Method for producing an alloy and alloy

Abstract

The application relates to a preparation method of an alloy and the alloy, and the preparation method of the alloy comprises the following steps: heat treating the alloy, and applying a pulse magnetic field in a cooling step of the heat treatment to obtain the alloy. Therefore, by applying the pulse magnetic field in the cooling step of the heat treatment of the alloy, the spin configuration of atoms in the alloy can be changed, the pinning effect between solute atoms and dislocations is reduced, the defects in the alloy are reduced, the diffusion of the atoms in the alloy is promoted, the uneven distribution of the structure in the alloy is improved, and the service performance of the alloy is improved.

Description

Technical Field

[0001] This invention relates to the field of metal processing and heat treatment technology, specifically to a method for preparing an alloy and the alloy itself. Background Technology

[0002] Alloy materials typically possess excellent properties. For example, titanium alloys exhibit superior comprehensive properties such as high specific strength, high temperature resistance, low temperature resistance, non-magnetic properties, weldability, and good biocompatibility. As a result, titanium alloy materials have found increasing applications in numerous fields, including chemical, aerospace, nuclear industry, weaponry, marine, petroleum, medical, and daily life.

[0003] Currently, the high-temperature melting method is commonly used in the preparation process of titanium alloys, including melting, casting, and heat treatment. However, this preparation process is prone to causing element segregation in the alloy, resulting in uneven alloy structure and affecting the service performance of the alloy. Summary of the Invention

[0004] In view of the technical problems existing in the background art, this application provides a method for preparing an alloy. The method provided by the present invention can reduce the segregation of elements in the alloy, thereby improving the unevenness of the structure in the alloy and enhancing the service performance of the alloy.

[0005] To achieve the above objectives, according to an embodiment of the present invention, the alloy preparation method includes: heat-treating the alloy and applying a pulsed magnetic field during the cooling step of the heat treatment to obtain the alloy.

[0006] According to the alloy preparation method of the above embodiments of the present invention, by applying a pulsed magnetic field in the cooling step of alloy heat treatment, the spin configuration of atoms inside the alloy can be changed, the pinning effect between solute atoms and dislocations can be reduced, thereby reducing defects inside the alloy, promoting the diffusion of atoms inside the alloy, improving the uneven distribution of microstructure in the alloy, and enhancing the service performance of the alloy.

[0007] In addition, the alloy preparation method according to the above embodiments of the present invention may also have the following additional technical features:

[0008] In some embodiments of the present invention, the pulsed magnetic field is applied t minutes after the start of cooling, where t ≤ 5. This can improve the inhomogeneity of the alloy structure and enhance its service performance.

[0009] In some embodiments of the present invention, the intensity of the pulsed magnetic field is 0.6T-3T, and can be selected as 1T-2T. This can improve the inhomogeneity of the alloy structure and enhance its service performance.

[0010] In some embodiments of the present invention, the application time of the pulsed magnetic field is 2 min-5 min, optionally 3 min-4 min. This can improve the unevenness of the microstructure in the alloy and enhance its service performance.

[0011] In some embodiments of the present invention, the pulse width of the pulsed magnetic field is 0.5s-10s. This can improve the inhomogeneity of the alloy structure and enhance its service performance.

[0012] In some embodiments of the present invention, the pulse period of the pulsed magnetic field is 2s-11s. This can improve the inhomogeneity of the alloy structure and enhance its service performance.

[0013] In some embodiments of the present invention, the cooling includes air cooling. This can improve the inhomogeneity of the alloy's microstructure and enhance its service performance.

[0014] In some embodiments of the present invention, the air cooling rate is 0.1℃ / s-2℃ / s. This can improve the inhomogeneity of the alloy's microstructure and enhance its service performance.

[0015] In some embodiments of the present invention, the heat treatment includes solution treatment, water quenching, aging, and cooling. This can improve the inhomogeneity of the alloy's microstructure and enhance its service performance.

[0016] In some embodiments of the present invention, the solution treatment temperature is 705°C-775°C. This can improve the service performance of the alloy.

[0017] In some embodiments of the present invention, the solution treatment time is 60-120 minutes. This can improve the service performance of the alloy.

[0018] In some embodiments of the present invention, the aging temperature is 480°C-620°C. This can improve the service performance of the alloy.

[0019] In some embodiments of the present invention, the aging time is 8-10 hours. This can improve the service performance of the alloy.

[0020] A second aspect of the present invention provides an alloy, which, according to an embodiment of the invention, is prepared by the method described above. Therefore, the method provided by the present invention can improve the inhomogeneity of the alloy's microstructure and enhance its service performance.

[0021] In addition, the alloy according to the above embodiments of the present invention may also have the following additional technical features:

[0022] In some embodiments of the present invention, the alloy includes at least one of titanium alloy and aluminum alloy.

[0023] Additional aspects and advantages of the invention will be set forth in part in the description which follows, and in part will be obvious from the description, or may be learned by practice of the invention. Attached Figure Description

[0024] The above and / or additional aspects and advantages of the present invention will become apparent and readily understood from the description of the embodiments taken in conjunction with the following drawings, in which:

[0025] Figure 1 A schematic diagram of one embodiment of the pulsed magnetic field device of the present invention is shown;

[0026] Figure 2 A schematic diagram of the pulsed magnetic field operation according to an embodiment of the present invention is shown;

[0027] Figure 3 A comparison graph of magnetic curves for Example 1 and Comparative Example 2 is shown;

[0028] Figure 4 A comparison graph of the magnetic curves of Comparative Example 1 and Comparative Example 2 is shown;

[0029] Figure 5 The tensile test comparison diagrams of Example 1 and Comparative Example 2 are shown;

[0030] Figure 6 A comparison graph showing the fatigue crack propagation rates of Example 1 and Comparative Example 2 is displayed.

[0031] Explanation of reference numerals in the attached figures:

[0032] 1: Movable magnetic yoke; 2: Sample stage; 3: Coil; 4: Fixed magnetic yoke. Detailed Implementation

[0033] The embodiments of the present invention are described in detail below. The embodiments described below are exemplary and are only used to explain the present invention, and should not be construed as limiting the present invention.

[0034] It should be noted that the terms "first" and "second" are used for descriptive purposes only and should not be construed as indicating or implying relative importance or implicitly specifying the number of indicated technical features. Therefore, a feature defined as "first" or "second" may explicitly or implicitly include one or more of that feature. Furthermore, in the description of this invention, unless otherwise stated, "a plurality of" means two or more.

[0035] Alloy materials possess superior properties compared to pure metals and are widely used in machinery, automotive, electronics, and aerospace industries. For example, Ti-1023 alloy has been used in the manufacture of components such as aircraft landing gear. To ensure the stability of Ti-1023 titanium alloy at room temperature, approximately 2% iron is added. Due to limitations in heat treatment processes during alloy preparation, iron atom clusters are prone to segregation, especially at high-energy defects such as grain boundaries, phase boundaries, and dislocations. This results in high microstructure inhomogeneity and a high crack propagation rate.

[0036] Currently, there are three main methods for improving the uniformity of the internal structure of alloys: (1) improving the melting process, such as improving the melting furnace, controlling the melting speed, and adjusting the electrode position; (2) improving the heat treatment process, such as improving the solution treatment, aging time, and cooling method; and (3) applying deformation after heat treatment, such as repeated rolling, utilizing the stress-induced phase transformation properties of the alloy to adjust its microstructure during the stress process. However, these techniques are not very effective in controlling the segregation of iron atom clusters and do not achieve targeted control from a microscopic perspective.

[0037] In view of this, in one aspect of the present invention, a method for preparing an alloy is proposed. According to an embodiment of the present invention, the method includes heat-treating the alloy and applying a pulsed magnetic field during the cooling step of the heat treatment to obtain the alloy.

[0038] According to the alloy preparation method of the above embodiments of the present invention, by applying a pulsed magnetic field in the cooling step of alloy heat treatment, the spin configuration of atoms inside the alloy can be changed, the pinning effect between solute atoms and dislocations can be reduced, thereby reducing defects inside the alloy, promoting the diffusion of atoms inside the alloy, improving the uneven distribution of microstructure in the alloy, and enhancing the service performance of the alloy.

[0039] It should be noted that the preparation process of alloys typically includes smelting, casting, forging, and heat treatment. Smelting involves melting the constituent elements of the alloy into a liquid metal using a heated furnace and then tempering it. Casting refers to pouring the molten liquid metal into a casting cavity conforming to the shape of the part, allowing it to cool and solidify to obtain an alloy billet. Forging is a processing method that uses forging machinery to apply pressure to the cast alloy billet, causing it to undergo plastic deformation to obtain a forging with specific mechanical properties, shape, and size. Heat treatment is a metal heat treatment process that uses heating, holding, and cooling to obtain the desired microstructure and properties. The specific processes for smelting, casting, forging, and heat treatment described above are not particularly limited, and those skilled in the art can flexibly choose according to their needs.

[0040] In some embodiments of the present invention, heat treatment includes solution treatment, water quenching, aging, and cooling. Solution treatment refers to heating the alloy to a high-temperature single-phase region and holding it at that temperature, so that the solute atoms in the alloy can dissolve to the maximum extent in the solid solution without causing the alloy to melt, thereby improving the alloy's toughness and corrosion resistance. Water quenching is a quenching process using water as a quenching agent. The alloy after solution treatment is placed in water, then removed, heated to red-hot, and then placed in water again, and so on, which can improve the rigidity of the alloy. Aging refers to a heat treatment process in which the properties, shape, and size of the alloy workpiece change over time after solution treatment and water quenching, and is placed at a high temperature or room temperature for a certain period of time. Aging treatment can eliminate the internal stress of the alloy workpiece, stabilize the microstructure and size, and improve the mechanical properties of the alloy. Cooling refers to cooling the alloy to room temperature after aging treatment, which facilitates the collection of the alloy.

[0041] It should be noted that the cooling method is not specifically limited, and those skilled in the art can choose according to their needs. In a specific embodiment of this application, air cooling is used, which is a type of cooling method that uses air as a medium to cool the object to be cooled. This typically involves increasing the surface area of ​​the object to be cooled, increasing the rate at which air flows over the object per unit time, or a combination of both methods. Therefore, using air cooling allows for finer grains within the alloy, improving its toughness and plasticity.

[0042] In some embodiments of the present invention, the air cooling rate is 0.1℃ / s-2℃ / s. For example, the air cooling rate can be 0.3℃ / s-1.8℃ / s, 0.5℃ / s-1.5℃ / s, 0.8℃ / s-1.2℃ / s, etc. When the air cooling rate is too fast, it will be detrimental to the refinement of the internal grains of the alloy, making crystallization difficult; when the air cooling rate is too slow, it will slow down the crystallization process inside the alloy, which can weaken the diffusion ability of atoms. Therefore, limiting the air cooling rate within the above range can promote the slow cooling of the alloy, making the internal grains of the alloy finer, and improving the toughness and plasticity of the alloy.

[0043] In some embodiments of the present invention, the solution treatment temperature is 705℃-775℃. For example, the solution treatment temperature can be 710℃-770℃, 715℃-765℃, 720℃-760℃, 725℃-755℃, 730℃-750℃, 735℃-745℃, etc. When the solution treatment temperature is too high, overheating will occur, causing the alloy to crack during water quenching and reducing its toughness. When the solution treatment temperature is too low, the alloy's performance after aging will not meet requirements. Therefore, limiting the solution treatment temperature within the above range can effectively reduce the residual stress caused by the thermal expansion of the metal material, giving the alloy better heat treatment morphological stability and improving its service performance.

[0044] In some embodiments of the present invention, the solution treatment time is 60 min-120 min, for example, it can be 70 min-110 min, 80 min-100 min, 90 min-100 min, etc. Therefore, limiting the solution treatment time to the above range can effectively reduce the residual stress caused by the thermal expansion of the metallic material, giving the alloy better heat treatment morphological stability and improving its service performance.

[0045] In some embodiments of the present invention, the aging temperature is 480℃-620℃, for example, 490℃-600℃, 500℃-580℃, 530℃-550℃, etc. When the aging temperature is too high, atomic diffusion in the alloy is facilitated, and the critical nucleus size of the precipitated phase in the supersaturated solid solution is large, leading to lower strength and hardness of the alloy. When the aging temperature is too low, solute atom diffusion in the alloy is difficult, and solute atom segregation is likely to occur. Therefore, limiting the aging temperature within the above range can improve the phenomenon of solute atom segregation in the alloy and improve the service performance of the alloy.

[0046] In some embodiments of the present invention, the aging time is 8-10 hours. For example, the aging time can be 8.3-9.8 hours, 8.5-9.6 hours, 8.6-9.2 hours, etc. If the aging time is too long, the alloy will be over-aged, reducing the strengthening effect and even causing softening; if the aging time is too short, the alloy will be under-aged, reducing the strengthening effect. Therefore, limiting the aging time to the above range can improve the service performance of the alloy.

[0047] It should be noted that "applying a pulsed magnetic field during the cooling step of heat treatment" refers to applying a pulsed magnetic field during the slow cooling process of the alloy in a natural environment after aging treatment. The pulsed magnetic field uses an intermittent oscillator to generate intermittent pulsed current, which, when passed through the coil of an electromagnet, produces pulsed magnetic fields of various shapes. The characteristic of a pulsed magnetic field is that it appears intermittently, and the frequency, waveform, and peak value of the magnetic field can be adjusted as needed. The device for applying the pulsed magnetic field is not particularly limited; in one embodiment of the invention, the pulsed magnetic field device used is as follows: Figure 1 As shown, specifically, the pulsed magnetic field device includes a movable magnetic yoke 1, a sample stage 2, a coil 3, and a fixed magnetic yoke 4. The aged alloy is placed on the sample stage. The distance between the movable magnetic yoke 1 and the fixed magnetic yoke 4 can be adjusted according to the size of the alloy sample. The strength, pulse width, and pulse period of the magnetic field are adjusted by the built-in controller to generate a low-frequency square wave current, thereby performing pulsed magnetic field treatment on the alloy.

[0048] In some embodiments of the present invention, the pulsed magnetic field is applied t minutes after the start of cooling, where t ≤ 5. For example, t can be 0-4.5, 1-4, 1.5-3.5, 2-3, etc. During the cooling process after aging, the solute atoms inside the alloy are still in a dispersed state. Applying a pulsed magnetic field at this time utilizes the magnetoplastic effect to cause the solute atoms in the high-energy defects inside the alloy sample to depolymerize and diffuse, thereby improving the segregation phenomenon of solute atoms. However, if the pulsed magnetic field is applied after the cooling time is too long, the diffusion rate of solute atoms will decrease, affecting the service performance of the alloy. Therefore, limiting the start time of applying the pulsed magnetic field to within the above-mentioned cooling time range can improve the segregation phenomenon of solute atoms, thereby improving the service performance of the alloy.

[0049] It should be noted that magnetoplastic effect refers to the influence of magnetic field on the plasticity, strength and structural defect state of alloy materials. High-energy defects refer to grain boundaries, phase boundaries and dislocations that appear inside the alloy during the alloy preparation process. The presence of these defects will increase the internal energy of the system and cause solute atoms to accumulate at these defects, resulting in high non-uniformity of the alloy structure, high crack propagation rate and reduced service performance of the alloy.

[0050] In some embodiments of the present invention, the intensity of the pulsed magnetic field is 0.6T-3T. For example, the intensity of the pulsed magnetic field can be 0.8T-2.8T, 1T-2.6T, 1.2T-2.3T, 1.5T-2.0T, 1.6T-1.8T, etc. Limiting the intensity of the pulsed magnetic field within the above range is beneficial for the diffusion of solute atoms under the conditions of the pulsed magnetic field, improving the segregation phenomenon of solute atoms, thereby improving the service performance of the alloy. The intensity of the pulsed magnetic field is preferably 1T-2T.

[0051] In some embodiments of the present invention, the application time of the pulsed magnetic field is 2-5 minutes. For example, the application time of the pulsed magnetic field can be 2.5-4.5 minutes, 3-4 minutes, 3.3-3.8 minutes, etc. It should be noted that the application time of the pulsed magnetic field refers to the total application time of the pulsed magnetic field process, that is, the time from the start of the application of the pulsed magnetic field to the end of the application of the pulsed magnetic field, as shown in the reference. Figure 2 The working spectrum of the pulsed magnetic field is displayed. The time shown at point e in the graph is the application time of the pulsed magnetic field. Limiting the pulsed magnetic field time within the above range ensures short processing time, minimal disruption to production, and simplicity. The preferred application time of the pulsed magnetic field is 3-4 minutes.

[0052] In some embodiments of the present invention, the pulse width of the pulsed magnetic field is 0.5s-10s, where pulse width refers to the duration during which a single pulse can reach its maximum value. Figure 2 The difference between the time at point c and the time at point b is the pulse width. For example, the pulse width of the pulsed magnetic field can be 1s-9s, 2s-8s, 3s-7s, 4s-6s, etc. Therefore, limiting the pulse width of the pulsed magnetic field within the above range is beneficial for the diffusion of solute atoms under the pulsed magnetic field conditions, improving the segregation phenomenon of solute atoms, thereby improving the service performance of the alloy.

[0053] In some embodiments of the present invention, the pulse period of the pulsed magnetic field is 2s-11s. The pulse period refers to the difference in arrival times of adjacent pulses, as shown in the reference... Figure 2 The time interval from point a to point c is one pulse cycle. For example, the pulse cycle of the pulsed magnetic field can be 3s-10s, 4s-9s, 5s-8s, 6s-7s, etc. Therefore, by limiting the pulse cycle of the pulsed magnetic field to the above range, the duration of the pulsed magnetic field can be controlled, which will hardly affect the production rhythm of the alloy. This is beneficial for the diffusion of solute atoms under the conditions of the pulsed magnetic field, improves the segregation phenomenon of solute atoms, and thus improves the service performance of the alloy.

[0054] According to embodiments of the present invention, by applying a pulsed magnetic field for a certain period of time during the alloy cooling process, the solute atom clusters at high-energy defects inside the alloy are depolymerized and diffused using the magnetoplastic effect. This improves the alloy's strength, reduces the crack propagation rate on the alloy surface, and enhances the service performance of the alloy material. Furthermore, the method provided by the present invention does not affect the appearance, size, or morphology of the alloy sample, can be used as the final step in the processing, has a short processing time, hardly affects the alloy production rhythm, and does not generate thermal effects, making it convenient and environmentally friendly.

[0055] In another aspect, the present invention provides an alloy. According to an embodiment of the present invention, the alloy is obtained using the above-described alloy preparation method. During the cooling process of the alloy heat treatment, a pulsed magnetic field is applied for a certain period of time. Utilizing the magnetoplastic effect, the solute atoms in the clusters at high-energy defects within the alloy sample undergo depolymerization and diffusion, thereby improving the alloy's strength, reducing the crack propagation rate on the alloy surface, and enhancing the service performance of the alloy material. Furthermore, the method provided by the present invention does not affect the appearance, dimensions, or morphology of the alloy sample, can be used as the final step in the processing steps, has a short processing time, hardly affects the alloy production rhythm, and does not generate thermal effects, making it convenient and environmentally friendly.

[0056] In some embodiments of the present invention, the alloy comprises at least one of titanium alloy and aluminum alloy. Thus, by applying a pulsed magnetic field during the cooling step of alloy heat treatment, the spin configuration of atoms within the alloy can be altered, thereby reducing the pinning effect of solute atoms on defects such as dislocations, promoting atomic diffusion, improving the uneven distribution of microstructure within the alloy, and enhancing the alloy's service performance.

[0057] The present disclosure will be explained below with reference to embodiments. Those skilled in the art will understand that the following embodiments are for illustrative purposes only and should not be construed as limiting the scope of the disclosure. Where specific techniques or conditions are not specified in the embodiments, they are performed in accordance with the techniques or conditions described in the literature in the art or according to the product instructions. Reagents or instruments whose manufacturers are not specified are all conventional products that can be obtained commercially.

[0058] Example 1

[0059] (1) The Ti-1023 alloy sample was subjected to solution treatment at 760℃ for 120 min, and then the solution-treated Ti-1023 alloy was subjected to water quenching.

[0060] (2) The water-quenched Ti-1023 alloy was aged for 8 hours at 520℃, and then the aged Ti-1023 alloy was air-cooled, with the air cooling rate controlled at 1℃·s. -1 .

[0061] (3) After the Ti-1023 alloy is air-cooled for 1 minute, a pulsed magnetic field with an intensity of 1.5T is applied, and the pulse width of the pulsed magnetic field is controlled to be 0.5s and the pulse period is 2s. After 3 minutes of pulsed magnetic field treatment, the pulsed magnetic field is stopped, and the Ti-1023 alloy is air-cooled to room temperature to obtain the magnetically treated Ti-1023 alloy.

[0062] The Ti-1023 alloys obtained in Examples 2-13 and Comparative Examples 1-2 were the same as those in Example 1, except for the parameters of air cooling rate and pulsed magnetic field in the heat treatment process (see Table 1).

[0063] The parameters for heat treatment of Ti-1023 alloy in Examples 1-13 and Comparative Examples 1-2 of this application are shown in Table 1.

[0064] Table 1

[0065]

[0066] "-" indicates that no pulsed magnetic field was applied.

[0067] Performance testing

[0068] (1) Magnetic curve test:

[0069] Taking Example 1 as an example, the magnetization curves of the Ti-1023 alloy before and after magnetic treatment were measured at room temperature using a superconducting quantum interference magnetometer (SQUID). This device provides good detection results for weakly magnetic samples and can be used to characterize the enrichment degree of Fe atom clusters. This is because Fe atoms are usually concentrated at high-energy defects in the material system, such as grain boundaries, phase boundaries, and dislocations. The magnetometer applied a periodic magnetic field to the sample, gradually varying the magnetic field strength from 15000 Oe to -15000 Oe and back to 15000 Oe. Paramagnetic and ferromagnetic materials within the system exhibited different changes in response to this applied magnetic field. For the Ti-1023 alloy, its main internal components are Ti, Al, V, and Fe, of which only Fe is ferromagnetic, while the others are paramagnetic. When the Fe concentration is high in a certain region, the instrument can detect the change in magnetic moment caused by it in the magnetic field. However, when Fe atoms are dispersed, their local concentration is below the detection limit, which will no longer contribute to the overall magnetization curve of the material obtained by testing. The samples were first subjected to a magnetization curve test, then magnetically treated, and the magnetization curves of these samples were tested again after the magnetic treatment. The samples were demagnetized before each test. Figure 3 The graph shows a comparison of the magnetic curves of Example 1 and Comparative Example 2. Figure 4 The graph shows a comparison of the magnetic curves for Comparative Example 1 and Comparative Example 2. The vertical axis in the graph represents the saturation magnetization of the alloy, which can be seen from the 5.0 × 10⁻⁶ axis in the graph. 5 A / m-1.0×10 6 The plateau between A and m reads the saturation magnetization M of the alloy. S , of which M S M can characterize the enrichment degree of Fe atom clusters. S The larger the value, the more severe the Fe atom segregation.

[0070] M of the Ti-1023 alloys obtained in Examples 2-13 and Comparative Examples 1-2 S The testing process is the same as above.

[0071] (2) Tensile test:

[0072] Taking Example 1 as an example, a tensile test was conducted at room temperature on a Zwick / Roell Z100 tensile tester at a rate of 2 mm / min. The length of the Ti-1023 alloy was 65 mm. The clamping section was threaded, and the extensometer was used at low strain amplitude (less than 2%) with an initial gauge length of 25 mm. The tensile test conformed to the relevant national standard (GB / T 228.1-2010). Figure 5 The tensile test comparison graphs of Example 1 and Comparative Example 2 are shown. The longitudinal axis in the graph represents the engineering stress, which is also the tensile strength of the alloy. The peak value in the graph is the tensile strength of the alloy.

[0073] The tensile strength testing procedures for the Ti-1023 alloys obtained in Examples 2-13 and Comparative Examples 1-2 are the same as those described above.

[0074] (3) Fatigue crack propagation rate test:

[0075] Taking Example 1 as an example, the fatigue crack propagation rate was tested on an MTS810 testing machine. The test conformed to the relevant national standard (GB / T 6398-2017), and the crack propagation direction was consistent with the longitudinal direction of the Ti-1023 alloy forging. All tests were conducted at room temperature, using the K-lift method, with a stress ratio of 0.1, a frequency of 10Hz, and a sine wave loading waveform. Figure 6 The graph shows a comparison of fatigue crack propagation rates between Example 1 and Comparative Example 2. The vertical axis represents the length of crack propagation in each cycle, and the horizontal axis represents the stress intensity factor applied during the test. By comparing the crack propagation length of the alloy under the same stress intensity factor, the smaller the crack propagation length, the better the fatigue resistance of the alloy.

[0076] The testing process for the fatigue crack propagation rate of the Ti-1023 alloys obtained in Examples 2-13 and Comparative Examples 1-2 was the same as above.

[0077] The performance test results of the Ti-1023 alloys in each embodiment and comparative example are shown in Table 2.

[0078] Table 2

[0079]

[0080]

[0081] From Table 2 and Figure 3It can be seen that, compared with Comparative Example 1 and Comparative Example 2, the alloy in Comparative Example 2 that was not magnetically treated during air cooling has a higher M value. S The value is 0.0046 emu / g, while Example 1 is an alloy that has undergone magnetic treatment during air cooling, and its M... S The value is 0.0022 emu / g, which is significantly smaller than that of Comparative Example 2. This is because the application of the pulsed magnetic field causes the Fe atom clusters to diffuse. The low concentration of Fe atom clusters cannot be detected by the instrument, and therefore no longer contributes to the overall magnetization curve of the alloy material.

[0082] Figure 4 A comparison graph of the magnetic curves of Comparative Example 1 and Comparative Example 2 is shown. From the graph, the M of the alloy obtained in Comparative Example 1 can be obtained. S The value is 0.0041 emu / g, and the M of the alloy obtained in Comparative Example 1 is... S The value is 0.0046 emu / g, while the M value in Example 1 of this application is... S The value was 0.0022 emu / g, compared to M in comparative examples 1-2. S The value is significantly greater than that in Example 1. It can be seen that Fe atoms clustered in the alloys prepared in Comparative Examples 1-2, while the application of the pulsed magnetic field in this application caused the Fe atom clusters to diffuse.

[0083] Figure 5 The tensile test comparison graphs of Example 1 and Comparative Example 2 are shown. From the graphs, it can be seen that the tensile strength of the alloy obtained in Example 1 is 1197 MPa, and the tensile strength of the alloy obtained in Comparative Example 2 is 1150 MPa. It can be seen that the tensile strength of the alloy obtained in Example 1 is significantly higher than that of the alloy obtained in Comparative Example 2. This shows that the alloy preparation method of this application can improve the service performance of the alloy.

[0084] Figure 6 The graph shows a comparison of fatigue crack propagation rates between Example 1 and Comparative Example 2. To increase the reliability of the test, two sets of tests were conducted on the alloys obtained in Example 1 and Comparative Example 2 using the same parameters. As can be seen from the graph, after the two sets of tests, the fatigue crack propagation rate of the alloy obtained in Comparative Example 2 is higher, while the crack propagation rate of the alloy obtained in Example 1 is lower. This indicates that applying a pulsed magnetic field during the cooling step of alloy heat treatment in this application can improve the service performance of the alloy.

[0085] In the description of this specification, the references to terms such as "one embodiment," "some embodiments," "example," "specific example," "some implementations," or "some examples," etc., indicate that a specific feature, structure, material, or characteristic described in connection with that embodiment or example is included in at least one embodiment or example of the present invention. In this specification, the illustrative expressions of the above terms do not necessarily refer to the same embodiment or example. Furthermore, the specific features, structures, materials, or characteristics described may be combined in any suitable manner in one or more embodiments or examples. Moreover, without contradiction, those skilled in the art can combine and integrate the different embodiments or examples described in this specification, as well as the features of different embodiments or examples.

[0086] Although embodiments of the present invention have been shown and described above, it is understood that the above embodiments are exemplary and should not be construed as limiting the present invention. Those skilled in the art can make changes, modifications, substitutions and variations to the above embodiments within the scope of the present invention.

Claims

1. A method for preparing an alloy, characterized in that, include: The alloy was heat-treated, and a pulsed magnetic field was applied during the cooling step of the heat treatment to obtain the alloy. The pulsed magnetic field is applied t minutes after the cooling begins, where t ≤ 5; The alloy includes at least one of titanium alloy and aluminum alloy; The pulsed magnetic field is applied for 2-5 minutes. The pulse width of the pulsed magnetic field is 0.5s-10s; The pulse period of the pulsed magnetic field is 2s-11s; The intensity of the pulsed magnetic field is 0.6T-3T.

2. The method for preparing the alloy according to claim 1, characterized in that, The intensity of the pulsed magnetic field is 1T-2T.

3. The method for preparing the alloy according to claim 1, characterized in that, The pulsed magnetic field is applied for 3-4 minutes.

4. The method for preparing the alloy according to any one of claims 1-2, characterized in that, The cooling includes air cooling.

5. The method for preparing the alloy according to claim 4, characterized in that, The air cooling rate is 0.1℃ / s-2℃ / s.

6. The method for preparing the alloy according to any one of claims 1-2, characterized in that, The heat treatment includes solution treatment, water quenching, and aging.

7. The method for preparing the alloy according to claim 6, characterized in that, The solution temperature is 705℃-775℃.

8. The method for preparing the alloy according to claim 6, characterized in that, The solution treatment time is 60 min to 120 min.

9. The method for preparing the alloy according to claim 6, characterized in that, The aging temperature is 480℃-620℃.

10. The method for preparing the alloy according to claim 6, characterized in that, The effective period is 8-10 hours.

11. An alloy, characterized in that, The alloy is prepared by the method described in any one of claims 1-10.

12. The alloy according to claim 11, characterized in that, The alloy includes at least one of titanium alloys and aluminum alloys.

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