Classifications

• • C—CHEMISTRY; METALLURGY
  • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
  • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
  • C25D5/00—Electroplating characterised by the process; Pretreatment or after-treatment of workpieces
  • C25D5/34—Pretreatment of metallic surfaces to be electroplated
  • C25D5/36—Pretreatment of metallic surfaces to be electroplated of iron or steel
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21B—ROLLING OF METAL
  • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B65—CONVEYING; PACKING; STORING; HANDLING THIN OR FILAMENTARY MATERIAL
  • B65D—CONTAINERS FOR STORAGE OR TRANSPORT OF ARTICLES OR MATERIALS, e.g. BAGS, BARRELS, BOTTLES, BOXES, CANS, CARTONS, CRATES, DRUMS, JARS, TANKS, HOPPERS, FORWARDING CONTAINERS; ACCESSORIES, CLOSURES, OR FITTINGS THEREFOR; PACKAGING ELEMENTS; PACKAGES
  • B65D25/00—Details of other kinds or types of rigid or semi-rigid containers
  • B65D25/14—Linings or internal coatings
• • 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
  • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
  • C21D1/26—Methods of 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
  • C21D8/0221—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
• • 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
  • 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
  • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
  • C21D8/0284—Application of a separating or insulating coating
• • 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
• • 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
  • C22C38/02—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
  • 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
  • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
  • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
  • C25D5/00—Electroplating characterised by the process; Pretreatment or after-treatment of workpieces
  • C25D5/48—After-treatment of electroplated surfaces
• • C—CHEMISTRY; METALLURGY
  • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
  • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
  • C25D7/00—Electroplating characterised by the article coated
  • C25D7/06—Wires; Strips; Foils
  • C25D7/0614—Strips or foils
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B05—SPRAYING OR ATOMISING IN GENERAL; APPLYING FLUENT MATERIALS TO SURFACES, IN GENERAL
  • B05D—PROCESSES FOR APPLYING FLUENT MATERIALS TO SURFACES, IN GENERAL
  • B05D2202/00—Metallic substrate
  • B05D2202/10—Metallic substrate based on Fe
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B05—SPRAYING OR ATOMISING IN GENERAL; APPLYING FLUENT MATERIALS TO SURFACES, IN GENERAL
  • B05D—PROCESSES FOR APPLYING FLUENT MATERIALS TO SURFACES, IN GENERAL
  • B05D2701/00—Coatings being able to withstand changes in the shape of the substrate or to withstand welding
  • B05D2701/10—Coatings being able to withstand changes in the shape of the substrate or to withstand welding withstanding draw and redraw process, punching
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B22—CASTING; POWDER METALLURGY
  • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
  • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
• • 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
  • C21D2251/00—Treating composite or clad material
• • 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
  • Y10T428/26—Web or sheet containing structurally defined element or component, the element or component having a specified physical dimension
  • Y10T428/263—Coating layer not in excess of 5 mils thick or equivalent
• • 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
  • Y10T428/31504—Composite [nonstructural laminate]
  • Y10T428/31678—Of metal

Definitions

• the present invention relates to a high-strength, high-workability steel plate suitable for application to an easy open end steel plate and a method for producing the same.
• steel plates called DR Double Reduce
• steel plates called DR (Double Reduce) materials may be used for lids, bottoms, three-piece can bodies, drawn cans, and the like.
• the DR material manufactured by the DR method in which cold rolling is performed again after annealing is easier to reduce the plate thickness than the SR (Single Reduce) material manufactured only by temper rolling with a small rolling rate. . For this reason, can-making cost can be reduced by using DR material.
• SR Single Reduce
• work hardening occurs by performing cold rolling again after annealing, so that a thin and hard steel plate can be manufactured, but on the other hand, it is inferior in workability as compared with the R material.
• EOE Electronic Open End
• a lid for beverage cans and food cans.
• a steel plate as a can-making material is required to have a strength corresponding to the plate thickness.
• a tensile strength of about 520 MPa or more is required in order to ensure an economic effect by making it thin. Since it is difficult for the conventional DR material to achieve both the workability and strength as described above, the SR material has been used for EOE.
• Patent Document 1 discloses a rivet formability characterized in that the carbon content is 0.02% or less and the boron content is in the range of 0.010 to 0.020%.
• An excellent easy open can lid steel sheet and a method for producing the steel sheet characterized by performing secondary cold rolling at a rolling reduction of 30% or less are disclosed.
• Patent Document 2 discloses a DR material characterized in that the average rankford value after aging treatment is 1.0 or less, and this DR material is excellent in rivet formability of EOE. Is stated.
• the steel sheet described in Patent Document 2 achieves good rivet formability by reducing the average Rankford value.
• this method is effective only when a rivet is formed by a nearly cylindrical projecting process, and when the rivet is formed by a nearly spherical projecting process, the rivet formability becomes insufficient. . Therefore, it has been expected to provide a high-strength and high-workability steel sheet having a tensile strength of 520 MPa or more and an Erichsen value of 5.0 mm or more.
• the present invention has been made in view of the above problems, and its purpose is to provide a high strength and high workability steel sheet having a tensile strength of 520 MPa or more and an Erichsen value of 5.0 mm or more. It is providing the high workability steel plate and its manufacturing method.
• Inventors of the present invention in order to achieve both the workability and strength of the steel sheet, while limiting the carbon content to an appropriate range, while preventing deterioration of workability, It has been found that it is effective to secure the strength by increasing the nitrogen content and to limit the secondary cold rolling rate after annealing to an appropriate range.
• the inventors of the present invention need to limit the coiling temperature to an appropriate temperature range because the cementite deposited becomes coarse and the local elongation decreases when the coiling temperature after hot rolling is high. I found out.
• the inventors of the present invention have found that providing a resin film layer having an appropriate thickness on the side that becomes the inner surface of the can significantly improves the rivet formability by overhanging.
• the high-strength, high-workability steel sheet according to the present invention is, in mass%, C: more than 0.020% and less than 0.040%, Si: 0.003% to 0.100%, Mn: 0.10% to 0 .60% or less, P: 0.001% to 0.100%, S: 0.001% to 0.020%, Al: 0.005% to 0.100%, N: 0.0130% More than 0.0170% is contained, the remainder is made of Fe and inevitable impurities, has a resin film layer on at least the inner surface of the can, has a tensile strength in the rolling direction of 520 MPa or more, and an Erichsen value of 5. It is 0 mm or more.
• the thickness of the resin film layer is in the range of 5 to 100 ⁇ m.
• the manufacturing method of the high-strength, high-workability steel sheet according to the present invention is, in mass%, C: more than 0.020% and less than 0.040%, Si: 0.003% to 0.100%, Mn: 0.10 %: 0.61% or less, P: 0.001% or more and 0.100% or less, S: 0.001% or more and 0.020% or less, Al: 0.005% or more and 0.100% or less, N: 0 .0130% and 0.0170% or less, the balance being Fe and inevitable impurities made into steel as a slab by continuous casting, slab reheating temperature is 1150 ° C or higher and hot rolling is performed at a temperature of 600 ° C or lower , followeded by primary cold rolling, followed by continuous annealing at a soaking temperature of 600 to 700 ° C.
• Hot rolled and surface treated by electrolytic method Paste the resin film on the side where the at least can inner after forming the tensile strength in the rolling direction is not less than 520 MPa, characterized in that to produce a steel sheet Erichsen value is 5.0mm or more.
• a high-strength and highly workable steel sheet having a tensile strength of 520 MPa or more and an Erichsen value of 5.0 mm or more can be obtained.
• cracks do not occur during rivet molding of EOE, and it is possible to make a lid made of a DR material having a thin plate thickness, thereby realizing a significant reduction in the thickness of the EOE steel plate.
• the high-strength, high-workability steel sheet according to the present invention can be applied to an easy open-end steel sheet having a tensile strength of 520 MPa or more and an Erichsen value of 5.0 mm or more.
• Such a steel sheet uses steel containing less than 0.040% carbon, sets the coiling temperature after hot rolling and the secondary cold rolling rate to appropriate conditions, and further becomes the inner surface of the can It becomes possible to manufacture by sticking a resin film on the substrate.
• the component composition of the high-strength, high-workability steel sheet according to the present invention will be described.
• Component composition of high-strength, high-workability steel sheet (1) C: More than 0.020% and less than 0.040%
• the high-strength, high-workability steel sheet according to the present invention exhibits high workability by keeping the C (carbon) content low. If the C content is 0.040% or more, the steel sheet becomes excessively hard, and it becomes impossible to produce a thin steel sheet by secondary cold rolling while ensuring workability. For this reason, the upper limit of the C content is less than 0.040%. On the other hand, if the C content is 0.020% or less, the tensile strength 520 MPa necessary for obtaining a remarkable economic effect due to the thinning of the steel sheet cannot be obtained. For this reason, the lower limit of the C content is over 0.020%.
• Si 0.003% or more and 0.100% or less
• the content of Si silicon
• the upper limit of the Si content is set to 0.100%.
• the refining cost is excessive to make the Si content less than 0.003%.
• the lower limit of the Si content is set to 0.003%.
• a preferable Si content is in the range of 0.003% to 0.035%.
• Mn 0.10% or more and 0.60% or less
• Mn manganese
• S sulfur
• Mn manganese
• Mn has a function of preventing red heat embrittlement during hot rolling due to S (sulfur) and miniaturizing crystal grains. It is an element necessary for securing. In order to exert these effects, it is necessary to add at least 0.10% of Mn.
• the upper limit of the Mn content is set to 0.60%.
• the preferred Mn content is in the range of 0.19% to 0.60%.
• P phosphorus
• the upper limit of the content of P is set to 0.100%.
• dephosphorization cost becomes excessive to make the P content less than 0.001%.
• the lower limit of the P content is 0.001%.
• a preferable P content is in the range of 0.001% to 0.015%.
• S 0.001% or more and 0.020% or less S is a harmful element that exists as an inclusion in steel and causes deterioration of workability and corrosion resistance. For this reason, the upper limit of the S content is 0.020%. On the other hand, desulfurization cost becomes excessive to make the S content less than 0.001%. For this reason, the lower limit of the S content is 0.001%.
• a preferable P content is in the range of 0.007% to 0.014%.
• Al 0.005% or more and 0.100% or less
• Al aluminum
• Al is an element necessary as a deoxidizer during steelmaking.
• the content of Al is small, deoxidation becomes insufficient, inclusions increase, and workability deteriorates. If the Al content is 0.005% or more, it can be considered that deoxidation is sufficiently performed.
• the Al content exceeds 0.100%, the frequency of occurrence of surface defects due to alumina clusters or the like increases. For this reason, content of Al shall be 0.005% or more and 0.100% or less.
• N 0.0130% to 0.0170% or less
• the N (nitrogen) content is increased and the strength is increased. Secure. Since strengthening with N has little influence on the stretchability, it is possible to increase the strength of the steel sheet without impairing the Erichsen value. If the N content is 0.0130% or less, the strength required for the can lid cannot be obtained. On the other hand, when N is added in a large amount, the hot ductility deteriorates and cracking of the slab occurs in continuous casting. For this reason, the upper limit of the content of N is set to 0.0170%.
• Fe iron
• unavoidable impurities may contain component elements generally contained in known steel sheets for welding cans.
• Cr chromium
• Cu copper
• Ni nickel
• Mo molybdenum
• Ti titanium
• Nb niobium
• Zr zirconium
• V vanadium
• Ca calcium
• the tensile strength of the high strength and high workability steel sheet according to the present invention is 520 MPa or more. If the tensile strength is less than 520 MPa, the steel plate cannot be made thin enough to obtain a remarkable economic effect in order to secure the strength of the steel plate as the lid-making material. Therefore, the tensile strength is set to 520 MPa or more.
• the tensile strength can be measured by a metal material tensile test method shown in the document “JIS Z 2241”.
• the Erichsen value of the high strength and high workability steel sheet according to the present invention is 5.0 mm or more. If the Eriksen value is less than 5.0 mm, cracking occurs during rivet forming. Therefore, the Erichsen value is 5.0 mm or more.
• the Erichsen value can be measured by the Eriksen test method shown in the document “JIS Z 2247”.
• the processing mode applied to the steel sheet is an overhanging process, which can be considered as tensile deformation in all directions parallel to the plate surface. In order to evaluate the deformability of the steel sheet with respect to such processing, a test by the same overhanging process is necessary, and it cannot be evaluated by the total elongation value or the Rankford value by a simple uniaxial tensile test.
• Rivet forming is performed by overhanging, and overhanging is applied to the outer surface of the can. For this reason, at the time of a process, a tool contacts the side used as a can inner surface, and deforms a steel plate. The lubricity between the tool and the steel sheet is improved by sandwiching and contacting the resin film between the tool and the steel sheet. Thereby, the uniformity of the overhang process is improved and the occurrence of cracks can be effectively suppressed. In addition, it is more preferable that the resin film is not only sandwiched between the tool and the steel plate but also covered with the resin film, which contributes to corrosion resistance.
• the resin film is not particularly limited, and various thermoplastic resins and thermosetting resins can be used.
• a urethane adhesive an epoxy adhesive, an acid-modified olefin resin adhesive, a copolyamide adhesive, a copolyester adhesive (thickness: 0. 1 to 5.0 ⁇ m) is preferably used.
• a thermosetting paint may be applied to the steel plate side or the resin film side in a thickness range of 0.05 to 2.0 ⁇ m, and this may be used as an adhesive.
• modified epoxy paints such as phenol epoxy and amino-epoxy, vinyl chloride-vinyl acetate copolymer, saponified vinyl chloride-vinyl acetate copolymer, vinyl chloride-vinyl acetate-maleic anhydride copolymer, epoxy-modified- , Epoxyamino-modified, epoxyphenol-modified-vinyl paint or modified vinyl paint, acrylic paint, thermoplastic or thermosetting paint such as synthetic rubber paint such as styrene-butadiene copolymer, or a combination of two or more It may be.
• the thickness of the resin film is preferably in the range of 5 to 100 ⁇ m.
• the thickness of the resin film is less than 5 ⁇ m, the resin film breaks during the overhanging process, and there is a high possibility that the effect is not sufficiently exhibited.
• the thickness of the resin film exceeds 100 ⁇ m, the effect of increasing the deformation amount of the steel sheet is increased, and the steel sheet is easily cracked.
• the high-strength, high-workability steel sheet according to the present invention uses a steel slab having the above composition produced by continuous casting, and after hot rolling with a slab reheating temperature of 1150 ° C. or higher, winding at a temperature of 600 ° C. or lower. And then primary cold rolling, followed by continuous annealing at a soaking temperature of 600 to 700 ° C. and a soaking time of 10 to 50 seconds, and then secondary cold at a rolling rate of 8.0 to 15.0%. After rolling and forming a surface treatment film by an electrolytic method, it is manufactured by sticking a resin film on at least the side that becomes the inner surface of the can.
• the load on the rolling mill is excessive, and it is impossible depending on the equipment capacity.
• the final plate thickness is 0.15 mm
• the primary cold rolling rate as large as 92.5% is required when the plate thickness after hot rolling is 2.0 mm.
• rolling is performed thinner than usual in the hot rolling stage.
• the predetermined finish rolling temperature cannot be obtained.
• the plate thickness before annealing is reduced, when continuous annealing is performed, the possibility of troubles such as breakage and deformation of the steel plate during annealing increases. For these reasons, in the present invention, it is preferable to perform the second cold rolling (secondary cold rolling) after annealing to obtain an ultrathin steel plate.
• the coiling temperature after hot rolling is preferably 600 ° C. or lower, more preferably 550 to 600 ° C.
• the soaking temperature of continuous annealing is less than 600 ° C. or the soaking time is less than 10 seconds, recrystallization becomes insufficient and it is difficult to obtain an Erichsen value of 5.0 mm or more.
• the soaking temperature exceeds 700 ° C. or the soaking time exceeds 50 seconds, grain growth due to recrystallization becomes excessive, and it is difficult to obtain a tensile strength of 520 MPa. Therefore, it is desirable to perform the continuous annealing under conditions of a soaking temperature of 600 to 700 ° C. and a soaking time of 10 to 50 seconds.
• the secondary cold rolling rate exceeds 15.0%, work hardening by secondary cold rolling becomes excessive, and it becomes difficult to obtain an Erichsen value of 5.0 mm or more. Therefore, the secondary cold rolling rate is preferably 15.0% or less. On the other hand, if the secondary cold rolling rate is less than 8.0%, it is difficult to obtain the strength required for the can lid. Therefore, the lower limit of the secondary cold rolling rate is preferably 8.0%.
• a surface treatment film is formed by electrolytic method.
• Sn electroplating film widely used for tin cans and tin-free steel, and electrolytic Cr acid-treated film can be applied. By providing these films, it becomes possible to improve the adhesion between the resin film and the steel sheet.
• a resin film is affixed on at least the inner surface of the can.
• a method of attaching a method of heating a steel plate and thermally fusing a resin film, a method of attaching using an adhesive, and the like are possible.
• Example ⁇ Steel containing the component composition shown in Table 1 and the balance being Fe and inevitable impurities was melted in an actual converter, and a steel slab was obtained by a continuous casting method. After the obtained steel slab was reheated, it was hot rolled under the conditions shown in Table 2. The finish rolling temperature of hot rolling was 880 ° C., and pickling was performed after rolling. Next, after performing primary cold rolling at a rolling rate of 90%, continuous annealing and secondary cold rolling were performed under the conditions shown in Table 2. The steel plate obtained as described above was subjected to electrolytic Cr acid treatment continuously on both sides to obtain tin-free steel with a single-sided Cr deposit of 100 mg / m 2 .
• an isophthalic acid copolymerized polyethylene terephthalate film having a copolymerization ratio of 12 mol% was laminated on both sides to obtain a resin-coated steel sheet.
• Lamination was performed by sandwiching a steel plate and a film heated to 245 ° C. between a pair of rubber rolls, fusing the film to a metal plate, and cooling with water within 1 second after passing through the rubber roll.
• the feeding speed of the steel plate was 40 m / min
• the nip length of the rubber roll was 17 mm.
• the nip length is the length in the conveying direction of the portion where the rubber roll and the steel plate are in contact. Table 1 shows the thickness of the film layer.
• a tensile test was performed on the resin-coated steel sheet obtained as described above.
• the tensile strength (tensile strength) was measured using a tensile test piece of JIS No. 5 size according to the metal material tensile test method shown in the document “JIS Z 2241”.
• the Erichsen test was done with respect to the obtained resin-coated steel plate.
• the Eriksen test according to the Eriksen test method shown in the document “JIS Z 2247”, the Eriksen value (the overhang height at which through cracking occurs) was measured using a 90 mm ⁇ 90 mm test piece.
• the rivet for EOE tab attachment was shape
• Rivet forming was performed by three-stage press work, and after the overhanging process, a diameter reduction process was performed to form a spherical head rivet having a diameter of 4.0 mm and a height of 2.5 mm.
• the case where cracks occurred at the rivet part was evaluated as x
• the case where necking in the thickness direction before cracking occurred was evaluated as ⁇
• the case where cracking or necking in the thickness direction did not occur was evaluated as ⁇ .
• the obtained results are shown in Table 3.
• the invention example No. The steel plates 1 to 6 are excellent in strength, and have achieved a tensile strength of 520 MPa or more necessary as an ultrathin steel plate for cans. Moreover, it is excellent in workability and has an Erichsen value of 5.0 mm or more necessary for EOE processing. Further, even when rivet forming is performed, neither cracking nor thickness constriction occurs. In contrast, No. of the comparative example.
• Each of the steel sheets Nos. 7 and 9 has insufficient tensile strength because the contents of C and N are too small. Since the steel sheet of Comparative Example 8 has too much C, the workability is impaired by secondary cold rolling, the Erichsen value is insufficient, and cracking occurs in rivet forming.
• the comparative example No. Since the steel plate No. 10 has too much N content, slab cracking occurs in continuous casting. Moreover, No. of the comparative example. Steel sheet No. 11 has a coiling temperature after hot rolling that is too high, resulting in a decrease in local elongation, resulting in a lack of Erichsen value and cracking in rivet forming. Moreover, No. of the comparative example. The steel plate No. 12 has a low soaking temperature in continuous annealing, so that recrystallization is insufficient, the Eriksen value is insufficient, and cracking occurs in rivet forming. Moreover, No. of the comparative example. In No.
• Comparative Example No. No. 14 steel plate has insufficient recrystallization because the soaking time in continuous annealing is too short, the Eriksen value is insufficient, and cracking occurs in rivet forming.
• Comparative Example No. No. 16 steel plate has insufficient tensile strength because the secondary cold rolling rate is too small.
• the comparative example No. In No. 18, the thickness of the resin film coated on the surface of the steel plate is too thin, so that the effect is not sufficiently exhibited in the rivet forming, and a constriction crack in the thickness direction before cracking occurs.
• the thickness of the resin film coated on the surface of the steel plate is too thick, so that the deformation amount of the steel plate is increased in rivet forming, and a constriction crack in the thickness direction before cracking occurs.

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• 2013
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