JP6464753B2 - Soft magnetic Fe-based metal plate having a plurality of crystal orientation layers and manufacturing method thereof - Google Patents

Description

  The present invention relates to a soft magnetic Fe-based metal plate having a plurality of crystal orientation layers in the thickness direction, and particularly excellent in magnetic flux density and high-frequency iron loss, and compressive stress is applied to the core material when assembled as a motor core. Even in this case, the present invention relates to a soft magnetic Fe-based metal plate with little deterioration of magnetic characteristics.

  A soft magnetic steel plate represented by a silicon steel plate is used as a core member for an electric motor, a generator, a transformer or the like. As its magnetic characteristics, it is required that the magnetic energy loss (iron loss) in an alternating magnetic field is small and that the magnetic flux density is high from the viewpoint of miniaturization and weight reduction. Furthermore, due to the recent increase in demand for small high-speed rotary motors in the automobile field and the like, there is also a demand for excellent high-frequency iron loss.

  In addition, the core member using the soft magnetic steel plate has a problem in that when it is assembled to the motor, a compressive stress acts on the core material in the in-plane direction and the magnetic characteristics deteriorate.

The technique currently disclosed by patent documents 1-4 is known with respect to such a request | requirement and a problem.
In Patent Documents 1 and 2, a metal layer containing a ferrite-forming element such as Si or Al is formed on the surface of an Fe-based metal plate having a composition capable of causing α-γ transformation, and then α A high heat flux density in which the {200} plane integration degree of the ferrite phase with respect to the plate surface is 30% or more after cooling is performed after heating and holding at a temperature equal to or higher than the −γ transformation point (A3 point). A technique for obtaining an Fe-based metal plate is disclosed.

  In Patent Document 3, in a range from the steel plate surface to at least a distance of 10% of the plate thickness, the {222} plane integration with respect to the steel plate surface of the αFe phase is increased to 55% or more and 99% or less, thereby being parallel to the steel plate surface. The <111> orientation, which is a difficult magnetization direction, can be eliminated from any direction, so that relatively preferable magnetic characteristics can be realized without integrating the <100> orientation, which is the easy magnetization direction, in the magnetic field direction used. A soft magnetic steel sheet is disclosed in which distortion hardly occurs when punching is performed, and deterioration of magnetic properties due to distortion is reduced.

In patent document 4, Si: more than 6.6%, 10% or less, Al: 1% or less, Mn: 0.05-2%, S: 0.005% or less, N: 0.005% or less Or having a component composition containing Ni: 30 to 45%, and the magnetostriction constant of the core material in the direction corresponding to the circumferential direction of the stator (for example, the direction perpendicular to the rolling direction) is −0.1 × 10 ⁻⁷ or less By using a steel sheet with a negative value of 1 so that the compressive stress in the core circumferential direction is 10 MPa or more, the orientation of the magnetization vector due to the compressive stress in the steel sheet thickness direction is suppressed, and the increase in eddy current loss is reduced. Thus, there is disclosed a technology capable of realizing a motor with small iron loss deterioration even under compressive stress due to shrink fitting or the like during product assembly.

However, Patent Documents 1 to 4 are excellent in high-frequency iron loss while ensuring a high magnetic flux density, and at the same time, suppressing deterioration of magnetic characteristics due to assembly to the core when manufacturing a core member from a soft magnetic steel sheet. No possible means are disclosed.
Moreover, since the technique of Patent Document 4 makes the magnetostriction constant a negative value, it is necessary to contain Si, Ni, etc. at a high concentration, which not only deteriorates workability but also reduces the theoretical saturation magnetic flux density. Degradation of practical magnetic flux density is inevitable.
On the other hand, in order to achieve a plurality of functions that cannot be achieved with a single steel sheet, a single steel sheet allows each layer to have a desired individual function as a multilayer steel sheet. It is known from documents 5, 6 and the like.

  In patent document 5, it is set as the three-layer clad structure which made the surface layer the both sides of the directional electrical steel plate of an inner layer with the non-oriented electrical steel plate, and about non-oriented electrical steel plates which are surface layers, Si: 2-7 mass% and Al: 3% by mass or less in a range satisfying (Si + Al) ≧ 4% by mass. On the other hand, for the grain-oriented electrical steel sheet as the inner layer, Si: 5% by mass or less and Al: 0.5% by mass or less. An electromagnetic steel sheet that achieves both high magnetic flux density and high frequency and low iron loss by using the composition contained is disclosed.

In Patent Document 6, a laminated steel plate in which a plurality of steel plates made of one or both of carbon steel and alloy steel are laminated and integrated, and an αFe phase or a γFe phase at both the steel plate surface and the thickness center of the laminated steel plate. The {222} plane integration degree with respect to the steel sheet surface is 60% or more and 99% or less and the {200} plane integration degree is 0.01% or more and 15% or less. Technology that can improve the workability of laminated steel sheets by increasing the degree of surface integration, and by selecting the type of each layer of laminated steel sheets, it is possible to achieve high strength, improved rough skin resistance, and improved corrosion resistance. Is disclosed.
However, these documents do not show a soft magnetic steel sheet that simultaneously solves the problem of high magnetic flux density and excellent high-frequency iron loss and the problem of preventing the deterioration of magnetic properties during the manufacture of core members.

Japanese Patent No. 5136687 Japanese Patent No. 5533801 JP 2009-256758 A JP 2011-089170 A JP 2010-1332938 A JP 2009-256734 A

  In view of the prior art as described above, the present invention is a soft magnetic Fe-based metal plate that has a high magnetic flux density and a low high-frequency iron loss, and can reduce the deterioration of iron loss even when manufacturing a product such as a motor core. The purpose is to provide.

Patent Documents 1 and 2 disclose a soft magnetic Fe-based metal plate having a high magnetic flux density, and Patent Document 4 discloses a soft magnetic steel sheet having a small deterioration in magnetic properties when a core is manufactured through an assembly process. Has been.
Therefore, the present inventors do not realize the functions of these soft magnetic Fe-based metal plates with a single-structure metal plate, but instead have a multilayer structure as described in Patent Documents 5 and 6. The realization simultaneously with one Fe-based metal plate was studied.

The inventors have disclosed a structure disclosed in Patent Documents 1 and 2, which has an increased degree of {200} plane integration to ensure good magnetic properties, and is further disclosed in Patent Document 4. We examined the combination of technologies to suppress iron loss deterioration during assembly to existing products.
In the course of the study, (i) assembling the core material by making the magnetostriction of only the central layer of the metal plate negative even if the magnetostriction of the whole metal plate is not made negative as in Patent Document 4 (Ii) If a structure with increased {222} plane integration is formed, Si and Ni are contained in a high concentration as in Patent Document 4 It was found that the magnetostriction can be made negative even if it is not performed.

As a result of further examination based on such knowledge, a region where the {200} plane integration degree is increased is formed on the surface layer, and the saturation magnetostriction is a negative value in the central layer, and the {222} plane integration degree is increased. The present invention having the multilayer structure (1) to ( 6 ) below has been reached.

(1) In the soft magnetic Fe-based metal plate having a plurality of crystal orientation layers in the plate thickness direction,
Contains at least one ferrite-forming element of Al, Cr, Ga, Ge, Mo, Sb, Si, Sn, Ti, V, W, and Zn, and has a {200} plane integration degree of 25% or more of the αFe phase with respect to the plate surface Then, the region where the {222} plane integration degree of the αFe phase is 40% or less is defined as A layer,
At least one ferrite-forming element of Si, Al, Sn, Ti, and V, in mass%, Si = 0 to 1.5%, Al = 0 to 3.5%, Sn = 0 to 4%, Ti = In the range of 0 to 3% and V = 0 to 6.5%, the {222} plane integration degree of the αFe phase with respect to the plate surface is 55% or more and 99% or less, and the average saturation magnetostriction in the plate surface is − A region that is 0.2 × 10 ⁻⁶ or less as a B layer,
The A layer and the B layer exist in the thickness direction,
And on both surfaces of a metal plate, it becomes a laminated structure in which an A layer exists between the plate surface and the B layer first confirmed from the plate surface toward the plate surface opposite to the plate surface. And
A metal plate, wherein the interface between the A layer and the B layer is integrated by metal bonding .

(2) In the soft magnetic Fe-based metal plate having a plurality of crystal orientation layers in the plate thickness direction,
The region that is neither the A layer nor the B layer is a C layer, and the A layer, the B layer, and the C layer exist in the thickness direction ,
Interface of the A layer and the B layer, further metal sheet according to (1) the interface between the A layer and the B layer and the C layer is characterized that you have been integrated with a metal bond.

(3) In the soft magnetic Fe-based metal plate having a plurality of crystal orientation layer in the thickness direction,
When the A layer, the B layer, and the C layer are present, the difference in Fe concentration in the region at a distance of 10 μm from the interface between the C layers on both sides is 1.0% or less. The metal plate according to (1) or (2) .

( 4 ) In the soft magnetic Fe-based metal plate having a plurality of crystal orientation layers in the plate thickness direction,
The metal plate according to any one of (1) to ( 3 ), wherein the thickness of the A layer closest to the plate surface is 70 to 97% with respect to the entire plate thickness. .

( 5 ) In the soft magnetic Fe-based metal plate having a plurality of crystal orientation layers in the plate thickness direction,
The metal plate according to any one of (1) to ( 4 ), wherein the metal plate has a thickness of 0.03 mm to 1.5 mm.

( 6 ) In the production of a soft magnetic Fe-based metal plate having a plurality of crystal orientation layers in the plate thickness direction,
The metal plate _{A 1} having the composition which can cause alpha-gamma transformation contains 70 mass% or more Fe and cold rolling at 97 percent 99.99% less reduction ratio, Al on the surface of that, Cr, Ga , and Ge, Mo, Sb, Si, Sn, Ti, V, a metal plate is adhered at least one kind of ferrite forming elements of W and Zn and the metal plate _{a 2,}
A metal plate _{B 1} having a composition that may occur were alpha-gamma transformation containing 70 mass% or more Fe and cold rolling at a reduction ratio of 95% or more and 30% or less, Si in the surface of that, Al, Sn, Ti and a metal plate obtained by attaching at least one kind of ferrite-forming elements V and the metal plate B _2,
Heat-treating at least the α-γ transformation point or higher at least the metal plate A ₂ and the metal plate B ₂ laminated,
Production method of (1) to a soft magnetic Fe-based metal sheet according to any one of (5), characterized in that diffusing the ferrite forming elements into the interior of the metal plate A ₁ and the metal plate B _1.

  Here, the {200} plane integration degree or the {222} plane integration degree is determined by X-ray diffraction using MoKα rays, and there are 11 orientation planes ({110}, {200}, {200} having an αFe phase parallel to the sample surface. 211}, {310}, {222}, {321}, {411}, {420}, {332}, {521}, {442}), and measure each of the measured values in a random orientation. The ratio of the intensity of the {200} or {222} azimuth plane to the value obtained by dividing by the theoretical integrated intensity of the sample is obtained as a percentage.

In the present invention as described above, the effect of suppressing the deterioration of the magnetic properties under compressive stress by setting the magnetostriction of only the central layer region of the metal plate having a multilayer structure to a negative value is different from that of the metal plate having a different crystal orientation. Simply laminating does not give sufficient expression, but it remarkably develops due to magnetic interaction between the layers by integrating the metal plates by metal bonding such as element diffusion.
This effect is manifested in a material with a negative magnetostriction that maintains the direction of magnetization in the plane under in-plane compressive stress, and a material with a non-negative magnetostriction integrated by metal bonding. It is also a phenomenon that utilizes a phenomenon that is not widely assumed in the conventional multi-layer technology, which is relatively widespread.

In addition, such a metal plate configuration contributes to an improvement in the magnetic flux density of the entire metal plate because a metal plate having a high degree of {200} plane integration of a low alloy can be disposed in the surface layer region.
In particular, when used in a high-frequency region such as a high-speed rotating machine, the magnetic flux concentrates on the surface layer, so that the high-frequency iron loss can be effectively reduced by improving the magnetic flux density of the surface layer portion.

  According to the present invention, there is provided a soft magnetic Fe-based metal plate that has a high magnetic flux density and a low high-frequency iron loss that cannot be achieved by a conventional soft magnetic steel sheet, and that can reduce the deterioration of magnetic properties even during product manufacturing such as assembly. can do.

  In the present invention, a layer in which the {200} plane is preferentially oriented and a layer having a composition in which the {222} plane is preferentially oriented and the magnetostriction is negative are formed by metal bonding by mutual diffusion of elements. By integrating, a soft magnetic Fe-based metal plate having a high magnetic flux density, excellent high-frequency iron loss, and small deterioration in magnetic properties due to assembly during product manufacture is obtained.

  Hereinafter, the reason for limitation of individual conditions, preferable conditions, and a manufacturing method are demonstrated about the soft-magnetic Fe type metal plate of this invention. In the following description,% of the element content means mass%.

The soft magnetic Fe-based metal plate of the present invention includes a layer in which the {200} plane is preferentially oriented (hereinafter referred to as A layer), and a layer having a composition in which the {222} plane is preferentially oriented and magnetostriction is negative. (Hereinafter referred to as B layer) is a laminated structure. In addition to the A layer and the B layer, a layer that is neither the A layer nor the B layer (hereinafter referred to as the C layer) is stacked.
Below, the characteristic of each layer is demonstrated first.

Characteristics of A to C layers (Crystal orientation of A layer)
As will be described later, the A layer is basically a layer constituting the outermost layer of the metal plate or a layer in the vicinity of the surface, and is a layer for imparting high magnetic flux density and low high-frequency iron loss to the metal plate. About A layer, the {200} plane integration degree with respect to the metal plate surface of (alpha) Fe phase is raised. As a result, the ratio of the [100] orientation, which is the easy magnetization direction, increases in the direction of the magnetic field used, and the ratio of the [111] orientation, which is the hard magnetization direction, decreases, so that the magnetic flux density of the metal plate of the present invention is effective. Can be increased. Moreover, since the magnetic flux concentrates on the surface layer when used in a high frequency region, it is possible to simultaneously reduce the high frequency iron loss.
In order to obtain such an effect, the A layer has a {200} plane integration degree of 25% or more and a {222} plane integration degree of 40% or less with respect to the plate surface. Preferably, the {200} plane integration degree is 30% or more and the {222} plane integration degree is 30% or less.
It is desirable that the {200} plane integration degree is high, but even if it exceeds 99%, the effect of improving the magnetic flux density is saturated, and manufacturing is also difficult.

(Crystal orientation of layer B)
As will be described later, the B layer is basically a layer constituting the central layer of the metal plate or a layer near the center, and has a chemical composition such that the average saturation magnetostriction value in the plate surface is negative. is there.
In the present invention, in order to suppress the content of Si or Ni added to make magnetostriction negative, the {222} plane integration degree with respect to the metal plate surface of the αFe phase of the B layer is increased. Further, when the degree of {222} plane integration increases, the [100] orientation, which is the easy magnetization direction, decreases in the used magnetic field direction, that is, the ratio existing in the plate surface, but the [111] orientation, which is the hard magnetization orientation, is used. Since the ratio existing in the magnetic field direction is also reduced, there is an effect that the deterioration of the magnetic flux density is suppressed to an acceptable level.

If the {222} plane integration degree with respect to the plate surface of the αFe phase is 55% or more, it is possible to obtain the effect of avoiding deterioration of the magnetic characteristics under the in-plane compressive stress by setting the magnetostriction to a negative value even with a low alloy. At the same time, it is possible to enjoy the effect of improving the magnetic characteristics by eliminating the [111] orientation.
It is desirable that the {222} plane integration degree is high, but even if it exceeds 99%, the effect of preventing the deterioration of the magnetic characteristics is saturated and there is a difficulty in manufacturing.

(Measurement of surface integration of A and B layers)
The measurement of the surface integration degree can be performed by X-ray diffraction (reflection method) using MoKα rays.
Specifically, for each sample, eleven orientation planes ({110}, {200}, {211}, {310}, {222}, {321}, {411 of the parallel αFe phase with respect to the metal plate surface. }, {420}, {332}, {521}, {442}) are measured, and each of the measured values is divided by the theoretical integrated intensity of a sample having a random orientation, and the sum of the measured values is { 200} strength or {222} strength ratio as a percentage.

That is, the {200} strength ratio is represented by the following formula (1), and the {222} strength ratio is represented by the following formula (2).
{200} plane integration degree = [{i (200) / I (200)} / Σ {i (hkl) / I (hkl)}] × 100 (1)
{222} plane integration degree = [{i (222) / I (222)} / Σ {i (hkl) / I (hkl)}] × 100 (2)
However, the symbols are as follows.
i (hkl): Measured integrated intensity of {hkl} plane in the measured sample I (hkl): Theoretical integrated intensity of {hkl} plane in the sample with random orientation Σ: Sum of 11 orientation planes of αFe phase The integrated intensity of a sample having a random orientation may be obtained by preparing a sample and actually measuring it.

In addition, it is necessary to perform said measurement in the area | region subdivided in the plate | board thickness direction so that the change of the crystal orientation in the plate | board thickness direction can fully be grasped | ascertained. Specifically, the crystal structure in the plate thickness direction is observed, and the measurement is performed by subdividing the thickness into portions corresponding to the average grain size of each region at the plate thickness direction position. This means that, for example, if there is a region with an average grain size of 30 μm, it means that the degree of surface integration is measured at intervals of 30 μm, and since one crystal grain has the same crystal orientation, the crystal at a specific position The orientation is based on the idea that it does not vary within a distance of about the average grain size in that region. The procedure for polishing the surface of the metal plate to a target thickness position in the plate thickness direction and irradiating the polished surface with X-rays is not different from the general procedure for measuring crystal orientation in the plate thickness direction.
If it is clear that there is only a change of about three layers or several layers in the thickness direction as seen from the crystal grain structure, the measurement may be performed at a position where each of these layers can be judged as representative.
The crystal grain size is determined by measuring the number of crystal grains observed within a certain area by measuring the number of crystal grains observed by chemical etching such as polishing and nital in the plate thickness section, and calculating the average area of one crystal grain. This is the diameter when it is equivalent to a circle.

(B-layer magnetostriction)
When the core material punched from the soft magnetic Fe-based metal plate is assembled to the core member, compressive stress is applied in a direction parallel to the surface of the metal plate, causing deterioration of the magnetic properties of the core member. In the present invention, the average saturation magnetostriction in the plate surface is set to −0.2 × 10 ⁻⁶ or less in the state where the {222} plane integration degree is increased in the B layer, thereby reducing the iron loss due to the compressive stress in the plate surface. Deterioration is suppressed.
This effect is characteristic of the present invention, and is caused not only by the magnetostriction described here, but also by magnetic interactions that develop in relation to the laminated structure of each layer and the coupling state (interface structure) of each layer. . After defining the laminated structure and interface structure of the present invention, the mechanism will be described later.

The saturation magnetostriction defined in the present invention is measured as follows.
First, in accordance with the change in the crystal orientation distribution in the plate thickness direction described above, a layer having an αFe phase {222} plane integration degree of 55% or more and 99% or less is cut out by polishing or the like. And about the cut-out metal plate, a saturation magnetostriction is measured over 360 degrees every 22.5 degrees within a plate surface. At this time, a magnetic field of 800 kA / m is applied to each direction and the direction perpendicular thereto, and the magnetostriction with respect to the magnetic field 0 is measured with a strain gauge or the like, and then the magnetostriction difference between the target direction and the magnetostriction in the vertical direction is 2 A value obtained by multiplying / 3 is the saturation magnetostriction in each direction, and the saturation magnetostriction defined in the present invention can be obtained as an average value of these.

By the way, in the crystal oriented in the {222} plane on the plate surface, the orientation in the plate surface where the magnetization is easily oriented is [110], so the magnetostriction of the crystal in the {222} plane orientation is in the [110] direction. It becomes magnetostriction.
The magnetostriction λ _{110 in the} [110] direction is obtained from the equation [λ ₁₁₀ = (1/4) λ ₁₀₀ + (3/4) λ ₁₁₁ ].
In the Fe-X alloys, the magnetostriction in the [100] direction is all positive except that it becomes zero at 6.5% Si, and the magnetostriction in the [111] direction is Si, Al, V, Ti, and Sn are negative values in the range of Si = 0 to 4%, Al = 0 to 9%, V = 0 to 14%, Ti = 0 to 3%, and Sn = 0 to 4%. (For example, refer to FIGS. 1 and 61 of “Handbook of Steel Materials”).
In consideration of these, the saturation magnetostriction λ ₁₁₀ of the Fe-based metal of the α-γ transformation component is such that each content of Si, Al, V, Ti, and Sn is Si = 0 to 1.5%, Al = 0-3.5%, V = 0-6.5%, Ti = 0-3%, Sn = 0-4%. It can be negative in the range.

(About layer C)
In the present invention, the C layer is defined as a metal layer that is neither the A layer nor the B layer. That is, the {222} plane integration degree with respect to the plate surface is more than 40% and less than 55%, the {222} plane integration degree is more than 99%, or the {222} plane integration degree is 55% or more and 99% or less. Even if the average saturation magnetostriction in the plate surface is more than −0.2 × 10 ⁻⁶ or the {222} plane integration degree is 40% or less, the {200} plane integration degree is 25%. It is a layer that is less than.

  The C layer can be intentionally formed so as to be included in the metal plate of the present invention, but the practical merit of intentionally forming the layer is small. In the present invention, the C layer is formed between the A layer and the B layer. In many cases, it is inevitable to exist in a special region such as the transition region or the outermost surface. This is because, for example, the interface between the A layer and the B layer is rarely formed completely in parallel and linearly with the plate surface, and has a slight angle with the plate surface or is often uneven. Therefore, when the A layer and the B layer are defined in a region parallel to the plate surface in the present invention, it is assumed that there is a mixed region having both the characteristics of the A layer and the features of the B layer. is there.

Further, for example, as described later, when the crystal orientation of the A layer or the B layer is formed by crystal grain growth caused by diffusion of ferrite-forming elements and transformation behavior related thereto, {200} plane orientation grains or {222} It is also assumed that crystal grains other than {200} plane orientation grains or {222} plane orientation grains inevitably remain at the growth end point of plane orientation grains.
Under such circumstances, in the present invention, the presence of a metal layer that is not classified as either the A layer or the B layer is allowed.

Metal plate configuration (laminated structure)
In the metal plate of the present invention, the A layer, the B layer, and the C layer described above exist in a state of being laminated in the plate thickness direction. However, the arrangement is necessary for the plate surface and the plate surface on the opposite side of the plate surface. That is, a layered structure in which an A layer exists between the B layer first confirmed toward the plate surface. The metal plate of the present invention must satisfy this condition for both the front and back surfaces of the metal plate.
As a specific example, the simplest configuration is “ABA”.
The present invention is not limited to this, and for example, “ACBCA”, “CABAC”, and the like are possible, and it is not necessary to be an object with respect to the thickness center. For example, configurations such as “ACBA”, “CACBABA” Is possible.

In addition, the A layer, the B layer, and the C layer constituting the metal plate of the present invention are defined by the orientation of the crystal plane and the magnetostriction. When each of these layers has two or more layers, they have the same orientation. It need not be magnetostrictive. For example, if the A1 and A2 layers satisfy the definition of the A layer but have different orientation and magnetostriction, and the B1 and B2 layers satisfy the definition of the B layer but have different orientation, A configuration such as “B-A2” or a configuration such as “A1-B1-C-B2-C-A2” may be used.
Of course, when “ABA” is simply used as described above, the crystal plane orientation and magnetostriction may vary in the thickness direction in each of the A and B layers. That is, a configuration such as “A1-A2-B1-B2-A1-A2” can be simply expressed as “ABA”. In general, for example, even in the configuration of “ABA”, it can be said that the orientation and magnetostriction are usually accompanied by some variation in the thickness direction in the A layer.

(thickness)
The total thickness of the soft magnetic Fe-based metal plate of the present invention is preferably 0.03 mm to 1.5 mm. When the thickness of the plate is 0.03 mm or less, it takes time and labor to laminate the core member produced from the soft magnetic Fe-based metal plate on the magnetic core, resulting in poor productivity. Moreover, when thickness exceeds 1.5 mm, an eddy current will become large and an iron loss will increase. More preferably, it is 0.05 mm or more and 1 mm or less.

The thickness of the A layer that is first confirmed from the plate surface toward the plate surface opposite to the plate surface is preferably 70 to 97% with respect to the plate thickness of the entire metal plate. If this value is not 70% or more, it is difficult to obtain a high magnetic flux density as a whole metal plate. On the other hand, when this value exceeds 97%, the B layer becomes thin, and the effect of suppressing the reduction in iron loss under the in-plane compressive stress during the production of the core material cannot be sufficiently obtained.
The C layer is inevitably present in the measurement, and will be described later. However, since the merit in terms of the magnetic interaction between the layers is reduced, the total of the C layers in the entire metal plate of the present invention is reduced. The thickness is smaller than the total thickness of each of the A layer and the B layer, and the thinner the thickness when it is, the better.

(Integration of each layer and interface)
As described above, the metal plate of the present invention has a structure in which the A layer, the B layer, and the C layer are laminated, but the integration method is not particularly limited. Simply, a material having a special function such as an adhesive may be interposed between the layers and integrated. However, in this case, the effect of the magnetic interaction between the respective layers, particularly between the A layer and the B layer, which is an original feature of the present invention, becomes very small. That is, if a non-metal or non-magnetic material such as an adhesive is interposed between the A layer and the B layer, the magnetic interaction between each layer is reduced, so that deterioration of magnetic characteristics under in-plane compressive stress is avoided. The effect is reduced.

For this reason, in the present invention, the A layer, the B layer, and the C layer are preferably integrated by direct metal bonding, and in particular, a situation where Fe atoms exhibiting ferromagnetism are continuously connected is preferable. Specifically, if the difference in Fe concentration is 1.0% or less at a distance of 10 μm from each interface to each adjacent layer, the magnetic interaction characteristic of the present invention can be fully utilized. .
The effect of avoiding the deterioration of the magnetic characteristics under the in-plane compressive stress due to the magnetic interaction is mainly due to the magnetic interaction between the A layer and the B layer, and the A layer and the B layer are continuously laminated. It is preferable. When the C layer is interposed between the A layer and the B layer, it is preferable that the thickness of the C layer is thin.
The Fe concentration distribution at the interface of each layer can be measured by EPMA line analysis in the thickness direction across the interface in a cross section including the interface.

As described above, the above magnetic interaction and effect are manifested in relation to the magnetostriction of the A layer, the laminated structure of each layer, and the coupling state (interface structure) of each layer. This mechanism is considered as follows.
In general, when compressive stress acts on the plate surface, the magnetic characteristics deteriorate due to the following phenomenon.

In a magnetic material with a general magnetostriction constant having a positive value, the magnetization vector has the same orientation with respect to tensile stress, but the direction of the perpendicular direction with respect to compressive stress reduces the energy of the system. . For this reason, when a compressive stress acts on the plate surface, the magnetization vector deviates from the plate surface direction and increases the component in the plate thickness direction. Since the metal plate of the present invention is used by applying a magnetic field in the plate surface, it is not preferable for improving the magnetic flux density that the magnetization vector deviates from the plate surface. When an alternating magnetic field is applied, if the plate thickness direction component of the magnetization vector increases, the eddy current generated on the vertical plane of the magnetization vector increases the current flowing in the plate surface. Comparing the case where the current flows in the plate surface and the case where the current flows in the plate cross section, the eddy current loss increases because the specific resistance decreases when flowing in the plate surface having a large area.
On the other hand, when the magnetostriction constant is negative, the magnetization vector does not deviate from the plane of the plate even if a compressive stress is applied in the direction of the plane of the plate. If there is a vector, it comes to face in the plane of the plate, which is preferable for improving the magnetic flux density. Since the eddy current flows in the cross section of the plate having a large specific resistance, eddy current loss is also suppressed.

  Further, when the A layer and the B layer having different magnetic properties are integrated as in the metal plate of the present invention, a magnetic interaction mainly composed of a magnetic dipole interaction works between the layers. In general, the behavior in an orientation with a low coercivity follows the behavior in an orientation with a high coercivity. That is, the A layer oriented in the {200} plane orientation with low coercivity follows the behavior of the B layer oriented in the {222} plane orientation with high coercivity.

  Based on the two basic phenomena described above, in the present invention, the A layer has a negative magnetostriction constant, but the B layer has a negative magnetostriction constant. However, the magnetization vector can be maintained in the in-plane direction. As a result, the layer A, which is inherently susceptible to the effects of in-plane compressive stress, is less susceptible to the in-plane compressive stress, and the metal plate as a whole is less susceptible to in-plane compressive stress. Magnetic property deterioration due to is avoided.

(composition)
The composition of the soft magnetic Fe-based metal plate of the present invention is not particularly limited. What is necessary for the composition is that it is an “Fe-based metal”. This is because the metal plate of the present invention is used as a motor core material and requires various magnetic properties.
In the present invention, the “Fe-based metal” is an average composition of the entire metal plate and contains 70% or more of Fe. As a general example of an Fe-based metal, C: 1 ppm to 0.02%, pure iron composed of the balance Fe and inevitable impurities, C: carbon steel containing 0.02 to 0.2%, and as appropriate, , Steel containing additive elements, C: 0.1% or less, silicon steel having Si: 0.1-2.5% as a basic component, Mn: 0.02-3%, P: 0.3 Examples include various known steels including% or less, S: 0.05% or less, Al: 4% or less, and N: 0.1% or less.

The Fe-based metal plate of the present invention comprises an A layer and a B layer of different materials, and a C layer depending on the situation, but the composition of these layers is not particularly limited. However, in order to exhibit the magnetic properties required in the present invention, the A layer and the B layer are required to be Fe-based metals. The C layer is also preferably an Fe-based metal because it directly affects the magnetic properties and contributes to the magnetic interaction when interposed between the A and B layers.
Each layer need not have a different composition. However, since each layer has a difference in material, it is common to have a difference in composition, and that is not a problem.

In the present invention, it is meaningless to consider the average composition of the entire metal plate. This is because, in the present invention, it is particularly important to control the crystal orientation and magnetostriction of the A layer and the B layer. For this reason, the composition of each layer is considered, but the composition of the entire metal plate further includes the thickness of each layer. This is because the relationship with the characteristics of the metal plate is small because it depends on the laminated structure including the metal layer.
Furthermore, even if each layer is viewed individually, a uniform composition in each layer is not a necessary condition for the manifestation of the effects of the present invention, and for example, component variations in the thickness direction are allowed.

Since this may be the case, what is preferable regarding the average composition for each layer will be described below.
The chemical composition of the A layer is, for example, Al, Cr, Ga, Ge, Mo, Sb, Si, Sn, Ta, Ti, which are generally used in electrical steel sheets controlled to include many {200} plane orientations. The composition contains one or more of V, W, and Zn.
The chemical composition of the B layer is, for example, a composition that is generally used in electrical steel sheets to control necessary characteristics, and further includes any one or more of Si, Al, V, Ti, and Sn to control magnetostriction. It becomes. In particular, in order to set the magnetostriction to a negative value, Si = 0 to 1.5%, Al = 0 to 3.5%, V = 0 to 6.5%, Ti = 0 to 3%, Sn = 0 to It is preferable to make it contain in 4% of range.
Similarly to the A layer and the B layer, the C layer may be composed of an element that is generally used in an electromagnetic steel sheet.
Even if each layer further contains an element other than the above for a known specific purpose, the effects of the present invention are not lost.

  Further, depending on the production method, the layers of the metal plate of the present invention may be assumed to have a nonuniform composition within each layer. That is, if the metal plate is viewed in the thickness direction, a region where the concentration of elements other than Fe is considerably high and the Fe concentration is less than 70% is also assumed. Such a situation is not preferable for the metal plate of the present invention utilizing the magnetic properties of Fe atoms, which are ferromagnetic materials, as described above. In particular, if there is a region where the Fe concentration is less than 70% in the transition region between the A layer and the B layer where magnetic interaction between the A layer and the B layer occurs, the interaction is inhibited.

(Other)
The metal plate of the present invention may be coated as is known in general electromagnetic steel sheets. Such a coating does not lose the effect of the present invention.

Method for Producing Soft Magnetic Fe-Based Metal Plate The soft magnetic Fe-based metal plate having a plurality of crystal orientation layers of the present invention is obtained, for example, through the following steps.
Below, it demonstrates in order of the preparation of the raw material regarding A layer, the preparation of the raw material regarding B layer, integration of this raw material, and the heat processing of the integrated material.

(Material that forms layer A)
As a material for forming the layer A for example, Fe-based metal plate having a composition may result in containing and alpha-gamma transformation 70 mass% or more Fe (hereinafter referred to as metal plate _{A 1)} 97 percent 99.99 Or a metal containing at least one ferrite-forming element of Al, Cr, Ga, Ge, Mo, Sb, Si, Sn, Ti, V, W, and Zn on the surface thereof. metal plate adhered with alloy (hereinafter referred to as metal plate a ₂₎ can be used.
The metal plate A ₂ is processed and heat treated as described below, can be finally formed a region corresponding to the A layer in the present invention the metal plate.

Here the assumed that the composition of the metal plate A ₁ as the material can result in alpha-gamma transformation, in the heat treatment described later, to increase the {200} plane integration of the A layer by utilizing the alpha-gamma transformation It is. In the method described in this manufacturing method, the ferrite-forming elements from the surface toward the inside of the metal plate A ₂ is occurred locally see the considerable Zaru composition change alloyed, the at least a portion alpha-gamma transformation It changes to a composition (α single phase composition) that cannot be generated. The composition that can cause the α-γ transformation needs to be the metal plate A _{1 as} a raw material, and finally the entire region corresponding to the metal plate A ₁ changes to the α single-phase composition. The situation is also conceivable. Details will be described later.

It should be noted that the metal plate A ₁ used above has a composition that changes in a direction in which the ferrite-forming element finally adhered to the surface penetrates by diffusion and the Fe concentration decreases. It is necessary to set the Fe content so that the layer has a composition equivalent to the Fe-based metal. It is easy for those skilled in the art having ordinary metallurgy knowledge to appropriately control this by the kind and thickness of the metal deposited on the surface, the degree of alloying by diffusion, and the like.

(Material that forms layer B)
As a material for forming the B layer, for example, Fe-based metal plate which can cause alpha-gamma transformation containing 70 mass% or more Fe (hereinafter, a metal plate B ₁ and referred) reduction below 95% 30% or more cold rolling at a rate, Si on the surface, Al, Sn, metal plate to adhere the metal or alloy containing at least one or more of ferrite forming elements of Ti and V to (hereinafter referred to as metal plate B ₂₎ Can be used.

Here the assumed that the composition of the metal plate B ₁ as the material can result in alpha-gamma transformation, in the heat treatment described later, to increase the {222} plane integration of the B layer by utilizing the alpha-gamma transformation As in the case of the metal plate A ₁ , there is a possibility that the composition changes due to the heat treatment and that at least a part of the composition in the region corresponding to the metal plate B ₁ eventually changes to one that cannot cause the α-γ transformation. It is. Details will be described later.
Regarding the Fe concentration of the Fe-based metal plate B ₁ used above, the same caution as for the metal plate A ₁ is necessary.

The thicknesses of the Fe-based metal plate A ₁ and the Fe-based metal plate B ₁ may be determined so that the final thickness of the Fe-based metal plate of the present invention is 0.03 mm or more and 1.5 mm. However, it is desirable that the thickness be 0.01 mm or more from the viewpoint of manufacturing and handling.

The ferrite-forming element can be attached to each metal plate by a hot dipping method, an electroplating method, a dry process method, a rolling clad method, or the like, and any method may be used.
The thickness of the ferrite-forming element attached to each metal plate is preferably 0.05 μm or more. If the thickness is less than 0.05 μm, it is not possible to obtain an A layer or a B layer having a sufficient {200} plane or {222} plane integration degree in the heat treatment step described later.
Further, in the method described here, the metal plate of the present invention may eventually have a considerable concentration variation in the plate thickness direction, but the final metal plate of the present invention will be covered over the entire plate thickness. Since the concentration of Fe, which is a ferromagnetic element, is preferably 70% or more, the maximum thickness of the ferrite-forming element layer formed on the surface of the metal plate A ₂ or B ₂ is the heat treatment condition described later. In view of the above, it is preferable to set so as to sufficiently alloy with the Fe-based metal plate A ₁ or the Fe-based metal plate B ₁ after the heat treatment.

The metal plate A ₁ and the metal plate B ₁ represents, to be able to use a Fe-based metal plate of the same composition, it is also possible to use a Fe-based metal plate of a different composition.
Furthermore, to the ferrite forming elements you can also use the same element in the metal plate A ₂ and the metal plate B _2, can also be used in combination of different elements.
By using the Fe-based metal plate having the same composition in the metal plate A ₁ and the metal plate B ₁ and using the same element in the metal plate A ₂ and the metal plate B ₂ as the ferrite-forming element, the average composition of the entire metal plate is generally It is also possible to use an Fe-based metal plate formed of a plurality of layers that are substantially the same as a typical single-layer metal plate and have different crystal orientation and magnetostriction constant.

(Laminated metal plate _{A 2} and the metal plate _{B 2)}
The metal plate A ₂ and the metal plate B _2, the first metal plate to be verified are stacked such that the metal plate A ₁ toward the opposite surface of the surface from the outermost surface of the laminate. In this way, after the heat treatment described later, in the final metal plate of the present invention, the plate surface and the B layer first confirmed from the plate surface toward the plate surface opposite to the plate surface It can be set as the laminated structure in which A layer exists in between.

  Eventually, the metal plates are integrated by metal bonding by mutual diffusion by heat treatment described later. However, if the metal plates are simply stacked and heat-treated, the gaps between the opposing surfaces of the metal plates will remain after heat treatment. Remaining or facing surfaces oxidize and remain, which tends to hinder integration. For this reason, it is desirable to remove the foreign matters by cleaning the surface of each steel plate before lamination, for example, pickling or reverse sputtering is desirable to bring out a new surface. Further, it may be bonded at a low temperature before heat treatment or may be joined by electric discharge. To prevent oxidation and nitridation of the laminated voids of each metal plate during heat treatment, the voids are evacuated in advance to remove oxygen and nitrogen from the vicinity of the surface, and then the periphery of the laminate is sealed to remove oxygen and nitrogen from the external atmosphere. It is also effective to prevent intrusion and to make the heat treatment atmosphere an inert gas. It is also effective to apply a load in the stacking direction during heat treatment.

(Heat treatment of laminate)
The laminated body prepared as described above is subjected to a heat treatment, and ferrite forming elements on the surfaces of the metal plates A ₂ and B ₂ are diffused in each metal plate and to each other so that each metal plate is integrated and at the same time each metal plate. Using the recrystallization and transformation of A, an A layer having a high {200} plane integration degree and a B layer having a high {222} plane integration degree are formed. Further, in the B layer, the ferrite-forming element is diffused and alloyed so that the saturation magnetostriction value becomes negative.

In order to make the above, the laminated body, it is necessary to heat up both metal plate A ₁ and the metal plate B ₁ is equal to or larger than A3 point. Along with the transformation from the γ phase to the α phase in the process of cooling from the A3 point or higher, in the region that was originally the metal plate A ₁ , α phase grains having a {200} plane orientation grew preferentially. In the region that was the metal plate B ₁ , α-phase grains having the {222} plane orientation grow preferentially, so that the {200} plane integration degree is increased in the A layer and the {222} plane integration degree is increased in the B layer. Can be made.

This mechanism is described in detail in Patent Documents 1 and 2, and will be briefly described here together with a range of heat treatment conditions in the present invention.
In the following, the A layer will be described, and the situation in which the ferrite-forming element is Al and the {200} plane integration degree will be described.
Heating the laminate, the area of the metal plate A ₁ that cold working has been performed to start the re-crystallization. In the metal plate A _1, orientation oriented in {100} for cold rolling rate is preferably controlled to a relatively large number generation. Further, Al adhering to the metal plate A ₁ diffuses into the metal plate A ₁ as the temperature rises, and the region where the Al concentration is increased due to alloying becomes an α single phase component.

The laminate is further heated and held at a temperature of not less than A3 and not more than 1300 ° C.
In the region already having an α single phase component, {100} oriented grains generated by recrystallization are preserved as they are, and {100} oriented grains are preferentially grown in the region, and the {200} plane integration degree is increased. To increase. In this case, the region not α single phase composition (the center side region of the original metal plate A ₁₎ is transformed into γ phase from α phase.
Holding in this temperature range, single phase composition region α with the diffusion of Al spreads toward the center of the original metal plate A _1. This region which has been transformed into γ phase in the center side region of the original metal plate A ₁ because gradually transformed into α phase again from the surface side region of the original metal plate A _1. At that time, the crystal grains in the α phase region having the α single phase composition and the {100} orientation grains preferentially growing grow on the γ phase side. For this reason, the γ phase is transformed in the form of taking over the crystal orientation of the α single phase region, and as the retention time increases, the {200} plane integration degree of the region that was the original metal plate A ₁ further increases. Go.
Development of such a {100} oriented grains takes place even the Fe atoms of a metal plate A ₁ side diffuses into the original metal plate A ₁ in Al layer that has adhered to the surface. As a result, so that the {200} plane integration throughout the original metal plate A ₂ region is increased.

When the original metal plate A ₂ region is held at A3 or higher until it is alloyed as an α single-phase composition, the entire structure of the original metal plate A ₂ region is already highly integrated in the {200} plane. Since it is formed, it is maintained even after cooling.
Also, if it is not alloyed until α single phase composition throughout the original metal plate A ₂ region, the central region of the original metal plate A ₂ has residual γ phase, which during cooling α Transform to phase. At this time, similarly to the above, the γ phase region is transformed by taking over the crystal orientation of the α phase grains. As a result, the degree of alloying independently, high layer of {200} plane integration throughout the original metal plate A ₂ regions, i.e. A layer can be formed.

The same behavior applies to regions about the original metal plate B _2, a high layer of {222} plane integration throughout the original metal plate B ₂ region, i.e. B layer can be formed.

Regarding the heat treatment conditions, the above-mentioned diffusion phenomenon and transformation behavior itself are basically general phenomena, and those skilled in the art having knowledge of ordinary metallurgy should control in detail to control this. Is easy.
It should be particularly noted in the present invention that if the diffusion becomes excessive, for example, if the diffusion proceeds between the A layer and the B layer, the boundary of the region having an appropriate crystal orientation and magnetostriction constant is lost. Such a region also corresponds to the above-described C layer. Those skilled in the art who also have knowledge of ordinary metallurgy are easy to adjust, but excessive heat treatment should be avoided.
Further, for example, depending on the thickness of the metal plate A _{1 and} the amount of ferrite-forming elements attached thereto, when diffusion proceeds by heat treatment, all of the original metal plate A ₂ region becomes an α-γ two-phase region during the heat treatment. turn into. Such a situation is not preferable because the crystal orientation from the α single phase region to the γ phase region as described above becomes insufficient. In the case of such a configuration, it is preferable to cool while the α single-phase region remains to transform the whole into the α phase.

In addition, for the B layer, depending on the degree of alloying in consideration of the metal plate B ₁ , the type and amount of ferrite-forming elements selected from Si, Al, Sn, Ti and V to be adhered, and the heat treatment conditions, The magnetostriction constant is controlled to be within the range of the present invention. Since there are many cases of this condition due to the above factors, they are not described here, but only shown in the examples described later. It is easy for a person skilled in the art with knowledge of ordinary metallurgy to alloy to an appropriate composition using the diffusion phenomenon.

  The Fe-based metal plate of the present invention configured as described above will be described in more detail with reference to examples.

(Production of metal plates A ₁ and B ₁ )
C in Table 1 as a metal plate A _1, prepared Fe-based metal component system shown in D and F, were prepared Fe-based metal component system shown in A and B of Table 1 as a metal plate B _1. The A3 point of each component system is shown in Table 1.
First, ingots having respective compositions were melted by vacuum melting, and then processed to a predetermined thickness by hot rolling and cold rolling.
Preparation of the metal plate A ₁ was performed as follows. In hot rolling, an ingot having a thickness of 250 mm heated to 1200 ° C. was thinned to a thickness of 50 mm to 3 mm. For the hot-rolled sheet thinned to 3 mm, after removing the scale from the surface, it is cold-rolled to a minimum thickness of 0.4 mm, and the cold-rolled material of each thickness is subjected to heat treatment at 800 ° C. for 600 seconds in nitrogen gas. And recrystallized to remove strain. The surface scale of the hot rolled sheet of 50 mm to 3 mm was also removed. Subsequently, the thickness was reduced from 50 mm to 0.4 mm to 0.7 mm to 0.01 mm by final cold rolling.
Preparation of the metal plate B ₁ represents, was performed as follows. In hot rolling, an ingot having a thickness of 250 mm heated to 1200 ° C. was thinned to a thickness of 3 mm. After removing the scale from the surface of the hot-rolled sheet, the thickness was reduced to 2.0 mm to 0.02 mm by cold rolling. Further, a heat treatment was performed in nitrogen gas at 800 ° C. for 600 seconds to recrystallize and remove the strain. Subsequently, the thickness was reduced to 0.2 mm to 0.005 mm by final cold rolling.
Table 2-1, Table 4-1, Table 6-1, Table 8-1, cold rolled front plate thickness of the final cold rolling of the metal plate _{A 1} and the metal plate _{B 1} produced cold rolled KoitaAtsu, and The rolling ratio is also described.

A film was formed on both surfaces of each metal plate by attaching ferrite-type forming elements.
The metal plate _{A 1} is, Zn, Sn, Al, Si , Ti, Mo, V, Cr, to form one of the W layer, the metal plate _{B 1} represents, Si, Al, V, Ti, and Sn layer Either formed. Sn was formed by electroplating or hot dipping, and Zn and Al were formed by hot dipping. However, the sputtering method was used when the thickness of Al deposited was 1 μm or less. Others were performed by ion plating (hereinafter referred to as IP method) and sputtering method.
The types and adhesion thicknesses of the ferrite-type forming elements and the amounts of ferrite-type forming elements (described as coating elements) are also described in the respective tables. The amount of the coating element, by summing the adhesion amount and the content of the metal plate A _1, was determined by mass% to the total (mass% as indicated).

Each metal plate A ₂ and B ₂ to which the ferrite-forming element is attached is laminated in combination as shown in Table 2-1, Table 4-1, Table 6-1, and Table 8-1, and joined to form a laminate. Then, the laminate was heat treated to produce a soft magnetic Fe-based metal plate to be a product plate. The joining method, thickness, and heat treatment conditions are shown in Table 2-2, Table 4-2, Table 6-2, and Table 8-2.
When the metal plates A ₂ and B ₂ were joined by the roll pressure bonding method, the surface of each metal plate was degreased before roll pressure bonding so that a new surface appeared.
A gold image furnace is used for heat treatment of the laminate, and the heating rate is set to 10 ° C./min under program control, and the heating temperature and the holding time at that temperature are shown in Table 2-2, Table 4-2, Table 6-2, Control was performed under the conditions described in Table 8-2. The temperature raising and holding were performed in an atmosphere evacuated to a level of 10 ⁻³ Pa. At the time of cooling the laminated body, Ar gas was introduced and cooled at a cooling rate of 100 ° C./min by adjusting the flow rate.

  Various test pieces were produced from the obtained product plate, the following measurements were performed, and the results are shown in Table 3, Table 5, Table 7, and Table 9.

The thickness of the product plate and the thickness of each layer were determined from observation of the structure of the cross section of the product plate. At that time, the bonding state of each phase was determined from the structure photograph. When no gap or the like was found between the layers, it was determined that they were “integrated”.
The {200} plane integration degree and the {222} plane integration degree in the plate thickness direction are as described above for each region obtained by observing the crystal structure in the plate thickness direction and dividing in the plate thickness direction into a thickness corresponding to the average crystal grain size. Measured by the X-ray diffraction method. A method of repeating mechanical polishing and chemical polishing with emery paper from the surface of the product plate was used as a method of obtaining each X-ray measurement surface in the plate thickness direction.

  Furthermore, for the B layer having a {222} plane integration degree of 55% or more and 99% or less, the region other than the B layer is removed by the above-described mechanical polishing or chemical polishing, and only the B layer is taken out. Average saturation magnetostriction was measured. Specifically, for the extracted B layer, the saturation magnetostriction is measured over 360 ° every 22.5 ° within the plate surface. At this time, after applying a magnetic field of 800 kA / m perpendicularly to each direction and measuring the magnetostriction based on the magnetic field 0 with a strain gauge or the like, the difference between the magnetostriction in the target direction and the magnetostriction in the perpendicular direction is measured. The value obtained by multiplying by 2/3 is the saturation magnetostriction in each direction, and was obtained as an average value in each direction. When the plate thickness is thin, it is difficult to measure the strain. In that case, a plurality of cut samples were stacked in the same direction and measured.

  In this way, for each test piece, the laminated structure of the A layer in the plate thickness direction (the A layer on the other side is described as the A ′ layer in the table), the B layer, and the C layer (other than A and B layers). It was determined.

  The iron concentration at the interface was examined. The measurement was performed by EPMA. The measurement position is 21 points in total from the interface position to the distance of 10 μm from the interface at a pitch of 1 μm on each side. The difference between the maximum value and the minimum value among the 21 points is defined as the “Fe concentration difference at the interface”. The maximum value of the measurement results at a plurality of locations was defined as “the maximum value of the Fe concentration difference at the interface”. Measurements were made at five locations at one interface, and when there were multiple interfaces, measurement was made at five locations at each interface. However, when the thickness of the layer was less than 10 μm, only the thickness of the layer was measured, and the difference between the maximum value and the minimum value among the measurement points of less than 21 points was obtained.

Evaluation of magnetic characteristics was performed using SST (Single Sheet Tester). For the magnetic flux density, the magnetic flux density B ₅₀ for a magnetizing force of 5000 A / m was determined. At this time, the measurement frequency was 50 Hz. Furthermore, the iron loss was measured as W10 / 800 at a frequency of 800 Hz in an exciting magnetic field with a magnetic flux density of 1.0T. The presence or absence of magnetic property deterioration when compressive stress was applied to the plate surface was examined by applying 30 MPa compressive stress to the sample parallel to the measurement direction during SST measurement.

Tables 2 and 3 show examples No. 1 to No. 24 and comparative examples.
In the comparative examples of No. 1, No. 2 and No. 11, since the {222} plane integration degree of the B layer is less than 55%, the proportion of crystals facing the [110] direction in the plate surface is The saturation magnetostriction is not reduced to −0.2 × 10 ⁻⁶ or less. Therefore, when the rate of increase in iron loss due to compressive stress loading is viewed as a ratio of iron loss after compressive stress loading to iron loss before compressive stress loading (simply described as “after loading / before loading”), It is larger than 1.3 times.
In the comparative examples of No. 3, No. 4, and No. 6, since the saturation magnetostriction of the B layer is more than −0.2 × 10 ⁻⁶ , iron loss deterioration due to compressive stress load is When viewed from the previous ratio, it is 1.3 times or more.
In the comparison of the examples of No. 7 to No. 10, as the saturation magnetostriction decreases toward the negative value, the value of the ratio after load / before load becomes smaller and the iron loss deterioration is further suppressed. I understand.
In the examples of No. 13 to No. 18, the {222} plane integration degree increases from 57% to 93% from No. 13 to No. 18, but in this range of integration degree, Iron loss deterioration due to compressive stress loading is stably suppressed.
In the comparative examples of No. 1, No. 5, and No. 12, the {200} plane integration degree of the A layer is less than 25%, so that the magnetic flux density B ₅₀ is a low value of 1.6 T or less. Yes. On the other hand, in the embodiment in which the {200} plane integration degree of the A layer is 25% or more and the {222} plane integration degree is 40% or less, the level exceeds 1.75T, and in part exceeds 1.9T. A high B ₅₀ is also achieved.

Tables 4 and 5 show examples No. 31 to No. 57.
In each example, the C layer was formed at the interface when the ferrite-forming elements to be deposited were Ti, W, and Mo. The thicknesses of these C layers were all 3 μm or less. In the case of elements other than these, the C layer could not be confirmed.
In the examples of No. 31 to No. 57, the B layer has an αFe phase {222} plane integration degree of 55% or more and 99% or less with respect to the plate surface, and the average saturation magnetostriction in the plate surface is −0. In order to satisfy .2 × 10 ⁻⁶ or less, iron loss deterioration due to compressive stress load is simultaneously suppressed.
Further, {200} plane integration of αFe phase layer A with respect to the plate surface is 25% or more, since the {222} plane integration of αFe phase satisfies 40% or less, a high _{B 50} is obtained.

Tables 6 and 7 show Examples No. 61 to No. 66. Table 7 shows the result of changing the difference in Fe concentration at the interface by using the laminate prepared in Tables 2 and 4 as shown in Tables 6-1 and 2 and heat-treating under different conditions as shown in Table 6-2. It is a thing.
As the Fe concentration difference at the interface increases from No. 61-1 to No. 61-5, the rate of increase in iron loss when a compressive stress is applied increases, and the difference in Fe concentration exceeds 1.0%. The iron loss increase rate is 1.1 times or more, increasing by 10% or more. This means that the magnetic interaction at the interface can be fully utilized as the Fe concentration difference increases. No. 62-1 to No. 62-4, No. 63-1 to No. 63-4, No. 64-1 to No. 64-4, No. 65-1 to No. 65-4, and The same applies to the comparison of each of No. 66-1 to No. 66-4.

Tables 8 and 9 show examples No. 71 to No. 84.
In No. 71, the total plate thickness is thinner than 0.024 mm and 0.03 mm, and the total plate thickness of both surfaces of the A layer is 66.7% and less than 70% of the total plate thickness. In this case, since the overall plate thickness is too thin, it becomes easy to bend during handling, and the influence increases the iron loss increase rate due to the compressive stress load, and the ratio of the B layer increases and the ratio of the A layer increases. Since it decreases, the magnetic flux density B ₅₀ also decreases. As the overall plate thickness increases from No. 71 to No. 78, the iron loss increases. With No. 78 having an overall plate thickness of 1.6 mm, the iron loss exceeds 50 W / kg. This is because eddy current loss increases as the overall plate thickness increases. Further, as the overall plate thickness increases, B ₅₀ decreases because the {200} plane integration degree decreases.
From No. 79 to No. 84, it can be seen that B ₅₀ tends to increase as the ratio of the total thickness of the A layer on both sides to the total thickness increases. This is because the thickness ratio of the A layer having a high {200} plane integration degree, which has a large effect due to the improvement of B ₅₀ , is relatively increased. No. In No. 79, since the total thickness of the A layer on both sides is 66.7% of the total plate thickness, which is lower than 70%, B ₅₀ is low. In No. 84, the ratio of the total A layer on both sides to the total plate thickness is 98.4%, which is larger than 97%. In this case, since the B layer becomes too thin, the effect of suppressing an increase in iron loss due to a compressive stress load is reduced.

Claims (6)

In the soft magnetic Fe-based metal plate having a plurality of crystal orientation layers in the plate thickness direction,
Contains at least one ferrite-forming element of Al, Cr, Ga, Ge, Mo, Sb, Si, Sn, Ti, V, W, and Zn, and has a {200} plane integration degree of 25% or more of the αFe phase with respect to the plate surface Then, the region where the {222} plane integration degree of the αFe phase is 40% or less is defined as A layer,
At least one ferrite-forming element of Si, Al, Sn, Ti, and V, in mass%, Si = 0 to 1.5%, Al = 0 to 3.5%, Sn = 0 to 4%, Ti = In the range of 0 to 3% and V = 0 to 6.5%, the {222} plane integration degree of the αFe phase with respect to the plate surface is 55% or more and 99% or less, and the average saturation magnetostriction in the plate surface is − A region that is 0.2 × 10 ⁻⁶ or less as a B layer,
The A layer and the B layer exist in the thickness direction,
And on both surfaces of a metal plate, it becomes a laminated structure in which an A layer exists between the plate surface and the B layer first confirmed from the plate surface toward the plate surface opposite to the plate surface. And
A metal plate, wherein the interface between the A layer and the B layer is integrated by metal bonding . In the soft magnetic Fe-based metal plate having a plurality of crystal orientation layers in the plate thickness direction,
The region that is neither the A layer nor the B layer is a C layer, and the A layer, the B layer, and the C layer exist in the thickness direction ,
Interface of the A layer and the B layer, further, the metal plate according to claim 1, the interface of A layer and B layer and the C layer is characterized that you have been integrated with a metal bond. In the soft magnetic Fe-based metal plate having a plurality of crystal orientation layers in the plate thickness direction,
When the A layer, the B layer, and the C layer are present, the difference in Fe concentration in the region at a distance of 10 μm from the interface between the C layers on both sides is 1.0% or less. The metal plate according to claim 1 or 2 . In the soft magnetic Fe-based metal plate having a plurality of crystal orientation layers in the plate thickness direction,
For the A layer, according to any one of claims 1 to 3, wherein the sum of the surfaces of the thickness of the closest A layer on the plate surface is 70 to 97% relative to the thickness of the entire Metal plate. In the soft magnetic Fe-based metal plate having a plurality of crystal orientation layers in the plate thickness direction,
The thickness of this metal plate is 0.03 mm or more and 1.5 mm or less, The metal plate of any one of Claims 1-4 characterized by the above-mentioned. In the production of a soft magnetic Fe-based metal plate having a plurality of crystal orientation layers in the plate thickness direction,
The metal plate _{A 1} having the composition which can cause alpha-gamma transformation contains 70 mass% or more Fe and cold rolling at 97 percent 99.99% less reduction ratio, Al on the surface of that, Cr, Ga , and Ge, Mo, Sb, Si, Sn, Ti, V, a metal plate is adhered at least one kind of ferrite forming elements of W and Zn and the metal plate _{a 2,}
A metal plate _{B 1} having a composition that may occur were alpha-gamma transformation containing 70 mass% or more Fe and cold rolling at a reduction ratio of 95% or more and 30% or less, Si in the surface of that, Al, Sn, Ti and a metal plate obtained by attaching at least one kind of ferrite-forming elements V and the metal plate B _2,
A material obtained by laminating at least a metal plate A ₂ and the metal plate B _2,
Heat treatment at a temperature equal to or higher than the α-γ transformation point,
Soft Fe-based method for producing a metal plate according to any one of claims 1 to 5, characterized in that diffusing the ferrite forming elements into the interior of the metal plate A ₁ and the metal plate B _1.