A coherency nanophase enhanced feco-based high-temperature soft magnetic alloy and a preparation method thereof

Abstract

This invention discloses a coherent nanophase-reinforced FeCo-based high-temperature soft magnetic alloy and its preparation method, belonging to the technical field of high-temperature soft magnetic materials. The alloy composition is Fe. x Co y -(V) z )-Cu t (30≤x,y≤60,0≤z≤5,0<t<20), this alloy underwent casting, homogenization, hot forging, hot rolling, quenching, cold rolling, solution treatment, and aging treatment. The solution treatment was conducted at 1100–1400℃ for 4–12 h, and the aging treatment was conducted at 400–600℃ for 2–50 h. The final product was an alloy strip with a thickness of 0.1–0.3 mm. Coherent nanophases with a size of 25–45 nm precipitated in the matrix. During plastic deformation, the nanophases hindered dislocation movement, significantly improving the alloy's yield strength and tensile strength. The maximum yield strength was 600–800 MPa, and the tensile strength was 900–1100 MPa. Simultaneously, the alloy maintained excellent soft magnetic properties, with a saturation magnetization of 210–230 emu / g and a coercivity of 0.5–20 Oe. The alloy prepared by this invention meets the application requirements of high-performance soft magnetic materials in aerospace and other fields.

Description

Technical Field

[0001] This invention belongs to the field of special functional magnetic materials, and is a high-temperature soft magnetic alloy. More precisely, it relates to a coherent nanophase-reinforced FeCo-based high-temperature soft magnetic alloy and its preparation method. Background Technology

[0002] Soft magnetic materials are ferromagnetic materials with very low coercivity (Hc) and very high permeability (μ). They are characterized by narrow hysteresis loops, extremely high response to external magnetic fields, easy magnetization under external magnetic fields, and demagnetization after the external magnetic field is removed. Soft magnetic materials are used as core materials in relays, inductors, filters, and other devices, playing an important role in the energy sector, power transmission, and satellite communications.

[0003] In aerospace and other fields, there is a demand for high-temperature soft magnetic materials. For example, in multi-electric aircraft (MEAs) of aviation and aerospace, soft magnetic materials are used in integrated power units (IPUs), where the operating temperature has increased from the current 300℃ to 500-600℃, and high-speed rotors also withstand shear stresses of 500MPa-600MPa. In the main thrust engines of unmanned combat aerial vehicles (UCAVs), soft magnetic materials are used in the stators and rotors of the integrated starter and generator (IS / G), where the operating temperature reaches 400℃ and is subjected to stresses of 825MPa. In the gas turbine engines of spacecraft propulsion systems (SPS), soft magnetic materials are used to manufacture non-contact magnetic bearings, including rotating elements of thrust bearings and radial bearings, where the operating temperature reaches 550℃.

[0004] High-temperature soft magnetic materials require soft magnetic alloys to have high Curie temperatures (Tc > 700℃), as well as excellent magnetic properties (high saturation magnetization (Ms > 200 emu / g) and low coercivity (Hc < 20 Oe)) and mechanical properties (high yield strength (> 600 MPa) and high tensile strength (> 900 MPa)).

[0005] FeCo-based soft magnetic alloys have the highest Curie temperature (Tc≈980℃), the largest saturation magnetization (Ms≈240emu / g), and low coercivity (Hc<2Oe), making them the soft magnetic materials currently available for high-temperature applications.

[0006] The Fe50Co50 alloy and the commercially available FeCo alloy (1J22 alloy, whose main components are Fe49Co49-V2) have low yield strengths, at 100 MPa and 300 MPa, respectively. Their tensile strengths are also low, less than 100 MPa and less than 600 MPa, respectively. These do not meet the performance requirements of high-speed rotors in the aerospace field for high-temperature soft magnetic materials, necessitating the development of new alloy systems. Summary of the Invention

[0007] The technical problem solved by this invention is that the application of high-speed rotor materials for motors in aerospace vehicles is limited due to the constraints of their mechanical properties.

[0008] To address the above issues, this invention proposes a coherent nanophase-reinforced FeCo-based high-temperature soft magnetic alloy. Cu is added to the FeCo binary alloy and FeCo-V composite system, and a solution- and aging heat treatment process is added to the traditional strip preparation process, which significantly improves the mechanical properties of the alloy.

[0009] The present invention adopts the following technical solution:

[0010] A coherent nanophase-reinforced FeCo-based high-temperature soft magnetic alloy, wherein the alloy composition is Fe x Co y -(V z )-Cu t Where x, y, z, and t are molar percentage contents, 30≤x≤60, 30≤y≤60, 0≤z≤5, 0<t<20. For example, x can be 30, 32, 34, 36, 38, 40, 42, 44, 46, 47, 48, 50, 52, 54, 56, 58, or 60; y can be 30, 32, 34, 36, 38, 40, 42, 44, 46, 47, 48, 50, 52, 54, 56, 58, or 60; z can be 0, 1, 2, 3, 4, or 5; and t can be 1, 2, 3, 4, 5, 6, 7, 8, 9, 10, 11, 12, 13, 14, 15, 16, 17, 18, 19, or 20.

[0011] Furthermore, Cu-rich nanophases with a size of 25–50 nm are precipitated on the alloy matrix and are coherent with the matrix.

[0012] Further, the alloy has a maximum yield strength of 600–800 MPa and a tensile strength of 900–1100 MPa. For example, the alloy has a maximum yield strength of 600 MPa, 620 MPa, 640 MPa, 660 MPa, 680 MPa, 700 MPa, 720 MPa, 740 MPa, 760 MPa, 780 MPa, or 800 MPa, and a tensile strength of 900 MPa, 920 MPa, 940 MPa, 950 MPa, 970 MPa, 990 MPa, 1000 MPa, 1020 MPa, 1040 MPa, 1060 MPa, 1080 MPa, or 1100 MPa.

[0013] Furthermore, it possesses excellent magnetic properties, with saturation magnetization of 210 emu / g, 215 emu / g, 220 emu / g, 225 emu / g, or 230 emu / g, and coercivity of 0.5 Oe, 1 Oe, 2 Oe, 4 Oe, 6 Oe, 8 Oe, 10 Oe, 12 Oe, 14 Oe, 16 Oe, 18 Oe, or 20 Oe.

[0014] A method for preparing a coherent nanophase-reinforced FeCo-based high-temperature soft magnetic alloy as described above, the method comprising sequentially performing smelting, homogenization, hot forging, hot rolling, quenching, cold rolling, solution treatment, and aging; wherein the solution treatment is performed at 1100–1300℃ for 4–12 h; and the aging treatment is performed at 400–600℃ for 2–50 h.

[0015] Based on the above principles, the alloy preparation method of the present invention follows the steps below:

[0016] (1) Formulate ingredients according to the target ingredients.

[0017] The target component is Fe. x Co y -(V z )-Cu t Where 30≤x≤60, 30≤y≤60, 0≤z≤5, and 0<t<20. Preferably, the raw materials used in the formulation are elemental Fe, elemental Co, elemental V, and elemental Cu.

[0018] (2) Melt the prepared raw materials into master alloy ingots.

[0019] The ingredients obtained in step (1) are placed in a vacuum non-consumable arc melting furnace for melting to form a master alloy ingot with the target composition.

[0020] (3) Homogenization of master alloy ingots

[0021] The master alloy obtained in step (2) is subjected to homogenization heat treatment at a temperature of 1100 to 1350°C (e.g., 1100°C, 1130°C, 1150°C, 1170°C, 1200°C, 1220°C, 1240°C, 1250°C, 1270°C, 1300°C, 1330°C or 1350°C) for a holding time of 4 to 20 hours (e.g., 4 hours, 6 hours, 8 hours, 10 hours, 12 hours, 14 hours, 16 hours, 18 hours or 20 hours).

[0022] (4) Hot forging of the master alloy

[0023] The master alloy treated in step (3) is held at 1100–1300℃ (e.g., 1100℃, 1120℃, 1140℃, 1160℃, 1180℃, 1200℃, 1220℃, 1240℃, 1260℃, 1280℃ or 1300℃) for 0.5–3 hours, then removed and hot-forged at an initial forging temperature of 1100–1300℃ (e.g., 1100℃, 1120℃, 1140℃, 1160℃, 1180℃, 1200℃, 1220℃, 1240℃, 1260℃, 1280℃ or 1300℃). The forging temperature is 1120℃, 1140℃, 1160℃, 1180℃, 1200℃, 1220℃, 1240℃, 1260℃, 1280℃ or 1300℃, with a final forging temperature of 800~900℃ (e.g. 800℃, 810℃, 820℃, 830℃, 840℃, 850℃, 860℃, 870℃, 880℃, 890℃ or 900℃). Forging blanks with a thickness of 10~50mm (e.g. 10mm, 12mm, 15mm, 20mm, 25mm, 30mm, 35mm, 40mm, 45mm or 50mm) are obtained.

[0024] (5) Hot rolling of forged billets

[0025] The forging billet obtained in step (4) is held at 1100–1300℃ (e.g., 1100℃, 1120℃, 1140℃, 1160℃, 1180℃, 1200℃, 1220℃, 1240℃, 1260℃, 1280℃ or 1300℃) for 0.5–3 hours, then taken out and hot rolled. The initial rolling temperature is 1100–1300℃ (e.g., 1100℃, 1120℃, 1140℃, 1160℃). The rolling temperature is 1180℃, 1200℃, 1220℃, 1240℃, 1260℃, 1280℃ or 1300℃, with a final rolling temperature of 800~900℃ (e.g. 800℃, 810℃, 820℃, 830℃, 840℃, 850℃, 860℃, 870℃, 880℃, 890℃ or 900℃), with 8~15 rolling passes, an average reduction of 5~15% per pass, and a total reduction of 70~90%.

[0026] (6) Quenching of hot-rolled alloys

[0027] The hot-rolled alloy obtained in step (5) is subjected to disordered heat treatment at a temperature of 800–900℃ (e.g., 800℃, 810℃, 820℃, 830℃, 840℃, 850℃, 860℃, 870℃, 880℃, 890℃, or 900℃) for 0.5–2 hours. After treatment, it is then quenched.

[0028] (7) Obtaining strip by cold rolling

[0029] The alloy quenched in step (6) is cold rolled in 10 to 50 passes, with an average reduction of 2 to 10% per pass and a total reduction of 70 to 95%, to obtain an alloy strip with a thickness of 0.1 to 0.3 mm.

[0030] (8) Solution treatment of rolled strip

[0031] The cold-rolled strip obtained in step (7) is subjected to solution treatment at a temperature of 1100 to 1300°C (e.g., 1100°C, 1120°C, 1140°C, 1160°C, 1180°C, 1200°C, 1220°C, 1240°C, 1260°C, 1280°C or 1300°C) for a holding time of 4 to 12 hours.

[0032] (9) Aging treatment of rolled strip

[0033] The alloy strip after solution treatment in step (8) is subjected to aging treatment at a temperature of 400-600℃ (e.g., 400℃, 410℃, 420℃, 430℃, 440℃, 450℃, 460℃, 470℃, 480℃, 490℃, 500℃, 510℃, 520℃, 530℃, 540℃, 550℃, 560℃, 570℃, 580℃, 590℃ or 600℃) for a holding time of 2-50h.

[0034] Preferably, the purity of the raw materials is greater than 99.99%, and the raw materials need to have their surface oxide scale removed and undergo ultrasonic treatment with anhydrous ethanol.

[0035] The advantages of this invention are:

[0036] (1) The yield strength and tensile strength of FeCo-based soft magnetic alloys are greatly improved, and they also have excellent magnetic properties.

[0037] (2) In addition to the traditional method of strip preparation, a solution aging process is introduced to artificially control the properties of the alloy.

[0038] The principle of this invention is based on the low solid solubility of Cu in FeCo and FeCo-V alloys (<2%). Adding Cu beyond this solubility will cause the precipitation of a nanoscale second phase. During plastic deformation, this phase hinders dislocation movement, increases dislocation slip resistance, and effectively improves the alloy's yield strength and tensile strength. Simultaneously, the nanoscale phase exhibits low domain wall pinning resistance and minimal coercivity change, maintaining excellent magnetic properties. Attached Figure Description

[0039] Figure 1 The Fe prepared in Example 1 of this invention 47 Co 47 Microstructure of V2-Cu4 high-performance soft magnetic alloy.

[0040] Figure 2 The Fe prepared in Example 1 of this invention 47 Co 47 High-resolution image of V2-Cu4 high-performance soft magnetic alloy.

[0041] Figure 3 The Fe prepared in Example 1 of this invention 47 Co 47 Hysteresis loop diagram of V2-Cu4 high-performance soft magnetic alloy; (a) Hysteresis loop diagram; (b) Enlarged view showing the intersection with the x-axis.

[0042] Figure 4 The Fe prepared in Example 1 of this invention 47 Co 47 -V2-Cu4 high-performance soft magnetic alloy tensile curve.

[0043] Figure 5 The Fe prepared in Comparative Example 1 of this invention 49 Co 49 -V2 alloy (abbreviated as FeCo-V alloy) and Fe 47 Co 47 Microstructure of FeCo-V-Cu4 alloy (abbreviated as FeCo-V-Cu alloy); (a) Microstructure of FeCo-V alloy; (b) Microstructure of FeCo-V-Cu alloy.

[0044] Figure 6 The Fe prepared in Comparative Example 1 of this invention 49 Co 49 -V2 alloy and Fe prepared in Example 1 47 Co 47 Hysteresis loop diagram of FeCo-V alloy; (a) Hysteresis loop diagram of FeCo-V alloy; (b) Enlarged view of Figure (a); (c) Hysteresis loop diagram of FeCo-V-Cu alloy; (d) Enlarged view of Figure (c);

[0045] Figure 7 The Fe prepared in Comparative Example 1 of this invention 49 Co 49 -V2 alloy and Fe prepared in Example 1 47 Co 47 Tensile curves of FeCo-V alloy; (a) Tensile curve of FeCo-V alloy; (b) Tensile curve of FeCo-V-Cu alloy. Detailed Implementation

[0046] The present invention will now be described in detail with reference to the accompanying drawings and specific embodiments. However, the following examples are only for illustrating the present invention, and the scope of protection of the present invention should include the entire contents of the claims, not just the embodiments described herein.

[0047] Example 1

[0048] The steps used in this embodiment are as follows:

[0049] 1. Ingredients

[0050] The selected raw materials are elemental Fe, Co, V, and Cu, all with a purity of 99.99 wt%. Before mixing, the oxide scale on the surfaces of Fe and Co is removed by grinding with a grinding wheel; the oxide scale on the surface of V is removed by soaking in 20 wt% hydrochloric acid; and Fe, Co, V, and Cu are all ultrasonically cleaned with anhydrous ethanol and dried in a vacuum to remove surface oil. Fe is then weighed. 47 Co 47 Prepare the raw materials in the -V2-Cu4 ratio for later use.

[0051] 2. Preparation of master alloy ingots

[0052] The weighed ingredients are placed in a vacuum non-consumable arc melting furnace for melting to form a master alloy ingot with the target composition.

[0053] The vacuum non-consumable arc melting furnace was evacuated to 5×10 -3 Then, high-purity argon gas is introduced into the furnace until the vacuum level inside the furnace reaches 1×10⁻⁶. -1 After stopping the inflation, repeat this step three times. Then, the raw materials prepared in step (1) are smelted. The first smelting current is 220A, the smelting time is 5 minutes, and the electrode head rotates 30 times. The ingot is turned over with a small shovel for smelting. The second smelting current is 240A, the smelting time is 5 minutes, and the electrode head rotates 30 times. The ingot is turned over with a small shovel for smelting. The third smelting current is 260A, the smelting time is 7 minutes, and the electrode head rotates 50 times. The ingot is turned over with a small shovel for smelting. The fourth smelting current is 280A, the smelting time is 7 minutes, and the electrode head rotates 50 times. Finally, the master alloy ingot is obtained.

[0054] 3. Homogenization treatment

[0055] The ingot obtained in step (2) is sealed with a quartz tube, and the tube is evacuated and filled with argon gas. The alloy is then placed in a muffle furnace for homogenization.

[0056] The homogenization temperature was 1300℃, and the treatment time was 12 hours. After the treatment, the furnace was air-cooled.

[0057] 4. Hot forging

[0058] The master alloy processed in step (3) is kept at 1300℃ for 1 hour, and then taken out and hot forged.

[0059] The initial forging temperature is 1300℃, and the final forging temperature is 900℃. A forging billet with a thickness of 50mm is obtained.

[0060] The forged billet is a cuboid with certain thickness requirements, and its width and length depend on the quality of the master alloy.

[0061] 5. Hot rolling of forged billets

[0062] The forged billet obtained in step (4) is placed in a vacuum tube furnace for heat preservation at a temperature of 1300℃ for 2 hours, and then taken out for hot rolling.

[0063] The initial rolling temperature is 1300℃, the final rolling temperature is 900℃, the rolling passes are 15, the average reduction per pass is 6%, and the total reduction is 90%.

[0064] The thickness of the hot-rolled strip is 5mm.

[0065] 6. Quenching of hot-rolled alloys

[0066] The hot-rolled alloy obtained in step (5) is subjected to disordered heat treatment at a temperature of 900℃ for 1 hour.

[0067] After heat treatment, the product undergoes brine quenching with continuous stirring to accelerate the cooling process.

[0068] 7. Remove oxide scale from the surface

[0069] The alloy sample obtained in step (6) was polished with a hand-held grinder to remove the surface oxide scale. It was then rinsed with 20wt% hydrochloric acid to further remove the oxide scale.

[0070] 8. Cold rolling

[0071] Cold rolling is divided into three steps: rough rolling, grinding, and finish rolling.

[0072] In the rough rolling process, the alloy is placed in the rolling mill and rolled in 20 passes, with an average reduction of 4% per pass and a total reduction of 80%.

[0073] After rough rolling, an alloy strip with a thickness of 1 mm is obtained.

[0074] After rough rolling, the oxide scale on the surface of the sample is removed using a hand-held grinder.

[0075] The alloy is polished to a high shine and then subjected to finish rolling. The alloy is placed in a rolling mill and rolled in 25 passes, with an average reduction of 2.8% per pass and a total reduction of 70%.

[0076] The strip thickness obtained after finishing rolling is 0.3 mm.

[0077] 9. Solution treatment of rolled strip

[0078] The cold-rolled strip obtained in step (8) is placed in a muffle furnace for solution treatment at a temperature of 1300℃ and a holding time of 8h.

[0079] After solution treatment, quench with brine.

[0080] 10. Aging treatment of rolled strip

[0081] The solution-treated alloy strip is placed in a vacuum tube furnace for aging treatment at a temperature of 600℃ for 2 hours.

[0082] After the aging period is over, quench with salt water.

[0083] Upon testing, the transmitted bright-field image of the alloy was as follows: Figure 1 As shown, it exhibits precipitated phases with sizes ranging from 25 to 45 nm; high-resolution images are shown below. Figure 2 As shown, the nanoscale matrix is ​​coherent;

[0084] The sample hysteresis loop was measured using a vibrating sample magnetometer. The sample was a small circular disc with a diameter of 3 mm and a thickness of 0.3 mm. The test conditions were ±20000 Oe and a sweep speed of 2 Oe / s. The hysteresis loop is shown below. Figure 3 As shown, the saturation magnetization is 221.3 emu / g and the coercivity is 9.4 Oe, indicating excellent magnetic properties.

[0085] The tensile curves of the specimens were tested using a 5966 tensile testing machine. The specimen specifications were based on the national standard GB / T 228.1-2010 "Metallic materials, tensile testing—Part 1: Tests at room temperature," page 6, with the specimens scaled down proportionally. The tensile curves are shown below. Figure 4 As shown, the yield strength is 676 MPa and the tensile strength is 989 MPa. Fe 47 Co 47 -V2-Cu4 exhibits excellent mechanical properties.

[0086] Example 2

[0087] The alloy composition is: Fe 48 Co 48 -V 1- Cu3.

[0088] 1. Batching and preparation of master alloy

[0089] This step is the same as steps (1) and (2) in Example 1.

[0090] 2. Homogenization treatment

[0091] Fe 48 Co 48 -V 1-Cu3 alloy ingots are placed in a VMI-200D vertical double-chamber vacuum heat treatment furnace, and vacuum is applied for homogenization.

[0092] The homogenization temperature was 1200℃, and the treatment time was 16 hours. After the treatment, the furnace was air-cooled.

[0093] 3. Hot forging

[0094] The master alloy processed in step (2) is kept at 1250℃ for 0.5h, and then hot-forged.

[0095] The initial forging temperature was 1250℃, and the final forging temperature was 850℃. A forging billet with a thickness of 40mm was obtained.

[0096] 4. Hot rolling of forged billets

[0097] This step is the same as step (5) in Example 1.

[0098] The thickness of the hot-rolled strip is 4mm.

[0099] 5. Quenching of hot-rolled alloys

[0100] The hot-rolled alloy obtained in step (5) was subjected to disordered heat treatment at a temperature of 880°C for 0.5 hours.

[0101] After heat treatment, the product undergoes brine quenching with continuous stirring to accelerate the cooling process.

[0102] 6. Remove oxide scale from the surface

[0103] This step is the same as step (7) in Example 1.

[0104] 7. Cold rolling

[0105] In the rough rolling process, the alloy is placed in the rolling mill and rolled in 15 passes, with an average reduction of 5% per pass and a total reduction of 75%.

[0106] After rough rolling, an alloy strip with a thickness of 1 mm is obtained.

[0107] After rough rolling, the oxide scale on the surface of the sample is removed using a hand-held grinder.

[0108] The alloy is polished to a high shine and then subjected to finish rolling. The alloy is placed in a rolling mill and rolled in 23 passes, with an average reduction of 3.5% per pass and a total reduction of 80%.

[0109] The strip thickness obtained after finishing rolling is 0.2 mm.

[0110] 8. Solution treatment of rolled strip

[0111] The cold-rolled strip obtained in step (7) is placed in a vacuum tube furnace for solution treatment at a temperature of 1200℃ and a holding time of 6h.

[0112] After solution treatment, quench with brine.

[0113] 9. Aging treatment of rolled strip

[0114] The solution-treated alloy strip is placed in a vacuum tube furnace for aging treatment at a temperature of 500℃ for 1 hour.

[0115] After the aging period is over, quench with salt water.

[0116] Tests showed that Fe 48 Co 48 -V 1- Cu3 alloy has precipitates with a size of about 30 nm, which are coherent with the matrix.

[0117] The sample hysteresis loop was tested using a vibrating sample magnetometer. The sample was a small circular disc with a diameter of 3 mm and a thickness of 0.2 mm. The test conditions were ±20000 Oe and a sweep speed of 2 Oe / s. The saturation magnetization was 224 emu / g and the coercivity was 8.3 Oe, indicating excellent magnetic properties.

[0118] The tensile curves of the specimens were tested using a 5966 tensile testing machine. The specimen specifications were proportionally scaled down from the national standard GB / T 228.1-2010 "Metallic materials, tensile testing—Part 1: Tests at room temperature" (P6). The yield strength was 680 MPa, and the tensile strength was 900 MPa. The mechanical properties were excellent.

[0119] Comparative Example 1

[0120] Alloy composition: Fe 49 Co 49 -V2 alloy

[0121] Preparation process.

[0122] The preparation process is the same as in Example 1. A 0.3 mm thick alloy strip is obtained.

[0123] Solution treatment and aging treatment of rolled strip

[0124] The solution aging process is the same as in Example 1.

[0125] Under a transmission electron microscope, such as Figure 5 As shown, Fe 49 Co 49 -V2 alloy is a single phase with no precipitated phases. In contrast, the Fe alloy prepared in Example 1... 47 Co 47 -V2-Cu4 alloy has obvious precipitates with a size of about 30 nm.

[0126] The magnetic testing conditions for the alloy were the same as in Example 1. Figure 6 As shown, in Comparative Example 1, Fe 49 Co 49 The saturation magnetization of the -V2 alloy is 224.3 emu / g; the coercivity is 1.5 Oe. Example 1: After adding Cu, the prepared Fe... 47 Co 47 The saturation magnetization of the -V2-Cu4 alloy decreased slightly from 224.3 emu / g to 221.3 emu / g; the coercivity increased slightly from 1.5 Oe to 9.4 Oe. The overall magnetism decreased slightly, but it still maintained excellent soft magnetic properties.

[0127] The tensile testing conditions for the alloy are the same as in Example 1, such as... Figure 7 As shown, in Comparative Example 1, Fe 49 Co 49 The yield strength of the -V2 alloy is 313 MPa, and the tensile strength is 538 MPa. In Example 1, after adding Cu, the yield strength of the alloy increased from 313 MPa to 676 MPa, and the tensile strength increased from 538 MPa to 989 MPa, resulting in a significant improvement in mechanical properties.

[0128] The Fe provided by this invention x Co y -(V z )-Cu t After adding Cu, the alloy was obtained as a high-temperature soft magnetic alloy with good comprehensive properties such as saturation magnetization, coercivity, yield strength and tensile strength, providing a good alternative material for motor materials in the aerospace field.

[0129] It should be noted that the above embodiments of the present invention are only used to illustrate the technical solutions of the present invention and not to limit them. Those skilled in the art can obviously modify the technical solutions of the present invention and apply the technical principles of the present invention to other examples without creative effort. Therefore, the present invention is not limited to the above examples, and any modifications or equivalent substitutions made without departing from the scope of the present invention should be within the protection scope of the present invention.

Claims

1. A coherent nanophase-reinforced FeCo-based high-temperature soft magnetic alloy, characterized in that, The alloy composition is Fe x Co y -(V z )-Cu t Where x, y, z, and t represent the molar percentage content, 30 ≤ x ≤ 60, 30 ≤ y ≤ 60, 0 ≤ z ≤ 5, 0 <t<20; Cu-rich nanophases with sizes below 100 nm precipitate on the alloy matrix and are coherent with the matrix. Taking advantage of the fact that the solid solubility of Cu in FeCo and FeCo-V alloys is less than 2%, the addition of Cu will precipitate a nanoscale second phase when the solid solubility is exceeded. During plastic deformation, this phase hinders dislocation movement, increases dislocation slip resistance, and improves the yield strength and tensile strength of the alloy. At the same time, the nanophases have low resistance to domain wall pinning and small changes in coercivity, thus maintaining excellent magnetic properties. The soft magnetic alloy has a yield strength of 600~800MPa and a tensile strength of 900~1100MPa; the soft magnetic alloy has a saturation magnetization of 210~230 emu / g and a coercivity of 0.5~20Oe; the preparation method of the coherent nanophase-reinforced FeCo-based high-temperature soft magnetic alloy includes smelting, homogenization, hot forging, hot rolling, quenching, cold rolling, solution treatment, and aging in sequence; wherein the solution treatment is performed at 1100~1300℃ for 4~12h; and the aging treatment is performed at 400~600℃ for 2~50h.

2. A method for preparing a coherent nanophase-reinforced FeCo-based high-temperature soft magnetic alloy as described in claim 1, characterized in that, The method includes sequential smelting, homogenization, hot forging, hot rolling, quenching, cold rolling, solution treatment, and aging; wherein the solution treatment is performed at 1100~1300℃ for 4~12h; and the aging treatment is performed at 400~600℃ for 2~50h.

3. The method according to claim 2, characterized in that, The specific steps include the following: (1) Formulate ingredients according to the target ingredients. The target component is Fe. x Co y -(V z )-Cu t Where 30≤x≤60, 30≤y≤60, 0≤z≤5, 0 <t<20; (2) Melt the prepared raw materials into master alloy ingots. The ingredients obtained in step (1) are placed in the furnace of a vacuum non-consumable arc melting furnace for melting to form a master alloy ingot with the target composition. (3) Homogenization of master alloy ingot The master alloy obtained in step (2) is subjected to homogenization heat treatment at a temperature of 1100~1350℃ and a holding time of 4~20 hours. (4) Hot forging of the master alloy The master alloy processed in step (3) is held at 1100~1300℃ for 0.5~3h, taken out and hot forged. The initial forging temperature is 1100~1300℃ and the final forging temperature is 800~900℃; a forging billet with a thickness of 10~50mm is obtained. (5) Hot rolling of forged billets The forging billet obtained in step (4) is kept at 1100~1300℃ for 0.5~3h, then taken out for hot rolling. The initial rolling temperature is 1100~1300℃, the final rolling temperature is 800~900℃, the number of rolling passes is 8~20, the average reduction per pass is 5~15%, and the total reduction is 70~90%. (6) Quenching of hot-rolled alloys The hot-rolled alloy obtained in step (5) is subjected to disordered heat treatment at a temperature of 800~900℃ for 0.5~2h; and then quenched. (7) Obtaining strip by cold rolling The alloy quenched in step (6) is cold rolled in 10 to 50 passes, with an average reduction of 2 to 10% per pass and a total reduction of 70 to 95%, to obtain an alloy strip with a thickness of 0.1 to 0.3 mm. (8) Solution treatment of rolled strip The cold-rolled strip obtained in step (7) is subjected to solution treatment at a temperature of 1100~1300℃ and a holding time of 4~12h. (9) Aging treatment of rolled strip The alloy strip after solution treatment in step (8) is subjected to aging treatment at an aging temperature of 400~600℃ and a holding time of 2~50h.

4. The method according to claim 3, characterized in that, In step (1), the purity of the raw materials is greater than 99.99%. The raw materials need to have their surface oxide scale removed and undergo ultrasonic treatment with anhydrous ethanol.

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