JP5648335B2 - Fe-based metal plate with partially controlled crystal orientation - Google Patents

Description

  The present invention relates to an Fe-based metal plate that is suitable for uses such as electric cores of electric motors, generators, and transformers, and that can contribute to downsizing of these magnetic cores and energy loss reduction. The present invention also relates to an Fe-based metal plate having excellent workability such as deep drawing, press forming, and punching.

  Steel sheets that are textured by aligning the orientation of each crystal grain constituting the steel sheet in a specific direction have been put to practical use at the industrial production level because they exhibit excellent functions due to the aligned orientation. Yes. These textured steel sheets are manufactured through hot rolling, cold rolling, and a heat treatment process in the middle of the rolling process, and are almost the same texture in the rolling direction of the steel sheet and in the sheet width direction. Yes.

  For example, a <100> {110} textured directional silicon steel plate, a <hkl> {100} textured silicon steel plate, etc. are steel plates with controlled <100> orientation, which is the easy axis of magnetization. Used in the magnetic cores of motors and generators, it contributes to reducing energy loss and downsizing equipment. In addition, a steel plate having {111} faces integrated on the rolled surface has a feature of improving workability such as deep drawability.

The following technique is disclosed as a manufacturing method of a steel plate in which {100} planes are highly integrated in the rolling plane.
In Patent Document 1, C is contained in a silicon steel plate base material containing Si in an amount of 0.2 to 6.5 mass%, and C is contained at a temperature at which it becomes an α-Fe single phase after decarburization. Is decarburized until 0.01 mass% or less, the {100} plane is parallel to the plate surface, and the <100> axis or the <110> axis is accumulated in parallel to the rolling direction. A technique for forming a texture is described.
In Patent Document 2, a steel plate slab containing 4% or less of Si and 3% or less of Al is subjected to final rolling at a rolling rate of 92% or more after hot rolling, and then decarburization annealing and then finish annealing. Thus, a method for producing an electrical steel sheet having excellent magnetic properties in the 45 ° direction with respect to the rolling direction is described.

The inventors of the present invention have previously proposed Patent Document 3 and Patent Document 4 to manufacture a steel sheet in which specific surfaces are highly integrated using a method different from the above-described method.
Patent Document 3 relates to a steel plate having an Al content of 6.5 mass% to 10 mass% and a highly integrated {222} plane parallel to the steel plate surface, and an Al content of 3.5 mass% to 6.5 mass%. A technique has been described in which Al is deposited as a second layer on a base steel sheet of less than that, diffused by heat treatment, and the {222} plane is highly integrated by the interaction between the dislocation structure of the base metal and Al.

  Patent Document 4 discloses a steel sheet having an Al content of less than 6.5 mass%, and the {222} plane integration degree of one or both of the αFe phase and the γFe phase with respect to the steel plate surface is 60% or more and 99% or less or { A steel sheet having a high {222} plane integration degree, characterized in that the degree of 200} plane integration is one or both of 0.01% or more and 15% or less.

JP-A-1-252727 JP-A-5-279740 JP 2006-144116 A WO2008-0629001

  A conventional steel sheet in which the texture is controlled in a predetermined direction has substantially the same texture in the longitudinal direction and the sheet width direction of the steel sheet due to its manufacturing method. In the development of manufacturing technology for these textured steel sheets, efforts have been made to make the degree of crystal orientation integration as uniform as possible throughout the steel sheet. This is because, when cutting out from a steel sheet into a predetermined shape according to each application, it has been necessary to produce the same performance regardless of where the steel sheet is cut out.

However, conversely, if it is possible to integrate only a predetermined region in the plate surface into a predetermined texture, for example, an Fe-based metal plate in which a {100} plane and another {hkl} plane coexist is used. When placed in a magnetic field, the magnetic field preferentially passes through the {100} region, so that the flow of magnetic flux can be controlled. Further, the {111} plane can be expected to improve workability.
As described above, the present invention provides an Fe-based metal plate that has not been conventionally provided in which only a region patterned in a predetermined shape in the plate surface is controlled to a predetermined crystal orientation, and further, the Fe-based metal plate It is an object to propose a new use of the.

  The feature of the Fe-based metal plate of the present invention is that a metal plate has a region patterned in a predetermined shape, and at least a part of the patterned region is a metal other than Fe. Further, the {200} plane integration degree of the α-Fe phase in the patterned region is 30% or more and 99% or less and {222}. } The surface integration degree is 0.01% or more and 30% or less, or the {200} plane integration degree is 0.01% or more and 15% or less, and the {222} plane integration degree is 60% or more and 99% or less. That is.

  Further, at least a part of the patterned region is alloyed with a dissimilar metal, and {100} or {111} oriented crystal grains formed in the alloyed region are Of {200} or {222} in order to increase the degree of integration, and with the progress of alloying, the adjacent region is transformed in the form of taking over the crystal orientation of the crystal grains to be the final, In other words, a texture with a high {200} plane integration and a low {222} plane integration or a texture with a low {200} plane integration and a high {222} plane integration is obtained.

Further, the alloying with the dissimilar metal remains in a part of the region, and the components in the remaining region are maintained in a composition that can cause the α-γ transformation. In particular, the dissimilar metal is a ferrite forming element (α former element). And {200} or {222} plane integration degree is higher.
The gist of the present invention is as follows.

(1) An Fe-based metal plate containing at least one metal element other than Fe among ferrite-forming elements ,
A part of the plate surface of the metal plate has a region patterned in a predetermined shape, and the crystal plane of the α-Fe phase in the region portion has a {200} plane integration degree of 30% or more and 99% or less. And {222} plane integration degree is 0.01% or more and 30% or less, or {200} plane integration degree is 0.01% or more and 15% or less, and {222} plane integration degree is 60% or more and 99% or less. A Fe-based metal plate having a partially controlled crystal orientation.
Here, the {200} plane integration degree or {222} plane integration degree is determined by X-ray diffraction using MoKα rays, and there are 11 orientation planes ({110}, {200}) of α-Fe crystals parallel to the sample surface. , {211}, {310}, {222}, {321}, {411}, {420}, {332}, {521}, {442}), and measure each of the measured values. 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 having a random orientation is obtained as a percentage.

(2) pre-Symbol Fe-based metal plate partially crystalline orientation according is controlled in the above (1) region portion, characterized by containing a metal element other than Fe alloyed.
( 3 ) The metal element other than Fe is one or more elements selected from the group consisting of Al, Cr, Ga, Ge, Mo, Sb, Si, Sn, Ti, V, W, and Zn. An Fe-based metal plate having a partially controlled crystal orientation according to 1) or (2 ).
( 4 ) The Fe-based metal with partially controlled crystal orientation according to any one of (1) to ( 3 ), wherein the thickness of the Fe-based metal plate is more than 10 μm and not more than 6 mm Board.

Since the Fe-based metal plate of the present invention could not be envisaged from the prior art, there was no idea.
Since the Fe-based metal plate of the present invention can integrate only a predetermined region in the plate surface in a predetermined crystal orientation, for example, the {100} plane and other {hkl} planes in the plate surface Is placed in a magnetic field, the magnetic field preferentially passes through the region of the {100} plane, so that the flow of magnetic flux can be controlled. In addition, the Fe-based metal plate in which the {111} plane and the other {hkl} plane coexist in the plate plane can improve the workability of only the portion that is desired to be processed while maintaining the surrounding strength.
Thus, a part of the plate surface of the metal plate has a region patterned in a predetermined shape, and the crystal orientation of the α-Fe phase in the patterned region is specified. The metal plates integrated in the orientation can be applied to various new uses that could not be envisaged in the past, such as application to electromagnetic materials and machining materials, improving energy conservation and productivity. A wide range of effects can be expected.

It is a figure explaining the process for obtaining the Fe-type metal plate which raised {200} plane integration degree. It is a figure explaining the form of the Fe-type metal plate which raised {200} plane integration degree. It is a figure explaining another form of the Fe-type metal plate which raised {200} plane integration degree. It is a figure explaining an example of the method of patterning a part of plate surface of a Fe-type metal plate to a predetermined shape. It is the figure using the cross-sectional optical microscope observation photograph of the Fe-type metal plate in which the crystal orientation of a part of the plate surface was integrated in {222}. It is a figure which shows an example which patterned a part of plate surface of Fe type metal plate in the predetermined shape. It is a figure which shows the other example which patterned a part of board surface of Fe type metal plate in the predetermined shape.

The present inventors have studied a method for increasing the {200} plane integration degree of the α-Fe phase, and deposits a different metal other than Fe on a base metal plate made of an Fe-based metal, and heat-treats it by {200}. } We invented an Fe-based metal plate with an increased degree of surface integration. This method increases the {200} plane integration degree by using a method of diffusing elements other than Fe from the surface of the metal plate.
When diffusing elements other than Fe from the surface, the present inventors conducted an experiment of diffusing only from a predetermined region on the surface of the Fe-based metal plate to determine a region where an element other than Fe was diffused and a region where it was not. Examine in detail.
As a result, an Fe-based metal plate with an increased degree of {200} plane integration was obtained in a region where metal elements other than Fe were diffused. In the region where elements other than Fe were not diffused, the integration of the surface having a specific surface index did not occur. In addition, the boundary between a region where an element other than Fe is diffused and a region where the element is not diffused can be clearly discriminated by, for example, observing the cross-sectional structure of the plate with an optical microscope.

  Thus, the present inventors diffuse the elements other than Fe only from the region patterned into a predetermined shape in the surface of the Fe-based metal plate, thereby changing the crystal orientation of only the patterned region to {200}. The Fe-based metal plate highly integrated on the surface could be realized for the first time. Furthermore, by using a steel plate manufactured under specific conditions as an Fe-based metal plate, an Fe-based metal plate in which the crystal orientation of only a predetermined region is highly integrated on the {222} plane can be realized for the first time. It was.

  The Fe-based metal plate in which the crystal orientation of only the patterned region of the present invention is controlled has never existed conventionally. Hereinafter, an embodiment for implementing the Fe-based metal plate according to the present invention in which predetermined regions are integrated in a {200} plane crystal orientation will be described in detail.

  The present inventors made a dissimilar metal in the iron plate by diffusion alloying by heating it to a temperature of A3 point or higher after attaching a different metal other than Fe to a predetermined region of the surface of the iron plate having processing strain. It has been found that, when cooled, the {200} plane integration degree of the steel plate surface is increased only in a predetermined region to which a different metal is adhered. In the region where different metals were not deposited, the specific crystal orientation did not accumulate, and the orientation was random. In the region where the dissimilar metal is adhered, the dissimilar metal adhering to the iron plate surface diffuses in the plate thickness direction, and the diffused dissimilar metal stabilizes the buds of the {100} orientation crystal below the A3 transformation point. The {100} orientation buds grow in the plate thickness direction, so that the region where the different metal is adhered and the region where it is not have different crystal orientations.

The reason why {200} crystal orientations accumulate in a predetermined region patterned in the plane of the metal plate will be described with reference to the conceptual diagram of FIG.
FIG. 1 shows a case where an α former element is attached as a dissimilar metal on the surface of a base metal plate having a composition capable of causing an α-γ transformation.
(A) As a base metal plate having a composition capable of causing α-γ transformation , a pure iron plate cold-rolled at a very high reduction ratio such as 99.8% is prepared, and an α former element is formed on the surface thereof. For example, a second layer using Al is formed (state shown in FIG. 1a).

(B) The iron plate is heat-treated to diffuse the second layer of Al.
At that time, the iron plate recrystallizes in the temperature rising process below the A3 point. However, when the rolling reduction is very high, the structure after recrystallization becomes a structure oriented in {100} (hereinafter, this state is referred to as this state). In some cases, {100} oriented buds are formed.) Further, as the temperature rises, Al diffuses into the iron plate and is alloyed with iron, but a structure oriented in {100} is formed even in the alloyed region (state of FIG. 1b).

(C) The temperature is further raised and held at A3 or higher.
In the region where Fe and Al are alloyed, an α-Fe single phase structure that does not undergo γ transformation is formed, so that the {100} crystal grains are preserved as they are, and the grains grow and the {200} plane integration degree increases. Further, if there is a region that is not alloyed in the thickness direction, the crystal grains undergo γ transformation in the region (the state of FIG. 1c).
When the holding time is lengthened, {100} grains grow preferentially due to grain engagement. As a result, the {200} plane integration degree further increases. In addition, with the diffusion of Al, the region where Fe and Al are alloyed transforms from the γ phase to the α phase. At that time, α-Fe grains oriented in {100} are already formed in the region adjacent to the region to be transformed in the thickness direction, and α-adjacent in the thickness direction when transforming from the γ phase to the α phase. Transformation takes place in the form of inheriting the crystal orientation of Fe grains. As a result, the holding time becomes longer and the {200} plane integration degree increases.

(D) Finally, cool to point A3 or below.
(D1) When there is a non-alloyed region in the thickness direction as seen from the region where the foreign metal is adhered at the start of cooling, the non-alloyed region is the γ-phase in the temperature range above the A3 point, and the A3 When cooled below the point, the γ-α transformation occurs, and the crystal orientation is usually randomized. However, in the region that is alloyed with Al and becomes α-Fe grains in the temperature change region above the A3 point and adjacent to the plate thickness direction, it is already oriented {100} during the transformation from γ to α. The transformation is carried out in the form of inheriting the crystal orientation of the α-Fe grain region, and as a result, the {200} plane integration degree increases. (State of FIG. 1d)
By this phenomenon, a high {200} plane integration degree can be obtained even in a non-alloyed region.

(D2) When the whole is alloyed In the previous stage (c), when the alloy is held at the A3 point or more until alloyed throughout the thickness direction, the {200} plane is already high throughout the thickness. Since the accumulation degree structure is formed, the structure is cooled while maintaining the state at the start of cooling.

  In the region where different metals are not attached, the iron plate recrystallizes in the temperature rising process below the A3 point, but when the rolling reduction is very high, the structure after recrystallization is oriented in the {100} plane. Become an organization. However, in the temperature range above the A3 point, it transforms into a γ-Fe phase, and when cooled to the A3 point or less as it is, the γ-α transformation occurs and the crystal orientation is usually randomized.

In the form shown above, the {200} plane integration degree of the iron plate surface is increased only in a predetermined region where different metals are adhered, and the integration of a specific crystal orientation does not occur in the region where different metals are not adhered. It becomes a random direction.
It is possible to clearly distinguish the boundary between a region where different metals are attached and the {200} plane is highly integrated and a region where different metals are not attached and randomized.

  The present invention has been made based on the knowledge about the new process for increasing the degree of {200} plane integration as described above, and further, the conditions of the base material as a starting material and the types of dissimilar metals to be alloyed. As a result of studying the conditions for alloying and the like, the inventors have reached the present invention described below.

In the present invention, an Fe-based metal plate as a base material (hereinafter, this metal plate may be referred to as a base metal plate) having a composition capable of causing α-γ transformation, and having a predetermined shape on the surface thereof. A heterogeneous metal other than Fe serving as the second layer is attached to the patterned region, and finally, a Fe-based metal plate having a high {200} plane integration degree only in the patterned predetermined region (this metal plate is , Hereinafter referred to as a product metal plate). Therefore, the shape of the product metal plate changes depending on the difference in holding time at a temperature of A3 or higher.

Therefore, first, the difference in the form of the product metal plate will be described with reference to FIGS.
Form of Product Metal Plate In the present invention, a metal plate made of Fe-based metal having a composition capable of causing α-γ transformation is used as a base metal plate. Well-known steels such as pure iron and low carbon steel correspond to the Fe-based metal having a composition capable of causing the α-γ transformation. As described with reference to FIG. 1, a second layer made of a different metal other than Fe is formed into a predetermined shape on at least one surface of a base metal plate such as a pure iron plate in which a high degree of strain has been accumulated by means of plating or the like. It is made to adhere to the patterned area | region, and this is heat-processed. As the dissimilar metal, a metal element (for example, Al) is selected such that when alloyed with Fe, it becomes an α-Fe single phase even at a temperature of A3 or higher.

  During the heating process of the heat treatment, the dissimilar metal of the steel plate diffuses into the base metal plate, and at the same time, the base metal plate recrystallizes. As a result, as shown in FIG. 1b, a structure is formed in which the degree of {200} plane integration of the α-Fe phase in the alloyed region is increased. The temperature is further raised and heated to a point A3 or higher. In the already alloyed region, the structure is an α-Fe single phase that does not undergo γ transformation, so the {100} crystal grains are preserved as they are. In addition, if there is an unalloyed region, the crystal grains are transformed into γ-Fe in that region. If the temperature is further maintained, diffusion of dissimilar metals proceeds, and as described above, the {200} plane integration degree increases, and as a result, the {222} plane integration degree decreases (state in FIG. 2a).

  Thereafter, when cooling is performed in a state where an unalloyed region remains, in the unalloyed region, α-Fe that has already been oriented to {100} during the transformation from the γ-Fe phase to the α-Fe phase. The transformation is carried out in the form of taking over the crystal orientation of the grain region, the {200} plane integration degree is increased, the {200} plane integration degree of the α-Fe phase is 30% or more and 99% or less, and {222 } A metal plate having a texture with a surface integration degree of 0.01% or more and 30% or less is obtained (state shown in FIG. 2b).

  In addition, the value of the {200} plane integration degree and the state of the second layer in the region patterned in a predetermined shape on the surface of the base metal plate change depending on the holding time and holding temperature of the A3 point or more, and in FIG. The grain structure oriented in {100} does not reach the center of the plate, and the second layer remains on the surface. However, as shown in FIG. The entire second layer on the surface can also be alloyed.

  In addition, when the sheet thickness is held at A3 or higher until alloyed, the α-Fe single phase structure reaches the center of the sheet thickness, and the crystal grain structure oriented in {100} reaches the sheet thickness center. Until it is held (state of FIG. 2c), and then cooled to obtain a texture in which the crystal grain structure oriented in {100} reaches the center of the plate thickness (state of FIG. 2d).

  Thereby, the dissimilar metal is alloyed on the entire plate, the {200} plane integration degree of the α-Fe phase is 30% or more and 99% or less, and the {222} plane integration degree is 0.01% or more and 30% or less. A metal plate having the following texture is obtained.

  As described above, the Fe-based metal plate according to the present invention can be formed according to the degree of diffusion of the dissimilar metal attached to the region patterned in a predetermined shape and the degree of formation of the crystal grain structure oriented in {100}, FIG. d and the form shown in FIG. 3, in any form, the dissimilar metal diffused and alloyed in the Fe-based metal plate is contained, and the α-Fe phase { 200} plane integration degree is 30% or more and 99% or less, and {222} plane integration degree is 0.01% or more and 30% or less.

  As described above, when the Fe-based metal plate in the region in which the {200} crystal orientation of the present invention is patterned into a predetermined shape is applied to an electromagnetic material, it is possible to pass magnetic flux preferentially only through a predetermined portion in the plate surface. become. Furthermore, magnetic flux can be preferentially passed only through a portion up to a predetermined thickness of the plate thickness also in the plate thickness direction.

As for the mode for carrying out the steel sheet of the present invention in which a predetermined region is integrated in the {222} plane crystal orientation, it is not necessary to replace {200} with {222} in the description of FIGS. It is the same. In order to obtain the Fe-based metal plate of the present invention in which the {222} plane is highly integrated, it is preferable to use a base metal plate that is cold-rolled at a reduction rate of 30% to 95%.
If the rolling reduction is less than 30%, the {222} plane integration degree of the steel sheet obtained after the heat treatment step is low, and the range of the present invention may not be reached. Moreover, even if it exceeds 95%, there is no further increase in the degree of {222} plane integration.
Thereby, the dissimilar metal is alloyed on the entire plate, the {222} plane integration degree of the α-Fe phase is 60% or more and 99% or less, and the {200} plane integration degree is 0.01% or more and 15% or less. A metal plate having the following texture is obtained.

Although the basic configuration of the present invention has been described above, the reasons for limiting the individual conditions of the present invention and the preferable conditions for carrying out the present invention will be further described.
As described above, in the product metal plate of the present invention, a different metal is alloyed with the base metal plate. Therefore, the component composition in the product metal plate differs depending on the type of base metal plate, the type of dissimilar metal alloyed with the base metal, and the ratio of the alloyed region. explain.

Type of base metal plate An Fe-based metal having a composition having an A3 point and capable of causing an α-γ transformation is used for the base metal plate. If the Fe-based metal used for the base metal plate has a composition capable of causing the α-γ transformation , the region of the α-Fe single-phase component can be formed by diffusion-alloying the dissimilar metal into the plate. it can. In principle, the present invention can be applied to an Fe-based metal having a composition capable of causing an α-γ transformation, and it is impossible to verify all cases and present whether or not the application is possible. A general application range will be described.

Typical examples of the composition that can cause the α-γ transformation include steels such as pure iron and ordinary steel. For example, pure iron or steel consisting of C: 1 ppm to 0.2%, the balance Fe and unavoidable impurities is used as a base, and additional elements are appropriately contained. In addition, silicon steel having a composition capable of causing an α-γ transformation containing C: 0.1% or less and Si: 0.1-1.5 % as basic components may be used. Other impurities include trace amounts of Mn, Ni, Cr, Al, Mo, W, V, Ti, Nb, B, Cu, Co, Zr, Y, Hf, La, Ce, N, O, P, S and the like are included.

When an α former element is attached as a foreign metal to a region patterned in a predetermined shape within the surface of the base metal plate made of Fe-based metal having a composition capable of causing α-γ transformation of the different metal. The part that has been diffused and alloyed becomes a component of the α-Fe single-phase system, and when that part is increased in the {200} plane integration degree in the plate, it becomes {100} -oriented buds, or {222} When increasing the degree of surface integration, it can be stored as {111} oriented buds. In particular, when at least one α former element of Al, Cr, Ga, Ge, Mo, Sb, Si, Sn, Ta, Ti, V, W, and Zn is at least one type, higher integration proceeds efficiently. It becomes like this .

Surface integration degree of α-Fe phase When the Fe-based metal plate of the present invention is applied to an electromagnetic material, the {200} surface integration degree of the α-Fe phase with respect to the plate surface of the product metal plate is 30% or more and 99% or less. It is necessary to. When the degree of integration is less than 30%, a sufficiently high magnetic flux density cannot be obtained. Even if it exceeds 99%, the magnetic flux density is saturated and the manufacture is not easy. Desirably, it is 50% or more and 95% or less.
Further, the {222} plane integration degree needs to be 0.01% or more and 30% or less. If it is less than 0.01%, the magnetic flux density is saturated and the production is not easy. If it exceeds 30%, a sufficiently high magnetic flux density cannot be obtained. Desirably, it is 0.01% or more and 15% or less.

  When the Fe-based metal plate of the present invention is applied to a machining material, the {222} plane integration degree of the α-Fe phase with respect to the plate surface of the product metal plate needs to be 60% or more and 99% or less. If the degree of integration is less than 60%, sufficiently high machinability cannot be obtained. Even if it exceeds 99%, the machinability is saturated and the production is not easy. Desirably, it is 70% or more and 95% or less.

Further, the {200} plane integration degree needs to be 0.01% or more and 15% or less. If it is less than 0.01%, the machinability is saturated and the production is not easy. If it exceeds 15%, sufficiently high machinability cannot be obtained. Desirably, it is 0.01% or more and 10% or less. Measurement of the {200} plane integration degree or {222} plane integration degree can be performed by X-ray diffraction using MoKα rays.
More specifically, for each sample, there are 11 orientation planes ({110}, {200}, {211}, {310}, {222}, {321}, which are 11 α-Fe crystals parallel to the sample surface. {411}, {420}, {332}, {521}, {442}) are measured, and each of the measured values is divided by the theoretical integrated intensity of the sample in a random orientation, and then the total value is obtained. , {200} or {222} strength ratio as a percentage.

In that case, for example, {200} intensity ratio is expressed by the following formula (I).
{200} plane integration degree = [{i (200) / I (200)} / Σ {i (hkl) / I (hkl)}] × 100 (I)
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 α-Fe crystal Here, the integrated intensity of a sample having a random orientation may be obtained by preparing a sample and actually measuring it.
The {222} plane integration degree can be obtained in the same manner.

Thickness of Product Metal Plate The thickness of the product metal plate is preferably more than 10 μm and 6 mm or less. When applied to an electromagnetic material, if the thickness exceeds 10 μm, a sufficient space factor is obtained when the laminate is used as a magnetic core, and a high magnetic flux density can be obtained. Moreover, if thickness is 6 mm or less, {200} plane integration degree will become high and a high magnetic flux density will be obtained. When applied to a machined material, a sufficient strength can be obtained if the thickness exceeds 10 μm. Moreover, if thickness is 6 mm or less, {222} plane integration degree will become high and high machinability will be acquired.

Second layer state Even if the second layer deposited as a coating on a predetermined region patterned on the base metal plate is partially covered with the product metal plate after heat treatment Alternatively, the dissimilar metal in the second layer may be all diffused into the plate, and the second layer may be extinguished.
For example, when applied to an electromagnetic material, when it is left for the purpose of increasing the electrical resistance of the surface and improving the iron loss, it is desirable that the thickness be in the range of 0.01 to 500 μm. When the thickness is 0.01 μm or more, defects such as tearing hardly occur and stable iron loss characteristics can be obtained. When the thickness is 500 μm or less, defects such as peeling hardly occur and stable iron loss characteristics can be obtained. Moreover, when applying to a machining member, when it remains for the purpose of improving the crack from the surface, it is desirable to make the thickness into the range of 0.01-500 micrometers. When the thickness is 0.01 μm or more, defects such as tearing are less likely to occur, and stable workability is obtained. When the thickness is 500 μm or less, defects such as peeling hardly occur and stable workability is obtained.
Even in the case of remaining, the second layer can be deleted as necessary.

Next, the manufacturing method of the product metal plate of this invention is demonstrated.
Since the type of Fe metal used as the base metal plate has already been described, the manufacturing requirements will be described here. First, the manufacturing requirements of a metal plate with a highly integrated {200} plane will be described.

  In the present invention, a base metal plate in which a dissimilar metal adheres to a patterned region having a predetermined shape is heat-treated, and the dissimilar metal is diffused inside to be alloyed with a base material component. In the temperature raising process of the heating, as already described as the stage of FIG. 1b, {100} oriented crystal grains that form buds for increasing the {200} plane integration degree in the plate are formed, and thereafter The transformation is allowed to proceed in the plate in a manner that inherits the crystal orientation of the α-Fe crystal grains to be sprout.

In one embodiment of the present invention, a base metal plate is used in which a highly strained region exists in at least a diffusion region of a different metal.
This is because when the base metal plate cold-rolled at a high rolling rate and highly strained is used, the {200} plane integration degree is remarkably increased in the temperature rising process. Based on what you found.

In order to obtain a high degree of {200} plane integration, a strain such that the dislocation density is 1 × 10 ¹⁵ m / m ³ or more and 1 × 10 ¹⁷ m / m ³ or less is accumulated in the base metal plate. It is desirable.
As a method of giving such distortion, there is a method of performing cold rolling at the time of manufacturing a base metal sheet at a high reduction rate. Although a higher reduction ratio is desirable, it is particularly preferable that the reduction ratio is more than 97% and not more than 99.99%.

  The strain accumulation range does not have to be the entire base metal plate, but may be in a region where dissimilar metals are diffused and alloyed. As a method therefor, there are a method of performing a shot blasting process on a base metal plate and a method of performing a process using both cold rolling and shot blasting. When cold rolling and shot blasting are used in combination, the rolling reduction of cold rolling is 50% or more and less than 99.99%, and a high degree of {200} plane integration can be obtained.

In addition, a means for imparting a shear strain of 0.2 or more by cold rolling may be used. Further, a method combining the application of shear strain and shot blasting may be used. In that case, the shear strain may be 0.1 or more.
Shear strain can be applied by rotating the upper and lower rolling rolls at different speeds during rolling. At that time, the shear strain increases as the difference in rotational speed between the upper and lower rolling rolls increases. The value of the shear strain is obtained by calculation from the difference between the roll diameter and the roll speed.

  In the above, a structure that becomes {100} -oriented buds when the base metal plate is heated is formed. However, as another embodiment of the present invention, an Fe texture in which a texture that is pre-oriented in {100} is formed in the surface layer portion. A system metal plate can also be used as a base metal plate. Such a metal plate can be obtained by recrystallizing the Fe-based metal plate having accumulated a high degree of strain as described above.

  The thickness of the base metal plate is preferably 10 μm or more and less than 5 mm so that the thickness of the product metal plate is more than 10 μm and 6 mm or less.

Next, the manufacturing requirements of a metal plate with a highly integrated {222} plane will be described.
In the present invention, a base metal plate in which a dissimilar metal adheres to a patterned region having a predetermined shape is heat-treated, and the dissimilar metal is diffused inside to be alloyed with a base material component. In the heating temperature raising process, as already described, {111} oriented crystal grains that form buds for increasing the degree of {222} plane integration in the plate are formed, and then α- The transformation is allowed to proceed in the plate in a manner that inherits the crystal orientation of the Fe crystal grains.

  In the present invention, it is preferable to use a base metal sheet that is cold-rolled at a rolling reduction of 30% to 95%. When applied to machining materials, it is preferable that the {222} highly integrated region exists over the entire thickness of the Fe-based metal plate. Even in such a case, the range in which the strain is accumulated by cold rolling does not have to be the entire base metal plate, but may be in a region where different metals are diffused and alloyed. As a method therefor, there are a method of performing a shot blasting process on a base metal plate and a method of performing a process using both cold rolling and shot blasting. When cold rolling and shot blasting are used in combination, the rolling reduction of cold rolling is 10% or more and less than 95%, and a high {222} plane integration degree is obtained.

In the above, a structure that becomes {111} -oriented buds when the base metal plate is heated is formed. However, as another embodiment of the present invention, a surface structure is previously formed with a texture that is oriented {111}. A system metal plate can also be used as a base metal plate.
Such a metal plate can be obtained by recrystallizing an Fe-based metal plate in which strain is accumulated by the strain introducing means described above.

  The thickness of the base metal plate is preferably 10 μm or more and less than 5 mm so that the thickness of the product metal plate is more than 10 μm and 6 mm or less.

The second layer is formed in the region patterned into a predetermined shape of the different metal base metal plate shape, but since the types of different metals that are metal elements other than Fe constituting the second layer have already been described Here, manufacturing requirements are described.

  A dissimilar metal is attached to the base metal plate in a layered manner as a second layer. Various methods such as plating methods such as hot dipping and electrolytic plating, rolling clad methods, dry processes such as PVD and CVD, and powder coating can be adopted as the method of adhesion, but for industrial implementation. A plating method or a rolling clad method is suitable as a method for efficiently attaching different kinds of metals.

  The thickness of the second layer before heating is preferably 0.05 μm or more and 1000 μm or less. If the thickness is less than 0.05 μm, a sufficient {200} plane integration degree cannot be obtained when the {200} plane is highly integrated, or a sufficient {222} plane is highly integrated { 222} plane integration cannot be obtained. Further, if it exceeds 1000 μm, even when the second layer is left, the thickness thereof becomes thicker than necessary.

  The plate thickness portion for diffusing the dissimilar metal may be the entire plate thickness of the metal plate or a part of the plate thickness. In any case, as described with reference to FIG. 2, a high {200} plane integration degree or a high {222} plane integration degree can be obtained.

  In order to pattern different kinds of metals into a predetermined shape, conventionally known methods can be used. For example, a predetermined region may be masked to prevent foreign metals from attaching, or the attached foreign metals may be removed by etching.

Heat Diffusion Treatment • When the {200} surface is highly integrated The base metal plate is heat diffusion treated and the {200} surface of the α-Fe phase in the region where the dissimilar metals are alloyed before reaching the A3 point. It is preferable that the integration degree is 25% or more and 50% or less, and the {222} plane integration degree is 1% or more and 40% or less. If the {200} plane integration degree is lower than the lower limit value or the {222} plane integration degree exceeds the upper limit value, a steel plate having a sufficient magnetic flux density cannot be manufactured. Further, if the {200} plane integration degree exceeds the upper limit value or the {222} plane integration degree falls below the lower limit value, the magnetic flux density of the manufactured steel sheet tends to be saturated, and it takes time to manufacture, which is not preferable. .

  Subsequently, the {200} plane integration degree of the α-Fe phase in the alloyed region after being heated and held above the A3 point is further improved, and the integration degree is 30% or more and 99% or less after cooling, As a result, the {222} plane integration degree is set to 0.01% or more and 30% or less. If the {200} plane integration degree is lower than the lower limit value or the {222} plane integration degree exceeds the upper limit value, a steel plate having a sufficient magnetic flux density cannot be manufactured. Moreover, if the {200} plane integration degree exceeds the upper limit value or the {222} plane integration degree falls below the lower limit value, the magnetic flux density of the manufactured steel sheet tends to be saturated, which is not preferable because it takes time to manufacture.

  When there is a non-alloyed region at the start of cooling, when the γ-Fe phase in that region is transformed into an α-Fe phase during the cooling process, the {200} plane integration degree of the α-Fe phase in that region is also 30% or more and 99% or less.

In the heat diffusion treatment, it is preferable that the rate of temperature increase to the A3 point is 0.1 ° C./s or more and 500 ° C./s or less. {200} plane oriented buds are efficiently formed at a temperature rising rate within this range.
The holding temperature after the temperature rise is preferably not less than A3 and not more than 1300 ° C. The effect is saturated even when heated at a temperature exceeding 1300 ° C. The heating and holding time may start cooling immediately after reaching the holding temperature, or may be held for a time of 360,000 s (100 h) or less to start cooling. When this condition is satisfied, the accumulation of {200} plane-oriented buds further proceeds, and the {200} plane accumulation degree of the α-Fe phase can be set to 30% or more after cooling more reliably.
In cooling after holding, the cooling rate is preferably 0.1 ° C./s or more and 500 ° C./s or less. When cooled in this temperature range, the growth of {200} plane oriented buds further proceeds.

・ When highly integrating the {222} plane: The base metal plate is subjected to heat diffusion treatment, and the {222} plane integration degree of the α-Fe phase in the region where the dissimilar metal is alloyed before reaching the point A3. It is preferable that the degree of integration is 55% or more and 70% or less, and the {200} plane integration degree is 1% or more and 30% or less. If the {222} plane integration degree is lower than the lower limit value or the {200} plane integration degree exceeds the upper limit value, a steel sheet having sufficient machinability cannot be manufactured. Further, when the {222} plane integration degree exceeds the upper limit value or the {200} plane integration degree falls below the lower limit value, the machinability of the manufactured steel sheet tends to be saturated, and it is not preferable because it takes time to manufacture. .

  Subsequently, the {222} plane integration degree of the α-Fe phase in the alloyed region after being heated and held above the A3 point is further improved, and the integration degree after cooling is 60% or more and 99% or less, As a result, the {200} plane integration degree is set to 0.01% or more and 15% or less. If the {222} plane integration degree is lower than the lower limit value or the {200} plane integration degree exceeds the upper limit value, a steel sheet having sufficient machinability cannot be manufactured. Further, when the {222} plane integration degree exceeds the upper limit value or the {200} plane integration degree falls below the lower limit value, the machinability of the manufactured steel sheet tends to be saturated, and it is not preferable because it takes time to manufacture. .

  When there is a non-alloyed region at the start of cooling, when the γ-Fe phase in that region is transformed into an α-Fe phase in the cooling process, the degree of {222} plane integration of the α-Fe phase in that region is also 60% or more and 99% or less.

In the heat diffusion treatment, it is preferable that the rate of temperature increase to the A3 point is 0.1 ° C./s or more and 500 ° C./s or less. {222} plane oriented buds are efficiently formed at a temperature rising rate within this range.
The holding temperature after the temperature rise is preferably not less than A3 and not more than 1300 ° C. The effect is saturated even when heated at a temperature exceeding 1300 ° C. The heating and holding time may start cooling immediately after reaching the holding temperature, or may be held for a time of 360,000 s (100 h) or less to start cooling. When this condition is satisfied, the accumulation of {222} plane oriented buds further proceeds, and the {222} plane accumulation degree of the α-Fe phase can be set to 60% or more after cooling more reliably.
In cooling after holding, the cooling rate is preferably 0.1 ° C./s or more and 500 ° C./s or less. When cooled in this temperature range, the growth of {222} plane oriented buds proceeds further.

  According to the method of the present invention, after dissimilar metal is adhered to the surface of the base metal plate patterned in a predetermined shape, the dissimilar metal is diffused in the metal plate subjected to diffusion heat treatment according to the method of the present invention. It can be clearly observed by observing the cross-sectional structure, etc. that the crystal structure of the part which has been made is different from that of the part which is not. Furthermore, by using a known method such as X-ray diffraction or EBSD method, the crystal orientation of the region where the dissimilar metal is diffused can be easily measured.

Hereinafter, the present invention will be described in more detail by way of examples.
Example 1
For the base metal plate, IF steel mainly composed of 0.002% C, 0.011% Si, 0.13% Mn, 0.01% P, 0.007% S and the balance Fe was used. An ingot having the composition was melted, hot-rolled, and cold-rolled to obtain a cold-rolled sheet having a thickness of 500 μm. Thereafter, strain relief annealing was performed at 800 ° C. for 30 minutes. This annealed plate was 70% cold-rolled to a thickness of 150 μm, and used as a base metal plate for conducting a confirmation experiment as to whether the highly integrated region of the {222} plane could be patterned.

This base metal plate was cut into 20 mm squares and masked using a Kapton tape as shown in FIGS. At that time, the position was shifted by about 200 μm on the front and back Kapton tapes. In this state, Al was deposited on both sides by 5.3 μm on one side, and heat treatment was performed to diffuse Al into the metal plate. An infrared gold image furnace was used for the heat treatment, the temperature was raised to 1000 ° C. at 10 ° C./min under program control, the temperature was maintained for 2 hours, and then the furnace was cooled. The heat treatment atmosphere is a vacuum of 10 ⁻³ Pa level.

  FIG. 5 shows a photomicrograph of an optical microscope observed in the visual field of FIG. In the region to which Al was attached, the crystal grains grew like a columnar crystal from the surface as shown in FIG. On the other hand, the crystal grains were isotropic in the region where Al was not attached. Thus, the area where Al was adhered and the area where Al was not adhered could be clearly distinguished.

  The surface integration degree of the {222} and {200} of the α-Fe phase in the Al-attached region and the non-attached region after the heat treatment was determined at the 1 / 2t position in the center of the plate thickness by the above-mentioned X-ray diffraction. It was measured. As a result, in the region where Al is adhered, {222} plane integration degree = 76% and {200} plane integration degree = 0.9%. In the region where Al is not adhered, the {222} plane integration degree = 24% and the {200} plane integration degree = 22%.

  From the above, according to the present invention, it becomes possible to integrate a predetermined region of the Fe-based metal plate into the {222} texture.

  The steel plate of the present invention shown in FIG. 5 is excellent in workability such as deep drawability in the {222} highly integrated region. In the adjacent non-highly integrated region, the deep drawability is inferior to that of the {222} highly integrated region, but the region is excellent in strength because the crystal grain size is fine. When processing such a steel sheet of the present invention, for example, the {222} highly integrated region is patterned in a circular shape, and the circular portion is used as a deep drawn portion, while maintaining the strength of the surroundings. Deep drawing can be performed.

Actually, similarly to the steel plate of the present invention shown in FIG. 5, 5.3 μm of Al was deposited on the center of a steel plate having a diameter of 100 mm in a region having a diameter of 60 mm. However, the positions of the front surface and the back surface were matched and adhered to both surfaces. An infrared gold image furnace was used for the heat treatment, the temperature was raised to 1000 ° C. at 10 ° C./min under program control, the temperature was maintained for 2 hours, and then the furnace was cooled. The heat treatment atmosphere is a vacuum of 10 ⁻³ Pa level. The surface integration degree of the {222} and {200} of the α-Fe phase in the Al-attached region and the non-attached region after the heat treatment was determined at the 1 / 2t position in the center of the plate thickness by the above-mentioned X-ray diffraction. It was measured. As a result, in the area where Al is adhered, {222} plane integration degree = 78% and {200} plane integration degree = 0.9%. In the region where Al is not attached, the {222} plane integration degree = 23% and the {200} plane integration degree = 22%.

  Using this circular plate, deep drawing was performed using a die having an inner diameter of 30 mm. The pushing of the punch was finished when the {222} highly integrated region having a diameter of 60 mm reached the inlet edge of the die (drawing ratio 2.0). As a comparative material, a steel plate not attached with Al was used. In this comparative material, there was no integration of a specific crystal orientation.

  As a result of the deep drawing test, the steel plate of the present invention was able to be formed into a flanged cup. The strength of the flange portion was 1.3 times the strength of the cup portion. In the comparative material, cracks occurred from the bottom of the cup during deep drawing, and deep drawing was not possible up to a drawing ratio of 2.0.

(Example 2)
As the base metal plate, a pure iron plate was used which was ingot made by vacuum melting, then hot-rolled and then cold-rolled to a predetermined thickness. The composition of the ingot is 0.0001% C, 0.0001% Si, 0.0002% Al, and pure iron containing inevitable impurities. The ingot was hot-rolled to a thickness of 75 mm, and strain relief annealing was performed at this thickness at 800 ° C. for 30 minutes. This annealed plate was 99.8% cold-rolled to a thickness of 150 μm, and used as a base metal plate for carrying out a confirmation experiment as to whether or not the highly integrated region of the {200} plane could be patterned.

Two pieces of this base metal plate were cut into 50 mm squares, and masking treatment was performed using Kapton tape in the same manner as in Example 1. At that time, the Kapton tape was aligned so that exactly half of the 50 mm square plate was masked, and the Kapton tape on the front surface and the back surface were aligned at the same position. In this state, Al was vapor-deposited on both sides by 3 μm on one side, and heat treatment was performed. An infrared gold image furnace was used for the heat treatment, the temperature was raised to 1000 ° C. at 10 ° C./min under program control, the temperature was maintained for 2 hours, and then the furnace was cooled. The heat treatment atmosphere is a vacuum of 10 ⁻³ Pa level. One was used for crystal orientation and structure observation, and the other was used for magnetic measurement.

  As in Example 1, as a result of observing the cross-sectional structure of the metal plate with an optical microscope, in the region to which Al was attached, crystal grains grew columnarly from the surface as shown in FIG. It was. On the other hand, the crystal grains were isotropic in the region where Al was not attached. Thus, the area where Al was adhered and the area where Al was not adhered could be clearly distinguished.

The {200} and {222} surface integration levels of the α-Fe phase in the region where the Al was adhered and the region where the Al was not adhered after the heat treatment were measured by the aforementioned X-ray diffraction. As a result, in the area where Al is adhered, {200} plane integration degree = 71% and {222} plane integration degree = 0.3%. In the region where Al is not adhered, the {200} plane integration degree = 14% and the {222} plane integration degree = 14%.
From the above, according to the present invention, it becomes possible to integrate a predetermined region of the Fe-based metal plate into a {200} texture.

Thus, the magnetic properties of the Fe-based metal plate in which half of the plate was patterned into {200} texture according to the present invention were examined.
An alternating magnetic field having a frequency of 50 Hz and a maximum applied magnetic field of 5000 A / m was applied in the direction shown in FIG. 6, and the magnetic flux density was measured in the textured region and the region that was not. The magnetic field was applied using a SST (Single Sheet Tester) yoke. A 1 mm hole for passing the coated copper wire was made in the portion shown in FIG. 6, and the detection coil was wound 10 turns. The voltage V induced in the detection coil is V = −N (dφ / dt) = − NS (dB / dt) where N is the number of turns of the detection coil and S is the cross-sectional area thereof. When N and S are the same, the voltage V is proportional to the magnetic flux density B, so that the magnetic flux density can be compared from the voltage comparison. The voltage at {200} texture was relatively compared with the voltage at random orientation as 1.

  The results are shown in Table 1. As can be seen from this result, even in the same plate, a higher magnetic flux density was obtained in the {200} integrated region than in the random region. This is because the {200} integrated region contains more [100] orientation, which is the easy axis of magnetization, and the permeability of this region is high. Thus, by using the Fe-based metal plate of the present invention, it becomes possible to control the flow of magnetic flux in the plate.

Example 3
Similarly, Al was vapor deposited on both sides of 3.5 μm on one side of the same pattern as shown in FIG. 7 on two 50 mm square base metal plates as in Example 2. An infrared gold image furnace was used for the heat treatment, the temperature was raised to 1000 ° C. at 10 ° C./min under program control, the temperature was maintained for 2 hours, and then the furnace was cooled. The heat treatment atmosphere is a vacuum of 10 ⁻³ Pa level. One was used for crystal orientation and structure observation, and the other was used for magnetic measurement.

  As in Example 1, as a result of observing the cross-sectional structure of the metal plate with an optical microscope, in the region to which Al was attached, crystal grains grew columnarly from the surface as shown in FIG. It was. On the other hand, the crystal grains were isotropic in the region where Al was not attached. Thus, the area where Al was adhered and the area where Al was not adhered could be clearly distinguished.

The {200} and {222} surface integration levels of the α-Fe phase in the region where the Al was adhered and the region where the Al was not adhered after the heat treatment were measured by the aforementioned X-ray diffraction. As a result, in the region where Al is adhered, the {200} plane integration degree = 70% and the {222} plane integration degree = 0.4%. In the region where Al is not adhered, the {200} plane integration degree = 13% and the {222} plane integration degree = 13%.
From the above, according to the present invention, it becomes possible to integrate a predetermined region of the Fe-based metal plate into a {200} texture.

  Thus, the magnetic properties of the Fe-based metal plate in which predetermined portions of the plate were patterned into {200} textures according to the present invention were examined. An alternating magnetic field having a frequency of 50 Hz and a maximum applied magnetic field of 5000 A / m was applied in the direction shown in FIG. 7, and the magnetic flux densities of the textured regions (A, B) and the regions that were not (C, D) were compared. The magnetic field was applied using a SST (Single Sheet Tester) yoke. The comparison of the magnetic flux density was obtained in the same manner as in Example 2 by opening a 1 mm hole for passing the coated copper wire through the portion shown in FIG. The areas of the four detection coils are the same. The detection coil C was taken as a reference voltage, and the voltages induced in the other detection coils were relatively compared.

The results are shown in Table 2. As can be seen from this result, even in the same plate, a higher magnetic flux density was obtained in the {200} integrated region than in the random region. Furthermore, it can be seen from comparison between the part A and the part B that the magnetic flux can be concentrated by the pattern shape.
Thus, by using the Fe-based metal plate of the present invention, it becomes possible to control the flow of magnetic flux in the plate.

Example 4
Investigate the effect when various film elements, Si, Sn, Ti, Ga, Ge, Mo, V, Cr, As, which are ferrite forming elements, are adhered to Fe-based base metal plates as dissimilar metals other than Fe It was.
Six types of component systems A to F shown in Table 3 were used for the Fe-based base metal plate. Each was melted in a 230 mm thick ingot by vacuum melting and then hot rolled at 1000 ° C. to a thickness of 50 mm. After cutting plate materials of various thicknesses from these hot-rolled plates by machining, shot blasting and cold rolling at various rolling reductions were performed alone or in combination as necessary. The thickness of the obtained base metal plate was in the range of 100 μm to 700 μm.

  Two of these base metal plates were cut out into 50 mm squares and masked using a Kapton tape in the same manner as in Example 2. At that time, the Kapton tape was aligned so that exactly half of the 50 mm square plate was masked, and the Kapton tape on the front surface and the back surface were aligned at the same position. In this state, various coating elements that are different metals were attached to each base metal plate with the following thickness in total on both surfaces by using the IP method, the hot dipping method, and the sputtering method. Si is 33 to 38 μm by IP method, Sn is 17 to 23 μm by hot dipping method, Ti is 8 to 29 μm by sputtering method, Ga is 18 μm by evaporation method, Ge is 11 μm by evaporation method, Mo is 8 μm by sputtering method, V Was 6 μm by sputtering, Cr was 5 μm by sputtering, and As was 11 μm by vapor deposition.

Table 4 shows the types of base metal plates, the types of coating elements, and the heat treatment conditions. The heat treatment atmosphere is a vacuum of 10 ⁻³ Pa level. During cooling, when the cooling rate was 1 ° C./s or less, temperature control was performed by controlling the furnace output in vacuum. When the cooling rate was 10 ° C./s or more, Ar gas was introduced and the cooling rate was controlled by adjusting the flow rate.
Under each condition, one sheet was used for crystal orientation and structure observation, and the other sheet was used for magnetic measurement.

As in Example 1, the cross-sectional structure of the metal plate produced under each condition was observed with an optical microscope. As a result, crystal grains grew like a columnar crystal from the surface as shown in FIG. It was. On the other hand, the crystal grains were isotropic in the region where the film was not attached. Thus, the region where the film element was adhered and the region where the film element was not adhered could be clearly distinguished.
Table 4 shows the results of measuring the surface integration degree of {200} and {222} of the α-Fe phase in the region where the film element is adhered and the region where the film element is not adhered after heat treatment by the X-ray diffraction described above. . From these results, it can be seen that according to the present invention, a predetermined region of the Fe-based metal plate can be integrated in the {200} texture.

Thus, the magnetic properties of the Fe-based metal plate in which half of the plate was patterned into {200} texture according to the present invention were examined in the same manner as in Example 2. The results are also shown in Table 4. For the Si film, a metal plate having the same film pattern as in Example 3 was also evaluated in the same manner.
The results are shown in Table 5. As can be seen from these results, even in the same plate, a higher magnetic flux density was obtained in the {200} integrated region than in the random region. This is because the {200} integrated region contains more [100] orientation, which is the easy axis of magnetization, and the permeability of this region is high. Thus, by using the Fe-based metal plate of the present invention, it becomes possible to control the flow of magnetic flux in the plate.

(Example 5)
The effect of depositing Al, Sb, W, Zn, Al—Si alloy, and Sn—Zn alloy, which are different metals, as a film on the Fe-based base metal plate was examined. Six types of component systems G to L shown in Table 6 were used for the Fe-based base metal plate. Each was melted in a 230 mm thick ingot by vacuum melting and then hot rolled at 1000 ° C. to a thickness of 50 mm. After cutting plate materials having various thicknesses from these hot-rolled plates by machining, cold rolling was subsequently performed to produce base metal plates having different shear strains and thicknesses of 10 μm to 6000 μm. Some samples were further subjected to shot blasting in the same manner as in Example 4. Shear strain was applied by rotating the upper and lower rolling rolls at different speeds during rolling. At that time, the shear strain was changed between 0.1 and 0.8 by changing the difference in rotational speed. As the value of the shear strain, a value obtained by calculation on a desk from the difference between the roll diameter and the roll speed was used.

  Two of these base metal plates were cut out into 50 mm squares and masked using a Kapton tape in the same manner as in Example 2. At that time, the Kapton tape was aligned so that exactly half of the 50 mm square plate was masked, and the Kapton tape on the front surface and the back surface were aligned at the same position. In this state, various coating elements were attached to each base metal plate with the following thickness per side. Al is 0.7 μm by IP method, 7 to 68 μm by hot dipping method, 205 and 410 μm by clad method, Sb is 6 μm film by sputtering method, W is 2 μm by sputtering method, Zn is 44 μm by hot dipping method, 90 μm % Al-10% Si alloy was 40 μm by hot dipping, and 92% Sn-8% Zn alloy was 26 μm by hot dipping.

Table 7 shows the types of base metal plates, the types of coating elements, and the heat treatment conditions. The heat treatment atmosphere is a vacuum of 10 ⁻³ Pa level. However, in the case of Zn, it was performed in Ar gas.
Under each condition, one sheet was used for observation of crystal orientation and structure, and the other sheet was used for magnetic measurement.

  As in Example 1, the cross-sectional structure of the metal plate produced under each condition was observed with an optical microscope. As a result, crystal grains grew like a columnar crystal from the surface as shown in FIG. It was. On the other hand, the crystal grains were isotropic in the region where the film was not attached. Thus, the region where the film element was adhered and the region where the film element was not adhered could be clearly distinguished.

  Table 7 also shows the results of measuring the surface integration degree of {200} and {222} of the α-Fe phase in the region where the film element is adhered and the region where the film element is not adhered after the heat treatment by the above-mentioned X-ray diffraction. Indicated. From these results, it can be seen that according to the present invention, a predetermined region of the Fe-based metal plate can be integrated in the {200} texture.

  Thus, the magnetic properties of the Fe-based metal plate in which half of the plate was patterned into {200} texture according to the present invention were examined in the same manner as in Example 2. The results are also shown in Table 7. As can be seen from these results, even in the same plate, a higher magnetic flux density was obtained in the {200} integrated region than in the random region. This is because the {200} integrated region contains more [100] orientation, which is the easy axis of magnetization, and the permeability of this region is high. Thus, by using the Fe-based metal plate of the present invention, it becomes possible to control the flow of magnetic flux in the plate.

(Example 6)
The component system A shown in Table 3 was used for the Fe-based base metal plate. After melting into a 230 mm thick ingot by vacuum melting, it was hot rolled at 1000 ° C. to a thickness of 50 mm. Cold-rolling was performed after cutting plate materials of various thicknesses from these hot-rolled plates by machining. The rolling reduction is 80%. The thickness of the obtained base metal plate was 150 μm.

  Two of these base metal plates were cut out into 50 mm squares and masked using a Kapton tape in the same manner as in Example 2. At that time, the Kapton tape was aligned so that exactly half of the 50 mm square plate was masked, and the Kapton tape on the front surface and the back surface were aligned at the same position. In this state, Zn and Sn as film elements were adhered to both surfaces with a thickness of 4 μm per side on each base metal plate. An infrared gold image furnace was used for the heat treatment, the temperature was raised to 1000 ° C. at 10 ° C./min under program control, the temperature was maintained for 2 hours, and then the furnace was cooled. The heat treatment atmosphere is Ar gas.

  As in Example 1, the cross-sectional structure of the metal plate produced under each condition was observed with an optical microscope. As a result, crystal grains grew like a columnar crystal from the surface as shown in FIG. It was. On the other hand, the crystal grains were isotropic in the region where the film element was not attached. Thus, the region where the film element was adhered and the region where the film element was not adhered could be clearly distinguished.

  Table 8 shows the results of measuring the surface integration degree of {200} and {222} of the α-Fe phase in the region where the film element is adhered and the region where the film element is not adhered after the heat treatment by the X-ray diffraction described above. . From these results, it can be seen that according to the present invention, a predetermined region of the Fe-based metal plate can be integrated in the {222} texture.

  The Fe-based metal plate of the present invention can be applied to various new uses that could not be conventionally envisaged, such as application to electromagnetic materials, machining materials, etc., energy saving, productivity improvement, etc. A wide range of effects can be expected. In particular, it is suitable for magnetic cores such as transformers in which silicon steel plates are used, and can contribute to miniaturization of these magnetic cores and energy loss reduction.

Claims (4)

An Fe-based metal plate containing at least one metal element other than Fe among ferrite-forming elements ,
A part of the plate surface of the metal plate has a region patterned in a predetermined shape, and the crystal plane of the α-Fe phase in the region portion has a {200} plane integration degree of 30% or more and 99% or less. And {222} plane integration degree is 0.01% or more and 30% or less, or {200} plane integration degree is 0.01% or more and 15% or less, and {222} plane integration degree is 60% or more and 99% or less. A Fe-based metal plate having a partially controlled crystal orientation.
Here, the {200} plane integration degree or {222} plane integration degree is determined by X-ray diffraction using MoKα rays, and there are 11 orientation planes ({110}, {200}) of α-Fe crystals parallel to the sample surface. , {211}, {310}, {222}, {321}, {411}, {420}, {332}, {521}, {442}), and measure each of the measured values. 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 having a random orientation is obtained as a percentage. Before SL region portion Fe-based metal plate partially crystalline orientation according is controlled in claim 1, characterized in that it contains a metal element other than Fe alloyed. Metal elements other than the Fe is, Al, Cr, Ga, Ge , Mo, Sb, Si, Sn, Ti, V, W, or claim 1, characterized in that at least one element among Zn 2 2. An Fe-based metal plate having a partially controlled crystal orientation. Fe-based metal plate partially crystalline orientation is controlled according to any one of claims 1 to 3, wherein the thickness of the Fe-based metal plate is 10μm ultra 6mm or less.