EP3476964B1 - Stahlblech für kronkorken, herstellungsverfahren dafür und kronkorken - Google Patents

Stahlblech für kronkorken, herstellungsverfahren dafür und kronkorken Download PDF

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Publication number
EP3476964B1
EP3476964B1 EP17855743.5A EP17855743A EP3476964B1 EP 3476964 B1 EP3476964 B1 EP 3476964B1 EP 17855743 A EP17855743 A EP 17855743A EP 3476964 B1 EP3476964 B1 EP 3476964B1
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EP
European Patent Office
Prior art keywords
steel sheet
crown cap
less
crown
rolling
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EP17855743.5A
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English (en)
French (fr)
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EP3476964A1 (de
EP3476964A4 (de
Inventor
Nobusuke Kariya
Tomonari Hiraguchi
Katsumi Kojima
Masashi Umemoto
Masami Tsujimoto
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JFE Steel Corp
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JFE Steel Corp
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Priority to PL17855743T priority Critical patent/PL3476964T3/pl
Publication of EP3476964A1 publication Critical patent/EP3476964A1/de
Publication of EP3476964A4 publication Critical patent/EP3476964A4/de
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    • 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
    • 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
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C21D1/28—Normalising
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0268—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
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese

Definitions

  • the present invention relates to a steel sheet, excellent in shape uniformity and pressure resistance to resist internal pressure, for crown caps used for beer bottles; a method for manufacturing the same; and a crown cap prepared using the steel sheet for crown caps.
  • crown caps are widely used for containers for beverages such as refreshing drinks and alcohols.
  • crown caps are manufactured from a thin steel sheet by press forming and include a disk-shaped portion for covering the mouth of a bottle and a pleated portion placed therearound. The bottle is tightly sealed by crimping the pleated portion to the mouth of the bottle.
  • a steel sheet used to manufacture crown caps is mainly an SR (single-reduced) steel sheet. This is obtained in such a manner that a steel plate is thinned by cold rolling, followed by annealing and temper rolling.
  • the thickness of a steel sheet for conventional crown caps is generally 0.22 mm or more and sufficient pressure resistance and formability can be ensured by the use of an SR material made of mild steel used for cans for foods and drinks.
  • gauge reduction has been increasingly required for steel sheets for crown caps, as well as steel sheets for cans, for cost reduction purposes.
  • a crown cap manufactured from a conventional SR material is short of pressure resistance.
  • a DR (double-reduced) steel sheet which is obtained by performing secondary cold rolling after annealing and which can take advantage of work hardening to compensate for a reduction in strength due to gauge reduction.
  • an increase in rolling reduction ratio during secondary cold rolling hardens a steel sheet to reduce the formability thereof.
  • a central portion is drawn to a certain degree in the initial stage of forming and an outside edge portion is then formed into a pleated shape.
  • a shape failure in which shapes of pleats are non-uniform occurs in some cases.
  • a crown cap with a non-uniform pleated shape has a problem that pressure resistance is not obtained by capping a bottle, contents leak, and the crown cap does not play a role as a lid.
  • a crown cap may possibly be detached due to insufficient pressure resistance even if the pleated shape thereof is uniform.
  • a method for evaluating pressure resistance has become strict because of the gauge reduction of steel sheets for crown caps.
  • Patent Literature 1 discloses an ultra-thin mild steel sheet with a thickness of 0.4 mm or less, excellent in can strength and can formability, for containers.
  • the ultra-thin mild steel sheet contains N: 0.0040% to 0.0300% and Al: 0.005% to 0.080% on a mass basis, has a 0.2% offset yield strength of 430 MPa or less and a total elongation of 15% to 40% as determined by a tensile test using a JIS No. 5 test specimen, and also has a Q -1 of 0.0010 or more due to internal friction.
  • Patent Literature 2 discloses a steel sheet for high-strength, high-formability cans.
  • the steel sheet contains C: 0.001% to 0.080%, Si: 0.003% to 0.100%, Mn: 0.10% to 0.80%, P: 0.001% to 0.100%, S: 0.001% to 0.020%, Al: 0.005% to 0.100%, N: 0.0050% to 0.0150%, and B: 0.0002% to 0.0050% on a mass basis and also contains 0.01% to 1.00% of crystal grains having an elongation rate of 5.0 or more in a cross section along the rolling-direction ,in terms of an area fraction.
  • Patent Literature 3 discloses a steel sheet for cans with high-strength and high-formability.
  • the steel sheet contains C: 0.001% to 0.040%, Si: 0.003% to 0.100%, Mn: 0.10% to 0.80%, P: 0.001% to 0.100%, S: 0.001% to 0.020%, Al: 0.005% to 0.100%, N: more than 0.015% to 0.020%, and B: 0.0002% to 0.0050% on a mass basis, the content of N which is present in the form of AlN being 0.0060% or less; also contains crystal grains having an average grain size of 5.00 ⁇ m or more and an elongation rate of 2.50 or less in a cross section along the rolling-direction; and has a tensile strength of 550 MPa or more and a breaking elongation of 7% or more.
  • EP 2253729 A1 and EP 1291447 A1 disclose cold rolled steel sheets.
  • Patent Literature 1 While a two-piece can is evaluated for flange formability and can strength after can-making, the pressure resistance of a crown cap after the crown cap is formed and a bottle is capped with the crown cap is not at all described.
  • the present invention has been made in view of the above problems. It is an object of the present invention to provide a steel sheet, having sufficient pressure resistance and formability regardless of gauge reduction, for crown caps; a method for manufacturing the same; and a crown cap. Solution to Problem
  • a steel sheet having sufficient pressure resistance and formability regardless of gauge reduction, for crown caps; a method for manufacturing the same; and a crown cap can be provided.
  • a steel sheet for crown caps according to the present invention has a composition containing C: 0.02% to 0.08%, Si: 0.02% or less, Mn: 0.10% to 0.60%, P: 0.020% or less, S: 0.020% or less, Al: 0.01% to 0.06%, and N: 0.0100% to 0.0180% on a mass basis, the remainder being Fe and inevitable impurities, wherein N total-(N as AlN) is 0.0090% to 0.0170%, the maximum grain size of a carbide is 2.0 ⁇ m or less in a cross section in a rolling direction, and the yield strength is 420 MPa to 600 MPa in the rolling direction.
  • the steel sheet for crown caps according to the present invention is described below.
  • composition of the steel sheet for crown caps according to the present invention is described.
  • the unit "%" of the content is all “mass percent”.
  • the content of C is set to 0.02 % to 0.08%.
  • the content of C is preferably 0.03% or more.
  • the content of C is preferably 0.06% or less.
  • the content of Si is set to 0.02% or less.
  • the lower limit of the content of Si is not particularly limited. Excessively reducing Si causes an increase in steelmaking cost. Therefore, the content of Si is preferably set to 0.004% or more.
  • the content of Mn is set to 0.10% or more.
  • the content of Mn is set to 0.60% or less.
  • the content of Mn is preferably 0.20% or more.
  • the steel sheet is hard and the reduction in corrosion resistance thereof is caused in addition to the reduction in formability of the crown cap.
  • the upper limit of the content of P is set to 0.020%.
  • S is a harmful element which forms inclusions in the steel sheet to cause the reduction in hot ductility of the steel sheet and the deterioration in corrosion resistance thereof.
  • the upper limit of the content of S is set to 0.020%.
  • Al is a necessary element serving as a deoxidizer during steelmaking.
  • the content of Al is less than 0.01%, deoxidization is insufficient, leading to the increase in amount of inclusions and the deterioration in formability of the crown cap.
  • Al forms AlN with N in steel to reduce the amount of solute N in steel.
  • the content of Al is set to 0.01% to 0.06%.
  • the content of Al is preferably set to 0.01% to 0.04%.
  • the content of N is less than 0.0100%, the amount of N total-(N as AlN) described below is not sufficiently obtained, the strength of the steel sheet is low, and the pressure resistance is low.
  • the content of N is set to 0.0100% to 0.0180%.
  • the content of N is preferably 0.0135% or more.
  • N in the steel is probably mainly present in the form of AlN. Therefore, (N total-(N as AlN)) obtained by subtracting the amount of N present in the form of AlN (N as AlN) from the total amount of N (N total) is regarded as the amount of solute N.
  • N total-(N as AlN) obtained by subtracting the amount of N present in the form of AlN (N as AlN) from the total amount of N (N total) is regarded as the amount of solute N.
  • the content of N total-(N as AlN) is less than 0.0090%, the strength of the steel sheet is low and the pressure resistance is low.
  • the content of N total-(N as AlN) is greater than 0.0170%, the strength of the steel sheet is excessively high, the formability of the crown cap is low, and the pressure resistance thereof is low.
  • the content of N total-(N as AlN) is set to 0.0090% to 0.0170%.
  • the content of N total-(N as AlN) is preferably set to 0.0110% to 0.0170%.
  • the amount of N present in the form of AlN can be confirmed in such a manner that AlN is dissolved and extracted using, for example, a 10% Br-methanol solution and N present in the form of AlN is quantitatively analyzed by absorptiometry.
  • the remainder are Fe and the inevitable impurities.
  • the steel sheet for crown caps according to the present invention has a microstructure containing the carbide and the maximum grain size of the carbide in the cross section in the rolling direction is 2.0 ⁇ m or less.
  • the carbide in the steel is mainly present in the form of cementite.
  • a pleated portion of the crown cap is a site suffering tensile and compressive strains or strain superimposed with tension and compression in each of the rolling direction of the steel sheet, directions perpendicular to the rolling direction, and thickness directions. Therefore, it is conceivable that if coarse carbides are present, then strain locally concentrates during forming to cause shape failures.
  • the maximum grain size of the carbide (cementite) is less than 0.3 ⁇ m, the steel sheet has excessively high strength and the formability of the crown cap may possibly be impaired. Therefore, the maximum grain size of cementite is 0.3 ⁇ m or more.
  • a through-thickness cross section parallel to the rolling direction of the steel sheet is polished and is then etched with an etchant (3 volume percent nital), a through-thickness one-fourth position (in the above cross section, a one-fourth position from a surface in a thickness direction) is observed over 10 fields of view at 2,000x magnification using a scanning electron microscope (SEM), and cementite is identified by visual judgment using a microstructure photograph taken with the SEM.
  • SEM scanning electron microscope
  • the size of cementite grains the area of each cementite grain is determined by image analysis and is converted into the equivalent circle diameter, which is defined as the size of the cementite grain.
  • the size of a cementite grain which is largest in size in the 10 fields of view is defined as the maximum grain size of the carbide.
  • the steel sheet for crown caps according to the present invention is required to have such a pressure resistance that the crown cap is not detached by the internal pressure in a bottle.
  • the thickness of steel sheets conventionally used for crown caps was 0.22 mm or more. In gauge reduction in which the thickness of a sheet is 0.20 mm or less, strength higher than ever is necessary. When the yield strength of the steel sheet in the rolling direction is less than 420 MPa, it is difficult to impart sufficient pressure resistance to such a thinned crown cap as described above.
  • the yield strength in the rolling direction is set to 420 MPa to 600 MPa.
  • the yield strength is preferably 450 MPa to 600 MPa.
  • the yield strength can be measured by a metallic material tensile test method specified in "JIS Z 2241".
  • a desired yield strength can be obtained in such a manner that the composition is adjusted; the coiling temperature during hot rolling, the average heating rate after cold rolling, the annealing temperature, and the average cooling rate after annealing are adjusted; and the cooling stop temperature and the retaining temperature after cooling stop are adjusted.
  • a yield strength of 420 MPa to 600 MPa can be obtained in such a manner that the above-mentioned composition is set, the coiling temperature in a hot rolling step is set to 670 °C or less, the average heating rate in a temperature range A from 500 °C to 600 °C in a heating course in a continuous annealing step after a cold rolling step is set to 10 °C/s to 30 °C/s, annealing is performed at an annealing temperature B in a temperature range from 620 °C to 740 °C, cooling is performed from the annealing temperature B to a cooling stop temperature C in a temperature range from 400 °C to 580 °C at an average cooling rate of 20 °C/s or more, the retention time for which retaining is performed in the temperature range from 400 °C to 580 °C after cooling at the above average cooling rate is stopped is set to 30 seconds to 90 seconds, and secondary cold rolling is performed at a rolling reduction ratio of 1.0% to 12%.
  • the steel sheet for crown caps is punched into a circular blank, which is then formed into the crown cap by press forming. After formation, the crown cap is crimped to the mouth of a bottle with a capper, whereby the airtightness after capping is maintained.
  • the strength of the side portion after crown cap forming is low, the crown cap is detached from the bottle mouth in some cases when the bottle is held in such a condition that the internal pressure of the bottle is high, leading to the leakage of contents in the bottle.
  • the strength of the side portion after crown cap forming closely correlates with the Vickers hardness of a cross section thereof.
  • the cross-sectional hardness of the side portion of the crown cap is less than 180 Hv, the strength of the side portion of the crown cap is low, leading to a reduction in airtightness, that is, a reduction in pressure resistance by a pressure test.
  • the cross-sectional hardness of the side portion of the crown cap is greater than 220 Hv, the strength of the side portion of the crown cap is excessively high and therefore cracks occur in the portion.
  • the cross-sectional hardness of the side portion of the crown cap is set to 180 Hv to 220 Hv.
  • the cross-sectional hardness of the side portion of the crown cap is preferably 190 Hv to 220 Hv.
  • the cross-sectional hardness of the side portion of the crown cap can be evaluated by a method specified in "JIS Z 2244".
  • positions for evaluating the cross-sectional hardness of the side portion of the crown cap are in a cross section of the side portion of the crown cap between pleats of the crown cap and a measuring is performed in terms of Vickers hardness.
  • the measuring positions are set to five points, in total, including one point at the center, two points in an upper surface direction of the crown cap, and two points in a downward direction of the crown cap, on the center being at a position (H/2) corresponding to half the height H of the crown cap.
  • the Vickers indentation load is set to 100 gf and the intervals between the points are set to 3d (d: the length of a diagonal of an indentation).
  • the average of the Vickers hardness values at the five points is defined as the cross-sectional hardness of the side portion of the crown cap.
  • a desired cross-sectional hardness can be obtained by forming the crown cap from the steel sheet for crown caps, the steel sheet being obtained in such a manner that the composition is adjusted; the coiling temperature during hot rolling, the average heating rate after cold rolling, the annealing temperature, and the average cooling rate after annealing are adjusted; and the secondary cold rolling reduction ratio is adjusted.
  • a cross-sectional hardness of the side portion of the crown cap of 180 Hv to 220 Hv can be obtained by forming the crown cap from the steel sheet for crown caps, the steel sheet being obtained in such a manner that the above-mentioned composition is set, the coiling temperature in the hot rolling step is set to 670 °C or less, the average heating rate in the temperature range A from 500 °C to 600 °C in the heating course in the continuous annealing step after the primary cold rolling step is set to 10 °C/s to 30 °C/s, annealing is performed at the annealing temperature B in the temperature range from 620 °C to 740 °C, cooling is performed from the annealing temperature B to the cooling stop temperature C in the temperature range from 400 °C to 580 °C at an average cooling rate of 20 °C/s or more, the retention time for which holding is performed in the temperature range from 400 °C to 580 °C after cooling at the above average cooling rate is stopped is set to 30 seconds to
  • the steel sheet for crown caps according to the present invention is manufactured by performing the following steps: a hot rolling step of coiling a steel material (steel slab) having the above-mentioned composition at a temperature of 670 °C or less after finish rolling in hot rolling; a pickling step of performing pickling as required after the hot rolling step; a primary cold rolling step of performing cold rolling after the pickling step; a continuous annealing step of performing heating at an average heating rate of 10 °C/s to 30 °C/s in a temperature range A from 500 °C to 600 °C in a heating course after the primary cold rolling step, annealing at an annealing temperature B in a temperature range from 620 °C to 740 °C, cooling from the annealing temperature B to a cooling stop temperature C in a temperature range from 400 °C to 580 °C at an average cooling rate of 20 °C/s or more
  • the temperature is the surface temperature of the steel sheet or the like.
  • the values thereof are values obtained by calculation based on the surface temperature.
  • the average heating rate in the temperature range A from 500 °C to 600 °C in the heating course is given by ((600 °C - 500 °C) / heating time from 500 °C to 600 °C).
  • the average cooling rate from the annealing temperature B to the cooling stop temperature C is given by ((annealing temperature B - cooling stop temperature C) / cooling time from annealing temperature B to cooling stop temperature C).
  • molten steel is prepared by a known process using a converter or the like so as to contain the above-mentioned chemical components and is then cast into a slab by, for example, a continuous casting process. Subsequently, the slab is preferably subjected to rough rolling in high heating temperature.
  • a rough rolling process is not particularly limited.
  • the heating temperature of the slab is preferably 1,200 °C or more. In order to further increase N total-(N as AlN), the heating temperature of the slab is preferably 1,230 °C or more.
  • the finish rolling temperature in the hot rolling step is preferably 850 °C or higher from the viewpoint of the stability of rolling load.
  • the finish rolling temperature is preferably within the range of 850 °C to 960 °C.
  • the coiling temperature in the hot rolling step is higher than 670 °C, because the amount of AlN precipitated in steel after coiling is increased, the amount of N total-(N as AlN) is less than 0.0090%, and thereby the yield strength of the steel sheet in the rolling direction is less than 420 MPa, and the cross-sectional hardness of the side portion of the crown cap after crown cap forming is less than 180 Hv in some cases.
  • the coiling temperature in the hot rolling step is higher than 670 °C, because the maximum grain size of the carbide in the cross section in the rolling direction is greater than 2.0 ⁇ m, and the shapes of the pleats of the crown cap become non-uniform during crown cap forming, leading to shape failures in some cases.
  • the coiling temperature in the hot rolling step is set to 670 °C or less.
  • the coiling temperature in the hot rolling step is preferably 640 °C or less.
  • the coiling temperature is preferably 500 °C or more.
  • pickling is performed as required.
  • Pickling may only be capable of removing surface scales and conditions for pickling need not be particularly limited.
  • a process such as mechanical removal may be used instead of pickling.
  • the rolling reduction ratio in the primary cold rolling step is not particularly limited and is preferably 85% to 94% for the purpose of adjusting the thickness of the steel sheet after secondary cold rolling to 0.20 mm or less.
  • heating is performed at an average heating rate of 10 °C/s to 30 °C/s in the temperature range A from 500 °C to 600 °C. It is not preferable that heating is performed at an average heating rate of less than 10 °C/s in the temperature range A, because the precipitation of AlN occurs during heating, the amount of N total-(N as AlN) is less than 0.0090%, the yield strength of the steel sheet in the rolling direction is less than 420 MPa, the cross-sectional hardness of the side portion of the crown cap after crown cap forming is less than 180 Hv, and the pressure resistance is low.
  • the average heating rate in the temperature range A is set to 10 °C/s or more.
  • the average heating rate therein is preferably set to 12 °C/s or more.
  • the average heating rate in the temperature range A is set to 30 °C/s or less.
  • the annealing temperature B is set in the temperature range from 620 °C to 740 °C.
  • the annealing temperature B is lower than 620 °C, the steel sheet is hard due to an incomplete recrystallization structure. Therefore, the yield strength of the steel sheet in the rolling direction is greater than 600 MPa, the cross-sectional hardness of the side portion of the crown cap after crown cap forming is greater than 220 Hv, the formability of the crown cap is poor, and the pressure resistance is low.
  • the annealing temperature B is set in the temperature range from 620 °C to 740 °C.
  • the annealing temperature B is preferably 640 °C or more.
  • the annealing temperature B is preferably 720 °C or less.
  • cooling is performed from the annealing temperature B to the cooling stop temperature C in the temperature range from 400 °C to 580 °C at an average cooling rate of 20 °C/s or more.
  • the average cooling rate is less than 20 °C/s, AlN precipitates excessively during cooling, the amount of N total-(N as AlN) is less than 0.0090%, the yield strength of the steel sheet in the rolling direction is less than 420 MPa, the cross-sectional hardness of the side portion of the crown cap after crown cap forming is less than 180 Hv, and the pressure resistance is low in some cases.
  • the average cooling rate is set to 20 °C/s or more.
  • the average cooling rate is preferably set to 40 °C/s or more.
  • the upper limit of the average cooling rate is not particularly limited.
  • the average cooling rate is preferably 150 °C/s or less.
  • the average cooling rate is more preferably 120 °C/s or less.
  • the cooling stop temperature C is set in the temperature range from 400 °C to 580 °C.
  • the cooling stop temperature is higher than 580 °C, AlN precipitates excessively, the amount of N total-(N as AlN) is less than 0.0090%, the yield strength of the steel sheet in the rolling direction is less than 420 MPa, the cross-sectional hardness of the side portion of the crown cap after crown cap forming is less than 180 Hv, and the pressure resistance is lowered in some cases.
  • the cooling stop temperature is preferably set to 550 °C or less.
  • the lower limit of the cooling stop temperature is set to 400 °C.
  • the cooling stop temperature is preferably set to 450 °C or more.
  • the retention time in the temperature range from 400 °C to 580 °C is set to 30 seconds to 90 seconds.
  • the retention time in the temperature range from 400 °C to 580 °C is more than 90 seconds, the carbide grows due to C diffusion into the carbide in steel, the maximum grain size of the carbide in the cross section in the rolling direction is greater than 2.0 ⁇ m, the shapes of pleats become non-uniform in crown cap forming, and the pressure resistance is lowered.
  • the retention time in the temperature range from 400 °C to 580 °C is preferably set to 75 seconds or less.
  • the lower limit of the retention time in the temperature range from 400 °C to 580 °C is set to 30 seconds or more.
  • the retention time is less than 30 seconds, the steel sheet is excessively hard, the shape becomes non-uniform in crown cap forming, and the pressure resistance is lowered.
  • the rolling reduction ratio during secondary cold rolling subsequent to the continuous annealing step is set to 1.0% to 12%.
  • the rolling reduction ratio during secondary cold rolling is less than 1.0%, the cross-sectional hardness of the side portion of the crown cap after crown cap forming is less than 180 Hv and the pressure resistance is lowered.
  • the reason for this is unclear and is considered as described below.
  • dislocations introduced by secondary cold rolling are anchored by solid solution during a heat treatment of lacquer baking.
  • the anchored dislocations serve as barriers at deformation and the strength increases.
  • drawing deformation is dominant and therefore force in slip systems which is different from tension acts.
  • the anchored dislocations do not act effectively during crown cap forming and the cross-sectional hardness of side portions of the crown caps is hard to increase. That is, in order to increase the cross-sectional hardness of the side portion of the crown cap in crown cap forming, a large number of dislocations need to be introduced by secondary cold rolling and the rolling reduction ratio needs to be 1.0% or more.
  • the rolling reduction ratio during secondary cold rolling is set to 1.0% to 12%.
  • the rolling reduction ratio during secondary cold rolling is preferably 3.0% or more.
  • the rolling reduction ratio during secondary cold rolling is preferably 10% or less.
  • a cold-rolled steel sheet obtained as described above is then subjected to a plating treatment such as tin plating, chromium plating, or nickel plating by, for example, electroplating as required such that a coated layer is formed on a surface of the steel sheet, whereby the steel sheet for crown caps is produced.
  • a plating treatment such as tin plating, chromium plating, or nickel plating by, for example, electroplating as required such that a coated layer is formed on a surface of the steel sheet, whereby the steel sheet for crown caps is produced.
  • the thickness of a film formed by surface treatment such as plating is sufficiently less than the thickness of the steel sheet and therefore the influence on mechanical properties of the steel sheet for crown caps is a negligible level.
  • the steel sheet for crown caps according to the present invention is capable of having sufficient strength and formability regardless of gauge reduction.
  • a crown cap according to the present invention is one which is formed by using the above-mentioned steel sheet for crown caps.
  • the crown cap is mainly composed of a disk-shaped portion for covering the mouth of a bottle and a pleated portion placed therearound.
  • the crown cap according to the present invention can be obtained in such a manner that a circular blank is stamped out, and formed by press forming.
  • the crown cap according to the present invention is manufactured from the steel sheet for crown caps, the steel sheet having sufficient yield strength and excellent formability; is therefore excellent in pressure resistance as a crown cap regardless of gauge reduction; and has the effect of reducing the amount of waste discharged in association with use.
  • the obtained steel slab was reheated to 1,220 °C and was then subjected to hot rolling at a rolling start temperature of 1,150 °C and at a finish rolling temperature shown in Table 2, followed by coiling at a coiling temperature. Pickling was performed after hot rolling.
  • primary cold rolling was performed at a rolling reduction ratio shown in Table 2 and continuous annealing was performed under conditions shown in Table 2.
  • secondary cold rolling was performed at a rolling reduction ratio shown in Table 2.
  • An obtained steel sheet was continuously subjected to usual Cr plating, whereby tin-free steel was obtained.
  • the steel sheet obtained as described above was subjected to a heat treatment corresponding to lacquer baking at 210 °C for 15 minutes, followed by tensile testing and measuring the cross-sectional hardness of a side portion of a crown cap.
  • Tensile testing was performed using a tensile test specimen with a JIS #5 size in accordance with "JIS Z 2241", whereby the yield strength in a rolling direction was measured.
  • the steel sheet was formed into the crown cap, which was measured for Vickers hardness by a method according to "JIS Z 2244".
  • a circular blank with a diameter of 37 mm was used and the blank was formed to have dimensions (an outside diameter of 32.1 mm, a height of 6.5 mm, the number of pleats being 21) of a type-3 crown cap specified in "JIS S 9017" (abolished standard) by press forming.
  • Evaluation positions were set to five points, in total, including one point at the center, two points in an upper surface direction of the crown cap, and two points in a downward direction of the crown cap as centered on a position (H/2) corresponding to half the height H of the crown cap.
  • the Vickers indentation load was set to 100 gf and the intervals between the points were set to 3d (d: the length of a diagonal of an indentation).
  • the average of the Vickers hardness values of the five points was defined as the cross-sectional hardness of the side portion of the crown cap.
  • a through-thickness cross section parallel to the rolling direction of the steel sheet was polished and was then etched with an etchant (3 volume percent nital), a through-thickness one-fourth position (in the above cross section, a one-fourth position from a surface in a thickness direction) was observed over 10 fields of view at 2,000x magnification using a scanning electron microscope (SEM), and cementite was identified by visual judgment using a microstructure photograph taken with the SEM.
  • SEM scanning electron microscope
  • the size of cementite grains the area of each cementite grain was determined by image analysis and was converted into the equivalent circle diameter, which was defined as the size of the cementite grain.
  • the size of a cementite grain which was largest in size in the 10 fields of view was defined as the maximum grain size of the carbide in the cross section in the rolling direction.
  • the obtained steel sheet was used to form crown caps and was evaluated for crown cap formability.
  • Circular blanks with a diameter of 37 mm were formed to have dimensions (an outside diameter of 32.1 mm, a height of 6.5 mm, the number of pleats being 21) of a type-3 crown cap specified in "JIS S 9017" (abolished standard) by press forming.
  • the length L of each fold 2 of the crown caps was measured as shown in Fig. 2 , a crown cap in which the standard deviation of L-values was 0.1 or less was rated O, and a crown cap in which the standard deviation of L-values was greater than 0.1 was rated ⁇ .
  • the evaluation was performed for five of the crown caps. All the five crown caps in which the standard deviation of L-values was 0.1 or less were rated O (acceptable) and those other than these were rated ⁇ (unacceptable).
  • a pressure test was performed using the formed crown caps.
  • a polyvinyl chloride liner was attached to the inside of the upper surface of each crown cap, a commercially available beer bottle was capped with the crown cap, a thin hole was made in an upper portion of the crown cap, a tool for feeding air into the bottle was fit therein, and the internal pressure of the bottle was increased by injecting air into the bottle at a rate of 5 psi per second.
  • Conditions for increasing the pressure in the bottle are as follows: the pressure in the bottle was increased to 100 psi (a pressurizing operation), was held at 100 psi for 1 minute (a holding operation), and was increased again at 5 psi per second (a repressurizing operation).
  • the internal pressure of the bottle that was obtained when air leaked from a gap between the crown cap and the mouth of the bottle or when the crown cap was detached from the bottle mouth was defined as the pressure resistance value of the crown cap.
  • the case where an anti-pressure value equal to or greater than that of a conventional crown cap was exhibited was rated O.
  • the case where the anti-pressure value of the conventional crown cap was not exhibited was rated ⁇ . After a rating of ⁇ was assigned, further evaluation was difficult; hence, - was given in the following tables.
  • the conventional crown cap used was made from an SR (single reduced) steel sheet with a thickness of 0.22 mm.
  • steel sheets of Steel Sheet Nos. 1 to 15 that were inventive examples had components within the scope of the present invention, had a yield strength of 420 MPa to 600 MPa in a rolling direction, and had the maximum grain size of a carbide 2.0 ⁇ m or less in a cross section in a rolling direction.
  • a crown cap formed from each of Steel Sheet Nos. 1 to 15 was such that the cross-sectional hardness of a side portion of the crown cap after crown cap forming was 180 Hv to 220 Hv.
  • Steel sheets for crown caps of Steel Sheet Nos. 1 to 15 were good in both crown cap formability and pressure resistance.
  • a steel sheet of Steel Sheet No. 16 that was a comparative example was such that since the content of C was less than 0.02%, the yield strength of the steel sheet in the rolling direction thereof was less than 420 MPa, the cross-sectional hardness of a side portion of a crown cap after crown cap forming was less than 180 Hv, the crown cap formability was good, but the pressure resistance was insufficient.
  • a steel sheet of Steel Sheet No. 17 was such that since the content of C was greater than 0.08%, the yield strength of the steel sheet in the rolling direction thereof was greater than 600 MPa, the maximum grain size of a carbide in a cross section in a rolling direction was greater than 2.0 ⁇ m, and the cross-sectional hardness of a side portion of a crown cap after crown cap forming was greater than 220 Hv; and therefore, the crown cap formability was poor, and the pressure resistance was insufficient.
  • a steel sheet of Steel Sheet No. 21 was such that since the content of N was greater than 0.0180%, N total-(N as AlN) was greater than 0.0170%; the yield strength of the steel sheet in the rolling direction thereof was greater than 600 MPa, and the cross-sectional hardness of a side portion of a crown cap after crown cap forming was greater than 220 Hv; and therefore the formed crown cap was poor in shape, and the pressure resistance was insufficient.
  • steel sheets of Steel Sheet Nos. 27, 28, 30, 32, 33, 35, 37 to 39, 41, 42, 45 to 48, and 50 to 52 that were inventive examples were such that the maximum grain size of a carbide in a cross section in a rolling direction was 2.0 ⁇ m or less, the yield strength in the rolling direction was 420 MPa to 600 MPa, the cross-sectional hardness of a side portion of a crown cap after crown cap forming was 180 Hv to 220 Hv, and therefore the crown cap formability and the pressure resistance were both good.
  • a steel sheet of Steel Sheet No. 24 that was a comparative example was such that since the coiling temperature was higher than 670 °C, the amount of N total-(N as AlN) was less than 0.0090%; the yield strength of the steel sheet in the rolling direction was less than 420 MPa, the cross-sectional hardness of a side portion of a crown cap after crown cap forming was less than 180 Hv, and the maximum grain size of a carbide in a cross section in a rolling direction was greater than 2.0 ⁇ m; and therefore the shapes of pleats of the crown cap became non-uniform during crown cap forming, shape failures occurred, the crown cap formability was poor, and the pressure resistance was poor.
  • a steel sheet of Steel Sheet No. 25 was such that since the average heating rate in a temperature range A from 500 °C to 600 °C was less than 10 °C/s, the amount of N total-(N as AlN) was less than 0.0090%, the yield strength of the steel sheet in the rolling direction thereof was less than 420 MPa, the cross-sectional hardness of a side portion of a crown cap after crown cap forming was less than 180 Hv, and the pressure resistance was poor.
  • a steel sheet of Steel Sheet No. 31 was such that since the average heating rate in a temperature range A from 500 °C to 600 °C was greater than 30 °C/s, the steel sheet was hard; the yield strength of the steel sheet in the rolling direction thereof was greater than 600 MPa, and the cross-sectional hardness of a side portion of a crown cap after crown cap forming was greater than 220 Hv; and the crown cap formability was poor, and the pressure resistance was poor.
  • steel sheets of Steel Sheet Nos. 43 and 53 were such that since the rolling reduction ratio during secondary cold rolling was greater than 12%, the yield strength of the steel sheets in the rolling direction thereof was greater than 600 MPa, and the cross-sectional hardness of a side portion of a crown cap after crown cap forming was greater than 220 Hv; the crown cap formability was poor, and the pressure resistance was poor.
  • a steel sheet of Steel Sheet No. 44 was such that since the rolling reduction ratio during secondary cold rolling was less than 1.0%, the yield strength of the steel sheet in the rolling direction thereof was less than 420 MPa, the cross-sectional hardness of a side portion of a crown cap after crown cap forming was less than 180 Hv, and the pressure resistance was low.
  • a steel sheet of Steel Sheet No. 54 was such that since the retention time in a temperature range from 400 °C to 580 °C was less than 30 seconds although the cooling stop temperature C was in the temperature range from 400 °C to 580 °C, the steel sheet was hard, the yield strength of the steel sheet in the rolling direction thereof was greater than 600 MPa, the cross-sectional hardness of a side portion of a crown cap after crown cap forming was greater than 220 Hv; the crown cap formability was poor, and the pressure resistance was poor.

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Claims (4)

  1. Kaltgewalztes Stahlblech für Kronkorken, das eine Zusammensetzung hat, die Folgendes enthält:
    C: 0,02 % bis 0,08 %,
    Si: 0,02% oder weniger,
    Mn: 0,10% bis 0,60 %,
    P: 0,020 % oder weniger,
    S: 0,020 % oder weniger,
    Al: 0,01 % bis 0,06 %, und
    N: 0,0100 % bis 0,0180 %
    auf die Masse bezogen, der Rest ist Fe und unvermeidbare Verunreinigungen,
    worin N insgesamt (N als AlN) 0,0090 % bis 0,0170 % beträgt, die maximale Korngröße eines Carbids 0,3 µm oder
    mehr und 2,0 µm oder weniger in einem Querschnitt in einer Walzrichtung beträgt, gemessen entsprechend der Beschreibung, und
    die Streckgrenze, gemessen an einer Zugfestigkeitsprobe mit einer Größe von JIS #5 entsprechend "JIS Z 2241" und nach einer 15-minütigen Erwärmung bei 210 °C, beträgt 420 MPa bis 600 MPa in Walzrichtung,
    wobei die N-Gesamtmenge die Gesamtmenge von N und das N als AlN die in Form von AlN vorhandene Menge von N ist, wobei das in AlN vorhandene N durch Auflösen und Extrahieren von AlN durch eine 10 %ige Br-Methanollösung bestätigt wird und
    das in AlN vorhandene N quantitativ durch Absorptionsmessung analysiert wird.
  2. Verfahren zur Herstellung eines Stahlblechs für Kronkorken, umfassend:
    einen Warmwalzschritt zur Durchführung des Wickelns bei einer Temperatur von 670 °C oder weniger nach dem Fertigwalzen beim Warmwalzen eines Stahlmaterials mit einer Zusammensetzung nach Anspruch 1; einen primären Kaltwalzschritt zur Durchführung des Kaltwalzens nach dem Warmwalzschritt;
    einen kontinuierlichen Glühschritt, bei dem nach dem primären Kaltwalzschritt ein Erwärmen mit einer durchschnittlichen Aufheizrate von 10 °C/s bis 30 °C/s in einem Temperaturbereich A von 500 °C bis 600 °C in einem Erwärmungsverlauf durchgeführt wird, Glühen bei einer Glühtemperatur B in einem Temperaturbereich von 620 °C bis 740 °C, Abkühlen von der Glühtemperatur B auf eine Kühlstopptemperatur C in einem Temperaturbereich von 400 °C bis 580 °C mit einer durchschnittlichen Abkühlgeschwindigkeit von 20 °C/s oder mehr und Halten im Temperaturbereich von 400 °C bis 580 °C für eine Verweilzeit von 30 Sekunden bis 90 Sekunden, nachdem die Abkühlung mit der oben genannten durchschnittlichen Abkühlgeschwindigkeit gestoppt wurde; und
    einen sekundären Kaltwalzschritt zur Durchführung des Kaltwalzens mit einem Walzreduktionsverhältnis von 1,0 % bis 12 % nach dem kontinuierlichen Glühen.
  3. Kronkorken, der unter Verwendung des Stahlblechs für Kronkorken entsprechend Anspruch 1 geformt wurde.
  4. Kronkorken nach Anspruch 3, wobei die Querschnittshärte eines Seitenteils des Kronkorkens 180 Hv bis 220 Hv beträgt.
EP17855743.5A 2016-09-29 2017-09-14 Stahlblech für kronkorken, herstellungsverfahren dafür und kronkorken Active EP3476964B1 (de)

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