EP2835438A1 - High-strength, highly workable steel sheet, and method for manufacturing same - Google Patents

High-strength, highly workable steel sheet, and method for manufacturing same Download PDF

Info

Publication number
EP2835438A1
EP2835438A1 EP20130773084 EP13773084A EP2835438A1 EP 2835438 A1 EP2835438 A1 EP 2835438A1 EP 20130773084 EP20130773084 EP 20130773084 EP 13773084 A EP13773084 A EP 13773084A EP 2835438 A1 EP2835438 A1 EP 2835438A1
Authority
EP
European Patent Office
Prior art keywords
less
steel sheet
strength
resin film
formability
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP20130773084
Other languages
German (de)
French (fr)
Other versions
EP2835438A4 (en
EP2835438B1 (en
Inventor
Takumi Tanaka
Katsumi Kojima
Yoichi Tobiyama
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by JFE Steel Corp filed Critical JFE Steel Corp
Publication of EP2835438A1 publication Critical patent/EP2835438A1/en
Publication of EP2835438A4 publication Critical patent/EP2835438A4/en
Application granted granted Critical
Publication of EP2835438B1 publication Critical patent/EP2835438B1/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

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.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Electrochemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Laminated Bodies (AREA)

Abstract

A high strength and high formability steel sheet contains, by mass% of the steel sheet: 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; and greater than 0.0130% and not greater than 0.0170% of N, wherein a remainder is Fe and inevitable impurities, and the steel sheet has: a tensile strength in a rolling direction of not lower than 520 MPa; an Erichsen value of not less than 5.0 mm; and a resin film layer at least on a side to be an inner surface of a can.

Description

    Field
  • 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.
    • Background
  • Among steel sheets used for beverage cans or food cans, 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. With the DR material manufactured by a DR method of performing cold rolling again after annealing, a sheet thickness can be made thin more easily than with a single reduced (SR) material manufactured only by temper rolling at a small reduction ratio. Thus, it is possible, using the DR material, to reduce costs for manufacturing cans. In the DR method, 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.
  • As lids of beverage cans and food cans, easy open ends (EOEs) that can be opened easily are widely used. In manufacturing an EOE, it is necessary to form, by bulging, a rivet for attaching a tab with which a finger is engaged. 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. However, demands for applying the DR material to EOEs also are currently increasing in terms of cost reduction.
  • Due to such background, 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%. Moreover, 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.
    • Citation List Patent Literature
    • Patent Literature 1: Japanese Patent No. 3740779
    • Patent Literature 2: WO 2008/018531
    Summary Technical Problem
  • However, the conventional techniques described above have problems. As a diameter of a can lid to be applied becomes greater, a greater strength is required for a steel sheet, but since the steel sheet described in Patent Literature 1 has the small carbon content, the nitrogen content needs to be large to obtain a large strength. However, because the steel sheet contains at least a certain amount of boron, when the nitrogen content is large, its ductility at a high temperature becomes small and a slab crack is caused upon continuous casting. Therefore, the steel sheet described in Patent Literature 1 cannot be applied to an EOE having a large diameter.
  • The steel sheet described in Patent Literature 2 achieves the good rivet formability by reducing the average Lankford value. However, 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.
    • Solution to Problem
  • As a result of diligently performing intensive studies, 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 µm.
  • 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 resin film at least on a side to be an inner surface of a can after forming a surface treatment film by an electrolytic process; and manufacturing a steel sheet having a tensile strength in a rolling direction of not less than 520 MPa and an Erichsen value of not less than 5.0 mm.
    • Advantageous Effects of Invention
  • According to 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.
    • Description of Embodiments
  • In the following, the present invention is described in detail.
  • 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. Such 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. In the following, the component composition of the high strength and high formability steel sheet of the present invention is described.
    • Component Composition of High Strength and High Formability Steel Sheet (1) C: Greater than 0.020% and less than 0.040%
  • The high strength and high formability steel sheet of the present invention exerts high formability by suppressing carbon (C) content to small. 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. Thus, the upper limit of C content is set to be less than 0.040%. However, when the C content is not greater than 0.020%, the tensile strength of 520 MPa that is required to obtain significant economic effects resulted by thinning of a steel sheet cannot be obtained. Thus, the lower limit of C content is set to exceed more than 0.020%.
    • (2) Si: Not less than 0.003% and not greater than 0.100%
  • When the silicon (Si) content exceeds 0.100%, there occur problems of deterioration of surface treatability, deterioration of corrosion resistance, etc. Thus, the upper limit of Si content is 0.100%. When Si content is set to be less than 0.003%, refining cost is excessively high. Therefore, 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%.
    • (3) Mn: Not less than 0.10% and not greater than 0.60%
  • 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. The addition of at least 0.10% or more of Mn is required in order to exert such effects. However, when an excessive amount of Mn is added, the corrosion resistance deteriorates and a steel sheet becomes excessively hard. 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%.
    • (4) P: Not less than 0.001% and not greater than 0.100%
  • Phosphorus (P) is a harmful element that hardens steel, and deteriorates formability, and in addition, deteriorates also corrosion resistance. Thus, the upper limit of P content is set to be 0.100%. However, when the P content is set to be less than 0.001%, the cost for dephosphorization becomes excessively high. 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%.
    • (5) S: Not less than 0.001% and not greater than 0.020%
  • 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%. When 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%.
    • (6) Al: Not less than 0.005% and not greater than 0.100%
  • Aluminum (Al) is an element necessary as deoxidizer in a steelmaking process. When the Al content is small, deoxidation is insufficient, and inclusions increase, thus deteriorating formability. When the Al content is not less than 0.005%, it can be considered that deoxidation is performed sufficiently. However, when 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%.
    • (7) N: Greater than 0.0130% and not greater than 0.0170%
  • In the high strength and high formability steel sheet of the present invention, nitrogen (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. When N content is not greater than 0.0130%, the strength necessary for a can lid cannot be obtained. However, when a large amount of N is added, the hot ductility deteriorates, thus causing a slab crack in continuous casting. The upper limit of N content is therefore set to be 0.0170%.
    • (8) Other components
  • 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. For example, 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.
    • Characteristics of High Strength and High Formability Steel Sheet
  • Next, the mechanical characteristics of the high strength and high formability steel sheet of the present invention are described.
  • 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. When the tensile strength is lower than 520 MPa, a steel sheet cannot be made thin enough to obtain significant economic effects, in order to ensure the strength of the steel sheet as a material for manufacturing lids. 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. When the Erichsen value is smaller than 5.0 mm, a crack occurs in rivet formation. The Erichsen value is therefore 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". In the rivet formation, 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.
    • Surface Coating of High Strength and High Formability Steel Sheet
  • Next, the surface coating of the high strength and high formability steel sheet of the present invention is described.
  • The rivet formation is performed by bulging, and processing for bulging toward the outer side of a can is performed. In the processing, therefore, 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. Thus, the uniformity of bulging is improved, suppressing the occurrence of a crack effectively. It is more preferable that 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. For example, there may 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.
  • 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 µm), 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 µm, and this may be regarded as an adhesive. Moreover, 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.
  • The thickness of a resin film is preferably set to be in a range of 5 to 100 µm. When the thickness of a resin film is smaller than 5 µm, the resin film is fractured in bulging, and it is more possible that the effects are not exerted sufficiently. When the thickness of a resin film exceeds 100 µm, the effect of increasing a deformation amount of a steel sheet becomes greater, and a crack of the steel sheet will occur more easily.
    • Manufacturing Method of High Strength and High Formability Steel Sheet
  • Next, the manufacturing method 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 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.
  • It is normally difficult, with only one-time cold rolling, to make a sheet thin enough to obtain significant economic effects. That is, in order to obtain a thin sheet with one-time cold rolling, the load on a mill becomes too high, and it is impossible to achieve it depending on a plant capacity. For example, when a final sheet thickness is made 0.15 mm, the first cold reduction ratio of as much as 92.5% is required if a sheet thickness after hot rolling is 2.0 mm. It can be also considered that a sheet is rolled to be thinner than usual at the step of hot rolling to reduce a sheet thickness after cold rolling. However, when the reduction ratio in hot rolling is increased, the reduction of a temperature of a steel sheet during rolling becomes great, and a given finish rolling temperature cannot be obtained. Moreover, when continuous annealing is performed, the possibility of the occurrence of troubles such as fracture or deformation of a steel sheet during annealing becomes higher if a sheet thickness before annealing is set to be small. For these reasons, it is preferable in the present invention that the cold rolling for the second time (second cold rolling) be performed after annealing to obtain an ultrathin steel sheet.
  • When a coiling temperature after hot rolling exceeds 600°C, a pearlite structure to be formed becomes coarse, which is a starting point of brittle fracture and thus reduces local elongation, making it difficult to obtain an Erichsen value of not less than 5.0 mm. 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.
  • When the soaking temperature of continuous annealing is lower than 600°C or the soaking period thereof is shorter than 10 seconds, recrystallization is insufficient, thus making it difficult to obtain an Erichsen value of not less than 5.0 mm. However, when the soaking temperature exceeds 700°C or the soaking period exceeds 50 seconds, the grain growth through recrystallization becomes excessive, thus making it difficult to obtain the tensile strength of 520 MPa. 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.
  • When the second cold rolling reduction ratio exceeds 15.0%, work hardening by the second cold rolling becomes excessive, thus making it difficult to obtain an Erichsen value of not less than 5.0 mm. The second cold rolling reduction ratio is therefore preferably not greater than 15.0%. However, when the second cold rolling reduction ratio is less than 8.0%, it is difficult to obtain strength necessary for a can lid. Thus, the lower limit of the second cold rolling reduction ratio is preferably 8.0%.
  • After the second cold rolling, a surface treatment film is formed by an electrolytic process. As a film, 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.
  • After the surface treatment film is formed, a resin film is attached at least on a side to become an inner surface of a can. 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.
    • Examples
  • 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. Next, after 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/m2 was obtained. Then, 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. Here, a feed rate of the steel sheet was 40 m/min, and 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 thickness of film layers was listed in Table 1. Table 1
    No. Component composition (mass%) Thickness of resin film layer (µm)
    C Si Mn P S Al N
    1 0.031 0.011 0.29 0.009 0.010 0.039 0.0153 18
    2 0.021 0.010 0.23 0.010 0.012 0.018 0.0161 24
    3 0.039 0.012 0.25 0.009 0.010 0.025 0.0140 15
    4 0.026 0.008 0.28 0.012 0.008 0.042 0.0170 5
    5 0.035 0.009 0.30 0.013 0.011 0.048 0.0131 51
    6 0.029 0.010 0.19 0.010 0.012 0.041 0.0148 100
    7 0.020 0.011 0.26 0.011 0.009 0.040 0.0152 30
    8 0.040 0.013 0.25 0.010 0.010 0.051 0.0160 29
    9 0.032 0.012 0.27 0.009 0.011 0.044 0.0130 19
    10 0.028 0.010 0.22 0.012 0.010 0.038 0.0175 -
    11 0.035 0.014 0.27 0.010 0.009 0.033 0.0162 20
    12 0.029 0.011 0.25 0.011 0.012 0.054 0.0159 36
    13 0.030 0.009 0.24 0.013 0.014 0.064 0.0141 14
    14 0.031 0.008 0.21 0.010 0.010 0.050 0.0135 27
    15 0.022 0.010 0.30 0.012 0.011 0.042 0.0155 43
    16 0.026 0.012 0.28 0.008 0.012 0.040 0.0152 26
    17 0.033 0.011 0.25 0.010 0.009 0.034 0.0143 39
    18 0.037 0.010 0.31 0.011 0.010 0.032 0.0148 3
    19 0.034 0.013 0.24 0.009 0.013 0.041 0.0151 112
    *Due to occurrence of slab crack in steel sheet No. 10 in continuous casting, operations thereafter were not performed.
    Table 2
    No. Hot rolling coiling temperature (°C) Continuous annealing soaking temperature (°C) Continuous annealing soaking period (second) Second cold rolling reduction ratio (%)
    1 582 668 21 11.5
    2 589 685 21 9.8
    3 575 698 10 8.3
    4 598 621 23 10.6
    5 552 605 49 14.9
    6 563 654 22 12.7
    7 584 620 23 13.1
    8 571 683 21 11.1
    9 591 667 21 10.9
    10 - - - -
    11 604 644 22 9.2
    12 585 598 24 12.2
    13 587 703 15 14.0
    14 592 683 9 12.5
    15 566 672 52 10.3
    16 570 658 22 7.8
    17 581 631 23 15.5
    18 590 689 21 13.3
    19 588 690 21 10.1
    *Due to occurrence of slab crack in steel sheet No. 10 in continuous casting, operations thereafter were not performed.
  • 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. Moreover, 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. Furthermore, 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, was evaluated as "B", and no occurrence of a crack or necking in a thickness direction was evaluated as "A". The obtained results are listed in Table 3. Table 3
    No. Tensile strength (MPa) Erichsen value (mm) Rivet formability
    1 552 6.9 A Inventive Example
    2 535 7.4 A Inventive Example
    3 523 7.6 A Inventive Example
    4 539 7.0 A Inventive Example
    5 591 5.2 A Inventive Example
    6 557 6.5 A Inventive Example
    7 516 6.2 A Comparative Example
    8 592 4.8 C Comparative Example
    9 517 7.3 A Comparative Example
    10 - - - Comparative Example
    11 532 4.2 C Comparative Example
    12 595 4.8 C Comparative Example
    13 512 6.1 A Comparative Example
    14 603 4.9 C Comparative Example
    15 515 7.2 A Comparative Example
    16 517 7.9 A Comparative Example
    17 599 4.9 C Comparative Example
    18 564 6.0 B Inventive Examples of Claims 1 and 3 Comparative Example of Claim 2
    19 538 7.3 B Inventive Examples of Claims 1 and 3 Comparative Example of Claim 2
    *Due to occurrence of slab crack in steel sheet No. 10 in continuous casting, operations thereafter were not performed.
  • As listed in Table 3, 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. By contrast, 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. Regarding the steel sheet of Comparative Example No. 11, 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. Regarding 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. Regarding the steel sheet of Comparative Example No. 13, grain growth is excessive because the soaking temperature in continuous annealing is too high, resulting in the lack in tensile strength. Regarding the steel sheet of Comparative Example No. 14, 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.
  • Regarding the steel sheet of Comparative Example No. 15, grain growth is excessive because the soaking period in continuous annealing is too long, resulting in the lack in tensile strength. The steel sheet of Comparative Example No. 16 is lacking in tensile strength because the second cold rolling reduction ratio is too small. Regarding the steel sheet of Comparative Example No. 17, work hardening becomes excessive because the second cold rolling reduction ratio is too high, resulting in the lack in Erichsen value and thus causing a crack in rivet formation. Regarding the steel sheet of No. 18 that is Inventive Example of claims 1 and 3 and is Comparative Example of claim 2, 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. Regarding the steel sheet of No. 19 that is Inventive Example of claims 1 and 3 and is Comparative Example of claim 2, 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.
  • Based on the above, it was confirmed that according to the steel sheets of the inventive examples, it is possible to obtain a high strength and high formability steel sheet having tensile strength of not lower than 520 MPa and an Erichsen value of not less than 5.0 mm.
  • The embodiments to which the present invention made by the inventors are applied have been described. However, the present invention is not limited by the description and the drawings that form a part of the disclosure of the present invention in the embodiments. That is, other embodiments, examples, and operation technologies that are made based on the present embodiments by a person skilled in the art, etc. are all included in the scope of the present invention.
    • Industrial Applicability
  • According to the present invention, it is possible to provide a high strength and high formability steel sheet having tensile strength of not lower than 520 MPa and an Erichsen value of not less than 5.0 mm.

Claims (3)

  1. A high strength and high formability steel sheet, comprising, 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.
  2. The high strength and high formability steel sheet according to claim 1, wherein a thickness of the resin film layer is in a range of 5 to 100 µm.
  3. A method of manufacturing a high strength and high formability steel sheet, the method comprising:
    forming a slab by continuously casting a steel including:
    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 resin film at least on a side to be an inner surface of a can after forming a surface treatment film by an electrolytic process; and
    manufacturing a steel sheet having a tensile strength in a rolling direction of not less than 520 MPa and an Erichsen value of not less than 5.0 mm.
EP13773084.2A 2012-04-06 2013-04-03 High-strength, highly workable steel sheet, and method for manufacturing same Active EP2835438B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2012087940 2012-04-06
PCT/JP2013/060175 WO2013151085A1 (en) 2012-04-06 2013-04-03 High-strength, highly workable steel sheet, and method for manufacturing same

Publications (3)

Publication Number Publication Date
EP2835438A1 true EP2835438A1 (en) 2015-02-11
EP2835438A4 EP2835438A4 (en) 2015-12-23
EP2835438B1 EP2835438B1 (en) 2019-06-26

Family

ID=49300566

Family Applications (1)

Application Number Title Priority Date Filing Date
EP13773084.2A Active EP2835438B1 (en) 2012-04-06 2013-04-03 High-strength, highly workable steel sheet, and method for manufacturing same

Country Status (9)

Country Link
US (1) US20150064448A1 (en)
EP (1) EP2835438B1 (en)
JP (1) JP5804195B2 (en)
KR (1) KR20140117602A (en)
CN (1) CN104245985B (en)
CO (1) CO7061066A2 (en)
MY (1) MY185149A (en)
TW (1) TWI473889B (en)
WO (1) WO2013151085A1 (en)

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
MX2016014060A (en) * 2014-04-30 2017-02-14 Jfe Steel Corp High-strength steel sheet and production method therefor.
WO2016157877A1 (en) * 2015-03-31 2016-10-06 Ｊｆｅスチール株式会社 Steel sheet for can lids and method for producing same
CN107429360B (en) * 2015-03-31 2019-06-25 杰富意钢铁株式会社 The manufacturing method of steel plate for tanks and steel plate for tanks
JP6421772B2 (en) * 2016-02-29 2018-11-14 Ｊｆｅスチール株式会社 Manufacturing method of steel sheet for cans
DE102020106164A1 (en) 2020-03-06 2021-09-09 Thyssenkrupp Rasselstein Gmbh Cold rolled flat steel product for packaging

Family Cites Families (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0533188A (en) * 1991-07-30 1993-02-09 Nippon Steel Corp Surface treated steel for vessel excellent in rust resistance and external appearance characteristic
JP3740779B2 (en) 1997-03-12 2006-02-01 Ｊｆｅスチール株式会社 Steel plate for easy open can lid excellent in openability and rivet formability, manufacturing method thereof, and easy open can lid
JP3840004B2 (en) * 1999-08-17 2006-11-01 新日本製鐵株式会社 Ultra-thin soft steel plate for containers with excellent can strength and can moldability and method for producing the same
TW558569B (en) * 2000-02-23 2003-10-21 Kawasaki Steel Co High tensile hot-rolled steel sheet having excellent strain aging hardening properties and method for producing the same
JP4665302B2 (en) * 2000-11-02 2011-04-06 Ｊｆｅスチール株式会社 High-tensile cold-rolled steel sheet having high r value, excellent strain age hardening characteristics and non-aging at room temperature, and method for producing the same
US20030015263A1 (en) * 2000-05-26 2003-01-23 Chikara Kami Cold rolled steel sheet and galvanized steel sheet having strain aging hardening property and method for producing the same
JP4519373B2 (en) * 2000-10-27 2010-08-04 Ｊｆｅスチール株式会社 High-tensile cold-rolled steel sheet excellent in formability, strain age hardening characteristics and room temperature aging resistance, and method for producing the same
JP4133520B2 (en) * 2002-11-21 2008-08-13 新日本製鐵株式会社 Steel plate for containers with extremely good deformation resistance and method for producing the same
EP1627820B1 (en) * 2003-05-22 2012-06-20 JFE Steel Corporation Laminated steel sheet
TW200827460A (en) * 2006-08-11 2008-07-01 Nippon Steel Corp DR steel sheet and manufacturing method thereof
CN101983251A (en) * 2008-04-03 2011-03-02 杰富意钢铁株式会社 High-strength steel plate for a can and method for manufacturing said high-strength steel plate
JP5453884B2 (en) * 2008-04-03 2014-03-26 Ｊｆｅスチール株式会社 Steel plate for high-strength container and manufacturing method thereof
CN102286688A (en) * 2010-06-21 2011-12-21 宝山钢铁股份有限公司 Steel for high-hardness tin plating primitive plate and manufacture method thereof

Also Published As

Publication number Publication date
TW201410879A (en) 2014-03-16
CN104245985B (en) 2017-08-11
EP2835438A4 (en) 2015-12-23
CN104245985A (en) 2014-12-24
TWI473889B (en) 2015-02-21
US20150064448A1 (en) 2015-03-05
CO7061066A2 (en) 2014-09-19
WO2013151085A1 (en) 2013-10-10
JPWO2013151085A1 (en) 2015-12-17
MY185149A (en) 2021-04-30
KR20140117602A (en) 2014-10-07
EP2835438B1 (en) 2019-06-26
JP5804195B2 (en) 2015-11-04

Similar Documents

Publication Publication Date Title
JP6505712B2 (en) Steel sheet products, steel parts manufactured from the steel sheet products, and automobile bodies
US8795443B2 (en) Lacquered baked steel sheet for can
JP5794004B2 (en) Steel sheet for high strength can excellent in flange workability and manufacturing method thereof
EP2835438B1 (en) High-strength, highly workable steel sheet, and method for manufacturing same
EP3725511B1 (en) Resin coated metal plate for containers
WO2013018334A1 (en) High-strength high-processability steel sheet for cans and method for producing same
EP2468909B1 (en) Highly processable steel sheet for three-piece welded can and method for producing same
KR20170063744A (en) Steel sheet for two-piece can and manufacturing method therefor
KR20190121810A (en) Steel plate for two-piece can and its manufacturing method
EP2860124B1 (en) Three-piece can and method for producing same
WO1999063124A1 (en) Resin-coated steel sheet suitable for use in thin-walled deep-drawn ironed can and steel sheet therefor
JP6455639B1 (en) Steel plate for 2-piece can and manufacturing method thereof
JP6019719B2 (en) Manufacturing method of high strength and high ductility steel sheet
WO2008123336A1 (en) Ultra-thin cold-rolled steel sheet for building material and process for production of the same
JP4564289B2 (en) Steel plate for high-rigidity can with less surface coating film damage after processing and manufacturing method thereof
JPH05247669A (en) Manufacture of high strength steel sheet for thinned and deep-drawn can
AU2018309964B2 (en) Steel sheet for crown cap, crown cap and method for producing steel sheet for crown cap
JP2002146474A (en) Steel sheet for easy open end and its production method

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20140805

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

DAX Request for extension of the european patent (deleted)
RA4 Supplementary search report drawn up and despatched (corrected)

Effective date: 20151124

RIC1 Information provided on ipc code assigned before grant

Ipc: C21D 9/46 20060101ALI20151118BHEP

Ipc: C25D 5/26 20060101ALI20151118BHEP

Ipc: B21B 3/00 20060101ALI20151118BHEP

Ipc: C25D 7/06 20060101ALI20151118BHEP

Ipc: C22C 38/50 20060101ALI20151118BHEP

Ipc: C25D 5/48 20060101ALI20151118BHEP

Ipc: C22C 38/04 20060101ALI20151118BHEP

Ipc: C21D 8/02 20060101ALI20151118BHEP

Ipc: C22C 38/00 20060101AFI20151118BHEP

Ipc: C22C 38/06 20060101ALI20151118BHEP

Ipc: C22C 38/02 20060101ALI20151118BHEP

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

17Q First examination report despatched

Effective date: 20170824

REG Reference to a national code

Ref country code: DE

Ref legal event code: R079

Ref document number: 602013057128

Country of ref document: DE

Free format text: PREVIOUS MAIN CLASS: C22C0038000000

Ipc: C21D0008020000

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/02 20060101ALI20190130BHEP

Ipc: C25D 5/48 20060101ALI20190130BHEP

Ipc: C22C 38/04 20060101ALI20190130BHEP

Ipc: B22D 11/00 20060101ALN20190130BHEP

Ipc: C22C 38/00 20060101ALI20190130BHEP

Ipc: C22C 38/06 20060101ALI20190130BHEP

Ipc: C21D 8/02 20060101AFI20190130BHEP

Ipc: C25D 7/06 20060101ALI20190130BHEP

Ipc: C21D 9/46 20060101ALI20190130BHEP

INTG Intention to grant announced

Effective date: 20190213

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1148341

Country of ref document: AT

Kind code of ref document: T

Effective date: 20190715

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602013057128

Country of ref document: DE

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: NL

Ref legal event code: FP

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190926

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190927

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190926

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 1148341

Country of ref document: AT

Kind code of ref document: T

Effective date: 20190626

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20191028

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20191026

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200224

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602013057128

Country of ref document: DE

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG2D Information on lapse in contracting state deleted

Ref country code: IS

26N No opposition filed

Effective date: 20200603

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200430

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200403

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200430

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20200430

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200430

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200403

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20210309

Year of fee payment: 9

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190626

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20220430

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: NL

Payment date: 20240315

Year of fee payment: 12

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 20240229

Year of fee payment: 12

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: IT

Payment date: 20240313

Year of fee payment: 12

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20240227

Year of fee payment: 12