A heat treatment method for regulating the dimensional stability of amorphous alloy materials and its product

Abstract

The present invention provides a heat treatment method and product for regulating the dimensional stability of amorphous alloy materials, and relates to the technical field of amorphous alloy material processing. Specifically comprising: Step 1: Characterizing the thermophysical properties of the initial amorphous alloy sample; Step 2: Determining the characteristic temperature range in which the free volume of the amorphous alloy sample is significantly reduced based on the thermophysical properties; Step 3: Determining the optimal temperature point and the optimal holding time when the maximum free volume is eliminated within the characteristic temperature range; Step 4: Heat treating the amorphous alloy sample based on the optimal temperature point and the optimal holding time. The overall control method is simple and accurate, and the obtained amorphous alloy material has excellent dimensional stability and repeatability, and can be widely used in the field of high-precision instrument preparation.

Description

Technical Field

[0001] The present invention belongs to the technical field of amorphous alloy material processing, and in particular relates to a heat treatment method for regulating and controlling the dimensional stability of an amorphous alloy material and a product thereof. Background Art

[0002] Amorphous alloy, also known as metallic glass, is a kind of advanced metal material with short-range order and long-range disorder in atomic structure arrangement. Compared with traditional crystalline alloys, amorphous alloys have excellent physical and chemical properties such as high strength, high hardness, high elasticity, high wear resistance and corrosion resistance, and have very broad application prospects in the fields of machinery, electronics, energy and military.

[0003] High-precision instruments, such as aerospace optical remote sensing devices, have extremely high structural dimensional stability requirements for the surface morphology and relative position of their optical components. Slight changes will cause significant changes in the imaging quality of the optical remote sensor. Therefore, the use of materials with high dimensional stability is an important basis for ensuring the functional characteristics of high-precision instrument devices.

[0004] Compared with crystalline metal materials used in high-precision instruments, amorphous alloys have the advantage of excellent near-net-shape casting of parts; at the same time, this type of material is considered to be a single-phase supersaturated solid solution with uniform chemical composition in all directions, and does not have the anisotropy or thermal mismatch problems caused by crystal orientation and organizational structure in polycrystalline materials and composite materials. Therefore, it has excellent application scenarios in key structural parts of high-precision instruments.

[0005] However, unlike traditional crystalline materials, amorphous alloys are usually prepared under non-equilibrium conditions, and this type of preparation process will retain a certain amount of non-equilibrium void volume units (i.e., free volume) inside the amorphous alloy material. Therefore, due to its own high energy state, the amorphous alloy is always in a metastable state, and its interior always undergoes relaxation movement towards an equilibrium structure over time. When amorphous alloys are used as high-precision instrument parts for a long time at ambient temperature, the free volume inside them is annihilated by thermal relaxation, causing the size of the amorphous alloy parts to change by one percent to one ten-thousandth of an order of magnitude, seriously affecting the dimensional stability of this type of material. Therefore, mastering the heat treatment process method for high dimensional stability of amorphous alloys is an important basis for their application as high-precision instrument parts. Summary of the invention

[0006] The purpose of the present invention is to provide a heat treatment method for regulating the dimensional stability of an amorphous alloy material. First, the free volume annihilation law of an amorphous alloy sample in an initial state under the conditions of temperature T and time t is characterized, and the characteristic temperature range in which the free volume is significantly reduced is determined in combination with the thermal characteristic temperature of the amorphous alloy in the initial state; then, the optimal heat treatment temperature T for regulating the dimensional stability is determined by theoretical calculation. best and heat treatment time t best , and implement this process to obtain a final amorphous alloy with high dimensional stability. Furthermore, the final sample can be subjected to a temperature-time multi-cycle accelerated aging experiment under low simulated temperature conditions to characterize the effect of medium and low temperature cyclic relaxation behavior on the dimensional change of the sample, and to re-test the dimensional stability of the non-gold alloy. The overall control method is simple and accurate, and the obtained amorphous alloy material has excellent dimensional stability and repeatability, and can be widely used in the field of high-precision instrument preparation.

[0007] To achieve the above object, the present invention provides a heat treatment method for regulating the dimensional stability of an amorphous alloy material, which specifically comprises the following steps:

[0008] Step 1: Characterize the thermophysical properties of the initial amorphous alloy sample;

[0009] Step 2: determining a characteristic temperature range in which the free volume of the amorphous alloy sample is significantly reduced according to the thermophysical properties;

[0010] Step 3: Determine the optimal temperature point and the optimal holding time for eliminating the maximum free volume within the characteristic temperature range;

[0011] Step 4: heat-treating the amorphous alloy sample according to the optimal temperature point and the optimal holding time.

[0012] In a preferred embodiment, the step 1 comprises the following steps:

[0013] Step 11: preparing the amorphous alloy material into an amorphous alloy sample capable of thermal expansion testing;

[0014] Step 12: Test the thermal expansion curve and thermal expansion coefficient of the amorphous alloy sample at a constant heating rate; test the glass transition temperature T of the amorphous alloy at the same heating rate. g , Crystallization start temperature T x test.

[0015] In a preferred embodiment, in step 11, the shape and specifications of the amorphous alloy material at room temperature are not limited. It can be a bulk material or other forms, as long as the thermophysical properties and volume change laws required by the present invention can be obtained through non-standard testing methods.

[0016] In a preferred embodiment, in step 11, the method for preparing the test sample can be any method known to those skilled in the art, such as cutting, grinding, etc., as long as a sample that meets the thermal expansion test can be obtained. Preferably, the size of the amorphous alloy sample is φ4mm×25mm (±0.1mm).

[0017] In a preferred embodiment, in the step 12, the instrument for conducting thermal expansion curve and thermal expansion coefficient testing is a thermal expansion instrument (DIL), and the instrument for testing the glass transition temperature and crystallization start temperature of the amorphous alloy is a differential scanning calorimeter (DSC). Preferably, the heating rate is 5-20K / min.

[0018] Since the reduction of the free volume of amorphous alloys during heating will lead to the contraction of the length of amorphous alloy wires, which is a common property of amorphous alloys, the basic thermophysical properties of the initial amorphous alloys can be determined through the above two experiments. Typical results of the thermal expansion coefficient of amorphous alloys during heating are as follows: Figure 1 shown.

[0019] In a preferred embodiment, the step 2 comprises the following steps:

[0020] Step 21: Determine the temperature point at which the thermal expansion coefficient of the amorphous alloy sample deviates from the baseline, as the nominal starting temperature T of the amorphous alloy free volume reduction sr-on ;

[0021] Determine the highest temperature point at which the amorphous alloy sample maintains its basic shape as the softening temperature T of the amorphous alloy. soft ;

[0022] Step 22: Obtain the characteristic temperature range ΔT at which the free volume of the amorphous alloy is significantly reduced by the following formula:

[0023] △T=T soft -T sr-on .

[0024] In a preferred embodiment, in step 21, an extrapolation method is used to determine the temperature point at which the thermal expansion coefficient of the amorphous alloy sample deviates from the baseline.

[0025] In a preferred embodiment, the step 3 specifically includes the following steps:

[0026] Step 31: selecting a plurality of temperature points within the characteristic temperature range, and heat-treating the amorphous alloy sample respectively to obtain a law of changes of a plurality of linear dimensions of the initial amorphous alloy sample over time;

[0027] Step 32: Obtaining the instantaneous volume change at the corresponding temperature according to the linear dimension change rule;

[0028] Step 33: determining the maximum free volume that can be eliminated by thermal relaxation at different temperatures according to the volume change formula of the amorphous alloy material during thermal relaxation corresponding to the temperature point;

[0029] Step 34: Determine the optimum temperature point and the optimum holding time according to the maximum free volume that can be eliminated.

[0030] In a preferred embodiment, in step 31, the method for obtaining the linear dimensional variation law is: using a dilatometer (DIL) to continuously heat the initial amorphous alloy sample and perform isothermal precise measurement under different temperature conditions.

[0031] In a preferred embodiment, in step 31, the linear dimension variation rule specifically includes ΔL=(L-L0) / L0, wherein L0 is the original sample line length, and L is the instant sample line length.

[0032] In a preferred embodiment, in step 32, because the amorphous alloy has an isotropic characteristic, its corresponding instantaneous volume change △V≈3△L, therefore, the free volume change law of the initial amorphous alloy sample with temperature and time can be obtained through this measurement.

[0033] In a preferred embodiment, in step 33, the volume change formula of the amorphous alloy material during thermal relaxation is:

[0034] △V(t)=△V eq {1-exp[-(t / τ) β ]}, where △V eq is the limit shrinkage of volume, τ is the characteristic relaxation time, and β is the shape factor. The above three physical quantities are calculated by curve fitting from experimental measurements. Through this equation, we can know the maximum free volume that can be eliminated by thermal relaxation at different temperatures.

[0035] In a preferred embodiment, in step 34, the optimal temperature point is selected from the local minimum value of the linear expansion coefficient within the characteristic temperature range where the free volume of the amorphous alloy is significantly reduced; and the optimal holding time is the holding time for eliminating 95% of the free volume at the optimal temperature point.

[0036] In traditional heat treatment solutions for stress relief and instability elimination, T g Related heat treatment temperatures (such as T g -50K, 0.85T g The present invention takes a unique approach and characterizes the linear expansion coefficient as the sample is heated continuously according to the linear expansion curve of the sample. g) is characterized by its changing pattern. Figure 1 It can be seen that during the heating process, the initial amorphous alloy undergoes obvious relaxation behavior starting from a certain temperature point, causing the free volume in the sample to decrease significantly, thereby leading to a contraction in the length (volume) of the sample. This is a common property of amorphous alloys, and it also indirectly illustrates that the scheme of the present invention is universal and can be widely applied to various amorphous alloy materials. Figure 1 The temperature point at which the midline expansion coefficient deviates from the baseline is the nominal starting temperature (T sr-on ), this characteristic temperature can be obtained by the extrapolation method of traditional thermal analysis; T soft is the softening temperature of the amorphous alloy, which is the highest temperature point at which the sample can basically maintain its shape; thus, the characteristic temperature range (△T=T soft -T sr-on ). The heat treatment temperature T used in the present invention a It is in T sr-on To T soft The present invention selects the local minimum value of the linear expansion coefficient as the optimal temperature point T in the characteristic temperature range where the free volume of the amorphous alloy is significantly reduced. best According to the volume change formula of amorphous alloy materials during thermal relaxation, the holding time required to eliminate 95% of the free volume at the optimal temperature point is taken as the optimal holding time t best , a dimensionally stabilized amorphous alloy sample can be obtained relatively quickly.

[0037] In a preferred embodiment, in step 4, the heat treatment can be performed using conventional equipment used by those skilled in the art for processing amorphous alloy materials, such as using a high temperature box to maintain a certain temperature for a period of time.

[0038] In a preferred embodiment, after the step 4 is completed, the dimensional stability of the treated amorphous alloy sample is further tested, and the dimensional stability of the treated amorphous alloy sample is characterized by the residual strain under a cyclic temperature field near room temperature.

[0039] Specifically, the near-room temperature cycle test conditions are: 20°C-150°C as the temperature cycle loading range, 5K / min as the heating and cooling rate, and 20 minutes of insulation at 20°C and 150°C. Each time the temperature stabilizes to 20°C, the sample length L is measured by using a thermal expansion instrument (DIL). i (i=1,2,3…), we get △L i The relationship between the number of cyclic loading and the residual strain △L i =L i -L0.

[0040] Another object of the present invention is to provide an amorphous alloy product prepared by any of the above methods. The amorphous alloy product treated by the steps of the present invention has excellent dimensional stability and can be used as an important basis for the application of high-precision instrument parts.

[0041] In a preferred embodiment, the amorphous alloy material after stabilization treatment is retested, and the result shows that the residual strain of the amorphous alloy sample is within 0.5×10 -5 Within.

[0042] Compared with the prior art, the technical solution of the present invention has the following advantages:

[0043] 1. The present invention can determine the starting and ending temperature points where the free volume inside the amorphous alloy changes significantly through the thermal expansion curve and the synchronous thermal analysis curve of the amorphous alloy, thereby determining the heat treatment process temperature range and the optimal heat treatment temperature for regulating the dimensional stability of the amorphous alloy.

[0044] 2. The present invention can fit the free volume change law of the amorphous alloy through the change curve of the length of the amorphous alloy during the isothermal process. After extrapolating the curve, the heat treatment time after the free volume of the amorphous alloy is reduced to a certain content can be obtained, providing a theoretical and experimental basis for the design of the heat treatment process.

[0045] 3. The present invention can ensure that the amorphous alloy treated by the optimal heat treatment process has excellent dimensional stability in the alternating temperature field (the dimensional stability of the sample is controlled within 0.5×10 -5 This provides a guarantee for the application of amorphous alloys as high-precision instrument structural parts. BRIEF DESCRIPTION OF THE DRAWINGS

[0046] These and / or other aspects and advantages of the present invention will become more clear and easier to understand from the following detailed description of the embodiments of the present invention in conjunction with the accompanying drawings, in which:

[0047] Figure 1 Schematic diagram of typical results of the curve of the thermal expansion coefficient α of the amorphous alloy sample tested by the DIL thermal expansion instrument as a function of temperature T, wherein T sr-on is the nominal starting temperature of the free volume reduction of the amorphous alloy, T soft is the nominal softening temperature of the amorphous alloy, ΔT is the characteristic temperature range in which the free volume of the amorphous alloy is significantly reduced, T best The optimal heat treatment temperature for regulating the dimensional stability of amorphous alloys.

[0048] Figure 2 The diameter of the Zr in Example 1 of the present invention is 4 mm. 52.5 Ti5Cu17.9 Ni 14.6 Al 10 X-ray diffraction (XRD) patterns of amorphous alloy samples.

[0049] Figure 3 is Zr in Example 1 of the present invention 52.5 Ti5Cu 17.9 Ni 14.6 Al 10 Differential scanning calorimetry (DSC) curve and thermal expansion coefficient α curve of amorphous alloy.

[0050] Figure 4 is Zr in Example 1 of the present invention 52.5 Ti5Cu 17.9 Ni 14.6 Al 10 Isothermal shrinkage curve of amorphous alloy within the thermal temperature range △T where the free volume decreases significantly.

[0051] Figure 5 This is a cyclic temperature field test curve for the dimensional stability test of the amorphous alloy used in the present invention, wherein the cyclic temperature field is 293K-423K (20°C-150°C).

[0052] Figure 6 The optimal heat treatment temperature T of Example 1 of the present invention best And the optimal heat treatment time t best The two Zr 52.5 Ti5Cu 17.9 Ni 14.6 Al 10 Residual strain curve of amorphous alloy in cyclic temperature field.

[0053] Figure 7 The thermal expansion coefficient α of amorphous alloy samples of other different systems tested in the present invention varies with the reduced glass transition temperature T / T g The curves show the nominal starting temperature T of the free volume reduction of the amorphous alloy for different amorphous alloy systems. sr-on , nominal softening temperature T soft , the characteristic temperature range △T where the free volume is significantly reduced and the optimal heat treatment temperature T for dimensional stability regulation best . DETAILED DESCRIPTION

[0054] In order to enable those skilled in the art to better understand the present invention, the present invention is further described in detail below in conjunction with the accompanying drawings and specific implementation methods, but it should be understood that the protection scope of the present invention is not limited to the specific implementation methods.

[0055] Example 1

[0056] Step 1: Zr 52.5 Ti5Cu 17.9 Ni 14.6 Al 10 Characterization of basic thermophysical properties of initial amorphous alloy samples

[0057] By machining, Zr 52.5 Ti5Cu 17.9 Ni 14.6 Al 10 Amorphous alloy materials are prepared into samples that can be tested for thermal expansion by cutting and surface grinding. The size of the sample is φ4mm×25mm. The amorphous structure is determined by X-ray diffraction. Figure 2 As shown, the XRD spectrum is a diffuse scattering peak, and there is no obvious crystal peak, indicating its amorphous structure. A thermal expansion instrument (DIL) was used to conduct preliminary tests on the thermal expansion curve and thermal expansion coefficient of the amorphous alloy at a constant heating rate of 5K / min. A differential scanning calorimeter (DSC) was used to measure the glass transition temperature T of the amorphous alloy at a corresponding heating rate. g , Crystallization start temperature T x The above two experiments determine the basic thermophysical properties of the initial amorphous alloy. The results of the thermal expansion coefficient of the amorphous alloy during the heating process and the thermal analysis results are shown in the figure. Figure 3 The specific thermal parameters are shown in Table 1.

[0058] Table 1 Zr 52.5 Ti5Cu 17.9 Ni 14.6 Al 10 Thermal parameters of amorphous alloys

[0059]

[0060] Step 2: Zr 52.5 Ti5Cu 17.9 Ni 14.6 Al 10 Measurement of free volume change of amorphous alloys

[0061] Based on the above basic thermophysical properties, in the characteristic temperature range where the free volume is significantly reduced (△T = T soft -T sr-on), a thermal expansion instrument (DIL) was used to continuously heat the initial amorphous alloy sample and perform isothermal fine measurements under different temperature conditions to obtain the linear size change law of the initial amorphous alloy sample when the single parameter of temperature and time changes (△L=(L-L0) / L0, L0 is the original sample line length, L is the instantaneous sample line length. Because amorphous alloys have isotropic characteristics, their corresponding instantaneous volume change △V≈3△L. Through this measurement, the free volume change law of the initial amorphous alloy sample with temperature and time can be obtained. The volume change law of amorphous alloy materials in a certain state during thermal relaxation conforms to △V(t)=△V eq {1-exp[-(t / τ) β ]} relationship, through which the maximum free volume that can be eliminated by thermal relaxation at different temperatures can be obtained. The volume change curve of the amorphous alloy during the isothermal process is shown in Figure 4 As shown, the equation can be fitted according to the curve, and the fitting results are shown in Table 2.

[0062] Table 2 Zr 52.5 Ti5Cu 17.9 Ni 14.6 Al 10 Isothermal process curve fitting parameters of amorphous alloys

[0063]

[0064] Step 3: Zr 52.5 Ti5Cu 17.9 Ni 14.6 Al 10 Stabilization treatment of amorphous alloy samples

[0065] According to the curve fitting extrapolation in step 2, it can be known that the optimal heat treatment temperature of the amorphous alloy is 633K and the optimal heat treatment time is 12.7h. 52.5 Ti5Cu 17.9 Ni 14.6 Al 10 The amorphous alloy sample is taken out after being subjected to a thermal stabilization heat treatment at 633K for 12.7 hours in a vacuum heat treatment furnace, thereby completing the regulation of the dimensional stability of the amorphous alloy material.

[0066] Effect example

[0067] Dimensional stability test of the processed amorphous alloy material under cyclic temperature field

[0068] The two Zr stabilized 52.5 Ti5Cu 17.9 Ni 14.6 Al 10The dimensional stability of the amorphous alloy samples was retested and their residual strain was measured under a cyclic temperature field near room temperature.

[0069] Among them, the temperature cycle process loading characteristics are as follows Figure 5 As shown in the figure, the specific conditions are: after keeping at 293K for 20 minutes, the temperature is raised to 423K at a rate of 5K / min, and after keeping at 20 minutes, the temperature is lowered to 293K at a rate of 5K / min, and a total of i cycles are performed. Each time the temperature stabilizes to 20℃, the sample length is L i (i=1,2,3…), its residual strain △L i =L i -L0, thus obtaining △L i The relationship with the number of cyclic loading is as follows: Figure 6 shown.

[0070] Depend on Figure 6 It can be found that after the amorphous alloy material is subjected to a dimensional stability heat treatment process by the technical solution of the present invention, Zr 52.5 Ti5Cu 17.9 Ni 14.6 Al 10 The residual strain △L of two samples of amorphous alloy was 20℃-150℃ cycled for more than 10 times. i Both are within 0.5×10 -5 It is proved that the heat treatment process adopted in the present invention is effective and has excellent repeatability.

[0071] Example 2

[0072] The same test method as in Example 1 was used to characterize the thermophysical properties of other amorphous alloy materials, and the characteristic temperature range in which the free volume of the amorphous alloy sample was significantly reduced was determined. The results are shown in Table 3.

[0073] Table 3 Thermal parameters of different amorphous alloys tested in the present invention

[0074]

[0075] According to the method of Example 1, the limit volume shrinkage at the optimal heat treatment temperature and the optimal heat treatment time determined according to the free volume change formula of the amorphous alloy sample with temperature and time are shown in Table 4.

[0076] Table 4 Limit volume shrinkage and optimal heat treatment time at the optimal heat treatment temperature of other amorphous alloys determined by the present invention

[0077]

[0078] Thermal expansion coefficient α of other amorphous alloy samples with reduced glass transition temperature T / Tg The change curve of Figure 7 As shown in the figure, it can be seen that the free volume annihilation of amorphous alloys before the glass transition is universal, which further illustrates the universality of this method for amorphous alloys.

[0079] Effect example

[0080] The dimensional stability test method under the cyclic temperature field in the effect example is used. The alloy material after stability control according to the optimal heat treatment temperature and optimal heat treatment time determined in Table 4 is cycled for more than 10 times in the cyclic temperature field of 20℃-150℃. The residual strain △L i Both are within 0.5×10 -5 It can be seen that the heat treatment method for regulating the dimensional stability of amorphous alloy materials provided by the present invention can be widely applied to amorphous alloy materials of various components.

[0081] The foregoing description of specific exemplary embodiments of the present invention is for the purpose of illustration and demonstration. These descriptions are not intended to limit the present invention to the precise form disclosed, and it is clear that many changes and variations can be made based on the above teachings. The purpose of selecting and describing the exemplary embodiments is to explain the specific principles of the present invention and its practical application, so that those skilled in the art can realize and utilize various different exemplary embodiments of the present invention and various different selections and changes. The scope of the present invention is intended to be limited by the claims and their equivalents.

Claims

1. A heat treatment method for regulating the dimensional stability of an amorphous alloy material, characterized in that: The following steps are involved: Step 1: Characterize the thermophysical properties of the initial amorphous alloy sample; Step 2: determining a characteristic temperature range in which the free volume of the amorphous alloy sample is significantly reduced according to the thermophysical properties; Step 3: Determine the optimal temperature point and the optimal holding time for eliminating the maximum free volume within the characteristic temperature range; Step 4: heat treating the amorphous alloy sample according to the optimal temperature point and the optimal holding time; Wherein, the step 2 comprises the following steps: Step 21: Determine the temperature point at which the thermal expansion coefficient of the amorphous alloy sample deviates from the baseline, as the nominal starting temperature of the amorphous alloy free volume reduction T sr-on ; Determine the highest temperature point at which the amorphous alloy sample maintains its basic shape as the softening temperature of the amorphous alloy T soft ; Step 22: Obtain the characteristic temperature range △ where the free volume of the amorphous alloy is significantly reduced by the following formula: T， △ T = T soft - T sr-on ； The step 3 specifically includes the following steps: Step 31: selecting a plurality of temperature points within the characteristic temperature range, and heat-treating the amorphous alloy sample respectively to obtain a law of changes of a plurality of linear dimensions of the initial amorphous alloy sample over time; Step 32: Obtaining the instantaneous volume change at the corresponding temperature according to the linear dimension change rule; Step 33: Determine the maximum free volume that can be eliminated by thermal relaxation at different temperatures according to the volume change formula of the amorphous alloy material during thermal relaxation corresponding to the temperature point; the volume change formula of the amorphous alloy material during thermal relaxation is: △ V (t) = △ V eq {1-exp [-( t / τ) β ]},in, △V eq is the limit shrinkage of volume, τ is the characteristic relaxation time, and β is the shape factor; Step 34: Determine the optimum temperature point and the optimum holding time according to the maximum free volume that can be eliminated.

2. The heat treatment method for regulating the dimensional stability of an amorphous alloy material according to claim 1, characterized in that: The step 1 comprises the following steps: Step 11: preparing the amorphous alloy material into an amorphous alloy sample capable of thermal expansion testing; Step 12: Test the thermal expansion curve and thermal expansion coefficient of the amorphous alloy sample at a constant heating rate; test the glass transition temperature of the amorphous alloy at the same heating rate. T g , Crystallization start temperature T x test.

3. The heat treatment method for regulating the dimensional stability of an amorphous alloy material according to claim 1, characterized in that: In step 31, the linear dimension variation rule specifically includes △ L =( L -L0) / L0, where L0 is the original sample line length, L is the instant sample line length; In step 32, the instantaneous volume change is △ V ≈3△ L .

4. The heat treatment method for regulating the dimensional stability of an amorphous alloy material according to claim 1, characterized in that: In step 34, The optimal temperature point is selected from the local minimum value of the linear expansion coefficient within the characteristic temperature range where the free volume of the amorphous alloy is significantly reduced; the optimal insulation time is the insulation time for eliminating 95% of the free volume at the optimal temperature point.

5. The heat treatment method for regulating the dimensional stability of an amorphous alloy material according to claim 1, characterized in that: After the step 4 is completed, the dimensional stability of the treated amorphous alloy sample is further tested, and the dimensional stability of the treated amorphous alloy sample is characterized by the residual strain under a cyclic temperature field near room temperature.

6. The amorphous alloy material prepared by the method according to any one of claims 1 to 5.

7. The amorphous alloy material prepared as claimed in claim 6, characterized in that: The amorphous alloy materials after stabilization treatment were retested, and the results showed that the residual strain of the amorphous alloy samples was within 0.5×10 -5 Within.

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