KR101142570B1 - Steel plate having high gathering degree of ?222?plane and process for production thereof - Google Patents

Abstract

A steel sheet having an Al content of less than 6.5% by mass, wherein (1) {222} surface area of one or both of αFe phase and γFe phase with respect to the steel sheet is 60% or more and 99% or less, and (2) with respect to the steel sheet A steel sheet having a high {222} area density, wherein the {200} area density of one or both of the αFe phase and the γFe phase is one or both of 0.01% or more and 15% or less.

Steel plate surface, αFe phase, γFe phase, surface area, Al content

Description

STEEL PLATE HAVING HIGH GATHERING DEGREE OF ｛222｝ PLANE AND PROCESS FOR PRODUCTION THEREOF}

The present invention relates to a steel sheet excellent in workability, such as deep drawing molding, press working, and punching processing, and a method for producing the steel sheet.

In addition to the demand for high strength and light weight, steel sheets for automobiles and home appliances are required to have excellent workability that can be processed without generating cracks and wrinkles in processing processes such as press molding.

The workability of the steel sheet can be improved depending on the aggregate structure of the αFe phase or the γFe phase, and in particular, by increasing the {222} surface integration degree of the crystal on the steel sheet surface. For this reason, some methods have been proposed to increase the workability of steel by controlling the aggregate structure.

Japanese Patent Application Laid-Open No. 6-2069 discloses X-rays of {222} planes and {200} planes in which the amounts of Si, Mn, and P in the high strength cold rolled steel sheet and hot dip galvanized steel sheet are parallel to the steel sheet surface. It is disclosed to secure the deep drawing property by controlling based on a constant relationship of the ratio of diffraction intensity.

Japanese Patent Application Laid-Open No. 8-13081 discloses a (111) aggregate structure by defining an amount of Nb in terms of C amount in a high strength cold rolled steel sheet for enamel and a method of manufacturing the same, and also defining the conditions of hot rolling and cold rolling. Control is disclosed.

Japanese Patent Application Laid-Open No. 10-18011 discloses an alloyed hot dip galvanized steel sheet and a method for manufacturing the same, wherein the ratio of {200} plane strength and {222} plane strength among X-ray diffraction intensities, I (200) / I (222). ) would be the generation of shape defect line on the coated surface lost is less than 0.17, and if the finish rolling temperature of the hot rolling as a _r3 + more than 30 ℃ X-ray diffraction intensity ratio, I (200) / I ( 222) Is disclosed to be less than 0.17.

Japanese Unexamined Patent Application Publication No. 11-350072 discloses a ferrite grain size No. of the surface layer portion occupying 1/10 of the total sheet thickness from the surface of the steel sheet in an ultra low carbon cold rolled steel sheet having a C content of 0.01% or less. Ab≥0.5, a≥7.0, and b≤7.5 are satisfied with b as the ferrite grain size No. of the inner layer portion, which accounts for half of the total sheet thickness, centered on the center of thickness, and the {222} plane and {200} Pressing the ratio I (222) / I (200) of the X-ray diffraction intensity from the surface to 5.0 or more in the 1 / 15th part of the overall sheet thickness from the surface of the steel sheet and 12 or more in the center of the sheet thickness of the steel sheet It is disclosed that the skin roughness of the steel sheet during molding can be reduced.

As described above, in order to improve the workability of the steel sheet, a method of increasing the {222} area accumulation degree of the αFe phase or the γFe phase has been devised so as to optimize the steel sheet components, rolling conditions, temperature conditions, and the like.

Further, Japanese Patent Application Laid-Open No. 2006-144116 discloses that in a high Al-containing steel sheet having an Al content of 6.5% by mass or more and 10% by mass or less, the {222} area density of the αFe crystal is 60% or more and 95% or less, or It is disclosed to improve the workability by setting the {200} surface integration degree to 0.01% or more and 15% or less.

In addition, in the publication, in the high Al-containing steel sheet, an Al alloy is attached to the surface of the base steel sheet having an Al content of 3.5% by mass or more and less than 6.5% by mass as a method of increasing the surface integration degree of the specific surface, and cold rolling. Then, diffusion heat treatment is disclosed.

In addition, since steel sheets are required to have a small burr generated at the cut surface during punching as one of workability, various methods have been conventionally proposed to suppress burr generation.

Japanese Patent Application Laid-Open No. Hei 3-277739 discloses a steel sheet in which the surface layer of the steel sheet is cured so as to make the burr at the time of shearing extremely small, and to have a smooth hardness distribution inside the steel sheet so as not to impair press formability. Specifically, the steel plate whose r value (rank pod value) is 1.7-2, and the burr height at the time of punching process becomes 12-40 micrometers is disclosed.

Japanese Patent Application Laid-open No. Hei 8-188850 discloses a cold rolled steel sheet in which deep drawing and punching workability are enhanced by adding 0.003 to 0.03% of S so as to satisfy a constant expression in the ultra low carbon steel. Specifically, the steel plate which r value is 2.2-2.6 and the burr height at the time of punching process is set to 30-80 micrometers is disclosed.

As described above, a method of improving the {222} area density of the αFe phase or the γFe phase by optimizing the steel sheet components, rolling conditions, temperature conditions, and the like has been devised in the past, and has been in demand to improve the workability of the steel sheet.

However, in order to cope with higher demands, it is difficult in the prior art and a new viewpoint is required.

That is, in the steel plate of the {222} area-integration degree conventional degree, the punching workability becomes poor in a machining process, and the plastic fluidity | liquidity required in complicated press work is inadequate, and it cannot cope with high processing and high efficiency of a machining process.

Specifically, the steel sheet has a problem that burrs are generated on the cut surface during punching, and a chamfering step for removing the burrs is required.

In addition, when the steel sheet is pressed into a complicated form, there is a problem that the slippage between the mold surface and the steel sheet is insufficient, so that the steel sheet cannot be processed into a complicated shape more than the conventional one.

Although the steel plate disclosed by Unexamined-Japanese-Patent No. 2006-144116 has the workability which can produce the foil which forms a honeycomb structure, the {222} area-integration degree which improves workability is higher than ever before, In the beginning, since there is much Al content, it cannot cope with high processing and high efficiency of a processing process as a normal steel plate for processing.

Further, the method disclosed in Japanese Patent Application Laid-Open No. 6-2069, Japanese Patent Application Laid-Open No. 8-13081, Japanese Patent Application Laid-Open No. 10-18011, and Japanese Patent Application Laid-open No. Hei 11-350072 Although the {222} plane can be integrated to a certain ratio, there is a limit to the improvement of the surface integration degree only by setting the conditions in the conventional process such as component conditions and annealing.

In the method disclosed in Japanese Patent Application Laid-Open No. 2006-144116, the {222} area density is increased by adding a step of attaching an Al alloy to the surface of the base material by a molten Al plating method to the base material surface.

However, the above method is a method in which the {222} area density is improved only when a base material having an Al content of 3.5% by mass or more and less than 6.5% by mass is used, and this method is simply applied to a steel sheet having a low Al content to improve the degree of integration of a specific surface. It is difficult to get high or low.

Further, the method disclosed in Japanese Patent Application Laid-Open No. 3-277739 and Japanese Patent Application Laid-Open No. 8-188850 succeeds in reducing generation of burrs accompanying punching process to some extent, but removing burrs It did not reach to the thing which can omit the chamfering process to make.

Therefore, the present invention has a high level of {222} surface integration degree, which has not been conventionally studied by further examining the technique of controlling the texture by plating or the like on the surface of the steel sheet, and does not generate burrs on the cut surface during punching. It aims at providing the "Al content steel plate less than 6.5 mass%" which is excellent in workability.

Moreover, an object of this invention is to provide the manufacturing method which manufactures the "less than 6.5 mass% Al content steel plate" which has the high {222} surface integration degree which has not existed conventionally.

The inventors of the present invention found that, in a steel sheet having an Al content of less than 6.5 mass%, the {222} area density of the (x1) Fe crystal is within a high specific range, and / or the {200} area density of the (x2) Fe crystal is low. When it set to the range, it discovered that the outstanding workability which has not existed conventionally that a burr does not generate | occur | produce in a cut surface at the time of a punching process was acquired.

In addition, the inventors of the present invention provide a method of effectively integrating a specific crystal plane at a high rate in a steel sheet having an Al content of less than 6.5% by mass, and (y1) on the surface of the base steel sheet having an Al content of less than 3.5% by mass (the base steel sheet). To form a first layer and a layer provided on the surface thereof as a second layer), and then heat treatment thereafter to make a specific crystal plane highly integrated, so that the Cr content in the base steel sheet is 12% by mass or less, and (y2 (2) It discovered that it was effective to adhere a 2nd layer to the surface of the base material steel plate whose Al content is less than 6.5 mass%, to carry out cold rolling, and to remove a 2nd layer after that and heat-treat.

The gist of the present invention is described below.

(1) It is a steel plate whose Al content is less than 6.5 mass%,

(1) the {222} surface area of one or both of the αFe phase and the γFe phase with respect to the steel plate surface, between 60% and 99%, and

(2) A steel sheet having a high {222} surface area density, characterized in that the {200} area accumulation degree of one or both of the αFe phase and the γFe phase with respect to the steel plate surface is one or both of 0.01% or more and 15% or less. .

(2) It is a steel plate with Al content less than 6.5 mass% with a 2nd layer affixed on at least one side of a surface,

(1) the {222} surface area of one or both of the αFe phase and the γFe phase with respect to the steel plate surface, between 60% and 99%, and

(2) A steel sheet having a high {222} surface area density, characterized in that the {200} area accumulation degree of one or both of the αFe phase and the γFe phase with respect to the steel plate surface is one or both of 0.01% or more and 15% or less. .

(3) It is a steel plate whose Al content is less than 6.5 mass% in which the 2nd layer is formed in at least one side of the surface, and the 2nd layer and the steel plate are alloyed in one part,

(1) the {222} surface area of one or both of the αFe phase and the γFe phase with respect to the steel plate surface, between 60% and 99%, and

(2) A steel sheet having a high {222} surface area density, characterized in that the {200} area accumulation degree of one or both of the αFe phase and the γFe phase with respect to the steel plate surface is one or both of 0.01% or more and 15% or less. .

(4) A steel sheet having an Al content of less than 6.5% by mass, in which the second layer attached to at least one side of the surface is alloyed with the steel sheet,

(1) the {222} surface area of one or both of the αFe phase and the γFe phase with respect to the steel plate surface, between 60% and 99%, and

(2) A steel sheet having a high {222} surface area density, characterized in that the {200} area accumulation degree of one or both of the αFe phase and the γFe phase with respect to the steel plate surface is one or both of 0.01% or more and 15% or less. .

(5) The steel sheet having the high {222} area integration degree according to any one of (1) to (4), wherein the {222} area integration degree is 60% or more and 95% or less.

(6) The second layer is Fe, Al, Co, Cu, Cr, Ga, Hf, Hg, In, Mn, Mo, Nb, Ni, Pb, Pd, Pt, Sb, Si, Sn, Ta, Ti, A steel sheet having a high {222} area density as described in any one of (2) to (5), wherein the steel sheet contains at least one element of V, W, Zn, and Zr.

(7) A steel sheet having a high {222} surface integration degree in any one of the above (1) to (6), wherein the steel sheet has a thickness of 5 µm or more and 5 mm or less.

(8) A steel sheet having a high {222} surface integration degree in any one of (2) to (7), wherein the thickness of the second layer is 0.01 µm or more and 500 µm or less.

(9) (a) Process of adhering 2nd layer to at least one side of steel plate whose Al content as a base material is less than 6.5 mass%,

(b) cold rolling the steel sheet with the second layer,

(c) removing the second layer from the steel sheet after cold rolling, and

(d) A method for producing a steel sheet having a high {222} surface area, characterized by having a step of subjecting the steel sheet from which the second layer is removed to recrystallize the steel sheet.

(10) (a) Process of adhering a 2nd layer to the at least single side | surface of the steel plate whose Al content as a base material is less than 3.5 mass%,

(b) cold rolling the steel sheet with a second layer, and

(c) a step of heat-treating the steel sheet after cold rolling to recrystallize the steel sheet,

(d) A method for producing a steel sheet having a high {222} area density, wherein the Al content of the steel sheet after recrystallization is less than 6.5 mass%.

(11) (a) Process of adhering 2nd layer to at least one side of steel plate whose Al content as a base material is less than 3.5 mass%,

(b) cold rolling the steel sheet with a second layer, and

(c) heat treating the steel sheet after cold rolling to alloy a part of the second layer and recrystallize the steel sheet;

(d) A method for producing a steel sheet having a high {222} area density, wherein the Al content of the steel sheet after alloying and recrystallization is less than 6.5 mass%.

(12) (a) Process of adhering a 2nd layer to at least one side of the steel plate whose Al content as a base material is less than 3.5 mass%,

(b) cold rolling the steel sheet with a second layer, and

(c) heat-treating the steel sheet after cold rolling to alloy the second layer and to recrystallize the steel sheet;

(d) A method for producing a steel sheet having a high {222} area density, wherein the Al content of the steel sheet is less than 6.5 mass%.

(13) In the manufacturing method of the steel plate which has a high {222} surface-density degree in any one of said (9)-(12),

(1) the {222} surface area of one or both of the αFe phase and the γFe phase with respect to the steel plate surface, between 60% and 99%, and

(2) High {222} surface area, characterized in that the {200} area density of one or both of the αFe phase and the γFe phase with respect to the steel sheet surface is controlled to be one or both of 0.01% or more and 15% or less. Method for producing a steel sheet having a.

(14) The manufacturing method of the steel plate which has a high {222} surface-density degree in any one of said (9)-(12),

(1) the {222} surface area of one or both of the αFe phase and the γFe phase with respect to the steel plate surface, between 60% and 95%, and

(2) High {222} surface area, characterized in that the {200} area density of one or both of the αFe phase and the γFe phase with respect to the steel sheet surface is controlled to be one or both of 0.01% or more and 15% or less. Method for producing a steel sheet having a.

(15) The manufacturing method of the steel plate which has a high {222} area-integration degree in any one of said (9)-(12) WHEREIN: A 2nd layer is Fe, Al, Co, Cu, Cr, Ga, Hf, Hg High {222, characterized in that it contains at least one of In, Mn, Mo, Nb, Ni, Pb, Pd, Pt, Sb, Si, Sn, Ta, Ti, V, W, Zn, and Zr } Method for producing steel sheet having surface density.

(16) (a) Fe, Co, Cu, Cr, Ga, Hf, Hg, In, Mn, Mo, Nb, Ni, Pb, as a second layer on at least one side of a steel sheet having an Al content of less than 6.5% by mass as the base material; Attaching at least one element of Pd, Pt, Sb, Si, Sn, Ta, Ti, V, W, Zn, and Zr,

(b) cold rolling the steel sheet with the second layer,

(c) removing the second layer from the steel sheet after cold rolling, and

(d) A method for producing a steel sheet having a high {222} surface area, characterized by having a step of subjecting the steel sheet from which the second layer is removed to recrystallize the steel sheet.

(17) (a) Fe, Co, Cu, Cr, Ga, Hf, Hg, In, Mn, Mo, Nb, Ni, Pb as a second layer on at least one side of a steel sheet having an Al content of less than 6.5% by mass as the base material Adhering at least one element of Pd, Pt, Sb, Si, Sn, Ta, Ti, V, W, Zn, and Zr,

(b) cold rolling the steel sheet with a second layer, and

(c) A method for producing a steel sheet having a high {222} surface area, characterized by having a step of subjecting the steel sheet after cold rolling to recrystallization of the steel sheet.

(18) (a) Fe, Co, Cu, Cr, Ga, Hf, Hg, In, Mn, Mo, Nb, Ni, Pb, as a second layer on at least one side of a steel sheet having an Al content of less than 6.5% by mass as the base material; Attaching at least one element of Pd, Pt, Sb, Si, Sn, Ta, Ti, V, W, Zn, and Zr,

(b) cold rolling the steel sheet with a second layer, and

(c) A method for producing a steel sheet having a high {222} surface area, characterized by having a step of subjecting the steel sheet after cold rolling to alloying a part of the second layer and recrystallizing the steel sheet.

(19) (a) Fe, Co, Cu, Cr, Ga, Hf, Hg, In, Mn, Mo, Nb, Ni, Pb on at least one side of a steel sheet having an Al content of less than 6.5% by mass as the base material Adhering at least one element of Pd, Pt, Sb, Si, Sn, Ta, Ti, V, W, Zn, and Zr,

(b) cold rolling the steel sheet with a second layer, and

(c) A method for producing a steel sheet having a high {222} surface area, characterized in that it has a step of heat-treating the steel sheet after cold rolling to alloy the second layer and recrystallize the steel sheet.

(20) The manufacturing method of the steel plate which has a high {222} area-density degree in any one of said (9)-(19) characterized by the thickness of the steel plate as said base material being 10 micrometers or more and 10 mm or less.

The thickness of the said 2nd layer is 0.05 micrometer or more and 1000 micrometers or less, The manufacturing method of the steel plate which has the high {222} surface-density degree in any one of said (9)-(19) characterized by the above-mentioned.

(22) A method for producing a steel sheet having a high {222} surface integration degree in any one of the above (9) to (19), wherein the steel sheet is subjected to a preliminary heat treatment before attaching the second layer.

(23) A method for producing a steel sheet having a high {222} surface integration degree according to (22), wherein the temperature of the preliminary heat treatment is 700 to 1100 ° C.

(24) The method for producing a steel sheet having a high {222} area density as described in (22) or (23), wherein the atmosphere of the preliminary heat treatment is at least one of a vacuum, an inert gas atmosphere, and a hydrogen atmosphere. .

(25) A method for producing a steel sheet having a high {222} surface integration degree according to any one of (9) to (19), wherein the step of attaching the second layer to the steel sheet is by a plating method.

(26) A method for producing a steel sheet having a high {222} surface integration degree according to any one of (9) to (19), wherein the step of attaching the second layer to the steel sheet is by a rolling clad method. .

(27) Production of a steel sheet having a high {222} surface integration degree in any one of (9) to (19), wherein the reduction ratio in the cold rolling step is 30% or more and 95% or less. Way.

(28) The high {222 to any one of the above (9) to (19), wherein the heat treatment temperature in the step of performing the heat treatment is 600 ° C or more and 1000 ° C or less and the heat treatment time is 30 seconds or more. } Method for producing steel sheet having surface density.

(29) The method for producing a steel sheet having a high {222} surface integration degree according to any one of (9) to (19), wherein the heat treatment temperature in the step of performing the heat treatment is more than 1000 ° C.

The steel sheet having the high {222} surface area of the present invention (steel plate of the present invention) has an Al content of less than 6.5% by mass, and also has a high {222} area density, or a low {200} area area, so that the punching process may be performed. It is a steel sheet excellent in workability which does not exist conventionally that burr does not generate | occur | produce in a cut surface.

Therefore, the steel sheet of the present invention can be easily processed into various shapes including a special shape from a conventional shape, and for example, various kinds including outer plates such as automobile parts and home appliance parts that require press molding of a complicated shape. It is useful for structural materials, functional materials, and the like.

The manufacturing method of this invention can make it easy and effective to make {222} surface integration degree high, or to make {200} surface integration degree low in the steel plate whose Al content is less than 6.5 mass%. Moreover, the manufacturing method of this invention can manufacture the steel plate of this invention which has a high {222} area-integration degree easily at low cost only by replacing the process of an existing installation, without making a new installation.

EMBODIMENT OF THE INVENTION Below, this invention is demonstrated in detail.

The inventors made the Al content of the steel sheet less than 6.5% by mass, increased the {222} area density of the (X1) Fe crystal phase to 60% or more and 99% or less, and / or (x2) {200} area density. By lowering the amount to 0.01% or more and 15% or less, it was found that a steel sheet excellent in workability, which does not exist in the past, in which no burr is generated on the cut surface during punching processing can be provided.

MEANS TO SOLVE THE PROBLEM The inventors found that "Al content 6.5 mass% or more and 10 mass% or less in which the {222} area density of the αFe phase is 60% or more and 95% or less, and the {200} area density of the αFe phase is 0.01% or more and 15% or less. High Al-containing steel sheet "is disclosed in Japanese Patent Application Laid-Open No. 2006-144116.

The manufacturing method of the said steel plate adheres the Al alloy to the at least single side | surface of the steel plate containing 3.5 mass% or more and 6.5 mass% or less of Al, cold-working and giving a deformation | transformation, and performing the heat processing which diffuses Al continuously, It is characterized by the above-mentioned. do.

MEANS TO SOLVE THE PROBLEM In the steel plate whose Al content is less than 6.5 mass%, the present inventors earnestly dealt with and developed various experiments to develop the technique which raises the {222} area-integration degree further.

As a result, with respect to the method of integrating a specific crystal plane, the present inventors use a base steel sheet having an Al content of less than 3.5% by mass, and the Cr content of the base steel sheet is 12% by mass or less, and not only Al but also an agent made of another metal. It was found that the {222} area density can be increased by attaching the two layers to the steel sheet and then performing heat treatment to recrystallize the steel sheet.

This is described in Japanese Patent Application Laid-Open No. 2006-144116, "A special dislocation structure formed in a steel sheet at the time of cold rolling is effectively formed, and recrystallization which develops {222} surface aggregation structure from dislocation structure by heat processing is carried out. The nucleus develops efficiently ”.

That is, according to the present invention, even if the component system of the steel sheet is a component system in which the Al content after recrystallization is less than 6.5 mass%, the frequency of occurrence of the recrystallization nucleus tends to be high, resulting in a steel sheet having a higher {222} surface area degree. You can get it.

Moreover, in this invention, Cr content in a base material steel plate is less than 10 mass% is preferable, and {222} surface integration degree can be raised more easily under this Cr content.

In the case of using a base steel sheet having an Al content of less than 6.5% by mass, the second layer is attached to the surface of the steel sheet to perform cold rolling, and subsequently, the second layer is removed, whereby a high {222} surface area can be obtained by subsequent heat treatment. have.

This phenomenon is also considered to be expressed based on the above-mentioned recrystallization nucleation mechanism.

Below, the detail of this invention is demonstrated further.

The steel plate of this invention is comprised in one or both of an alpha Fe phase and a gamma Fe phase at normal temperature, and Al content is less than 6.5 mass%.

When the Al content is 6.5% by mass or more, not only a high {222} surface-assembly structure can be easily obtained, but also the tensile elongation at break decreases, and sufficient workability cannot be obtained even with a high {222} surface-density degree.

In other words, in the steel sheet having an Al content of 6.5% by mass or more, no matter how the {222} area density is increased, and even if the {200} area density is reduced, burrs are generated on the cut surface during punching. Therefore, in the steel plate of this invention, Al content was made into less than 6.5 mass%.

As for Al content of the steel plate of this invention, 0.001 mass% or more is preferable. When Al is 0.001 mass% or more, the yield at the time of manufacture improves. More preferably, it is 0.11 mass% or more. If Al is 0.11 mass% or more, the {222} surface area becomes higher, and as a result, higher workability can be obtained.

The present inventors adhered the second layer to at least one side of the base steel sheet having an Al content of less than 3.5% by mass, and then subjected to heat treatment to recrystallize the steel sheet, thereby forming one or both of the αFe phase and the γFe phase with respect to the steel sheet surface. 222} found that the area density can be extremely high.

The steel sheet (steel sheet of the present invention) having a high {222} surface integration degree of the present invention is excellent in workability such as deep drawing molding and punching processing.

Since Al content of a base material steel plate is less than 3.5 mass%, even if Al is contained in a 2nd layer, deformation | transformation, such as shrinkage, does not occur easily in a steel plate in a manufacturing process. As for Al content of a base material steel plate, 0.001 mass% or more is preferable. If Al is 0.001 mass% or more, the manufacture yield of a base material steel plate will improve.

The steel sheet of this invention is comprised by one or both of an alpha Fe phase and gamma Fe phase.

The αFe phase is a Fe crystal phase in a body-centered orientation, and the γFe phase is a Fe crystal phase in a face-centered cubic structure. The Fe crystal phase contains that another atom partially substituted Fe or penetrated between Fe atoms.

The steel sheet of the present invention has an Al content of less than 6.5% by mass, and the {222} area density of one or both of the αFe phase and the γFe phase is 60% or more and 99% or less, and one or both of the αFe phase and the γFe phase. It is characterized by the fact that the {200} surface area density of is one or both of 0.01% or more and 15% or less.

If the said surface integration degree is in the range of this invention, the average r value (rank pod value) which is an evaluation value of drawing workability will be 2.5 or more, and the outstanding workability that burr does not generate | occur | produce in a cut surface at the time of punching process can be obtained.

The area density was measured by X-ray diffraction with MoKα rays. The {222} area density of the αFe phase and the {200} area density of the αFe phase were obtained as follows.

Α crystals of Fe parallel to the sample surface: {110}, {200}, {211}, {310}, {222}, {321}, {411}, {420}, {332}, { 521} and {442} integral strengths were measured, and each of the measured values was divided by the theoretical integral intensity of the sample in the random orientation, and then the ratio of the {200} intensity or {222} intensity was determined as a percentage.

For example, the ratio with {222} intensity | strength is shown by following formula (1).

{222} area

= [{i (222) / I (222)} / {Σi (hkl) / I (hkl)}] × 100 ??? (1)

However, symbols are as follows.

i (hkl): Actual integrated intensity of the {hkl} plane in the measured sample

I (hkl): The theoretical integral intensity of the {hkl} plane in a sample with random orientation

Σ: Sum of 11 planes of α-Fe crystals

Similarly, the {222} area density and the {200} area density of the γFe phase were obtained as follows.

Integral intensity of γ crystal 6 surfaces of Fe, {111}, {200}, {220}, {311}, {331}, and {420}, which are parallel to the sample surface, were measured, and each of the measured values was measured. After dividing by the theoretical integral intensity of the sample which is a random orientation, the ratio with {200} intensity | strength or {222} intensity | strength was calculated | required as a percentage.

For example, the ratio with {222} intensity | strength is shown by following formula (2).

{222} area

= [{i (111) / I (111)} / {Σi (hkl) / I (hkl)}] x 100... (2)

However, symbols are as follows.

i (hkl): Actual integrated intensity of the {hkl} plane in the measured sample

I (hkl): The theoretical integral intensity of the {hkl} plane in a sample with random orientation

Σ: Sum of six faces of γ-Fe crystals

Regarding the αFe grains, the {222} area density can also be obtained by EBSP (Electron Backscattering Diffraction Pattern, EBSP) method separately.

The area ratio of {222} to the total area of the crystal plane which can be measured by the EBSP method becomes the {222} density diagram. Therefore, in the steel sheet of this invention also by EBSP method, {222} surface area degree is 60% or more and 99% or less.

In this invention, the value obtained by all the analysis methods does not need to satisfy the range prescribed | regulated by this invention, and the effect of this invention is acquired when the value obtained by one analysis method meets the range of this invention.

In addition, in the EBSP method, a misalignment of the {222} plane occurs with respect to the steel plate surface, but the misalignment is preferably within 30 degrees.

It is preferable that the deviation of the {222} plane is observed in the L cross section, and the ratio of the area of the crystal grains having the deviation of the {222} plane of 30 ° or less is 80 to 99.9%.

Moreover, as for the deviation of the {222} plane in L cross section, it is more preferable that the area ratio of the crystal grain of 0-10 degrees is 40 to 98%.

 An average r value means the average plastic strain ratio calculated by JISZ2254, and is a value computed by the following formula | equation.

Average r value = (r0 + 2r45 + r90) / 4... (3)

Here, r0, r45, and r90 are the plastic deformation ratios which the test piece was extract | collected and measured in the direction of 0 degrees, 45 degrees, and 90 degrees with respect to the rolling direction of a plate surface, respectively.

In addition, the integrated intensity of a sample having a random orientation may be obtained by measuring the sample.

In the steel sheet of the present invention, (i) the {222} surface area 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, and / or (ii) the αFe phase with respect to the steel plate surface. And the {200} surface integration degree of one or both of the γFe phases is 0.01% or more and 15% or less.

If the {222} surface area is less than 60% and the {200} surface area is more than 15%, cracks or fractures are likely to occur during drawing, bending, and rolling, and burrs are generated on the cut surface during punching. .

If the {222} area concentration is more than 99% and the {200} area density is less than 0.01%, the effect of the present invention is saturated, and the production becomes difficult.

Therefore, the aggregate structure of the steel plate of this invention was prescribed | regulated as mentioned above.

Moreover, as for {222} surface integration degree of one or both of (alpha) Fe phase and (gamma) Fe phase with respect to a steel plate surface, 60% or more and 95% or less are preferable. If the {222} surface area is in the above range, production is easier and the yield is improved.

The {200} surface integration degree of one or both of the αFe phase and the γFe phase with respect to the steel sheet surface is preferably 0.01% or more and 10% or less. If {200} surface integration degree is in the said range, a burr will not generate | occur | produce in a cut surface at the time of a punching process.

One method of manufacturing the steel sheet of the present invention is a step of attaching the second layer to at least one side of the base steel sheet having an Al content of less than 6.5%, cold rolling to the steel sheet with the second layer, steel sheet after cold rolling The process of removing a 2nd layer from the process, and a process of heat-processing the steel plate from which the 2nd layer was removed, and recrystallizing a steel plate are comprised.

In order to obtain a high {222} surface area, cold rolling is essential in the state where the second layer is attached to the base steel sheet.

At this time, if the second layer is not attached to at least one side of the base steel sheet, a high {222} area density cannot be obtained. If the second layer is attached to both surfaces of the steel sheet and subjected to cold rolling, the effect of the present invention can be further enhanced.

When the steel sheet is recrystallized by heat treatment, the second layer does not necessarily have to be attached. The second layer adhered to the steel sheet may be removed before the heat treatment.

For example, when the elements constituting the second layer are diffused into the steel sheet during heat treatment, adversely affecting mechanical properties and the like, removing the second layer before heat treatment can achieve only the {222} surface area improvement effect.

A steel sheet having a second layer attached to at least one side of the surface, wherein the {222} surface 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, and αFe with respect to the steel plate surface The steel plate whose one or both of {200} surface integration degree of one or both of a phase and (gamma) Fe phase is one or both is contained in the steel plate of this invention.

If the {222} surface area is less than 60% and the {200} surface area is more than 15%, cracks or fractures are likely to occur during drawing, bending, and rolling, and burrs are generated on the cut surface during punching. .

If the {222} area concentration is more than 99% and the {200} area density is less than 0.01%, the effect of the present invention is saturated, and the production becomes difficult.

Here, if the second layer is attached to the steel sheet, internal oxidation, corrosion, etc. of the steel sheet can be prevented, and the steel sheet can be further functionalized.

The method for producing this steel sheet is a step of attaching a second layer to at least one side of a base steel sheet having an Al content of less than 3.5% by mass, a step of cold rolling in a state in which the second layer is attached, and a heat treatment to the steel sheet. To recrystallize the steel sheet.

In order to obtain a higher {222} surface area, cold rolling is preferably performed in a state in which the second layer is attached to the base steel sheet.

In the subsequent steps, the effect of the present invention can be obtained even if the second layer is attached to at least one side of the surface when the steel sheet is subjected to heat treatment to recrystallize the steel sheet. If the second layer is attached to both surfaces of the base steel sheet, the effect of the present invention is further enhanced.

The second layer and the steel sheet are alloyed in part, and the {222} area density of one or both of the αFe phase and the γFe phase with respect to the steel sheet is 60% or more and 99% or less, and the αFe phase and γFe with the steel sheet The steel plate of one or both of the {200} surface integration degree of one or both phases of 0.01% or more and 15% or less is also contained in the steel plate of this invention.

If the {222} surface area is less than 60% and the {200} surface area is more than 15%, cracks or fractures are likely to occur during drawing, bending, and rolling, and burrs are generated on the cut surface during punching. .

If the {222} area concentration is more than 99% and the {200} area density is less than 0.01%, the effect of the present invention is saturated, and the production becomes difficult.

If the second layer is attached to the surface of the steel sheet and a part of the second layer is alloyed with the steel sheet, it is possible to prevent internal oxidation, corrosion, etc. of the steel sheet, and to prevent peeling of the second layer, thereby making the steel sheet more functional. can do.

In order to obtain a higher {222} surface area, it is preferable to add a step of cold rolling in a state in which the second layer is attached to at least one side of the base steel sheet. If the second layer is attached to both surfaces of the base steel sheet, the effect of the present invention is further enhanced.

In a subsequent process, it is necessary to heat-treat and recrystallize a steel plate. At that time, a part of the second layer adhering to one or both surfaces is alloyed with the base steel sheet to obtain a higher {222} surface integration degree.

Here, the meaning that the second layer and the steel sheet are alloyed in part means that the alloy is partially alloyed by mutual diffusion near the boundary between the second layer and the steel sheet, for example.

The second layer and the steel sheet are alloyed, and the {222} area concentration of one or both of the αFe phase and the γFe phase on the steel sheet is 60% or more and 99% or less, and the αFe phase and γFe phase on the steel sheet The steel plate which is one or both of the {200} surface integration degree of one or both of them is 0.01% or more and 15% or less is also contained in the steel plate of this invention.

If the {222} surface area is less than 60% and the {200} surface area is more than 15%, cracks or fractures are likely to occur during drawing, bending, and rolling, and burrs are generated on the cut surface during punching. .

If the {222} area density is more than 99% and the {200} area density is less than 0.01%, the effects of the present invention will be saturated and manufacturing will be difficult.

When the said 2nd layer is affixed on the steel plate surface, and the 2nd layer is alloyed with a steel plate, the mechanical property or functionality of a steel plate will improve according to the element which comprises a 2nd layer. For example, when the element which comprises a 2nd layer is Al, the high temperature oxidation resistance and corrosion resistance of a steel plate will improve.

In order to obtain a higher {222} surface area, it is preferable to cold-roll in a state where the second layer is attached to the base steel sheet, and then heat-treat the steel sheet to recrystallize it.

At the time of cold rolling, the state in which the 2nd layer adheres to at least one side of the base material steel plate preferably on both sides is essential. Thereafter, the second layer is completely alloyed with the steel sheet through a heat treatment process to obtain a higher {222} surface area.

In the steel sheet of the present invention having the second layer, the second layer is preferably a metal.

The elements constituting the preferred second layer are Fe, Al, Co, Cu, Cr, Ga, Hf, Hg, In, Mn, Mo, Nb, Ni, Pb, Pd, Pt, Sb, Si, Sn, Ta, At least one of Ti, V, W, Zn, and Zr.

The above elements have a common feature of alloying elements with Fe. Especially preferably, it is an element of at least one or more of Al, Cr, Ga, Mo, Nb, P, Sb, Si, Sn, Ti, V, W, and Zn, which tend to solidify in αFe to stabilize the α phase.

And more preferably, it is an element of at least one of Al, Cr, Mo, Si, Sn, Ti, V, W, and Zn which is dissolved in αFe and tends to stabilize the α phase more.

For example, Al alloy, Zn alloy, Sn alloy, etc. can be selected as a 2nd layer.

Moreover, in the manufacturing method of the steel plate of this invention, it is preferable that it is a metal similarly to the above also about the 2nd layer performed on the surface of a base material steel plate.

The elements constituting the preferred second layer are Fe, Al, Co, Cu, Cr, Ga, Hf, Hg, In, Mn, Mo, Nb, Ni, Pb, Pd, Pt, Sb, Si, Sn, Ta, Ti At least one of V, W, Zn, and Zr.

The above elements have a common feature of alloying elements with Fe. Especially preferably, it is an element of at least one or more of Al, Cr, Ga, Mo, Nb, P, Sb, Si, Sn, Ti, V, W, and Zn, which tend to solidify in αFe to stabilize the α phase.

More preferably, it is an element of at least one or more of Al, Cr, Mo, Si, Sn, Ti, V, W, and Zn, which is dissolved in αFe and tends to stabilize the α phase.

For example, Al alloy, Zn alloy, Sn alloy, etc. can be selected as a 2nd layer.

Here, when Al contains in a 2nd layer, preferable Al content of a base material steel plate is less than 3.5 mass%. If the Al concentration of the base steel sheet is 3.5% by mass or more, and the heat treatment is performed while the Al alloy is attached as the second layer, shrinkage occurs during heat treatment, and the dimensional accuracy is significantly reduced.

Therefore, in the steel plate of this invention, when 2nd layer contains Al, Al content of a base material steel plate shall be less than 3.5 mass%.

When 2nd layer does not contain Al, Al content of a base material steel plate shall be less than 6.5 mass%.

The manufacturing process is Fe, Co, Cu, Cr, Ga, Hf, Hg, In, Mn, Mo, Nb, Ni, Pb, Pd, Pt, Sb, Si, Sn, Ta, Ti on at least one side. In the case of including the step of adhering at least one element of V, W, Zn, and Zr, when the Al content of the base steel sheet is 6.5% by mass or more, the tensile fracture elongation of the steel sheet obtained is lowered and has a high {222} surface area. Even if it exists, sufficient workability cannot be obtained and burr will generate | occur | produce in a cut surface at the time of punching processing.

Therefore, Al content of a base material steel plate in the case where a 2nd layer does not contain Al shall be less than 6.5 mass%.

In addition, even if the second layer contains Al, if the second layer is removed before the heat treatment, shrinkage does not occur. Therefore, when removing a 2nd layer before heat processing, the Al content of a base material steel plate is preferably less than 6.5 mass%.

The method of improving a work efficiency is also contained in this invention by omitting the process of removing a 2nd layer among these manufacturing methods.

Also included in the present invention is a method of producing a steel sheet having a high {222} surface area by alloying part or all of the second layer by heat treatment.

In the present invention, the alloying region of the steel sheet and the second layer is defined as follows.

In the second layer, the element having the highest content is A, and the Fe content is 0.5 mass% higher than the Fe content of the second layer before alloying, and the A content is 0.1 mass% higher than the A content of the base steel sheet before alloying. Is defined as the alloying region.

And the ratio of alloying is the ratio which an alloying area occupies for the whole area | region. In the steel sheet of the present invention, more excellent workability can be obtained by forming an alloying region according to the above definition.

Moreover, when Fe content and / or A content increase and an intermetallic compound etc. are formed, higher effect of this invention can be acquired.

Further, the alloying ratio can be obtained by analyzing the content distribution of Fe and element A in the L cross section using, for example, EPMA and the like, to determine the alloying region, and to obtain its area, and to obtain the ratio of the total area of the specific region area. have.

As for the thickness of the steel plate of this invention, 5 micrometers or more and 5 mm or less are preferable. This is the thickness including the second layer. If the thickness of the steel sheet is less than 5 µm, the production yield is lowered, which is not suitable for practical use.

When the thickness of the steel sheet exceeds 5 mm, the {222} area density may not fall within the scope of the present invention. Therefore, the thickness of the steel sheet is preferably 5 µm or more and 5 mm or less.

As for the thickness of a steel plate, 100 micrometers or more and 3 mm or less are more preferable. When the thickness of the steel sheet is 3 mm or less, the effect of suppressing the occurrence of burrs on the cut surface at the time of punching becomes more remarkable.

If the thickness of the steel sheet is 100 µm or more, the {222} surface integration degree is more easily controlled, and the effect of suppressing the occurrence of the burr becomes more remarkable.

In the thickness of the steel sheet of the present invention, the thickness of the second layer is preferably 0.01 µm or more and 500 µm or less. When the steel plate and the second layer are partially alloyed, the thickness of the alloyed portion is included in the thickness of the second layer. When the 2nd layer is affixed on both surfaces, it is the sum total of the thickness of both surfaces.

While the second layer has a function of increasing the {222} surface integration degree at the time of manufacture, it can be used as a rust-proof protective film of a steel plate, without removing after manufacture.

Since the possibility of peeling will become high when the thickness of a 2nd layer is more than 500 micrometers, 500 micrometers or less are preferable. When the thickness of the second layer is less than 0.01 µm, the film is likely to be damaged, and the rust preventing protection effect is reduced.

Therefore, the thickness of the second layer is preferably 0.01 μm or more. It is also preferable that the whole thickness of the steel sheet is alloyed, and in this case, the second layer is considered to have disappeared.

In the manufacturing method of the steel plate of this invention, the thickness of a base material steel plate is 10 micrometers or more and 10 mm or less. If the thickness of the base steel sheet is less than 10 µm, the production yield may decrease in the step after cold rolling, which may not be suitable for practical use.

If the thickness of the base steel sheet is more than 10 mm, there is a possibility that the {222} area density does not fall within the scope of the present invention.

Therefore, as for the thickness of a base material steel plate, 10 micrometers or more and 10 mm or less are preferable.

As for the thickness of a base material steel plate, more than 130 micrometers, 7 mm or less are more preferable. In this thickness range, an efficient and sufficient increase in the {222} area density can be expected, and it becomes easy to manufacture a steel sheet which can further suppress the occurrence of burrs during punching.

Prior to cold rolling, the thickness of the second layer attached to the base steel sheet is preferably 0.05 µm or more and 1000 µm or less. When the steel plate and the second layer are alloyed, the thickness of the alloyed portion is included in the thickness of the second layer. When the 2nd layer is affixed on both surfaces, it is the sum total of the thickness of both surfaces.

If the thickness of the second layer is less than 0.05 µm, the {222} area density may be lowered and fall within the scope of the present invention, so 0.05 µm or more is preferable.

In the case where the thickness of the second layer is more than 1000 µm, since the {222} area density becomes low and may not fall within the scope of the present invention, 1000 µm or less is preferable.

In order to express the effect of this invention which is further excellent, it is preferable to pre-heat-treat a base material steel plate before attaching a 2nd layer.

This preliminary heat treatment rearranges the dislocations accumulated in the manufacturing process of the base steel sheet. For this purpose, it is preferable to cause recrystallization, but it is not necessary to cause recrystallization.

The preliminary heat treatment temperature is preferably 700 ° C. or higher and 1100 ° C. or lower. If the preliminary heat treatment temperature is less than 700 ° C, it is difficult to change the dislocation structure for obtaining the effect of the present invention which is superior, and thus the preliminary heat treatment temperature is 700 ° C or more.

If the preheating temperature is higher than 1100 ° C, an undesirable oxide film is formed on the surface of the steel sheet, which adversely affects subsequent deposition of the second layer and cold rolling, so the preheating temperature is 1100 ° C or lower.

The atmosphere of the preliminary heat treatment may be any of vacuum, inert gas atmosphere, hydrogen atmosphere, and weakly oxidizing atmosphere. In any of the atmospheres, the effect of the present invention can be obtained. However, an atmosphere in which the oxide film adversely affects the adhesion of the second layer after preliminary heat treatment and cold rolling is required.

The preliminary heat treatment time does not need to be particularly limited, but considering the manufacturability of the steel sheet or the like, it is appropriate from several seconds to several hours.

The attachment of the second layer to the steel sheet can be carried out by a fusion plating method, an electroplating method, a dry process method, a clad method, or the like. Either method can be used to obtain the effects of the present invention. Moreover, it is also possible to add a desired alloying element to the 2nd layer made to adhere, and to alloy simultaneously.

Cold rolling is performed in the state which attached the 2nd layer to the steel plate, and the reduction ratio is 30% or more and 95% or less.

If the reduction ratio is less than 30%, the {222} area density of the steel sheet obtained after the heat treatment may be low, and may not reach the scope of the present invention. If the reduction ratio is more than 95%, the increase in surface area is saturated, and the manufacturing cost is increased. Therefore, reduction ratio is made into 30% or more and 95% or less.

In the case of removing the second layer before the heat treatment, as the removal method, a mechanical removal method such as polishing or a chemical removal method by dissolving a strong acid or strong alkali solution can be applied.

For example, in the case of an Al-coated steel sheet, only the plating component is removed by immersing the steel sheet in caustic soda water. As a result, the influence of the Al component can be eliminated in the heat treatment step.

The heat treatment for recrystallizing the steel sheet can be performed in a non-oxidizing atmosphere such as a vacuum atmosphere, an Ar atmosphere, or an H ₂ atmosphere. At this time, heat processing temperature is 600 degreeC or more and 1000 degrees C or less, and 30 second or more of heat processing time is preferable.

If heat processing temperature is 600 degreeC or more, {222} area | region integration degree becomes high and it reaches the range of this invention easily. If the heat treatment temperature is 1000 ° C. or lower and the heat treatment time is less than 30 seconds, the {222} area density is similarly higher, and easily reaches the scope of the present invention.

Therefore, heat processing temperature is 600 degreeC or more and 1000 degrees C or less, and, as for heat processing time, 30 second or more is preferable.

If the heat treatment temperature is more than 1000 ° C., there is no restriction on the heat treatment time, and a high {222} surface area can be obtained. Particularly, if it is more than 1000 ° C., even if the heat treatment time is less than 30 seconds, the {222} area density can be easily increased.

Moreover, as for heat processing temperature, 1300 degrees C or less is more preferable. If heat processing temperature is 1300 degrees C or less, plate shape, such as flatness of a steel plate, will become more excellent.

As for the temperature increase rate at the time of heat processing, 1 degreeC / min or more and 1000 degrees C / min or less are preferable. If the temperature increase rate is 1000 DEG C / min or lower, higher {222} area density can be easily obtained. Productivity will improve especially that a temperature increase rate is 1 degree-C / min or more.

Therefore, the temperature increase rate is preferably 1 ° C / minute or more and 1000 ° C / minute or less.

The heat treatment performed in a state where the second layer is attached is intended to recrystallize the steel sheet, and to diffuse the elements contained in the second layer into the steel.

When the element contained in the second layer diffuses into the steel, the {222} area density is further improved, and the high temperature oxidation resistance and mechanical properties are improved. Thus, in the method for manufacturing the steel sheet of the present invention, the second layer is included in the second layer. Actively use elemental diffusion.

It is preferable that a base material steel plate shall make Cr content 12 mass% or less under Al content mentioned above. As for Cr content, less than 10 mass% is more preferable.

In addition, a base material steel plate is a steel plate whose C content is 2.0 mass% or less, and contains a trace amount Mn, P, S, etc. as an impurity. For example, carbon steel is included in the base steel sheet of the present invention. In addition, alloy steel containing an alloying element such as Ni or Cr in addition to C is also included in the base steel sheet of the present invention.

Alloying elements which the base steel sheet may contain are Si, Al, Mo, W, V, Ti, Nb, B, Cu, Co, Zr, Y, Hf, La, Ce, N, 0, and the like.

 Example

Hereinafter, an Example demonstrates this invention further in detail.

(First embodiment)

The Al content of the base steel sheet was changed to investigate the manufacturability and the {222} area density.

A base steel plate was manufactured with five types of component systems of different Al content. Al content is mass%, 3.0% (component A), 3.4% (component E), 4.0% (component B), 6.0% (component C), 7.5% (component D), and others are C: 0.008%, Si: 0.2%, Mn: 0.4%, Cr: 20.0%, Zr: 0.08%, La: 0.08%, the residual component iron and an unavoidable impurity were used.

In these component systems, the ingot was melted by vacuum melting, the hot roll was applied to the ingot, and the thickness was reduced to 3.0 mm thickness.

In the case of components A, B, C, and E, it was easy to hot roll to a steel plate of 3.0 mm thickness, but in the case of component D, the steel sheet was frequently broken during hot rolling, and hot rolling could not be continued.

Thus, manufacture becomes difficult that Al content of a base material steel plate is 6.5% or more exceeding the range of this invention. Therefore, manufacturing the steel plate of the component D was abandoned, and the steel plates of the components A, B, C, and E were then cold rolled to 0.4 mm thickness.

The principal phase at normal temperature of the steel plate of components A, B, C, and E was (alpha) Fe phase. The aggregate structure of the αFe phase of the base steel sheet was measured by X-ray diffraction to calculate the area density as described above.

The {222} surface area is 32% in component A, 31% in component B, 31% in component C, and 30% in component E. The {200} surface area is 16% in component A, 15% in component B, and component It confirmed that it was 16% in C and 16% in component E.

Each steel plate was subjected to a heat treatment of 800 ° C. × 10 sec in a hydrogen atmosphere before forming the second layer. Then, Al alloy was made to adhere to the surface of a base material steel plate using the fusion plating method.

The composition of the plating bath was% by mass, 90% Al-10% Si, and the Al alloy was attached to both surfaces of the steel sheet.

The adhesion amount was controlled so that Al content might be 3.5% (component A), 4.5% (component B), 6.4% (component C), and 6.4% (component E) in mass% in the whole steel plate.

With the Al alloy adhering to the second layer, each steel sheet was cold rolled at a reduction ratio of 70%. Subsequently, heat treatment was performed under conditions of 1000 ° C. × 120 min in vacuum to recrystallize the steel sheet.

At this time, the steel sheets of the components B and C caused shrinkage during the heat treatment, and the dimensional accuracy was significantly reduced.

When Al was contained in the 2nd layer, when Al content of the base material steel plate was 3.5% or more which is outside the range of this invention, it confirmed that shrinkage occurred during heat processing, and it became difficult to provide practically.

On the other hand, shrinkage does not arise that Al content of a base material steel plate is less than 3.5% in the range of this invention, and it can provide for practical use.

The same heat treatment was performed by adhering the 2nd layer which does not contain Al to the base material steel plate which Al content is 3.5% or more. In this case, no shrinkage occurred during the heat treatment.

When the steel sheets of the components A and E were used as the base steel sheets, the {222} area density of the obtained steel sheets was 82% and 83%, respectively, and the {200} area density was 0.5% and 0.8%, respectively. Was in the range of.

Moreover, the average r value was measured about these steel sheets, and it confirmed that the average r value exists in the high level of 2.5 or more. These steel sheets have excellent drawing workability.

As described above, the steel sheet produced by the production method of the present invention has a {222} area density of 60% or more parallel to the steel sheet surface or a {200} area density of 15% or less parallel to the steel sheet surface. We confirmed that it was in range.

(2nd Example)

The result of manufacturing the steel plate which has high {222} surface area degree using Al alloy as a 2nd layer is shown.

The component of the base steel sheet is mass%, and the component system contains Al: 1.5%, C: 0.008%, Si: 0.1%, Mn: 0.2%, Cr: 18%, Ti: 0.1%, and the remainder part iron and unavoidable impurities. to be.

A base steel plate is a steel plate which melts an ingot by the vacuum melting method, hot-rolls an ingot, it is a 3.8 mm thick steel plate, and is 0.8 mm thick by cold rolling.

The columnar phase at normal temperature of a base material steel plate was an αFe phase. By X-ray diffraction, the aggregate structure of the αFe phase of the base steel sheet was measured, and it was confirmed that the {222} area density was 36% and the {200} area density was 20%.

Some base steel sheets were subjected to a heat treatment of 800 ° C. × 10 sec in a hydrogen atmosphere before plating. The Al alloy was attached to the surface of the base steel sheet using the fusion plating method.

The composition of the plating bath was 90% Al-10% Si in mass%, and the Al alloy was attached to both surfaces of the steel sheet. The thickness of the deposited Al alloy was controlled to be uniform in the steel plate surface.

Cold rolling was performed to the steel plate to which Al alloy was affixed. Thereafter, heat treatment was performed in a non-oxidizing atmosphere. Before the heat treatment, the Al alloy attached to the surface was removed as necessary.

Removal of the Al alloy was performed by immersing the steel sheet in a 10% aqueous solution of caustic soda to dissolve the Al alloy in a solution.

As a comparative example, the case where cold rolling was not performed after attaching Al alloy was also examined.

In Table 1, the alloying ratio of the steel plate manufactured on various conditions, the {222} area density degree of the αFe phase, the {200} area density degree of the αFe phase, and Al content were shown. The area density was measured using X-ray diffraction and calculated by the calculation processing method described above.

 The alloying ratio of the steel sheet was obtained as follows. In the L cross section, the surface distribution of the Fe content and the surface distribution of the Al content were measured using an EPMA (Electron Probe Micro-Analysis) method in a L-direction of 1 mm x total thickness.

The area of Fe ≧ 0.5% by mass and Al ≧ 1.6% by mass was obtained as an alloying region, and the area thereof was obtained to obtain an alloying area. The alloying ratio was calculated by dividing the alloying area by the area in the L direction of 1 mm × overall thickness.

In the first comparative example of No. 1, the deposition amount of the Al alloy was controlled by adjusting the plating thickness so that the Al content of the whole steel sheet became 3.2%. The Al alloy was removed without undergoing cold rolling after plating, and the steel sheet was subjected to heat treatment under conditions of 950 ° C × 10 min to recrystallize the steel sheet.

As a result, the {222} area density and {200} area density were outside the scope of the present invention. Al content in the obtained steel sheet was 1.5% in the same manner as the base steel sheet because the Al alloy was removed.

In the second comparative example of No. 2, the step of attaching the Al alloy as the second layer was omitted. The base steel sheet was cold rolled at a reduction ratio of 50%, and then the steel sheet was subjected to heat treatment under conditions of 950 ° C × 10 min to recrystallize the steel sheet.

In this case, the {222} area density and the {200} area density were outside the scope of the present invention.

In the invention example of No. 3, plating thickness was adjusted and controlled so that the adhesion amount of Al alloy might be set to 3.2% of the whole steel plate. After the plating, the steel sheet was cold rolled at a reduction ratio of 50%, the Al alloy was subsequently removed, and the steel sheet was subjected to heat treatment under conditions of 950 ° C × 0.1 min to recrystallize the steel sheet.

As a result, the {222} area density was out of the scope of the present invention, while the {200} area density was in the scope of the present invention. Since Al content in the obtained steel plate was removing Al alloy, it was 1.5% similar to a base material.

In Inventive Examples 1 and 2 of Nos. 4 and 5, the steel sheet was subjected to a heat treatment at 800 ° C., and then Al alloy was attached to the surface of the steel sheet so that the Al content was 3.2% in the whole steel sheet. Thereafter, the steel sheet was cold rolled at a reduction ratio of 50% to reduce the thickness.

After removing the Al alloy, in No. 4, the steel sheets were subjected to heat treatment under conditions of 950 ° C. × 1 min, and in No. 5, the steel sheets were subjected to heat treatment under conditions of 950 ° C. × 10 min to recrystallize each steel sheet.

As a result, the {222} area density and the {200} area density of both the first and second invention examples Nos. 4 and 5 are all controlled within the scope of the present invention, and the Al content is also within the scope of the present invention. I checked it. Al content in the obtained steel sheet was 1.5% which is the same as that of the base steel sheet because the Al alloy was removed.

The third invention example of No. 6 omits the heat treatment before attaching the Al alloy from the invention example of No. 5, but the {222} area density and {200} area density are all controlled within the scope of the present invention. It was confirmed that Al content was also within the scope of the present invention.

Since Al content in the obtained steel plate was removing Al alloy, it was 1.5% similar to a base material steel plate.

In the fourth invention example and the fifth invention example of Nos. 7 and 8, before the Al alloy was deposited, the steel sheet was subjected to heat treatment at 800 ° C., and the Al alloy was subsequently attached.

The Al alloy adhesion amount of No. 7 was controlled so that Al content might be 3.2% in the whole steel plate. The Al alloy adhesion amount of No. 8 was similarly controlled so that Al content might be 6.0% in the whole steel plate. Thereafter, both steel sheets were cold rolled at a reduction ratio of 50% to reduce the thickness.

After removing the Al alloy and eliminating the rolling oil on the surface of the steel sheet, the steel sheet was subjected to heat treatment under conditions of 1000 ° C. × 120 min to recrystallize the steel sheet. By this heat treatment, the Al alloy adhered to the steel sheet surface was completely alloyed with the steel sheet.

The obtained {222} area integration degree and the [200} area integration degree were all controlled within the scope of the present invention, and it was confirmed that the Al content was also within the scope of the present invention.

In the fourth comparative example of No. 9, the deposition amount of the second layer was increased in comparison with the invention examples of Nos. 7 and 8. Al alloy adhesion amount was controlled so that Al content might be 7.5% in the whole steel plate.

Other processes were the same as the invention examples of Nos. 7 and 8, and the Al alloy adhered to the steel sheet surface by heat treatment was completely alloyed with the steel sheet.

As a result, the Al content of the steel sheet became 7.5% and exceeded the range of the present invention. The {222} area density of this steel sheet was significantly improved, but the scope of the present invention was not reached.

As a result of the tensile test, the elongation at break was 10% or less, indicating that the toughness was low. From this, it turned out that the steel plate of No. 9 is not suitable for practical use.

In the fifth comparative example of No. 10, the Al alloy was attached to the surface of the steel sheet so that the Al content became 3.2% in the whole steel sheet. Cold rolling after adhering Al alloy was omitted. After the Al alloy was attached, the steel sheet was subjected to heat treatment under the condition of 1050 ° C. × 0.17 min to recrystallize the steel sheet.

As a result, the {222} area density and the {200} area density were both outside the scope of the present invention.

In the sixth invention example and the seventh invention example of Nos. 11 and 12, before the Al alloy was adhered, the Al alloy was attached to the steel sheet surface so that the Al content was 3.2% in the entire steel sheet by heat treatment at 800 ° C.

Then, in the 6th invention example of No.11, it cold-rolled and thinned the steel plate with 50% reduction ratio. In the seventh invention example of No. 12, the steel sheet was cold rolled and thinned at a reduction ratio of 75%.

The removal of Al alloy was abbreviate | omitted, the steel plate was heat-processed on condition of 1050 degreeCx 0.17min, and the steel plate was recrystallized.

As a result, also in any steel plate, {222} surface integration degree and {200} surface integration degree were all controlled in the scope of the present invention, and it confirmed that Al content also contained in the scope of this invention.

The burr resistance test was done about the said steel plate. Punching was performed using the punch of 10.0 mm (phi) and the die of 10.3mm (phi), and the burr height around the punching hole was measured by the point micrometer.

As a result, although the height of the burr was in the high level of 23-65 micrometers in the comparative example, it confirmed that it was in the extremely low level of 4-9 micrometers in the invention example.

When the average r value was measured about the steel plate of the above Example, it confirmed that the average r value was in the high level of 2.5 or more in the steel plate of the invention example, but in the steel plate of the comparative example, the average r value was less than 2.5, or the result of no measurement was possible. .

Therefore, the steel plate of the invention example has the outstanding drawing workability. In addition, about the steel plate of the invention example, the Ericsson test was done and the extrusion surface was observed and it confirmed that it was excellent also in press workability.

As described above, the steel sheet produced by the production method of the present invention has a {222} area accumulation degree of at least 60% parallel to the steel sheet surface or a {200} area accumulation degree of at most 15% or less parallel to the steel sheet surface. It confirmed that it was in the scope of the invention.

As a result, in the steel plate manufactured by the manufacturing method of this invention, it was confirmed that the outstanding burr resistance and drawing workability are compatible.

(Third Embodiment)

The result of manufacturing the steel plate which has a high {222} area-integration degree using Zn alloy as a deposit (2nd layer) is shown.

A base steel plate is the mass% by vacuum melting method, and contains Al content 0.01%, other C: 0.005%, Si: 0.2%, Mn: 0.5%, Ti: 0.05%, remainder iron, and an unavoidable impurity. It is the steel plate which melted the ingot of a component system, was made into 3.2 mm thickness by hot rolling, and then rolled to 1.8 mm thickness by cold rolling.

The columnar phase at normal temperature of a base material steel plate was an αFe phase. The aggregate structure of the αFe phase of the base steel sheet was measured by X-ray diffraction to confirm that the area density of {222} was 28% and the area density of {200} was 19%.

Some base steel sheets were subjected to a heat treatment of 770 ° C. × 5 sec in a hydrogen atmosphere before plating.

The Zn alloy was attached to the surface of the base steel sheet using the electroplating method. The plating bath uses a sulfuric acid-based acidic solution, and the deposited plating is an alloy of 94% Zn-6% Ni in mass%. The thickness of the deposited Zn alloy was controlled to be uniform in the steel plate surface.

Cold rolling was performed on the steel plate to which the Zn alloy was affixed, and heat processing was performed in non-oxidizing atmosphere after that. Before the heat treatment, the Zn alloy attached to the steel sheet surface was removed as necessary. Removal of the Zn alloy was performed by immersing the steel sheet in a 10% aqueous hydrochloric acid solution to dissolve the Zn alloy in a solution.

As a comparative example, the case where cold rolling was not performed after attaching Al alloy was also examined.

In Table 2, the alloying ratio of the steel plate manufactured on various conditions, the {222} area density of the αFe phase, the {200} area density of the αFe phase, and Al content were shown. In addition, the surface area was measured by X-ray diffraction and calculated by the aforementioned calculation processing method.

The alloying ratio of the steel sheet was obtained as follows. In L cross section, the surface distribution of Fe content and the surface distribution of Zn content were measured using EPMA method in the visual field of 1 mm x total thickness of L direction.

The area of Fe ≧ 0.5% by mass and Zn ≧ 0.1% by mass was obtained as an alloying region, and the area thereof was determined to be an alloying area. The alloying ratio was calculated by dividing the alloying area by the area in the L direction of 1 mm × overall thickness.

In addition, by the EBSP method, the {222} plane deviation of the {222} plane with respect to the steel plate surface, and the {222} plane deviation of the {222} plane with respect to the steel plate surface were determined in the L cross section. The area ratio obtained by observation was described.

Moreover, the burr resistance test was done about the said steel plate. Punching was performed using a punch of 30.0 mmφ and a die of 30.6 mmφ, and the burr height around the punching hole was measured by a point micrometer.

In Comparative Example 6 of No. 13, a Zn alloy having a thickness of 0.8 μm was attached to the surface of the steel sheet. Cold rolling was omitted, the Zn alloy was removed, and the steel sheet was then subjected to a heat treatment under conditions of 1050 ° C. × 0.1 min to recrystallize the steel sheet.

As a result, the {222} area density and the {200} area density of this steel sheet were all out of the scope of the present invention.

In the seventh comparative example of No. 14, the Zn alloy was omitted, and the steel sheet was cold rolled at a reduction ratio of 70%. Then, the steel plate was heat-treated on the conditions of 1050 degreeCx 0.1min, and the steel plate was recrystallized. In this case, the {222} area density and the {200} area density were all out of the scope of the present invention.

In Example 8 of Example No. 15, a Zn alloy having a thickness of 0.8 μm was deposited on the surface of the steel sheet after heat treatment at 770 ° C. Thereafter, the steel sheet was cold rolled at a reduction ratio of 70% to reduce the thickness. After the removal of the Zn alloy, the steel sheet was subjected to heat treatment under conditions of 1050 ° C. × 0.1 min to recrystallize the steel sheet.

As a result, it was confirmed that the {222} area integration degree and the {200} area integration degree were controlled within the scope of the present invention, and the Al content was also within the scope of the present invention.

In the ninth invention example of No. 16, the heat treatment before attaching the Zn alloy was omitted from the invention example of No. 15, but the {222} area density and {200} area density are all controlled within the scope of the present invention. , Al content was confirmed to be in the range of the present invention.

In the tenth invention example and the eleventh invention example of Nos. 17 and 18, heat treatment was performed at 770 ° C. before adhering the Zn alloy, and then the Zn alloy was deposited.

In No. 17, a Zn alloy having a thickness of 0.8 µm was attached to the surface of the steel sheet. In No. 18, a 0.4 µm thick Zn alloy was attached to the steel plate surface. Thereafter, both steel sheets were cold rolled at a reduction ratio of 70% to reduce the thickness.

After the removal of the Zn alloy was omitted and the rolling oil on the surface of the steel sheet was removed, the steel sheet was subjected to a heat treatment under conditions of 1050 ° C. × 0.1 min to recrystallize the steel sheet. By this heat treatment, part of the Zn alloy attached to the steel sheet surface was alloyed with the steel sheet.

The alloying ratio was 30% in No. 17 and 60% in No. 18. The obtained {222} area integration degree and {200} area integration degree were all controlled within the scope of the present invention, and it was confirmed that the Al content was also within the scope of the present invention.

In Comparative Example 8 of No. 19, a Zn alloy having a thickness of 0.8 μm was attached to the surface of the steel sheet. Cold rolling after adhering a Zn alloy was omitted. After the Zn alloy was attached, the steel sheet was subjected to heat treatment under conditions of 750 ° C. × 10 min to recrystallize the steel sheet.

As a result, the {222} area density and the {200} area density were all outside the scope of the present invention.

In the twelfth and thirteenth invention examples of Nos. 20 and 21, a heat treatment was performed at 770 ° C on a steel sheet before attaching the Zn alloy, and then a Zn alloy having a thickness of 0.8 탆 was deposited on the surface of the steel sheet.

Thereafter, in No. 20, the steel sheet was cold rolled and thinned at a reduction ratio of 30%. In No. 21, the steel plate was cold-rolled and thinned at a rolling reduction of 87%.

The removal of the Al alloy was omitted, and the steel sheet was subjected to heat treatment under conditions of 750 ° C. × 10 min to recrystallize the steel sheet.

As a result, also in any steel plate, {222} surface integration degree and {200} surface integration degree were all controlled in the scope of the present invention, and it turned out that Al content also exists in the scope of the present invention.

Although the burr height was in the high level of 82-92 micrometers in the steel plate of a comparative example, it confirmed that it was the extremely low level of 7-9 micrometers in the steel plate of an invention example.

When the average r value was measured about the steel plate of the above Example, it confirmed that the average r value was in the high level of 2.5 or more in the steel plate of the invention example, but it was a result that it was less than 2.5 in the steel plate of the comparative example.

From these results, in the steel plate manufactured by the manufacturing method of this invention, it was confirmed that the outstanding burr resistance and drawing workability are compatible.

Moreover, about the steel plate manufactured by the manufacturing method of this invention, the extrusion surface was observed by the Ericsson test and it confirmed that it was excellent also in press workability.

As described above, the steel sheet produced by the production method of the present invention has a {222} area accumulation degree of at least 60% parallel to the steel sheet surface or a {200} area accumulation degree of at most 15% or less parallel to the steel sheet surface. It confirmed that it was in the scope of the invention.

(Fourth Embodiment)

The result of manufacturing the steel plate which has high {222} area-integration degree using Cu as a deposit (2nd layer) is shown.

The component of a base steel plate is a mass% and is a component system containing Al: 0.015%, C: 0.15%, Si: 0.1%, Mn: 1.5%, Mo: 0.5%, remainder iron, and an unavoidable impurity.

As a base steel plate, the steel plate which melted the ingot by the vacuum melting method, hot-rolled the ingot, and had thickness 15mm, 10mm, and 3.8mm was used.

In addition, cold rolling was performed on the 3.8 mm steel sheet, and a cold rolled sheet having a thickness of 2.0 mm, 1.0 mm, 0.1 mm, 0.01 mm, and 0.005 mm was also used as the base steel sheet.

The columnar phase at normal temperature of a base material steel plate was an αFe phase. By X-ray diffraction, the aggregate structure of the αFe phase of the base steel sheet was measured, and it was confirmed that the area density of {222} was 36 to 40% and the area density of {200} was 17 to 22%.

Before attaching Cu to a base material steel plate, heat processing of 850 degreeC x 10 sec was performed in hydrogen atmosphere. Thereafter, Cu having different thicknesses was attached to both surfaces of the base steel sheet. Cu was attached using the clad method, the electroplating method or the sputtering method.

In the clad method, the thickness of Cu was changed by changing the thickness of the opposed Cu plate, in the plating method, by changing the energization current and the immersion time, and in the sputter method, by changing the sputter time. A sulfuric acid solution was used for the plating bath.

Cold rolling was performed on the steel plate which Cu adhered to, and the steel plate was heat-treated in non-oxidizing atmosphere after that.

Table 3 shows the {222} area density and the αFe phase {200} area density of the steel sheet prepared under various conditions. In addition, the surface area was measured by X-ray diffraction and calculated by the aforementioned calculation processing method.

In the 14th to 19th inventions of Nos. 22 to 27, Cu was used in a thickness within the scope of the present invention as shown in Table 3 using a cladding method, an electroplating method, or a sputtering method on a base steel sheet having a thickness of 2.0 mm. Attached.

The cold rolling was performed to the steel plate with 60% of the reduction ratio with Cu adhered. Next, the removal of the second layer was omitted, and the steel sheet was subjected to heat treatment under the condition of 1020 ° C. 0.3 min to recrystallize the steel sheet.

In any steel sheet, the {222} surface area was within the scope of the present invention, but the thickness of the second layer at the time of adhering the second layer was greater than 1000 µm, and the thickness of the second layer was 0.05 µm. In less than No. 27, the {222} area density slightly decreased, and the {222} area density exceeded 15%.

In the 14th invention example of No. 22, the thickness of the 2nd layer after manufacture exceeded 500 micrometers, and it was a state which was easy to peel slightly. In the 19th invention example of No.27, the thickness of the 2nd layer after manufacture was less than 0.01 micrometer, and a film was easy to be damaged, and there existed a problem in the rust prevention surface slightly.

In the twentieth to twenty-fifth invention examples of Nos. 28 to 33, 2 µm of Cu was attached to the base steel sheet having a thickness of 0.005 to 15 mm by electroplating. Next, cold rolling was performed to the steel plate at 50% of the reduction ratio in the state which adhered Cu. The removal of the second layer was omitted, and the steel sheet was subjected to heat treatment under conditions of 900 ° C. × 60 min to recrystallize the steel sheet.

Also in any steel plate, although {222} surface integration degree was in the range of this invention, when the thickness of the base material steel plate at the time of adhering was more than 10 mm, and the thickness of the base material steel plate was less than 10 micrometers, 222} area density slightly decreased, and {222} area density exceeded 15%.

When the average r value was measured about the steel plate of the above invention example, it confirmed that the steel plate of the invention example exists in the high level of 2.5 or more. Therefore, the steel plate of the invention example has the outstanding drawing workability.

As described above, the steel sheet produced by the production method of the present invention has a {222} area accumulation degree of at least 60% parallel to the steel sheet surface or a {200} area accumulation degree of at most 15% or less parallel to the steel sheet surface. It confirmed that it was in the scope of the invention.

(Fifth Embodiment)

The result of having produced the steel plate which has high {222} surface integration degree using Cr as a deposit (2nd layer) is shown.

The component of the base steel sheet is mass%, which is a component system containing Al: 0.02%, C: 0.06%, Si: 0.2%, Mn: 0.4%, Cr: 13.1%, Ni: 11.2%, and the remainder part iron and unavoidable impurities. to be.

A base steel plate is a steel plate which melted an ingot by the vacuum melting method, hot-rolled to an ingot after that, to be 3.0 mm thick, and also rolled to 0.8 mm thickness by cold rolling.

The columnar phase at normal temperature of a base material steel plate was a γFe phase. By X-ray diffraction, the aggregate structure of the γFe phase of the base steel sheet was measured, and the surface integration degree was calculated as described above. It was confirmed that the area density of {222} is 24% and the area density of {200} is 21%.

Some of the base steel sheets were subjected to a heat treatment of 950 ° C. × 10 sec in a hydrogen atmosphere before Cr plating.

Cr was attached to the surface of the base steel sheet using the electroplating method. The plating bath used chromium sulfate solution. The thickness of Cr adhered was 0.6 micrometer and it controlled so that it might become uniform in the steel plate surface.

Cold rolling was performed on the steel plate to which Cr was affixed, and the steel plate was heat-treated in non-oxidizing atmosphere after that. Prior to the heat treatment, Cr attached to the surface of the steel sheet was removed as necessary. Cr was removed by mechanical polishing.

In Table 4, the alloying ratio of the steel plate manufactured on various conditions, the {222} area density of γFe phase, the {200} area density of γFe phase, and Al content were shown. In addition, the surface area was measured by X-ray diffraction and calculated by the calculation process.

The alloying ratio of the steel sheet was obtained as follows. In L cross section, the surface distribution of Fe content and the surface distribution of Cr content were measured using EPMA method in the visual field of 1 mm x total thickness of L direction.

The area of Fe ≧ 0.5 mass% and Cr ≧ 13.2 mass% was obtained as the alloying region, and the area thereof was obtained to obtain an alloying area. The alloying ratio was calculated by dividing the alloying area by the area in the L direction of 1 mm × overall thickness.

In the ninth comparative example of No. 34, Cr having a thickness of 0.6 μm was deposited on the steel plate surface. Cold rolling was omitted, Cr was removed, and the steel sheet was then subjected to heat treatment under conditions of 1050 ° C x 0.2 min to recrystallize the steel sheet.

As a result, the {222} area density and {200} area density of this steel sheet were all out of the scope of the present invention.

In the tenth comparative example of No. 35, the deposition of Cr was omitted, and cold rolling was performed on the steel sheet without a deposit at a reduction ratio of 75%. Thereafter, the steel sheet was heat-treated under the condition of 1050 ° C × 0.2 min to recrystallize the steel sheet.

In this case, the {222} area density and the {200} area density were all out of the scope of the present invention.

In the twenty sixth invention example of No. 36, Cr having a thickness of 0.6 µm was deposited on the surface of a steel sheet after heat treatment at 950 ° C. Thereafter, the steel sheet was cold rolled at a reduction ratio of 75% to reduce the thickness.

In addition, after removing Cr, the steel sheet was heat-treated under the condition of 1050 ° C x 0.2 min to recrystallize the steel sheet.

As a result, it was confirmed that both the {222} area density and the {200} area density were controlled within the scope of the present invention, and the Al content was also within the scope of the present invention.

Moreover, it confirmed that it had high toughness about the steel plate of 26th invention example by the tension test.

In the twenty-seventh invention example of No. 37, the heat treatment before depositing Cr was omitted from the invention example of No. 36, but the {222} area density and the {200} area density were all controlled within the scope of the present invention, and the Al content. It was confirmed that it also falls in the scope of the present invention.

In the eleventh comparative example of No. 38, the steel sheet was subjected to heat treatment at 950 ° C. before the Cr was deposited, and then Cr was deposited to be cold rolled at a reduction ratio of 75% as it is to be thinned.

The removal of Cr was abbreviate | omitted, and after removing the rolling oil on the steel plate surface, the steel plate was heat-processed on 400 degreeC * 0.2min conditions. At this time, the steel sheet was not recrystallized.

As a result, the obtained {222} area density and {200} area density were not all within the scope of the present invention.

In Examples 28 to 30 of Nos. 39 to 41, before attaching Cr, the steel sheet was subjected to heat treatment at 950 ° C., and then Cr was adhered. Both were cold-rolled and thinned to the steel plate with the reduction ratio of 75%.

After eliminating Cr and removing the rolling oil on the surface of the steel sheet, in No. 39, the conditions were 1050 ° C. × 0.2 min, in No. 40, the conditions were 1100 ° C. × 0.2 min, and in No. 41, 1150 ° C. × 0.2 min. The steel sheet was subjected to heat treatment under the conditions of to recrystallize the steel sheet.

The adhered Cr was partially alloyed with the steel sheet. The alloying ratio was 10% in No. 39, 30% in No. 40, and 60% in No. 41.

It was confirmed that the obtained {222} area integration degree and {200} area integration degree were all controlled within the scope of the present invention, and the Al content was also within the scope of the present invention.

When the average r value was measured with respect to the steel plate of the above Example, it confirmed that the average r value was in the high level of 2.5 or more in the steel plate of the invention example, but the result was less than 2.5 in the steel plate of the comparative example.

As a result, it was found that the steel sheet of the invention example had excellent drawing workability.

Thus, the steel plate manufactured by the manufacturing method of this invention is the bone | skeleton whose {222} area-density degree of γFe phase parallel to a steel plate surface is 60% or more, or the {200} area-integration degree of γFe phase parallel to a steel plate surface is 15% or less. It confirmed that it was in the scope of the invention.

(Sixth Embodiment)

The thickness of the 2nd layer was changed using Al alloy as a 2nd layer, and the result of having produced the steel plate which has high {222} surface area degree is shown.

The components of the base steel sheet are% by mass, Al: 0.039%, C: 0.0019%, Si: 0.011%, Mn: 0.13%, N: 0.002%, Ti: 0.061%, Cr: 0.002% or less, and the remainder of iron and inevitable. It is a component system containing red impurities.

A base material steel plate is a steel plate of thickness 3.0mm manufactured by hot-rolling an ingot after melting an ingot by the vacuum melting method. In addition, the scale of the steel plate surface was removed by pickling.

The columnar phase at normal temperature of a base material steel plate was (alpha) Fe. The aggregate structure of the αFe phase of the base steel sheet was measured by X-ray diffraction to calculate the surface integration degree as described above. As a result, it was confirmed that the area density of {222} is 19% and the area density of {200} is 17%.

Before plating on the base steel sheet, a heat treatment of 780 ° C × 10 sec was performed in a hydrogen atmosphere. An Al alloy was attached to the surface of the base steel sheet by the fusion plating method. The composition of the plating bath was 90% Al-10% Si in mass%, and was stuck to both surfaces of the steel plate.

 The plating deposition was controlled by spraying nitrogen onto the steel sheet surface with a wiping nozzle before the plating was solidified to remove unnecessary plating.

Cold rolling was performed on the steel plate to which Al alloy was affixed, and it thinned to 0.8 mm. Thereafter, the steel sheet was heat-treated in a non-oxidizing atmosphere to recrystallize the steel sheet and to advance Al diffusion.

In Table 5, the various manufacturing conditions, the alloying ratio of the manufactured steel plate, the {222} area | region density of αFe phase, and the {200} area | region density of AlFe phase and Al content were shown. Each area density was measured by X-ray diffraction and calculated by the calculation process.

The alloying ratio of the steel sheet was obtained as follows. In L cross section, the surface distribution of Fe content and the surface distribution of Al content were measured using EPMA method in the visual field of 1 mm x total thickness of L direction.

The area of Fe ≧ 0.5 mass% and Al ≧ 0.139 mass% was obtained as the alloying region, and the area thereof was obtained to obtain an alloying area. The alloying ratio was calculated by dividing the alloying area by the area in the L direction of 1 mm × overall thickness.

In addition, by the EBSP method, the {222} plane deviation of the {222} plane with respect to the steel plate surface and the {222} plane deviation of the {222} plane with respect to the steel plate surface were observed from the L cross section. The obtained area ratio was described.

The burr resistance test was carried out using a punch of 10.0 mm phi and a die of 10.3 mm phi to measure the burr height around the punching hole with a point micrometer.

In the twelfth comparative example to the fourteenth comparative example of Nos. 42 to 44, the step of adhering the Al alloy was omitted, and cold rolling was performed on the steel sheet without a deposit at a reduction ratio of 73%. Thereafter, the steel sheet was heat treated under the conditions of 700 to 1010 ° C. to recrystallize the steel sheet.

In this case, the {222} area density and the {200} area density are both outside the scope of the present invention. The burr height showed a large value with 51-57 micrometers.

In the thirty-first and thirty-third invention examples of Nos. 45 to 47, an Al alloy having a thickness of 5 µm in front and back was attached. And cold rolling was performed to thickness 0.8mm, the steel plate was heat-processed on 700-1010 degreeC after that, and the steel plate was recrystallized.

In this case, {222} area density and {200} area density were all within the scope of the present invention. The height of a burr is 12-14 micrometers, and it is remarkably decreasing compared with the comparative example.

In the thirty-fourth to forty-fifth invention examples of Nos. 48 to 57, an Al alloy having a front and back total of 10 to 40 µm was attached. And cold rolling was performed to 0.8 mm, the steel plate was heat-processed on 700-010 degreeC after that, and the steel plate was recrystallized. At this time, the temperature increase rate was changed.

In any case, {222} area density and {200} area density were all within the scope of the present invention. The height of burr was 5-8 micrometers, and showed the remarkably small value.

When the average r value was measured about the steel plate of the above Example, it confirmed that the average r value was in the high level of 2.5 or more in the steel plate of the invention example, but it was a result that it was less than 2.5 in the steel plate of the comparative example.

As a result, it was found that the steel sheet of the invention example had excellent drawing workability.

Moreover, the Ericsson test was done and the extrusion surface was observed, and it was confirmed that the steel plate of the invention example was excellent also in press workability.

As described above, the steel sheet produced by the production method of the present invention has a {222} area accumulation degree of at least 60% parallel to the steel sheet surface or a {200} area accumulation degree of at most 15% or less parallel to the steel sheet surface. It was in the scope of the invention, and it was confirmed that excellent burr resistance and drawing workability were compatible.

(Seventh Embodiment)

The Cr content of the base steel sheet was changed to show the results of the manufacturability and the {222} area density.

A base steel plate was manufactured by the component system of four different Cr content. Cr content is mass%, 13.0% (component F), 11.9% (component G), 6.0% (component H), and 0.002% or less (detection limit or less) (component I), others are C: 0.083%, It was set as the component system containing Si: 0.11%, Mn: 0.23%, Al: 0.002%, N: 0.003, remainder iron, and an unavoidable impurity.

In these component systems, the ingot was melted by vacuum melting, the ingot was hot rolled, and the thickness was reduced to 3.5 mm thickness. Subsequently, four kinds of steel sheets were cold rolled to 1.3 mm thickness.

The principal phase at normal temperature of the steel plate of components F, G, H, and I was an alpha Fe phase. The aggregate structure of the αFe phase of the base steel sheet was measured by X-ray diffraction, and surface area was calculated as described above.

The area density of {222} is 8% in component F, 9% in component G, 9% in component H, and 8% in component I. The area density of {200} is 28% in component F and 30% in component G. It confirmed that it was 31% in component H and 29% in component I.

Sn was attached as a 2nd layer to the surface of a base steel plate using the electroplating method. The plating bath was an acidic acid solution, and the plated bath was controlled to have a basis weight of 1 g / m 2 and plated on both surfaces. No preheating was carried out before electroplating.

With Sn adhering to the second layer, each steel sheet was cold rolled at a reduction ratio of 40% to obtain a steel sheet having a thickness of 0.78 mm. For comparison, cold rolling was also performed at a rolling reduction of 40% even on steel sheets to which Sn of the components F, G, H, and I were not adhered.

Subsequently, the steel sheet was heat treated under conditions of a temperature increase rate of 100 ° C./min and 1100 ° C. × 60 min in vacuum to recrystallize the steel sheet. At this time, in any steel sheet, Sn on the surface of the steel sheet was diffused into the steel and all were alloyed.

For comparison, the same heat treatment was performed on the steel sheet without Sn.

{222} surface integration degree and {200} surface integration degree of the obtained 8 types of steel sheets were measured. The {222} surface area of Sn-bonded steel sheet is 65% in component F, 75% in component G, 79% in component H, and 85% in component I. {200} surface area is 12% in component F, and 4% in G, 2.5% in Component H, and 1.4% in Component I.

In all cases, the area density was included in the scope of the present invention, but it was found that particularly high {222} area density can be obtained when Cr is less than 12.0% by mass.

On the other hand, the {222} surface area of Sn-free steel sheet is 21% in component F, 12% in component G, 11% in component H, and 12% in component I. {200} surface area is 16 in component F. %, 17% in component G, 16% in component H, and 16% in component I.

Evaluation of burr resistance was performed by punching using a punch of 10.0 mm phi and a die of 10.3 mm phi to measure the burr height around the punching hole with a point micrometer.

The burr height of the steel plate to which Sn was stuck was 9 micrometers in component F, 7 micrometers in component G, 6 micrometers in component H, and 5 micrometers in component I, and it was confirmed that any steel plate has the outstanding characteristic.

The burr height of the steel plate which Sn did not adhere was 46 micrometers in component F, 52 micrometers in component G, 63 micrometers in component H, and 68 micrometers in component I, and it confirmed that a large burr generate | occur | produced also in any steel plate.

Moreover, when the average r value was measured about these steel plates, it was confirmed that the average r value of the steel plate with Sn was in the high level of 2.5 or more. The average r value of the steel sheet without Sn was about 1.1.

From this, it turned out that the steel plate which Sn adhered has the outstanding drawing workability. Moreover, as a result of performing an Ericsson test and observing the extrusion surface, it confirmed that the steel plate with Sn was excellent also in press workability.

As described above, the steel sheet produced by the production method of the present invention has a {222} area accumulation degree of αFe parallel to the steel plate surface of 60% or more or a {200} area accumulation degree parallel to the steel plate surface of 15% or less of the present invention. It confirmed that it was in a range.

(Example 8)

The Al content of a base material steel plate is changed and the result which investigated the manufacturability and {222} surface integration degree is shown.

A base steel plate was manufactured with four types of component systems of different Al content. Al content is mass%, 7.5% (component J), 6.4% (component K), 3.4% (component L), and 0.002% or less (ICP detection limit or less) (component M), and others are C: 0.083% , Si: 0.11%, Mn: 0.23%, Cr: 0.002% or less (less than the ICP analysis detection limit), N: 0.003, the residual component iron, and an unavoidable impurity.

In these component systems, the ingot was melted by vacuum melting, the ingot was hot rolled, and the thickness was reduced to 2.8 mm thickness.

The ingots of components K, L, and M could easily be hot rolled to the steel sheet, but the ingots of component J were frequently broken during hot rolling, and hot rolling could not be continued.

Thus, if Al content of a base material steel plate is 6.5% or more exceeding the range of this invention, manufacture is difficult and it was discouraged to manufacture the steel plate of component J. Then, the steel sheets of components K, L, and M were cold rolled to 1.6 mm thickness.

The principal phase at normal temperature of the steel plate of components K, L, and M was (alpha) Fe phase. By X-ray diffraction, the aggregate structure of the αFe phase of the base material was measured, and the surface area was calculated in the same manner as described above. The surface area of {222} is 11% in component K, 12% in component L and 12% in component M. The surface area of {200} is 8% in component K, 7% in component L, and 8 in component M. It confirmed that it was%.

Before forming a 2nd layer, this base material steel plate was heat-processed at 750 degreeC x 10 sec in hydrogen atmosphere. Then, the Zn alloy was made to adhere to the surface of a base steel plate using the fusion plating method.

The composition of the plating bath was 95% Zn-5% Fe, and the Zn alloy was attached to both surfaces of the steel sheet. The adhesion amount was made into 80 g / m <2> of front and back, so that the adhesion amount of the front and back might be as uniform as possible.

In the state which adhered the Zn alloy to the 2nd layer, each steel plate was cold-rolled by 50% of reduction ratio, and the steel plate of thickness 0.80mm was obtained.

For comparison, the steel sheets without the Zn alloy to which the components K, L, and M were not attached were cold rolled at a reduction ratio of 50% to make the thickness 0.80 mm.

Subsequently, the steel sheet was heat treated under conditions of a temperature increase rate of 10 ° C./min and 1100 ° C. × 60 min in vacuum to recrystallize the steel sheet. At this time, in any steel sheet, the Zn alloy on the surface of the steel sheet was diffused into steel and alloyed.

For comparison, the same heat treatment was performed on the steel sheet without Zn alloy.

{222} surface integration degree and {200} surface integration degree of the obtained 8 types of steel sheets were measured. The {222} area density of the Zn-alloy coated steel sheet was 78% in component K, 85% in component L, 90% in component M, and 85% in component I. {200} surface area was 1.4% in component K, It was 0.6% in component L and 0.4% in component M.

Although any surface area was included in the scope of the present invention, it was found that particularly high {222} area area can be obtained when Al contained is less than 3.5% by mass.

On the other hand, the {222} area density of the steel sheet without Zn alloy is 36% in component K, 32% in component L and 25% in component M, and {200} surface area is 17% in component K and component L. It was 16% in 19% and component M.

Evaluation of burr resistance was performed by punching using a punch of 10.0 mm phi and a die of 10.3 mm phi, and measuring the burr height around the punching hole with a point micrometer.

The burr height of the steel plate to which Zn was affixed was 7 micrometers in component K, 5 micrometers in component L, and 5 micrometers in component M, and it turned out that all have the outstanding characteristic.

The burr height of the steel plate which did not adhere Zn alloy was 52 micrometers in component K, 57 micrometers in component L, and 65 micrometers in component M, and it confirmed that a large burr generate | occur | produces all.

Moreover, the average r value was measured about these steel plates. It was confirmed that the average r value of the steel sheet to which the Zn alloy was affixed was at a high level of 2.5 or more. The average r value of the steel plate which did not adhere Zn alloy was about 1.1.

From this, it was found that the steel sheet to which the Zn alloy was affixed had excellent drawing workability.

Moreover, the steel plate which carried out the Ericsson test with respect to the said steel plate, and observed the extrusion surface confirmed that the steel plate to which the Zn alloy was stuck was also excellent in press workability.

As described above, the steel sheet produced by the production method of the present invention has a {222} area density of 60% or more parallel to the steel sheet surface or a {200} area density of 15% or less parallel to the steel sheet surface. It confirmed that it was in a range.

(Example 9)

The result of manufacturing the steel plate which has high {222} area-integration degree using Mo, Cr, Ge, Si, Ti, W, and V metal as a deposit of a 2nd layer is shown.

A hot rolled sheet having a thickness of 2.8 mm of the components K, L, and M used in the eighth example was used as the base steel sheet. The steel sheets of components K, L, and M were cold rolled to a thickness of 0.4 mm.

The principal phase at normal temperature of the steel plate of components K, L, and M was (alpha) Fe phase. The aggregate structure of the αFe phase of the base steel sheet was measured by X-ray diffraction, and surface area was calculated as described above.

The {222} surface area is 15% in component K, 17% in component L and 16% in component M. The {200} surface area is 7% in component K, 6% in component L and 8% in component M. Confirmed.

Before performing the sputtering for attaching the second layer, a heat treatment of 620 ° C. × 60 sec was performed on the base steel sheet in an Ar atmosphere. Mo, Cr, Ge, Si, Ti, W, and V metals were adhered to the surface of the base steel sheet using the sputtering method as a second layer.

The metal target material of purity 99.9% or more was prepared, respectively, and it controlled so that thickness per side may be 1 micrometer, and the film was formed on both surfaces.

In the state which attached the 2nd layer which consists of each metal, each steel plate was cold-rolled at the rolling reduction of 62.5%, and the steel plate of thickness 0.15 mm was obtained.

 For comparison, the steel sheets of components K, L, and M which did not adhere the second layer made of each metal were cold rolled at a reduction ratio of 62.5% to have a thickness of 0.15 mm.

Subsequently, the steel sheet was heat treated under conditions of a temperature increase rate of 500 ° C./min and 1150 ° C. × 15 sec in vacuum to recrystallize the steel sheet.

At this time, in any steel sheet, the second layer metal on the surface of the steel sheet was diffused into the steel and all were alloyed. For comparison, the same heat treatment was applied to the steel sheet without the second layer metal attached thereto.

Table 6 shows various manufacturing conditions, the alloying ratio of the steel sheet produced, the {222} area density of the αFe phase, the {200} area density of the αFe phase, and the Al content. The area density was measured by X-ray diffraction and calculated by the calculation process described above.

The alloying ratio of the steel sheet was obtained as follows. In the L section, the surface distribution of the Fe content and the surface distribution of the metal elements attached in Mo, Cr, Ge, Si, Ti, W, and V by using the EPMA method in the L-direction 0.5 mm x total thickness field of view. Was measured.

In addition, the area | region was calculated | required as the alloying area, and the area | region of content ≥0.1 mass% of the metal element adhered in Mo, Cr, Ge, Si, Ti, W, and V at Fe≥0.5 mass% was made into the alloying area. . The alloying ratio was calculated by dividing the alloying area by the area in the L direction of 0.5 mm × overall thickness.

In addition, by the EBSP method, the crystal grains having a deviation of the {222} plane with respect to the steel plate surface of 0 to 30 ° and the crystal grains having a deviation of the {222} plane with respect to the steel plate surface of 0 to 10 ° were observed for the observation of the L cross section. The area ratio calculated based on the above was described.

Moreover, the burr resistance test was done about the said steel plate. Punching was performed using a punch of 10.00 mmφ and a die of 10.15 mmφ, and the burr height around the punching hole was measured by a point micrometer.

In Nos. 60 to 62, the fifteenth comparative example to the seventeenth comparative example omitted the adhesion of the metal of the second layer. In this case, the {222} area density and the {200} area density were all out of the range of the present invention, and the burr height had a large value of 42 to 63 µm.

The 43rd to 45th Inventive Examples of Nos. 63 to 65 attach Mo metal as a second layer. {222} area density and {200} area density were all within the scope of the present invention, and the burr height was 8 to 9 µm, which was significantly reduced compared to the comparative example.

The 46th to 48th examples of Nos. 66 to 68 are obtained by adhering Cr metal as a second layer. {222} area density and {200} area density were all within the scope of the present invention, and the burr height was 7 to 8 µm, which was significantly reduced compared to the comparative example.

The 49th to 51st invention examples of Nos. 69 to 71 are obtained by adhering Si metal as a second layer. The {222} area density and the {200} area density were all within the scope of the present invention, and the burr height was 7 to 8 µm, which was markedly reduced in comparison with the comparative example.

Nos. 72 to 74 show that the Ge metal is deposited as the second layer. {222} area density and {200} area density were all within the scope of the present invention, and the burr height was 8 to 9 µm, which was significantly reduced compared to the comparative example.

Nos. 75 to 77 show that the T1 metal is deposited as the second layer. The {222} area density and the {200} area density were all within the scope of the present invention, and the burr height was 7 to 8 µm, which was markedly reduced in comparison with the comparative example.

In the 58th to 60th inventions of Nos. 78 to 80, the W metal was deposited as the second layer. The {222} area density and the {200} area density were all within the scope of the present invention, and the burr height was 7 to 9 µm, which was significantly reduced in comparison with the comparative example.

The 60th to 63rd invention examples of Nos. 81 to 83 are obtained by depositing a V metal as a second layer. The {222} area density and the {200} area density were all within the scope of the present invention, and the burr height was 6 to 8 µm, which was significantly reduced in comparison with the comparative example.

When the average r value was measured about the steel plate of the above Example, it was confirmed that the average r value exists in the high level of 2.5 or more in the steel plate of an invention example. In the steel plate of the comparative example, the result was less than 2.5.

Therefore, it was found that the steel sheet of the invention example had excellent drawing workability.

As described above, the steel sheet produced by the production method of the present invention has a {222} area accumulation degree of at least 60% parallel to the steel sheet surface or a {200} area accumulation degree of at most 15% or less parallel to the steel sheet surface. It was found that it was within the scope of the invention, and that excellent burr resistance and drawing workability were compatible.

As described above, since the steel sheet of the present invention has excellent workability, which does not exist in the past, that no burr is generated on the cut surface during punching processing, the steel sheet of the present invention can be easily processed from conventional shapes to various shapes including special shapes. .

Therefore, the steel plate of this invention is useful for various structural materials, functional materials, etc., including outer boards, such as a motor vehicle component and home appliance components which require press molding of a complicated shape, for example.

In addition, the production method of the present invention can easily and effectively reduce the {222} area density and / or the {200} area density even in a steel sheet having an Al content of less than 6.5 mass%.

Therefore, according to the manufacturing method of the present invention, it is possible to easily manufacture the steel sheet (steel sheet of the present invention) having a high {222} surface area degree easily by simply replacing the process of the existing equipment without making a new facility. Do.

Therefore, the present invention is highly applicable in the manufacturing industry using various structural materials and functional materials.

Claims (59)

C content is more than 0 mass% and less than 0.15 mass%, Si content is more than 0 mass% and less than 0.1 mass%, Mn content is more than 0 mass% and less than 1.5 mass%, Al content is 0.001 mass% or more and less than 6.5 mass% Steel plate, (1) the {222} surface area of one or both of the αFe phase and the γFe phase with respect to the steel plate surface, between 60% and 99%, and (2) having a high {222} surface area, characterized in that the {200} area density of one or both of the αFe phase and the γFe phase with respect to the steel plate surface is one or both of 0.01% or more and 15% or less. Grater. C content is more than 0 mass% and less than 0.15 mass%, Si content is more than 0 mass% and less than 0.1 mass%, and Mn content is more than 0 mass% and less than 1.5 mass% which the 2nd layer adheres to at least one side of the surface. It is a steel plate whose Al content is 0.001 mass% or more and less than 6.5 mass%, (1) the {222} surface area of one or both of the αFe phase and the γFe phase with respect to the steel plate surface, between 60% and 99%, and (2) having a high {222} surface area, characterized in that the {200} area density of one or both of the αFe phase and the γFe phase with respect to the steel plate surface is one or both of 0.01% or more and 15% or less. Grater. The C layer is more than 0 mass% and less than 0.15 mass%, the Si content is more than 0 mass% and less than 0.1 mass%, in which the 2nd layer is formed in at least one side of the surface, and the 2nd layer and the steel plate are alloyed in part, Mn content is more than 0 mass% less than 1.5 mass%, Al content is 0.001 mass% or more and less than 6.5 mass%, (1) the {222} surface area of one or both of the αFe phase and the γFe phase with respect to the steel plate surface, between 60% and 99%, and (2) having a high {222} surface area, characterized in that the {200} area density of one or both of the αFe phase and the γFe phase with respect to the steel plate surface is one or both of 0.01% or more and 15% or less. Grater. The C content is more than 0 mass% and less than 0.15 mass%, the Si content is more than 0 mass% and less than 0.1 mass%, and the Mn content is more than 0 mass%, in which the second layer adhered to at least one side of the surface is alloyed with the steel sheet. It is less than 1.5 mass%, It is a steel plate whose Al content is 0.001 mass% or more and less than 6.5 mass%, (1) the {222} surface area of one or both of the αFe phase and the γFe phase with respect to the steel plate surface, between 60% and 99%, and (2) having a high {222} surface area, characterized in that the {200} area density of one or both of the αFe phase and the γFe phase with respect to the steel plate surface is one or both of 0.01% or more and 15% or less. Grater. The steel plate according to any one of claims 1 to 4, wherein the {222} area density is 60% or more and 95% or less. The method according to any one of claims 2 to 4, wherein the second layer is made of Fe, Al, Co, Cu, Cr, Ga, Hf, Hg, In, Mn, Mo, Nb, Ni, Pb, Pd, Pt. , Sb, Si, Sn, Ta, Ti, V, W, Zn, and Zr containing at least one element, characterized in that the steel sheet having a high {222} surface area. The steel sheet according to any one of claims 1 to 4, wherein the steel sheet has a thickness of 5 µm or more and 5 mm or less. The steel sheet according to any one of claims 2 to 4, wherein the thickness of the second layer is 0.01 µm or more and 500 µm or less. delete (a) As a base material, C content is more than 0 mass% and less than 0.15 mass%, Si content is more than 0 mass% and less than 0.1 mass%, Mn content is more than 0 mass% and less than 1.5 mass%, Al content is 0.001 mass% Process of adhering a 2nd layer to at least one side of the steel plate which is more than 3.5 mass%, (b) cold rolling the steel sheet with a second layer, and (c) a step of heat-treating the steel sheet after cold rolling to recrystallize the steel sheet, (d) A method for producing a steel sheet having a high {222} area density, wherein the Al content of the steel sheet after recrystallization is 0.001% by mass or more and less than 6.5% by mass. (a) As a base material, C content is more than 0 mass% and less than 0.15 mass%, Si content is more than 0 mass% and less than 0.1 mass%, Mn content is more than 0 mass% and less than 1.5 mass%, Al content is 0.001 mass% Attaching the second layer to at least one side of the steel sheet that is less than or equal to 3.5% by mass, (b) cold rolling the steel sheet with a second layer, and (c) heat treating the steel sheet after cold rolling to alloy a part of the second layer and recrystallize the steel sheet; (d) The Al content of the steel plate after alloying and recrystallization is 0.001 mass% or more and less than 6.5 mass%, The manufacturing method of the steel plate which has high {222} surface area degree. (a) As a base material, C content is more than 0 mass% and less than 0.15 mass%, Si content is more than 0 mass% and less than 0.1 mass%, Mn content is more than 0 mass% and less than 1.5 mass%, Al content is 0.001 mass% Attaching the second layer to at least one side of the steel sheet that is less than or equal to 3.5% by mass, (b) cold rolling the steel sheet with a second layer, and (c) heat-treating the steel sheet after cold rolling to alloy the second layer and recrystallize the steel sheet; (d) A method for producing a steel sheet having a high {222} surface area degree, wherein the Al content of the steel sheet is 0.001% by mass or more and less than 6.5% by mass. The method according to any one of claims 10 to 12, (1) the {222} surface area of one or both of the αFe phase and the γFe phase with respect to the steel plate surface, between 60% and 99%, and (2) The high {222} plane, characterized in that the {200} surface integration degree of one or both of the αFe phase and the γFe phase with respect to the steel plate surface is controlled to be one or both of 0.01% or more and 15% or less. Manufacturing method of steel sheet having a degree of integration The method according to any one of claims 10 to 12, (1) the {222} surface area of one or both of the αFe phase and the γFe phase with respect to the steel plate surface, between 60% and 95%, and (2) The high {222} plane, characterized in that the {200} surface integration degree of one or both of the αFe phase and the γFe phase with respect to the steel plate surface is controlled to be one or both of 0.01% or more and 15% or less. Manufacturing method of steel sheet having a degree of integration The method according to any one of claims 10 to 12, wherein the second layer is made of Fe, Al, Co, Cu, Cr, Ga, Hf, Hg, In, Mn, Mo, Nb, Ni, Pb, Pd, Pt, A method for producing a steel sheet having a high {222} surface area, characterized by containing at least one element of Sb, Si, Sn, Ta, Ti, V, W, Zn, and Zr. delete delete delete delete The thickness of the steel plate as said base material is 10 micrometers or more and 10 mm or less, The manufacturing method of the steel plate which has a high {222} surface integration degree in any one of Claims 10-12. The thickness of the said 2nd layer is 0.05 micrometer or more and 1000 micrometers or less, The manufacturing method of the steel plate which has high {222} surface-density degree in any one of Claims 10-12. The method for producing a steel sheet having a high {222} surface integration degree according to any one of claims 10 to 12, wherein preheating is performed on the steel sheet before the second layer is attached. 23. The method of manufacturing a steel sheet having a high {222} area density according to claim 22, wherein the temperature of the preliminary heat treatment is 700 to 1100 ° C. 23. The method of manufacturing a steel sheet having a high {222} surface area density according to claim 22, wherein the atmosphere of the preliminary heat treatment is at least one of an inert gas atmosphere and a hydrogen atmosphere in a vacuum. The method for producing a steel sheet according to any one of claims 10 to 12, wherein the step of attaching the second layer to the steel sheet is by a plating method. The process for attaching the second layer to the steel sheet is by a rolling cladding method, according to any one of claims 10 to 12, wherein the method for producing a steel sheet having a high {222} surface area degree. The manufacturing method of the steel plate of any one of Claims 10-12 which is 30%-95% of the rolling reduction in the said cold rolling process. . The high {222} of any one of Claims 10-12 whose heat processing temperature in the process of performing the said heat processing is 600 degreeC or more and 1000 degrees C or less, and heat processing time is 30 second or more. Method for producing a steel sheet having a surface area degree. The heat processing temperature in the process of performing the said heat processing is more than 1000 degreeC, The manufacturing method of the steel plate which has a high {222} area-density degree in any one of Claims 10-12. The thickness of the steel plate as said base material is 10 micrometers or more and 10 mm or less, The manufacturing method of the steel plate which has a high {222} surface area degree. The method for manufacturing a steel sheet having a high {222} area density according to claim 13, wherein the thickness of the second layer is 0.05 µm or more and 1000 µm or less. The method for producing a steel sheet with a high {222} area density according to claim 13, wherein a preheating treatment is performed on the steel sheet before the second layer is attached. 33. The method according to claim 32, wherein the temperature of the preheat treatment is 700 to 1100 ° C. 33. The method according to claim 32, wherein the atmosphere of the preheat treatment is at least one of an inert gas atmosphere and a hydrogen atmosphere in vacuum. The method for producing a steel sheet having a high {222} area density according to claim 13, wherein the step of attaching the second layer to the steel sheet is by a plating method. The method for producing a steel sheet with a high {222} area density according to claim 13, wherein the step of attaching the second layer to the steel sheet is by a rolling cladding method. The manufacturing method of the steel plate which has a high {222} surface-density degree of Claim 13 which is 30%-95% of the reduction ratio in the said cold rolling process. The method for producing a steel sheet having a high {222} surface integration degree according to claim 13, wherein the heat treatment temperature in the step of performing the heat treatment is 600 ° C or more and 1000 ° C or less, and the heat treatment time is 30 seconds or more. . The method for producing a steel sheet having a high {222} surface area degree according to claim 13, wherein the heat treatment temperature in the step of performing the heat treatment is more than 1000 ° C. The steel sheet as a base material is 10 micrometers or more and 10 mm or less, The manufacturing method of the steel plate which has high {222} area-density degree of Claim 14 characterized by the above-mentioned. 15. The method for manufacturing a steel sheet having a high {222} area density according to claim 14, wherein the second layer has a thickness of 0.05 µm or more and 1000 µm or less. 15. The method of manufacturing a steel sheet with a high {222} area density according to claim 14, wherein preheating is performed on the steel sheet before the second layer is attached. 43. The method according to claim 42, wherein the temperature of the preliminary heat treatment is 700 to 1100 ° C. 43. The method according to claim 42, wherein the atmosphere of the preliminary heat treatment is at least one of an inert gas atmosphere and a hydrogen atmosphere in a vacuum. The method for producing a steel sheet having a high {222} area density according to claim 14, wherein the step of attaching the second layer to the steel sheet is by a plating method. The method for producing a steel sheet having a high {222} area density according to claim 14, wherein the step of attaching the second layer to the steel sheet is by a rolling cladding method. The manufacturing method of the steel plate which has a high {222} surface-density degree of Claim 14 which is 30%-95% of the rolling reduction in the said cold rolling process. 15. The method for producing a steel sheet having a high {222} surface integration degree according to claim 14, wherein the heat treatment temperature in the step of performing the heat treatment is 600 ° C or more and 1000 ° C or less and the heat treatment time is 30 seconds or more. . The method for producing a steel sheet having a high {222} surface area degree according to claim 14, wherein the heat treatment temperature in the step of performing the heat treatment is more than 1000 ° C. The thickness of the steel plate as said base material is 10 micrometers or more and 10 mm or less, The manufacturing method of the steel plate which has high {222} area-density degree of Claim 15. The method for producing a steel sheet having a high {222} surface integration degree according to claim 15, wherein the thickness of the second layer is 0.05 µm or more and 1000 µm or less. The method of manufacturing a steel sheet having a high {222} surface area degree according to claim 15, wherein a preheat treatment is performed on the steel sheet before the second layer is attached. 53. The method of claim 52, wherein the temperature of the preliminary heat treatment is 700 to 1100 ° C. 53. The method of claim 52, wherein the atmosphere of the preheat treatment is at least one of an inert gas atmosphere and a hydrogen atmosphere in a vacuum. The method for producing a steel sheet having a high {222} area density according to claim 15, wherein the step of attaching the second layer to the steel sheet is by a plating method. The method for producing a steel sheet having a high {222} area density according to claim 15, wherein the step of attaching the second layer to the steel sheet is by a rolling cladding method. The manufacturing method of the steel plate which has a high {222} surface-density degree of Claim 15 which is 30%-95% of the rolling reduction in the said cold rolling process. The method for producing a steel sheet having a high {222} surface integration degree according to claim 15, wherein the heat treatment temperature in the step of performing the heat treatment is 600 ° C or more and 1000 ° C or less, and the heat treatment time is 30 seconds or more. . The method for producing a steel sheet having a high {222} surface area degree according to claim 15, wherein the heat treatment temperature in the step of performing the heat treatment is more than 1000 ° C.