US20160362761A1 - Steel sheet for crown cap, method for manufacturing same, and crown cap - Google Patents

Steel sheet for crown cap, method for manufacturing same, and crown cap Download PDF

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US20160362761A1
US20160362761A1 US15/121,540 US201515121540A US2016362761A1 US 20160362761 A1 US20160362761 A1 US 20160362761A1 US 201515121540 A US201515121540 A US 201515121540A US 2016362761 A1 US2016362761 A1 US 2016362761A1
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steel sheet
mass
temperature
rolling
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Tomonari HIRAGUCHI
Katsumi Kojima
Hiroki Nakamura
Masami TSUJIMOTO
Toshihiro Kikuchi
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JFE Steel Corp
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JFE Steel Corp
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Assigned to JFE STEEL CORPORATION reassignment JFE STEEL CORPORATION ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: TSUJIMOTO, MASAMI, NAKAMURA, HIROKI, HIRAGUCHI, Tomonari, KIKUCHI, TOSHIHIRO, KOJIMA, KATSUMI
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    • 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
    • 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
    • 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
    • B65D41/00—Caps, e.g. crown caps or crown seals, i.e. members having parts arranged for engagement with the external periphery of a neck or wall defining a pouring opening or discharge aperture; Protective cap-like covers for closure members, e.g. decorative covers of metal foil or paper
    • B65D41/02—Caps or cap-like covers without lines of weakness, tearing strips, tags, or like opening or removal devices
    • B65D41/10—Caps or cap-like covers adapted to be secured in position by permanent deformation of the wall-engaging parts
    • B65D41/12—Caps or cap-like covers adapted to be secured in position by permanent deformation of the wall-engaging parts made of relatively stiff metallic materials, e.g. crown caps
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0468—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

Definitions

  • the present disclosure relates to a steel sheet for crown caps that is excellent in shape uniformity during forming of crown caps used for beer bottles etc., to a method for manufacturing the steel sheet, and to crown caps.
  • steel sheets for crown caps used for beer bottle caps etc. are being reduced in thickness.
  • SR Single Reduced
  • DR Double Reduced
  • steel sheets for crown caps the demand for steel sheets having a thickness of 0.20 mm or less is increasing, and DR steel subjected to secondary cold rolling is preferred because work hardening can be utilized in order to compensate for a reduction in pressure capacity due to a reduction in thickness.
  • the DR steel is generally harder than the SR steel, and a problem with the DR steel is its low formability.
  • a central portion is drawn to some extent at the initial stage of forming, and then an outer edge portion is formed into a fluted shape.
  • the use of a steel sheet with low formability may cause a defective shape, i.e., non-uniform flute shapes.
  • a crown cap with non-uniform flute shapes has a problem in that, after the crown cap is put on a bottle, pressure capacity is not achieved and leakage of the content occurs, so that the crown cap does not server as a cap. If the strength of the steel sheet of a crown cap is low, there is a risk that the crown cap comes off even when the shapes of the flutes are uniform.
  • the present inventors have conducted extensive studies.
  • the present inventors have studied the chemical composition, hot rolling conditions, cold rolling conditions (primary and secondary), and continuous annealing conditions of ultra-low carbon steel used as a base material.
  • the present inventors have found that, by increasing an average r value and controlling a YP to a suitable value, the rate of occurrence of defective shapes can be reduced and pressure capacity can be ensured.
  • Exemplary embodiments may include as follows.
  • a steel sheet for crown caps comprising, in mass %, C: 0.0005 to 0.0050%, Si: 0.020% or less, Mn: 0.10 to 0.60%, P: 0.020% or less, S: 0.020% or less, Al: 0.01 to 0.10% or less, N: 0.0050% or less, and Nb: 0.010 to 0.050%, the balance being Fe and inevitable impurities, the steel sheet having an average r value of 1.30 or more and a YP of 450 MPa or more and 650 MPa or less.
  • a method for manufacturing a steel sheet for crown caps comprising: hot rolling a steel slab having a chemical composition according to [1] at a slab reheating temperature of 1,150° C. or higher and a finishing temperature of 870° C. or higher; coiling the hot rolled steel sheet at a coiling temperature of 600° C. or higher; performing pickling; then performing primary cold rolling; performing annealing at an annealing temperature of recrystallization temperature or more and 790° C. or less; and then performing secondary cold rolling at a rolling reduction of 10% or more and 50% or less.
  • % indicating the percentage of each compositional component is percent by mass.
  • a steel sheet for crown caps that has an average r value or 1.30 or more and a YP of 450 MPa or more and 650 MPa or less and excellent in formability is obtained.
  • the use of the steel sheet for crown caps of the disclosed embodiments can improve the shape uniformity of crown caps used for beer bottles etc. and allows sufficient pressure capacity to be achieved.
  • FIG. 1 is an illustration showing the shape of flutes of a crown cap.
  • C is an element that increases the strength of the steel but decreases its formability. If the amount of solute C in the steel is large, yield elongation increases, and the large amount of solute C is likely to cause age hardening and stretcher strain during forming. Therefore, when a continuous annealing method is used, it is necessary to control and reduce the content of C as much as possible at the stage of steelmaking. If the amount of remaining solute C is large, the steel sheet becomes hard, and wrinkles easily occur at the initial stage of the forming of a crown cap, causing an increase in the rate of occurrence of defective shapes. C is also an element having an influence on recrystallization texture.
  • the content of C is 0.0050% or less.
  • the content of C is preferably 0.0035% or less and more preferably 0.0023% or less.
  • the lower limit of the content of C is 0.0005%.
  • the amount of Si is 0.020% or less.
  • Mn is added for the purpose of preventing thermal embrittlement. Mn also has the effect of preventing a reduction in hot ductility caused by S contained in the steel. It is necessary that the amount of Mn added be 0.10% or more in order to obtain these effects.
  • the upper limit of Mn in tin mill black plates used for general food containers is specified to be 0.60% or less. Therefore, the upper limit of Mn in the disclosed embodiments is 0.60% or less. From the viewpoint of formability, Mn is preferably 0.45% or less.
  • the upper limit of P is 0.020%.
  • S is bonded to Fe in the steel to thereby form FeS, and this causes a reduction in the hot ductility of the steel.
  • S is 0.020% or less. If the amount of S is excessively small, the risk of the occurrence of pitting corrosion increases. Therefore, S is preferably 0.008% or more.
  • Al is an element added as a deoxidizer.
  • Al and N form AlN
  • Al has the effect of reducing the amount of solute N in the steel. If the content of Al is less than 0.01%, the deoxidation effect and the effect of reducing the amount of solute N are not sufficient.
  • a content of Al exceeding 0.10% is not preferable because not only these effects are saturated but also the amount of inclusions such as alumina increases. Therefore, the content of Al is within the range of 0.01% or more and 0.10% or less.
  • the upper limit of N is 0.0050% or less. It is difficult to stably reduce the amount of N to less than 0.0010%, and this causes the cost of manufacturing to increase. Therefore, N is preferably 0.0010% or more.
  • Nb is an element that fixes solute C in the steel sheet as NbC to thereby reduce the amount of the solute C, whereby the average r value can be increased.
  • drawability is improved, and this is effective to suppress a defective shape.
  • the lower limit is set to 0.010%. If the amount of Nb added is large, recrystallization temperature becomes high, so that non-recrystallized crystals may be present after annealing. This may cause variations in material properties. Therefore, the amount of Nb is 0.050% or less.
  • the balance is Fe and inevitable impurities.
  • Cu, Ni, Cr, and Mo may be contained so long as the effects of the present disclosure are not impaired.
  • Cu is 0.2% or less
  • Ni is 0.15% or less
  • Cr is 0.10% or less
  • Mo is 0.05% or less.
  • Other elements are 0.02% or less.
  • Sn may be contained so long as the effects of the present disclosure are not impaired.
  • the amount of Sn is preferably less than 0.0050%.
  • the structure of the steel sheet for crown caps of the disclosed embodiments is a recrystallized structure. This is because, if non-recrystallized crystals are present after annealing, the material properties become non-uniform, and this causes variations in mechanical properties. However, when the area ratio of the non-recrystallized crystals is 5% or less, the non-recrystallized crystals have almost no influence on the variations in material properties, and therefore the area ratio of 5% or less is allowable.
  • the recrystallized structure is preferably a ferrite phase, and the amount of phases other than the ferrite phase is preferably less than 1.0%.
  • the elongation rate of the ferrite is preferably 4.2 or less. If the elongation rate of the ferrite grains in the steel sheet exceeds 4.2, it may be difficult to obtain uniformly-shaped flutes in a circumferential direction.
  • the elongation rate of the ferrite can be set to 4.2 or less by setting the rolling reduction in the secondary cold rolling to 50% or less.
  • the elongation rate of the ferrite can be measured by a method described in an Example described later.
  • a slab having the above-described composition is subjected to hot rolling at a slab reheating temperature of 1,150° C. or higher and a finishing temperature of 870° C. or higher, coiled at a coiling temperature of 600° C. or higher, pickled, then subjected to primary cold rolling, annealed at an annealing temperature of the recrystallization temperature or more and 790° C. or less, and then subjected to secondary cold rolling at a rolling reduction of 10% or more and 50% or less, whereby a steel sheet for crown caps having excellent formability can be obtained.
  • the slab reheating temperature before the hot rolling is excessively low, it is difficult to ensure final finishing rolling temperature. Therefore, the slab reheating temperature is 1,150° C. or higher. If the heating temperature is excessively high, problems such as defects on the surface of the product and an increase in energy cost occur. Therefore, the heating temperature is preferably 1,300° C. or lower.
  • the hot rolling finishing temperature is 870° C. or higher. If the hot rolling finishing temperature is excessively high, hot rolling scales are increased in thickness, and pickling properties deteriorate. Therefore, the hot rolling finishing temperature is preferably 910° C. or lower. In the disclosed embodiments, since the amount of a solute element is reduced by Nb added to form IF steel, it is unnecessary to perform treatment for precipitating carbide etc. before finishing rolling. Therefore, ordinary finishing rolling can be used.
  • the coiling temperature after the hot rolling is 600° C. or higher.
  • the coiling temperature is preferably higher than 700° C.
  • the coiling temperature after the hot rolling is preferably 730° C. or lower.
  • the conditions of the pickling are not particularly specified, so long as the scales in the surface layer can be removed.
  • the pickling may be performed by any commonly used method.
  • the picking has been described as an example of the method for removing scales. However, any method other than the pickling may be used so long as the scales can be removed. For example, the scales may be removed mechanically.
  • the rolling reduction in the primary cold rolling is excessively high, an excessively large load is applied to reduction rolls during the rolling, and this causes a large burden on the facility. If the rolling reduction is excessively low, it is necessary to reduce the thickness of the produced hot-rolled steel sheet accordingly. In this case, it is difficult to control the material properties. Therefore, the rolling reduction in the primary cold rolling is preferably 86 to 89%.
  • the annealing method is preferably a continuous annealing method.
  • the annealing temperature during continuous annealing must be the recrystallization temperature or more. However, if the annealing temperature is excessively high, the crystal grains become coarse, and the strength of the steel sheet is reduced. In this case, the YP may be outside the range defined in the disclosed embodiments. In thin sheets, the risk of fracture in a furnace and buckling increases. Therefore, the annealing temperature is 790° C. or lower.
  • the soaking time during the annealing is preferably 10 seconds or more and 90 seconds or less from the viewpoint of productivity.
  • secondary cold rolling is performed in order to reduce the thickness of the steel sheet and increase the strength of the steel sheet.
  • the secondary cold rolling is a particularly important manufacturing condition in the disclosed embodiments. If the rolling reduction exceeds 50%, the steel sheet is hardened excessively, and the formability is reduced. In addition, the average r value is reduced, and a ⁇ r value increases. Therefore, the rolling reduction in the secondary cold rolling is 50% or less.
  • the secondary rolling is performed at a rolling reduction of 10% or more. To further ensure the pressure capacity, the rolling reduction is preferably more than 30%.
  • the cold-rolled steel sheet obtained in the manner described above is subjected to the following surface treatment before it is formed into a crown cap.
  • the steel sheet subjected to the following surface treatment is also the steel sheet for crown caps of the disclosed embodiments.
  • the surface of the steel sheet subjected to the secondary cold rolling described above may be subjected to various types of surface treatment.
  • the surface treatment include general plating methods such as electroplating. Such a method is used to form at least one of tin plating, chromium plating, and nickel plating.
  • the thickness of the plating etc. formed by the surface treatment is sufficiently smaller than the thickness of the steel sheet. Therefore, the influence of the plating on the mechanical properties of the steel sheet for crown caps is negligible.
  • the defective shape of a crown cap is caused by the occurrence of wrinkles during drawing at the initial stage of the forming of the crown cap.
  • drawability i.e., to achieve a high average r value.
  • the average r value is 1.30 or more.
  • the average r value is preferably 1.40 or more. The practical upper limit of the average r value is 2.00.
  • the ⁇ r in-plane anisotropy
  • ⁇ 0.5 holds. It is more preferable that
  • the ⁇ r (in-plane anisotropy) can be measured using a natural oscillation method specified in JIS Z 2254 Appendix JA. Specifically, the resonance frequency of a steel sheet is measured in directions 0°, 45°, and 95° with respect to the rolling direction to compute the anisotropy ⁇ E of the Young's modulus, and an experimental formula representing the correlation between the ⁇ r and ⁇ E is used to compute the value of the ⁇ r.
  • the pressure capacity of a container is proportional to the YP of a lid material. If the strength of the steel sheet is insufficient, a sufficient pressure capacity is not obtained. Therefore, the lower limit of the YP is 450 MPa. If the YP is excessively high, circumferential compressive stress in the flute portions of the crown cap becomes high and exceeds the critical buckling stress at the initial stage of the forming of the crown cap, so that wrinkles are easily formed. To prevent such a defective shape, the upper limit is 650 MPa. A tensile test is performed according to JIS Z 2241 using a JIS No. 5 tensile test piece. The rolling direction (L direction) is used as the tensile direction.
  • the pressure capacity of a container is proportional to the square of the thickness of a lid material. If the thickness is excessively small, the pressure capacity becomes low, and the lid cannot play its role. Therefore, the thickness is preferably 0.13 mm or more and more preferably 0.16 mm or more. From the viewpoint of a reduction in thickness of the steel sheet for crown caps for the purpose of resource conservation, a reduction in environmental load, and a reduction in material cost, it is preferable that the thickness of the steel sheet is smaller than 0.22 mm, which is the thickness of the existing steel sheets for crown caps. To achieve the above effects, the thickness is preferably 0.18 mm or less.
  • the steel sheet for crown caps is excellent in formability is obtained in the manner described above.
  • the crown cap is a lid material used for, for example, a drink bottle and has flute-like protrusions on a side surface of the crown cap (the number of flutes is generally 21), and the content of the bottle is sealed by crimping the flute-like grooves onto the tap of the bottle.
  • a packing is provided on the inner surface of the crown cap in order to increase the sealing performance.
  • the material used for the packing is a cork sheet, PVC (polyvinyl chloride), PE (polyethylene), etc.
  • the obtained thin-steel sheet was annealed in a continuous annealing furnace at an annealing temperature (recrystallization temperature) shown in Table 2 and then subjected to secondary cold rolling at a rolling reduction shown in Table 2 to thereby manufacture a thin-steel sheet having a final finishing thickness shown in Table 2.
  • annealing temperature refcrystallization temperature
  • the structure observation was performed according to “JIS G 0551.” Specifically, nital was used to allow ferrite grains to appear, and a photograph was taken at 400 ⁇ using an optical microscope. The presence or absence of non-crystallized crystals was checked visually under the optical microscope, and grains not undergoing recrystallization were judged to be non-crystallized crystals. The photograph taken using the optical microscope was subjected to image processing to distinguish non-crystallized portions and recrystallization-completed portions from each other, and the area ratio of the non-crystallized grains was computed. An “AA” rating was assigned when the area ratio of the non-crystallized crystals was 0%.
  • a rating was assigned when the area ratio of the non-crystallized crystals was more than 0% and 5% or less.
  • a “C” rating was assigned when the area ratio of the non-crystallized crystals was more than 5%.
  • the elongation rate of the ferrite grains was computed using a method shown in “JIS G 0202.”
  • Each of the steel sheets obtained by the above-described manufacturing method was subjected to surface treatment, i.e., chromium (tin-free) plating, and coated with paint (baking conditions: heat treatment at 210° C. for 20 minutes), and pressed into the shape of a crown cap. Mechanical properties and formability were examined under the following test conditions.
  • the natural oscillation method specified in JIS Z 2254 Appendix JA was used for the average r value (average plastic strain ratio). Specifically, the resonance frequencies of the steel sheet in directions 0°, 45°, and 95° with respect to the rolling direction and the average Young's modulus were determined, and the average r value was computed.
  • the natural oscillation method specified in JIS Z 2254 Appendix JA was used for the ⁇ r (in-plane anisotropy). Specifically, the resonance frequencies of the steel sheet in directions 0°, 45°, and 95° with respect to the rolling direction were measured to compute the anisotropy ⁇ E of the Young's modulus, and an experimental formula representing the correlation between the ⁇ r and ⁇ E was used to compute the value of ⁇ r.
  • a tensile test for YP measurement was performed according to JIS Z 2241 using a JIS No. 5 tensile test piece.
  • the rolling direction (L direction) was used as the tensile direction.
  • Crown caps were formed, and the uniformity of the flute shape of each of the crown caps was evaluated. A crown cap ruptured during forming was evaluated as fail (“F” in Table 3). For each of crown caps formed without any rupture, the lengths (L in FIG. 1 ) of the flutes of the crown cap were measured. A crown cap with a standard deviation a of the L value of 0.1 or less was evaluated as pass (“P” in Table 3). A crown cap with a standard deviation a of the L value of more than 0.1 was evaluated as fail (“F” in Table 3).
  • the average r value is 1.30 or more, and the YP is 450 MPa or more and 650 MPa or less.
  • Non-recrystallized crystals that may cause variations in material properties are not present, and shape uniformity and pressure capacity are high.
  • At least one of the shape uniformity and the pressure capacity is poor, or non-recrystallized crystals that may cause variations in material properties are present at an area ratio of more than 5%.

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  • Physics & Mathematics (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • General Chemical & Material Sciences (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Closures For Containers (AREA)
  • Metal Rolling (AREA)
US15/121,540 2014-02-25 2015-02-13 Steel sheet for crown cap, method for manufacturing same, and crown cap Abandoned US20160362761A1 (en)

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PCT/JP2015/000684 WO2015129191A1 (ja) 2014-02-25 2015-02-13 王冠用鋼板およびその製造方法ならびに王冠

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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3663428A4 (en) * 2017-07-31 2020-06-10 JFE Steel Corporation STEEL SHEET FOR CROWN CAPSULE, CROWN CAPSULE AND METHOD FOR PRODUCING STEEL SHEET FOR CROWN CAPSULE
US11359255B2 (en) 2017-07-31 2022-06-14 Jfe Steel Corporation Steel sheet for crown cap, crown cap and method for producing steel sheet for crown cap
WO2023217382A1 (de) * 2022-05-12 2023-11-16 Actega Ds Gmbh Dichtungseinlage für kronkorken mit verringerter blechstärke

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CN107335967A (zh) * 2016-11-19 2017-11-10 张红伟 密封瓶盖制作工艺
CN106868400A (zh) * 2017-03-21 2017-06-20 德龙钢铁有限公司 一种瓶盖用钢及其制造方法
KR102259719B1 (ko) * 2017-03-31 2021-06-01 제이에프이 스틸 가부시키가이샤 강판 및 그의 제조 방법과 왕관 및 drd캔
WO2018181451A1 (ja) * 2017-03-31 2018-10-04 Ｊｆｅスチール株式会社 鋼板およびその製造方法と王冠およびｄｒｄ缶

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Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3663428A4 (en) * 2017-07-31 2020-06-10 JFE Steel Corporation STEEL SHEET FOR CROWN CAPSULE, CROWN CAPSULE AND METHOD FOR PRODUCING STEEL SHEET FOR CROWN CAPSULE
US11359255B2 (en) 2017-07-31 2022-06-14 Jfe Steel Corporation Steel sheet for crown cap, crown cap and method for producing steel sheet for crown cap
US11459149B2 (en) 2017-07-31 2022-10-04 Jfe Steel Corporation Steel sheet for crown cap, crown cap and method for producing steel sheet for crown cap
WO2023217382A1 (de) * 2022-05-12 2023-11-16 Actega Ds Gmbh Dichtungseinlage für kronkorken mit verringerter blechstärke
WO2023217587A1 (de) * 2022-05-12 2023-11-16 Actega Ds Gmbh Dichtungseinlagen für kronkorken mit verringerter blechstärke

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CN106029926A (zh) 2016-10-12
CN106029926B (zh) 2018-10-02
MY174492A (en) 2020-04-23
JP6195012B2 (ja) 2017-09-13
BR112016019612A2 (pt) 2018-10-23
TWI541363B (zh) 2016-07-11
WO2015129191A1 (ja) 2015-09-03
KR101871735B1 (ko) 2018-06-27
TW201536930A (zh) 2015-10-01
JPWO2015129191A1 (ja) 2017-03-30

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