Multi-component alloy with high mechanical property and soft magnetic property and preparation method thereof

Abstract

The invention discloses a multi-component alloy with high mechanical property and soft magnetic property and a preparation method of the multi-component alloy, an alloy matrix is of an FCC or BCC solid solution structure, a small amount of intermetallic compounds are introduced after Gd and Al are alloyed, the alloy is composed of Fe, Co, Ni, Gd and Al, and according to atomic percent, Fe accounts for 38-50%, Co accounts for 28-50%, Ni accounts for 5-30%, Gd accounts for 0-0.05%, and Al accounts for 0-5%. Fe, Co and Ni are combined according to a proper proportion to serve as an alloy matrix, Gd, Al and other elements are introduced into the matrix alloy, a uniform organization structure with the moderate grain size is obtained through a proper heat treatment technology and a proper plastic processing system, and therefore excellent plasticity and mechanical strength are obtained while high saturation magnetization intensity and low coercive force are guaranteed; the material can be used as a soft magnetic material in the fields of power industry and electronic equipment.

Description

Technical Field

[0001] The present invention belongs to the technical field of preparation of soft magnetic materials, and particularly relates to a multi-component soft magnetic alloy with high plasticity, high saturation magnetization intensity and low coercivity, and a preparation method thereof. Background Art

[0002] Soft magnetic materials refer to materials that can quickly respond to changes in an externally applied magnetic field and can obtain a high magnetic flux density with low loss. Soft magnetic materials have characteristics such as low coercivity, high magnetic permeability and high saturation magnetization intensity. They are easily magnetized and demagnetized under the action of an external magnetic field, and are widely used in the power industry and electronic devices to improve efficiency and reduce losses. However, soft magnetic materials usually need to bear mechanical loads during use, so certain strength of soft magnetic properties is required. At the same time, good plasticity of soft magnetic materials can reduce the possibility of material scrapping caused by defects such as cracks during complex processing, improve the yield rate, and further enhance the reliability and performance of the equipment during use. Currently, there are various methods for strengthening and toughening the design of soft magnetic materials, but to varying degrees, their soft magnetic properties are damaged. For example, doping with non-magnetic elements reduces the saturation magnetization intensity, and phase interfaces increase the coercivity, etc. In the global market, the huge application scale of soft magnetic materials makes even a small reduction in magnetic properties cause huge waste of resources. Therefore, the reduction of soft magnetic properties caused by material strengthening and toughening will greatly hinder the wider application of soft magnetic materials. Reducing the loss of magnetic properties during the strengthening and toughening process of soft magnetic materials is particularly crucial in the design of new soft magnetic alloys.

[0003] The complex chemical composition of multi-component high-entropy alloys gives them a broader space for microstructural regulation and greater potential for performance optimization, providing new ideas for the development of alloys with both soft magnetic properties and mechanical properties. From the design of equiatomic ratio to non-equiatomic ratio multi-principal element alloys, by adjusting different element compositions and ratios, the structural properties and functionality of materials are changed, which makes alloy design more flexible. Recent research reported a new type of FeCoNiTaAl-based soft magnetic high-entropy alloy and proposed various strengthening and toughening methods. For example, Fe 32.6 Co 27.7 Ni 27.7 Ta 5.0 Al 7.0 (at.%), its tensile strength can reach 1336 MPa and the elongation can reach 54% [Han, et al. Nature, 2022.]; Fe 35 Co 30 Ni 30The tensile strength of Ta5 (at.%) can reach 1.93 GPa, and the elongation is 12.6% [Han, et al. Nature Communications, 2024]. However, the saturation magnetization intensities of the above two high-strength, tough and soft magnetic high-entropy alloys are relatively low, both lower than 120 A / m 2 / kg (~1.3 T), making it difficult to meet the requirements for soft magnetic properties of materials in practical applications.

[0004] In summary, although soft magnetic high-entropy alloys can possess excellent mechanical properties, they often come at the cost of sacrificing some saturation magnetization intensity. A new solution is urgently needed to address the coordination problem between excellent soft magnetic properties and mechanical properties. Summary of the Invention

[0005] The purpose of this section is to outline some aspects of the embodiments of the present invention and briefly introduce some preferred embodiments. Simplifications or omissions may be made in this section, as well as in the abstract and title of the present application, to avoid obscuring the purpose of this section, the abstract, and the title. However, such simplifications or omissions shall not be used to limit the scope of the present invention.

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

[0007] One of the objectives of the present invention is to provide a multi-component alloy with excellent mechanical properties and soft magnetic properties. By combining Fe, Co, and Ni in appropriate proportions as the alloy matrix, elements such as Gd and Al are introduced into the matrix alloy, and a uniform and moderately sized grain structure is obtained using appropriate heat treatment processes and plastic processing systems, thereby achieving excellent plasticity and mechanical strength while ensuring high saturation magnetization intensity and low coercivity.

[0008] To solve the above technical problems, the present invention provides the following technical solution: a multi-component soft magnetic alloy with high plasticity, high saturation magnetization intensity, and low coercivity. The alloy matrix has an FCC or BCC solid solution structure, and a small amount of intermetallic compounds are introduced after alloying with Gd and Al. 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] Among them, the sum of the atomic percentages of Fe, Co, and Ni is ≤100% and ≥94%; the atomic ratio range of Fe and Co is >1 and ≤1.35; the sum of the atomic percentages of Gd and Al doping is ≥0% and ≤5%; the sum of the atomic percentages 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] Through the design concept of multi-component alloy, the present invention uses Fe, Co, Ni, Gd, Al alloy raw materials to obtain a multi-component alloy with characteristics such as high plasticity, high saturation magnetization and low coercivity;

[0013] The Fe element is an important strengthening element, which can improve the strength and workability of the alloy, and as a transition metal element itself, it can enhance the magnetism of the alloy. The addition of Co and Ni can produce strong ferromagnetic coupling with the Fe element to obtain a relatively high saturation magnetization, increase the Curie temperature, and the two are infinitely soluble with the Fe element. Among them, the Co element can strengthen the solid solution strengthening of the alloy; the Ni element can stabilize the face-centered cubic configuration of the alloy and improve the plasticity of the alloy. In order to make full use of the coupling effect and magnetic moment contribution between Fe and Co atoms, the present invention requires that the atomic percentages of Fe and Co elements are not greater than 1.35.

[0014] The doping of a large amount of non-magnetic metals may lead to magnetic dilution and thus reduce the performance of soft magnetic materials. As a rare earth element with ferromagnetism at room temperature, Gd doping has the potential to increase the saturation magnetization of the FeCoNi matrix alloy; however, due to its too large atomic radius and small solid solubility in the matrix, its content is controlled below 0.1%. In addition, the Al element may interact with other elements with multiple magnetic configurations to change its magnetic moment distribution and thus increase the saturation magnetization; however, since the Al element is an element that stabilizes the BCC phase, its content is controlled below 10%.

[0015] The present invention can effectively increase the saturation magnetization and reduce the coercivity of the soft magnetic alloy by applying different heat treatment methods to the FeCoNi multi-component matrix alloy with appropriate atomic ratios; further introducing Gd and Al elements, it is found that when the content of the Al element is within a specific range, the alloy has obvious low coercivity characteristics and maintains relatively high plasticity.

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

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

[0018] (b) The coercivity is 30-650 A / m;

[0019] (c) Under the condition of quasi-static tension 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 preparation method of a multi-component soft magnetic alloy with high plasticity, high saturation magnetization intensity and low coercivity as described above, including: allocating each component according to the atomic percentage of the alloy, melting under the protection of an inert gas or in a vacuum condition, casting to obtain an alloy ingot, and obtaining the alloy after hot mechanical processing of the ingot.

[0023] 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, wherein: when melting under the protection of an inert gas, the furnace cavity needs to be purged with gas multiple times, and then an inert gas is filled and the gas pressure is maintained at 0.000001 - 0.05 MPa.

[0024] 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, wherein: the hot mechanical processing includes hot rolling, homogenization, cold rolling and annealing treatment.

[0025] 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, wherein: for the hot rolling, the temperature is 1173 - 1523 K, and the reduction ratio is 30% - 80%.

[0026] 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, wherein: for the homogenization, the heat treatment temperature is higher than or equal to the hot rolling temperature, and the holding time is 5 - 300 min.

[0027] 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, wherein: for the cold rolling, the reduction ratio is 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, wherein: for the annealing treatment, the temperature is 1123 - 1323 K, and the holding time is 10 - 300 min; the cooling method is air cooling, furnace cooling or air cooling after furnace cooling to a certain temperature.

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

[0030] The present invention provides a multi-component soft magnetic alloy of Fe, Co, Ni, Gd, and Al with an appropriate atomic ratio. This alloy series has a high content of ferromagnetic elements. By combining the design concept of multi-component alloys with appropriate heat treatment processes and plastic processing techniques, the soft magnetic alloy can enhance its plasticity while maintaining a high saturation magnetization intensity and a low coercivity, which has great practical significance and value. BRIEF DESCRIPTION OF THE DRAWINGS

[0031] To more clearly illustrate the technical solutions of the embodiments of the present invention, the following briefly introduces the drawings required for the description of the embodiments. Obviously, the following drawings are only some embodiments of the present invention. For those of ordinary skill in the art, without creative efforts, other drawings can also be obtained based on these drawings. Among them:

[0032] Figure 1 is the XRD spectrum of the alloy material in Embodiment 1 of the present invention.

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

[0034] Figure 3 is the room temperature tensile engineering stress-strain curve diagram of the alloy material in Embodiment 3 of the present invention.

[0035] Figure 4 is the XRD spectrum of the alloy material in Embodiment 2 of the present invention.

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

[0037] Figure 6 is the XRD spectrum of the alloy material in Embodiment 3 of the present invention.

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

[0039] Figure 8 is the XRD spectrum of the alloy material in Embodiment 4 of the present invention.

[0040] Figure 9 is the scanning electron microscope morphology diagram and energy spectrum surface distribution diagram of the alloy material in Embodiment 4 of the present invention.

[0041] Figure 10 is the EBSD scan diagram of the alloy material in Embodiment 4 of the present invention.

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

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

[0044] Figure 13 It is the XRD spectrum diagram of the alloy material in Example 5 of the present invention.

[0045] Figure 14 It is the scanning electron microscope morphology diagram and energy spectrum surface distribution diagram of the alloy material in Example 5 of the present invention.

[0046] Figure 15 It is the EBSD scanning diagram of the alloy material in Example 5 of the present invention.

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

[0048] Figure 17 It is the room-temperature tensile engineering stress-strain curve diagram of the alloy material in Example 5 of the present invention.

[0049] Figure 18 It is the XRD spectrum diagram of the alloy material in Example 6 of the present invention.

[0050] Figure 19 It is the EBSD scanning diagram of the alloy material in Example 6 of the present invention.

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

[0052] Figure 21 It is the room-temperature tensile engineering stress-strain curve diagram of the alloy material in Example 6 of the present invention.

[0053] Figure 22 It is the XRD spectrum diagram of the alloy material in Comparative Example 1 of the present invention.

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

[0055] Figure 24 It is the XRD spectrum diagram of the alloy material in Comparative Example 2 of the present invention.

[0056] Figure 25 It is the EBSD scanning diagram of the alloy material in Comparative Example 2 of the present invention.

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

[0058] Figure 27 It is the room-temperature tensile engineering stress-strain curve diagram of the alloy material in Comparative Example 2 of the present invention.

[0059] Figure 28It is the scanning electron microscope morphology diagram and energy spectrum surface distribution diagram of the alloy material of Comparative Example 3 of the present invention.

[0060] Figure 29 It is the hysteresis loop diagram of the alloy material of Comparative Example 4 of the present invention. Specific Embodiments

[0061] To make the above objects, features, and advantages of the present invention more obvious and understandable, the specific embodiments of the present invention will be described in detail below in conjunction with the embodiments of the specification.

[0062] Many specific details are set forth in the following description in order to fully understand the present invention, but the present invention may also be implemented in other ways different from those described herein. Those skilled in the art can make similar generalizations without departing from the connotation of the present invention. Therefore, the present invention is not limited by the specific embodiments disclosed below.

[0063] Secondly, the so-called "one embodiment" or "embodiment" herein refers to a specific feature, structure, or characteristic that may be included in at least one implementation manner 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 separate or alternative embodiment that excludes other embodiments.

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

[0065] Embodiment 1

[0066] According to the chemical formula Fe 40.0 Co 30.0 Ni 30.0 (atomic percentage) for batching, and the raw materials of Fe, Ni, and Co use their corresponding elemental particles. After the air pressure in the vacuum arc furnace is pumped to 5×10 -3 Pa, an inert gas argon is filled, and each alloy sample is turned over and remelted 6 times to obtain a billet.

[0067] The obtained billet is hot-rolled at 1455K with a reduction of 50%. Next, it undergoes a homogenization treatment at 1455K / 15min. Then it is cold-rolled with a reduction of 50%. After that, a recrystallization annealing treatment at 1225K / 30min is carried out. The heat-treated samples are all air-cooled, and finally the alloy in Embodiment 1 is obtained.

[0068] From Figure 1 it can be seen that this embodiment is an FCC solid solution structure. Figure 2 It shows that at room temperature, the saturation magnetization intensity of this alloy is 1.67T, the coercivity is 43.74A / m, the initial magnetic permeability is 2.71mH / m, and the magnetic loss is 195.3J / m^3. Figure 3It shows that the elongation of this alloy at room temperature is 62.6%, and the tensile strength is 511 Mpa.

[0069] Example 2

[0070] Ingredients are prepared according to the chemical formula Fe 49.0 Co 46.0 Ni 5.0 (atomic percentage). The raw materials of Fe, Ni, and Co use their corresponding elemental particles. After the air pressure in the vacuum arc furnace is pumped to 5×10 -3 Pa, inert gas argon is filled. Each alloy sample is turned over and remelted 6 times to obtain a billet.

[0071] The obtained billet is hot-rolled at 1225K with a reduction of 50%. Next, it undergoes homogenization treatment at 1225K / 20min. Then it is cold-rolled with a reduction of 50%. After that, it undergoes recrystallization annealing treatment at 1225K / 15min. The heat-treated samples are all air-cooled, and finally the alloy in Example 2 is obtained.

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

[0073] Example 3

[0074] Ingredients are prepared according to the chemical formula Fe 47.0 Co 46.0 Ni 7.0 (atomic percentage). The raw materials of Fe, Ni, and Co use their corresponding elemental particles. After the air pressure in the vacuum arc furnace is pumped to 5×10 -3 Pa, inert gas argon is filled. Each alloy sample is turned over and remelted 6 times to obtain a billet.

[0075] The obtained billet is hot-rolled at 1225K with a reduction of 50%. Next, it undergoes homogenization treatment at 1225K / 20min. Then it is cold-rolled with a reduction of 50%. After that, it undergoes recrystallization annealing treatment at 1225K / 15min. The heat-treated samples are all air-cooled, and finally the alloy in Example 3 is obtained.

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

[0077] Example 4

[0078] According to the chemical formula Fe 39.97 Co 29.99 Ni 29.99 G 0.05 (atomic percentage) for batching, Fe, Ni, Co, Gd raw materials use their corresponding single substance particles. When the pressure in the vacuum arc furnace is pumped to 5×10 -3 After Pa, inert gas argon was filled in, and each alloy sample was turned over and melted repeatedly for 6 times to obtain a casting.

[0079] The obtained ingot was hot rolled at 1455K with a reduction of 50%. Then, it was homogenized at 1455K / 5min. Then, it was cold rolled with a reduction of 50%. Then, it was recrystallized annealed at 1225K / 30min. The heat-treated samples were all air-cooled, and finally, the alloy in Example 4 was obtained.

[0080] Depend on Figures 8 - 10 It can be seen that this embodiment has an FCC solid solution structure, the matrix is ​​doped with Gd and Ni-enriched intermetallic compounds, and the grain size is uniform. Figure 11 It shows that the saturation magnetization of the alloy at room temperature is 1.696T, the coercive force is 36.75A / m, the initial magnetic permeability is 3.45mH / m, and the magnetic loss is 178.2J / m^3; Figure 12 It shows that the elongation is 51.87% and the tensile strength is 511Mpa.

[0081] Example 5

[0082] According to the chemical formula Fe 39.18 Co 29.39 Ni 29.39 G 0.05 Al 2.00 (atomic percentage) for batching, Fe, Ni, Co, Gd, Al raw materials use their corresponding single substance particles. When the pressure in the vacuum arc furnace is pumped to 5×10 -3 After Pa, inert gas argon was filled in, and each alloy sample was turned over and melted repeatedly for 6 times to obtain a casting.

[0083] The obtained ingot was hot rolled at 1455K with a reduction of 50%. Then, it was homogenized at 1455K / 5min. Then, it was cold rolled with a reduction of 50%. Then, it was recrystallized annealed at 1225K / 30min. The heat-treated samples were all air-cooled, and finally, the alloy in Example 5 was obtained.

[0084] Depend on Figures 13 - 15 It can be seen that this embodiment has an FCC solid solution structure, the matrix is ​​doped with Gd and Ni-enriched intermetallic compounds, the Al element is evenly distributed, and the grain size is uniform. Figure 16It shows that the saturation magnetization of the alloy at room temperature is 1.619T, the coercive force is 36.21A / m, the initial magnetic permeability is 3.37mH / m, and the magnetic loss is 178.2J / m^3; Figure 17 It shows that the elongation is 51.85% and the tensile strength is 521Mpa.

[0085] Example 6

[0086] According to the chemical formula Fe 38.38 Co 28.79 Ni 28.79 G 0.05 Al 4.00 (atomic percentage) for batching, Fe, Ni, Co, Gd, Al raw materials use their corresponding single substance particles. When the pressure in the vacuum arc furnace is pumped to 5×10 -3 After Pa, inert gas argon was filled in, and each alloy sample was turned over and melted repeatedly for 6 times to obtain a casting.

[0087] The obtained ingot was hot rolled at 1455K with a reduction of 50%. Then, it was homogenized at 1455K / 5min. Then, it was cold rolled with a reduction of 50%. Then, it was recrystallized annealed at 1225K / 30min. The heat-treated samples were all air-cooled, and finally, the alloy in Example 6 was obtained.

[0088] Depend on Figures 18 - 19 It can be seen that this embodiment has an FCC solid solution structure, the matrix is ​​doped with Gd and Ni-enriched intermetallic compounds, the Al element is evenly distributed, and the grain size is uniform. Figure 20 It shows that the saturation magnetization of the alloy at room temperature is 1.513T, the coercive force is 41.38A / m, the initial magnetic permeability is 2.68mH / m, and the magnetic loss is 171.7J / m^3; Figure 21 It shows that the elongation is 54.21% and the tensile strength is 552Mpa.

[0089] Comparative Example 1

[0090] According to the chemical formula Fe 46.3 Co 43.9 Ni 9.8 (atomic percentage) for batching, Fe, Ni, and Co raw materials use their corresponding single-substance particles. When the pressure in the vacuum arc furnace is pumped to 5×10 -3 After Pa, inert gas argon was filled in, and each alloy sample was turned over and melted repeatedly for 6 times to obtain a casting.

[0091] The obtained ingot was hot-rolled at 1225 K with a reduction of 50%. Next, it was subjected to homogenization treatment at 1225 K for 20 min. Then cold rolling was carried out with a reduction of 50%. After that, recrystallization annealing treatment at 1225 K for 15 min was carried out. All heat-treated samples were water-cooled, and finally the alloy in Comparative Example 1 was obtained.

[0092] Figure 22 It can be seen that the alloy has a BCC solid solution structure. Figure 23 It shows that the saturation magnetization intensity of the alloy at room temperature is 1.344 T, the coercivity is 1564 A / m, the initial permeability is 0.05 mH / m, and the magnetic loss is 6006 J / m^3; the lower initial permeability indicates that the alloy in this comparative example is less responsive to magnetic field changes, and the too high coercivity is not suitable for applications.

[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 (atomic percentage) for batching, and the raw materials of Fe, Ni, Co, Gd, and Al used their corresponding single-element particles. After the air pressure in the vacuum arc furnace was pumped to 5×10 -3 Pa, inert gas argon was filled, and each alloy sample was turned over and remelted 6 times to obtain an ingot.

[0095] The obtained ingot was hot-rolled at 1455 K with a reduction of 50%. Next, it was subjected to homogenization treatment at 1455 K for 5 min. Then cold rolling was carried out with a reduction of 50%. After that, recrystallization annealing treatment at 1225 K for 30 min was carried out. All heat-treated samples were air-cooled, and finally the alloy in Comparative Example 2 was obtained.

[0096] Figures 24 - 25 It shows that the matrix of the alloy is an FCC solid solution, and it can be seen from the energy spectrum surface distribution that Gd and Ni elements combine and precipitate, but there are separate Gd particles. Figure 26 It shows that at room temperature, the saturation magnetization intensity of the alloy is reduced to 1.381 T compared with Example 5, the coercivity is 50.31 A / m, and the initial permeability is also reduced to 1.87 mH / m, and the magnetic loss is 164.2 J / m^3; Figure 27 It shows that the elongation of the alloy at room temperature is 57.65%, and the tensile strength is 609 Mpa.

[0097] Comparative Example 3

[0098] According to the chemical formula Fe 38.8 Co 29.1 Ni 29.1 Gd 3.0(atomic percentage), the raw materials of Fe, Ni, Co, and Gd use their corresponding elemental particles. After the air pressure in the vacuum arc furnace is pumped to 5×10 -3 Pa, an inert gas argon is filled, and each alloy sample is turned over and remelted 6 times to obtain a billet.

[0099] Figure 28 It shows that Gd in the sample after 6 times of melting fails to combine with any element and forms an incomplete surrounding network structure alone. The obtained billet is hot-rolled at 1455K with a reduction of 50%. The surface layer of the as-cast sample is severely oxidized, and the uneven internal structure and composition cause the alloy to crack during hot rolling. The difference in the elemental composition of this comparative example from that of Example 4 is only the content of the Gd element, indicating that the Gd element needs to be appropriate.

[0100] Comparative Example 4

[0101] According to the chemical formula Fe 49.0 Co 46.0 Ni 5.0 (atomic percentage), the raw materials of Fe, Ni, Co use their corresponding elemental particles. After the air pressure in the vacuum arc furnace is pumped to 5×10 -3 Pa, an inert gas argon is filled, and each alloy sample is turned over and remelted 6 times to obtain a billet.

[0102] The obtained billet is hot-rolled at 1225K with a reduction of 50%. Next, it undergoes a homogenization treatment at 1225K / 20min. Then it is cold-rolled with a reduction of 50%. After that, it undergoes a recrystallization annealing treatment at 1225K / 15min. The heat-treated samples are all water-cooled, and finally the alloy in Comparative Example 4 is obtained.

[0103] Figure 29 It shows that at room temperature, the saturation magnetization intensity of this alloy is 1.78T, the coercivity is 654.3A / m, the initial permeability is 0.21mH / m, and the magnetic loss is 3599J / m^3. The only difference between this comparative example alloy and Example 1 is the heat treatment system. The water-cooling treatment method causes severe stress concentration inside the sample, and both the saturation magnetization intensity and the initial permeability are reduced.

Claims

1. A multi-component alloy with high mechanical properties and soft magnetic properties, characterized in that: It is composed of elements Fe, Co, Ni, Gd and Al; 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%; Among them, the sum of the atomic percentage contents of Fe, Co, and Ni is ≤100% and ≥94%; the atomic ratio range of Fe and Co is >1 and ≤1.35; the sum of the atomic percentage contents of Gd and Al doping is ≥0% and ≤5%; the sum of the atomic percentages of each component is 100%.

2. The multi-component alloy with high mechanical properties and soft magnetic properties according to claim 1, wherein: The atomic percentage of the said Ni is 5-8% or 25-30%.

3. The multi-component alloy with high mechanical properties and soft magnetic properties according to claim 1 or 2, characterized in that: The said alloy has the following characteristics: (a) The saturation magnetization at room temperature is 1.5-2.1T; (b) The coercivity is 30-650 A / m; (c) Under the condition of quasi-static tensile 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.

4. The preparation method of the multi-component alloy with high mechanical properties and soft magnetic properties according to any one of claims 1 to 3, characterized in that: It includes taking each component according to the atomic percentage of the alloy, melting under the protection of inert gas or in vacuum, casting to obtain an alloy ingot, and obtaining the alloy after hot mechanical processing.

5. The preparation method of the multi-component alloy with high mechanical properties and soft magnetic properties according to claim 4, characterized in that: When melting under the protection of inert gas, the furnace cavity needs to be purged with gas for many times, and then filled with inert gas and the gas pressure is maintained at 0.000001-0.05 MPa.

6. The preparation method of the multi-component alloy with high mechanical properties and soft magnetic properties according to claim 4, characterized in that: The said hot mechanical processing includes hot rolling, homogenization, cold rolling and annealing treatment.

7. The preparation method of the multi-component alloy with high mechanical properties and soft magnetic properties as described in claim 6, characterized in that: For the said hot rolling, the temperature is 1173-1523 K, and the reduction ratio is 30%-80%.

8. The preparation method of the multi-component alloy with high mechanical properties and soft magnetic properties according to claim 6 or 7, characterized in that: For the said homogenization, the heat treatment temperature is higher than or equal to the hot rolling temperature, and the holding time is 5-300 min.

9. The preparation method of the multi-component alloy with high mechanical properties and soft magnetic properties according to claim 8, characterized in that: For the said cold rolling, the reduction ratio is 30-80%.

10. The preparation method of the multi-component alloy with high mechanical properties and soft magnetic properties according to any one of claims 6, 7 or 9, characterized in that: For the said annealing treatment, the temperature is 1123-1323 K, the holding time is 10-300 min, and the cooling method is air cooling, furnace cooling or air cooling after furnace cooling to a certain temperature.

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