WO2018061787A1 - 王冠用鋼板およびその製造方法並びに王冠 - Google Patents

王冠用鋼板およびその製造方法並びに王冠 Download PDF

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WO2018061787A1
WO2018061787A1 PCT/JP2017/033179 JP2017033179W WO2018061787A1 WO 2018061787 A1 WO2018061787 A1 WO 2018061787A1 JP 2017033179 W JP2017033179 W JP 2017033179W WO 2018061787 A1 WO2018061787 A1 WO 2018061787A1
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Prior art keywords
crown
less
rolling
temperature
steel plate
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PCT/JP2017/033179
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English (en)
French (fr)
Japanese (ja)
Inventor
房亮 假屋
智也 平口
克己 小島
雅資 梅本
雅巳 辻本
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Ｊｆｅスチール株式会社
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Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to EP17855743.5A priority Critical patent/EP3476964B1/en
Priority to MX2019002404A priority patent/MX2019002404A/es
Priority to PL17855743T priority patent/PL3476964T3/pl
Priority to MYPI2019000961A priority patent/MY197920A/en
Priority to JP2018542371A priority patent/JP6601571B2/ja
Publication of WO2018061787A1 publication Critical patent/WO2018061787A1/ja
Priority to PH12019550011A priority patent/PH12019550011A1/en
Priority to ZA2019/00744A priority patent/ZA201900744B/en
Priority to CONC2019/0001705A priority patent/CO2019001705A2/es

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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 crown steel plate having excellent shape uniformity and pressure resistance against internal pressure, a manufacturing method thereof, and a crown made by using the crown steel plate, which are used for beer bottles and the like.
  • a metal stopper called a crown is widely used for containers for beverages such as soft drinks and alcoholic beverages.
  • a crown is manufactured by press-molding a thin steel plate, and consists of a disk-shaped part that closes the mouth of the bottle and a bowl-shaped part around it. Seal the jar by caulking.
  • the crown In bottles filled with beer, carbonated drinks, etc., internal pressure is generated by the contents.
  • the crown needs to have high pressure strength so that when the internal pressure increases due to temperature changes or the like, the crown will not deform and the bottle will not be sealed and the contents will not leak.
  • the strength of the material is sufficient, if the moldability is poor, the shape of the jar will be non-uniform, and even if it is caulked to the mouth of the bottle, sufficient sealing performance may not be obtained, so moldability is improved. It must also be excellent.
  • SR (Single Reduced) steel plates are mainly used as thin steel plates for the crown material.
  • annealing is performed and temper rolling is performed.
  • the sheet thickness of conventional steel plates for crowns is generally 0.22 mm or more, and sufficient compressive strength and formability are ensured by applying SR material made of mild steel used for food and beverage cans and the like. It was possible.
  • the conventional pressure-resistant strength evaluation was a method of measuring the pressure at which the crown comes off by increasing the internal pressure of the bottle at a constant speed by caulking the crown into the bottle and injecting air from the top of the crown. Then, the pressure is maintained at a predetermined pressure for a certain time, and the internal pressure is further increased.
  • Patent Document 1 contains, by mass%, N: 0.0040 to 0.0300%, Al: 0.005 to 0.080%, 0.2% proof stress in a tensile test using a JIS No. 5 test piece: 430 MPa.
  • Patent Document 2 by mass%, 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%, B: 0.0002 to 0.0050% Further disclosed is a steel plate for a high-strength, high-workability can, characterized by containing 0.01 to 1.00% in terms of area ratio of crystal grains having a degree of elongation of crystal grains of 5.0 or more in the cross section in the rolling direction. ing.
  • Patent Document 3 by mass, 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: 0.015% to 0.020% or less, B: 0.0002 to 0.0050%
  • N contained as AlN is 0.0060% or less, and in the cross section in the rolling direction, the average crystal grain size is 5.00 ⁇ m or more, the elongation of crystal grains is 2.50 or less, and the tensile strength
  • a steel sheet for a high-strength, high-workability can that has a breaking elongation of 7% or more and 550 MPa or more is disclosed.
  • Patent Document 1 evaluates flange formability and can strength after making cans into a two-piece can, but nothing is said about crown molding and crown pressure strength after the crown is plugged into a bottle.
  • the steel sheet described in Patent Document 2 is also strengthened by N, but it is difficult to achieve both the pressure strength required for the crown and formability.
  • crown molding is a process. Since the can body is mainly molded by different bending methods, it is not suitable for forming crowns, which are mainly drawn.
  • the present invention has been made in view of the above problems, and an object of the present invention is to provide a steel plate for a crown having sufficient pressure resistance and formability even when it is thinned, a manufacturing method thereof, and a crown.
  • the N total is a total amount of N
  • the N as AlN is an N amount existing as AlN.
  • Annealing is performed at an annealing temperature B in the temperature range, and the cooling is performed from the annealing temperature B to a cooling stop temperature C in a temperature range of 400 ° C. to 580 ° C. at an average cooling rate of 20 ° C./s or more, and cooling at the average cooling rate
  • a continuous annealing step in which the residence time for retaining in the temperature range from 400 ° C. to 580 ° C. is 30 seconds to 90 seconds, and after the continuous annealing step, the rolling rate is 1.0 to 12%. Having a secondary cold rolling process for cold rolling Method of manufacturing a crown for steel sheet and butterflies.
  • [3] A crown produced by using the crown steel plate according to [1].
  • [4] The crown according to [3], wherein the cross-sectional hardness of the side surface portion of the crown is 180 Hv or more and 220 Hv or less.
  • the present invention it is possible to provide a crown steel plate having sufficient pressure strength and formability even when it is thinned, a manufacturing method thereof, and a crown.
  • the crown steel plate according to the present invention is, in mass%, C: 0.02% to 0.08%, Si: 0.02% or less, Mn: 0.10% to 0.60%, P: 0 0.020% or less, S: 0.020% or less, Al: 0.01% or more and 0.06% or less, N: 0.0100% or more and 0.0180% or less, and the balance from Fe and inevitable impurities N total- (N as AlN) is 0.0090% or more and 0.0170% or less, and the maximum grain size of carbide is 2.0 ⁇ m or less in the cross section in the rolling direction, yielding in the rolling direction.
  • the strength is 420 MPa or more and 600 MPa or less.
  • the unit of content “%” is all “mass%”.
  • C content 0.02% to 0.08%
  • the C content is less than 0.02%, the steel sheet strength decreases, the cross-sectional hardness of the crown side surface after crown forming decreases, and the pressure resistance decreases.
  • the content of C exceeds 0.08%, the strength of the steel sheet becomes remarkably high, so that the shape of the crown of the formed crown becomes non-uniform and the shape becomes defective.
  • the maximum grain size of the carbide in the cross section in the rolling direction is increased, the shape of the crown of the molded crown becomes non-uniform, resulting in a defective shape and a decrease in pressure strength. Therefore, the C content is 0.02% or more and 0.08% or less.
  • the C content is preferably 0.03% or more. Further, the content of C is preferably 0.06% or less.
  • Si content 0.02% or less
  • the Si content is set to 0.02% or less in order to cause deterioration of the surface treatment property and corrosion resistance of the steel plate.
  • the lower limit of the Si content is not particularly limited, but excessively lowering Si causes an increase in steelmaking costs, so the Si content is preferably 0.004% or more.
  • Mn content 0.10% or more and 0.60% or less
  • Mn content is 0.10% or more.
  • Mn content is set to 0.60% or less.
  • the Mn content is preferably 0.20% or more.
  • S content 0.020% or less
  • S is a harmful element that forms inclusions in the steel sheet and causes a decrease in hot ductility and corrosion resistance of the steel sheet. Therefore, the upper limit of the S content is 0.020%.
  • Al content 0.01% or more and 0.06% or less
  • Al is an element necessary as a deoxidizer during steelmaking.
  • the Al content is less than 0.01%, deoxidation is insufficient, inclusions increase, and the moldability of the crown deteriorates.
  • Al forms N and AlN in the steel and reduces the solute N in the steel.
  • the Al content exceeds 0.06%, the amount of N total- (N as AlN) described later cannot be obtained sufficiently, and the steel sheet strength is lowered. Therefore, the Al content is 0.01% or more and 0.06% or less.
  • the Al content is 0.01% or more and 0.04% or less.
  • N content 0.0100% or more and 0.0180% or less
  • the N content is set to 0.0100% or more and 0.0180% or less.
  • the N content is preferably 0.0135% or more.
  • N in steel is mainly present as AlN. Therefore, the N amount (N as AlN) present as AlN is subtracted from the total amount of N (N total) (N total- (N as AlN )) Was regarded as the amount of dissolved N.
  • the content of N total- (N as AlN) is less than 0.0090%, the strength of the steel sheet is lowered and the pressure resistance is lowered.
  • the content of N total- (N as AlN) exceeds 0.0170%, the steel sheet strength excessively increases, the crown formability decreases, and the pressure resistance decreases. Therefore, the content of N total- (N as AlN) is set to 0.0090% or more and 0.0170% or less. Preferably, the content is 0.0110% or more and 0.0170% or less.
  • the amount of N present as AlN can be confirmed by, for example, dissolving and extracting AlN using a 10% Br-methanol solution and performing quantitative analysis of N present as AlN by absorptiometry. it can.
  • the balance is Fe and inevitable impurities.
  • the crown steel plate according to the present invention has a structure containing carbides, and the maximum particle size of carbides in the cross section in the rolling direction is 2.0 ⁇ m or less.
  • carbides in the steel exist mainly as cementite. If the maximum grain size of the carbide in the cross section in the rolling direction exceeds 2.0 ⁇ m, the shape of the crown of the molded crown becomes non-uniform, resulting in a defective shape and a decrease in pressure strength. The reason for this is not clear, but is presumed as follows.
  • the crown of the crown is a part that undergoes tension and compression, or tension and compression superimposed in the rolling direction of the steel sheet, the direction perpendicular to the rolling direction and the thickness direction, there is coarse carbide Then, it is thought that distortion concentrates locally during molding, resulting in a shape defect.
  • the maximum particle size of carbide (cementite) is less than 0.3 ⁇ m, the steel sheet becomes excessively strong and the formability of the crown may be impaired. Therefore, the maximum particle size of cementite is preferably 0.3 ⁇ m or more.
  • the cementite metallographic structure is obtained by polishing a plate thickness section parallel to the rolling direction of the steel plate, then corroding with a corrosive solution (3% by volume nital), and using a scanning electron microscope (SEM) with a scanning electron microscope (SEM) at a magnification of 2000 times a plate thickness of 1 / 4 position (in the above cross section, 1/4 position from the surface in the plate thickness direction), cementite was identified by visual judgment using a structural photograph taken with SEM, and each cementite particle size was analyzed for image analysis. Thus, the area of each cementite was obtained and converted to an equivalent circle diameter to obtain each cementite particle diameter. The largest cementite particle size in 10 fields of view was defined as the maximum particle size of the carbide.
  • the crown steel plate of the present invention is required to have a pressure strength that prevents the crown from coming off against the internal pressure of the bottle.
  • the steel plate for crowns that has been used conventionally has a thickness of 0.22 mm or more, but a higher strength than before is required in order to reduce the thickness to 0.20 mm or less.
  • the yield strength in the rolling direction of the steel sheet is less than 420 MPa, it is difficult to give sufficient pressure resistance to the thinned crown as described above.
  • the yield strength exceeds 600 MPa, the compressive stress in the circumferential direction of the crown of the crown increases, and the yield strength exceeds the critical buckling strength at the early stage of the crown molding.
  • the yield strength in the rolling direction is set to 420 MPa or more and 600 MPa or less.
  • the yield strength is preferably 450 MPa or more and 600 MPa or less.
  • the yield strength can be measured by a metal material tensile test method shown in “JIS Z 2241”.
  • the desired yield strength is adjusted by adjusting the component composition, adjusting the coiling temperature of hot rolling, the average heating rate after cold rolling, the annealing temperature, the average cooling rate after annealing, and the cooling stop temperature, after cooling stop. It can be obtained by adjusting the holding time.
  • the yield strength of 420 MPa or more and 600 MPa or less is the above component composition
  • the coiling temperature in the hot rolling process is 670 ° C. or less
  • the continuous annealing process after the cold rolling process is 500 to 600 ° C. in the heating process.
  • An average heating rate in the temperature range A is set to 10 ° C./s or more and 30 ° C./s or less
  • annealing is performed at an annealing temperature B in a temperature range of 620 to 740 ° C.
  • the yield strength in the direction perpendicular to the rolling direction of the steel sheet is preferably 450 MPa or more and 600 MPa or less.
  • the steel plate for the crown is punched into a circular blank and then formed into a crown by press forming. After molding, the crown is caulked to the bottle mouth by a stopper, so that the sealing performance after the stopper is maintained. If the strength of the side surface after the crown molding is low, the crown may come off from the bottle mouth when held in a state where the internal pressure of the bottle is increased, leading to leakage of the contents of the bottle.
  • the strength of the side surface after crown molding is closely related to the Vickers hardness value of the cross section. If the cross sectional hardness of the crown side surface is less than 180 Hv, the strength of the side surface of the crown is reduced and the sealing performance is reduced. The pressure strength at is reduced.
  • the cross-sectional hardness of the crown side surface portion is more than 220 Hv, the strength of the crown side surface portion becomes excessively high, so that the side surface portion is cracked.
  • the cross-sectional hardness of the crown side surface is set to 180 Hv or more and 220 Hv or less.
  • the cross-sectional hardness of the crown side portion is preferably 190 Hv or higher and 220 Hv or lower.
  • the cross-sectional hardness of the crown side portion can be evaluated by the method shown in “JIS Z 2244”.
  • the cross-sectional hardness evaluation position of the crown side surface portion is the crown side surface cross section between the crown and the heel of the crown, and the measuring method is Vickers hardness.
  • the evaluation position is centered on a position (H / 2) that is 1/2 of the crown height H, one point at the center, two points in the direction of the crown upper surface, and the direction below the crown.
  • the total score was 2 points.
  • the Vickers indentation load was 100 gf, and the interval between the points was 3d (d: diagonal length of the indentation).
  • the average value of the five Vickers hardness values was taken as the cross-sectional hardness of the crown side surface.
  • the desired cross-sectional hardness is adjusted by adjusting the composition of components, adjusting the coiling temperature of hot rolling, the average heating rate after cold rolling, the annealing temperature, the average cooling rate after annealing, and adjusting the secondary cold rolling rate. It can be obtained by forming a crown from the crown steel plate obtained by doing so.
  • the cross-sectional hardness of the crown side surface portion of 180 Hv or more and 220 Hv or less is the above component composition, the coiling temperature in the hot rolling process is 670 ° C.
  • An average heating rate in a temperature range A of 500 to 600 ° C. is set to 10 ° C./s or more and 30 ° C./s or less, and annealing is performed at an annealing temperature B in a temperature range of 620 to 740 ° C., and 20 ° C./s or more from the annealing temperature B
  • the cooling time is cooled to the cooling stop temperature C in the temperature range of 400 ° C. or more and 580 ° C. or less at an average cooling rate of, and the residence time is retained in the temperature range of 400 ° C. or more and 580 ° C. or less after stopping the cooling at the average cooling rate.
  • the steel plate for crowns of the present invention is a steel material (steel slab) having the above component composition, after a hot rolling step of finishing rolling in hot rolling at a temperature of 670 ° C. or lower, and after the hot rolling step, A pickling step for pickling as necessary, a primary cold rolling step for cold rolling after the pickling step, and a temperature range A of 500 to 600 ° C. in the heating process after the primary cold rolling step.
  • Cooling to the cooling stop temperature C in the temperature range of 580 ° C. or lower and stopping the cooling at the average cooling rate, the residence time for staying in the temperature range of 400 ° C. or higher and 580 ° C. or lower is 30 seconds or longer and 90 seconds or shorter.
  • the temperature is the surface temperature of a steel plate or the like.
  • the average heating rate and average cooling rate are values obtained by calculation based on the surface temperature.
  • the average heating rate in the temperature range A of 500 to 600 ° C. in the heating process is expressed as ((600 ° C.-500 ° C.) / 500 ° C. to 600 ° C. heating time).
  • the average cooling rate from the annealing temperature B to the cooling stop temperature C is represented by ((annealing temperature B ⁇ cooling stop temperature C) / cooling time from the annealing temperature B to the cooling stop temperature C).
  • the molten steel is adjusted to the above chemical components by a known method using a converter or the like, for example, a slab is formed by a continuous casting method. Subsequently, it is preferable that the slab is roughly rolled hot.
  • the method of rough rolling is not limited, but in order to secure N total- (N as AlN) of 0.0090% or more, the heating temperature of the slab is preferably 1200 ° C. or more. In order to further increase N total- (N as AlN), the slab heating temperature is more preferably 1230 ° C. or higher.
  • the finish rolling temperature in the hot rolling process is preferably 850 ° C. or higher from the viewpoint of the stability of the rolling load. On the other hand, raising the finish rolling temperature more than necessary may make it difficult to produce a thin steel sheet. Specifically, the finish rolling temperature is preferably in the temperature range of 850 to 960 ° C.
  • the coiling temperature in the hot rolling process exceeds 670 ° C., the amount of AlN precipitated in the steel after coiling increases, and the amount of N total- (N as AlN) is less than 0.0090%.
  • the yield strength in the rolling direction is less than 420 MPa, and the cross-sectional hardness of the crown side surface after crown molding may be less than 180 Hv.
  • the coiling temperature in the hot rolling process exceeds 670 ° C.
  • the maximum particle size of carbide in the cross section in the rolling direction exceeds 2.0 ⁇ m, and the shape of the crown collar becomes uneven during crown molding, resulting in poor shape. It may cause, which is not preferable. Therefore, the coiling temperature in the hot rolling process is 670 ° C. or less.
  • the coiling temperature in the hot rolling process is preferably 640 ° C. or less.
  • the yield strength in the rolling direction of the steel sheet exceeds 600 MPa, and the cross-sectional hardness of the crown side surface after crown forming may exceed 220 Hv. Is preferred.
  • the pickling is not particularly limited as long as the surface scale can be removed. Further, instead of pickling, a method such as mechanical removal may be used.
  • the rolling reduction in the primary cold rolling step is not particularly limited, but is preferably 85 to 94% in order to make the thickness of the steel sheet after the secondary cold rolling 0.20 mm or less.
  • the temperature range A of 500 to 600 ° C. is heated at an average heating rate of 10 ° C./s to 30 ° C./s.
  • the temperature range A is heated at an average heating rate of less than 10 ° C./s, precipitation of AlN occurs during the heating, and the amount of N total- (N as AlN) is less than 0.0090%, which is in the rolling direction of the steel sheet.
  • the yield strength is less than 420 MPa, and the cross-sectional hardness of the crown side surface after crown molding is less than 180 Hv, which is not preferable because the pressure strength decreases. Therefore, the average heating rate in the temperature range A is 10 ° C./s or more.
  • the average heating rate in the temperature range A is 30 ° C./s or less.
  • the average heating rate in the temperature range A exceeds 30 ° C./s, the annealing temperature becomes difficult to control, and there is a possibility that overheating may occur and the energy cost increases.
  • the annealing temperature B is a temperature range of 620 to 740 ° C.
  • the annealing temperature B is less than 620 ° C.
  • the steel sheet becomes hard due to an incomplete recrystallized structure, so the yield strength in the rolling direction of the steel sheet exceeds 600 MPa, and the cross-sectional hardness of the crown side surface after crown forming Over 220 Hv, the crown moldability is inferior, and the pressure strength is reduced.
  • the annealing temperature B is set to a temperature range of 620 to 740 ° C.
  • the annealing temperature B is preferably 640 ° C. or higher in order to achieve a good balance between the moldability of the crown and the pressure strength.
  • the annealing temperature B is preferably 720 ° C. or lower.
  • cooling is performed from the annealing temperature B to a cooling stop temperature C in a temperature range of 400 ° C. or more and 580 ° C. or less at an average cooling rate of 20 ° C./s or more.
  • the average cooling rate is less than 20 ° C./s
  • AlN is excessively precipitated during cooling
  • the amount of N total- (N as AlN) is less than 0.0090%
  • the yield strength in the rolling direction of the steel sheet is less than 420 MPa.
  • the cross-sectional hardness of the side surface portion of the crown after crown molding becomes less than 180 Hv, and the pressure resistance may be reduced. Therefore, an average cooling rate shall be 20 degrees C / s or more.
  • the average cooling rate is 40 ° C./s or more.
  • the upper limit of the average cooling rate is not particularly limited, but when the average cooling rate exceeds 150 ° C./s, not only the increase in steel sheet strength due to N total- (N as AlN) is saturated, but also into the ferrite grains.
  • the average cooling rate is preferably 150 ° C./s or less because ductility may be reduced due to excessive carbide precipitation and cracking may occur in crown molding. More preferably, the average cooling rate is 120 ° C./s or less.
  • the cooling stop temperature C is a temperature range of 400 ° C or higher and 580 ° C or lower.
  • the cooling stop temperature is higher than 580 ° C., AlN is excessively precipitated, the amount of N total- (N as AlN) is less than 0.0090%, and the yield strength in the rolling direction of the steel sheet is less than 420 MPa. In some cases, the cross-sectional hardness of the side surface portion of the crown becomes less than 180 Hv, and the compressive strength decreases.
  • the cooling stop temperature is 550 ° C. or lower.
  • the lower limit of the cooling stop temperature is 400 ° C. If the cooling stop temperature is excessively low, the steel sheet is excessively hardened, the shape becomes non-uniform by crown molding, and the pressure resistance may be reduced.
  • the cooling stop temperature is 450 ° C. or higher.
  • the residence time in the temperature range of 400 ° C. to 580 ° C. is set to 30 seconds to 90 seconds.
  • the residence time in the temperature range of 400 ° C. or higher and 580 ° C. or lower exceeds 90 seconds, the carbide grows as C diffuses into the carbide in the steel, and the maximum particle size of the carbide in the cross section in the rolling direction exceeds 2.0 ⁇ m.
  • the residence time in the temperature range from 400 ° C. to 580 ° C. is preferably 75 seconds or less.
  • the minimum of the residence time in the temperature range of 400 degreeC or more and 580 degrees C or less shall be 30 second or more.
  • the residence time is less than 30 seconds, the steel sheet is excessively hardened, the shape becomes non-uniform by crown molding, and the pressure strength decreases.
  • the rolling reduction of secondary cold rolling following the continuous annealing process is 1.0 to 12%.
  • the rolling reduction of secondary cold rolling is less than 1.0%, the cross-sectional hardness of the crown side surface after crown forming is less than 180 Hv, and the pressure strength is reduced.
  • the reason for this is not clear, but is presumed as follows.
  • dislocations introduced by secondary cold rolling are fixed by solid solution during the heat treatment process in paint baking. In the subsequent tension, the fixed dislocation becomes an obstacle at the time of deformation, and the strength increases.
  • the rolling reduction of secondary cold rolling is set to 1.0 to 12%.
  • the reduction ratio of the secondary cold rolling is preferably 3.0% or more. Further, the rolling reduction of secondary cold rolling is preferably 10% or less.
  • the cold-rolled steel sheet obtained as described above is then subjected to plating treatment such as tin plating, chromium plating, nickel plating, etc. on the surface of the steel sheet, for example, by electroplating, if necessary, to form a plating layer, and crown Steel plate.
  • plating treatment such as tin plating, chromium plating, nickel plating, etc.
  • the film thickness of surface treatments, such as plating is sufficiently small with respect to plate
  • the crown steel sheet of the present invention can have sufficient pressure strength and formability even if it is thinned.
  • the crown of the present invention is formed by using the above-described crown steel plate.
  • the crown is mainly composed of a disk-shaped part that closes the mouth of the bottle and a bowl-shaped part provided around the disk-shaped part.
  • the crown of the present invention can be formed by press molding after being punched into a circular blank. Since the crown of the present invention is manufactured from a crown steel plate having sufficient yield strength and excellent formability, it is excellent in pressure resistance as a crown even if it is thinned. It also has the effect of reducing emissions.
  • a steel slab was obtained by containing the component composition shown in Table 1, with the balance being made of Fe and unavoidable impurities in a converter and continuously cast.
  • the steel slab obtained here was reheated to 1220 ° C. and then hot-rolled at a rolling start temperature of 1150 ° C. to obtain the finish rolling temperature shown in Table 2, and wound at the winding temperature. After hot rolling, pickling was performed.
  • primary cold rolling was performed at the rolling reduction shown in Table 2, and continuous annealing was performed under the conditions shown in Table 2, followed by secondary cold rolling at the rolling reduction shown in Table 2.
  • the obtained steel plate was continuously subjected to normal Cr plating to obtain tin-free steel.
  • the steel sheet obtained as described above was subjected to a heat treatment equivalent to coating baking at 210 ° C. for 15 minutes, and then subjected to a tensile test and a measurement of the cross-sectional hardness of the crown side surface.
  • the tensile test was performed according to “JIS Z 2241” using a JIS No. 5 size tensile test piece, and the yield strength in the rolling direction was measured.
  • the cross-sectional hardness of the crown side portion was formed into a crown using a steel plate, and the Vickers hardness was measured by a method in accordance with “JIS Z 2244”.
  • the crown uses a circular blank with a diameter of 37 mm, and the dimensions of the three crowns described in “JIS S 9017” (obsolete standard) by press working (outer diameter 32.1 mm, height 6.5 mm, number of ridges 21) It was formed by molding.
  • the evaluation position was a total of 5 points, with one point at the center, 2 points in the crown upper surface direction, and 2 points in the crown lower direction, centering on the 1/2 position of the crown height.
  • the Vickers indentation load was 100 gf, and the interval between the points was 3d (d: diagonal length of the indentation).
  • the average value of the five Vickers hardness values was taken as the cross-sectional hardness of the crown side surface.
  • the grain size of carbides in the cross section in the rolling direction is determined by polishing a plate thickness cross section parallel to the rolling direction of the steel sheet, then corroding with a corrosive liquid (3% by volume nital), and scanning electron microscope (SEM) over 10 fields of view at 2000 times magnification.
  • the sheet thickness is 1 ⁇ 4 position (in the cross section, 1 ⁇ 4 position from the surface in the sheet thickness direction), and cementite is identified by visual judgment using a structure photograph taken with SEM. Then, the area of each cementite was obtained by image analysis, and converted to an equivalent circle diameter to obtain each cementite particle diameter.
  • the largest cementite particle size in 10 fields of view was defined as the maximum particle size of carbide in the cross section in the rolling direction.
  • the resulting steel sheet was molded into a crown and the crown formability was evaluated.
  • a circular blank with a diameter of 37 mm it was molded into the dimensions of the three crowns described in “JIS S 9017” (obsolete standard) (outer diameter: 32.1 mm, height: 6.5 mm, number of ridges: 21) .
  • the crown formability is evaluated by measuring the length L of each ridge 2 of the crown, ⁇ for a crown whose standard deviation of L value is 0.1 or less, and 0 for standard deviation of L value. ..> 1 crown was rated as x.
  • the said evaluation was implemented with five crowns, and the standard deviation of L value was 0.1 or less by all (5), and it was set as x (pass) other than that.
  • the pressure resistance test was conducted using a molded crown. Place a vinyl chloride liner on the inside of the top of the crown, plug it into a commercial beer bottle, drill a small hole in the top of the crown, and install a device that sends air into the bottle. Inside the bottle at a speed of 5 psi / second The internal pressure in the bottle was increased by injecting air into the bottle. As the pressure increase condition in the bottle, the pressure in the bottle was increased to 100 psi (pressure increase operation), held at 100 psi for 1 minute (hold operation), and increased again at 5 psi / second (repressurization operation).
  • the internal pressure value in the bottle when the air leaks from the gap between the crown and the bottle mouth or when the crown is removed from the bottle mouth (unplugging).
  • the pressure resistance value of the crown was evaluated as ⁇ when the pressure resistance value was equal to or higher than that of the conventional crown, and ⁇ when the pressure resistance value of the conventional crown was not reached. Since it was difficult to evaluate further after x, it was marked as-in the table.
  • a SR (Single Reduced) steel plate having a thickness of 0.22 mm was used as a conventional crown.
  • steel plate No. which is an example of the present invention.
  • Steel plates 1 to 15 are components within the range specified in the present invention, the yield strength in the rolling direction was 420 MPa or more and 600 MPa or less, and the maximum grain size of carbide in the rolling direction cross section was 2.0 ⁇ m or less.
  • Steel plate No. The crown molded from 1 to 15 had a cross-sectional hardness of 180 Hv or more and 220 Hv or less after the crown molding.
  • the steel plates for crowns 1 to 15 had good crown formability and pressure strength.
  • steel plate No. which is a comparative example. Since the steel plate No. 16 has a C content of less than 0.02%, the yield strength in the rolling direction of the steel plate is less than 420 MPa, the cross-sectional hardness of the crown side surface after crown forming is less than 180 Hv, and the crown formability is good However, it was found that the pressure strength is insufficient.
  • Steel plate No. Steel plate No. 17 has a C content exceeding 0.08%, so the yield strength in the rolling direction exceeds 600 MPa, the maximum grain size of carbide in the cross section in the rolling direction exceeds 2.0 ⁇ m, and the crown side surface after crown molding Since the cross-sectional hardness of the part exceeds 220 Hv, it was found that the crown moldability was inferior and the pressure resistance was insufficient.
  • the 20 steel plate has an N content of less than 0.0100%, so N total- (N as AlN) is less than 0.0090%, the yield strength in the rolling direction of the steel plate is less than 420 MPa, and Since the cross-sectional hardness of the crown side surface portion was less than 180 Hv, it was found that the pressure strength was insufficient.
  • Steel plate No. Steel plate No. 21 has an N content exceeding 0.0180%, so N total- (N as AlN) exceeds 0.0170%, the yield strength in the rolling direction of the steel plate exceeds 600 MPa, and the crown after crown forming Since the cross-sectional hardness of the side surface portion exceeds 220 Hv, it was found that the molded crown had a defective shape and the pressure resistance was insufficient.
  • Steel plate No. 22 has a Si content of more than 0.02%.
  • Steel plate No. 23 has a P content exceeding 0.020%, so the yield strength in the rolling direction exceeds 600 MPa, and the cross-sectional hardness of the crown side surface after crown forming exceeds 220 Hv. I found out that it was insufficient.
  • the steel No. shown in Table 1 was used.
  • Steel slabs were obtained by containing B, G, K, and S component compositions, with the balance being made of Fe and unavoidable impurities in a converter and continuous casting.
  • the manufacturing conditions shown in Table 3 were applied to the steel slab obtained here.
  • the obtained steel plate was continuously subjected to normal Cr plating to obtain tin-free steel.
  • Steel plate No. obtained by the above. 24 to 56 were subjected to heat treatment equivalent to coating baking at 210 ° C. for 15 minutes, and then the yield strength in the rolling direction, the maximum grain size of carbides in the cross section in the rolling direction, and the crown side surface after crown molding by the above-described methods.
  • the cross-sectional hardness was determined.
  • crown formability and pressure strength were evaluated by the methods described above.
  • steel plate No. which is an example of the present invention.
  • Steel sheets 27 to 28, 30, 32 to 33, 35, 37 to 39, 41 to 42, 45 to 48, and 50 to 52 have a maximum carbide grain size of 2.0 ⁇ m or less in the cross section in the rolling direction.
  • steel plate No. which is a comparative example.
  • the steel plate No. 24 has a coiling temperature of over 670 ° C., so the amount of N total- (N as AlN) is less than 0.0090%, the yield strength in the rolling direction of the steel plate is less than 420 MPa, and the crown side surface after crown forming
  • the cross section hardness of the part is less than 180 Hv, the maximum grain size of carbide in the cross section in the rolling direction is over 2.0 ⁇ m, the shape of the crown of the crown becomes non-uniform at the time of crown molding, the shape is poor, and the crown moldability is inferior It was also found that the pressure strength was inferior.
  • the average heating rate is less than 10 ° C./s in the temperature range A of 500 to 600 ° C., so the amount of N total- (N as AlN) is less than 0.0090%, and the rolling direction of the steel plate It was found that the yield strength was less than 420 MPa, the cross-sectional hardness of the crown side surface after crown molding was less than 180 Hv, and the pressure strength was inferior.
  • the steel plate No. 26 has an annealing temperature of less than 620 ° C., so the steel plate becomes hard due to an incomplete recrystallization structure, the yield strength in the rolling direction of the steel plate exceeds 600 MPa, and the cross-section of the crown side portion after crown forming It was found that the hardness was over 220 Hv, the crown moldability was inferior, and the pressure strength was inferior.
  • Steel plate No. No. 29 steel plate has an annealing temperature exceeding 740 ° C., so the maximum grain size of carbides in the cross section in the rolling direction is over 2.0 ⁇ m, and the shape of the heel is non-uniform in the formation of the crown. It was.
  • Steel plate No. Steel plate No. 31 has an average heating rate of more than 30 ° C./s in the temperature range A of 500 to 600 ° C., so that the steel plate becomes hard, the yield strength in the rolling direction of the steel plate exceeds 600 MPa, and the crown side surface after crown forming It was found that the cross-sectional hardness was over 220 Hv, the crown moldability was inferior, and the pressure resistance was inferior.
  • steel plate No. The residence times in the temperature range of 400 ° C. or more and 580 ° C. or less in the steel plates 36 and 40 indicate residence times at the respective cooling stop temperatures C.
  • the steel plate No. 44 has a rolling reduction of secondary cold rolling of less than 1.0%, so the yield strength in the rolling direction of the steel plate is less than 420 MPa, and the cross-sectional hardness of the crown side surface after crown forming is less than 180 Hv, It was found that the pressure strength decreased.
  • the cooling stop temperature C is in the temperature range of 400 ° C. or higher and 580 ° C. or lower
  • the residence time in the temperature range of 400 ° C. or higher and 580 ° C. or lower is less than 30 seconds. It was found that the yield strength in the rolling direction was over 600 MPa, the cross-sectional hardness of the crown side surface after crown molding was over 220 Hv, the crown formability was poor, and the pressure resistance was poor.
  • the 55 and 56 steel sheets have an Al content exceeding 0.06%, so N total- (N as AlN) is less than 0.0090%, the yield strength in the rolling direction of the steel sheet is less than 420 MPa, and after crown forming It was found that the cross-sectional hardness of the crown side surface portion was less than 180 Hv, and the pressure strength was inferior.

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PCT/JP2017/033179 2016-09-29 2017-09-14 王冠用鋼板およびその製造方法並びに王冠 WO2018061787A1 (ja)

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EP17855743.5A EP3476964B1 (en) 2016-09-29 2017-09-14 Steel sheet for crown caps, production method therefor, and crown cap
MX2019002404A MX2019002404A (es) 2016-09-29 2017-09-14 Lamina de acero para corcholatas, metodo para fabricar las mismas, y corcholata.
PL17855743T PL3476964T3 (pl) 2016-09-29 2017-09-14 Blacha stalowa na zamknięcie koronowe, sposób jej wytwarzania oraz zamknięcie koronowe
MYPI2019000961A MY197920A (en) 2016-09-29 2017-09-14 Steel sheet for crown caps, method for manufacturing the same, and crown cap
JP2018542371A JP6601571B2 (ja) 2016-09-29 2017-09-14 王冠用鋼板およびその製造方法並びに王冠
PH12019550011A PH12019550011A1 (en) 2016-09-29 2019-01-23 Steel sheet for crown caps, method for manufacturing the same, and crown cap
ZA2019/00744A ZA201900744B (en) 2016-09-29 2019-02-05 Steel sheet for crown caps, method for manufacturing the same, and crown cap
CONC2019/0001705A CO2019001705A2 (es) 2016-09-29 2019-02-26 Hoja de acero para tapas corona, método para fabricarla, y tapa corona

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JP2019215227A (ja) * 2018-06-12 2019-12-19 株式会社神戸製鋼所 超音波探傷方法
EP3901300A4 (en) * 2018-12-20 2022-04-27 JFE Steel Corporation STEEL SHEET FOR CAN AND METHOD FOR PRODUCING IT

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EP3901300A4 (en) * 2018-12-20 2022-04-27 JFE Steel Corporation STEEL SHEET FOR CAN AND METHOD FOR PRODUCING IT

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