JP2001026846A - Composite magnetic member, production of ferromagnetic part in composite magnetic member and formation of nonmagnetic part in composite magnetic member - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a composite magnetic member of a single material combining a ferromagnetic part and a nonmagnetic part, in which the ferromagnetic part has soft magnetism more excellent than that of the conventional member, and the nonmagnetic part has stable characteristics equal to those of the conventional member, to provide a method for producing the ferromagnetic part in the member and to provide a method for forming the nonmagnetic part. SOLUTION: This composite magnetic member is composed of Fe-Cr-C base alloy steel contg. 0.1 to 7.0% Si or Si and Al by 0.1 to 12.0% in total and has a ferromagnetic part in which the number of carbides having >=0.1 μm grain size is controlled to <=50 pieces in the area of 100 μm2, also the ratio of the number of the carbides having >=1.0 μm grain size to the number of the carbides to >=15%, and the maximum magnetic permeability to >=400 and a nonmagnetic part whose magnetic permeability is controlled to <=2.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a composite magnetic member having both a ferromagnetic portion and a non-magnetic portion in a single material, which can be applied to an industrial product using a magnetic circuit such as a motor.
And a method of manufacturing the same.

[0002]

2. Description of the Related Art Conventionally, in industrial products requiring a magnetic circuit, such as a rotor of a motor and a magnetic scale, a part of a ferromagnetic material (generally, a soft magnetic material) is required to form a magnetic circuit. Is provided with a non-magnetic portion. As a method of providing a non-magnetic portion on a part of a ferromagnetic material, a method of brazing a ferromagnetic component and a non-magnetic component or laser welding has been used. In contrast to the method of joining these dissimilar materials, the present inventors have used a single material and formed a composite magnetic member having a ferromagnetic portion and a non-magnetic portion provided by cold working or heat treatment on the single material. is suggesting. The use of such a single composite magnetic member makes it possible to secure the airtightness, prevent damage due to vibration, etc., as well as to ensure reliability and reduce costs. Will be better than

For example, Japanese Patent Application Laid-Open No.
No. 157802 discloses a martensitic stainless steel containing 0.5 to 4.0% Ni as a composite magnetic member suitable for an oil control device of an automobile. This proposal proposes the addition of an appropriate amount of Ni to a martensitic stainless steel in an annealed state consisting of ferrite and carbide, which can provide ferromagnetic properties with a maximum magnetic permeability of 200 or more, by adding an appropriate amount of Ni. The austenite in the non-magnetic portion having a magnetic permeability of 2 or less obtained by heating and cooling a part of the stainless steel is stabilized, and the Ms point (the temperature at which austenite starts to become martensite) is reduced by -3.
It is disclosed that the temperature can be reduced to 0 ° C. or less.

Further, Japanese Patent Application Laid-Open No.
No. 228004 discloses a composite magnetic material used for a magnetic scale or the like, in which Cr is 10 to 16% and C is 0.35 to 0.
By adding Mn: more than 2% to 7% or less and N: 0.01 to 0.05% to a C-Cr-Fe-based alloy containing 75% and having ferromagnetic properties with a maximum magnetic permeability of 200 or more. It discloses that the residual austenite having a magnetic permeability of 2 or less obtained by cooling after heating can be stabilized and the Ms point can be lowered to -10 ° C or less. These proposals consist of a ferromagnetic part having a maximum magnetic permeability of 200 or more in a single material and a magnetic permeability of 2 or more.
This is excellent in that a stable nonmagnetic portion having a low Ms point can be obtained below.

[0005]

SUMMARY OF THE INVENTION The above-mentioned Japanese Patent Application Laid-Open No. 9-1 is disclosed.
The composite magnetic members disclosed in Japanese Patent No. 57802 and JP-A-9-228004 are based on martensitic stainless steel having ferromagnetic properties, and to which an appropriate amount of an austenite-forming element such as Ni or Mn is added. It is proposed that a non-magnetic part stable at a low temperature can be formed in a part of a ferromagnetic material by performing a partial solution treatment, and a ferromagnetic material having a maximum magnetic permeability of 200 μm or more in a single material is proposed. It can be said that this is an excellent technique in that it can have both a non-magnetic part and a stable non-magnetic part having a magnetic permeability of μ2 or less.

According to the study of the present inventors, among composite magnetic members used as a magnetic circuit, soft magnetic characteristics (hereinafter referred to as soft magnetic characteristics) superior to conventional members, such as a motor rotor, are provided. That is, a high maximum magnetic permeability and a low coercive force may be required. On the other hand, in the above two proposals, there is a limit to the soft magnetism obtained by the ferromagnetic portion.

That is, the ferromagnetic portion of the composite magnetic member made of Fe—Cr—C alloy steel has a microstructure in which carbides are precipitated on a matrix base of ferrite. In order to obtain a high maximum magnetic permeability, which is one of the indices shown, it is necessary to minimize the precipitates inside the member and create a state in which domain wall movement is easy, and among them, carbide having a particle diameter of 0.1 μm or more is required. The presence of a large number of the barriers particularly hinders the movement of the domain wall, and there has been a limit to the maximum magnetic permeability that can be obtained in the ferromagnetic portion.

In order to obtain a low coercive force, which is another index showing excellent soft magnetism, it is effective to increase the crystal grains of the matrix. However, when a large number of carbides are present, the growth of ferrite crystal grains as a matrix is suppressed, so that the ferrite grain size becomes extremely fine, which is a factor that hinders a decrease in the coercive force obtained in the ferromagnetic portion. Was.

SUMMARY OF THE INVENTION An object of the present invention is to solve the above-mentioned problems and, among composite magnetic members having both a ferromagnetic portion and a non-magnetic portion in a single material, have a ferromagnetic portion having soft magnetism superior to conventional members. Another object of the present invention is to provide a composite magnetic member having a non-magnetic portion having stable characteristics which is not different from that of a conventional member, a method of manufacturing a ferromagnetic portion of the member, and a method of forming a non-magnetic portion.

[0010]

Means for Solving the Problems As a method of increasing the soft magnetism of the ferromagnetic portion of the composite magnetic member, the present inventors have added Si, which has not been positively added so far, In addition, attention was paid to the complex addition of Al, which exhibits an effect very similar to that of Si, with Si. The composite magnetic member of Japanese Patent Application Laid-Open No. 9-157802 proposed by the present inventors contains one or more of Si, Mn, and Al as a deoxidizing agent in a total of 2.0% or less. . This proposal is Si,
Elements such as Mn and Al were expected only to remove oxygen in molten steel as a deoxidizing agent, and it was thought that these elements should not remain in the member. However, according to further studies by the present inventors, in a composite magnetic member made of an Fe-Cr-C-based alloy steel, Si is actively added to the alloy steel as a material in a range of 0.1 to 7.0%. It has been found that the soft magnetism of the ferromagnetic portion is remarkably improved by adding Si or Al positively in a total range of 0.1 to 12.0%.

Subsequently, the present inventors investigated in detail the effect of Si addition on the microstructure of the ferromagnetic portion and the effect of (Si, Al) composite addition. As a result, the ferromagnetic part is irrespective of whether or not these elements are added (ferrite + carbide)
As for the main metal structure, it has been found that when Si is added, the number of carbides per unit area decreases and the individual carbides increase, and the crystal grain size of ferrite grains increases. In addition, it was found that when Si and Al were added in combination, the change in the microstructure described above became more remarkable, and the present invention was reached.

That is, according to the present invention, Si is contained in an amount of 0.1 to 7.0.
% Or a Fe-Cr-C alloy steel containing 0.1 to 12.0% in total of Si and Al, and a particle diameter of 0.1 μm
The maximum permeability 4 in which the number of carbides is 50 or less in an area of 100 μm ² and the ratio of the number of carbides having a particle size of 1.0 μm or more to the number of carbides is adjusted to 15% or more.
This is a composite magnetic member having a ferromagnetic portion of 00 or more and a non-magnetic portion of a magnetic permeability of 2 or less.

[0013] The present invention also relates to the present invention, wherein the content of Si is 0.1 to 7.0%;
Alternatively, it is made of a Fe—Cr—C alloy steel containing 0.1 to 12.0% in total of Si and Al, and is adjusted to a coarser grain including a crystal grain size number of 14, and has a coercive force of 1000 A /
This is a composite magnetic member having a ferromagnetic portion of m or less and a non-magnetic portion of a magnetic permeability of 2 or less.

Preferably, when the crystal orientation is measured by X-rays from the surface side, the ferrite (200) and the ferrite (11
0) is a composite magnetic member having a ferromagnetic portion having an X-ray integrated intensity ratio of 6 or more, and more preferably, the electric resistivity is 0.1.
This is a composite magnetic member having a ferromagnetic portion of 7 μΩm or more.

The preferred chemical composition of the present invention is Ni equivalent (=% Ni + 30 ×% C + 0.5 ×% Mn + 30 ×%
N) is a composite magnetic member made of an alloy steel with 10.0 to 25.0%.

When Si is added alone, the preferred composition is as follows: C: 0.30 to 0.80% by weight;
0 to 25.0%, Si; 0.1 to 7.0%, Ni: 0.
1 to 4.0%, Mn; 0.1 to 2.0%, N: 0.01
0.10%, the balance being a composite magnetic member made of an alloy steel having a composition of Fe and unavoidable impurities.
This is a composite magnetic member containing 0.3 to 3.5% by weight of Si. When Si is added alone, Al may be contained in a range of less than 0.05% as a deoxidizing element.

In the case where Si and Al are added in combination, the preferred composition is as follows: C: 0.30 to 0.80% by weight, Cr: 1
0.0-25.0%, Si; 0.05-7.0%, A
l; 0.05-5.0%, Ni: 0.1-4.0%, M
n: 0.1 to 2.0%, N: 0.01 to 0.10%, the balance being a composite magnetic member made of an alloy steel having a composition of Fe and unavoidable impurities. A composite magnetic member containing 0.3 to 3.5% by weight.

Further, in the production method of the present invention, the content of Si is 0.1 to 7.0% or the total content of Si and Al is 0.1 to 7.0%.
Fe-Cr-C alloy steel containing 12.0%
After hot working at a temperature of 00 ° C. or less, the steel is annealed at least once at an A3 transformation point or less to reduce the number of carbides having a grain size of 0.1 μm or more to 1
50% or less in the area of 00 μm ² and the ratio of the number of carbides having a particle size of 1.0 μm or more to the number of carbides is 15%
This is a method for manufacturing a ferromagnetic portion of a composite magnetic member for obtaining a ferromagnetic material adjusted as described above.

As a method of forming the non-magnetic portion of the member of the present invention, a part of the ferromagnetic material obtained by
After heating in the temperature range from 0 ° C to the melting temperature, it is quenched,
This is a method for forming a nonmagnetic portion of a composite magnetic member to be demagnetized.

[0020]

DETAILED DESCRIPTION OF THE INVENTION As noted above, the present invention has two important features. The first feature is that to increase the soft magnetism of the ferromagnetic part of the composite magnetic member, Si, which has been regarded only as a deoxidizer, was actively added to the alloy steel used as the material of the composite magnetic member. It was done. The second feature is that Al having the same effect as Si is added in combination with Si. By adding Si or by adding Si and Al in combination, Fe—Cr
In the ferromagnetic portion of the composite magnetic member made of -C alloy steel, the number of carbides having a particle diameter of 0.1 μm or more, the ratio of the number of carbides having a particle diameter of 1.0 μm or more to the number of carbides, and the crystal grain size of ferrite grains And the crystal orientation were adjusted to specific ranges, respectively, and excellent soft magnetism was obtained.
i and Al are important elements of the present invention added to the alloy material to improve soft magnetism in the ferromagnetic portion of the composite magnetic member.

First, the effect of adding Si to the alloy steel as the material of the composite magnetic member, which is the first feature of the present invention, will be described in detail. The present inventors have found that adding Si to the Fe—Cr—C-based alloy, which is the material of the composite magnetic member, requires 4%.
Has been found to have two effects, which will be described in turn. The present inventors have proposed F, which is a material of the composite magnetic member.
For the e-Cr-C-based alloy, among various additional elements, Si
Has for the first time found an effect of growing individual carbides, an effect of reducing the number of carbides, and an effect of increasing the size of ferrite crystal grains in the matrix, and dramatically improving the magnetic properties of the ferromagnetic portion. Then, it has been confirmed by EDX surface analysis that Si in the ferromagnetic portion is present not in the carbide but in the ferrite of the matrix. However, since Si is present in the matrix, the mechanism by which the carbides become larger, or by adding Si, the carbides become larger and less, so the ferrite grains become larger, or conversely, the ferrite grains become larger, so the carbides become larger. The cause of the change in the metal structure due to the addition of Si, such as whether it is large and small, is unknown and is currently being clarified.

Next, the relationship between the amount of added Si, the carbide form of the ferromagnetic portion, and the maximum magnetic permeability will be specifically described. Here, A
1 is contained only as about 0.002% as a deoxidizing element, and is not substantially added. Among the experiments performed by the present inventors, Fe-17.5% Cr-0.5 by weight%.
% C-2.0% Ni as an example, a composite magnetic member made of an alloy steel containing Si as a main component is used.
When only 0.2% is contained and substantially not added, the number of carbides having a particle diameter of 0.1 μm or more in the ferromagnetic portion is 66 in an area of 100 μm ^2, of which 1 μm
The above carbide is 1 to the total number of carbides measured.
There are eight of 2.1%, and the maximum magnetic permeability is 315. The ferromagnetic portion of the composite magnetic member made of alloy steel obtained by adding 0.44% by weight of Si to this alloy steel has a grain size of 0.1%.
The number of carbides of μm or more is 45 in an area of 100 μm ^2.
The number of carbides having a particle diameter of 1 μm or more is 8 at 17.7% of the total number of carbides measured, and the maximum magnetic permeability increases to 436.

When the alloy steel to which 0.91% by weight of Si is added is used as the material, the number of carbides having a grain size of 0.1 μm or more in the ferromagnetic portion is up to 36 in an area of 100 μm ^2. Among them, the number of carbides having a particle diameter of 1 μm or more becomes 9 of 25.0% of the total number of carbides measured, and the maximum magnetic permeability increases to 628. Further, when 1.94% by weight of Si is added, the particle size is 0.1%.
The number of carbides of μm or more is reduced to 24 in an area of 100 μm ^{2, and} the number of carbides of 1 μm or more in particle size is 9 of 37.5% of the total number of carbides measured,
The maximum permeability rises to 920. By adding Si in this manner, the grain size in the ferromagnetic portion is reduced to 0.1.
It can be seen that the number of carbides having a particle diameter of 1 μm or more increases as the number of carbides having a particle diameter of 1 μm or more decreases. Further, it was found that a high maximum magnetic permeability was obtained with the change in the carbide form. The above is the first effect of adding Si to the Fe—Cr—C alloy steel used as the material of the composite magnetic material member.

Next, the relationship between the amount of added Si, the crystal grain size of ferrite grains in the ferromagnetic portion, and the coercive force will be specifically described. weight%
In the case of a composite magnetic member made of an alloy steel containing Fe-17.5% Cr-0.5% C-2.0% Ni as a main component, for example, 0.02% of Si is used as a deoxidizing agent. When only ferromagnetic particles are contained and substantially not added, the size of the ferrite grains in the ferromagnetic portion is a crystal grain size number of 16.0, and the coercive force is 1220 A / m. 0.4% by weight to this alloy steel
In the ferromagnetic portion of the composite magnetic member made of alloy steel to which 4% Si is added, the size of ferrite grains increases to a crystal grain size number of 13.5, the coercive force decreases to 980 A / m, and the soft magnetic property increases. (Soft magnetic characteristics) can be improved. Also,
When an alloy steel to which 0.91% by weight of Si is added is used as a material, the crystal grain number of the ferromagnetic portion is 13.0, and the coercive force is 700 A / m. Furthermore, 1.94% of S by weight%
When i was added, the size of the ferrite grains increased to a grain size number of 12.0, and the coercive force was 490 A / m
And the soft magnetism (soft magnetic properties) can be further improved. It can be seen that the addition of Si increases the size of the ferrite grains, thereby decreasing the coercive force and improving the soft magnetism (soft magnetic properties). The above is the second effect of adding Si to the Fe-Cr-C alloy steel used as the material of the composite magnetic material member.

Further, when the composite magnetic member is used as a magnetic circuit component, it is often required that the residual magnetic flux density of the ferromagnetic portion is high and the squareness of the hysteresis curve is good. The good squareness of the hysteresis curve means that
This means that the magnetic loss of the material is small and the on / off characteristics when a positive magnetic field-reverse magnetic field is continuously applied, that is, the magnetic responsiveness is good. In general, it is known that the squareness of the hysteresis curve is related to the crystal orientation of the magnetic material. The present inventors can control the crystal orientation of ferrite grains, which are the matrix of the ferromagnetic portion, by adding Si to the Fe—Cr—C-based alloy that is the material of the composite magnetic member. It has been found that there is a close relationship between densities.

That is, when Fe—Cr—C alloy steel is used as a material, changes in the integrated strength and residual magnetic flux density of the ferrite phase (200) whose crystal orientation is measured by X-rays from the surface of the rolling plane, which is the surface side, are shown. When the influence of the addition of Si is in good agreement, that is, when the degree of integration of (200) viewed from the surface side is increased by adding Si, the residual magnetic flux density can be increased. The mechanism by which the crystal orientation can be controlled by the addition of Si is not known, and is currently being elucidated.

The relationship between the amount of added Si, the crystal orientation of ferrite grains in the ferromagnetic portion, and the residual magnetic flux density will be specifically described. In this case, the crystal orientation refers to the ferrite (110) (200) (2) on the rolling plane side, which is the surface side measured by X-ray diffraction.
11) is a measurement of the integrated intensity ratio. F in weight%
e-17.5% Cr-0.5% C-2.0% As an example of a composite magnetic member made of an alloy steel containing Ni as a main component, only 0.02% is used with Si as a deoxidizing agent. When it is contained and substantially not added, the crystal orientation of ferrite grains in the ferromagnetic part is (110) 9.2%, (20)
0) was 39.1%, (211) was 51.7%, (20)
0) and (110) integrated intensity ratio (200) / (110)
Is 4.3, and the residual magnetic flux density at this time is 0.73
T (Tesla). This alloy steel contains Si in an amount of 0.
In the ferromagnetic portion of the composite magnetic member made of an alloy steel to which 44% was added, the crystal orientation of ferrite grains was (110) 6.0%, (200) 36.6%, and (211) 5%.
At 7.5%, the value of (200) / (110) becomes 6.1, and the residual magnetic flux density increases to 0.87T.

When 0.91% by weight of Si is added, the crystal orientation of ferrite grains in the ferromagnetic portion is (1).
10) is 3.5%, (200) is 47.4%, (21)
1) is 49.1%, and the value of (200) / (110) is 1
3.5, and the residual magnetic flux density increases to 0.94T. Further, in the ferromagnetic portion of the composite magnetic member made of an alloy steel to which 1.44% by weight of Si is added, the crystal orientation of ferrite grains is (110) 2.0% and (200) 4%.
4.4%, (211) is 53.6%, (200) / (1
The value of 10) is 22.2 and the residual magnetic flux density is 0.98
It becomes T. By adding Si in this manner, the crystal orientation of the ferrite grains becomes an orientation in which (200) / (110) increases when measured from the rolled plane serving as the surface, and the residual magnetic flux density increases accordingly. You can see that. The above is the description of Fe-Cr-
This is the third effect of adding Si to the C-based alloy steel. In addition,
When the measurement surface by X-ray diffraction has a curved shape, the surface on the side processed into a flat surface by the rolling roll on the surface side may be measured.

The addition of Si not only increases the soft magnetic surface of the ferromagnetic portion described above, but also increases the electrical resistivity of the ferromagnetic portion, that is, when the soft magnetic material is used in an alternating magnetic field. The effect of improving the magnetic responsiveness is that the eddy current loss can be reduced by increasing the electrical resistivity of the material, and the above is the effect of Fe-Cr- This is the fourth effect of adding Si to the C-based alloy steel.

The second important feature of the present invention is that Si
In addition, attention is paid to Al, which is an element having the same effect as that described above, and it is added in combination with Si. By adding Si and Al in combination, the effect of adjusting the carbide morphology and crystal grain size described above is further enhanced than when only Si is added, and the soft magnetism of the ferromagnetic portion is further improved. In this case, S
It has been confirmed by EDX that both i and Al exist not in carbide but in ferrite of the matrix.

Specifically, when 0.91% of Si is added by weight% and Al is contained only as 0.002% as a deoxidizing agent and is not substantially added, as described above, the particles in the ferromagnetic portion are not added. The number of carbides having a diameter of 0.1 μm or more is 36 in an area of 100 μm ^{2, and} the number of carbides having a particle diameter of 1 μm or more is 25.0% of the total number of carbides, and the maximum magnetic permeability is 628. is there. The grain size number of the ferromagnetic portion is 1
3.0, the coercive force is 700 A / m. Further, when 1.94% by weight of Si was added, the size of the ferrite grains was 12.0 and the coercive force was 490 A / m.
It is. Here, 0.95% of Si and 0.98% of Al are added as a composite by weight, and the total amount of Si and Al is 1.93.
% Of alloy steel, the number of carbides having a grain size of 0.1 μm or more in the ferromagnetic portion is 25 in an area of 100 μm ^2, of which the carbides having a grain size of 1 μm or more are based on the total number of carbides. There are 8 of 32.0%, and the maximum magnetic permeability increases to 1120. Further, the crystal grains of the ferromagnetic portion increase to a particle size number of 9.5, and the coercive force decreases to 360 A / m. As described above, by adding Si and Al to the alloy steel as a material, the carbide morphology and crystal grain size of the ferromagnetic portion are further improved in obtaining excellent soft magnetism than in the case where only Si is added. It can be seen that the composition was adjusted favorably, and further excellent soft magnetism was obtained. Further, the combined addition of Si and Al is effective from the viewpoint of further increasing the electrical resistivity.

Next, the reason for defining each numerical value in the present invention will be described. First, Fe—Cr—C which is a material of the composite magnetic member is used.
0.1% to 7% by weight of Si added to the base alloy steel.
The reason specified in the range of 0% will be described. As described above, Si is an important element of the present invention that changes the metal structure such as the carbide morphology, crystal grain size, and crystal orientation of the ferromagnetic portion, and consequently significantly improves the soft magnetism of the ferromagnetic portion. . The reason why the range of Si is set to 0.1 to 7.0% or less is that when the Si content is less than 0.1%, the effect of changing the metal structure of the ferromagnetic portion and improving soft magnetism is small. If the content exceeds 0.0%, the workability deteriorates, and it becomes difficult to manufacture a composite magnetic member. In fact, those containing 7.10% of Si could not be forged. The more preferable range of Si is 0.3 to 3.5%.

Next, the material of the composite magnetic member, Fe-C
The reason why the total amount of addition of Si and Al to the r-C alloy steel is 0.1 to 12.0% will be described.
As described above, the effect of adding Si and Al in combination is that the metal structure and soft magnetism can be further improved as compared with the case where Si is added alone. The reason why the total amount of Si and Al is set to more than 0.1% and 12.0% or less is 0.1%.
If it is less than 1%, the above effect is small, and if it is more than 12.0%, the workability is also deteriorated, and it becomes difficult to manufacture a composite magnetic member. In fact, alloy steel containing 7.11% of Si and 5.19% of Al and having a total content of Si and Al of 12.30% could not be forged. Si content and A when Si and Al are added in combination
The amount of 1 is desirably 0.3 to 3.5%, respectively.

Next, the reason why the grain size and the number of carbides of the ferromagnetic portion and the ratio of the number of carbides having a grain size of 1.0 μm or more to the total carbides to be measured will be described. When counting the number of carbides, it was difficult to observe carbides with a particle size of less than 0.1 μm, because the carbides with a particle size of 0.1 μm or more were targeted.
If the size is less than 0.1 μm, the movement of the domain wall is not hindered, and the influence on soft magnetism is small. The number of carbides having a particle size of 0.1 μm or more is 100 μm
50 in the ^second area below, had a ratio of more carbides number particle diameter 1.0μm and 15% or more with respect to the total carbide number, as can be seen from the experimental results described above, the range carbides form This makes it possible to easily move the domain wall and to easily obtain a maximum magnetic permeability of 400 or more of the ferromagnetic portion. A more preferred range of the carbide form is that the number of carbides having a particle diameter of 0.1 μm or more is 40 or less in an area of 100 μm ² , and the ratio of the number of carbides having a particle diameter of 1.0 μm or more to the total number of carbides is 20% or more, By adjusting to this range, characteristics with a maximum magnetic permeability of 500 or more can be easily achieved.

Next, the reason why the maximum magnetic permeability of the ferromagnetic portion and the magnetic permeability of the non-magnetic portion are specified will be described. Since the member of the present invention is a composite magnetic member, one member must satisfy both the soft magnetic and non-magnetic properties. The reason why the maximum magnetic permeability of the ferromagnetic portion is 400 or more is to sufficiently cope with an application requiring a high maximum magnetic permeability such as a motor component. A desirable range of the maximum magnetic permeability of the ferromagnetic portion is 500 or more, more preferably 700 or more. The reason why the magnetic permeability of the non-magnetic portion is set to 2 or less is that if it exceeds this range, the magnetic flux easily passes and becomes unsuitable for use as a non-magnetic material. A more desirable range of the magnetic permeability of the non-magnetic portion is 1.1 or less.

Next, the reason for defining the size of the ferrite grains as the matrix of the ferromagnetic portion and the range of the coercive force will be described. The size of the ferrite grains should be coarser, including the grain size number 14, and the coercive force of the ferromagnetic portion should be 10
The reason why the size is set to be not more than 00 A / m is that the size of the ferrite grains and the coercive force are mutually related characteristics.
The following characteristics are easily obtained, and the coercive force is 1000 A / m
By obtaining the following characteristics, it can be used for applications requiring a small coercive force as soft magnetism, such as core components.

The reason why the crystal orientation of the ferromagnetic portion and the range of the residual magnetic flux density are defined as desirable ranges will be described. When the material of the member of the present invention is a rolled steel sheet, the ferrite (200)
And the ferrite (110) having an X-ray integrated intensity ratio of 6 or more and the residual magnetic flux density of the ferromagnetic portion being 1.0 T or more are as follows.
Ferrite (200)
If the X-ray integrated intensity ratio between the ferrite and the ferrite (110) is adjusted to 6 or more, characteristics with a residual magnetic flux density of 0.8T or more can be easily obtained. It can also be used for applications that require excellent ON / OFF characteristics, that is, responsiveness to a magnetic field.

Next, the reason why the electric resistivity of the ferromagnetic portion is specified as a desirable range will be described. The electric resistivity of the ferromagnetic portion is set to 0.7 μΩm or more, when the member is used in an alternating magnetic field, the magnetic loss due to eddy current is reduced, and the magnetic circuit is required to have quick response. for,
This is in order to be able to respond sufficiently.

The reason why the Ni equivalent of the alloy steel as a material is specified as a desirable range will be described. As described above, in the member of the present invention, the soft magnetism of the ferromagnetic portion is superior to the conventionally disclosed composite magnetic member. In the member of the present invention, in order to obtain a stable non-magnetic portion, when the non-magnetic treatment is performed, the non-magnetic structure of
An element having an action to stabilize the stain is required. Important elements in the material of the member of the present invention are Si, Al,
There are five Fe, Cr, and C, and among them, only C has the above-mentioned action. Therefore, when it is desired to lower the magnetic permeability of the non-magnetic portion to further stabilize the characteristics, Ni,
An austenate-forming element such as Mn or N is replaced with a Ni equivalent (=
% Ni + 30.times.C + 0.5.times.Mn + 30.times.N) in the range of 10.0 to 25.0%. The reason why the lower limit of the Ni equivalent is set to 10.0% is 10.0%.
If the amount is less than%, it is difficult to obtain a non-magnetic portion having a magnetic permeability of 2 or less. The reason why the upper limit of the Ni equivalent is set to 25.0% is that if it exceeds 25.0%, the soft magnetism of the ferromagnetic portion deteriorates, and it becomes difficult to obtain a characteristic having a maximum magnetic permeability of 400 or more.

As a more desirable range, the reason for defining the chemical components of elements other than Si and Al in the alloy steel as the material of the composite magnetic member will be described. C is an essential element of the present invention effective as an austenite forming element for forming a non-magnetic portion as described above. Further, the addition of C is also effective in ensuring the strength of the member. If C is less than 0.30%, it is difficult to obtain a stable non-magnetic austenite structure when cooled after heating to austenite transformation temperature or higher. On the other hand, 0.
If it exceeds 80%, the number of carbides in the ferromagnetic portion of the composite magnetic member becomes too large, and it becomes difficult to satisfy the specification of the carbide form in the present invention. Moreover, it becomes too hard and the workability is also deteriorated. Therefore, in the present invention, the range of C is set to 0.30.
It was specified to ０．８0.80%. A more desirable range of C is
0.45 to 0.65%.

Cr dissolves in the matrix and
A part of the ferromagnetic portion becomes a carbide, which is an essential element of the present invention for ensuring the mechanical strength and corrosion resistance of the composite magnetic member. The reason for setting the range of Cr to 10.0 to 25.0% is that if it is less than 10.0%, the corrosion resistance is poor, and conversely, 25.0%
This is because, in the range exceeding, the corrosion resistance is excellent, but the soft magnetism of the ferromagnetic portion is deteriorated. A more desirable range of Cr is 16.0 to 20.0%.

Ni is an effective element for forming a nonmagnetic portion as an austenite forming element. Ni range 0.1
The reason why the content is set to -4.0% is that if it is less than 0.1%, it is difficult to obtain a stable non-magnetic portion, and if it exceeds 4.0%, it is difficult to obtain good soft magnetic properties and workability. It is because it becomes. N is an element having the same effect as Ni as an austenite generating element. The range of N is 0.01 to 0.10
The reason for setting% is that if it is less than 0.01%, it is difficult to obtain a stable non-magnetic portion, and if it exceeds 0.10%, it becomes too hard and the moldability deteriorates.

The alloy steel used as the material of the composite magnetic member of the present invention may contain Mn as a deoxidizing element in an amount of 2.0% or less. Mn is also effective in forming austenite like C, Ni, N and the like. P, S, O are inevitable impurities.
May be contained in an amount of 0.1% or less, respectively, as a range that does not deteriorate the magnetic properties.

Next, the reasons for limiting the manufacturing process will be described. In the present invention, the hot working temperature of the Fe—Cr—C alloy steel to which an appropriate amount of Si, which is a material of the composite magnetic member, or the composite addition of Si and Al is added is set to 1100 ° C. or less. When hot working is performed at a temperature exceeding 1100 ° C., the amount of C dissolved in the matrix of the alloy steel increases, and the precipitated carbide becomes very fine. As a result, even if the steel is annealed below the A3 transformation point after hot working, the precipitated carbides cannot be sufficiently increased, and C which has been dissolved in the matrix at the time of hot working, Therefore, it is difficult to control the form of the carbide within the scope of the present invention. In order to reduce the number of carbides having a grain size of 0.1 μm or more to 50 or less in an area of 100 μm ² after annealing and to make the ratio of carbides having a grain size of 1.0 μm or more to 15% or more to the carbides, it is necessary to use carbide during hot working. Is required to remain, and the maximum temperature at which carbide nuclei can be left is defined as 1100 ° C. Preferably, the hot working is 90
It is desirable to carry out in the range of 0 to 1100 ° C.

The annealing temperature performed after the hot working was set to the A3 transformation point or lower. The A3 transformation point is a structure (ferrite + carbide) below this temperature, and conversely, above this temperature,
It is the temperature at which the formation of the austenitic structure starts, and in the claims of the present invention, for example, Fe-17.5% Cr-
0.5% C-1.0% Si-2.0% Ni-0.02%
In the case of N alloy, the A3 transformation point is about 880 ° C. Since the magnetic properties of the ferromagnetic portion are due to the soft magnetic ferrite structure, it is not preferable that the annealing temperature exceeds the A3 transformation point.

The reason for annealing at least once in this temperature range is to remove the processing strain of the ferrite phase, to increase the carbide serving as a nucleus at the time of processing, and to adjust the form of the carbide within the scope of the present invention. . In addition, in the member of this invention, annealing at A3 transformation point or less is performed twice or more as needed,
May go. By performing annealing multiple times, the effect of further increasing the carbide obtained by one-time annealing and the effect of reducing the number of carbides are further enhanced.

In the member of the present invention, hot working,
After performing at least one annealing below the A3 transformation point,
If necessary, cold working may be performed, and after the cold working, annealing at an A3 transformation point or lower may be performed. This is because, in the case of a general soft magnetic material, a steel sheet annealed after cold rolling or cold drawing is often used, and it is considered that the same applies to the composite magnetic member of the present invention. Annealing after cold working may be performed a plurality of times in the same manner as after hot working. Further, the steps of cold working and annealing may be repeated a plurality of times. There is no great difference in soft magnetism as a ferromagnetic part in both cases of annealing after hot working and annealing after cold working.

In the present invention, as a method of providing a non-magnetic portion in a part of the alloy steel which has become a ferromagnetic material by the above-mentioned process, a part of the member is heated to an austenitizing temperature or higher by high frequency heating, for example. After heating and solution treatment, it is quenched or heated to a melting temperature with a CO ₂ laser or the like,
A method such as rapid cooling is preferred. The heating temperature during the demagnetization treatment is such that an austenite structure is obtained after cooling.
The temperature ranges from 50 ° C to the melting temperature, preferably from 1150 ° C to the melting temperature. The lower limit of the heating temperature is 10
The temperature of 50 ° C. is the lower limit temperature necessary for forming an austenite structure after heating and cooling and obtaining a non-magnetic portion having a magnetic permeability of 2 or less.
The reason why the temperature is set to 150 ° C. is that if the heating temperature is 1150 ° C. or higher, a more stable nonmagnetic portion can be obtained. The reason why the upper limit temperature is set as the melting temperature is not only that the solution is formed by heating and cooling, but also that the magnetic permeability substantially consisting of an austenite structure is obtained by using a method of melting and solidifying at a higher temperature.
This is because the following nonmagnetic portions can be formed. In the case where a laser beam is used as a heating source, the demagnetization by melting and solidifying is an effective means.

By performing the above-mentioned heating, solution, quenching or heating, melting, and quenching treatments, substantially o
It is possible to obtain a non-magnetic part composed of a stainless steel structure.
In this case, the structure substantially composed of austenite means that when solution is formed at a relatively low temperature, a small amount of martensite generated at the time of rapid cooling may be contained in the structure. Specifically, if the amount of martensite in the structure is 10% or less, there is no problem without deviating from the range of magnetic permeability μ2 or less, which is a characteristic required for the nonmagnetic portion of the composite magnetic member. By performing the above-described manufacturing steps, the composite magnetic member of the present invention can be obtained.

[0050]

(Embodiment 1) In the present invention, first, a ferromagnetic portion such as an Si amount and an Al amount, a carbide form, a crystal grain size, and a crystal orientation added to an Fe—Cr—C-based alloy which is a material of a composite magnetic member. The magnetic characteristics of the ferromagnetic portion, such as the metal structure, the maximum magnetic permeability, the coercive force and the residual magnetic flux density, are important. Next, the permeability of the non-magnetic portion of the composite magnetic member and the Ni equivalent for adjusting the permeability are also important. In order to clearly understand the effects of Si addition and (Si, Al) composite addition on the metal structure and soft magnetism of the ferromagnetic part, and the relationship between Ni equivalent and the magnetic permeability of the non-magnetic part, vacuum melting was used as an alloy material. Si, Al,
Alloy steel ingots in which the element contents of C and Ni were variously changed were melted.

Table 1 shows the chemical composition and Ni equivalent (=% Ni + 30 ×% C + 0.5) of the alloy steel as the material of the composite magnetic member.
×% Mn + 30 ×% N). Member No. Materials 1 to 9 make the addition amounts of C, Mn, Ni and Cr almost equal,
This is an alloy steel in which the amount of Si added is changed, and the amount of Al is 0.0
0.01 to 0.007% and substantially no additive. Member N
o. In the materials Nos. 10 to 13, the addition amounts of C, Mn, Ni, and Cr are the same as those of the member Nos. It is almost the same as the materials Nos. 1 to 9;
It is an alloy steel in which Si and Al are added in a range of 1 ≦ (Si + Al) ≦ 12.0. The member No. Material No. 14 has a low C and Ni content and a low Ni equivalent. In the fifteen materials, the contents of C and Ni were both increased, and the Ni equivalent was increased. Member N
o. Material No. 16 has a Si content and an Al content of 0.002%, and does not substantially contain both elements. The member No. Material No. 17 has a Si content exceeding 7.0%. The material No. 18 has a total amount of Si and Al exceeding 12.0%.

[0052]

[Table 1]

The obtained alloy steel ingot was heated to 1000 ° C. and forged to form a plate having a thickness of 20 mm.
And hot-rolled to obtain a rolled plate having a thickness of 5.0 mm. Here, the member No. whose Si content exceeds 7.0%. 1
No. 7 and the member No. 7 in which the total amount of Si and Al exceeds 12.0%. Material No. 18 was used as a comparative example of the present invention because the steel ingot was broken during forging and hot working could not be performed. Member N
o. The materials Nos. 1 to 16 were obtained by hot rolling.
After a 0 mm thick plate was annealed at 780 ° C. below the A3 transformation point to soften, cold rolling was performed to obtain a 1.0 mm thick cold rolled plate. This cold-rolled sheet is again subjected to the A3 transformation point below 7
Annealed at 00 ° C. to obtain a soft magnetic material. A part of the steel sheet made of soft magnetic material is heated at about 1200 ° C for 10
After holding for 1 minute, the mixture was cooled with water and partially demagnetized. By this partial demagnetization treatment, the alloy steel sheet was used as a composite magnetic member.

The number of carbides in the ferromagnetic portion was determined by cutting out a sample for microstructure observation from the ferromagnetic portion of the obtained composite magnetic member that was not affected by the heat of high-frequency heating. After embedding in a resin so as to obtain a mirror-polished surface, chemical corrosion was performed using aqua regia, and 10 fields of view were observed and photographed at 6000 × with a scanning electron microscope. Image analysis of the photographed 10 fields of view was performed to determine the particle size to 0.1.
The number of carbides having a particle size of 1.0 μm or more and the number of carbides having a particle size of 1.0 μm or more were counted, and the number of carbides per 100 μm ² and the ratio of the carbide having a particle size of 1.0 μm or more to the total number of carbides were determined. As an observation example of the microstructure, member No. No. 3 in FIG. No. 10 in FIG. 16 is shown in FIG. 3 and the carbide form of the ferromagnetic portion is shown in one view for each member.

The grain size number of the ferrite grains in the ferromagnetic portion was determined according to JIS G 0 using the same sample as above.
According to the ferrite grain size test method described in 552,
An average value was obtained by observing five visual fields with an optical microscope. The crystal orientation of the ferromagnetic portion is determined by cutting out a block of about 10 mm square from the ferromagnetic portion, electrolytically polishing the rolled surface, and analyzing the X-ray diffraction to a diffraction angle 2θ = 30 ° to 120 °, and detecting the ferrite. (110), ferrite (200) and ferrite (211) were measured, and (200) / (110)
Was determined.

The magnetic properties of the ferromagnetic portion were obtained by cutting a JIS ring having an outer diameter of 45 mm and an inner diameter of 33 mm from the ferromagnetic portion.
After winding the primary winding 150 times and the secondary winding 30 times,
The measurement was performed by applying a DC magnetic field of 000 A / m. As a measurement example of the direct current magnetic characteristics, the member No. No. 3 in FIG. 10
In FIG. The BH curve of the ferromagnetic portion is shown in FIG. Further, the electric resistivity of the ferromagnetic portion was measured by cutting out a measuring piece of 10 mm × 80 mm from the ferromagnetic portion.

On the other hand, the non-magnetic portion formed by high-frequency heating is substantially composed of an austenite phase by X-ray diffraction analysis after cutting out a block of about 15 squares from the non-magnetic portion and electropolishing the surface. Confirmed that.
In this case, the substantially austenitic state means that the diffraction angle 2θ in X-ray diffraction is 2θ = 30 to 1
Assuming that the total integrated intensity of the martensite phase peak detected when scanning to 20 ° is α and the total integrated intensity of the austenite phase is γ, γ / (α + γ) ≧ 0.9 (1) It was decided. As a result of the X-ray diffraction analysis, the member No. 1
-13, No. It was confirmed that all of the nonmagnetic portions 15 to 16 satisfied the above expression (1) and consisted substantially of an austenite phase. However, the Ni equivalent of the material was 5.19.
% As low as In No. 14, the above expression (1) was not satisfied. Further, the magnetic permeability of the non-magnetic portion was measured with a permeability meter by cutting out a block of about 10 mm square from the non-magnetic portion formed by high-frequency heating.

The alloy steel, which is the material of the composite magnetic member, is made of Si.
Table 2 summarizes the amounts, (Si + Al) amounts, and Ni equivalents, the morphology and soft magnetism, electrical resistivity of the ferromagnetic portion of the composite magnetic member, and the magnetic permeability of the non-magnetic portion of the composite magnetic member.

[0059]

[Table 2]

In Table 2, the member No. Reference numerals 1 to 13 denote members of the present invention, and member Nos. 14 to 18 are comparative examples. First, the amount of Si added to the alloy material, the texture of the ferromagnetic portion, and the soft magnetism will be described. In the members 1 to 9 of the present invention to which Si was added in the range of 0.1 to 7.0%, the number of carbides having a particle diameter of 0.1 μm or more in the ferromagnetic portion was 50/10
0 μm ² or less, and a particle size of 1.0 with respect to the total number of carbides.
The proportion occupied by carbides of μm or more is all 15% or more, and the maximum magnetic permeability of the ferromagnetic portion is all 400 or more. Among them, in the members 2 to 9, the ferrite grain size in the ferromagnetic part is all coarse including 14 in the grain size number, and the coercive force is 1000 A / m.
Satisfies the following characteristics.

Next, the addition of (Si, Al) composite to the alloy material, the structure of the ferromagnetic portion, and the soft magnetism will be described. S
Inventive member No. 1 in which the total amount of i and Al is in the range of 0.1 to 12.0%. In Nos. 10 to 13, the number of carbides having a particle size of 0.1 μm or more in the ferromagnetic portion was 50/100.
μm ² or less, and a particle size of 1.0 μm with respect to the total number of carbides.
The proportion occupied by carbides of m or more is all 15% or more, and the maximum magnetic permeability of the ferromagnetic portion is all 400 or more. Further, the ferrite grain size in the ferromagnetic portion is all coarse, including the crystal grain size number of 14, and satisfies the coercive force of 1000 A / m or less.
Further, it can be seen that the combined addition of Si and Al has the effect of improving the metal structure and soft magnetism of the ferromagnetic portion more than the case of adding Si alone.

On the other hand, the member No. 16-18
Looking at No. 16 (Si = 0.002%, Al =
(0.002%), both the Si content and the Al content are too small, so that the number of carbides in the ferromagnetic portion increases, and the crystal grain size number 1
6.0 and the maximum magnetic permeability of the ferromagnetic portion is 3
It remains at a low value of 15. The member No. 17
(Si = 7.10%, Al = 0.002%) and material No. 18 materials (Si = 7.11%, Al = 5.1)
9%), conversely, the amount of Si added and the total amount of Si and Al are too large, so that hot working cannot be performed.

Next, the Ni equivalent and the maximum magnetic permeability of the ferromagnetic portion
This will be described from the viewpoint of the magnetic permeability of the non-magnetic portion. Inventive member No.
Each of the samples Nos. 1 to 13 satisfies the composite magnetic characteristics in which the maximum magnetic permeability of the ferromagnetic portion is 400 or more and the magnetic permeability of the non-magnetic portion is 2 or less. The member No. of Comparative Example in which the Ni equivalent was as low as 5.19%.
In No. 14, although the soft magnetism of the ferromagnetic portion is excellent, the magnetic permeability of the non-magnetic portion is as large as 2.53, so that the magnetic flux easily passes. Conversely, the member No. of the comparative example having a high Ni equivalent of 28.90%. In No. 15, it can be seen that the maximum magnetic permeability of the ferromagnetic portion was low at 389, and the soft magnetism was deteriorated. From the above results, the preferable range of the Ni equivalent is 10.0% to 2%.
It turns out that it is 5.0%.

(Embodiment 2) In the present invention, in the process of manufacturing a composite magnetic member, the hot working temperature of Fe-Cr-C-based alloy steel to which Si as a raw material or Si and Al is added in combination is also reduced. Since it becomes important, the member No. 3 and N
o. The hot working temperature of the alloy steel used as the material No. 10 was 950
When the temperature was changed in the range of １1150 ° C., the number of carbides having a particle diameter of 0.1 μm or more and the number of carbides having a particle diameter of 1.0 μm or more in the ferromagnetic portion of the obtained composite magnetic member were measured. The method for measuring the number of carbides is the same as described above. Table 3 shows the measurement results.
Shown in

[0065]

[Table 3]

From Table 3, it can be seen that by setting the hot working temperature of the alloy steel as a raw material to 1100 ° C. or less, the number of carbides having a particle diameter of 0.1 μm or more in the ferromagnetic portion is at least 1.0 μm with respect to the total number of carbides. It can be seen that a composite magnetic member of the present invention having a carbide ratio of 15% or more can be obtained.

[0067]

According to the present invention, Si is used as a material for a composite magnetic member having a ferromagnetic portion and a non-magnetic portion in a single material.
To 7.0%, or 0.1 to 12 in total of Si and Al.
By applying Fe-Cr-C alloy steel added in the range of 0% and performing hot working and annealing in an appropriate temperature range, the number of carbides having a grain size of 0.1 µm or more is 100 µm ^2.
50 or less in the area of, and the particle size with respect to the number of carbides is 1.
The ratio of carbide of 0 μm or more is 15% or more, and an excellent soft magnetic ferromagnetic material can be obtained. Further, by performing partial heating in an appropriate temperature range, the magnetic characteristics can be maintained at the same level as in the past. A stable non-magnetic portion having the same can be obtained. The present invention is an indispensable technique when applying a composite magnetic member to a magnetic circuit requiring excellent soft magnetism.

[Brief description of the drawings]

FIG. 1 is a microstructure photograph showing a carbide form of a ferromagnetic portion of a composite magnetic member of the present invention.

FIG. 2 is a micrograph showing a carbide morphology of a ferromagnetic portion of the composite magnetic member of the present invention.

FIG. 3 is a microstructure photograph showing a carbide form of a ferromagnetic part as a comparative example.

FIG. 4 is a BH curve of a ferromagnetic portion of the composite magnetic member of the present invention.

FIG. 5 is a BH curve of a ferromagnetic portion of the composite magnetic member of the present invention.

FIG. 6 is a BH curve of a ferromagnetic portion as a comparative example.

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[Procedure amendment]

[Submission date] July 27, 1999 (July 7, 1999
7)

[Procedure amendment 1]

[Document name to be amended] Statement

[Correction target item name] 0024

[Correction method] Change

[Correction contents]

Next, the relationship between the amount of added Si, the crystal grain size of ferrite grains in the ferromagnetic portion, and the coercive force will be specifically described. weight%
In the case of a composite magnetic member made of an alloy steel containing Fe-17.5% Cr-0.5% C-2.0% Ni as a main component, for example, 0.02% of Si is used as a deoxidizing agent. When only ferromagnetic particles are contained and substantially not added, the size of the ferrite grains in the ferromagnetic portion is a crystal grain size number of 16.0, and the coercive force is 1220 A / m. 0.4% by weight to this alloy steel
In the ferromagnetic portion of a composite magnetic member made of alloy steel containing 4% Si, the size of ferrite grains is determined by the grain size number.
It increases to 14.0 , the coercive force decreases to 980 A / m, and the soft magnetism (soft magnetic properties) can be improved. Also,
When an alloy steel to which 0.91% by weight of Si is added is used as a material, the crystal grain number of the ferromagnetic portion is 13.0, and the coercive force is 700 A / m. Furthermore, 1.94% of S by weight%
When i was added, the size of the ferrite grains increased to a grain size number of 12.0, and the coercive force was 490 A / m
And the soft magnetism (soft magnetic properties) can be further improved. It can be seen that the addition of Si increases the size of the ferrite grains, thereby decreasing the coercive force and improving the soft magnetism (soft magnetic properties). The above is the second effect of adding Si to the Fe-Cr-C alloy steel used as the material of the composite magnetic material member.

Claims (11)

[Claims] 1. An Fe—Cr— containing 0.1 to 7.0% of Si, or 0.1 to 12.0% of Si and Al in total.
The number of carbides having a grain size of 0.1 μm or more is 50 or less in an area of 100 μm ² , and the ratio of the number of carbides having a grain size of 1.0 μm or more to the number of carbides is 1
A composite magnetic member having a ferromagnetic portion having a maximum magnetic permeability of 400 or more adjusted to 5% or more and a non-magnetic portion having a magnetic permeability of 2 or less. 2. The crystal grain size of the ferromagnetic portion is adjusted to a coarser grain size including a grain size number 14, and the coercive force is 1000 A /
The composite magnetic member according to claim 1, wherein m is equal to or less than m. 3. When the crystal orientation is measured by X-rays from the surface side, the X-rays of the ferrite (200) and the ferrite (110) are measured.
The composite magnetic member according to claim 1, further comprising a ferromagnetic portion having a linear integral intensity ratio of 6 or more. 4. The composite magnetic member according to claim 1, wherein the composite magnetic member has a ferromagnetic portion having an electric resistivity of 0.7 μΩm or more. 5. Ni equivalent (=% Ni + 30 ×% C + 0.
5. The composite magnetic member according to claim 1, wherein the composite magnetic member is made of an alloy steel having (5 ×% Mn + 30 ×% N) 10.0 to 25.0%. 6. C: 0.30 to 0.80% by weight, C
r: 10.0 to 25.0%, Si; 0.1 to 7.0%,
Ni: 0.1 to 4.0%, Mn; 0.1 to 2.0%,
The composite magnetic member according to any one of claims 1 to 5, wherein N: 0.01 to 0.10%, the balance being alloy steel having a composition of Fe and inevitable impurities. 7. C: 0.30 to 0.80% by weight, C
r: 10.0 to 25.0%, Si; 0.05 to 7.0
%, Al: 0.05 to 5.0%, Ni: 0.1 to 4.0
%, Mn; 0.1 to 2.0%, N: 0.01 to 0.10
The composite magnetic member according to any one of claims 1 to 5, wherein the balance is made of alloy steel having a composition of Fe and inevitable impurities. 8. The composite magnetic member according to claim 1, wherein Si is 0.3 to 3.5% by weight. 9. The method according to claim 1, wherein Al is 0.3 to 3.5% by weight.
The composite magnetic member according to any one of the above. 10. Si of 0.1 to 7.0%, or Si
Fe-Cr containing 0.1-12.0% in total of Al and Al
After hot working -C based alloy steel at 1100 ° C or lower,
Anneal at least once at A3 transformation point or less, and particle size 0.1μ
a ferromagnetic material in which the number of carbides of m or more in an area of 100 μm ² is 50 or less, and the ratio of the number of carbides having a particle size of 1.0 μm or more to the number of carbides is adjusted to 15% or more. A method for manufacturing a ferromagnetic portion of a magnetic member. 11. An alloy containing 0.1 to 7.0% of Si,
Fe-Cr containing 0.1-12.0% in total of Al and Al
After hot working -C based alloy steel at 1100 ° C or lower,
Anneal at least once at A3 transformation point or less, and particle size 0.1μ
The number of carbides of m or more in an area of 100 μm ² is 50 or less, and the ratio of the number of carbides having a particle size of 1.0 μm or more to the number of carbides is adjusted to 15% or more.
A method for forming a non-magnetic portion of a composite magnetic member, wherein the non-magnetic portion is formed by quenching after heating in a temperature range of 050 ° C. to a melting temperature.