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
  • 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
  • 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
  • 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
• • 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
  • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following 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
  • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
  • C21D8/0268—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment between cold rolling steps
• • 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
  • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
• • 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
  • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
• • 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
  • 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

Definitions

• the present invention relates to a high-strength steel sheet suitable for can container materials used for the production of food cans and beverage cans and a method for producing the same. Since the high-strength steel sheet of the present invention has particularly excellent formability, it can be preferably applied to the manufacture of an easy-open lid (EOE) and a welded can body.
• EEE easy-open lid
• a steel plate called DR (Double Reduced) material is sometimes used as a steel plate for cans used in the production of beverage cans and food cans and formed on the lid, bottom, and body of a three-piece can.
• the DR material is a steel plate manufactured by performing cold rolling again after annealing. Compared with SR (Single Reduced) material which performs only temper rolling with a small rolling rate, the DR material can be easily made hard and thin in thickness.
• Patent Documents 1 and 2 propose DR materials with improved formability.
• Patent Document 1 in mass%, C: 0.02% to 0.06%, Si: 0.03% or less, Mn: 0.05% to 0.5%, P: 0.02% or less, S: 0.02% or less, Al: 0.02% to 0.10%, N: 0.008% to 0.015%, with the balance being solid solution N in the steel sheet consisting of Fe and inevitable impurities
• the amount (Ntotal-NasAlN) is 0.006% or more, the total elongation value in the rolling direction after the aging treatment is 10% or more, the total elongation value in the sheet width direction after the aging treatment is 5% or more, and the aging treatment
• a DR steel characterized by a later average rankford value of 1.0 or less has been proposed.
• Patent Document 2 in mass%, C: more than 0.04% and 0.08% or less, Si: 0.02% or less, Mn: 1.0% or less, P: 0.04% or less, S: 0 0.05% or less, Al: 0.1% or less, N: 0.005 to 0.02% or less, and the total of solid solution C and solid solution N dissolved in the steel sheet is 50 ppm ⁇ solid solution C + solid Flange formability characterized by satisfying the relationship of dissolved N ⁇ 200 ppm, solid solution C in the steel sheet being 50 ppm or less, solid solution N in the steel sheet being 50 ppm or more, and the balance being Fe and inevitable impurities
• a thin steel plate for a high-strength welded can excellent in strength has been proposed.
• This invention is made
• the present inventors have conducted intensive research to solve the above problems.
• the tensile strength in the direction perpendicular to the rolling after aging treatment is 530 MPa.
• the elongation becomes 7% or more.
• the present inventors have found that the ferrite average particle diameter and the dislocation density of 1 ⁇ 4 part thickness contribute to both the tensile strength and the elongation, and have completed the present invention.
• the present invention is as follows.
• the density is 4.0 ⁇ 10 14 m ⁇ 2 or more and 2.0 ⁇ 10 15 m ⁇ 2 or less, the tensile strength in the direction perpendicular to the rolling after aging treatment is 530 MPa or more, and the elongation is 7% or more.
• High strength steel sheet is 4.0 ⁇ 10 14 m ⁇ 2 or more and 2.0 ⁇ 10 15 m ⁇ 2 or less, the tensile strength in the direction perpendicular to the rolling after aging treatment is 530 MPa or more, and the elongation is 7% or more.
• High strength steel sheet is 4.0 ⁇ 10 14 m ⁇ 2 or more and 2.0 ⁇ 10 15 m ⁇ 2 or less, the tensile strength in the direction perpendicular to the rolling after aging treatment is 530 MPa or more, and the elongation is 7% or more.
• the high-strength steel sheet of the present invention has a specific composition, has an average ferrite grain size of 7.0 ⁇ m or less, and has a dislocation density of 4.0 ⁇ 10 14 m ⁇ at a 1/4 depth position from the surface. By being 2 or more and 2.0 ⁇ 10 15 m ⁇ 2 or less, the tensile strength in the direction perpendicular to the rolling after the aging treatment is 530 MPa or more and the elongation is 7% or more.
• the high-strength steel sheet of the present invention since the high-strength steel sheet of the present invention has high formability, it can be preferably applied to applications in which rivets and flanges are formed.
• the high-strength steel sheet of the present invention has a tensile strength of 530 MPa or more and has a sufficient strength, so that a high-quality can body or can lid can be obtained even if the sheet thickness is suppressed as compared with the conventional one. By reducing the plate thickness, resource saving and cost reduction can be realized.
• the high-strength steel sheet of the present invention which is excellent in terms of formability and strength, can be expected to be applied not only to various metal cans but also to a wide range of dry battery interior cans, various home appliances / electrical parts, automotive parts and the like.
• the high-strength steel sheet of the present invention has a specific component composition and is adjusted so that the ferrite average particle diameter and the dislocation density at the 1/4 position of the sheet thickness are in a specific range. As a result, the high-strength steel sheet of the present invention has high strength and excellent formability.
• description will be made in the order of the component composition, the ferrite average particle diameter, the dislocation density at the 1/4 position of the plate thickness, the material of the high-strength steel plate (high strength, high formability), and the manufacturing method of the high-strength steel plate.
• the high-strength steel sheet of the present invention is, in mass%, C: 0.010% to 0.080%, Si: 0.05% or less, Mn: 0.10% to 0.70%, P: 0.00. 03% or less, S: 0.020% or less, Al: 0.005% or more and 0.070% or less, N: 0.0120% or more and 0.0180% or less, with the balance being Fe and inevitable impurities It has an ingredient composition. And among said N to contain, N content as solid solution N is 0.0100% or more.
• % means “mass%”.
• C 0.010% or more and 0.080% or less C is an element that contributes to improving the strength of the steel sheet.
• the tensile strength in the direction perpendicular to the rolling after the aging treatment can be set to 530 MPa or more.
• the C content exceeds 0.080%, the elongation in the direction perpendicular to the rolling after the aging treatment is reduced to less than 7%, and the flange workability and rivet formability of the steel sheet are reduced. Therefore, the C content needs to be 0.080% or less.
• the C content is preferably less than 0.040%. Since the ferrite average particle size can be refined as the C content increases, the C content is preferably 0.020% or more in order to increase the strength of the steel sheet.
• Si 0.05% or less
• Si content needs to be 0.05% or less.
• Mn 0.10% or more and 0.70% or less Mn has an effect of improving the hardness of the steel sheet by solid solution strengthening. Further, Mn forms MnS and has an effect of preventing a decrease in hot ductility due to S contained in the steel. In order to acquire this effect, it is necessary to make Mn content 0.10% or more. Furthermore, since Mn has an effect of reducing the particle size, the Mn content is preferably 0.20% or more. Further, by reducing the diffusion rate of N, there is an effect of suppressing the generation of AlN and ensuring solid solution N, which is particularly effective when the tensile strength is increased to 590 MPa or more. For this reason, it is more preferable to make Mn content more than 0.50%. Moreover, even if Mn is added excessively, the above effect is not only saturated, but also the elongation is remarkably reduced. Therefore, the Mn content is set to 0.70% or less.
• P 0.03% or less
• the P content is 0.03% or less.
• it is 0.02% or less.
• S 0.020% or less S forms a sulfide in the steel and reduces the hot ductility of the steel sheet. Therefore, the S content is 0.020% or less. Preferably it is 0.015% or less.
• Al 0.005% or more and 0.070% or less
• Al is an element added as a deoxidizer. In order to acquire this effect, it is necessary to make Al content 0.005% or more. Al forms N and AlN, thereby reducing solute N in the steel. When the solid solution N decreases, the strength of the steel sheet decreases, so the Al content is set to 0.070% or less. From the viewpoint of ensuring a solid solution N amount of 0.0100% or more stably, the Al content is preferably 0.020% or less, and more preferably 0.018% or less.
• solid solution N 0.0120% or more and 0.0180% or less
• solid solution N: 0.0100% or more N is present as solid solution N, thereby contributing to high strength of the steel sheet.
• the presence of 0.010% or more of solute N promotes the introduction of dislocations during secondary cold rolling, improving the balance between high strength and formability.
• the N content as the solute N needs to be 0.0100% or more. More preferably, it is 0.0120% or more.
• solid solution N 0.0100% or more, it is necessary to make N content 0.0120% or more.
• the N content is greater than 0.0130%.
• Mn is contained more than 0.50%
• the coiling temperature in hot rolling is 640 ° C. or less
• AlN in the manufacturing process is combined with one or more conditions of 600 ° C. or less, more preferably 580 ° C. or less
• annealing temperature 690 ° C. or less, more preferably less than 680 ° C. It is preferable to suppress the production of.
• the N content is set to 0.0180% or less. Preferably it is 0.0170% or less. When the N content is within this range, the N content as the solid solution N is 0.0180% or less.
• the balance other than the above essential components is iron and inevitable impurities.
• ⁇ Ferrite average particle size 7.0 ⁇ m or less> High strength is achieved by refining the ferrite grains so that the average ferrite grain size is 7.0 ⁇ m or less in a steel sheet that satisfies the above component composition and has a dislocation density in a specific range of the thickness of the plate 1/4. The balance between processing and formability is improved. Furthermore, there is an advantage that rough skin after processing is suppressed by reducing the average ferrite grain size. For this reason, it is preferable that a ferrite average particle diameter is 6.5 micrometers or less. In addition, the value measured by the method as described in an Example is employ
• the finer the ferrite grain size after annealing the more the introduction of dislocations in secondary cold rolling is promoted, and higher strength can be obtained even at a lower rolling rate, further improving the balance between higher strength and formability. .
• the secondary cold rolling becomes smaller. More preferably, the average ferrite grain size after secondary cold rolling is 6.0 ⁇ m or less.
• the lower limit of the average ferrite particle diameter is not particularly limited, but is preferably 1.0 ⁇ m or more because the balance between high strength and formability is reduced when the ferrite is too fine.
• the steel structure of the present invention is mainly composed of ferrite, and the ferrite phase is 98 vol% or more.
• ⁇ Dislocation density at a thickness of 1/4 position 4.0 ⁇ 10 14 m ⁇ 2 or more and 2.0 ⁇ 10 15 m ⁇ 2 or less>
• control of the dislocation density in the steel sheet is important for achieving both the strength and formability of the steel sheet.
• it is necessary to set the dislocation density at the 1/4 depth position of the plate thickness to 4.0 ⁇ 10 14 m ⁇ 2 or more in order to increase the strength.
• Excess dislocation density induces the formation of voids during forming and reduces the formability of the steel sheet. Therefore, the dislocation density needs to be 2.0 ⁇ 10 15 m ⁇ 2 or less.
• the solid solution N amount is 0.0100% or more, preferably 0.0120% or more, the ferrite average particle size is 7.0 ⁇ m or less, preferably 6.5 ⁇ m or less, It is important that the thickness is preferably 6.0 ⁇ m or less.
• the value measured by the method as described in an Example is employ
• the high-strength steel sheet of the present invention has the above-described composition, the ferrite average particle diameter is adjusted to 7.0 ⁇ m or less, and the dislocation density at the 1/4 position of the sheet thickness is 4.0 ⁇ 10 14 m ⁇ 2 or more. Since it is adjusted to 0 ⁇ 10 15 m ⁇ 2 or less, it has high formability while having high strength.
• “Thin is thin” refers to 0.26 mm or less. If it is this invention, high intensity
• High strength means that the tensile strength in the direction perpendicular to the rolling after the aging treatment is 530 MPa or more. If the said tensile strength is 530 Mpa or more, when it shape
• the tensile strength is preferably 550 MPa or more, and more preferably 590 MPa or more. If the tensile strength is 550 MPa or more, both high strength and high formability can be achieved even when the thickness is particularly thin. “Especially thin” refers to 0.18 mm or less.
• High formability means that the elongation in the direction perpendicular to the rolling after aging treatment is 7% or more. If the elongation is 7% or more, when the high-strength steel sheet of the present invention is applied to a can body or an EOE can, the flange workability required for manufacturing the can body and the rivet formability required for manufacturing the EOE can Can be secured sufficiently. When the tensile strength is as high as 550 MPa or higher, more formability is required. Therefore, the elongation in the direction perpendicular to the rolling after the aging treatment is preferably 10% or more.
• the high-strength steel sheet of the present invention can be manufactured by a method having a hot rolling process, a primary cold rolling process, an annealing process, and a secondary cold rolling process. Hereinafter, each step will be described.
• Hot rolling process is a process in which a slab other than the solid solution N has the above component composition (the solid solution N may or may not be filled) is heated at a heating temperature of 1180 ° C. or higher, and hot rolled. This is a step of rolling at a finishing temperature of 820 to 900 ° C. and winding at a winding temperature of 640 ° C. or less.
• heating temperature shall be 1180 degreeC or more. Preferably it is 1200 degreeC or more.
• the upper limit of the heating temperature is not particularly defined, but if the heating temperature is too high, excessive scale may be generated and defects may occur on the product surface. For this reason, it is preferable that heating temperature shall be 1300 degrees C or less.
• the hot rolling finishing temperature is set to 900 ° C. or less.
• the hot-rolling finishing temperature is set to 820 ° C. or higher.
• it is 840 degreeC or more.
• winding temperature shall be 640 degrees C or less. Preferably it is 600 degrees C or less, More preferably, it is 580 degrees C or less.
• the lower limit of the coiling temperature is not particularly limited, but if the coiling temperature is too low, the temperature variation during cooling increases, and the variation in tensile strength and elongation may increase. Therefore, the winding temperature is preferably 500 ° C. or higher.
• the primary cold rolling process is a process of pickling and hot rolling at a rolling rate of 85% or more after the hot rolling process.
• the pickling conditions are not particularly limited as long as the surface scale can be removed. Pickling can be performed by a conventional method.
• the rolling rate is set to 85% or more.
• the rolling rate in this process shall be less than 91.5%.
• Annealing process is a process annealed with the annealing temperature of 620 degreeC or more and 690 degrees C or less after a cold rolling process.
• the annealing temperature needs to be 620 ° C. or higher. If the annealing temperature is too high, the ferrite average particle size becomes coarse, and the balance between tensile strength and elongation decreases. Therefore, the annealing temperature is set to 690 ° C. or less. When the annealing temperature is increased, AlN is generated, and the amount of dissolved N tends to decrease. Therefore, the annealing temperature is preferably set to 680 ° C. or lower.
• the annealing method is not particularly limited, but the continuous annealing method is preferable from the viewpoint of material uniformity. Although the holding time in the annealing step is not particularly limited, it is preferably 5 seconds or more from the viewpoint of the uniformity of the steel sheet temperature, and preferably 90 seconds or less from the viewpoint of preventing the ferrite average grain size from becoming coarse. .
• Secondary cold rolling (DR rolling) step The secondary cold rolling step is a step of performing secondary cold rolling at a rolling rate of 8 to 20% after the annealing step.
• the steel plate after annealing is strengthened by secondary rolling. Moreover, the thickness of a steel plate becomes thin by secondary rolling.
• the rolling rate (DR rate) during secondary cold rolling is set to 8% or more. If the DR ratio is too high, the dislocation density becomes excessively high and the formability deteriorates. For this reason, the DR rate is set to 20% or less. In particular, when moldability is required, the DR rate is preferably 15% or less.
• the high-strength steel plate of the present invention is obtained. Even if the steel sheet obtained here is subjected to surface treatment such as plating or chemical conversion, the effects of the invention are not lost.
• a steel slab was obtained by melting a steel having the composition of steel symbols A to N shown in Table 1, with the balance being Fe and inevitable impurities.
• the obtained steel slab was heated under the conditions shown in Table 2, then hot rolled, the scale was removed by pickling, and then primary cold rolled at the primary cold rolling rate shown in Table 2, followed by a continuous annealing furnace.
• the steel sheet was annealed at each annealing temperature and subjected to secondary cold rolling (DR rolling) at each secondary cold rolling rate, and a steel plate having a thickness of 0.15 to 0.26 mm (steel plate symbols No. 1 to 22). )
• DR rolling secondary cold rolling
• 2.8 g / m 2 of single-sided tin plating was applied to both surfaces of the obtained steel plate, and the characteristics of the tin-plated steel plate were evaluated by the following methods.
• Solid solution N amount The solid solution N amount was evaluated by subtracting the amount of N as AlN measured by extraction analysis with 10% Br methanol from the total N amount.
• Ferrite average grain size After embedding in the cross section in the rolling direction, polishing and corroding with nital to reveal grain boundaries, the average grain size is measured by a cutting method according to JIS G 0551, and the ferrite average grain size is evaluated. did.
• EOE rivet formability After an aging treatment equivalent to baking coating at 210 ° C. for 10 minutes, a rivet for attaching an EOE tab was formed, and the rivet formability was evaluated. Rivet forming was performed by three stages of press working, and after the overhanging process, a diameter reduction (drawing) process was performed to form a cylindrical rivet having a diameter of 4.0 mm and a height of 2.5 mm. The case where wrinkles or cracks occurred on the rivet surface was evaluated as “ ⁇ ”, and the case where no wrinkles or cracks occurred was evaluated as “ ⁇ ”.
• Can body flangeability After aging treatment equivalent to baking coating at 210 ° C for 10 minutes, can body molding with outer diameter of 52.8mm is performed by seam welding, and after the end is neck-in processed to an outer diameter of 50.4mm, the outer Flange processing was performed up to a diameter of 55.4 mm, and the presence or absence of occurrence of flange cracking was evaluated.
• the can body was formed into a 190 g beverage can size and welded along the rolling direction of the steel sheet.
• Neck-in processing was performed by a die neck method, and flange processing was performed by a spin flange method. The case where a crack occurred in the flange processed part was evaluated as “ ⁇ ”, and the case where no crack occurred was evaluated as “ ⁇ ”.
• Can body strength The sample which was able to perform the above-mentioned neck-in processing and flange processing was wrapped with a lid to prepare a can body, and the can body strength was measured by a dent test.
• the indenter with a tip radius of 10 mm and a length of 42 mm is pressed into the center of the can body opposite to the welded portion, and the load when the can body is buckled is measured. Since it was good, “ ⁇ ” and less than 70 N were evaluated as “x”. In addition, the case where a crack could not be created due to the flange processing was marked as “-”.
• the tensile strength is 530 MPa or more
• the elongation is 7% or more
• the ferrite grain size is 7.0 ⁇ m or less
• the dislocation density at the 1/4 depth position of the plate thickness is 4.0 ⁇ 10 14 m ⁇ . It is 2 or more and 2.0 ⁇ 10 15 m ⁇ 2 or less, and is excellent in steel plate strength and formability.
• any one or more of the above characteristics are inferior.

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