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
  • C21D8/0247—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
• • 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
• • 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 and high formability steel sheet suitable for application to a steel sheet for easy open ends, and a manufacturing method thereof.
• a steel sheet referred to as a double reduced (DR) material may be used for lids, bottoms, bodies of three-pieced cans, drawn cans, or the like.
• DR double reduced
• SR single reduced
• the cold rolling performed again after annealing causes work hardening, and thus although a thin and hard steel sheet can be manufactured, its formability is less than an R material.
• EOEs easy open ends
• steel sheets as materials for manufacturing cans are required to have strengths according to sheet thicknesses, and as for the DR material, a tensile strength of not lower than about 520 MPa is necessary to ensure an economic effect due to thinning thereof. It is difficult to ensure for conventional DR materials both of formability and strength as mentioned above and thus the SR material has been used for EOEs.
• demands for applying the DR material to EOEs also are currently increasing in terms of cost reduction.
• Patent Literature 1 discloses a steel sheet for easy open cans lids excellent in rivet formability, characterized in that its carbon content is not greater than 0.02% and its boron content is in a range of 0.010 to 0.020%, and a manufacturing method thereof, characterized in that second cold rolling is performed with a rolling reduction ratio of not greater than 30%.
• Patent Literature 2 discloses a DR material characterized in that its average Lankford value after an aging treatment is not greater than 1.0, and describes that the DR material is excellent in EOE rivet formability.
• Patent Literature 2 achieves the good rivet formability by reducing the average Lankford value.
• this method exerts its effects only when a rivet is formed by column-like bulging, and when a rivet is formed by sphere-like bulging, the rivet formability becomes insufficient. Therefore, provision of a high strength and high formability steel sheet having a tensile strength of not lower than 520 MPa and an Erichsen value of not less than 5.0 mm has been desired.
• the present invention has been made in view of the above problems, and its object is to provide a high strength and high formability steel sheet and a manufacturing method thereof, which are able to provide a high strength and high formability steel sheet having a tensile strength of not lower than 520 MPa and an Erichsen value of not less than 5.0 mm.
• the inventors of the present invention have found that it is effective, for achieving both formability and strength of a steel sheet, to ensure strength by increasing a nitrogen content while preventing deterioration of formability by restricting a carbon content to an appropriate range, and to restrict a second cold rolling reduction ratio after annealing to an appropriate range. Moreover, the inventors of the present invention have found that it is necessary to restrict also a coiling temperature to an appropriate range because, when the coiling temperature after hot rolling is high, precipitated cementite becomes coarse and local elongation deteriorates. Furthermore, the inventors of the present invention have found that rivet formability by bulging is remarkably improved by providing a resin film layer having an appropriate thickness on a side to be an inner surface of a can.
• a high strength and high formability steel sheet according to the present invention includes, in mass%: greater than 0.020% and less than 0.040% of C; not less than 0.003% and not greater than 0.100% of Si; not less than 0.10% and not greater than 0.60% of Mn; not less than 0.001% and not greater than 0.100% of P; not less than 0.001% and not greater than 0.020% of S; not less than 0.005% and not greater than 0.100% of Al; greater than 0.0130% and not greater than 0.0170% of N; and a remainder being Fe and inevitable impurities, wherein the high strength and high formability steel sheet has: a resin film layer at least on a side to be an inner surface of a can; a tensile strength in a rolling direction of not less than 520 MPa; and an Erichsen value of not less than 5.0 mm.
• a thickness of the resin film layer is preferably in a range of 5 to 100 ⁇ m.
• a method of manufacturing a high strength and high formability steel sheet according to the present invention includes: forming a slab by continuously casting a steel including, in mass%: greater than 0.020% and less than 0.040% of C; not less than 0.003% and not greater than 0.100% of Si; not less than 0.10% and not greater than 0.60% of Mn; not less than 0.001% and not greater than 0.100% of P; not less than 0.001% and not greater than 0.020% of S; not less than 0.005% and not greater than 0.100% of Al; greater than 0.0130% and not greater than 0.0170% of N; and a remainder being Fe and inevitable impurities; performing hot rolling at a slab reheating temperature of not lower than 1150°C; coiling at a temperature of not higher than 600°C; thereafter performing first cold rolling; thereafter performing continuous annealing at a soaking temperature of 600 to 700°C for a soaking period of 10 to 50 seconds; thereafter performing second cold rolling at a reduction ratio of 8.0 to 15.0%; attaching a
• the high strength and high formability steel sheet and the manufacturing method thereof of the present invention it is possible to obtain a high strength and high formability steel sheet having a tensile strength of not lower than 520 MPa and an Erichsen value of not less than 5.0 mm. Further, as a result, it is possible to manufacture a lid with a DR material having a small thickness, without cracking upon EOE rivet formation, and thus to achieve thinning of a steel sheet for EOEs to a great extent.
• the high strength and high formability steel sheet of the present invention can be applied to a steel sheet for easy open ends having tensile strength of not lower than 520 MPa and an Erichsen value of not less than 5.0 mm.
• a steel sheet can be manufactured with steel having carbon content of less than 0.040%, by setting a coiling temperature after hot rolling and a second cold rolling reduction ratio to appropriate conditions, and attaching a resin film on a side to become an inner surface of a can.
• the component composition of the high strength and high formability steel sheet of the present invention is described.
• the high strength and high formability steel sheet of the present invention exerts high formability by suppressing carbon (C) content to small.
• C content When the C content is not less than 0.040%, a steel sheet becomes excessively hard, thus making it impossible to manufacture a thin steel sheet by second cold rolling while ensuring formability.
• the upper limit of C content is set to be less than 0.040%.
• the tensile strength of 520 MPa that is required to obtain significant economic effects resulted by thinning of a steel sheet cannot be obtained.
• the lower limit of C content is set to exceed more than 0.020%.
• the silicon (Si) content exceeds 0.100%, there occur problems of deterioration of surface treatability, deterioration of corrosion resistance, etc.
• the upper limit of Si content is 0.100%.
• the lower limit of Si content is set to be 0.003%.
• the preferable Si content is in a range of not less than 0.003% and not greater than 0.035%.
• Manganese (Mn) has functions of preventing red shortness during hot rolling due to sulfur (S) and of refining crystal grains, and is an element necessary for ensuring the desirable quality of a material.
• S sulfur
• Mn has functions of preventing red shortness during hot rolling due to sulfur (S) and of refining crystal grains, and is an element necessary for ensuring the desirable quality of a material.
• the addition of at least 0.10% or more of Mn is required in order to exert such effects.
• the upper limit of Mn amount is therefore set to be 0.60%.
• the preferable Mn content is in a range of not less than 0.19% and not greater than 0.60%.
• Phosphorus (P) is a harmful element that hardens steel, and deteriorates formability, and in addition, deteriorates also corrosion resistance.
• the upper limit of P content is set to be 0.100%.
• the lower limit of P content is therefore set to be 0.001%.
• the preferable P content is in a range of not less than 0.001% and not greater than 0.015%.
• S exists as inclusions in steel, and is a harmful element causing deterioration of formability and deterioration of corrosion resistance.
• the upper limit of S content is therefore set to be 0.020%.
• the S content is set to be less than 0.001%, the cost for desulfurization becomes excessively high.
• the lower limit of S content is therefore set to be 0.001%.
• the preferable P content is in a range of not less than 0.007% and not greater than 0.014%.
• Aluminum (Al) is an element necessary as deoxidizer in a steelmaking process.
• Al content is small, deoxidation is insufficient, and inclusions increase, thus deteriorating formability.
• the Al content is not less than 0.005%, it can be considered that deoxidation is performed sufficiently.
• the Al content exceeds 0.100%, the frequency of occurrence of surface defects due to alumina clusters, etc. is increased.
• the Al content is therefore set to be not less than 0.005% and not greater than 0.100%.
• N Greater than 0.0130% and not greater than 0.0170%
• N content is increased, instead of reducing C content, to ensure strength.
• the strengthening using N has small effects on bulging formability, and thus it is possible to strengthen a steel sheet without deteriorating an Erichsen value.
• N content is not greater than 0.0130%, the strength necessary for a can lid cannot be obtained.
• the upper limit of N content is therefore set to be 0.0170%.
• the balance other than the components described above is iron (Fe) and inevitable impurities, and may include component elements normally contained in a known steel sheet for welded cans.
• the component elements such as chromium (Cr): not greater than 0.10%, copper (Cu): not greater than 0.20%, nickel (Ni): not greater than 0.15%, molybdenum (Mo): not greater than 0.05%, titanium (Ti): not greater than 0.3%, niobium (Nb): not greater than 0.3%, zirconium (Zr): not greater than 0.3%, vanadium (V): not greater than 0.3%, calcium (Ca): not greater than 0.01%, may be contained depending on a purpose.
• the tensile strength of the high strength and high formability steel sheet of the present invention is set to be not lower than 520 MPa.
• the tensile strength is therefore set to be not lower than 520 MPa.
• the above tensile strength can be measured by Metallic materials-Tensile testing defined in the document "JIS Z 2241".
• the Erichsen value of the high strength and high formability steel sheet of the present invention is set to be not less than 5.0 mm.
• the Erichsen value can be measured by Method of Erichsen cupping test defined in the document "JIS Z 2247".
• JIS Z 2247 Method of Erichsen cupping test defined in the document "JIS Z 2247".
• the processing form applied on a steel sheet is bulging, which can be regarded as tensile deformation toward all directions parallel to a sheet surface.
• the evaluation of deformability of a steel sheet by such processing requires a test by similar bulging, and the deformability cannot be evaluated with a total elongation value or a Lankford value by the simple uniaxial tensile testing.
• the rivet formation is performed by bulging, and processing for bulging toward the outer side of a can is performed.
• a steel sheet is deformed by a tool contacting with the inner side surface of the can.
• the lubricating ability between a tool and a steel sheet is improved by contacting them with a resin film interposed therebetween.
• the uniformity of bulging is improved, suppressing the occurrence of a crack effectively.
• a surface of a steel sheet be coated with a resin film in addition to interposing a resin film between a tool and a steel sheet, because those contribute to corrosion resistance.
• a resin film is not particularly limited, and various thermoplastic resins and thermosetting resins can be used.
• an olefin resin film such as of polyethylene, polypropylene, ethylenepropylene copolymer, ethylene-vinyl acetate copolymer, ethylene-acrylic ester copolymer, and ionomer, or a polyester film such as of polybutylene terephthalate, or a thermoplastic resin film including a polyamide film such as of nylon 6, nylon 6-6, nylon 11, and nylon 12, a polyvinylchloride film, and a polyvinylidene chloride film without stretching them or by stretching them biaxially.
• an adhesive When an adhesive is used to attach a resin film on a steel sheet, an urethane adhesive, an epoxy adhesive, an acid-modified olefin resin adhesive, a copolyamide adhesive, a copolyester adhesive (thickness: 0.1 to 5.0 ⁇ m), etc. are used preferably. Moreover, thermosetting coating is applied on the steel sheet side or the resin film side with a thickness in a range of 0.05 to 2.0 ⁇ m, and this may be regarded as an adhesive.
• thermoplastic or thermosetting coating including modified epoxy coating such as of phenol epoxy and amino-epoxy, vinyl chloride-vinyl acetate copolymer, vinyl chloride acetate saponified copolymer, vinyl chloride-vinyl acetate-maleic anhydride copolymer, epoxy modified-, epoxy amino modified-, epoxy phenol modified-vinyl coating or modified vinyl coating, acryl coating, and a synthetic rubber coating such as of styrene-butadiene copolymer may be used individually or in combination of two or more thereof.
• modified epoxy coating such as of phenol epoxy and amino-epoxy
• vinyl chloride-vinyl acetate copolymer vinyl chloride acetate saponified copolymer
• vinyl chloride-vinyl acetate-maleic anhydride copolymer epoxy modified-, epoxy amino modified-, epoxy phenol modified-vinyl coating or modified vinyl coating
• acryl coating and a synthetic rubber coating such as of styrene-butadiene copo
• the thickness of a resin film is preferably set to be in a range of 5 to 100 ⁇ m.
• the thickness of a resin film is smaller than 5 ⁇ m, the resin film is fractured in bulging, and it is more possible that the effects are not exerted sufficiently.
• the thickness of a resin film exceeds 100 ⁇ m, the effect of increasing a deformation amount of a steel sheet becomes greater, and a crack of the steel sheet will occur more easily.
• the high strength and high formability steel sheet of the present invention is manufactured, with use of a steel slab having the above composition manufactured by continuous casting, by performing hot rolling at a slab reheating temperature of not lower than 1150°C, coiling it at a temperature of not higher than 600°C, performing first cold rolling, performing continuous annealing at a soaking temperature of 600 to 700°C for a soaking period of 10 to 50 seconds, performing second cold rolling with a reduction ratio of 8.0 to 15.0%, forming a surface treatment film by an electrolytic process, and then attaching a resin film at least on a side to become an inner surface of a can.
• the cold rolling for the second time (second cold rolling) be performed after annealing to obtain an ultrathin steel sheet.
• the coiling temperature after hot rolling is therefore preferably not higher than 600°C, and is more preferably in a range of 550 to 600°C.
• the continuous annealing is therefore preferably performed under conditions of a soaking temperature of 600 to 700°C and a soaking period of 10 to 50 seconds.
• the second cold rolling reduction ratio is therefore preferably not greater than 15.0%.
• the lower limit of the second cold rolling reduction ratio is preferably 8.0%.
• a surface treatment film is formed by an electrolytic process.
• a Sn electroplating film, an electrolytic Cr acid treatment film, or the like which is widely used for a can lid as a tin plate or tin-free steel, can be applied.
• the adherence between a resin film and a steel sheet can be improved by providing such a film.
• the attachment method can be a method of heating a steel sheet and heat-sealing a resin film, or a method of attaching it using an adhesive.
• a steel slab was obtained by melting steel having the component compositions illustrated in Table 1 and the balance including Fe and inevitable impurities in an actual converter and subjecting it to continuous casting.
• the obtained steel slab was heated again, and subjected to hot rolling under the conditions illustrated in Table 2.
• a finish rolling temperature of hot rolling was set to be 880°C, and pickling was performed after the rolling.
• first cold rolling was performed with a reduction ratio of 90%
• continuous annealing and second cold rolling were performed under the conditions illustrated in Table 2.
• the electrolytic Cr acid treatment was continuously performed on the both surfaces of the steel sheet obtained in the above manner, whereby tin-free steel having a Cr coating build-up per side of 100 mg/m 2 was obtained.
• an isophthalic acid copolymerized polyethylene terephthalate film having a copolymerization ratio of 12 mol% was laminated on the both surfaces, and thus a resin coated steel sheet was obtained.
• the laminating was performed in such a manner that a steel sheet heated to 245°C and a film were nipped by a pair of rubber covered rolls so that the film was fused to the metallic sheet, and the laminate was cooled with water within one second after it passed the rubber covered rolls.
• a feed rate of the steel sheet was 40 m/min
• the nip length of the rubber covered rolls was 17 mm.
• the nip length is a length in a feed direction of a part where the rubber covered rolls and the steel sheet are in contact.
• the resin coated steel sheet obtained as described above was subjected to tensile testing.
• the tensile testing conforms to Metallic materials-Tensile testing defined in the document "JIS Z 2241", and strength of tension (tensile strength) was measured using a test piece for tensile testing having a size of JIS5.
• the obtained resin coated steel sheet was subjected to Erichsen test.
• the Erichsen test conforms to Method of Erichsen cupping test defined in the document "JIS Z 2247”, and an Erichsen value (a bulging height at which a penetration crack occurred) was measured using a test piece of 90 mm x 90 mm.
• a rivet for attaching an EOE tab was formed using the obtained resin coated steel sheet, and the rivet formability was evaluated.
• the rivet formation was performed by three phases of press working, and processing for reducing a diameter was performed after bulging to form a spherical-head-formed rivet having a diameter of 4.0 mm and a height of 2.5 mm.
• Occurrence of a crack in a rivet portion was evaluated as "C”
• occurrence of necking in a thickness direction which is a previous stage leading to a crack
• B no occurrence of a crack or necking in a thickness direction was evaluated as "A”.
• the steel sheets of Inventive Examples No. 1 to No. 6 are excellent in strength, and achieve tensile strength of not lower than 520 MPa that is required as an ultrathin steel sheet for cans. Moreover, they are also excellent in formability, and have an Erichsen value of not less than 5.0 mm that is required in EOE processing. Furthermore, even if the rivet formation is performed, no crack or necking in a thickness direction occurs.
• each of the steel sheets of Comparative Examples No. 7 and No. 9 has such small C and N content that they are lacking in tensile strength.
• the steel sheet of Comparative Example No. 8 has such large C content that the formability is deteriorated by second cold rolling, resulting in the lack in Erichsen value and thus causing a crack in rivet formation.
• the steel sheet of Comparative Example No. 10 has such large N content that a slab crack has occurred in continuous casting.
• the local elongation deteriorates because the coiling temperature after hot rolling is too high, resulting in the lack in Erichsen value and thus causing a crack in rivet formation.
• the steel sheet of Comparative Example No. 12 recrystallization is insufficient because the soaking temperature in continuous annealing is too low, resulting in the lack in Erichsen value and thus causing a crack in rivet formation.
• grain growth is excessive because the soaking temperature in continuous annealing is too high, resulting in the lack in tensile strength.
• recrystallization is insufficient because the soaking period in continuous annealing is too short, resulting in the lack in Erichsen value and thus causing a crack in rivet formation.
• the thickness of the resin film coating the surface of the steel sheet is too thin, and thus the effects thereof are not sufficiently exerted in rivet formation, causing a necking crack in a thickness direction before leading to a crack.
• the thickness of the resin film coating the surface of the steel sheet is too thick, and thus the deformation amount of the steel sheet is increased in rivet formation, causing a necking crack in a thickness direction before leading to a crack.

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• 2013
  • 2013-04-03 CN CN201380017624.8A patent/CN104245985B/zh active Active
  • 2013-04-03 EP EP13773084.2A patent/EP2835438B1/fr active Active
  • 2013-04-03 US US14/382,363 patent/US20150064448A1/en not_active Abandoned
  • 2013-04-03 JP JP2014509184A patent/JP5804195B2/ja active Active
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• 2014
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