阅读说明：本技术 一种高饱和磁感高磁导率铁基软磁材料及其制备方法 (High-saturation-magnetic-induction high-permeability iron-based soft magnetic material and preparation method thereof ) 是由 薛佳宁 李重阳 徐明舟 杨帆 张�荣 李振瑞 于 2021-10-08 设计创作，主要内容包括：本发明公开了一种高饱和磁感高磁导率铁基软磁材料及其制备方法,高饱和磁感高磁导率铁基软磁材料含有以下组分：0-5.0wt％Co,2.0-6.0wt％Si,0-4.0wt％Cr,0-2.0wt％Mo,0-2.0wt％Al,0-0.06wt％C,余量为Fe；制备方法包括以下步骤：S1、称取上述原料；S2、将称取的原料完全熔化并浇铸为合金铸锭；S3、将合金铸锭在900-1200℃下进行锻造加工,得到热加工合金型材；锻造比不低于3:1；S4、将热加工合金型材在900-1100℃下热轧,获得冷带坯；S5、将冷带坯冷加工至冷带半成品,进行连续退火处理；S6、连续退火后继续冷加工得到高饱和磁感高磁导率铁基软磁材料。本发明公开的高饱和磁感高磁导率铁基软磁材料有高饱和磁感、高磁导率、低矫顽力、高电阻率、低密度等优点,成本低廉且加工性能好,应用前景广泛。(The invention discloses a high-saturation-magnetic-induction high-permeability iron-based soft magnetic material and a preparation method thereof, wherein the high-saturation-magnetic-induction high-permeability iron-based soft magnetic material comprises the following components: 0-5.0 wt% of Co, 2.0-6.0 wt% of Si, 0-4.0 wt% of Cr, 0-2.0 wt% of Mo, 0-2.0 wt% of Al, 0-0.06 wt% of C and the balance of Fe; the preparation method comprises the following steps: s1, weighing the raw materials; s2, completely melting the weighed raw materials and casting the raw materials into an alloy ingot; s3, forging the alloy ingot at the temperature of 900-1200 ℃ to obtain a hot-working alloy section; the forging ratio is not less than 3: 1; s4, hot rolling the hot-processed alloy section at 900-1100 ℃ to obtain a cold strip blank; s5, cold-working the cold strip blank to a cold strip semi-finished product, and carrying out continuous annealing treatment; and S6, continuously performing cold working after continuous annealing to obtain the iron-based soft magnetic material with high saturation magnetic induction and high magnetic permeability. The high-saturation-magnetic-induction high-permeability iron-based soft magnetic material disclosed by the invention has the advantages of high saturation magnetic induction, high magnetic permeability, low coercive force, high resistivity, low density and the like, and is low in cost, good in processability and wide in application prospect.)

1. The iron-based soft magnetic material with high saturation magnetic induction and high magnetic permeability is characterized by comprising the following components in percentage by mass:

0-5.0 wt% of Co, 2.0-6.0 wt% of Si, 0-4.0 wt% of Cr, 0-2.0 wt% of Mo, 0-2.0 wt% of Al, 0-0.06 wt% of C and the balance of Fe.

2. The iron-based soft magnetic material with high saturation magnetic induction and high magnetic permeability according to claim 1, wherein the sum of the mass percentages of Al and Si is greater than or equal to 3.0 wt%.

3. The iron-based soft magnetic material with high saturation induction and high permeability according to claim 1, wherein the sum of the mass percentages of Co and Cr is less than or equal to 6.0 wt%.

4. The iron-based soft magnetic material with high saturation magnetic induction and high magnetic permeability according to claim 1 is characterized by comprising the following components in percentage by mass:

2.0-4.0 wt% of Co, 2.5-4.0 wt% of Si, 1.0-3.0 wt% of Cr, 0-0.5 wt% of Mo, 0-2.0 wt% of Al, 0-0.03 wt% of C and the balance of Fe.

5. The iron-based soft magnetic material with high saturation magnetic induction and high permeability according to claim 1, wherein the iron-based soft magnetic material with high saturation magnetic induction and high permeability has saturation magnetic induction of not less than 2.0T and resistivity of not less than 0.55 x 10^-6Ω·m。

6. The iron-based soft magnetic material with high saturation induction and high permeability according to claim 1, wherein the iron-based soft magnetic material with high saturation induction and high permeability is a single alpha phase structure.

7. The iron-based soft magnetic material with high saturation induction and high permeability according to claim 1, wherein the density of the iron-based soft magnetic material with high saturation induction and high permeability is less than or equal to 7.7g/cm³。

8. A method for preparing a high saturation induction and high permeability iron-based soft magnetic material according to claim 1, comprising the steps of:

s1, weighing the following raw materials in percentage by mass:

0-5.0 wt% of Co, 2.0-6.0 wt% of Si, 0-4.0 wt% of Cr, 0-2.0 wt% of Mo, 0-2.0 wt% of Al, 0-0.06 wt% of C and the balance of Fe;

s2, mixing all the raw materials weighed in the S1, completely melting the raw materials, and casting the mixture into an alloy ingot;

s3, forging the alloy ingot to obtain a hot-working alloy section; the heating temperature of the forging processing is 900-1200 ℃; the forging ratio of the forging processing is more than or equal to 3: 1;

s4, carrying out hot rolling on the hot-processed alloy section to obtain a cold strip blank; the heating temperature during hot rolling is 900-1100 ℃;

s5, cold-working the cold strip blank to a cold strip semi-finished product, and then carrying out continuous annealing treatment; the treatment temperature of the continuous annealing treatment is 800-1100 ℃, and the annealing atmosphere is H₂The cold belt semi-finished product is subjected to continuous annealing treatment at a belt travelling speed of 0.5-2.0 m/min;

s6, continuously performing cold machining on the cold strip semi-finished product subjected to the continuous annealing treatment to obtain the high-saturation-magnetic-induction high-permeability iron-based soft magnetic material; compared with the cold belt semi-finished product, the deformation of the high-saturation-magnetic-induction high-permeability iron-based soft magnetic material is 50-98%.

9. The method according to claim 8, further comprising a step S7, which is specifically:

and carrying out heat treatment on the iron-based soft magnetic material with high saturation magnetic induction and high magnetic permeability, wherein the heat treatment temperature range is 850-1150 ℃, and the heat preservation time is 2-8 h.

10. The preparation method of claim 9, wherein the maximum permeability of the iron-based soft magnetic material with high saturation magnetic induction and high permeability after heat treatment is more than or equal to 15.0mH/m, and the coercive force is less than or equal to 30A/m.

Technical Field

The invention relates to the field of materials, in particular to an iron-based soft magnetic material with high saturation magnetic induction and high magnetic permeability and a preparation method thereof.

Background

In recent years, the design requirements of light markets such as military and civil unmanned aerial vehicles, traction transformers, light medical equipment and the like on electronic devices are continuously improved, the electronic devices are rapidly developed towards light weight, miniaturization and high efficiency, and the soft magnetic materials applied to the devices are required to have excellent performances such as high saturation magnetic induction, high magnetic conductivity, low loss, light weight and the like.

At present, the traditional crystalline state soft magnetic materials which are widely applied are mainly divided into electrician pure iron, silicon steel, Fe-Ni alloy, Fe-Co alloy, soft magnetic ferrite, amorphous soft magnetic alloy and the like. The advantages and the application range of each series of soft magnetic alloys are as follows:

electrical pure iron: it features high saturation magnetic induction, low cost and high machinability. However, since electrical pure iron has low resistivity and large eddy current loss under an alternating magnetic field, it is generally not suitable for use under ac magnetization conditions. The magnetic flux-cored wire is mainly applied to direct current magnetization occasions, such as direct current motors, iron cores, magnetic conductors and the like.

Silicon steel: after adding silicon to pure iron, as the content of Si increases, the resistivity ρ increases significantly and the magnetocrystalline anisotropy constant K1 decreases, but the saturation induction decreases and the thermal conductivity decreases. And after the Si element is added, the alloy hardness is increased, the brittleness is increased, cold rolling is difficult when the Si content exceeds 3.5 wt%, and the elongation is almost zero when the Si content exceeds 5 wt%, so that the processing difficulty of the high-silicon steel is very high, and the industrial application is difficult. The silicon steel is mainly used for iron cores of motors, transformers, relays and the like.

Fe-Ni alloy: compared with other soft magnetic materials, the iron-nickel alloy has higher magnetic conductivity and lower coercive force under a weak magnetic field, has good processing performance, is sensitive to stress and has lower saturation magnetic induction (the saturation magnetic induction of the high-nickel alloy is basically about 0.7T). The method is suitable for devices operating in weak magnetic fields.

Fe-Co alloy: the iron-cobalt alloy has higher saturation magnetic induction than pure iron, and has higher magnetic permeability than other soft magnetic alloys under high magnetic induction, but the alloy is brittle at normal temperature, so that cold machining is difficult, the resistivity of the alloy is very low, the loss is large, and in addition, the Co element is expensive and the cost is very high. The alloy is suitable for use in strong magnetic field and is mainly used for making pole shoe, motor rotor or stator, electromagnet pole head, etc.

Soft magnetic ferrite: the magnetic material has high resistivity, low eddy current loss and low saturation magnetic induction, and is suitable for low-power high-frequency magnetic elements.

Amorphous soft magnetic alloy: it has no magnetocrystalline anisotropy, higher resistivity than crystalline alloy, insensitivity to stress, corrosion resistance and high strength. However, the amorphous material has the disadvantages that crystallization can occur at a lower temperature, and structural relaxation can occur at a lower temperature, so that the working temperature of the amorphous material is not more than 100-150 ℃ under the long-term use condition.

As can be seen from the above comparison, these conventional soft magnetic materials inevitably have short plates in some properties, which limits the range of applications of the materials. For example, Si added to silicon steel can increase resistivity and reduce iron loss, but also reduce saturation magnetic induction; Fe-Co alloy has high saturation magnetic induction, but has lower resistivity, expensive cost and poorer cold processing performance; Fe-Ni alloy in weak fieldThe magnetic material has higher magnetic conductivity and smaller loss of the soft magnetic ferrite, but the two materials are very easy to saturate under a stronger magnetic field, and the saturation magnetic induction is smaller (the saturation magnetic induction of the iron-nickel soft magnetic alloy is not more than 1.6T, and the saturation magnetic induction of the soft magnetic ferrite is not more than 0.5T), so that the magnetic material is not suitable for the application environment of a high-power strong magnetic field; the amorphous soft magnetic alloy has the characteristics of low coercive force, high magnetic conductivity, high resistivity and the like due to the absence of magnetocrystalline anisotropy, but the crystallization temperature of the amorphous material is low, the working temperature of the amorphous material is not more than 100-150 ℃, and the preparation technical requirement is high. In addition, the density of the mainstream soft magnetic alloys such as Fe-Co and Fe-Ni is high, usually exceeding 8.0g/cm³It is disadvantageous for weight reduction of the electronic device.

In summary, in order to solve the problems of the conventional soft magnetic materials, there is an urgent need to develop a soft magnetic material that has excellent properties such as high saturation magnetic induction, high magnetic permeability, low iron loss, light weight, etc., can be produced in large quantities under the existing conventional metallurgical technology and processing level, has low cost, and can meet the use requirements of the existing high-efficiency light market on the soft magnetic material.

Disclosure of Invention

Therefore, the embodiment of the invention provides an iron-based soft magnetic material with high saturation magnetic induction and high magnetic permeability and a preparation method thereof, so as to solve the problems in the prior art.

In order to achieve the above object, the embodiments of the present invention provide the following technical solutions:

in a first aspect, an embodiment of the present invention provides an iron-based soft magnetic material with high saturation magnetic induction and high magnetic permeability, which contains the following components by mass:

0-5.0 wt% of Co, 2.0-6.0 wt% of Si, 0-4.0 wt% of Cr, 0-2.0 wt% of Mo, 0-2.0 wt% of Al, 0-0.06 wt% of C and the balance of Fe.

Preferably, the sum of the mass percent of Al and Si is more than or equal to 3.0 wt%.

Preferably, the sum of the mass percentages of Co and Cr is less than or equal to 6.0 wt%.

Preferably, the composition comprises the following components in percentage by mass:

2.0-4.0 wt% of Co, 2.5-4.0 wt% of Si, 1.0-3.0 wt% of Cr, 0-0.5 wt% of Mo, 0-2.0 wt% of Al, 0-0.03 wt% of C and the balance of Fe.

Preferably, the saturation induction of the iron-based soft magnetic material with high saturation induction and high permeability is more than or equal to 2.0T, and the resistivity is more than or equal to 0.55 multiplied by 10^-6Ω·m。

Preferably, the high saturation induction and high permeability iron-based soft magnetic material is of a single alpha phase structure.

Preferably, the density of the iron-based soft magnetic material with high saturation magnetic induction and high magnetic permeability is less than or equal to 7.7g/cm³。

In a second aspect, an embodiment of the present invention provides a method for preparing the iron-based soft magnetic material with high saturation magnetic induction and high magnetic permeability, including the following steps:

s1, weighing the following raw materials in percentage by mass:

0-5.0 wt% of Co, 2.0-6.0 wt% of Si, 0-4.0 wt% of Cr, 0-2.0 wt% of Mo, 0-2.0 wt% of Al, 0-0.06 wt% of C and the balance of Fe;

s2, mixing all the raw materials in the S1, completely melting the raw materials, and casting the mixture into an alloy ingot;

s3, forging the alloy ingot to obtain a hot-working alloy section; the heating temperature for forging processing is 900-1200 ℃; the forging ratio of the forging processing is not less than 3: 1;

s4, hot rolling the hot-processed alloy section to obtain a cold strip blank; the heating temperature during hot rolling is 900-1100 ℃;

s5, cold working the cold strip blank to a cold strip semi-finished product at the temperature of 800-1100 ℃ in H₂Carrying out continuous annealing treatment on the cold belt semi-finished product at the speed of 0.5-2.0m/min in the atmosphere;

s6, continuously performing cold machining on the cold strip semi-finished product subjected to the continuous annealing treatment to obtain the iron-based soft magnetic material with high saturation magnetic induction and high magnetic permeability; compared with a cold belt semi-finished product, the high-saturation magnetic induction and high-permeability iron-based soft magnetic material has the deformation of 50-98%.

Preferably, the method further includes step S7, which is specifically:

and carrying out heat treatment on the iron-based soft magnetic material with high saturation magnetic induction and high magnetic permeability, wherein the heat treatment temperature range is 850-1150 ℃, and the heat preservation time is 2-8 h.

Preferably, the maximum magnetic permeability of the iron-based soft magnetic material with high saturation magnetic induction and high magnetic permeability after heat treatment is more than or equal to 15.0mH/m, and the coercive force is less than or equal to 30A/m.

Compared with the prior art, the invention has at least the following beneficial effects:

(1) according to the iron-based soft magnetic material with high saturation magnetic induction and high magnetic permeability provided by the embodiment of the invention, through accurately blending specific types and specific contents of alloy elements, a synergistic effect and a joint effect are generated between the alloy elements, so that the comprehensive performance of the soft magnetic material is remarkably improved, and particularly: the saturation magnetic induction is improved by adding Co element, the resistivity is improved by adding Cr, Si, Al, Mo and other elements, the density is reduced by adding Al and Si elements, and the large grain size which can have high magnetic conductivity and low coercive force after heat treatment is obtained by regulating the content of Co + Cr and Si + Al; the loss of the soft magnetic material is obviously reduced due to the high resistivity and low coercive force; by reasonably designing the element components, the soft magnetic material has good processing performance and low cost, and can be produced and applied on a large scale.

(2) The iron-based soft magnetic material with high saturation magnetic induction and high magnetic permeability provided by the embodiment of the invention has unique performance combination of high saturation magnetic induction, high magnetic permeability, low coercive force, high resistivity, low density and the like, and is suitable for efficient and light electronic devices working under a direct-current magnetic field.

Drawings

In order to more clearly illustrate the technical solution of the present invention, the drawings used in the description of the embodiments of the present invention will be briefly described below. It should be apparent that the drawings in the following description are merely exemplary, and that other drawings may be derived from the provided drawings by those of ordinary skill in the art without inventive effort.

The drawings are only for purposes of illustration and description, and are not intended to limit the scope of the invention, which is defined by the claims, which follow.

FIG. 1 is a metallographic picture of a material provided in example 1 of the present invention after heat treatment;

FIG. 2 is a metallographic picture of a material provided in example 5 of the present invention after heat treatment;

FIG. 3 is a metallographic photograph of the material provided in comparative example 3 after heat treatment;

FIG. 4 is a DSC curve of the materials provided in examples 3, 6 and comparative example 3 of the present invention;

fig. 5 is XRD patterns of the materials provided in examples 1 and 3 of the present invention before and after heat treatment.

Detailed Description

In order to make the objects, technical solutions and advantages of the present invention more apparent, the present invention is described in further detail below with reference to the accompanying drawings and embodiments. It should be understood that the specific embodiments described herein are merely illustrative of the invention and are not intended to limit the invention.

In the description of the present invention, the terms "comprises," "comprising," and any other variations thereof, are intended to cover a non-exclusive inclusion, such that a process, method, system, article, or apparatus that comprises a list of steps or elements is not necessarily limited to those steps or elements specifically listed, but may include other steps or elements not expressly listed or inherent to such process, method, article, or apparatus or additional steps or elements based on further optimization of the inventive concepts.

The mass percentages of the components of examples 1-7 and comparative examples 1-3 are shown in table 1 below.

TABLE 1-EXAMPLES 1-7 AND COMPARATIVE EXAMPLES 1-3 Each component mass percentage (unit: wt%)

The preparation of examples 1 to 7 is as follows:

s1, weighing the raw materials according to the mass percentage shown in the table 1;

the iron-based soft magnetic materials with high saturation magnetic induction and high magnetic permeability prepared in the embodiments 1-7 are all iron-based alloys, and the effect of adding a proper amount of Co element is to enable the materials to have higher saturation magnetic induction (more than or equal to 2.0T); in addition, the addition of Cr, Si, Al and Mo elements obviously improves the resistivity of the material, effectively reduces the loss and improves the use efficiency of the material; cr plays a role in improving the uniformity of the structure; mo plays a role in improving the plasticity of the alloy; compared with the existing soft magnetic alloy, the material provided by the embodiment of the invention has obviously reduced density due to the addition of low-density elements such as Si, Al and the like, and has good weight reduction effect when being applied to electronic devices;

in the soft magnetic materials provided in examples 2, 4, 6 and 7, the sum of the mass percentages of Al and Si is not less than 3.0 wt%, because, as determined by experiments, the addition of Al and Si elements can make the material have a larger grain size, so that the material obtains a higher magnetic permeability after heat treatment; the addition of Al and Si elements obviously increases the resistivity of the alloy, and the resistivity (10) within the range of the components of the invention is obtained by fitting according to experimental data^-6Omega m) is proportional to the Al and Si contents (wt%), and the proportionality coefficient is about 0.1; because the hysteresis loss of the soft magnetic material under the direct current or low-frequency alternating current magnetic field is dominant on the total power loss, and the hysteresis loss of the alloy is smaller due to the high resistivity and low coercive force, the efficiency of the alloy can be obviously improved when the alloy works under the direct current or low-frequency alternating current magnetic field; the sum of Al and Si contents in the alloy is preferably controlled to be not less than 3.0 wt%, if the sum of the Al and Si contents is less than 3.0 wt%, the grain size cannot be obviously lengthened after heat treatment, so that the coercive force is slightly larger, the magnetic permeability level is slightly lower than 15.0mH/m, the resistivity is lower, the material loss is slightly increased, and the working efficiency is slightly reduced;

in the soft magnetic materials provided in examples 1 to 7, the sum of the mass percentages of Co and Cr is not more than 6.0 wt%, because, as determined by experiments, Co and Cr elements have a grain refining effect and a certain inhibiting effect on grain growth during high-temperature heat treatment; in addition, the addition of excessive Cr has adverse effect on the saturation magnetic induction, so that the sum of the contents of Co and Cr is controlled to be 6.0 wt%, the higher saturation magnetic induction can be ensured, the fine grain effect of the Co and Cr can be inhibited, and the soft magnetic material with both high saturation magnetic induction and low coercive force can be obtained;

s2, melting the raw materials weighed in the S1, casting into 20kg of alloy cast ingot, and smelting by a vacuum induction smelting furnace, a vacuum arc furnace and a vacuum electroslag remelting technology, or by non-vacuum intermediate frequency smelting;

s3, forging the alloy cast ingot into a round bar with the diameter of 50mm to obtain a hot-working alloy section; the heating temperature for forging processing is 900-1200 ℃; the forging ratio of the forging processing is not less than 3: 1;

too low forging ratio can cause residual coarse as-cast structure, the uniformity of the structure cannot be ensured, the structure is difficult to crush and refine in the subsequent working procedures of hot rolling, cold working and the like, and the magnetic property is deteriorated; the over-sintering phenomenon can occur when the forging processing temperature is too high; the material can also be forged and processed into other round bars or square billets and other sectional materials with different sizes;

s4, hot rolling the hot-processed alloy section to a cold strip blank with the thickness of 6 mm; the heating temperature during hot rolling is 900-1100 ℃;

s5, performing cold processing on the cold strip blank to obtain a cold strip semi-finished product; carrying out continuous annealing treatment on the cold belt semi-finished product; the treatment temperature of the continuous annealing treatment is 800-1100 ℃, and the annealing atmosphere is H₂Atmosphere, the speed of the cold belt semi-finished product is 0.5-2.0 m/min;

s6, continuously performing cold machining on the continuously annealed cold strip semi-finished product to obtain the required iron-based soft magnetic material with high saturation magnetic induction and high magnetic permeability; the soft magnetic material is a thin strip with the thickness of 0.35mm, and the deformation amount of the soft magnetic material is 50-98% compared with that of a cold strip semi-finished product; the purposes of hot rolling and cold working are to refine grains and improve magnetic property;

s7, performing heat treatment on the iron-based soft magnetic material with high saturation magnetic induction and high magnetic permeability, wherein the heat treatment temperature range is 850-1150 ℃, and is 1100 ℃ specifically; the heat preservation time is 2-8h, specifically 5 h; the purpose of the heat treatment is to obtain excellent magnetic properties such as high magnetic permeability and low coercive force.

Comparative examples 1 to 3 were prepared in the same manner as in examples 1 to 7.

Next, a series of performance tests were performed on the materials provided in examples 1 to 7 and comparative examples 1 to 3, respectively, to illustrate the advantageous effects of the present invention.

Test 1

The grain sizes of the heat-treated materials provided in examples 1 and 5 and comparative example 3 were observed under an optical microscope, and their metallographic images are shown in fig. 1, 2 and 3, respectively. As can be seen from fig. 1-3, after heat treatment, the grains of examples 1 and 5 significantly grow, and the grain grades reach 0 grade and 00 grade, respectively; in contrast, in comparative example 3, since the sum of the contents of Co and Cr, which are fine crystalline elements, exceeds 6.0 wt%, and the content of Si, which is lower than the composition range of the present invention (2.0 to 6.0 wt%), the grain growth process is significantly suppressed and the grain size rating is only 6.0 at a high heat treatment temperature of 1100 deg.C, which results in the material provided in comparative example 3 not having high magnetic permeability and low coercive force level.

Test 2

The materials provided in examples 1-7 and comparative examples 1-3 were tested for performance data after heat treatment, respectively, as shown in table 2 below.

Table 2-performance data after heat treatment of the materials provided in examples 1-7 and comparative examples 1-3

Table 2 shows the magnetic induction (B) at 10000A/m magnetic field after heat treatment of the materials provided in examples 1 to 7 of the present invention and comparative examples 1 to 3_10000A/m) Performance data such as saturation induction (Bs), coercive force (Hc), maximum permeability (μm), resistivity (ρ), and alloy density (ρ).

As can be seen from the data in Table 2, the saturation induction of the materials provided in examples 1 to 7 of the present invention increases with the increase of Co content and decreases with the increase of Cr content, but within the composition range of the present invention, the saturation induction of the materials provided in examples 1 to 7 is 2.0T or more, more than that of the non-oriented silicon steel of comparative example 2, and more than that of the Fe-Ni alloy (the saturation induction is not more than 1.6T). Comparing the coercive force and the maximum permeability of the examples 1 to 7 and the comparative examples 1 to 3 of the present invention, it can be seen that although the Fe-Co alloy 1J27 (comparative example 2) has a high saturation induction, the coercive force thereof is as high as 273.2A/m, and the maximum permeability of the silicon steel (comparative example 1) and the Fe-Co alloy (comparative example 2) is not more than 10mH/m, while the materials provided by the examples 1 to 7 of the present invention achieve a large grain size with high permeability and low coercive force after heat treatment by designing and controlling the contents of Co + Cr and Si + Al, as shown in fig. 1 and 2, the materials have excellent combinations of high saturation induction, high resistivity and the like.

In addition, comparing the resistivity data of the inventive and comparative examples in Table 2, it can be seen that the materials of examples 1-7 all maintain high resistivity values due to the addition of Si, Al, Cr, etc., wherein the resistivity of examples 2, 4, 7 even reaches 0.70X 10^-6Omega · m or more. Whereas the electrical resistivity of the silicon steel in the comparative example was 0.48 × 10^-6Omega.m, while the resistivity of the Fe-Co alloy 1J27 is only 0.20X 10^-6Omega.m. The high resistivity makes the loss value of the alloy of the embodiment lower than that of the traditional Fe-Co alloy and silicon steel, and can effectively improve the working efficiency.

The density of the embodiment of the invention is not more than 7.7g/cm³In example 7, in which 1.0 wt% of Al element was contained, the density was reduced to 7.6g/cm³. Compared with the traditional Fe-Co alloy (more than or equal to 8.2 g/cm)³) Or Fe-Ni alloy (not less than 8.2 g/cm)³) Compared with the prior art, the materials provided by the embodiments 1 to 7 of the invention have good weight reduction effect when applied to electronic devices.

Test 3

DSC curves of the materials provided in examples 1 to 7 and comparative examples 1 to 3 were measured, respectively, wherein the DSC curves of example 3, example 6 and comparative example 3 are shown in fig. 4.

As can be seen from FIG. 4, in comparative example 3, since the Co + Cr content and the Si content are out of the design ranges of the components of the present invention, the alpha phase (ferrite) appears in the high temperature region around 900 ℃Whereas the beta phase (austenite) transformed, no transformation occurred in the DSC curves of example 3 and example 6. The phase transformation of comparative example 3 makes the heat treatment temperature of the alloy not too high, which may otherwise leave residual austenite in the alloy to deteriorate magnetic properties, while the lower heat treatment temperature does not significantly contribute to microstructure improvement, so that comparative example 3 does not have the excellent magnetic properties of examples 3 and 6.

Test 4

XRD patterns of the materials provided in examples 1 to 7 and comparative examples 1 to 3 before and after heat treatment were measured, respectively, wherein the XRD patterns of examples 1 and 3 are shown in fig. 5.

Comparing the characteristic peak in the spectral line of fig. 5 with the standard PDF card, it can be seen that the materials provided in examples 1 and 3 are all single-phase structures, and the phases of the materials before and after heat treatment do not change, and the phases of the materials correspond to the alpha phase (ferrite).

Test 5

The heat-treated materials provided in examples 1-7 and comparative examples 1-3 were tested for core loss (P) at 1.0T at 50Hz_1.0/50) The test results of example 1, example 3, example 6 and comparative example 2 are shown in table 3 below.

Table 3-core loss of heat treated materials provided in examples 1, 3, 6 and comparative example 2

	Example 1	Example 3	Example 6	Comparative example 2
					P1.0/50(W/kg)	1.3	1.6	1.6	6.3

As can be seen from Table 3, the loss value at 50Hz is remarkably reduced compared with the Fe-Co alloy 1J27 (comparative example 2) because of the high resistivity and low coercive force of the examples of the invention.

All the technical features of the above embodiments can be combined arbitrarily, and for simplicity of description, all possible combinations of the technical features of the above embodiments are not described; these examples, which are not explicitly described, should be considered to be within the scope of the present description.

The present invention has been described in considerable detail by the general description and the specific examples given above. It should be noted that it is obvious that several variations and modifications can be made to these specific embodiments without departing from the inventive concept, which falls within the scope of protection of the present application. Therefore, the protection scope of the present patent shall be subject to the appended claims.