 10g of alloy. Melt the elemental components into a master alloy ingot using an electric arc furnace. Before melting, evacuate to a vacuum level of 8×10⁻⁶. -3 Pa, during the melting process, high-purity Ar is introduced as a protective atmosphere, and the melting is carried out at 3000℃ for 5 minutes. The melting is repeated 5 times to ensure that the alloy composition is uniform.

[0047] Step 3: Crush the master alloy ingot obtained in Step 2, take 3g of the alloy and heat it to melt in an Ar protective atmosphere. Prepare a Re-based amorphous alloy thin strip sample using the melt spin quenching method. The specific operating conditions for the melt spin quenching method include: evacuating to a vacuum degree of 1×10⁻⁶. -2 Pa, filled with 0.05MPa high-purity Ar gas, heated to 2000℃, and injected at 0.02MPa, is induction heated to melt it for 15s, and then injected onto the surface of a copper wheel rotating at 3000r / min to obtain the product.

[0048] The thin strip samples exhibit uniform thickness and smooth surfaces, making them suitable for rapid structural verification of materials. Therefore, XRD was used to analyze the phase composition of the 30 μm thick amorphous alloy strip prepared in Example 1. The XRD scanning speed was 6° / min, and the scanning range was 20°–80°. The results are as follows: Figure 1 As shown.

[0049] Depend on Figure 1 It can be seen that Re 45 Si 40 Zr 15 Re 45 Si 40 Ta 15 Re 50 Si 25 Mo 25 Re 45 Si 40 Hf 15 The XRD patterns of all samples showed obvious broadened diffuse scattering peaks, with no other crystal diffraction peaks, indicating that all the prepared strip samples were completely amorphous.

[0050] Example 2

[0051] The difference from Example 1 is as follows:

[0052] In step 1, Re a M b N c In the alloy composition design, Re represents rhenium, M represents silicon, and N represents zirconium. The specific atomic proportions of each element are as follows: Re 55 Si 35 Zr 10 ;

[0053] In step 3, the master alloy ingot obtained in step 2 is crushed, and 3g of the alloy is heated and melted in an Ar protective atmosphere. The molten alloy is then sprayed into a copper mold with an inner diameter of 1mm using a copper mold casting method to obtain a 1mm Re-based amorphous alloy rod. The specific operating conditions for the copper mold casting method include: evacuating to a vacuum degree of 1×10⁻⁶. -2 Pa, filled with 0.05MPa high-purity Ar gas, heated to 2000℃, and injected at 0.02MPa, is induction heated to melt it for 15s and then injected into a 1mm copper mold.

[0054] The shape of the test block is closer to the actual application scenario. Therefore, the performance of the Re-based amorphous alloy block prepared in Example 2 was tested, and the results are as follows:

[0055] (1) XRD was used to analyze the prepared Re 55 Si 35 Zr 10 Phase analysis was performed on the amorphous alloy bulk material using XRD at a scanning speed of 6° / min and a scanning range of 20°–80°. The results are as follows: Figure 2 As shown.

[0056] Depend on Figure 2 As can be seen, the XRD pattern shows a broadened diffuse scattering peak, with no other crystal diffraction peaks appearing, indicating that the prepared bulk sample is a completely amorphous structure.

[0057] (2) The prepared Re was tested using a differential scanning calorimeter (DSC) according to GB / T 19466.2-2004. 55 Si 35 Zr 10 The thermal properties of the amorphous alloy were measured at a heating rate of 20 K / min, with a sample mass of 20 mg. The results are as follows: Figure 3 As shown.

[0058] Depend on Figure 3 It can be seen that its glass transition temperature T g The temperature at which crystallization begins is 1249 K. x The K value is 1279 K. Its density ρ, measured using Archimedes' displacement method, is 16.61 g / cm³. 3The microhardness Hv was determined according to the standard "Metallic Vickers Hardness Test: Inspection and Calibration of Hardness Testers" (GB / T 4340.2 2012). 0.2 The value was 17 GPa. Its elastic properties were tested using ultrasonic waves according to the standard "Nondestructive Testing: Ultrasonic Measurement Method for Elastic Modulus and Poisson's Ratio" (GB / T 38897-2020). The elastic modulus E was 265 GPa, the shear modulus G was 99 GPa, and the bulk modulus B was 267 GPa. Specific data are shown in Table 1.

[0059] Table 1 Re 55 Si 35 Zr 10 Performance table of 1mm amorphous alloy samples

[0060]

[0061] Example 3

[0062] Step 1: Re a M b N c The alloy composition is designed with Re representing rhenium, M representing boron, N representing niobium, yttrium, scandium, and hafnium, and the specific atomic proportions of each element are as follows: Re 50 B 25 Nb 25 Re 55 B 40 Y 15 Re 55 B 30 Sc 15 Re 50 B 35 Hf 15 .

[0063] Step 2: In the high-frequency induction melting furnace, according to Re 58 B 42 The pre-alloying process involves calculating the required mass of Re metallic element and B non-metallic element for 20g of pre-alloying according to atomic percentages and relative atomic masses, placing them in a boron nitride crucible, and evacuating the vacuum to ≤3×10⁻⁶. -2 After Pa, high-purity Ar gas at 0.05 MPa is introduced, and the alloy is melted at 2000℃ for 10 minutes in the Ar atmosphere. The melting is repeated 5 times to ensure uniform composition. After cooling, Re is removed. 58 B 42 Pre-alloyed;

[0064] Based on the alloy composition designed in step 1, weigh out the masses of other elemental substances (Re, Zr, Nb, Y, Sc, Hf), and evacuate them to ≤8×10⁻⁶ in an electric arc melting furnace. -3After Pa, high-purity Ar gas of 0.05 MPa is introduced, and the alloy is melted in the Ar atmosphere at 3000℃ for 3 minutes. The melting is repeated 5 times to ensure uniform composition. After cooling, the master alloy ingot is taken out.

[0065] Step 3: Crush the master alloy ingot obtained in Step 2, take 3g of the alloy and heat it to melt in an Ar protective atmosphere. Prepare a Re-based amorphous alloy thin strip sample using the melt spin quenching method. The specific operating conditions for the melt spin quenching method include evacuating to a vacuum degree of 1×10⁻⁶. -2 Pa, filled with 0.05MPa high-purity Ar gas, heated to 2000℃, and injected at 0.02MPa, is induction heated to melt it for 15s, and then injected onto the surface of a copper wheel rotating at 3000r / min to obtain the product.

[0066] Phase analysis of the 30 μm thick amorphous alloy ribbon prepared in Example 3 was performed using XRD. The XRD scanning speed was 6° / min, and the scanning range was 20°–80°. The results are as follows: Figure 4 As shown.

[0067] Depend on Figure 4 It can be seen that Re 50 B 25 Nb 25 Re 55 B 40 Y 15 Re 55 B 30 Sc 15 Re 50 B 35 Hf 15 The XRD patterns of all samples showed obvious broadened diffuse scattering peaks, with no other crystal diffraction peaks, indicating that the prepared strip samples were completely amorphous.

[0068] Example 4

[0069] The difference from Example 3 is as follows:

[0070] In step 1, Re a M b N c In the alloy composition design, Re represents rhenium, M represents boron, and N represents zirconium. The specific atomic proportions of each element are as follows: Re 55 B 35 Zr 10 ;

[0071] In step 3, the master alloy ingot obtained in step 2 is crushed, and 3g of the alloy is heated and melted in an Ar protective atmosphere. The molten alloy is then sprayed into a copper mold with an inner diameter of 1mm using a copper mold casting method to obtain a 1mm Re-based amorphous alloy rod. The specific operating conditions for the copper mold casting method include: vacuuming to a vacuum degree ≤1×10⁻⁶. -2 The gas is filled with 0.05 MPa of high-purity Ar gas and heated to 2000℃. The injection pressure is 0.02 MPa, and after induction heating to melt it for 15 seconds, it is injected into a 1 mm copper mold.

[0072] The performance of the Re-based amorphous alloy bulk prepared in Example 4 was tested, and the results are as follows:

[0073] (1) XRD was used to analyze the prepared Re 55 B 35 Zr 10 Phase analysis was performed on the amorphous alloy bulk material using XRD at a scanning speed of 6° / min and a scanning range of 20°–80°. The results are as follows: Figure 5 As shown.

[0074] Depend on Figure 5 As can be seen, the XRD pattern shows a broadened diffuse scattering peak, with no other crystal diffraction peaks appearing, indicating that the prepared bulk sample is a completely amorphous structure.

[0075] (2) The prepared Re was tested using a differential scanning calorimeter (DSC) according to GB / T 19466.2-2004. 55 B 35 Zr 10 The thermal properties of the amorphous alloy were measured at a heating rate of 20 K / min, with a sample mass of 20 mg. The results are as follows: Figure 6 As shown.

[0076] Depend on Figure 6 It can be seen that its glass transition temperature T g The crystallization initiation temperature is 1352K, T. x The K value is 1398 K. Its density ρ, measured using Archimedes' displacement method, is 17.265 g / cm³. 3 The microhardness Hv was determined according to the standard "Metallic Vickers Hardness Test: Inspection and Calibration of Hardness Testers" (GB / T 4340.2 2012). 0.2 The elastic modulus was 25.1 GPa. According to the standard "Nondestructive Testing: Ultrasonic Measurement Method for Elastic Modulus and Poisson's Ratio" (GB / T 38897-2020), its elastic properties were tested using ultrasonic waves. The elastic modulus E was 347 GPa, the shear modulus G was 131 GPa, and the bulk modulus B was 348 GPa. Specific data are shown in Table 2.

[0077] Table 2 Re55 B 35 Zr 10 Performance table of 1mm amorphous alloy samples

[0078]

[0079] (3) The prepared Re was tested according to the "Metallic Materials - Room Temperature Compression Test Method" (GB / T 7314-2017). 55 B 35 Zr 10 The compressive mechanical properties of the amorphous alloy sample were tested, and its compressive stress-strain curves are shown below. Figure 7 As shown.

[0080] Figure 7 The compression curve shows that the material's compressive fracture strength is 7.25 GPa, which is not only the current strength record in the field of amorphous alloys, but also the highest fracture strength in the entire field of metallic materials.

[0081] Therefore, the Re-based amorphous alloy material provided by this invention breaks through the performance limits of existing amorphous alloy materials, while taking into account the material properties of ultra-high temperature, ultra-high strength and ultra-high hardness. It has broad application prospects in many fields such as the preparation of precision glass forming molds, semiconductor processing cleavers, micro drill bits, wear-resistant coatings and thin films, radiation-resistant materials and anti-neutron shielding materials.

[0082] The foregoing description of specific exemplary embodiments of the invention is for illustrative and explanatory purposes. These descriptions are not intended to limit the invention to the precise forms disclosed, and it will be apparent that many changes and variations can be made in accordance with the foregoing teachings. The exemplary embodiments were chosen and described in order to explain the specific principles of the invention and its practical application, thereby enabling those skilled in the art to implement and utilize various different exemplary embodiments of the invention, as well as various different choices and variations. The scope of the invention is intended to be defined by the claims and their equivalents.

Claims

1. A Re-based amorphous alloy material, characterized in that, The chemical formula of the Re-based amorphous alloy material is Re. a M b N c Wherein, Re is rhenium, M is boron and / or silicon, and N includes at least one element selected from scandium, yttrium, zirconium, vanadium, niobium, hafnium, tantalum, molybdenum, and tungsten; a, b, and c are the atomic percentages of the corresponding elements, where a = 40–60, b = 20–45, and c = 10–30, and the sum of the atomic percentages of each element a + b + c = 100.

2. The Re-based amorphous alloy material as described in claim 1, characterized in that, In the Re-based amorphous alloy material, when M is silicon and N includes at least one of zirconium, hafnium, tantalum, and molybdenum, the atomic percentages of each element are a = 45–55, b = 25–40, and c = 10–25, respectively, and a + b + c = 100.

3. The Re-based amorphous alloy material as described in claim 1, characterized in that, The Re a Si b Zr c The glass transition temperature of amorphous alloy materials is above 1200K.

4. The Re-based amorphous alloy material as described in claim 1, characterized in that, The Re a Si b Zr c The amorphous alloy material has a Young's modulus of 265 GPa and a Vickers microhardness of over 17 Ga.

5. The Re-based amorphous alloy material as described in claim 1, characterized in that, In the Re-based amorphous alloy material, when M is boron and N includes at least one of zirconium, niobium, yttrium, scandium, and hafnium, the atomic percentages of each element are a = 40–60, b = 20–40, and c = 10–30, respectively, and a + b + c = 100.

6. The Re-based amorphous alloy material as described in claim 1, characterized in that, The Re a B b Zr c The glass transition temperature of amorphous alloy materials is above 1300K.

7. The Re-based amorphous alloy material as described in claim 1, characterized in that, The Re a B b Zr c The compressive fracture strength of the amorphous alloy material at room temperature is 7.25 GPa.

8. The Re-based amorphous alloy material as described in claim 1, characterized in that, The Re a B b Zr c The amorphous alloy material has a Young's modulus of 347 GPa and a Vickers microhardness of over 25 Ga.

9. The method for preparing the Re-based amorphous alloy material according to any one of claims 1-8, characterized in that, Includes the following steps: Step 1: According to the chemical formula Re of the Re-based high-temperature amorphous alloy a M b N c Calculate the mass ratio of each element and weigh and mix the ingredients. Step 2: Melt the elemental materials weighed in Step 1 in a protective atmosphere until homogeneous to obtain a master alloy ingot; Step 3: The master alloy ingot obtained in Step 2 is heated and melted in a protective atmosphere, and Re-based amorphous alloy strips are prepared by melt spin quenching; or the master alloy ingot obtained in Step 2 is heated and melted in a protective atmosphere, and Re-based amorphous alloy bulk is prepared by copper mold casting.

10. The application of the Re-based amorphous alloy material as described in any one of claims 1-8 in the preparation of precision glass forming molds, semiconductor processing cleavers, micro drill bits, wear-resistant coatings and films, radiation-resistant materials, and neutron-resistant shielding materials.

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