Fe-Co-based soft magnetic material and method for manufacturing the same.

Abstract

This invention provides an Fe-Co-based soft magnetic material having low iron loss, high magnetic flux density, and good cold workability, as well as a method for manufacturing the same. [Solution] An alloy containing Co: 10.0~40.0 wt%, Ti: 0.2~3.0 wt%, Ni: 0.1~3.0 wt%, V: 0.1~3.0 wt%, and Fe: 51.0~89.6 wt%, with a Cr content of less than 0.5 wt%, and the content of elements other than Co, Ti, Ni, V, Fe, and Cr being 9.0 wt% or less, is melted down, and casting, hot working, cold working, and final magnetic annealing are performed in order. After hot working and before the final cold working, a heat treatment is performed to a soaking temperature of 800°C or higher.

Description

Technical Field

[0001] The present invention relates to an Fe-Co-based soft magnetic material and a method for manufacturing the same.

Background Art

[0002] An Fe-Co-based alloy containing Co in the range of 45.0 to 55.0 wt% is called Permendur, and as a soft magnetic material having high magnetic permeability and high saturation magnetic flux density, it is widely used in motors, generator cores, electromagnetic core magnets, and further in actuators, magnetostrictive vibrators, etc. However, this Fe-Co-based alloy generates an intermetallic compound (regular phase) of Fe-Co near 730 to 500 °C and becomes extremely brittle. Conventionally, as a cold-worked material of Permendur, a hot-rolled sheet hot-rolled to a thickness of about 5 mm was reheated to 800 to 1000 °C and then rapidly cooled in salt ice water (at -2 °C or lower) to impart ductility, thereby enabling cold rolling. Such rapid cooling not only increases the manufacturing cost but also has the problem of high raw material cost of Co. Also, regarding Permendur, although the saturation magnetic flux density is high, the electrical resistance is low. Therefore, as an iron core material for electric aircraft and motors for flying cars, the iron loss at frequencies of several hundred Hz or more is not necessarily superior to that of conventional 3% Si electrical steel sheets.

[0003] In order to improve the cold workability deterioration due to regular phase formation, which greatly inhibits the productivity, attempts have been made to suppress the formation of the regular phase by reducing the Co content. However, when a part of Fe is replaced with Co, as the amount of Co increases, the magnetostriction constant monotonically increases. Alloys with Co of 40 wt% or less have large magnetostriction and large magnetic anisotropy, so the core loss is large and not practical.

[0004] On the other hand, the saturation magnetization of pure Fe is 2.15 T, but at present, since the magnetic permeability is low, the magnetic flux density under a low magnetic field is not very high. The magnetic flux density (B at a magnetomotive force of 5000 A / m 50The magnetic flux density (DC) of pure Fe is 1.8T, which is not particularly high compared to the value of 1.6-1.7T for practical non-oriented silicon steel sheets. Adding Co to Fe increases the saturation magnetization, but the magnetostriction increases, further decreasing the permeability. For this reason, the magnetic flux density under a magnetic field of about 5000 A / m, which is practically important, cannot necessarily be obtained with the addition of Co. Also, due to the decrease in permeability, the iron loss value becomes large in Fe-Co alloys with low Co concentration, making them unsuitable for practical use.

[0005] To improve the iron loss and magnetization properties that deteriorate when the Co content of the material is reduced, attempts have been made to add a third element. As for the addition of a third element, the addition of electrical resistance-increasing elements such as Si and Al has been disclosed (see, for example, Patent Documents 1 to 4). Furthermore, a technique for forming a compacted magnetic core of Fe-Co-based soft magnetic material in a near-net shape has been disclosed (see, for example, Patent Documents 5 and 6). [Prior art documents] [Patent Documents]

[0006] [Patent Document 1] Patent No. 2615543 [Patent Document 2] Japanese Patent Application Publication No. 9-195010 [Patent Document 3] Patent No. 7181083 [Patent Document 4] Japanese Patent Publication No. 2022-22832 [Patent Document 5] Japanese Patent Publication No. 2002-75721 [Patent Document 6] Japanese Patent Publication No. 2003-68514 [Overview of the project] [Problems that the invention aims to solve]

[0007] However, the technologies described in Patent Documents 1 to 4 show improvement in iron loss characteristics by adding electrical resistance-increasing elements such as Si and Al, but there is a problem in that the improvement in magnetization characteristics in the low magnetic field region is insufficient. Furthermore, while the technologies described in Patent Documents 5 and 6 can avoid the problem of degraded workability, they have the drawback that the density of the formed magnetic core is lower than that of the bulk material, which inevitably leads to a decrease in magnetic flux density.

[0008] This invention has been made in view of these problems, and aims to provide an Fe-Co-based soft magnetic material having low iron loss, high magnetic flux density, and good cold workability, as well as a method for manufacturing the same. [Means for solving the problem]

[0009] The inventors, through diligent research to achieve the above objectives, have found that combining Ti, Ni, and V as material components, reducing Cr, and performing heat treatment at 800°C or higher before the final cold working is extremely effective in achieving the desired objectives. In other words, the addition of Ti improves the soft magnetic properties of the material, and the addition of Ni improves the ND / / after magnetic annealing. <100> We have newly discovered that the decrease in saturation magnetic flux density can be minimized by increasing the {100} orientation concentration of the structure, ensuring cold workability through V addition, and reducing the amount of Cr.

[0010] The Fe-Co-based soft magnetic material according to the present invention contains Co: 10.0 to 40.0 wt%, Ti: 0.2 to 3.0 wt%, Ni: 0.1 to 3.0 wt%, V: 0.1 to 3.0 wt%, and Fe: 51.0 to 89.6 wt%, with a Cr content of less than 0.5 wt%, and the content of elements other than Co, Ti, Ni, V, Fe, and Cr being 9.0 wt% or less. The Fe-Co-based soft magnetic material according to the present invention may contain C: 0.01 wt% or less, B: 0.01 wt% or less, Si: 3.0 wt% or less, Al: 2.0 wt% or less, Mn: 2.0 wt% or less, Nb: 1.0 wt% or less, Zr: 1.0 wt% or less, and Mo: 1.0 wt% or less, in a total content of 9.0 wt% or less, using one or a combination of two or more of these elements. In the Fe-Co-based soft magnetic material according to the present invention, it is preferable that the area ratio of the {100} crystal orientation is 25% or more, with an allowable range of 15°.

[0011] The present invention relates to a method for producing an Fe-Co-based soft magnetic material, comprising: melting an alloy containing Co: 10.0~40.0 wt%, Ti: 0.2~3.0 wt%, Ni: 0.1~3.0 wt%, V: 0.1~3.0 wt%, and Fe: 51.0~89.6 wt%, with a Cr content of less than 0.5 wt%, and the content of elements other than Co, Ti, Ni, V, Fe, and Cr being 9.0 wt% or less; and then sequentially performing casting, hot working, cold working, and final magnetic annealing, characterized in that a heat treatment to a soaking temperature of 800°C or higher is performed after the hot working and before the final cold working. The final magnetic annealing may be a single magnetic annealing, which is the first and last. Similarly, the final cold working may be a single cold working, which is the first and last. In the method for producing an Fe-Co-based soft magnetic material according to the present invention, the alloy may contain C: 0.01 wt% or less, B: 0.01 wt% or less, Si: 3.0 wt% or less, Al: 2.0 wt% or less, Mn: 2.0 wt% or less, Nb: 1.0 wt% or less, Zr: 1.0 wt% or less, and Mo: 1.0 wt% or less, in a total content of 9.0 wt% or less, using one or a combination of two or more of these elements.

[0012] The combined addition of Ti and Ni improves soft magnetic properties and increases the {100} orientation concentration. The reasons for this are not entirely clear, but the improvement in soft magnetic properties may be due to a change in the 3d electron orbital arrangement, while the improvement in {100} orientation concentration may be due to a decrease in {100} surface energy when the plate thickness is thin during magnetic annealing. In particular, for components with low Co content of 10.0-40.0 wt%, the magnetic anisotropy constant increases compared to Permendur, resulting in an increased magnetization easy axis (ND / / <100> It is believed that increasing the concentration of {100} orientations within the structure can significantly improve magnetization characteristics at low magnetic fields due to the movement of 180° magnetic domain walls, thereby greatly reducing iron loss.

[0013] While the B2 phase (FeCo) is known as the ordered phase of Fe-Co alloys, its formation ceases when the Co content is reduced to 30% or less, according to the phase diagram. However, in practice, cracking is more likely to occur during cold working, especially if heat treatment is applied before the final cold working. In terms of free energy, the formation of ordered phases other than the B2 phase, such as Fe3Co, is also predicted, and it has been pointed out that embrittlement occurs in impact tests at a Co content of around 18-24% (see Yalin Li et al. Materials Science & Engineering A 852 (2022) 143718 "Atomic ordering of Fe3Co and its impact on the mechanical properties of low-cobalt (18-24wt%) iron-cobalt alloys"). In this invention, by adding V, embrittlement after heat treatment before the final cold working can be suppressed. One possible reason for this is that it suppresses the formation of ordered phases other than the B2 phase.

[0014] The inventors have further discovered that this magnetic property improvement effect is enhanced by performing the heat treatment before the final cold working at a soaking temperature of 800°C or higher. The reason for the magnetic property improvement effect due to the heat treatment before the final cold working is not entirely clear, but it may be due to an increase in the {100} structure before the final cold working. The Fe-Co-based soft magnetic material and its manufacturing method according to the present invention are conceivable applications as core materials for motors in electric aircraft and flying cars. The present invention makes it possible to realize an Fe-Co-based soft magnetic material that is lower cost, has lower iron loss, higher magnetic flux density, and better cold workability than conventional permendur. The method for producing the Fe-Co-based soft magnetic material according to the present invention preferably includes the steps of splitting the alloy and cold working it. [Effects of the Invention]

[0015] According to the present invention, it is possible to provide an Fe-Co-based soft magnetic material having low iron loss, high magnetic flux density, and good cold workability, as well as a method for producing the same.

Embodiments for Carrying Out the Invention

[0016] Hereinafter, the Fe-Co-based soft magnetic material and its manufacturing method according to the embodiments of the present invention will be described in detail. The Fe-Co-based soft magnetic material according to the embodiments of the present invention contains Co: 10.0 to 40.0 wt%, Ti: 0.2 to 3.0 wt%, Ni: 0.1 to 3.0 wt%, V: 0.1 to 3.0 wt%, and Fe: 51.0 to 89.6 wt%, the Cr content is less than 0.5 Wt%, and the content of elements other than Co, Ti, Ni, V, Fe, and Cr is 9.0 wt% or less. The Fe-Co-based soft magnetic material may contain C: 0.01 wt% or less, B: 0.01 wt% or less, Si: 3.0 wt% or less, Al: 2.0 wt% or less, Mn: 2.0 wt% or less, Nb: 1.0 wt% or less, Zr: 1.0 wt% or less, and Mo: 1.0 wt% or less in a total content range of 9.0 wt% or less by one or a combination of two or more.

[0017] The reason for limiting the component composition to the above range will be explained. Co: 10.0 to 40.0 wt% Co is an essential element for ensuring soft magnetic properties, and it is necessary to adjust it within the range of Co: 10.0 to 40.0 wt% in order to obtain an excellent saturation magnetic flux density. When the Co content is less than 10.0 wt%, the effect of increasing the saturation magnetic flux density is small, and when it exceeds 40.0 wt%, the regularization of FeCo is likely to occur and the workability decreases. Therefore, Co is set to 10.0 to 40. wt%.

[0018] Ti: 0.2 to 3.0 wt% Ti is an essential element for reducing the magnetic anisotropy constant and increasing the electrical resistance, and thus improving the iron loss, particularly the hysteresis iron loss. However, when the content is less than 0.2 wt%, the effect is poor, and on the other hand, when it exceeds 3.0 wt%, the saturation magnetic flux density decreases. Therefore, it is limited to the range of 0.2 to 3.0 wt%. Ni: 0.2 to 3.0 wt% Ni is ND after final magnetic annealing. <100> This element enhances the {100} orientation concentration of the structure and exhibits an effect of improving magnetic flux density under low excitation magnetic flux density. However, its effect is poor below 0.1 wt%, while the saturation magnetic flux density decreases above 3.0 wt%, so the range was limited to 0.2 to 3.0 wt%.

[0019] V: 0.1~3.0 wt% V is a useful element that suppresses the formation of ordered phases detrimental to workability and improves cold workability. However, its effect is poor below 0.1 wt%, while the saturation magnetic flux density decreases above 3.0 wt%, so the range was limited to 0.1 to 3.0 wt%. Fe: 51.0~89.6 wt% Fe accounts for the portion remaining after excluding additives.

[0020] Cr: Less than 0.5 wt% Since a high concentration of Cr as an impurity significantly reduces the saturation magnetic flux density and increases iron loss, it is essential to reduce its content to less than 0.5 wt%, and preferably less than 0.1 wt%, by carefully considering the raw material composition. The essential components and essential components to be reduced have been explained above. Other components are as follows:

[0021] C: 0.01wt% or less Since carbon (C) degrades the magnetic properties of this alloy, it is desirable to reduce it as much as possible. However, if it is below 0.01 wt%, the adverse effects are minimal, and further reductions would lead to increased costs, so it is preferable to keep it below 0.01 wt%. B: 0.01wt% or less B is a useful element that increases grain boundary strength and improves cold workability, but if it exceeds 0.01 wt%, it forms nitrides at the grain boundaries and degrades iron loss, so it is desirable to keep it below 0.01 wt%.

[0022] Si:3.0wt% or less Si is a useful element for improving iron loss by increasing the electrical resistance of the material and reducing the magnetic anisotropy constant. However, if its content exceeds 3.0%, it promotes the formation of ordered phases and reduces workability, so it is desirable to keep it below 3.0 wt%. Al: 2.0wt% or less Al is also a useful element for improving iron loss by increasing the electrical resistance of the material, but if it exceeds 2.0%, the saturation magnetic flux density drops significantly, so it is desirable to keep it below 2.0 wt%.

[0023] Mn: 2.0wt% or less While Mn is exceptional in that it does not significantly reduce the saturation magnetic flux density and is effective in increasing electrical resistance to reduce iron loss, if it is included in too large an amount, it will lead to a decrease in magnetic flux density, so it is preferable to keep it at 2.0 wt% or less. Nb: 1.0wt% or less Nb is a useful element that exhibits a solid solution strengthening effect, but if it exceeds 1.0 wt%, the saturation magnetic flux density decreases significantly, so it is desirable to keep it below 1.0 wt%.

[0024] Zr: 1.0wt% or less Zr is also a useful element that exhibits a solid solution strengthening effect, but the saturation magnetic flux density decreases significantly when it exceeds 1.0 wt%, so it is desirable to keep it below 1.0 wt%. Mo: 1.0 wt% or less Mo is a useful element for improving corrosion resistance in this invention by reducing Cr, but since it reduces the saturation magnetic flux density, it is desirable to keep it below 1.0 wt%. The total content of one or more of C, B, Si, Al, Mn, Nb, Zr, and Mo is preferably 9.0 wt% or less, and particularly preferably 3.0 wt% or less.

[0025] In Fe-Co soft magnetic materials, it is preferable that the area ratio of {100} crystal orientation after final magnetic annealing is 25% or more, and particularly 50% or more, with a tolerance of 15°. The crystal orientation is determined by measuring the orientation of at least 1000 crystal grains using SEM (scanning electron microscope)-EBSD (backscattered electron diffraction). If the area ratio of {100} crystal orientation is less than 25%, both the magnetic flux density and iron loss will deteriorate significantly.

[0026] The method for manufacturing an Fe-Co alloy sheet according to an embodiment of the present invention is shown below. The method for producing Fe-Co soft magnetic materials involves melting a molten alloy raw material containing Co: 10.0~40.0 wt%, Ti: 0.2~3.0 wt%, Ni: 0.1~3.0 wt%, V: 0.1~3.0 wt%, and Fe: 51.0~89.6 wt%, with a Cr content of less than 0.5 wt%, and a total content of elements other than Co, Ti, Ni, V, Fe, and Cr of 9.0 wt% or less. Casting, hot working, cold working, and final magnetic annealing are then performed in sequence. Magnetic properties can be improved by performing a heat treatment at a soaking temperature of 800°C or higher after hot working and before the final cold working. The final magnetic annealing may be performed only once as the first and final magnetic annealing. Similarly, the final cold working may be performed only once as the first and final cold working. The heat treatment before the final cold working is preferably annealing. Magnetic annealing may be performed once or multiple times between casting and the final magnetic annealing, in addition to the final magnetic annealing.

[0027] First, the raw alloy material, formulated to have the aforementioned component composition, is melted and cast using conventional techniques, such as a vacuum induction furnace. The cast soft magnetic alloy is then hot-worked. Hot-working involves splitting, hot forging, and / or hot rolling to obtain a hot-rolled material. The heating temperature during hot-working is preferably 1000 to 1250°C.

[0028] The resulting hot-rolled material is subjected to cold working after the formed oxide scale is removed by shot blasting, pickling, etc. If cold working cannot be done in a single pass, it can be done in multiple passes. In this case, intermediate annealing may be performed to facilitate cold working. If intermediate annealing is performed, it may be a heat treatment performed before the final cold working. Next, annealing is performed at a soaking temperature of 800°C or higher as needed before the final cold working. This annealing process homogenizes the crystalline structure of the hot-rolled material through recrystallization, thereby improving the magnetic flux density after the final magnetic annealing, which is performed after the final cold working or after assembly into component shapes such as cores. While there are no specific requirements for the heating rate during the heat treatment before final cold working, rapid heating at 20°C / s or more between 400 and 700°C strengthens the {100} structure before cold working and increases the degree of integration of the {100} crystal orientation after final magnetic annealing. Similarly, there are no specific requirements for the cooling rate during the heat treatment before final cold working, but in cases where the material has a high Co content and high Si content, making it prone to the formation of ordered phases, rapid cooling at 20°C / s or more between 700 and 400°C is desirable to suppress the formation of ordered phases and ensure cold workability.

[0029] After the final cold working of the obtained cold-worked material, or after assembling it into a desired shape such as a core, a final magnetic annealing is performed. This final magnetic annealing is an annealing process that reduces iron loss by coarsening and leveling the crystal grains, and is preferably performed at a high temperature close to the α / α+γ transformation point. For example, it is held at a temperature in the range of 850 to 1050°C under a vacuum or a non-oxidizing atmosphere such as ammonia decomposition gas or hydrogen. This allows for the leveling and leveling of the alloy structure, resulting in a soft magnetic material with excellent iron loss.

[0030] In the method for manufacturing an Fe-Co soft magnetic material according to an embodiment of the present invention, by using an Fe-Co alloy material in which Ti, Ni, and V are compounded and the amount of Cr is reduced, and by performing a heat treatment before the final cold working at a soaking temperature of 800°C or higher, the degree of {100} orientation integration after the final magnetic annealing can be increased, thereby improving iron loss and magnetic flux density. If the soaking temperature is below 800°C, recrystallization by annealing will be insufficient, resulting in inadequate improvement of magnetic properties. To achieve an average heating rate of 20°C / s or higher during annealing before final cold rolling, it is preferable to apply high-frequency induction heating.

[0031] Thus, by using an Fe-Co alloy material with composite additions of Ti, Ni, and V, and reduced Cr, and further performing heat treatment before the final cold working at a soaking temperature of 800°C or higher, the {100} orientation concentration after final magnetic annealing is increased, making it possible to obtain a low-cost, high-productivity, low-Co-content component system that exhibits high magnetic flux density, particularly for electrical steel sheets, comparable to Permendur, and also low-loss soft magnetic materials. [Examples]

[0032] An alloy with the component composition shown in Table 1 was melted in a vacuum induction furnace and cast into a 2-ton steel ingot. In Table 1, the remaining 100 wt% is Fe. The resulting steel ingot was divided, hot forged at 1100°C, and then hot rolled at 1100°C to produce a hot-rolled material in the form of a 4.0 mm thick plate coil. Subsequently, the hot-rolled material was subjected to a heat treatment prior to final cold working, with a soaking time of 2 minutes at 1000°C. Furthermore, after removing scale by shot blasting and pickling, the material was cold-rolled to obtain a final cold-rolled sheet of Fe-Co-based soft magnetic material with a thickness of 0.15 mm.

[0033] [Table 1]

[0034] In Table 1, materials that could be thinned to a thickness of 0.15 mm by cold rolling are marked with "○", while those that cracked severely and could not proceed to the next process are marked with "×". Subsequently, a final magnetic annealing was performed, involving holding the material at a temperature of 900°C for 3 hours in a hydrogen atmosphere. A 30mm x 120mm cut sheet sample was taken from the steel sheet after the final magnetic annealing, and the magnetic flux density (DC H=5000A / m) and iron loss (Bm=1.5T f=1kHz) were measured using a single-sheet measuring instrument. The measured values ​​shown in Table 1 are the average values ​​in the rolling direction and the direction perpendicular to the rolling direction. For comparison, the measured values ​​of commercially available 0.15mm thick Permendur (sample 21) and commercially available electrical steel sheet (sample 22) are also shown in Table 1.

[0035] To investigate the crystal orientation, the surface was pre-treated by electrolytic polishing to a mirror finish, and then approximately 5000 crystal orientations were analyzed using SEM (Scanning Electron Microscope)-EBSD (Backscattered Electron Diffraction), resulting in ND / / <100> Table 1 shows the area percentage of the {100} crystal orientation, which is the structural element, with a tolerance of 15°.

[0036] As shown in Table 1, by using an Fe-Co alloy material with composite additions of Ti, Ni, and V as material components and reduced Cr, and by performing annealing at a soaking temperature of 800°C or higher before the final cold working, it was possible to obtain a soft magnetic material with a low Co content that exhibits a high magnetic flux density, particularly for electrical steel sheets, and a high magnetic flux density and low loss comparable to that of Permendur. [Examples]

[0037] Alloy A (containing Co: 20.0 wt%, Ti: 1.5 wt%, Ni: 1.9 wt%, and V: 2.0 wt%, with Cr reduced to less than 0.1 wt%, the remaining 74.6 wt being Fe) and Alloy B (containing Co: 20.4 wt%, V: 2.0 wt%, and Cr: 0.9 wt%, the remaining 76.7 wt being Fe) were melted in a vacuum induction furnace and cast into 1-ton steel ingots. The resulting steel ingots were divided, hot-forged at 1120°C, and then hot-rolled at 1120°C to produce hot-rolled coils of 3.0 mm thickness. Subsequently, the hot-rolled materials were subjected to a heat treatment before final cold working under the conditions shown in Table 2, with a soaking time of 2 minutes. Furthermore, after removing scale by shot blasting and pickling, the material was cold-rolled to obtain a final cold-rolled sheet with a thickness of 0.15 mm. Subsequently, a final magnetic annealing was performed, which involved holding the sheet at 900°C for 3 hours in a hydrogen atmosphere.

[0038] A 30mm x 120mm cut sheet sample was taken from the steel sheet after the final magnetic annealing, and the magnetic flux density (DC H=5000A / m) and iron loss (Bm=1.5T f=1kHz) were measured using a single-sheet measuring instrument. The measured values ​​are shown in Table 2. The measured values ​​are the average values ​​in the rolling direction and the direction perpendicular to the rolling direction. To investigate the crystal orientation, the surface was pre-treated by electrolytic polishing to a mirror finish. Then, approximately 5000 crystal orientations were analyzed using SEM (Scanning Electron Microscope)-EBSD (Backscattered Electron Diffraction), and the results were determined to be ND / / <100> Table 2 shows the area percentage of the {100} crystal orientation, which is the structural element, with a tolerance of 15°.

[0039] [Table 2]

[0040] As shown in Table 2, by using an Fe-Co alloy material with composite additions of Ti, Ni, and V as material components and reduced Cr, and further performing heat treatment before the final cold working at a soaking temperature of 800°C or higher, it was possible to obtain a soft magnetic material with a low Co content that exhibits a high magnetic flux density, particularly for electrical steel sheets, and a high magnetic flux density and low loss comparable to that of Permendur.

Claims

1. An Fe-Co-based soft magnetic material containing Co: 10.0-40.0 wt%, Ti: 0.2-3.0 wt%, Ni: 0.1-3.0 wt%, V: 0.1-3.0 wt%, and Fe: 51.0-89.6 wt%, with a Cr content of less than 0.5 wt%, and the content of elements other than Co, Ti, Ni, V, Fe, and Cr being 9.0 wt% or less.

2. The Fe-Co-based soft magnetic material according to claim 1, comprising C: 0.01 wt% or less, B: 0.01 wt% or less, Si: 3.0 wt% or less, Al: 2.0 wt% or less, Mn: 2.0 wt% or less, Nb: 1.0 wt% or less, Zr: 1.0 wt% or less, and Mo: 1.0 wt% or less, in a total content of 9.0 wt% or less, by one or a combination of two or more of these elements.

3. The Fe-Co-based soft magnetic material according to claim 1 or 2, wherein the area ratio of the {100} crystal orientation is 25% or more, with an allowable range of 15°.

4. A method for producing an Fe-Co soft magnetic material, comprising melting an alloy containing 10.0 to 40.0 wt% Co, 0.2 to 3.0 wt% Ti, 0.1 to 3.0 wt% Ni, 0.1 to 3.0 wt% V, and 51.0 to 89.6 wt% Fe, with a Cr content of less than 0.5 wt%, and the content of elements other than Co, Ti, Ni, V, Fe, and Cr being 9.0 wt% or less, and then sequentially performing casting, hot working, cold working, and final magnetic annealing, characterized in that a heat treatment at a soaking temperature of 800°C or higher is performed after the hot working and before the final cold working.

5. The method for producing an Fe-Co-based soft magnetic material according to claim 4, wherein the alloy contains C: 0.01 wt% or less, B: 0.01 wt% or less, Si: 3.0 wt% or less, Al: 2.0 wt% or less, Mn: 2.0 wt% or less, Nb: 1.0 wt% or less, Zr: 1.0 wt% or less, and Mo: 1.0 wt% or less, in a total content of 9.0 wt% or less, by one or a combination of two or more of these.

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