Classifications

• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
  • C21D8/0226—Hot rolling
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
  • C21D8/0236—Cold rolling
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
  • C21D8/0273—Final recrystallisation annealing
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
  • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
  • C21D8/0426—Hot rolling
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
  • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
  • C21D8/0436—Cold rolling
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
  • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
  • C21D8/0473—Final recrystallisation annealing
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
  • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
• • C—CHEMISTRY; METALLURGY
  • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
  • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
  • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
  • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
  • C23C2/12—Aluminium or alloys based thereon
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D2201/00—Treatment for obtaining particular effects
  • C21D2201/05—Grain orientation
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D2211/00—Microstructure comprising significant phases
  • C21D2211/001—Austenite
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D2211/00—Microstructure comprising significant phases
  • C21D2211/005—Ferrite
• • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
  • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
  • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
  • Y10T428/00—Stock material or miscellaneous articles
  • Y10T428/12—All metal or with adjacent metals
  • Y10T428/12451—Macroscopically anomalous interface between layers

Definitions

• the present invention relates to steel sheet excellent in deep drawability, press formability, punchability, and other workability and a method of production of that steel sheet.
• the workability of steel sheet depends on the texture of the ⁇ Fe phase or the ⁇ Fe phase.
• the texture of the ⁇ Fe phase or the ⁇ Fe phase depends on the texture of the ⁇ Fe phase or the ⁇ Fe phase.
• Japanese Patent Publication (A) No. 6-2069 discloses high strength cold rolled steel sheet and hot dip galvanized steel sheet wherein the amounts of Si, Mn, and P are controlled based on a fixed relationship with the X-ray diffraction intensities of the ⁇ 222 ⁇ planes and ⁇ 200 ⁇ planes parallel to the steel sheet surface so as to secure deep drawability.
• Japanese Patent Publication (A) No. 8-13081 discloses an enameling use high strength cold rolled steel sheet and a method of production of the same wherein the amount of Nb is defined by the amount of C and, furthermore, the hot rolling and cold rolling conditions are defined so as to control the (111) texture Japanese Patent Publication (A) No.
• 10-18011 discloses a hot dip galvannealed steel sheet and method of production of the same wherein, when, among the X-ray diffraction intensities, the ratio of the ⁇ 200 ⁇ plane intensity and the ⁇ 222 ⁇ plane intensity, that is, I(200)/I(222), becomes less than 0.17, there are no longer streak like defects at the plating surface and wherein when the final rolling temperature of the hot rolling is made A r3 +30°C or more, the X-ray diffraction intensity ratio I(200)/I(222) becomes less than 0.17.
• Japanese Patent Publication (A) No. 11-350072 discloses very low carbon cold rolled steel sheet with a content of C in the steel of 0.01% or less which, when the particle size of the ferrite at the surface layer part accounting for 1/10 of the total thickness from the surface of the steel sheet is a and the particle size of the ferrite at the inner layer part accounting for 1/2 of the total thickness centered at the center of thickness is b, satisfies a-b ⁇ 0.5, a ⁇ 7.0, and b ⁇ 7.5 and which, if controlling the ratio I(222)/I(200) of X-ray diffraction intensities from the ⁇ 222 ⁇ plane and the ⁇ 200 ⁇ plane to be 5.0 or more at the part of 1/15 the total sheet thickness from the surface of the steel sheet and to be 12 or more at the center part of sheet thickness of the steel sheet, it is possible to reduce the orange skin peel state of the steel sheet at the time of press formation.
• Japanese Patent Publication (A) No. 2006-144116 discloses high Al content steel sheet having an Al content of 6.5 mass% to 10 mass% wherein the ⁇ 222 ⁇ plane integration of the ⁇ Fe crystals is made 60% to 95% or the ⁇ 200 ⁇ plane integration is made 0.01% to 15% so as to improve the workability.
• the above publication discloses a method of raising the plane integration of specific planes in high Al content steel sheet comprising treating the surface of matrix steel sheet having an Al content of 3.5 mass% to less than 6.5 mass% by hot dip Al coating to deposit Al alloy, cold rolling, then performing diffusion heat treatment.
• Japanese Patent Publication (A) No. 3-277739 discloses steel sheet hardened at its surface so as to make the burrs formed at the time of shearing extremely small and give a soft hardness distribution inside the steel sheet so as to prevent reduction of the press formability. Specifically, steel sheet having an r value (Rankford value) of 1.7 to 2 and having a burr height at the time of punching of 12 to 40 ⁇ m is disclosed.
• Japanese Patent Publication (A) No. 8-188850 discloses cold rolled steel sheet comprised of very low carbon steel to which S is added in an amount of 0.003 to 0.03% so as to satisfy a fixed formula and raised in deep drawability and punchability. Specifically, steel sheet having an r value of 2.2 to 2.6 and a burr height at the time of punching of 30 to 80 ⁇ m is disclosed.
• the above steel sheet had the problem of formation of burrs at the cross-section at the time of punching and the need for a chamfering process to remove the formed burrs.
• the above steel sheet had the problem of insufficient slip of the steel sheet with the die surface at the time of press formation by a complicated die and therefore the inability to form shapes more complicated than in the past.
• the steel sheet disclosed in Japanese Patent Publication (A) No. 2006-144116 has a ⁇ 222 ⁇ plane integration for raising the workability higher than the past and has workability enough for forming foil for forming a honeycomb structure, but has a large Al content, so cannot be used as usual processing use steel sheet for sophisticated working or for higher efficiency of the working process.
• Japanese Patent Publication (A) No. 6-2069 Japanese Patent Publication (A) No. 8-13081 , Japanese Patent Publication (A) No. 10-18011 , and Japanese Patent Publication (A) No. 11-350072 enable integration of the ⁇ 222 ⁇ planes up to a certain ratio, but there are limits to the improvement of the plane integration with just setting the ingredient conditions and conditions in the annealing and other conventional processes.
• the conventional process is augmented by a step of deposition of an Al alloy on the matrix surface by hot dip Al coating so as to raise the ⁇ 222 ⁇ plane integration.
• the above method is a method improving the ⁇ 222 ⁇ plane integration only when using a matrix having an Al content of 3.5 mass% to less than 6.5 mass%. If just applying this method to steel sheet with a low Al content, it is difficult to raise or lower the integration of specific planes.
• Japanese Patent Publication (A) No. 3-277739 and Japanese Patent Publication (A) No. 8-188850 succeed in reducing the formation of burrs accompanying punching to a certain extent, but have not reached the point of enabling elimination of the chamfering step for removing the burrs.
• the present invention has as its object the provision of "less than 6.5 mass% Al content steel sheet" excellent in workability having an unprecedentedly high level of ⁇ 222 ⁇ plane integration and free from formation of burrs at the cross-section at the time of punching.
• the present invention has as its object the provision of a method of production for producing a "less than 6.5 mass% Al content steel sheet" having an unprecedentedly high ⁇ 222 ⁇ plane integration.
• the inventors discovered that in steel sheet with an Al content of less than 6.5 mass%, if (x1) making the ⁇ 222 ⁇ plane integration of the Fe crystals a high specific range and/or (x2) making the ⁇ 200 ⁇ plane integration of the Fe crystals a low specific range, no burrs form at the cross-section at the time of punching and unprecedentedly excellent workability is obtained.
• the steel having a high ⁇ 222 ⁇ plane integration of the present invention (the present invention steel sheet) sheet is an unprecedented steel sheet excellent in workability which has an Al content of less than 6.5 mass% and a high ⁇ 222 ⁇ plane integration and has a low ⁇ 200 ⁇ plane integration, so not being formed with burrs at the cross-section at the time of punching.
• the present invention steel sheet can easily be worked to various shapes including conventional shapes to special shapes and for example are useful for outer panels for auto parts, home electrical appliance parts, etc. requiring complicatedly shaped press formation and other various structural materials, functional materials, etc.
• the method of production of the present invention in steel sheet having an Al content of less than 6.5 mass%, it is possible to increase the ⁇ 222 ⁇ plane integration or to lower the ⁇ 200 ⁇ plane integration easily and effectively. Further, the method of production of the present invention enables the production of the present invention steel sheet having a high ⁇ 222 ⁇ plane integration without production of new facilities by just switching processes of existing facilities easily and at low cost.
• the inventors discovered that by making the Al content of the steel sheet less than 6.5 mass% and (x1) raising the ⁇ 222 ⁇ plane integration of the Fe crystal phase to 60% to 99% and/or (x2) lowering the ⁇ 200 ⁇ plane integration to 0.01% to 15%, it is possible to provide unprecedented steel sheet excellent in workability free from the occurrence of burrs at the cross-section at the time of punching.
• the inventors disclosed "high Al content steel sheet having an Al content of 6.5 mass% to 10 mass%" having a ⁇ 222 ⁇ plane integration of an ⁇ Fe phase of 60% to 95% and/or a ⁇ 200 ⁇ plane integration of an ⁇ Fe phase of 0.01% to 15% in Japanese Patent Publication (A) No. 2006-144116 .
• the above method of production of steel sheet is characterized by depositing an Al alloy on at least one surface of steel sheet containing Al in 3.5 mass% to 6.5 mass%, applying working strain by cold working, then applying heat treatment for making the Al diffuse.
• the inventors after this, tackled the development of technology for further raising the ⁇ 222 ⁇ plane integration in steel sheet having an Al content of less than 6.5 mass% and ran various experiments.
• the inventors found that by using a matrix steel sheet having an Al content of less than 3.5 mass%, making the content of Cr of the matrix steel sheet 12 mass% or less, depositing a second layer comprised of not only Al, but also another metal on the steel sheet, then heat treating this to make the steel sheet recrystallize, it is possible to raise the ⁇ 222 ⁇ plane integration.
• the ingredients of the steel sheet are ingredients where the Al content after recrystallization becomes less than 6.5 mass%, the frequency of occurrence of the above recrystallization nuclei tends to become higher and as a result steel sheet having a higher ⁇ 222 ⁇ plane integration can be obtained.
• the content of Cr in the matrix steel sheet is preferably less than 10 mass%. With such a Cr content, it is possible to more easily raise the ⁇ 222 ⁇ plane integration.
• This phenomenon is basically also considered to arise based on the mechanism of formation of recrystallization nuclei.
• the present invention steel sheet at ordinary temperature, is comprised or one or both of an ⁇ Fe phase and ⁇ Fe phase.
• the Al content is less than 6.5 mass%.
• the Al content of the present invention steel sheet is preferably 0.001 mass% or more. If the Al is 0.001 mass% or more, the yield at the time of production will rise. More preferably, it is 0.11 mass% or more. If Al becomes 0.11 mass% or more, the ⁇ 222 ⁇ plane integration becomes higher and as a result a higher workability can be obtained.
• the inventors discovered that by depositing a second layer on at least one side of a matrix steel sheet having an Al content of less than 3.5 mass% and then heat treating this to make the steel sheet recrystallize, it is possible to raise the ⁇ 222 ⁇ plane integration of one or both of an ⁇ Fe phase and ⁇ Fe phase with respect to the steel sheet surface very high.
• the steel sheet having a high ⁇ 222 ⁇ plane integration of the present invention (the present invention steel sheet) is excellent in deep drawability, punchability, and other workability.
• the Al content of the matrix steel sheet is less than 3.5 mass%, even if the second layer contains Al, in the production process, the steel sheet is resistant to shrinkage and other deformation.
• the Al content of the matrix steel sheet is preferably 0.001 mass% or more. If the Al is 0.001 mass% or more, the production yield of the matrix steel sheet is improved.
• the present invention steel sheet is comprised of one or both of an ⁇ Fe phase and ⁇ Fe phase.
• the ⁇ Fe phase is an Fe crystal phase of a structure of a body centered orientation, while the ⁇ Fe phase is an Fe crystal phase of a structure of a face centered orientation.
• the Fe crystal phase includes phases where other atoms replace part of the Fe or enter between the Fe atoms.
• the present invention steel sheet has an Al content of less than 6.5 mass% and is characterized in that a ⁇ 222 ⁇ plane integration of one or both of the ⁇ Fe phase and ⁇ Fe phase is 60% to 99% and a ⁇ 200 ⁇ plane integration of one or both of the ⁇ Fe phase and ⁇ Fe phase is 0.01% to 15%.
• the value for evaluation of the drawability that is, the average r value (Rankford value) becomes 2.5 or more. Furthermore, at the time of punching, excellent workability free of formation of burrs at the cross-section can be obtained.
• the plane integration was measured by X-ray diffraction using MoK ⁇ rays.
• the ⁇ 222 ⁇ plane integration of the ⁇ Fe phase and the ⁇ 200 ⁇ plane integration of the ⁇ Fe phase were found as follows.
• the integrated intensities of the 11 ⁇ crystal planes of Fe parallel to a sample surface that is, ⁇ 110 ⁇ , ⁇ 200 ⁇ , ⁇ 211 ⁇ , ⁇ 310 ⁇ , ⁇ 222 ⁇ , ⁇ 321 ⁇ , ⁇ 411 ⁇ , ⁇ 420 ⁇ , ⁇ 332 ⁇ , ⁇ 521 ⁇ , and ⁇ 442 ⁇ , were measured.
• the measurement values were respectively divided by the theoretical integrated intensities of a sample of random orientation, then the ratios with the ⁇ 200 ⁇ intensity or ⁇ 222 ⁇ intensity were found by percentages.
• the ratio with the ⁇ 222 ⁇ intensity is expressed by the following formula (1).
• 222 ⁇ p ⁇ l ⁇ a ⁇ n ⁇ e int ⁇ e ⁇ g ⁇ r ⁇ a ⁇ t ⁇ i ⁇ o ⁇ n i 222 / I 222 ⁇ ⁇ i h ⁇ k ⁇ l / I h ⁇ k ⁇ l ⁇ 100 where the symbols are as follows:
• the ratio with the ⁇ 222 ⁇ intensity is expressed by the following formula (2).
• 222 ⁇ p ⁇ l ⁇ a ⁇ n ⁇ e int ⁇ e ⁇ g ⁇ r ⁇ a ⁇ t ⁇ i ⁇ o ⁇ n i 111 / I 111 ⁇ ⁇ i h ⁇ k ⁇ l / I h ⁇ k ⁇ l ⁇ 100 where the symbols are as follows:
• the EBSP Electro Backscattering Diffraction Pattern
• the area rate of the ⁇ 222 ⁇ planes with respect to the total area of the crystal planes measured by the EPSP method becomes the ⁇ 222 ⁇ integration. Therefore, even by the EBSP method, in the present invention steel sheet, the ⁇ 222 ⁇ plane integration becomes 60% to 99%.
• the present invention it is not necessary that the values obtained by all analysis methods satisfy the range prescribed by the present invention.
• the effect of the present invention is obtained if the value obtained by one analysis method satisfies the range of the present invention.
• the ⁇ 222 ⁇ plane deviates from the steel sheet surface. This deviation is preferably within 30°.
• the deviation of the ⁇ 222 ⁇ plane is observed by the L cross-section.
• the area ratio of the crystal grains with deviation of the ⁇ 222 ⁇ plane of 30° or less is preferably 80 to 99.9%.
• the area ratio of the crystal grains with deviation of the ⁇ 222 ⁇ plane in the L cross-section of 0 to 10° is more preferably 40 to 98%.
• r0, r45, and r90 are the plastic strain ratios measured when taking test samples in directions of 0°, 45°, and 90° with respect to the rolling direction of the sheet surface.
• the integrated intensity of the sample having a random orientation may also be found by measurement using a sample prepared in advance.
• steel sheet (i) a ⁇ 222 ⁇ plane integration of one or both of an ⁇ Fe phase and ⁇ Fe phase with respect to the steel sheet surface is 60% to 99% and/or (ii) a ⁇ 200 ⁇ plane integration of one or both of an ⁇ Fe phase and ⁇ Fe phase with respect to the steel sheet surface is 0.01% to 15%.
• ⁇ 222 ⁇ plane integration is less than 60% and the ⁇ 200 ⁇ plane integration is over 15%, cracks and breakage easily occur at the time of drawing, bending, and rolling. Further, burrs occur at the cross-section at the time of punching.
• the ⁇ 222 ⁇ plane integration of one or both of an ⁇ Fe phase and ⁇ Fe phase with respect to the steel sheet surface is preferably 60% to 95%. If the ⁇ 222 ⁇ plane integration is in the above range, production becomes easier and the yield is improved.
• the ⁇ 200 ⁇ plane integration of one or both of an ⁇ Fe phase and ⁇ Fe phase with respect to the steel sheet surface is preferably 0.01% to 10%. If the ⁇ 200 ⁇ plane integration is in the above range, burrs will not occur at the cross-section at the time of punching.
• One method for producing the present invention steel sheet is comprised of a step of depositing a second layer on at least one surface of a matrix steel sheet having an Al content of less than 6.5%, a step of cold rolling the steel sheet on which the second layer is deposited, a step of removing the second layer from the cold rolled steel sheet, and a step of heat treating the steel sheet from which the second layer has been removed to make the steel sheet recrystallize.
• the second layer is not deposited on at least one surface of the matrix steel sheet, a high ⁇ 222 ⁇ plane integration cannot be obtained. If making the second layer deposit on both surfaces of the steel sheet and then cold rolling, the effect of the present invention can be improved more.
• the second layer does not necessarily have to be deposited.
• the second layer deposited on the steel sheet may therefore be removed before heat treatment.
• a steel sheet on at least one surface of which a second layer is deposited and having one or both of a ⁇ 222 ⁇ plane integration of one or both of an ⁇ Fe phase and ⁇ Fe phase with respect to the steel sheet surface of 60% to 99% and a ⁇ 200 ⁇ plane integration of one or both of an ⁇ Fe phase and ⁇ Fe phase with respect to the steel sheet surface of 0.01% to 15% is included in the present invention steel sheet.
• ⁇ 222 ⁇ plane integration is less than 60% and the ⁇ 200 ⁇ plane integration is over 15%, cracks and breakage will easily occur at the time of drawing, bending, and rolling and, further, burrs will form at the cross-section at the time of punching.
• the second layer is deposited on the steel sheet, it is possible to prevent internal oxidation, corrosion, etc. of the steel sheet and possible to make the steel sheet more sophisticated in functions.
• the method of production of this steel sheet includes a step of depositing the second layer on at least one surface of a matrix steel sheet having an Al content of less than 3.5 mass%, a step of cold rolling the sheet in the state with the second layer deposited, and a step of heat treating the steel sheet to make the steel sheet recrystallize.
• the effects of the present invention can be obtained. If the second layer is deposited on both surfaces of the matrix steel sheet, the effect of the present invention is further improved.
• Steel sheet wherein the second layer and the steel sheet are partially alloyed and having one or both of a ⁇ 222 ⁇ plane integration of one or both of an ⁇ Fe phase and ⁇ Fe phase with respect to the steel sheet surface of 60% to 99% and a ⁇ 200 ⁇ plane integration of one or both of an ⁇ Fe phase and ⁇ Fe phase with respect to the steel sheet surface of 0.01% to 15% is also included in the present invention steel sheet.
• ⁇ 222 ⁇ plane integration is less than 60% and the ⁇ 200 ⁇ plane integration is over 15%, cracks and breakage will easily occur at the time of drawing, bending, and rolling and, further, burrs will form at the cross-section at the time of punching.
• the second layer is deposited on the steel sheet surface and part of the second layer is alloyed with the steel sheet, internal oxidation, corrosion, etc. of the steel sheet can be prevented, peeling of the second layer can be prevented, and the steel sheet can be made more sophisticated in function.
• the matrix steel sheet in a state with the second layer deposited on at least one surface. If the second layer is deposited on both surfaces of the matrix steel sheet, the effect of the present invention is further improved.
• the steel sheet has to be heat treated to make it recrystallize.
• the second layer deposited on one or both surfaces is alloyed with the matrix steel sheet, a higher ⁇ 222 ⁇ plane integration can be obtained.
• the second layer and the steel sheet partially alloying means, for example, the second layer and the steel sheet partially alloying near their boundary by interdiffusion.
• Steel sheet where the second layer and steel sheet are alloyed and having one or both of a ⁇ 222 ⁇ plane integration of one or both of an ⁇ Fe phase and ⁇ Fe phase with respect to the steel sheet surface of 60% to 99% and a ⁇ 200 ⁇ plane integration of one or both of an ⁇ Fe phase and ⁇ Fe phase with respect to the steel sheet surface of 0.01% to 15% is also included in the present invention steel sheet.
• ⁇ 222 ⁇ plane integration is less than 60 and the ⁇ 200 ⁇ plane integration is over 15%, cracks and breakage will easily occur at the time of drawing, bending, and rolling and, further, burrs will form at the cross-section at the time of punching.
• the mechanical properties or functionality of the steel sheet will be improved in accordance with the elements making up the second layer.
• the element forming the second layer is Al
• the high temperature oxidation resistance and corrosion resistance of the steel sheet will be improved.
• the second layer has to be deposited on at least one surface of the matrix steel sheet, preferably both surfaces. After this, after the heat treatment step, the second layer completely alloys with the steel sheet whereby a higher ⁇ 222 ⁇ plane integration can be obtained.
• the second layer is preferably a metal.
• the preferable elements forming the second layer are at least one element among 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.
• the above elements have the common feature of being alloying elements with Fe.
• the elements are at least one element among Al, Cr, Ga, Mo, Nb, P, Sb, Si, Sn, Ti, V, W, and Zn which become solid solute in ⁇ Fe and tend to stabilize the ⁇ phase.
• the elements are at least one element among Al, Cr, Mo, Si, Sn, Ti, V, W, and Zn which become solid solute in ⁇ Fe and tend to stabilize the ⁇ phase more.
• the second layer it is possible to select an Al alloy, Zn alloy, Sn alloy, etc.
• the second layer applied to the surface of the matrix steel sheet is, in the same way as the above, preferably a metal.
• the preferable elements forming the second layer are at least one element among 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.
• the above elements have the common feature of being alloying elements with Fe.
• the elements are at least one element among Al, Cr, Ga, Mo, Nb, P, Sb, Si, Sn, Ti, V, W, and Zn which become solid solute in ⁇ Fe and tend to stabilize the ⁇ phase.
• the elements are at least one element among Al, Cr, Mo, Si, Sn, Ti, V, W, and Zn which become solid solute in ⁇ Fe and tend to stabilize the ⁇ phase more.
• the second layer it is possible to select an Al alloy, Zn alloy, Sn alloy, etc.
• the preferable Al content of the matrix steel sheet is less than 3.5 mass%. If the Al concentration of the matrix steel sheet is 3.5 mass% or more, if heat treating the sheet with the Al alloy deposited as the second layer, shrinkage will occur during the heat treatment and the dimensional precision will remarkably drop.
• the Al content of the matrix steel sheet is made less than 3.5 mass%.
• the Al content of the matrix steel sheet is made less than 6.5 mass%.
• the production process includes a step of depositing on at least one surface a second layer of at least one element among Fe, Co, Cu, Cr, Ga, Hf, Hg, In, Mn, Mo, Nb, Ni, Pb, Pd, Pt, Sb, Si, Sn, Ta, Ti, V, W, Zn, and Zr, if the Al content of the matrix steel sheet is 6.5 mass% or more, the tensile elongation at break of the obtained steel sheet falls and even if having a high ⁇ 222 ⁇ plane integration, sufficient workability will no longer be obtained and burrs will form at the cross-section at the time of punching.
• the Al content of the steel sheet when the second layer does not contain Al is made less than 6.5 mass%.
• the Al content of the matrix steel sheet is preferably less than 6.5 mass%.
• the method of omitting the step of removing the second layer so as to raise the work efficiency is also included in the present invention.
• the method of heat treating the sheet to alloy part or all of the second layer and produce steel sheet having a high ⁇ 222 ⁇ plane integration is also included in the present invention.
• the alloyed region of the steel sheet and second layer is defined as follows.
• the region where the Fe content is 0.5 mass% higher than the Fe content of the second layer before alloying and the content of A is 0.1 mass% higher than the content of A of the matrix steel sheet before alloying is defined as an "alloyed region”.
• the ratio of alloying is the ratio of the alloyed region in the overall region.
• steel sheet by forming the alloyed region in accordance with the above definition, a more superior workability can be obtained.
• the alloying ratio for example can be found by using EPMA etc., analyzing the distribution of contents of the Fe and element A at the L cross-section, identifying the alloyed region, finding that area, and finding the ratio of the area of the identified region to the overall area.
• the thickness of the steel sheet of the present invention is preferably 5 ⁇ m to 5 mm. This is the thickness including the second layer. If the thickness of the steel sheet is less than 5 ⁇ m, the production yield falls so this is not suitable for practical application.
• the thickness of the steel sheet is preferably 5 ⁇ m to 5 mm.
• the thickness of the steel sheet is more preferably 100 ⁇ m to 3 mm. If the thickness of the steel sheet is 3 mm or less, the effect of suppression of the formation of burrs at the cross-section at the time of punching becomes more remarkable.
• the thickness of the steel sheet is 100 ⁇ m or more, the ⁇ 222 ⁇ plane integration becomes higher and more easily controlled. Similarly, the effect of suppression of formation of burrs becomes more remarkable.
• the thickness of the second layer is preferably 0.01 ⁇ m to 500 ⁇ m.
• the thickness of the alloyed part is included in the thickness of the second layer.
• the second layer is deposited at both surfaces, this is the thicknesses of the two surfaces in total.
• the second layer has the function of improving the ⁇ 222 ⁇ plane integration at the time of production and can be left after production and used as a rust-preventive and protective coating of the steel sheet.
• the thickness of the second layer is over 500 ⁇ m, the possibility of peeling rises, so 500 ⁇ m or less is preferable. If the thickness of the second layer is less than 0.01 ⁇ m, the coating will easily tear and the rust-preventive and protective effect will be reduced.
• the thickness of the second layer is preferably 0.01 ⁇ m or more.
• the case where the entire thickness of the steel sheet is alloyed is also preferable. In this case, the second layer may be considered to have disappeared.
• the thickness of the matrix steel sheet is 10 ⁇ m to 10 mm. If the thickness of the matrix steel sheet is less than 10 ⁇ m, the production yield will drop in the steps from cold rolling on so this is not suitable for practical application in some cases.
• the ⁇ 222 ⁇ plane integration may not fall in the range of the present invention.
• the thickness of the matrix steel sheet is preferably 10 ⁇ m to 10 mm.
• a thickness of the matrix steel sheet of over 130 ⁇ m to 7 mm is more preferable. In this range of thickness, an efficient and sufficient increase in the ⁇ 222 ⁇ plane integration can be expected and production of steel sheet able to suppress the formation of burrs at the time of punching becomes easy.
• the thickness of the second layer deposited on the matrix steel sheet before cold rolling is preferably 0.05 ⁇ m to 1000 ⁇ m.
• the thickness of the alloyed part is included in the thickness of the second layer.
• the second layer is deposited at both surfaces, this becomes the thicknesses of the two surfaces in total.
• the thickness of the second layer is less than 0.05 ⁇ m, the ⁇ 222 ⁇ plane integration becomes lower and may not fall in the range of the present invention, so 0.05 ⁇ m or more is preferable.
• the ⁇ 222 ⁇ plane integration becomes lower and may not fall in the range of the present invention, so 1000 ⁇ m or less is preferable.
• the matrix steel sheet before deposition of the second layer is preferably given preheat treatment.
• This preheat treatment causes rearrangement of the dislocations accumulated in the process of production of the matrix steel sheet. Therefore, causing recrystallization is preferable, but there is not necessarily a need to cause recrystallization.
• the preheat treatment temperature is preferably 700°C to 1100°C. If the preheat treatment temperature is less than 700°C, changes in the dislocation structure for obtaining more superior effects of the present invention are hard to occur, so the preheat treatment temperature is made 700°C or more.
• the steel sheet surface is formed with an unpreferable oxide film. This has a detrimental effect on the later deposition of the second layer and the cold rolling, so the preheat treatment temperature is made 1100°C or less.
• the atmosphere of the preheat treatment may be a vacuum, inert gas atmosphere, hydrogen atmosphere, or weak acidic atmosphere.
• the effect of the present invention can be obtained, but an atmosphere is sought of conditions not forming on the steel sheet surface an oxide film having a detrimental effect on the deposition of the second layer after the preheat treatment or on the cold rolling.
• the preheat treatment time does not particularly have to be limited, but if considering the production of the steel sheet etc., several seconds to several hours are suitable.
• the second layer may be deposited on the steel sheet by the hot dip method, electroplating method, dry process, cladding, etc. No matter which method is used, the effect of the present invention can be obtained. Further, it is also possible to add desired alloy elements to the second layer deposited and simultaneously alloy it.
• the cold rolling is performed with the second layer deposited on the steel sheet.
• the reduction rate is 30% to 95%.
• the reduction rate is less than 30%, the ⁇ 222 ⁇ plane integration of the steel sheet obtained after heat treatment is low and sometimes will not reach the range of the present invention. If the reduction rate is over 95%, the increase in plane integration becomes saturated and the production cost increases. Therefore, the reduction rate is made 30% to 95%.
• the steel sheet is dipped in an aqueous solution of caustic soda to remove the plating ingredient.
• an aqueous solution of caustic soda to remove the plating ingredient.
• the heat treatment for causing the steel sheet to recrystallize can be performed in a vacuum atmosphere, Ar atmosphere, H 2 atmosphere, or other nonoxidizing atmosphere. At this time, preferably the heat treatment temperature is 600°C to 1000°C and the heat treatment time is 30 seconds or more.
• the heat treatment temperature is 600°C or more, the ⁇ 222 ⁇ plane integration becomes higher and more easily reaches the range of the present invention.
• the ⁇ 222 ⁇ plane integration becomes higher and more easily reaches the range of the present invention.
• the heat treatment temperature is 600°C to 1000°C and the heat treatment time is 30 seconds or more.
• the heat treatment temperature is over 1000°C, a high ⁇ 222 ⁇ plane integration can be obtained without restriction by the heat treatment time. In particular, if over 1000°C, even with less than 30 seconds heat treatment time, the ⁇ 222 ⁇ plane integration can be easily increased.
• the heat treatment temperature is more preferably 1300°C or less. If the heat treatment temperature is 1300°C or less, the flatness of the steel sheet and other sheet properties become more superior.
• the temperature rise rate at the time of the heat treatment is preferably 1°C/min to 1000°C/min. If the temperature rise rate is 1000°C/min or less, a higher ⁇ 222 ⁇ plane integration can be easily obtained. If the temperature rise rate is 1°C/min or more, the productivity is remarkably improved.
• a temperature rise rate of 1°C/min to 1000°C/min is preferable.
• the heat treatment performed in the state with the second layer deposited is designed to make the steel sheet recrystallize and also to make the elements included in the second layer diffuse into the steel.
• the diffusion of elements included in the second layer is positively utilized.
• the matrix steel sheet preferably has a content of Cr of 12 mass% or less under the above Al content.
• a Cr content of less than 10 mass% is more preferable.
• the matrix steel sheet is a steel sheet with a C content of 2.0 mass% or less and includes as impurities slight amounts of Mn, P, S, etc.
• carbon steel is included in the matrix steel sheet of the present invention.
• alloyed steel containing alloy elements such as Ni and Cr in addition to C is also included in the matrix steel sheet of the present invention.
• the alloy elements which the matrix steel sheet may contain are Si, Al, Mo, W, V, Ti, Nb, B, Cu, Co, Zr, Y, Hf, La, Ce, N, O, etc.
• the Al content of the matrix steel sheet was changed to investigate the manufacturability and ⁇ 222 ⁇ plane integration.
• Matrix steel sheets of ingredients of five different types of Al content were produced.
• the Al contents were, by mass%, 3.0% (ingredients A), 3.4% (ingredients E), 4.0% (ingredients B), 6.0% (ingredients C), and 7.5% (ingredients D).
• the ingredients included C: 0.008%, Si: 0.2%, Mn: 0.4%, Cr: 20.0%, Zr: 0.08%, La: 0.08%, and a balance of iron and unavoidable impurities.
• ingots were produced by vacuum melting and hot rolled to try to reduce them to 3.0 mm thickness.
• the ingots could be easily hot rolled to 3.0 mm thick steel sheets, but in the case of the ingredients D, the steel sheet frequently broke during the hot rolling, so hot rolling could not be continued.
• the main phases of the steel sheets of the ingredients A, B, C, and E at ordinary temperature were ⁇ Fe phases.
• X-ray diffraction was used to measure the texture of the ⁇ Fe phase of each matrix steel sheet and, in the same way as above, the plane integration was calculated.
• Each steel sheet was heat treated at 800°C ⁇ 10 sec in a hydrogen atmosphere before forming the second layer. After this, the hot dip method was used to deposit Al alloy on the surface of the matrix steel sheet.
• the composition of the plating bath was, by mass%, 90%Al-10%Si.
• the Al alloy was deposited on both surfaces of each steel sheet.
• each steel sheet was cold rolled by a reduction rate of 70%. Next, it was heat treated in a vacuum under conditions of 1000°C ⁇ 120 min to cause the steel sheet to recrystallize.
• the second layer does not include Al
• the Al content in the matrix steel sheet is outside the range of the present invention at 3.5% or more, it was confirmed that shrinkage occurs during heat treatment and use for practical applications is difficult.
• the Al content of the matrix steel sheet is in the range of the present invention at less than 3.5%, no shrinkage occurs and use is possible for practical applications.
• a second layer not containing Al was deposited on a matrix steel sheet having an Al content of 3.5% or more and similar heat treatment was performed. In this case, no shrinkage occurred during the heat treatment.
• the ⁇ 222 ⁇ plane integrations of the obtained steel sheets were respectively 82% and 83% and the ⁇ 200 ⁇ plane integrations were respectively 0.5% and 0.8%. Both integrations were in the range of the present invention.
• steel sheets produced by the method of production of the present invention were in the range of the present invention with a ⁇ 222 ⁇ plane integration of the ⁇ Fe phase parallel to the steel sheet surface of 60% or more or with a ⁇ 200 ⁇ plane integration parallel to the steel sheet surface of 15% or less.
• the ingredients of the matrix steel sheet were, by mass%, Al: 1.5%, C: 0.008%, Si: 0.1%, Mn: 0.2%, Cr: 18%, Ti: 0.1%, and a balance of iron and unavoidable impurities.
• the matrix steel sheet was a steel sheet obtained by producing an ingot by the vacuum melting method, hot rolling the ingot to obtain steel sheet of 3.8 mm thickness, then cold rolling it to obtain steel sheet of 0.8 mm thickness.
• the main phase of the matrix steel sheet at ordinary temperature was the ⁇ Fe phase.
• X-ray diffraction was used to measure the texture of the ⁇ Fe phase of the matrix steel sheet whereupon it was confirmed that the ⁇ 222 ⁇ plane integration was 36% and the ⁇ 200 ⁇ plane integration was 20%.
• Part of the matrix steel sheet was heat treated at 800°C ⁇ 10 sec in a hydrogen atmosphere before plating.
• Al alloy was deposited on the surface of the matrix steel sheet using the hot dip method.
• the composition of the plating bath was, by mass%, 90%Al-10%Si.
• the Al alloy was deposited on both surfaces of the steel sheet. The thickness of the deposited Al alloy was controlled to be uniform in the steel sheet surface.
• the steel sheet with the Al alloy deposited was cold rolled. After this, it was heat treated in a nonoxidizing atmosphere. Before the heat treatment, if necessary, the Al alloy deposited on the surface was removed.
• the Al alloy was removed by dipping the steel sheet in heated caustic soda 10% aqueous solution to dissolve the Al alloy in the solution.
• Table 1 shows the alloying ratio, ⁇ 222 ⁇ plane integration of the ⁇ Fe phase, ⁇ 200 ⁇ plane integration of the ⁇ Fe phase, and Al content for steel sheets produced under various conditions.
• the plane integration was obtained by measurement using X-ray diffraction and calculation by the above-mentioned calculation processing method.
• the alloying ratio of the steel sheet was found as follows: At the L cross-section, in a field of the L direction 1 mmxentire thickness, the EPMA (Electron Probe Micro-Analysis) method was used to measure the plane distribution of the Fe content and the plane distribution of the Al content.
• EPMA Electro Probe Micro-Analysis
• the alloying ratio was calculated by dividing the alloyed area by the L direction 1 mmxtotal thickness area.
• the ⁇ 222 ⁇ plane integration and the ⁇ 200 ⁇ plane integration were outside the range of the present invention.
• the Al content of the obtained steel sheet was the same as the matrix steel sheet, that is, 1.5%, since the Al alloy was removed.
• the amount of deposition of the Al alloy was controlled by adjusting the plating thickness to become 3.2% of the steel sheet as whole. After plating, the steel sheet was cold rolled by a reduction rate of 50%, then the Al alloy was removed and the steel sheet was heat treated under conditions of 950°C ⁇ 0.1 min to make the steel sheet recrystallize.
• the ⁇ 222 ⁇ plane integration was outside the range of the present invention, but the ⁇ 200 ⁇ plane integration was in the range of the present invention.
• the Al content in the obtained steel sheet was the same as the matrix, that is, 1.5%, since the Al alloy was removed.
• each steel sheet was heat treated at 800°C, then Al alloy was deposited on the steel sheet surface so that the Al content became 3.2% at the steel sheet as a whole. After this, the steel sheet was cold rolled at a reduction rate of 50% to make it thinner.
• the Al content in the obtained steel sheet was the same as the matrix, that is, 1.5%, since the Al alloy was removed.
• the amount of deposition of the Al alloy in No. 7 was controlled to give an Al content of 3.2% in the steel sheet as a whole.
• the amount of deposition of the Al alloy in No. 8 was similarly controlled to give an Al content of 6.0% in the steel sheet as a whole. After this, the two steel sheets were cold rolled at a reduction rate of 50% to make them thinner.
• Each of the above steel sheets was tested for burr resistance.
• a 10.0 mm ⁇ punch and a 10.3 mm ⁇ die were used for punching and the burr height around the punched hole was measured by a point micrometer.
• the burr height was a high level of 23 to 65 ⁇ m in the comparative examples, but was an extremely low level of 4 to 9 ⁇ m in the invention examples.
• the steel sheets of the above examples were measured for the average r value, whereupon it was confirmed that in the steel sheets of the invention examples, the average r value was at a high level of 2.5 or more, but in the steel sheets of the comparative examples, the average r value was less than 2.5 or measurement was not possible.
• the steel sheets of the invention examples have excellent drawability. Further, the steel sheets of the invention examples were subjected to Erichsen tests and the extruded surfaces were observed whereupon excellent press workability was also confirmed.
• the steel sheet produced by the method of production of the present invention in this way was confirmed to have a ⁇ 222 ⁇ plane integration of ⁇ Fe phase parallel to the steel sheet surface of 60% or more and a ⁇ 200 ⁇ plane integration of the ⁇ Fe phase parallel to the steel sheet surface of 15% or less or both in the range of the present invention.
• the matrix steel sheet was a steel sheet obtained by using the vacuum melting method to obtain an ingot of ingredients, by mass%, of an Al content of 0.01% and also C: 0.005%, Si: 0.2%, Mn: 0.5%, Ti: 0.05%, and a balance of iron and unavoidable impurities, hot rolling to a thickness of 3.2 mm, then cold rolling to a thickness of 1.8 mm.
• the main phase of the matrix steel sheet at ordinary temperature was an ⁇ Fe phase.
• X-ray diffraction was used to measure the texture of the ⁇ Fe phase of the matrix steel sheet whereupon it was confirmed that the ⁇ 222 ⁇ plane integration was 28% and the ⁇ 200 ⁇ plane integration was 19%.
• Part of the matrix steel sheet was heat treated by 770°Cx5 sec in a hydrogen atmosphere before plating.
• the electroplating method was used to deposit an Zn alloy.
• a sulfuric acid type acidic solution was used for the plating bath.
• the deposited plating was, by mass%, a 94%Zn-6%Ni alloy.
• the thickness of the deposited Zn alloy was controlled to become uniform in the steel sheet surface.
• the steel sheet on which the Zn alloy was deposited was cold rolled, then heat treated in a nonoxidizing atmosphere. Before the heat treatment, if necessary, the Zn alloy deposited on the steel sheet surface was removed. The Zn alloy was removed by dipping the steel sheet into a heated hydrochloric acid 10% aqueous solution to make the Zn alloy dissolve in the solution.
• Table 2 shows the alloying ratio, the ⁇ 222 ⁇ plane integration of the ⁇ Fe phase, the ⁇ 200 ⁇ plane integration of the ⁇ Fe phase, and the Al content of steel sheet produced under various conditions. Note that the plane integration was found by measurement using X-ray diffraction and calculation by the above-mentioned calculation processing method.
• the alloying ratio of the steel sheet was found as follows: At the L cross-section, in a field of the L direction 1 mmxentire thickness, the EPMA method was used to measure the plane distribution of the Fe content and the plane distribution of the Zn content.
• the alloying ratio was calculated by dividing the alloyed area by the L direction 1 mm ⁇ total thickness area.
• the above steel sheet was tested for burr resistance.
• a 30.0 mm ⁇ punch and a 30.6 mm ⁇ die were used for punching and the burr height around the punched hole was measured by a point micrometer.
• the alloying ratio was 30% in No. 17 and 60 in No. 18. It was confirmed that the obtained ⁇ 222 ⁇ plane integration and ⁇ 200 ⁇ plane integration were both controlled to within the range of the present invention and the Al content was also in the range of the present invention.
• the steel sheet was cold rolled by a reduction rate of 30% to make it thinner.
• the steel sheet was cold rolled by a reduction rate of 87% to make it thinner.
• the burr height was a high level of 82 to 92 ⁇ m, but in the steel sheets of the invention examples, it was an extremely low level of 7 to 9 ⁇ m.
• the steel sheets of the above examples were measured for the average r value. It was confirmed that in the steel sheets of the invention examples, the average r value was a high level of 2.5 or more, but in the steel sheets of the comparative examples, it was less than 2.5.
• the steel sheets produced by the method of production of the present invention were examined at their extruded surfaces in Erichsen tests and confirmed to be excellent in press workability as well.
• the steel sheet produced by the method of production of the present invention had a ⁇ 222 ⁇ plane integration of the ⁇ Fe phase parallel with respect to the steel sheet surface of 60% or more and a ⁇ 200 ⁇ plane integration of the ⁇ Fe phase parallel to the steel sheet surface of 15% or less or in the range of the present invention.
• the ingredients of the matrix steel sheet were, by mass%, ingredients including Al: 0.015%, C: 0.15%, Si: 0.1%, Mn: 1.5%, Mo: 0.5%, and a balance of iron and unavoidable impurities.
• the matrix steel sheet steel sheets obtained by using the vacuum melting method to produce an ingot and hot rolling the ingot to thicknesses of 15 mm, 10 mm, and 3.8 mm were used.
• cold rolled sheets obtained by cold rolling 3.8 mm steel sheet to thicknesses of 2.0 mm, 1.0 mm, 0.1 mm, 0.01 mm, and 0.005 mm were used as the matrix steel sheet.
• the main phase of the matrix steel sheet at ordinary temperature was the ⁇ Fe phase.
• X-ray diffraction was used to measure the texture of the ⁇ Fe phase of the matrix steel sheet whereupon it was confirmed that the ⁇ 222 ⁇ plane integration was 36 to 40% and the ⁇ 200 ⁇ plane integration was 17 to 22%.
• the matrix steel sheet Before deposition of Cu, the matrix steel sheet was heat treated at 850°C ⁇ 10 sec in a hydrogen atmosphere. After this, different thicknesses of Cu were deposited on the two surfaces of matrix steel sheets.
• the Cu was deposited by the cladding method, the electroplating method, or the sputtering method.
• the thickness of the Cu was changed, in the cladding method, by changing the thickness of the Cu sheet clad, in the plating method, by changing the conducted current and dipping time, and, further, in the sputtering method, by changing the sputtering time.
• a sulfuric acid solution was used for the plating bath.
• Table 3 shows the ⁇ 222 ⁇ plane integration of the ⁇ Fe phase and the ⁇ 200 ⁇ plane integration of the ⁇ Fe phase of steel sheets produced under various conditions. Note that the plane integration was obtained by measurement by X-ray diffraction and calculation by the above-mentioned calculation processing method.
• the steel sheet was cold rolled by a reduction rate of 60%. Next, the removal of the second layer was omitted and the steel sheet was heat treated under conditions of 1020°C ⁇ 0.3 min to make the steel sheet recrystallize.
• the ⁇ 222 ⁇ plane integration was in the range of the present invention. In No. 22 where the thickness of the second layer when depositing the second layer was over 1000 ⁇ m and in No. 27 where the thickness of the second layer less than 0.05 ⁇ m, the ⁇ 222 ⁇ plane integration fell somewhat and the ⁇ 222 ⁇ plane integration was over 15%.
• the thickness of the second layer after production was over 500 ⁇ m and peeling occurred somewhat easily.
• the thickness of the second layer after production was less than 0.01 ⁇ m, the coating tore easily, and there was some problem in terms of rust prevention.
• the ⁇ 222 ⁇ plane integration was in the range of the present invention, but in No. 28 where the thickness of the matrix steel sheet at the time of deposition was over 10 mm and in No. 33 where the thickness of the matrix steel sheet was less than 10 ⁇ m, the ⁇ 222 ⁇ plane integration fell somewhat and, furthermore, the ⁇ 222 ⁇ plane integration exceeded 15%.
• the steel sheets of the above invention examples were measured for the average r value. It was confirmed that in the steel sheets of the invention examples, the average r value was a high level of 2.5 or more. Therefore, the steel sheets of the invention examples had excellent drawability.
• the steel sheet produced by the method of production of the present invention had a ⁇ 222 ⁇ plane integration of the ⁇ Fe phase parallel with respect to the steel sheet surface of 60% or more and a ⁇ 200 ⁇ plane integration of the ⁇ Fe phase parallel to the steel sheet surface of 15% or less or in the range of the present invention.
• the ingredients of the matrix steel sheet were, by mass%, ingredients including Al: 0.02%, C: 0.06%, Si: 0.2%, Mn: 0.4%, Cr:13.1%, Ni: 11.2%, and a balance of iron and unavoidable impurities.
• the matrix steel sheet steel sheet obtained by using the vacuum melting method to produce an ingot and hot rolling the ingot to a thickness of 3.0 mm and, furthermore, cold rolling to a thickness of 0.8 mm was used.
• the main phase of the matrix steel sheet at ordinary temperature was the ⁇ Fe phase.
• X-ray diffraction was used to measure the texture of the ⁇ Fe phase of the matrix steel sheet and the plane integration was calculated in the same way as above. It was confirmed that the ⁇ 222 ⁇ plane integration was 24% and that the ⁇ 200 ⁇ plane integration was 21%.
• Part of the matrix steel sheet was heat treated at 950°C ⁇ 10 sec in a hydrogen atmosphere before Cr plating.
• Cr was deposited on the surface of the matrix steel sheet using the electroplating method.
• a chrome sulfate solution was used for the plating bath.
• the thickness of the deposited Cr was 0.6 ⁇ m. This was controlled to become uniform in the steel sheet surface.
• Table 4 shows the alloying ratio, the ⁇ 222 ⁇ plane integration of the ⁇ Fe phase, the ⁇ 200 ⁇ plane integration of the ⁇ Fe phase, and the Al content of steel sheet produced under various conditions. Note that the plane integration was found by measurement using X-ray diffraction and calculation by the above-mentioned calculation processing method.
• the alloying ratio of the steel sheet was found as follows: At the L cross-section, in a field of the L direction 1 mmxentire thickness, the EPMA method was used to measure the plane distribution of the Fe content and the plane distribution of the Cr content.
• the sheet was heat treated at 950°C, then Cr of a thickness of 0.6 ⁇ m was deposited on the steel sheet surface. After this, the steel sheet was cold rolled by a reduction rate of 75% to make it thinner.
• the Cr was removed, then the steel sheet was heat treated under conditions of 1050°C ⁇ 0.2 min to make the steel sheet recrystallize.
• the ratio of alloying was, in No. 39, 10%, in No. 40, 30%, and in No. 41, 60%.
• the steel sheets of the above examples were measured for the average r value. It was confirmed that in the steel sheets of the invention examples, the average r value was a high level of 2.5 or more, but in the steel sheets of the comparative examples, it was less than 2.5.
• the steel sheet produced by the method of production of the present invention had a ⁇ 222 ⁇ plane integration of the ⁇ Fe phase parallel with respect to the steel sheet surface of 60% or more and a ⁇ 200 ⁇ plane integration of the ⁇ Fe phase parallel to the steel sheet surface of 15% or less or in the range of the present invention.
• the ingredients of the matrix steel sheet were, by mass%, ingredients including Al: 0.039%, C: 0.0019%, Si: 0.011%, Mn: 0.13%, N: 0.002%, Ti: 0.061%, Cr: 0.002% or less and a balance of iron and unavoidable impurities.
• the matrix steel sheet was steel sheet obtained by using the vacuum melting method to produce an ingot and hot rolling the ingot to a thickness of 3.0 mm. Note that pickling was used to remove the scale from the steel sheet surface.
• the main phase of the matrix steel sheet at ordinary temperature was the ⁇ Fe phase.
• X-ray diffraction was used to measure the texture of the ⁇ Fe phase of the matrix steel sheet and the plane integration was calculated in the same way as above. It was confirmed that the ⁇ 222 ⁇ plane integration was 19% and that the ⁇ 200 ⁇ plane integration was 17%.
• This matrix steel sheet was heat treated at 780°C ⁇ 10 sec in a hydrogen atmosphere before plating.
• Al alloy was deposited by the hot dip method.
• the composition of the plating bath was, by mass%, 90%Al-10%Si. The alloy was deposited on the two surfaces of the steel sheet.
• the amount of plating deposition was controlled by, before the plating solidified, using a wiping gas to blow nitrogen over the steel sheet surface to blow off unnecessary plating.
• Table 5 shows the alloying ratio of the produced steel sheet, the ⁇ 222 ⁇ plane integration of the ⁇ Fe phase, the ⁇ 200 ⁇ plane integration of the ⁇ Fe phase, and the Al content of steel sheet produced under various conditions. Note that the plane integration was found by measurement using X-ray diffraction and calculation by the above-mentioned calculation processing method.
• the alloying ratio of the steel sheet was found as follows: At the L cross-section, in a field of the L direction 1 mmxentire thickness, the EPMA method was used to measure the plane distribution of the Fe content and the plane distribution of the Al content.
• the alloying ratio was calculated by dividing the alloyed area by the L direction 1 mm ⁇ total thickness area.
• the above steel sheet was tested for burr resistance.
• a 10.0 mm ⁇ punch and a 10.3 mm ⁇ die were used for punching and the burr height around the punched hole was measured by a point micrometer.
• the ⁇ 222 ⁇ plane integration and the ⁇ 200 ⁇ plane integration were both outside the range of the present invention.
• the burr height was a large value of 51 to 57 ⁇ m.
• the ⁇ 222 ⁇ plane integration and the ⁇ 200 ⁇ plane integration were both in the range of the present invention.
• the burr height was 12 to 14 ⁇ m or remarkably lower than the comparative examples.
• the ⁇ 222 ⁇ plane integration and the ⁇ 200 ⁇ plane integration were both in the range of the present invention.
• the burr height was 5 to 8 ⁇ m or a remarkably small value.
• the steel sheets of the above examples were measured for the average r value. It was confirmed that in the steel sheets of the invention examples, the average r value was a high level of 2.5 or more, but in the steel sheets of the comparative examples, it was less than 2.5.
• the steel sheet produced by the method of production of the present invention had a ⁇ 222 ⁇ plane integration of the ⁇ Fe phase parallel with respect to the steel sheet surface of 60% or more and a ⁇ 200 ⁇ plane integration of the ⁇ Fe phase parallel to the steel sheet surface of 15% or less or in the range of the present invention and that both excellent burr resistance and drawability were achieved.
• the matrix steel sheet was produced by four types of ingredients with different Cr content.
• the Cr content was, by mass%, 13.0% (ingredients F), 11.9% (ingredients G), 6.0% (ingredients H), and 0.002% or less (detection limit or less) (ingredients I).
• C 0.083%
• Si 0.11%
• Mn 0.23%
• Al 0.002%
• N 0.003
• a balance of iron and unavoidable impurities were included in the ingredients.
• vacuum melting was used to produce an ingot and the ingot was hot rolled to reduce it to a thickness of 3.5 mm.
• the four types of steel sheets were cold rolled to a thickness of 1.3 mm.
• the main phases of the steel sheets of the ingredients F, G, H, and I at ordinary temperature were the ⁇ Fe phases.
• X-ray diffraction was used to measure the texture of the ⁇ Fe phase of the matrix steel sheet and the plane integration was calculated in the same way as above.
• the electroplating method was used to deposit Sn on the surface of the matrix steel sheet as the second layer.
• the plating bath was a sulfuric acid acidic solution.
• the process was controlled to give a basis weight per side of 1 g/m 2 . Both surfaces were plated. Before the electroplating, no preheat treatment was applied.
• each steel sheet was cold rolled by a reduction rate of 40% to obtain steel sheet of a thickness of 0.78 mm.
• steel sheets of the ingredients F, G, H, and I with no Sn deposited were also cold rolled by a reduction rate of 40%.
• each steel sheet was heat treated in vacuum at a temperature rise rate of 100°C/min under conditions of 1100°C ⁇ 60 min to make the steel sheet recrystallize. At this time, at each steel sheet, the Sn of the steel sheet surface diffused in the steel and was completely alloyed.
• the obtained eight types of steel sheets were measured for the ⁇ 222 ⁇ plane integration and the ⁇ 200 ⁇ plane integration.
• the ⁇ 222 ⁇ area integration of the steel sheets on which Sn was deposited was, for the ingredients F, 65%, the ingredients G, 75%, the ingredients H, 79%, and the ingredients I, 85%, while the ⁇ 200 ⁇ plane integration was, for the ingredients F, 12%, the ingredients G, 4%, the ingredients H, 2.5%, and the ingredients I, 1.4.
• the plane integration was within the range of the present invention, but it was learned that if the Cr contained is, by mass%, less than 12.0%, a particularly high ⁇ 222 ⁇ plane integration can be obtained.
• the plane integration of the steel sheets on which Sn was not deposited was, for the ingredients F, 21%, the ingredients G, 12%, the ingredients H, 11%, and the ingredients I, 12 and the ⁇ 200 ⁇ plane integration was, for the ingredients F, 16%, the ingredients G, 17%, the ingredients H, 16%, and the ingredients I, 16%.
• the burr resistance was evaluated by using 10.0 mm ⁇ punch and a 10.3 mm ⁇ die for punching and measuring the burr height around the punched hole by a point micrometer.
• the burr height of the steel sheets on which Sn was deposited was, for the ingredients F, 9 ⁇ m, the ingredients G, 7 ⁇ m, the ingredients H, 6 ⁇ m, and the ingredients I, 5 ⁇ m. It was confirmed that each steel sheet had excellent properties.
• the burr height of the steel sheets on which Sn was not deposited was, for the ingredients F, 46 ⁇ m, the ingredients G, 52 ⁇ m, the ingredients H, 63 ⁇ m, and the ingredients I, 68 ⁇ m. It was confirmed that each steel sheet suffered from large burrs.
• each steel sheet was measured for the average r value, whereupon it was confirmed that the average r value of a steel sheet on which Sn was deposited was a high level of 2.5 or more.
• the average r value for a steel sheet on which Sn was not deposited was about 1.1.
• the steel sheet produced by the method of production of the present invention had a ⁇ 222 ⁇ plane integration of the ⁇ Fe phase parallel with respect to the steel sheet surface of 60% or more and a ⁇ 200 ⁇ plane integration of the ⁇ Fe phase parallel to the steel sheet surface of 15% or less or in the range of the present invention.
• the matrix steel sheet was produced by four types of ingredients with different Al content.
• the Al content was, by mass%, 7.5% (ingredients J), 6.4% (ingredients K), 3.4% (ingredients L), and 0.002% or less (ICP detection limit or less) (ingredients M).
• C 0.083%
• Si 0.11%
• Mn 0.23%
• Cr 0.002% or less
• N 0.003
• a balance of iron and unavoidable impurities were included in the ingredients.
• vacuum melting was used to produce an ingot and the ingot was hot rolled to reduce it to a thickness of 2.8 mm.
• the ingots of the ingredients K, L, and M could be easily hot rolled to steel sheets, but the ingot of the ingredients J frequently broke during hot rolling so hot rolling could not be continued.
• the main phases of the steel sheets of the ingredients K, L, and M at ordinary temperature were the ⁇ Fe phases.
• X-ray diffraction was used to measure the texture of the ⁇ Fe phase of the matrix and the plane integration was calculated in the same way as above. It was confirmed that the ⁇ 222 ⁇ plane integration was, for the ingredients K, 11%, the ingredients L, 12%, and the ingredients M, 12%, while the ⁇ 200 ⁇ plane integration was, for the ingredients K, 8%, the ingredients L, 7%, and the ingredients M, 8%.
• the composition of the plating bath was 95%Zn-5%Fe.
• the Zn alloy was deposited on both surfaces of the steel sheet.
• the amount of deposition, in total for the front and back, was made 80 g/m 2 .
• the amounts of deposition on the front and back were made as uniform as possible.
• each steel sheet was cold rolled by a reduction rate of 50% to obtain steel sheet of a thickness of 0.80 mm.
• each steel sheet was heat treated in a vacuum at a temperature rise rate of 10°C/min under conditions of 1100°C ⁇ 60 min to make the steel sheet recrystallize.
• the Zn alloy of the steel sheet surface diffused in the steel and was completely alloyed.
• the obtained eight types of steel sheets were measured for the ⁇ 222 ⁇ plane integration and the ⁇ 200 ⁇ plane integration.
• the ⁇ 222 ⁇ area integration of the steel sheets on which Zn alloy was deposited was, for the ingredients K, 78%, the ingredients L, 85%, the ingredients M, 90%, and the ingredients I, 85%, while the ⁇ 200 ⁇ plane integration was, for the ingredients K, 1.4%, the ingredients L, 0.6%, and the ingredients M, 0.4%.
• the plane integration was within the range of the present invention, but it was learned that if the Al contained is, by mass%, less than 3.5%, a particularly high ⁇ 222 ⁇ plane integration can be obtained.
• the plane integration of the steel sheets on which Zn alloy was not deposited was, for the ingredients K, 36%, the ingredients L, 32%, and the ingredients M, 25%, and the ⁇ 200 ⁇ plane integration was, for the ingredients K, 17%, the ingredients L, 19%, and the ingredients M, 16%.
• the burr resistance was evaluated by using 10.0 mm ⁇ punch and a 10.3 mm ⁇ die for punching and measuring the burr height around the punched hole by a point micrometer.
• the burr height of the steel sheets on which Zn was deposited was, for the ingredients K, 7 ⁇ m, the ingredients L, 5 ⁇ m, and the ingredients M, 5 ⁇ m. It was confirmed that each steel sheet had excellent properties.
• the burr height of the steel sheets on which Zn alloy was not deposited was, for the ingredients K, 52 ⁇ m, the ingredients L, 57 ⁇ m, and the ingredients M, 65 ⁇ m. It was confirmed that each steel sheet suffered from large burrs.
• each steel sheet was measured for the average r value, whereupon it was confirmed that the average r value of a steel sheet on which Zn alloy was deposited was a high level of 2.5 or more.
• the average r value for a steel sheet on which Zn alloy was not deposited was about 1.1.
• the steel sheet produced by the method of production of the present invention had a ⁇ 222 ⁇ plane integration of the ⁇ Fe phase parallel with respect to the steel sheet surface of 60% or more and a ⁇ 200 ⁇ plane integration of the ⁇ Fe phase parallel to the steel sheet surface of 15% or less or in the range of the present invention.
• the hot rolled sheets of the thicknesses of 2.8 mm of the ingredients K, L, and M used in Example 8 were used as the matrix steel sheets. Steel sheets of the ingredients K, L, and M were cold rolled to 0.4 mm thickness.
• the main phases of the steel sheets of the ingredients K, L, and M at ordinary temperature were ⁇ Fe phases.
• X-ray diffraction was used to measure the texture of the ⁇ Fe phase of each matrix steel sheet and the plane integration was calculated in the same way as above.
• each matrix steel sheet was heat treated at 620°Cx60 sec in an Ar atmosphere.
• the sputtering method was used to deposit on the surface of the matrix steel sheet a second layer of Mo, Cr, Ge, Si, Ti, W, and V metal.
• Metal target materials of purities of 99.9% or more were prepared and the thicknesses per side were controlled to 1 ⁇ m to form coatings on the two surfaces.
• each steel sheet was cold rolled by a reduction rate of 62.5% to obtain steel sheet of a thickness of 0.15 mm.
• steel sheets of the ingredients K, L, and M on which no second layer comprised of a metal is deposited were also cold rolled by a reduction rate of 62.5% to a thickness of 0.15 mm.
• each steel sheet was heat treated in vacuum at a temperature rise rate of 500°C/min under conditions of 1150°C ⁇ 15 sec to make the steel sheet recrystallize.
• Table 6 shows the alloying ratio, the ⁇ 222 ⁇ plane integration of the ⁇ Fe phase, the ⁇ 200 ⁇ plane integration of the ⁇ Fe phase, and the Al content of steel sheet produced under various conditions.
• the plane integration was found by measurement using X-ray diffraction and calculation by the above-mentioned calculation processing method.
• the alloying ratio of the steel sheet was found as follows: At the L cross-section, in a field of the L direction 1 mmxentire thickness, the EPMA method was used to measure the plane distribution of the Fe content and the plane distribution of the content of the deposited metal elements among Mo, Cr, Ge, Si, Ti, W, and V.
• a region of Fe ⁇ 0.5 mass% and a content of the deposited metal element among Mo, Cr, Ge, Si, Ti, W, and V ⁇ 0.1 mass% was deemed an alloyed region and its area was found as the alloyed area.
• the alloying ratio was calculated by dividing the alloyed area by the L direction 1 mm ⁇ total thickness area.
• the above steel sheet was tested for burr resistance.
• a 10.0 mm ⁇ punch and a 10.3 mm ⁇ die were used for punching and the burr height around the punched hole was measured by a point micrometer.
• Si metal was deposited as the second layer.
• the ⁇ 222 ⁇ plane integration and the ⁇ 200 ⁇ plane integration were both in the range of the present invention.
• the burr height was 7 to 8 ⁇ m or much lower than the comparative examples.
• Ge metal was deposited as the second layer.
• the ⁇ 222 ⁇ plane integration and the ⁇ 200 ⁇ plane integration were both in the range of the present invention.
• the burr height was 8 to 9 ⁇ m or much lower than the comparative examples.
• V metal was deposited as the second layer.
• the ⁇ 222 ⁇ plane integration and the ⁇ 200 ⁇ plane integration were both in the range of the present invention.
• the burr height was 6 to 8 ⁇ m or much lower than the comparative examples.
• the steel sheets of the above examples were measured for the average r value. It was confirmed that in the steel sheets of the invention examples, the average r value was a high level of 2.5 or more, but in the steel sheets of the comparative examples, it was less than 2.5.
• the steel sheet produced by the method of production of the present invention had a ⁇ 222 ⁇ plane integration of the ⁇ Fe phase parallel with respect to the steel sheet surface of 60% or more and a ⁇ 200 ⁇ plane integration of the ⁇ Fe phase parallel to the steel sheet surface of 15% or less or in the range of the present invention and that excellent burr resistance and drawability were both achieved.
• the present invention steel sheet has the unprecedented superior workability of absence of formation of burrs at the cross-section at the time of punching, so can be easily worked into various shapes including everything from conventional shapes to special sheets.
• the present invention steel sheet is for example useful for outer panels of auto parts, home electrical appliances, etc. requiring press formation into complicated shapes and other various structural materials and functional materials.
• the method of production of the present invention enables the ⁇ 222 ⁇ plane integration to be raised and/or the ⁇ 200 ⁇ plane integration to be lowered easily and effectively even in steel sheet having an Al content of less than 6.5 mass%.
• the present invention is high in industrial applicability in the manufacturing industries utilizing the various structural materials and functional materials.

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• 2007
  • 2007-11-21 RU RU2009123511/02A patent/RU2428489C2/ru active
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