A multi-component alloy having high mechanical and soft magnetic properties and a method of making the same

Abstract

The application discloses a multi-component alloy with high mechanical properties and soft magnetic properties and a preparation method thereof. The alloy matrix is an FCC or BCC solid solution structure, a small amount of intermetallic compound is introduced after alloying of Gd and Al, the alloy is composed of Fe, Co, Ni, Gd and Al elements, and according to atomic percentage, Fe is 38-50%, Co is 28-50%, Ni is 5-30%, Gd is 0-0.05%, and Al is 0-5%. The application combines Fe, Co and Ni in a suitable ratio as an alloy matrix, introduces Gd, Al and other elements in the matrix alloy, and obtains a uniform and grain size moderate structure by using a proper heat treatment process and plastic processing system. Therefore, excellent plasticity and mechanical strength are obtained while high saturation magnetization and low coercivity are ensured, and the alloy can be applied to the fields of electric power industry and electronic equipment as a soft magnetic material.

Description

Technical Field

[0001] This invention belongs to the field of soft magnetic material preparation technology, specifically involving multi-component soft magnetic alloys with high plasticity, high saturation magnetization and low coercivity, and their preparation methods. Background Technology

[0002] Soft magnetic materials are materials that can rapidly respond to changes in an applied magnetic field and achieve high magnetic flux density with low loss. Soft magnetic materials possess characteristics such as low coercivity, high permeability, and high saturation magnetization. They are easily magnetized and demagnetized under the influence of an external magnetic field, and are widely used in the power industry and electronic equipment to improve efficiency and reduce losses. However, soft magnetic materials typically need to withstand mechanical loads during use, thus requiring a certain level of strength. Simultaneously, good plasticity in soft magnetic materials can reduce the possibility of defects such as cracks during complex processing, leading to material scrap and improving yield. This also further enhances the reliability and performance of equipment during use. Currently, various methods exist for strengthening and toughening soft magnetic materials, but all of them compromise their soft magnetic properties to varying degrees. For example, doping with non-magnetic elements reduces saturation magnetization, and increasing coercivity at the phase interface. In the global market, the vast application scale of soft magnetic materials means that even a small reduction in magnetic properties can result in significant resource waste. Therefore, the reduction in soft magnetic properties caused by the toughening of materials will greatly hinder the wider application of soft magnetic materials. Reducing the loss of magnetic properties during the toughening process of soft magnetic materials is particularly important in the design of new soft magnetic alloys.

[0003] The complex chemical composition of multi-principal element high-entropy alloys provides a broader space for microstructure control and greater potential for performance optimization, offering new ideas for the development of alloys that combine soft magnetic and mechanical properties. From equiatomic to unequal atomic ratios, multi-principal element alloy designs allow for greater flexibility in alloy design by adjusting the composition and proportion of different elements to alter the material's structural properties and functionality. Recent research reports a novel FeCoNiTaAl-based soft magnetic high-entropy alloy and proposes several strengthening and toughening methods, such as Fe... 32.6 Co 27.7 Ni 27.7 Ta 5.0 Al 7.0 (at.%), its tensile strength can reach 1336 MPa and its elongation can reach 54% [Han, et al. Nature, 2022.]; Fe 35 Co 30 Ni 30The Ta5 (at.%) alloy exhibits a tensile strength of up to 1.93 GPa and an elongation of 12.6% [Han, et al. Nature Communications, 2024]. However, the saturation magnetization of both of these high-strength, high-toughness soft magnetic high-entropy alloys is relatively low, both below 120 Am. 2 / kg (~1.3T), which is difficult to meet the soft magnetic properties requirements of materials in practical applications.

[0004] In summary, although soft magnetic high-entropy alloys can possess excellent mechanical properties, this often comes at the cost of sacrificing some saturation magnetization. The problem of balancing excellent soft magnetic properties with mechanical properties urgently requires new solutions. Summary of the Invention

[0005] The purpose of this section is to outline some aspects of embodiments of the present invention and to briefly describe some preferred embodiments. Simplifications or omissions may be made in this section, as well as in the abstract and title of this application, to avoid obscuring the purpose of these documents; however, such simplifications or omissions should not be construed as limiting the scope of the invention.

[0006] In view of the problems existing in the above and / or prior art, the present invention is proposed.

[0007] One objective of this invention is to provide a multi-component alloy with excellent mechanical and soft magnetic properties. This is achieved by combining Fe, Co, and Ni in appropriate proportions as the alloy matrix, introducing elements such as Gd and Al into the matrix alloy, and using appropriate heat treatment processes and plastic processing regimes to obtain a uniform microstructure with moderate grain size. This ensures high saturation magnetization and low coercivity while achieving excellent plasticity and mechanical strength.

[0008] To solve the above-mentioned technical problems, the present invention provides the following technical solution: a multi-component soft magnetic alloy with high plasticity, high saturation magnetization and low coercivity, wherein the alloy matrix is ​​an FCC or BCC solid solution structure, and a small amount of intermetallic compounds are introduced after Gd and Al alloying, and the alloy is composed of Fe, Co, Ni, Gd and Al elements;

[0009] By atomic percentage, Fe is 38–50%, Co is 28–50%, Ni is 5–30%, Gd is 0–0.05%, and Al is 0–5%.

[0010] The total atomic percentage of Fe, Co, and Ni is ≤100% and ≥94%; the atomic ratio of Fe and Co is >1 and ≤1.35; the total atomic percentage of Gd and Al dopants is ≥0% and ≤5%; and the total atomic percentage of each component is 100%.

[0011] As a preferred embodiment of the multi-component soft magnetic alloy with high plasticity, high saturation magnetization and low coercivity of the present invention, wherein the atomic percentage of Ni is 5-8% or 25-30%.

[0012] This invention utilizes a multi-component alloy design approach, employing Fe, Co, Ni, Gd, and Al alloy raw materials to obtain a multi-component alloy that combines high plasticity, high saturation magnetization, and low coercivity.

[0013] Fe is an important strengthening element, improving the strength and machinability of alloys, and as a transition metal, it can enhance the magnetism of alloys. The addition of Co and Ni can produce strong ferromagnetic coupling with Fe, resulting in higher saturation magnetization and increasing the Curie temperature; both Co and Ni are infinitely soluble in Fe. Specifically, Co enhances solid solution strengthening of the alloy, while Ni stabilizes the face-centered cubic configuration and improves its ductility. To fully utilize the coupling effect and magnetic moment contribution between Fe and Co atoms, this invention requires that the atomic percentages of Fe and Co not exceed 1.35%.

[0014] The doping of large amounts of non-magnetic metals may lead to magnetic dilution, thereby reducing the performance of soft magnetic materials. Gd, as a rare earth element exhibiting ferromagnetism at room temperature, has the potential to improve the saturation magnetization of FeCoNi matrix alloys; however, due to its large atomic radius and low solid solubility in the matrix, its content is controlled below 0.1%. Additionally, Al may interact with other elements possessing various magnetic configurations, thereby altering its magnetic moment distribution and enhancing saturation magnetization; however, since Al is a stable BCC phase element, its content is controlled below 10%.

[0015] This invention demonstrates that applying different heat treatment methods to FeCoNi multi-component matrix alloys with appropriate atomic ratios can effectively improve the saturation magnetization and reduce the coercivity of soft magnetic alloys. Furthermore, by introducing Gd and Al elements, it was found that within a specific range of Al content, the alloy exhibits significantly lower coercivity while maintaining high plasticity.

[0016] As a preferred embodiment of the multi-component soft magnetic alloy of the present invention, which exhibits high plasticity, high saturation magnetization, and low coercivity, it has the following characteristics:

[0017] (a) The saturation magnetization at room temperature is 1.5–2.1 T;

[0018] (b) Coercivity is 30–650 A / m;

[0019] (c) Under quasi-static tensile conditions at room temperature, the tensile elongation is greater than 50%;

[0020] (d) The tensile yield strength at room temperature is 210–400 MPa, and the tensile strength is 430–600 MPa;

[0021] (e) The initial permeability is 0.29–3.45 mH / m.

[0022] Another object of the present invention is to provide a method for preparing a multi-component soft magnetic alloy with high plasticity, high saturation magnetization and low coercivity as described above, comprising: taking each component according to the atomic percentage of the alloy, melting under inert gas protection or vacuum conditions, casting to obtain an alloy billet, and obtaining the alloy after thermomechanical processing of the billet.

[0023] As a preferred embodiment of the method for preparing the multi-component alloy with excellent mechanical properties and soft magnetic properties according to the present invention, wherein: the melting under inert gas protection conditions requires multiple gas purging of the furnace cavity, followed by filling with inert gas and maintaining the gas pressure at 0.000001 to 0.05 MPa.

[0024] As a preferred embodiment of the method for preparing multi-component alloys with excellent mechanical properties and soft magnetic properties according to the present invention, the thermomechanical processing includes hot rolling, homogenization, cold rolling and annealing.

[0025] As a preferred embodiment of the method for preparing a multi-component alloy with excellent mechanical properties and soft magnetic properties according to the present invention, wherein: the hot rolling temperature is 1173-1523K and the reduction is 30%-80%.

[0026] As a preferred embodiment of the method for preparing a multi-component alloy with excellent mechanical properties and soft magnetic properties according to the present invention, the homogenization process involves a heat treatment temperature higher than or equal to the hot rolling temperature, and a holding time of 5 to 300 min.

[0027] As a preferred embodiment of the method for preparing a multi-component alloy with excellent mechanical and soft magnetic properties according to the present invention, wherein the cold rolling has a reduction of 30-80%.

[0028] As a preferred embodiment of the preparation method of the multi-component alloy with excellent mechanical properties and soft magnetic properties of the present invention, the annealing treatment is carried out at a temperature of 1123-1323K and a holding time of 10-300min; the cooling method is air cooling, furnace cooling, or furnace cooling to a certain temperature followed by air cooling.

[0029] Compared with the prior art, the present invention has the following beneficial effects:

[0030] This invention proposes a multi-component soft magnetic alloy with a suitable atomic ratio of Fe, Co, Ni, Gd, and Al. This alloy series has a high content of ferromagnetic elements. By combining the multi-component alloy design concept with appropriate heat treatment and plastic processing techniques, the soft magnetic alloy can improve its plasticity while maintaining high saturation magnetization and low coercivity, which has great practical significance and value. Attached Figure Description

[0031] To more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings used in the following description of the embodiments will be briefly introduced. Obviously, the drawings described below are only some embodiments of the present invention. For those skilled in the art, other drawings can be obtained based on these drawings without creative effort. Wherein:

[0032] Figure 1 This is the XRD pattern of the alloy material in Example 1 of the present invention.

[0033] Figure 2 This is a hysteresis loop diagram of the alloy material in Embodiment 1 of the present invention.

[0034] Figure 3 This is a room temperature tensile stress-strain curve of the alloy material in Example 3 of the present invention.

[0035] Figure 4 This is the XRD pattern of the alloy material in Example 2 of the present invention.

[0036] Figure 5 This is the hysteresis loop diagram of the alloy material in Embodiment 2 of the present invention.

[0037] Figure 6 This is the XRD pattern of the alloy material in Example 3 of the present invention.

[0038] Figure 7 This is the hysteresis loop diagram of the alloy material in Embodiment 3 of the present invention.

[0039] Figure 8 This is the XRD pattern of the alloy material in Example 4 of the present invention.

[0040] Figure 9 These are scanning electron microscope (SEM) images and energy dispersive spectroscopy (EDS) distribution diagrams of the alloy material in Example 4 of this invention.

[0041] Figure 10 This is an EBSD scan of the alloy material in Example 4 of the present invention.

[0042] Figure 11 This is the hysteresis loop diagram of the alloy material in Embodiment 4 of the present invention.

[0043] Figure 12This is the room temperature tensile stress-strain curve of the alloy material in Example 4 of the present invention.

[0044] Figure 13 This is the XRD pattern of the alloy material in Example 5 of the present invention.

[0045] Figure 14 These are scanning electron microscope (SEM) images and energy dispersive spectroscopy (EDS) distribution diagrams of the alloy material in Example 5 of this invention.

[0046] Figure 15 This is an EBSD scan of the alloy material in Example 5 of the present invention.

[0047] Figure 16 This is the hysteresis loop diagram of the alloy material in Embodiment 5 of the present invention.

[0048] Figure 17 This is the room temperature tensile stress-strain curve of the alloy material in Embodiment 5 of the present invention.

[0049] Figure 18 This is the XRD pattern of the alloy material in Example 6 of the present invention.

[0050] Figure 19 This is an EBSD scan of the alloy material in Example 6 of the present invention.

[0051] Figure 20 This is the hysteresis loop diagram of the alloy material in Embodiment 6 of the present invention.

[0052] Figure 21 This is a room temperature tensile stress-strain curve of the alloy material in Embodiment 6 of the present invention.

[0053] Figure 22 This is the XRD pattern of the alloy material in Comparative Example 1 of this invention.

[0054] Figure 23 This is the hysteresis loop diagram of the alloy material in Comparative Example 1 of this invention.

[0055] Figure 24 This is the XRD pattern of the alloy material in Comparative Example 2 of this invention.

[0056] Figure 25 This is an EBSD scan of the alloy material in Comparative Example 2 of this invention.

[0057] Figure 26 This is the hysteresis loop diagram of the alloy material in Comparative Example 2 of this invention.

[0058] Figure 27 This is a room temperature tensile stress-strain curve of the alloy material in Comparative Example 2 of this invention.

[0059] Figure 28These are scanning electron microscope (SEM) images and energy dispersive spectroscopy (EDS) distribution diagrams of the alloy material in Comparative Example 3 of this invention.

[0060] Figure 29 This is the hysteresis loop diagram of the alloy material in Comparative Example 4 of this invention. Detailed Implementation

[0061] To make the above-mentioned objects, features and advantages of the present invention more apparent and understandable, the specific embodiments of the present invention will be described in detail below with reference to the examples in the specification.

[0062] Many specific details are set forth in the following description in order to provide a full understanding of the invention. However, the invention may also be practiced in other ways different from those described herein, and those skilled in the art can make similar extensions without departing from the spirit of the invention. Therefore, the invention is not limited to the specific embodiments disclosed below.

[0063] Secondly, the term "one embodiment" or "embodiment" as used herein refers to a specific feature, structure, or characteristic that may be included in at least one implementation of the present invention. The phrase "in one embodiment" appearing in different places in this specification does not necessarily refer to the same embodiment, nor is it a single or selective embodiment that is mutually exclusive with other embodiments.

[0064] Unless otherwise specified, all raw materials used in the examples are commercially available.

[0065] Example 1

[0066] According to the chemical formula Fe 40.0 Co 30.0 Ni 30.0 The ingredients are proportioned by atomic percentage, with Fe, Ni, and Co raw materials using their corresponding elemental particles. The gas pressure in the vacuum arc furnace is then evacuated to 5 × 10⁻⁶. -3 After Pa, inert argon gas is introduced, and each alloy sample is flipped over and repeatedly melted 6 times to obtain a casting billet.

[0067] The resulting billet was hot-rolled at 1455 K with a reduction of 50%. It was then homogenized at 1455 K for 15 min, followed by cold rolling with a reduction of 50%. Finally, it underwent recrystallization annealing at 1225 K for 30 min. All heat-treated samples were air-cooled, resulting in the alloy described in Example 1.

[0068] Depend on Figure 1 It can be seen that this embodiment is an FCC solid solution structure. Figure 2 The results show that the alloy has a saturation magnetization of 1.67 T, a coercivity of 43.74 A / m, an initial permeability of 2.71 mH / m, and a magnetic loss of 195.3 J / m^3 at room temperature. Figure 3This indicates that the alloy has an elongation of 62.6% and a tensile strength of 511 MPa at room temperature.

[0069] Example 2

[0070] According to the chemical formula Fe 49.0 Co 46.0 Ni 5.0 The ingredients are proportioned by atomic percentage, with Fe, Ni, and Co raw materials using their corresponding elemental particles. The gas pressure in the vacuum arc furnace is then evacuated to 5 × 10⁻⁶. -3 After Pa, inert argon gas is introduced, and each alloy sample is flipped over and repeatedly melted 6 times to obtain a casting billet.

[0071] The resulting billet was hot-rolled at 1225 K with a reduction of 50%. It was then homogenized at 1225 K for 20 min, followed by cold rolling with a reduction of 50%. Finally, it underwent recrystallization annealing at 1225 K for 15 min. All heat-treated samples were air-cooled, resulting in the alloy of Example 2.

[0072] Depend on Figure 4 It can be seen that this embodiment has a BCC solid solution structure. Figure 5 The results show that the saturation magnetization of the alloy at room temperature is 2.09T, the coercivity is 409.9A / m, the initial permeability is 0.44mH / m, and the magnetic loss is 2411J / m^3.

[0073] Example 3

[0074] According to the chemical formula Fe 47.0 Co 46.0 Ni 7.0 The ingredients are proportioned by atomic percentage, with Fe, Ni, and Co raw materials using their corresponding elemental particles. The gas pressure in the vacuum arc furnace is then evacuated to 5 × 10⁻⁶. -3 After Pa, inert argon gas is introduced, and each alloy sample is flipped over and repeatedly melted 6 times to obtain a casting billet.

[0075] The resulting billet was hot-rolled at 1225 K with a reduction of 50%. It was then homogenized at 1225 K for 20 min, followed by cold rolling with a reduction of 50%. Finally, it underwent recrystallization annealing at 1225 K for 15 min. All heat-treated samples were air-cooled, resulting in the alloy described in Example 3.

[0076] Depend on Figure 6 It can be seen that this embodiment has a BCC solid solution structure. Figure 7 The results show that the saturation magnetization of the alloy at room temperature is 1.97T, the coercivity is 649.9A / m, the initial permeability is 0.29mH / m, and the magnetic loss is 4199J / m^3.

[0077] Example 4

[0078] According to the chemical formula Fe 39.97 Co 29.99 Ni 29.99 Gd 0.05 The ingredients are proportioned according to atomic percentage, with Fe, Ni, Co, and Gd raw materials using their corresponding elemental particles. The gas pressure in the vacuum arc furnace is then evacuated to 5 × 10⁻⁶. -3 After Pa, inert argon gas is introduced, and each alloy sample is flipped over and repeatedly melted 6 times to obtain a casting billet.

[0079] The resulting billet was hot-rolled at 1455 K with a reduction of 50%. It was then homogenized at 1455 K for 5 min, followed by cold rolling with a reduction of 50%. Finally, it underwent recrystallization annealing at 1225 K for 30 min. All heat-treated samples were air-cooled, resulting in the alloy described in Example 4.

[0080] Depend on Figure 8-10 As can be seen, this embodiment has an FCC solid solution structure, with intermetallic compounds enriched in Gd and Ni embedded in the matrix, and the grain size is uniform. Figure 11 The results show that the saturation magnetization of the alloy at room temperature is 1.696T, the coercivity is 36.75A / m, the initial permeability is 3.45mH / m, and the magnetic loss is 178.2J / m^3. Figure 12 This indicates an elongation of 51.87% and a tensile strength of 511 MPa.

[0081] Example 5

[0082] According to the chemical formula Fe 39.18 Co 29.39 Ni 29.39 Gd 0.05 Al 2.00 The ingredients are proportioned according to atomic percentage, with Fe, Ni, Co, Gd, and Al raw materials using their corresponding elemental particles. The gas pressure in the vacuum arc furnace is then evacuated to 5 × 10⁻⁶. -3 After Pa, inert argon gas is introduced, and each alloy sample is flipped over and repeatedly melted 6 times to obtain a casting billet.

[0083] The resulting billet was hot-rolled at 1455 K with a reduction of 50%. It was then homogenized at 1455 K for 5 min, followed by cold rolling with a reduction of 50%. Finally, it underwent recrystallization annealing at 1225 K for 30 min. All heat-treated samples were air-cooled, resulting in the alloy described in Example 5.

[0084] Depend on Figure 13-15 As can be seen, this embodiment has an FCC solid solution structure, with intermetallic compounds enriched in Gd and Ni embedded in the matrix, and the Al element is evenly distributed with uniform grain size. Figure 16The results show that the saturation magnetization of the alloy at room temperature is 1.619T, the coercivity is 36.21A / m, the initial permeability is 3.37mH / m, and the magnetic loss is 178.2J / m^3. Figure 17 This indicates that the elongation is 51.85% and the tensile strength is 521 MPa.

[0085] Example 6

[0086] According to the chemical formula Fe 38.38 Co 28.79 Ni 28.79 Gd 0.05 Al 4.00 The ingredients are proportioned according to atomic percentage, with Fe, Ni, Co, Gd, and Al raw materials using their corresponding elemental particles. The gas pressure in the vacuum arc furnace is then evacuated to 5 × 10⁻⁶. -3 After Pa, inert argon gas is introduced, and each alloy sample is flipped over and repeatedly melted 6 times to obtain a casting billet.

[0087] The resulting billet was hot-rolled at 1455 K with a reduction of 50%. It was then homogenized at 1455 K for 5 min, followed by cold rolling with a reduction of 50%. Finally, it underwent recrystallization annealing at 1225 K for 30 min. All heat-treated samples were air-cooled, resulting in the alloy described in Example 6.

[0088] Depend on Figure 18-19 As can be seen, this embodiment has an FCC solid solution structure, with intermetallic compounds enriched in Gd and Ni embedded in the matrix, and the Al element is evenly distributed with uniform grain size. Figure 20 The results show that the saturation magnetization of the alloy at room temperature is 1.513T, the coercivity is 41.38A / m, the initial permeability is 2.68mH / m, and the magnetic loss is 171.7J / m^3. Figure 21 This indicates that the elongation is 54.21% and the tensile strength is 552 MPa.

[0089] Comparative Example 1

[0090] According to the chemical formula Fe 46.3 Co 43.9 Ni 9.8 The ingredients are proportioned by atomic percentage, with Fe, Ni, and Co raw materials using their corresponding elemental particles. The gas pressure in the vacuum arc furnace is then evacuated to 5 × 10⁻⁶. -3 After Pa, inert argon gas is introduced, and each alloy sample is flipped over and repeatedly melted 6 times to obtain a casting billet.

[0091] The resulting billet was hot-rolled at 1225 K with a reduction of 50%. It was then homogenized at 1225 K for 20 min, followed by cold rolling with a reduction of 50%. Finally, it underwent recrystallization annealing at 1225 K for 15 min. All heat-treated samples were water-cooled, resulting in the alloy shown in Comparative Example 1.

[0092] Figure 22 It is evident that this alloy has a BCC solid solution structure. Figure 23 The results show that the alloy has a saturation magnetization of 1.344 T, a coercivity of 1564 A / m, an initial permeability of 0.05 mH / m, and a magnetic loss of 6006 J / m^3 at room temperature. The low initial permeability indicates that the comparative alloy is difficult to respond to changes in the magnetic field, and the excessively high coercivity is not suitable for application.

[0093] Comparative Example 2

[0094] According to the chemical formula Fe 37.19 Co 27.88 Ni 27.88 Gd 0.05 Al 7.00 The ingredients are proportioned according to atomic percentage, with Fe, Ni, Co, Gd, and Al raw materials using their corresponding elemental particles. The gas pressure in the vacuum arc furnace is then evacuated to 5 × 10⁻⁶. -3 After Pa, inert argon gas is introduced, and each alloy sample is flipped over and repeatedly melted 6 times to obtain a casting billet.

[0095] The resulting billet was hot-rolled at 1455 K with a reduction of 50%. It was then homogenized at 1455 K for 5 min, followed by cold rolling with a reduction of 50%. Finally, it underwent recrystallization annealing at 1225 K for 30 min. All heat-treated samples were air-cooled, resulting in the alloy shown in Comparative Example 2.

[0096] Figure 24-25 This indicates that the matrix of the alloy is an FCC solid solution, and the energy dispersive spectroscopy shows that Gd and Ni elements are combined and precipitated, but individual Gd particles also exist. Figure 26 The results show that the saturation magnetization of the alloy at room temperature is reduced to 1.381T compared to Example 5, the coercivity is 50.31A / m, the initial permeability is also reduced to 1.87mH / m, and the magnetic loss is 164.2J / m^3. Figure 27 This indicates that the alloy has an elongation of 57.65% at room temperature and a tensile strength of 609 MPa.

[0097] Comparative Example 3

[0098] According to the chemical formula Fe 38.8 Co 29.1 Ni 29.1 Gd 3.0The ingredients are proportioned according to atomic percentage, with Fe, Ni, Co, and Gd raw materials using their corresponding elemental particles. The gas pressure in the vacuum arc furnace is then evacuated to 5 × 10⁻⁶. -3 After Pa, inert argon gas is introduced, and each alloy sample is flipped over and repeatedly melted 6 times to obtain a casting billet.

[0099] Figure 28 This indicates that after six melting cycles, Gd in the sample failed to combine with any other element to form a partially enclosed network structure. The resulting billet was hot-rolled at 1455 K with a reduction of 50%. The surface of the as-cast sample showed severe oxidation, and the inhomogeneity of the internal structure and composition led to cracking of the alloy during hot rolling. The only difference between this comparative example and Example 4 in terms of elemental composition is the content of Gd, indicating that an appropriate amount of Gd is required.

[0100] Comparative Example 4

[0101] According to the chemical formula Fe 49.0 Co 46.0 Ni 5.0 The ingredients are proportioned by atomic percentage, with Fe, Ni, and Co raw materials using their corresponding elemental particles. The gas pressure in the vacuum arc furnace is then evacuated to 5 × 10⁻⁶. -3 After Pa, inert argon gas is introduced, and each alloy sample is flipped over and repeatedly melted 6 times to obtain a casting billet.

[0102] The resulting billet was hot-rolled at 1225 K with a reduction of 50%. It was then homogenized at 1225 K for 20 min, followed by cold rolling with a reduction of 50%. Finally, it underwent recrystallization annealing at 1225 K for 15 min. All heat-treated samples were water-cooled, resulting in the alloy shown in Comparative Example 4.

[0103] Figure 29 The results show that the alloy has a saturation magnetization of 1.78 T, a coercivity of 654.3 A / m, an initial permeability of 0.21 mH / m, and a magnetic loss of 3599 J / m^3 at room temperature. This comparative alloy differs from Example 1 only in its heat treatment process; the water-cooling method resulted in severe stress concentration within the sample, leading to a decrease in both saturation magnetization and initial permeability.

Claims

1. A multi-component alloy with high mechanical properties and soft magnetic properties, characterized in that: It is composed of the elements Fe, Co, Ni, Gd and Al; By atomic percentage, Fe is 38-50%, Co is 28-50%, Ni is 5-8% or 25-30%, Gd is greater than 0 and ≤0.05%, and Al is greater than 0 and ≤5%. The total atomic percentage of Fe, Co, and Ni is ≤100% and ≥94%; the atomic ratio of Fe and Co is >1 and ≤1.35; the total atomic percentage of Gd and Al dopants is >0 and ≤5%; and the total atomic percentage of all components is 100%. The alloy has the following properties: (a) The saturation magnetization at room temperature is 1.5~2.1 T; (b) Coercivity is 30~650 A / m; (c) Under quasi-static tensile conditions at room temperature, the tensile elongation is greater than 50%; (d) The tensile yield strength at room temperature is 210~400 MPa, and the tensile strength is 430~600 MPa; (e) The initial permeability is 0.29~3.45 mH / m.

2. The method for preparing a multi-component alloy with high mechanical properties and soft magnetic properties as described in claim 1, characterized in that: The process includes taking each component according to the atomic percentage of the alloy, melting it under inert gas protection or vacuum conditions, casting it to obtain an alloy billet, and then obtaining the alloy by thermomechanical processing of the billet.

3. The method for preparing a multi-component alloy with high mechanical properties and soft magnetic properties as described in claim 2, characterized in that: The smelting under inert gas protection conditions requires multiple gas purgings of the furnace cavity, followed by the introduction of inert gas and maintenance of the gas pressure at 0.000001~0.05 MPa.

4. The method for preparing a multi-component alloy with high mechanical properties and soft magnetic properties as described in claim 2, characterized in that: The thermomechanical processing includes hot rolling, homogenization, cold rolling, and annealing.

5. The method for preparing a multi-component alloy with high mechanical properties and soft magnetic properties as described in claim 4, characterized in that: The hot rolling process is carried out at a temperature of 1173~1523 K and a reduction of 30%~80%.

6. The method for preparing a multi-component alloy with high mechanical properties and soft magnetic properties as described in claim 4 or 5, characterized in that: The homogenization process involves a heat treatment temperature higher than or equal to the hot rolling temperature, with a holding time of 5 to 300 minutes.

7. The method for preparing a multi-component alloy with high mechanical properties and soft magnetic properties as described in claim 6, characterized in that: The cold rolling process involves a reduction of 30-80%.

8. The method for preparing a multi-component alloy with high mechanical properties and soft magnetic properties as described in any one of claims 4, 5, or 7, characterized in that: The annealing process is carried out at a temperature of 1123~1323 K, with a holding time of 10~300 min, and the cooling method is air cooling, furnace cooling, or furnace cooling to a certain temperature followed by air cooling.

Images