JP6405632B2 - Fe-based metal plate and manufacturing method thereof - Google Patents

Description

  The present invention is particularly suitable for applications such as electric motors, generators, transformer cores, and the like, and relates to an Fe-based metal plate with reduced iron loss that can contribute to downsizing and energy loss reduction of these magnetic cores and a method for manufacturing the same. .

  Conventionally, silicon steel plates have been used for magnetic cores of electric motors, generators, transformers and the like. A silicon steel plate is required to have a high value in the ratio B50 / Bs of the average magnetic flux density B50 to the saturation magnetic flux density Bs in a small excitation magnetic field and to have a low iron loss in an AC excitation magnetic field. In order to obtain the ratio B50 / Bs of the average magnetic flux density B50 to the high saturation magnetic flux density Bs, it is effective to integrate the <100> axis of the α-Fe phase, which is the easy magnetization direction, in the magnetic field direction to be used. Yes. Therefore, it is necessary to highly integrate the {100} plane of the α-Fe phase in the steel plate surface. On the other hand, the iron loss can be reduced by reducing the inclusions that obstruct the movement of the domain wall, or by increasing the electrical resistance to reduce the eddy current.

Regarding the Fe-based metal plate in which the {100} plane is highly integrated in the rolled surface and the ratio B50 / Bs of the average magnetic flux density B50 to the high saturation magnetic flux density Bs is obtained, the present inventors have previously described Patent Document 1 The following technologies have been proposed.
(A) a step of attaching a ferrite-forming element to one or both sides of a base metal plate made of a Fe-based metal of α-γ transformation; and (b) the base metal plate from point A3 of the base metal plate. And the ferrite-forming element is diffused in the base metal plate, and a part thereof is alloyed with the base material, and the {200} plane integration degree of the α-Fe phase in the alloyed region is 25% or more. 50% or less and a {222} plane integration degree of 40% or less, and (c) the base metal sheet was heated and held at a temperature of A3 or higher to be alloyed with a ferrite-forming element. Regarding the surface integration degree of the α-Fe phase, the step of increasing the {200} surface integration degree and decreasing the {222} surface integration degree; and (d) cooling the base metal plate to a temperature lower than the A3 point, When the γ-Fe phase in the non-alloyed region is transformed into the α-Fe phase, the α And a step of increasing the {200} plane integration degree of the Fe phase so that the {200} plane integration degree is 30% or more and 99% or less and the {222} plane integration degree is 30% or less. The manufacturing method of the Fe-type metal plate which has the high {200} plane integration degree characterized by these.

  Further, in order to reduce the iron loss, it has been carried out to increase the electric resistance to reduce the eddy current or to reduce the inclusions that obstruct the domain wall movement.

  In Patent Document 2, Sol. A unidirectional electrical steel sheet composed of secondary recrystallized grains containing Al in a range of 25 ppm to 300 ppm is subjected to cold rolling and a siliconizing treatment at 1050 ° C. to 1300 ° C. to obtain high magnetic flux density and low iron loss. A technique for obtaining compatible magnetic properties is described.

  Furthermore, in Patent Document 3, an Sn diffusion layer containing 1% by mass or more of Sn in the surface layer portion of the steel sheet and decreasing in the Sn amount from the outermost surface side toward the center portion is formed, and excellent in AC magnetic characteristics. Techniques for obtaining soft magnetic steel parts are described.

  However, in the technique described in Patent Document 2, a unidirectional electrical steel sheet having a uniform composition and already highly oriented in the {100} plane is subjected to a siliconization treatment to reduce the iron loss. It will take. Moreover, in the technique described in Patent Document 3, since deformation resistance and cold forgeability are also taken into consideration, it is difficult to achieve both high magnetic flux density and low iron loss at a high level.

International Publication No. 2011/052654 JP 2008-169450 A JP 2012-62503 A

  The present invention has been made in view of such circumstances, and an object of the present invention is to provide an Fe-based metal plate that is inexpensive, excellent in magnetic properties, and low in iron loss, and a method for manufacturing the same.

  The present inventors diligently studied and examined the iron loss of the Fe-based metal plate having a non-uniform composition. As a result, the inventors have found that when the ferrite-forming element is concentrated, a high degree of {200} plane integration is obtained, and the electrical resistance of the surface layer of the Fe-based metal plate is increased to suppress the skin effect. I found it. Furthermore, it has been found that the iron loss is remarkably reduced when the electric resistivity of the base metal plate is 38 μΩ · cm or more and the texture is controlled.

The present invention is as follows.
(1) An Fe-based metal plate having ferrite-forming elements concentrated on both sides,
The chemical composition at the center of the thickness of the Fe-based metal plate is, by mass, Si: 0.001% to 10.0%, Mn: more than 2.0% and 12.0% or less, and Al: 0.00. Fe-based components having a composition that contains 001% to 4.0% and the balance can cause an α-γ transformation that is iron and inevitable impurities,
When the electrical resistivity at the center of the thickness of the Fe-based metal plate is Ra and the electrical resistivity of the outermost layer is Rb, the electrical resistivity Ra at the center of the thickness is 38 μΩ · cm to 200 μΩ · cm, and the plate The electrical resistivity Ra of the thickness center portion <the electrical resistivity Rb of the outermost layer,
The X-ray random intensity ratios of {001} <470>, {116} <6 12 1>, {223} <692> on the surface of the Fe-based metal plate are A, B, and C, respectively, and Z = (A + 0 .98B) / (4 × 0.98C), an Fe-based metal plate wherein the Z value satisfies 0.5 <Z ≦ 50.
(2) The Fe-based metal plate according to (1), wherein a part or the whole of the region where the ferrite-forming element is concentrated is an α-Fe single phase.
(3) The Fe-based metal plate according to (1) or (2), wherein the electrical resistivity Ra at the central portion of the plate thickness is 45 μΩ · cm to 170 μΩ · cm.
(4) The ferrite-forming element is one or more elements selected from the group consisting of Al, Cr, Ga, Ge, Mo, Sb, Si, Sn, Ta, Ti, V, W, and Zn. The Fe-based metal plate according to any one of (1) to (3).
(5) A region that is 1.2 times or more the electrical resistivity Ra at the center of the plate thickness is formed from the outermost layer to a depth of x μm, x is 0.05 μm or more and 500 μm or less, and the plate thickness The Fe-based metal plate according to any one of (1) to (4), wherein
(6) A group in which the chemical component composition of the center portion of the thickness of the Fe-based metal plate is mass%, and consists of Cr: 0.001% to 9.0% and Ni: 0.001% to 8.0%. The Fe-based metal plate according to any one of (1) to (5), wherein the Fe-based metal plate includes one or two selected from the group consisting of iron and inevitable impurities.
(7) The Fe-based metal plate according to any one of (1) to (6), wherein a thickness of the Fe-based metal plate is 10 μm or more and 5 mm or less.
(8) A method of manufacturing a Fe-based metal plate having a high degree of {200} plane integration by attaching a ferrite-forming element on a base metal plate made of Fe-based metal, heat-treating and diffusing it,
In mass%, Si: 0.001% to 10.0%, Mn: more than 2.0% and 12.0% or less, and Al: 0.001% to 4.0%, with the balance being iron and inevitable When the electrical resistivity Ra is 38 μΩ · cm or more and 200 μΩ · cm or less when the electrical resistivity Ra is a composition that can cause an α-γ transformation that is an impurity and the central portion of the plate thickness is Ra, the both sides of the base metal plate A step of attaching a ferrite-forming element;
Heating the base metal plate to which the ferrite-forming element is adhered to A3 point of the base metal plate, and diffusing the ferrite-forming element into the base metal plate;
A step of further heating and holding the base metal plate in which the ferrite-forming element is diffused to a temperature of not less than A3 and not more than 1300 ° C .;
The base metal plate heated and held at a temperature not lower than A3 point and not higher than 1300 ° C. is cooled to a temperature lower than A3 point to transform the γ-Fe phase in the non-alloyed region into an α-Fe phase, The X-ray random intensity ratios of {001} <470>, {116} <6 12 1>, {223} <692> on the surface of the Fe-based metal plate are A, B, and C, respectively, and Z = (A + 0. 98B) / (4 × 0.98C), the Z value satisfies 0.5 <Z ≦ 50, and the electrical resistivity of the outermost layer is Rb, and the electrical resistance at the center of the plate thickness A step of obtaining an Fe-based metal plate satisfying a ratio Ra <the outermost layer electrical resistivity Rb ;
The manufacturing method of the Fe-type metal plate characterized by having.
(9) The ferrite-forming element is at least one element selected from the group consisting of Al, Cr, Ga, Ge, Mo , Sb, Si, Sn, Ta, Ti, V, W, and Zn. The method for producing an Fe-based metal plate according to (8), which is characterized.
(10) In the Fe-based metal plate, a region that is 1.2 times or more the electrical resistivity Ra of the thickness center portion is formed from the outermost layer to a depth of x μm, and x is 0.05 μm or more and 500 μm or less. And the Fe-based metal plate production method according to (8) or (9), characterized in that the thickness is less than ½ of the plate thickness.
(11) The base metal plate may be one or two selected from the group consisting of Cr: 0.001% to 9.0% and Ni: 0.001% to 8.0% by mass%. The method for producing an Fe-based metal plate according to any one of (8) to (10), wherein the balance is iron and inevitable impurities.
(12) The method for producing an Fe-based metal plate according to any one of (8) to (11), wherein the base metal plate has a thickness of 10 μm or more and less than 5 mm.

  According to the present invention, an Fe-based metal plate having excellent magnetic properties and low iron loss can be manufactured at low cost.

  Iron loss is expressed as the sum of eddy current loss and hysteresis loss. In the prior art, eddy current loss has been reduced by increasing the electrical resistance of the steel sheet or making it thinner. By concentrating ferrite-forming elements, the inventors increase the electrical resistance of the surface layer to suppress the skin effect, increase the electrical resistance at the center of the plate thickness, and control the texture of the steel plate. As a result, it was found that the iron loss was significantly reduced.

(Description of the basic principle of the present invention)
First, the X-ray random intensity ratios of {001} <470>, {116} <6 12 1>, {223} <692> on the surface of the Fe-based metal plate are A, B, and C, respectively, and Z = ( When A + 0.98B) / (4 × 0.98C), 0.5 <Z ≦ 50, and the electrical resistivity Ra at the central portion of the plate thickness is 38 μΩ · cm or more and 200 μΩ · cm or less, and the plate thickness A ratio B50 / Bs (hereinafter referred to as B50 / Bs value) of the average magnetic flux density B50 to the saturation magnetic flux density Bs higher than that of the prior art is obtained when the electric resistivity Ra of the central portion <the electric resistivity Rb of the outermost layer, and Explain the basic principle of low iron loss.

  In the present invention, an Fe-based component capable of causing α-γ transformation is used for the base metal plate, a ferrite-forming element is adhered to both surfaces thereof, and finally the ferrite-forming element is diffused to obtain a high B50 / Bs value and a low value. An Fe-based metal plate that causes iron loss is obtained.

  In the base metal plate, eddy currents are suppressed by adding Al, Si, Mn or the like so that the electric resistivity Ra is 38 μΩ · cm or more. Furthermore, the ferrite forming element is diffused on both surfaces of the base metal plate so that the electrical resistivity Ra of the central portion of the plate thickness <the electrical resistivity Rb of the outermost layer, thereby suppressing the skin effect particularly in the high frequency region. Yes. In addition, the plate | board thickness center part of a Fe-type metal plate shall point out the area | region where the ferrite production | generation element is not diffused. Here, when the Z value calculated from the X-ray random intensity ratio of the Fe-based metal plate enriched with ferrite-forming elements on both surfaces of the base metal plate satisfies 0.5 <Z ≦ 50, α It has been found that eddy current is further suppressed because stress is applied to the crystal lattice of the -Fe phase and the magnetic domain width is narrowed. This phenomenon occurs when the electrical resistivity Ra at the center of the plate thickness is 38 μΩ · cm or more and 200 μΩ · cm or less, and the electrical resistivity Ra at the center of the plate thickness is less than the electrical resistivity Rb of the outermost layer. Current loss is significantly reduced. The reason why the magnetic domain width narrows when stress is applied to the crystal lattice is considered to be due to the subdivision of the magnetic domain due to the inverse effect of magnetostriction, based on the relationship between the crystal orientation and magnetostriction depending on the Z value.

  Here, the Z value is the ratio of {001} <470>, {116} <6 12 1>, {223} <692> among the X-ray random intensity ratio of the α-Fe phase to the plate surface of the Fe-based metal plate. When the intensity ratios are A, B and C, respectively, the values satisfy the relationship Z = (A + 0.98B) / (4 × 0.98C).

  In order to satisfy the Z value of 0.5 <Z ≦ 50, an orientation close to {100} is formed on both surfaces of the base metal plate having a composition capable of causing α-γ transformation on the entire surface of the plate by strong processing or decarburization. To the oriented structure. Then, a ferrite-forming element is attached to the base metal plate, heated to the A3 point or higher of the base metal plate, and ferrite is partially or entirely in a region oriented in a direction near {100} in the base metal plate. The produced element is diffused and alloyed with the base material, and the α-Fe phase is stored in the alloyed region. Alternatively, the ferrite-forming element is diffused inside beyond the region where the orientation close to {100} is oriented, and the region that was the γ-Fe phase is transformed into the α-Fe phase. At that time, since the transformation of the preserved α-Fe phase is taken over, a structure oriented in an orientation close to {100} is formed even in the alloyed region. Further, even in the α-phased grains, the orientation in the direction closer to {100} is further increased.

  Here, the base metal plate with the ferrite-forming elements attached on both sides is further heated and held at a temperature of A3 or higher and 1300 ° C. or lower. Since the region of the α single phase component is an α-Fe phase that does not cause γ transformation, the crystal grains oriented in the orientation close to {100} are preserved as they are, and the orientation of the orientation close to {100} in the region is preserved. The crystal grains preferentially grow and the Z value increases. A region that is not an α single phase component undergoes γ transformation. When the holding time is lengthened, the {100} crystal grains grow preferentially by biting. As a result, the Z value further increases.

  Next, the base metal plate in which the ferrite-forming element is partially diffused is cooled to a temperature below the A3 point. At this time, the γ-Fe phase in the non-alloyed inner region is transformed into the α-Fe phase. This internal region is adjacent to a region that is already α grains oriented in a direction close to {100} in the temperature range of the A3 point or higher, and the adjacent α is transformed when transforming from the γ phase to the α phase. It takes over the crystal orientation of the grains and transforms. For this reason, directions close to {100} are also accumulated in that region.

  Although the basic configuration of the present invention has been described above, the reasons for limiting the individual conditions that define the production method of the present invention and the preferable conditions for carrying out the present invention will be described.

(Components of base metal plate)
For the base metal plate, an Fe-based metal having a component having a composition capable of causing the α-γ transformation is used. Further, in order to further increase the electric resistance, by mass%, Si: 0.001% to 10.0%, Mn: 0.001% to 12.0%, and Al: 0.001% to 4.0% are contained. In addition, it is preferable to use a material in which the balance is based on Fe and inevitable impurities and appropriately contains additional elements. Other impurities include trace amounts of Ni, Cr, Mo, W, V, Ti, Nb, B, Cu, Co, Zr, Y, Hf, La, Ce, N, O, P, S, etc. It is. Furthermore, you may contain Cr: 0.001% -9.0% and Ni: 0.001% -8.0% by mass% as another element. If the content exceeds this, the base metal becomes hard and it becomes difficult to produce an Fe-based metal plate as a product.

(Electric resistance of base metal plate (Fe-type metal plate thickness center))
The base metal plate has an electrical resistivity Ra of 38 μΩ · cm to 200 μΩ · cm. When the electrical resistivity is less than 38 μΩ · cm, eddy current loss cannot be sufficiently reduced when used in a high frequency region. Moreover, when an alloy element is added so that it exceeds 200 microhm * cm, it will become hard and manufacture of a base metal plate will become difficult. More preferably, it is 45 μΩ · cm or more and 170 μΩ · cm or less. Note that the electrical resistance of the base metal plate is almost the same regardless of the measurement position.

(Electric resistance of outermost layer)
The electrical resistivity Rb of the outermost layer of the Fe-based metal plate enriched with ferrite-forming elements on both sides needs to be higher than the electrical resistivity Ra of the base metal plate in order to suppress the skin effect. Here, it is preferable to make it higher than the electrical resistivity Ra of the base metal plate from the outermost layer to a certain region in the depth direction. For example, a region that is 1.2 times or more the electrical resistivity Ra at the center of the plate thickness is formed from the outermost layer to a depth of x μm, and in this region, ferrite forming elements are concentrated, so x is 0.05 μm. When the thickness is 500 μm or less, the skin effect can be more efficiently suppressed. If x is less than 0.05 μm, the skin effect cannot be sufficiently suppressed. In addition, it takes a long time to exceed 500 μm. More preferably, it is 1.5 times or more of the electrical resistivity Ra of the central portion of the plate thickness, which is a thickness of (thickness-2x) or less. The depth x μm is measured by measuring the concentrations of Al, Si, Mn, Cr and Ni at a plurality of positions in the cross section of the Fe-based metal plate using the EPMA method, and R obtained from the following formula (1) is the base metal. It calculates | requires from the position used as 1.2Ra with respect to electrical resistivity Ra of a board. The concentration of each element is mass%.
R = 9.9 + 12.4 × [Si%] + 10 × [Al%] + 6.6 × [Mn%] + 3 × [Cr%] + 1.5 × [Ni%] (1)
Here, [] represents the concentration of each element.

(Types of ferrite-forming elements)
When a ferrite-forming element is diffused into a base metal plate made of an Fe-based metal having an α-γ transformation component, the diffused and alloyed region becomes an α single-phase component, and {200} in the plate In order to increase the degree of surface integration, it can be stored as {100} oriented buds. Further, when the ferrite-forming element is one or more selected from the group consisting of Al, Cr, Ga, Mo, Sb, Si, Sn, Ta, Ti, V, W, and Zn, Integration can be performed more efficiently.

(Fe metal plate thickness)
The thickness of the Fe-based metal plate is preferably 10 μm or more and 5 mm or less. When the thickness is less than 10 μm, the number of stacked layers increases when the layers are used as a magnetic core, and the gap increases, making it difficult to obtain a high magnetic flux density. On the other hand, if the thickness exceeds 5 mm, the {100} texture does not grow sufficiently after cooling after the diffusion treatment, making it difficult to obtain a high magnetic flux density.

(Texture of Fe-based metal plate)
The X-ray random intensity ratio of the α-Fe phase to the plate surface of the Fe-based metal plate is the intensity ratio of {001} <470>, {116} <6 12 1>, {223} <692> as A and B, respectively. , C and Z = (A + 0.98B) / (4 × 0.98C), the Z value must satisfy the condition of 0.5 <Z ≦ 50. If the Z value is less than 0.5, a sufficiently high magnetic flux density cannot be obtained. On the other hand, when it exceeds 50, the magnetic flux density is saturated while the iron loss is increased. Preferably they are 2 or more and 48 or less.

  The Z value represents a three-dimensional texture calculated by the series expansion method based on the {200}, {110}, {310}, and {211} pole figures of the α-Fe phase measured by X-ray diffraction. What is necessary is just to obtain | require from a crystal orientation distribution function (Orientation Distribution Function, ODF). The random intensity ratio means that the X-ray intensity of a standard sample and a test material that do not accumulate in a specific orientation is measured under the same conditions, and the X-ray intensity of the obtained test material is the X-ray intensity of the standard sample. It is a numerical value divided by intensity. As the Fe-based metal plate grows with the diffusion of ferrite-forming elements, the surface layer structure grows inward, so X-ray diffraction may be measured on the surface of the Fe-based metal plate or at the thickness center. .

(Heat diffusion treatment)
First, the base metal plate with the ferrite-forming element attached is heated to point A3 of the base metal plate, and the ferrite-forming element is diffused in part or all of the base metal plate and alloyed with the base material. The α phase is stored in the alloyed region. Then, the base metal plate is further heated to a temperature of A3 or higher and 1300 ° C. or lower and held. In the already alloyed region, it becomes an α single phase structure that does not undergo γ transformation, and the region of the α single phase component is an α-Fe phase that does not undergo γ transformation. In the region, crystal grains having an orientation close to {100} preferentially grow and the Z value increases. A region that is not an α single phase component undergoes γ transformation. In addition, as Al diffuses, the transformation from the γ phase to the α phase occurs in the Fe-Al alloyed region. At that time, in the region adjacent to the region to be transformed, α grains are already oriented in an orientation close to {100}, and when transforming from the γ phase to the α phase, the crystal orientation of the adjacent α grains is taken over. Metamorphosis. As a result, the Z value increases as the holding time increases. While holding for a long time increases the Z value, the electrical resistivity of the surface layer decreases. Therefore, the holding time is preferably 0.5 sec or more and 36000 sec or less.

(Cooling after heat diffusion treatment)
After the diffusion treatment, when cooling is performed in a state where an unalloyed region remains, in the non-alloyed region, α grains already oriented in an orientation close to {100} are formed during the transformation from γ to α. In this way, a metal plate having a texture that satisfies the above-mentioned Z value condition is obtained by transforming the crystal orientation of the region and increasing the Z value. The cooling rate is preferably 0.1 ° C./sec or more and 500 ° C./sec or less. Cooling in this temperature range gives a higher Z value.

  The invention is further described in the examples. The conditions in the examples are one condition example adopted to confirm the feasibility and effects of the present invention, and the present invention is not limited to this one condition example. The present invention can adopt various conditions as long as the object of the present invention is achieved without departing from the gist of the present invention.

Example 1
Ingots were cast by melting steel of various components in a vacuum melting furnace. The ingot was hot-rolled to a thickness of 50 mm in the γ region, and subsequently processed warm or cold to obtain a base metal plate. Table 1 shows the chemical composition, A3 point, and electrical resistivity Ra of the base metal plate. Next, a ferrite-forming element was adhered to both surfaces of the base metal plate. In the comparative example, the case where the ferrite forming element was not adhered was examined. Each element was attached by EB vapor deposition, plating, and sputtering. Next, heat treatment was performed on the metal plate to which the ferrite-forming element was adhered. An infrared furnace was used as the heat treatment furnace, and heat treatment was performed in an atmosphere evacuated to a level of 10 ⁻³ Pa. The holding temperature was 900 ° C. to 1100 ° C., and the holding time was 100 sec to 1200 sec.

The obtained Fe-based metal plate was evaluated as follows. First, the texture was evaluated by the X-ray diffraction method. Subsequently, for the magnetic characteristics, a magnetic flux density B ₅₀ with respect to a magnetizing force of 5000 A / m was obtained using SST (Single Sheet Tester). At this time, the measurement frequency was 50 Hz. Next, the saturation magnetic flux density Bs was determined using a VSM (Vibrating Sample Magnetometer). At this time, the applied magnetizing force was set to 0.8 × 10 ⁶ A / m. The iron loss conforms to JIS C2256 and is based on a single plate magnetic tester (SS
T). The region where the ferrite-generating element is concentrated and has a high electric resistance is measured by using the EPMA (Electron Probe Micro-Analysis) method to measure the concentrations of Al, Si, Mn, Cr and Ni at a plurality of positions in the plate thickness direction. The position where R obtained from the above-described equation (1) is 1.2 Ra with respect to the electrical resistivity Ra of the base metal plate was obtained.

  The electrical resistivity was measured using the four probe method. The electrical resistivity of the base metal plate was measured before attaching the ferrite-forming element, and the electrical resistivity of the outermost layer was measured after attaching the ferrite-forming element and performing heat treatment.

  As is clear from Tables 1 and 2, it was confirmed that the Fe-based metal plate of the present invention had a high B50 / Bs value and at the same time a low iron loss. On the other hand, when the condition of the present invention is not satisfied or when no element is adhered, an Fe-based metal plate that achieves both a high B50 / Bs value and a low iron loss cannot be obtained. Moreover, when the electrical resistance of the base metal plate was low as in Comparative Examples 1 and 4, the iron loss could not be reduced sufficiently. Further, as in Comparative Example 2, a sufficiently high magnetic flux density could not be obtained when the composition of the base metal plate was an α single phase system having no A3 point. When the Z value was low as in Comparative Examples 3 and 5, a high B50 / Bs value could not be obtained, and the iron loss could not be reduced sufficiently. Further, in Comparative Example 6 in which the ferrite-forming element was not concentrated, the B50 / Bs value was low and the iron loss was large. When the component of the base metal plate was a high alloy as in Comparative Example 7, it was cracked during processing, and the metal plate could not be created. In Comparative Example 8 where the Z value exceeded 50, the B50 / Bs value was almost the same as that when the Z value was 50 or less, but the iron loss could not be reduced sufficiently.

(Example 2)
In this example, steel types C, E, F, J, K, S, V, and B ′ shown in Table 1 were used as the base material. These base materials are prepared by melting an ingot by vacuum melting and then processing it to a predetermined thickness by hot rolling, warm or cold rolling. In hot rolling, an ingot having a thickness of 245 mm heated to 1200 ° C. was thinned to a thickness of 50 mm. After cutting plate materials of various thicknesses from this hot-rolled plate by machining, warm or cold rolling was performed to produce a base metal plate having a thickness in the range of 8 μm to 5200 μm.

The resulting base metal plate is plated with Al, Cr, Ga, Ge, Mo, Ni, Sb, Si, Sn, Ti, V, W, or Zn as an element for forming ferrite by ion plating, hot dipping, electroplating. The method was applied by sputtering. The heat treatment was performed using an infrared furnace in an atmosphere evacuated to a level of 10 ⁻³ Pa. The holding temperature was 800 ° C. to 1350 ° C., and the holding time was 0.3 sec to 38000 sec. Evaluation was performed by the same method as in Example 1.

  As shown in Table 3, it was found that when the ferrite-forming element was concentrated, a high magnetic flux density (B50 / Bs value) was obtained and the iron loss was low. On the other hand, when Ni which is an austenite generating element was adhered as in Comparative Example 9, the Z value was low and a high B50 / Bs value was not obtained. It was also found that the magnetic properties were inferior even when the Z value was low and the texture development was insufficient.

(Example 3)
In this example, a mixture of two kinds of metals was used as a ferrite-forming element. As a base material, steel type G shown in Table 1 of Example 1 was used. The ferrite-forming element was deposited by applying a hot dipping method or a sputtering method. The heat treatment was performed using an infrared furnace in an atmosphere evacuated to a level of 10 ⁻³ Pa. The holding temperature was 1025 ° C. to 1050 ° C., and the holding time was 2 sec to 500 sec. The evaluation was performed in the same manner as in Example 1.

  As shown in Table 4, it was found that a high B50 / Bs value and a low iron loss can be obtained with a combination of ferrite-forming elements.

Claims (12)

Fe-based metal plate with ferrite-forming elements concentrated on both sides,
The chemical composition at the center of the thickness of the Fe-based metal plate is, by mass, Si: 0.001% to 10.0%, Mn: more than 2.0% and 12.0% or less, and Al: 0.00. Fe-based components having a composition that contains 001% to 4.0% and the balance can cause an α-γ transformation that is iron and inevitable impurities,
When the electrical resistivity at the center of the thickness of the Fe-based metal plate is Ra and the electrical resistivity of the outermost layer is Rb, the electrical resistivity Ra at the center of the thickness is 38 μΩ · cm to 200 μΩ · cm, and the plate The electrical resistivity Ra of the thickness center portion <the electrical resistivity Rb of the outermost layer,
The X-ray random intensity ratios of {001} <470>, {116} <6 12 1>, {223} <692> on the surface of the Fe-based metal plate are A, B, and C, respectively, and Z = (A + 0 .98B) / (4 × 0.98C), an Fe-based metal plate wherein the Z value satisfies 0.5 <Z ≦ 50.   2. The Fe-based metal plate according to claim 1, wherein a part or the whole of the region where the ferrite-forming element is concentrated is an α-Fe single phase.   3. The Fe-based metal plate according to claim 1, wherein an electrical resistivity Ra at the central portion of the plate thickness is 45 μΩ · cm to 170 μΩ · cm.   The ferrite-forming element is one or more elements selected from the group consisting of Al, Cr, Ga, Ge, Mo, Sb, Si, Sn, Ta, Ti, V, W, and Zn. Item 4. The Fe-based metal plate according to any one of Items 1 to 3.   A region that is 1.2 times or more the electrical resistivity Ra at the center of the plate thickness is formed from the outermost layer to a depth of x μm, x is 0.05 μm or more and 500 μm or less, and 1 / th of the plate thickness. The Fe-based metal plate according to any one of claims 1 to 4, wherein the Fe-based metal plate is less than 2.   The chemical composition at the center of the thickness of the Fe-based metal plate is selected from the group consisting of Cr: 0.001% to 9.0% and Ni: 0.001% to 8.0% in mass%. The Fe-based metal plate according to claim 1, wherein the Fe-based metal plate includes one or two kinds, and the balance is iron and inevitable impurities.   The thickness of the said Fe-type metal plate is 10 micrometers or more and 5 mm or less, The Fe-type metal plate of any one of Claims 1-6 characterized by the above-mentioned. A method of producing a Fe-based metal plate having a high {200} plane integration degree by attaching a ferrite-forming element on a base metal plate made of Fe-based metal, and heat-treating and diffusing the element.
In mass%, Si: 0.001% to 10.0%, Mn: more than 2.0% and 12.0% or less, and Al: 0.001% to 4.0%, with the balance being iron and inevitable When the electrical resistivity Ra is 38 μΩ · cm or more and 200 μΩ · cm or less when the electrical resistivity Ra is a composition that can cause an α-γ transformation that is an impurity and the central portion of the plate thickness is Ra, the both sides of the base metal plate A step of attaching a ferrite-forming element;
Heating the base metal plate to which the ferrite-forming element is adhered to A3 point of the base metal plate, and diffusing the ferrite-forming element into the base metal plate;
A step of further heating and holding the base metal plate in which the ferrite-forming element is diffused to a temperature of not less than A3 and not more than 1300 ° C .;
The base metal plate heated and held at a temperature not lower than A3 point and not higher than 1300 ° C. is cooled to a temperature lower than A3 point to transform the γ-Fe phase in the non-alloyed region into an α-Fe phase, The X-ray random intensity ratios of {001} <470>, {116} <6 12 1>, {223} <692> on the surface of the Fe-based metal plate are A, B, and C, respectively, and Z = (A + 0. 98B) / (4 × 0.98C), the Z value satisfies 0.5 <Z ≦ 50, and the electrical resistivity of the outermost layer is Rb, and the electrical resistance at the center of the plate thickness A step of obtaining an Fe-based metal plate satisfying a ratio Ra <the outermost layer electrical resistivity Rb ;
The manufacturing method of the Fe-type metal plate characterized by having. The ferrite-forming element is one or more elements selected from the group consisting of Al, Cr, Ga, Ge, Mo , Sb, Si, Sn, Ta, Ti, V, W, and Zn. The manufacturing method of the Fe-type metal plate of Claim 8.   In the Fe-based metal plate, a region that is 1.2 times or more the electrical resistivity Ra of the plate thickness center portion is formed from the outermost layer to a depth of x μm, and x is 0.05 μm or more and 500 μm or less, And the manufacturing method of the Fe-type metal plate of Claim 8 or 9 made into less than 1/2 of plate | board thickness.   The base metal plate contains one or two selected from the group consisting of Cr: 0.001% to 9.0% and Ni: 0.001% to 8.0% by mass%, and the balance The method for producing an Fe-based metal plate according to any one of claims 8 to 10, wherein is iron and inevitable impurities.   The thickness of the said base metal plate is 10 micrometers or more and less than 5 mm, The manufacturing method of the Fe type metal plate of any one of Claims 8-11 characterized by the above-mentioned.