WO2018181449A1 - 鋼板およびその製造方法と王冠およびdrd缶 - Google Patents
鋼板およびその製造方法と王冠およびdrd缶 Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B65—CONVEYING; PACKING; STORING; HANDLING THIN OR FILAMENTARY MATERIAL
- B65D—CONTAINERS FOR STORAGE OR TRANSPORT OF ARTICLES OR MATERIALS, e.g. BAGS, BARRELS, BOTTLES, BOXES, CANS, CARTONS, CRATES, DRUMS, JARS, TANKS, HOPPERS, FORWARDING CONTAINERS; ACCESSORIES, CLOSURES, OR FITTINGS THEREFOR; PACKAGING ELEMENTS; PACKAGES
- B65D41/00—Caps, e.g. crown caps or crown seals, i.e. members having parts arranged for engagement with the external periphery of a neck or wall defining a pouring opening or discharge aperture; Protective cap-like covers for closure members, e.g. decorative covers of metal foil or paper
- B65D41/02—Caps or cap-like covers without lines of weakness, tearing strips, tags, or like opening or removal devices
- B65D41/10—Caps or cap-like covers adapted to be secured in position by permanent deformation of the wall-engaging parts
- B65D41/12—Caps or cap-like covers adapted to be secured in position by permanent deformation of the wall-engaging parts made of relatively stiff metallic materials, e.g. crown caps
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0426—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0436—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
- C21D8/0468—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment between cold rolling steps
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
- C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
Definitions
- the present invention relates to a steel sheet, particularly a high-strength thin steel sheet having excellent formability and a method for producing the same.
- a steel plate there is a thin steel plate used as a material such as a crown used as a stopper of a DRD (Drawing and Redrawing) can or glass bottle formed by combining drawing and redrawing.
- the present invention relates to a crown and a DRD can obtained by forming the steel plate.
- crowns are widely used in 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 provided around it. Seal the jar by caulking.
- Bottles that use crowns are often filled with high internal pressure contents such as beer and carbonated drinks. Therefore, when the internal pressure increases due to a change in temperature or the like, the crown needs to have a high pressure strength so that the crown is not deformed and the bottle is not sealed and the contents are not leaked. Furthermore, when the internal pressure increases due to changes in temperature or the like, impact resistance is also important so that the bottle seal is not broken by an external impact during transportation. In addition, even if 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 sheet is mainly used for the thin steel sheet used for the crown material.
- annealing is performed and temper rolling is performed.
- the thickness of conventional steel plates for crowns is generally 0.22 mm or more, and by using SR material made of mild steel used for food and beverage cans, etc., sufficient pressure strength and impact resistance and molding It was possible to secure the sex.
- the crown is squeezed to some extent at the center in the initial stage of molding, and then the outer edge is molded into a bowl shape.
- the material of the crown is a steel plate having low formability, a defect as shown in FIG. 1 may be formed from the upper surface side of the crown from the appropriate position. This poorly shaped crown not only looks bad and lowers the consumer's willingness to purchase, but even if it is struck into a bottle, the pressure resistance and impact resistance are not obtained and the contents may leak.
- the DRD can needs high pressure strength so that the can does not deform when the pressure inside the can rises or falls. Furthermore, if the DRD can is deformed by an external impact during transportation, the contents are leaked, and the consumer's purchasing motivation is reduced due to the appearance being deteriorated. Therefore, impact resistance is also important. In addition, even if the strength of the steel sheet used as the material of the DRD can is sufficient, if the steel sheet is poor in formability, a shape defect that causes wrinkles in the flange portion at the time of forming the DRD can is induced.
- the steel plate used for the material of the DRD can needs to be excellent in formability.
- Patent Document 1 As a chemical composition, in mass%, C: 0.0010% to 0.0060%, Si: 0.005 to 0 0.050%, Mn: 0.10% to 0.50%, Ti: 0 to 0.100%, Nb: 0 to 0.080%, B: 0 to 0.0080%, P: 0 0.040% or less, S: 0.040% or less, Al: 0.1000% or less, N: 0.0100% or less, the balance containing Fe and impurities, and 25% with respect to the rolling direction of the steel sheet.
- the minimum value of r value in the direction of ⁇ 65 ° is 1.80 or more, and the average value of the r value in the direction of 0 ° or more and less than 360 ° with respect to the rolling direction is 1.70 or more,
- a steel plate for a crown which has a yield strength of 570 MPa or more, has been proposed.
- Patent Document 2 as a chemical composition, by mass, C: 0.0030 to 0.0060%, Si: 0.04% or less, Mn: 0.60% or less, P: 0.005% or more 0.03% or less, S: 0.02% or less, Al: more than 0.005%, 0.1% or less, N: 0.005% or less, satisfying the predetermined formula, the balance being It consists of Fe and inevitable impurities, the plate thickness is 0.2 mm or less, the hardness level (HR30T) is 67 ⁇ 3 to 76 ⁇ 3, and the ⁇ r value indicating in-plane anisotropy is ⁇ 0.2 or less.
- HR30T hardness level
- ⁇ r value indicating in-plane anisotropy is ⁇ 0.2 or less.
- Patent No. 6057023 Japanese Patent No. 4559918
- Patent Document 1 The steel sheet produced by the technique described in Patent Document 1 tends to have a lack of formability and strength, particularly when thinned, and the crown formed from the steel sheet has a higher impact resistance than the conventional crown. Also had problems with inferior points. This problem is the same when the material for DRD cans is used.
- Patent Document 2 The steel sheet manufactured by the technique described in Patent Document 2 tends to have insufficient formability and strength particularly when it is thinned, and a DRD can formed using the steel sheet as a material has the impact resistance of the conventional DRD. Had problems with inferiority. This problem is the same when the crown material is used.
- the present invention has been made in view of the above problems, and an object of the present invention is to provide a steel sheet having sufficient formability and strength even when it is thinned, and a method for manufacturing the steel sheet.
- the inventors of the present invention have made extensive studies to solve the above problems. As a result, it has been found that a steel sheet having sufficient formability and strength can be provided even if it is thinned by optimizing the alloy components and manufacturing conditions and controlling the dislocation density at a position 1/2 depth from the surface. did.
- the present invention is derived from this finding, and the gist thereof is as follows.
- a DRD can comprising the steel plate according to (1) or (2).
- the present invention it is possible to provide a steel plate having sufficient strength and excellent formability even if it is thinned.
- a crown or DRD can is manufactured using this steel plate as a raw material, the impact resistance can be maintained at a high level even in a thin crown or DRD can.
- FIG. 1 It is a schematic diagram which shows the crown of a shape defect. It is a figure which shows the cross-sectional shape profile observation surface of a crown. It is a figure which shows the typical example of the cross-sectional shape profile of a crown. It is a figure which shows the point of the impact resistance test performed to a DRD can. It is a figure which shows the evaluation object of the impact resistance test performed to a DRD can.
- the steel sheet according to the present invention is, by mass%, C: more than 0.006% and 0.012% or less, Si: 0.02% or less, Mn: 0.10% or more and 0.60% or less, P: 0.020. %: S: 0.020% or less, Al: 0.01% or more and 0.07% or less, N: 0.0080% or more and 0.0200% or less, with the balance being the component composition of Fe and inevitable impurities And the dislocation density at a half depth position of the plate thickness from the steel plate surface is 2.0 ⁇ 10 14 / m 2 or more and 1.0 ⁇ 10 15 / m 2 or less.
- the "%" display regarding a component shows "mass%".
- C More than 0.006% and 0.012% or less C is an interstitial element, and a large solid solution strengthening can be obtained by adding a small amount. As a result of improving the frictional force of the steel sheet substrate by this solid solution strengthening, the movement speed of dislocations during the secondary cold rolling described later is reduced, and a large amount of dislocations are introduced into the material even at a low rolling reduction, thereby improving the dislocation density. . That is, when the C content is 0.006% or less, the dislocation density at a position 1/2 the depth of the sheet thickness from the steel sheet surface is less than 2.0 ⁇ 10 14 / m 2 , and the steel sheet is used for a crown, for example.
- the impact resistance equivalent to that of a conventional crown cannot be obtained.
- a steel plate is used for a DRD can, for example, to form a thin DRD can, impact resistance equivalent to that of a conventional DRD can cannot be obtained.
- the C content exceeds 0.012%
- the dislocation density at the 1/2 depth position of the plate thickness from the steel plate surface exceeds 1.0 ⁇ 10 15 / m 2, and the formability of the steel plate decreases.
- a wrinkle is caused by a shape defect that occurs from the top surface of the crown when the crown is formed.
- the C content is more than 0.006% and 0.012% or less. Preferably, it is 0.007% or more and 0.01% or less.
- the Si content is set to 0.02% or less.
- the content is 0.01% or less. Since excessively reducing Si causes an increase in steelmaking cost, the Si content is preferably 0.004% or more.
- Mn 0.10% or more and 0.60% or less
- Mn is an interstitial element, and a large solid solution strengthening can be obtained by adding a small amount.
- the movement speed of dislocations during the secondary cold rolling described later is reduced, and a large amount of dislocations are introduced into the material even at a low rolling reduction, thereby improving the dislocation density.
- the content of Mn is less than 0.10%
- the dislocation density at the 1/2 depth position of the plate thickness from the steel plate surface is less than 2.0 ⁇ 10 14 / m 2 , and the steel plate is used for, for example, a crown.
- the same impact resistance as a conventional crown cannot be obtained.
- a steel plate is used for a DRD can, for example, to form a thin DRD can, impact resistance equivalent to that of a conventional DRD can cannot be obtained.
- the Mn content is less than 0.10%, it becomes difficult to avoid hot brittleness even if the S content is reduced, and problems such as surface cracks occur during continuous casting.
- the Mn content exceeds 0.60%, the formability of the steel sheet is lowered, and when the steel sheet is used for, for example, a crown, a wrinkle is caused by a shape defect generated from the top surface of the crown.
- the Mn content is set to 0.10% to 0.60%.
- the Mn content is 0.15% or more and 0.50% or less.
- the content of P exceeds 0.020%, the formability of the steel sheet decreases, and when the steel sheet is used for, for example, a crown, a shape in which wrinkles are generated from the top surface of the crown at the time of crown molding It leads to defects. Similarly, when a steel plate is used for, for example, a DRD can, a shape defect that causes wrinkles in the flange portion at the time of forming the DRD can results. Furthermore, the corrosion resistance decreases. From the above, the content of P is set to 0.020% or less. Preferably, it is 0.015% or less. In order to make P less than 0.001%, the P removal cost becomes excessive, so the P content is preferably 0.001% or more.
- the S content is 0.020% or less.
- the S content is 0.020% or less.
- it is 0.015% or less.
- the S-removal cost becomes excessive, so the S content is preferably made 0.004% or more.
- Al 0.01% or more and 0.07% or less Al is an element necessary as a deoxidizer during steelmaking, but if the Al content is less than 0.01%, deoxidation is insufficient and inclusions increase.
- the formability of the steel sheet is reduced and the steel sheet is used for, for example, a crown, a wrinkle is generated due to a shape defect generated from the top surface of the crown at the time of crown molding.
- a steel plate is used for, for example, a DRD can, a shape defect that causes wrinkles in the flange portion at the time of forming the DRD can results.
- the Al content is set to 0.01% or more and 0.07% or less.
- the content is 0.15% or more and 0.55% or less.
- N 0.0080% or more and 0.0200% or less
- N is an interstitial element, and like C, a large solid solution strengthening can be obtained by adding a small amount.
- the movement speed of dislocations during the secondary cold rolling described later is reduced, and a large amount of dislocations are introduced into the material even at a low rolling reduction, thereby improving the dislocation density.
- the N content is less than 0.0080%
- the dislocation density at the 1/2 depth position of the plate thickness from the steel plate surface is less than 2.0 ⁇ 10 14 / m 2 , and the steel plate is used for a crown, for example.
- the same impact resistance as that of the conventional thick-walled crown cannot be obtained.
- a steel plate is used for a DRD can, for example, to form a thin DRD can, impact resistance equivalent to that of a conventional DRD can cannot be obtained.
- the N content exceeds 0.0200%
- the dislocation density at the 1/2 depth position of the plate thickness from the steel plate surface exceeds 1.0 ⁇ 10 15 / m 2, and the formability of the steel plate decreases.
- a wrinkle is caused by a shape defect that occurs from the top surface of the crown when the crown is formed.
- the N content is set to 0.0080% or more and 0.0200% or less. Preferably, it is 0.0090% or more and 0.019% or less.
- the balance other than the above components is Fe and inevitable impurities.
- Cu, Ni, Cr and Mo may be contained within a range not impairing the effects of the present invention. At that time, it is preferable that Cu is 0.2% or less, Ni is 0.15% or less, Cr is 0.10% or less, and Mo is 0.05% or less in accordance with ASTM A623M-11. The other elements are preferably 0.02% or less.
- the dislocation density at the position of 1/2 depth of the plate thickness from the steel plate surface is 2.0 ⁇ 10 14 / m 2 or more and 1.0 ⁇ 10 15 / m 2 or less. is there.
- the strength of the steel sheet can be evaluated by the impact resistance of the crown when the steel sheet is used for, for example, a crown, or the steel sheet is used for, for example, a DRD can.
- the impact resistance of the DRD can be evaluated, and it has been found that the impact resistance is improved by increasing the dislocation density.
- the dislocation density at a depth of 1/2 of the plate thickness from the steel plate surface is 2.0 ⁇ 10 14 / m 2 or more, even if the thickness is reduced, the same resistance to resistance as conventional thick crowns and DRD cans. Impact properties can be obtained.
- the reason for this is not clear, but it is considered that when the dislocation density increases, deformation resistance increases due to pinning by dislocations. Therefore, for example, when the impact is applied to the crown from the outside in a state where the bottle internal pressure is high, the crown is difficult to come off. Alternatively, for example, when an impact is applied to the DRD can from the outside, the can is difficult to deform. Therefore, the dislocation density at a position 1/2 the depth of the plate thickness from the steel plate surface is set to 2.0 ⁇ 10 14 / m 2 or more.
- the dislocation density at the 1/2 depth position of the plate thickness from the steel plate surface exceeds 1.0 ⁇ 10 15 / m 2 , the formability of the steel plate is reduced, and when the steel plate is used for, for example, a crown, When a crown is formed, wrinkles will cause shape defects that occur from the top of the crown. Similarly, when a steel plate is used for, for example, a DRD can, a shape defect that causes wrinkles in the flange portion at the time of forming the DRD can results. From the above, the dislocation density from the steel sheet surface at the 1/2 depth position of the sheet thickness is 2.0 ⁇ 10 14 / m 2 or more and 1.0 ⁇ 10 15 / m 2 or less.
- a more preferable range is 3.0 ⁇ 10 14 / m 2 or more and 9.0 ⁇ 10 14 / m 2 or less.
- the steel slab according to the above-mentioned component composition in order to make a dislocation density into said range.
- the dislocation density at the half depth position of the plate thickness from the steel sheet surface is the surface expressed by reducing the thickness from the steel plate surface to the half depth position of the plate thickness by chemical polishing.
- the peak positions and half-value widths of the four surfaces of Fe (110) (200) (211) (220) were measured using a Co source.
- the measured half width was corrected with the half width of the Si single crystal without strain, the local strain ⁇ was determined by the Williamson hall method, and the dislocation density ⁇ was calculated using the following equation (1).
- Burgers vector b was 0.25 nm.
- the structure of the steel sheet of the present invention is preferably a recrystallized structure. This is because, if there is unrecrystallized after annealing, the material becomes non-uniform and, for example, wrinkles occur from the top surface of the crown when forming the crown. Alternatively, for example, it leads to a shape defect in which wrinkles occur in the flange portion during DRD can molding. However, if the area ratio of the non-recrystallized structure is 5% or less, there is almost no influence on the shape defect in which wrinkles at the time of crown molding occur from the top surface of the crown or the wrinkle at the flange part at the time of DRD can molding. acceptable.
- the recrystallized structure is preferably a ferrite phase, and the phase other than the ferrite phase is preferably less than 1.0%.
- the manufacturing method of this invention As a manufacturing process, it has a hot rolling process, a pickling process, a primary cold rolling process, an annealing process, and a secondary cold rolling process.
- the temperature is defined as the surface temperature of the steel plate (material).
- steel adjusted to the above component composition is melted in a converter or the like to obtain a steel material such as a slab.
- the steel material to be used is preferably manufactured by a continuous casting method in order to prevent macro segregation of components, but may be manufactured by an ingot forming method or a thin slab casting method.
- the steel material was not cooled to room temperature, but was charged in a heating furnace as it was, or a little heat was retained.
- Energy saving processes such as direct feed rolling and direct rolling, which are rolled immediately afterwards, can be applied without any problem.
- the obtained steel material is subjected to a hot rolling process.
- This hot rolling step is a step of heating a steel material having the above component composition at 1200 ° C. or higher and winding it in a temperature range of 670 ° C. or lower after finish rolling.
- Step material heating temperature 1200 ° C or higher
- the steel material reheating temperature is less than 1200 ° C.
- AlN cannot be sufficiently dissolved, and solid solution N cannot be secured during the secondary cold rolling process, so the effect of improving the dislocation density is obtained.
- the dislocation density at the 1/2 depth position of the plate thickness from the steel plate surface is less than 2.0 ⁇ 10 14 / m 2 and the steel plate is used for a crown, for example, to form a thin crown, Impact resistance equivalent to that of the crown is not obtained.
- impact resistance equivalent to that of a conventional DRD can cannot be obtained.
- the slab heating temperature is desirably 1300 ° C. or less because of an increase in scale loss accompanying an increase in oxidized weight. From the viewpoint of preventing troubles during hot rolling even if the slab heating temperature is lowered, a so-called sheet bar heater that heats the sheet bar may be used.
- the finish rolling temperature in the hot rolling step is preferably 850 ° C. or higher from the viewpoint of rolling load stability. 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 is 670 ° C. or lower.
- it is set to 640 ° C. or lower.
- the lower limit of the coiling temperature is not particularly limited, but if the coiling temperature is excessively decreased, the strength of the hot-rolled steel sheet obtained in the hot rolling process is increased, and the rolling load in the primary cold rolling process is increased. Since rolling control becomes difficult, the winding temperature is preferably 500 ° C. or higher.
- part or all of the finish rolling may be lubricated rolling in order to reduce the rolling load during hot rolling.
- Performing lubrication rolling is also effective from the viewpoint of uniform steel plate shape and uniform material.
- the coefficient of friction during lubrication rolling is preferably in the range of 0.25 to 0.10.
- the application of the continuous rolling process is also desirable from the viewpoint of the operational stability of hot rolling.
- the pickling step is a step of removing the oxidized scale on the surface of the hot-rolled steel sheet obtained in the hot rolling step by pickling.
- Pickling conditions are not particularly limited, and may be set as appropriate.
- the primary cold rolling step is a step of performing cold rolling on the pickled plate after the pickling step.
- the cold rolling conditions are not particularly limited.
- the conditions such as the rolling reduction may be determined from the viewpoint of the desired sheet thickness.
- the rolling reduction is preferably 85 to 94%.
- the annealing step is a step of annealing the cold-rolled steel sheet obtained in the primary cold rolling step in a temperature range of 650 ° C. or higher and 750 ° C. or lower. If the annealing temperature is less than 650 ° C., AlN precipitates during annealing, and solid solution N cannot be secured during the subsequent secondary cold rolling process, so the effect of improving the dislocation density cannot be obtained, and 1 / The dislocation density at the 2 depth position is less than 2.0 ⁇ 10 14 / m 2 . Furthermore, if the annealing temperature is less than 650 ° C., the area ratio of the non-recrystallized structure exceeds 5%, and the formability deteriorates.
- the annealing temperature is set to 650 ° C. or higher and 750 ° C. or lower. Preferably, it is set to 660 ° C. or higher and 740 ° C. or lower.
- the residence time is less than 5 seconds, the unrecrystallized structure may exceed 5%, and if it exceeds 120 seconds, C Is segregated at the grain boundaries and aggregates to form carbides, and there is a risk that the solid solution C cannot be sufficiently secured during the secondary cold rolling process, and the cost is increased.
- Secondary cold rolling is performed on the annealed plate after the annealing.
- the average tension between the stands is set to 98 MPa or more in the rolling equipment having two or more stands on the annealed plate obtained in the annealing step, and the reduction ratio is 10% or more and 30% or less. It is the process of performing cold rolling in.
- the average tension between the stands is less than 98 MPa, the dislocation density from the steel sheet surface to the half depth position of the sheet thickness is less than 2.0 ⁇ 10 14 / m 2 .
- the average tension between the stands is preferably 127.4 MPa or more.
- the upper limit of the average tension between the stands is not particularly limited, and may be determined from the viewpoint of operability.
- the tension may be such that the steel plate does not break.
- 392 MPa or less is preferable.
- the rolling reduction ratio of the secondary cold rolling is less than 10%, the dislocation density at the 1/2 depth position of the plate thickness from the steel plate surface is less than 2.0 ⁇ 10 14 / m 2 .
- the rolling reduction of secondary cold rolling exceeds 30%, the dislocation density at the 1/2 depth position of the plate thickness from the steel plate surface exceeds 1.0 ⁇ 10 15 / m 2 , and the formability of the steel plate is high. descend. From the above, the rolling reduction of secondary cold rolling is set to 10% or more and 30% or less.
- the rolling reduction of secondary cold rolling is preferably 12% or more and 28% or less.
- the number of rolling stands for secondary cold rolling may be plural, and if it is 5 or more, the equipment cost increases, and 2 to 4 stands are preferable.
- the cold-rolled steel sheet obtained as described above is then subjected to plating treatment such as tin plating, chromium plating, nickel plating, etc., for example, by electroplating on the surface of the steel sheet, if necessary, to form a plating layer.
- plating treatment such as tin plating, chromium plating, nickel plating, etc.
- electroplating on the surface of the steel sheet, if necessary, to form a plating layer.
- the steel sheet of the present invention can have sufficient formability and strength even if it is thinned. Therefore, the steel plate of the present invention is particularly suitable as a material for crowns or DRD cans.
- the crown is mainly composed of a disk-shaped part that closes the mouth of the bottle and a bowl-shaped part provided around it. After punching the above steel plate into a circular blank, it can be formed by press molding. it can.
- the crown made of the steel plate of the present invention has an excellent molded shape as a crown, is excellent in impact resistance, and has an effect of reducing the amount of waste discharged with use.
- the DRD can be formed by punching the steel plate described above into a circular blank and then performing drawing and redrawing.
- the DRD can made of the steel plate of the present invention has excellent impact resistance, and since the shape is uniform and does not deviate from the product standard, the yield in the DRD can manufacturing process is improved and accompanying the DRD can manufacturing It also has the effect of reducing waste emissions.
- Steel slabs were 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 heated to 1220 ° C., finish-rolled at 890 ° C., and then wound at the winding temperature shown in Table 2. After hot rolling, pickling was performed. Next, primary cold rolling is performed at a rolling reduction of 90%, annealing is performed at the annealing temperature shown in Table 2, and then secondary cold rolling is performed at the rolling reduction shown in Table 2 to obtain a steel sheet having a thickness of 0.17 mm. Obtained.
- the obtained steel sheet was continuously subjected to electrolytic chromic acid treatment to obtain tin-free steel.
- the dislocation density at the 1/2 depth position of the plate thickness from the steel plate surface was expressed by reducing the thickness from the steel plate surface to the 1/2 depth position of the plate thickness by chemical polishing.
- the peak positions and half-value widths of the four surfaces of Fe (110) (200) (211) (220) were measured using X-ray diffraction and a Co source.
- the measured half width was corrected with the half width of the Si single crystal without strain, and the local strain ⁇ was determined by the Williamson hall method to calculate the dislocation density ⁇ using the following equation (1).
- Burgers vector b was 0.25 nm.
- the obtained steel sheet was heat-treated at 210 ° C. for 15 minutes and then molded into a crown, and the crown formability was evaluated.
- a circular blank with a diameter of 37 mm was used, and was pressed into the dimensions of the three kinds of crowns described in “JIS S9017” (1957) (outer diameter 32.1 mm, height 6.5 mm, number of ridges 21).
- the crown thus obtained was measured for 3D shape from the upper surface using a 3D shape measuring machine VR-3000 manufactured by Keyence, and its formability was evaluated.
- the evaluation of the moldability of the crown was based on the presence or absence of shape defects that occurred from the top surface of the crown.
- the cross-sectional profile was observed on the cross-sectional profile observation surface shown in FIG. Specifically, as shown in FIGS. 3 (a) and 3 (b), typical examples of cross-sectional profiles are the inflection points at the beginning of Ulsan, the inflection points at the shoulder of the crown, The vertical distance H at the start of Ulsan was measured. As shown in FIG. 3 (a), if the vertical distance H is not 0, it is a normal wrinkle, and as shown in FIG.
- the impact resistance of the crown was evaluated by a drop impact test using the molded crown.
- a drop impact test using the molded crown.
- commercial beer was poured into a commercial bottle, the molded crown was capped and stirred for 1 minute, and the angle of the bottle was tilted by 20 ° and a 500 g hard polyvinyl chloride ball was directed from the height of 1 m directly above the crown to the crown. After free-falling, the presence or absence of beer leakage was evaluated.
- the drop impact test was conducted on five bottles stoppered with five crowns formed from each steel plate. When this test is performed for each steel plate, when the number of beer leaks is zero, the impact resistance is particularly excellent, so it is excellent ( ⁇ ).
- the impact resistance of the conventional crown is Equivalent good ( ⁇ ), and in the case of two or more beer leaks, it was inferior ( ⁇ ) to the impact resistance of the conventional crown.
- the evaluation results are shown in Table 3.
- the conventional crown used as a reference is a crown formed using mild steel having a thickness of 0.22 mm.
- the obtained steel sheet was subjected to heat treatment equivalent to 210 ° C. and 15 minutes of paint baking, and then formed into a DRD can, and the DRD can formability was evaluated. That is, using a circular blank having a diameter of 158 mm, drawing and redrawing were performed, a DRD can having an inner diameter of 82.8 mm and a flange diameter of 102 mm was formed, and DRD can moldability was evaluated. For the evaluation, a sample in which three or more fine wrinkles were visually observed in the flange portion was (x), and a sample in which the fine wrinkles in the flange portion was two or less was visually indicated as ( ⁇ ). The evaluation results are shown in Table 3.
- the impact resistance of the DRD can was evaluated.
- a circular steel plate having a diameter of 45 mm was cut out from the bottom of the DRD can and subjected to an impact resistance test.
- the shooting mold had a diameter of 12.7 mm and a flat bottom, and a circular hole with a diameter of 13.5 mm was provided in the cradle and the plate holder.
- the positional relationship between the shooting mold, the cradle and the plate holder and the circular steel plate is such that the hole of the shooting mold and the cradle, the hole of the plate holding plate and the center of the circular steel plate are aligned. It was installed and the bottom of the shooting mold could be pushed downward by 0.5 mm.
- the conventional DRD can used as a reference is a DRD can formed by using 0.22 mm thick mild steel.
- the steel sheet of the present invention has a dislocation density of 2.0 ⁇ 10 14 / m 2 or more and 1.0 ⁇ 10 15 / m 2 or less at a half depth position from the surface in the plate thickness direction.
- the crown formed using the steel plate of the present invention did not cause the shape defect that the cocoon was generated from the top surface of the crown, and the beer leakage in the drop impact test was equal to or higher than that of the conventional crown.
- the DRD can formed using the steel plate of the present invention does not have a defective shape in which wrinkles occur in the flange portion, and the amount of dents in the impact resistance test is equal to or higher than that of a conventional DRD can, and has excellent formability. And shows impact resistance.
- the steel plate of the comparative example which deviates from the scope of the present invention has a dislocation density of less than 2.0 ⁇ 10 14 / m 2 at a half depth position from the surface in the plate thickness direction, or 1.0. and the more than ⁇ 10 15 / m 2, the crown and DRD cans molded using the steel sheets of the comparative examples are inferior either moldability and impact resistance.
- No. No. 3 is that the slab heating temperature in the hot rolling process is less than 1200 ° C outside the range of the present invention, and the dislocation density at the 1/2 depth position from the surface in the plate thickness direction is out of the range of the present invention. It is less than 2.0 ⁇ 10 14 / m 2 and its impact resistance is inferior to conventional crowns and DRD cans.
- No. No. 7 is that the rolling reduction in the secondary cold rolling process exceeds the range of the present invention and exceeds 40%, and the dislocation density at the 1/2 depth position from the surface in the sheet thickness direction is out of the scope of the present invention.
- 1.0 ⁇ 10 15 / m 2 and in the molding of the crown, the wrinkles cause a defective shape from the top surface of the crown, and in the DRD can molding, the flange portion has a defective shape that causes wrinkles. And inferior to DRD cans.
- No. No. 8 shows that the coiling temperature in the hot rolling process exceeds the range of the present invention and exceeds 670 ° C., and the dislocation density at the 1/2 depth position from the surface in the sheet thickness direction is out of the range of the present invention. It is less than 2.0 ⁇ 10 14 / m 2 and its impact resistance is inferior to conventional crowns and DRD cans.
- No. No. 12 is an average tension between the stands in the secondary cold rolling step is less than 98 MPa outside the range of the present invention, and the dislocation density at the 1/2 depth position of the plate thickness from the surface in the plate thickness direction is that of the present invention. Out of the range, it is less than 2.0 ⁇ 10 14 / m 2 , and the impact resistance is inferior to the conventional crown and DRD can.
- No. No. 13 has an annealing temperature of less than 650 ° C. in the annealing step, and the dislocation density at the 1/2 depth position of the plate thickness from the surface in the plate thickness direction is out of the range of the present invention, and is 2.0 ⁇ 10 14 / m 2.
- the unrecrystallized structure exceeds 5%.
- crown molding defects occur in the shape of wrinkles generated from the upper surface of the crown.
- DRD can molding, defects in the shape of wrinkles occur in the flange. It is inferior to the crown and DRD can.
- No. No. 17 has an annealing temperature of more than 750 ° C. in the annealing step, and the dislocation density at the 1/2 depth position of the plate thickness from the surface in the plate thickness direction is out of the range of the present invention, and is 2.0 ⁇ 10 14 / m 2.
- the impact resistance is inferior to conventional crowns and DRD cans.
- No. No. 20 has a rolling reduction ratio of less than 10% in the secondary cold rolling process, and the dislocation density at the 1/2 depth position from the surface in the sheet thickness direction is out of the range of the present invention to be 2.0 ⁇ 10. 14 / m is less than 2, the impact resistance is inferior conventional crown and DRD cans.
- No. No. 24 has a C content of 0.006% or less, and the dislocation density at the 1/2 depth position of the plate thickness from the surface in the plate thickness direction is out of the range of the present invention to be 2.0 ⁇ 10 14 / m.
- the impact resistance is inferior to that of conventional crowns and DRD cans.
- No. No. 25 has a C content of more than 0.012%, and the dislocation density at the 1/2 depth position of the plate thickness from the surface in the plate thickness direction is out of the range of the present invention, and is 1.0 ⁇ 10 15 / m.
- wrinkles cause a shape defect that occurs from the upper surface of the crown, and in DRD can molding, a shape defect that causes wrinkles in the flange portion occurs, and the moldability is inferior to conventional crowns and DRD cans.
- the N content is less than 0.0080%, and the dislocation density at the 1/2 depth position of the plate thickness from the surface in the plate thickness direction is out of the range of the present invention to be 2.0 ⁇ 10 14 / m.
- the impact resistance is inferior to that of conventional crowns and DRD cans.
- the N content exceeds 0.0200%, and the dislocation density at the 1/2 depth position from the surface in the thickness direction is 1.0 ⁇ 10 15 / m outside the scope of the present invention.
- wrinkles cause a shape defect that occurs from the upper surface of the crown, and in DRD can molding, a shape defect that causes wrinkles in the flange portion occurs, and the moldability is inferior to conventional crowns and DRD cans.
- the Si content is over 0.02%, the formability of the steel sheet is lowered, the shape forming the wrinkles from the top surface of the crown in crown molding, and the shape in which wrinkles are generated in the flange portion in DRD can molding It produces defects and is inferior to conventional crowns and DRD cans.
- No. No. 29 has a Mn content exceeding 0.60%, and the formability of the steel sheet is lowered.
- a wrinkle is generated from the top surface of the crown, and in the DRD can molding, the flange portion is wrinkled. It produces defects and is inferior to conventional crowns and DRD cans.
- the P content is over 0.020%, the formability of the steel sheet is lowered, the shape forming the wrinkles from the top surface of the crown in crown forming, and the shape in which wrinkles are generated in the flange portion in DRD can forming It produces defects and is inferior to conventional crowns and DRD cans.
- No. No. 31 has an Al content exceeding 0.07%, and the dislocation density at the 1/2 depth position of the plate thickness from the surface in the plate thickness direction deviates from the range of the present invention to be 2.0 ⁇ 10 14 / m.
- the impact resistance is inferior to that of conventional crowns and DRD cans.
- the Al content is less than 0.01%, the formability of the steel sheet is lowered, the shape forming the wrinkles from the top surface of the crown in crown forming, and the shape in which wrinkles are generated in the flange portion in DRD can forming It produces defects and is inferior to conventional crowns and DRD cans.
- No. No. 33 has a C content of 0.0060 or less, and the dislocation density at the 1/2 depth position of the plate thickness from the surface in the plate thickness direction is out of the range of the present invention to be 2.0 ⁇ 10 14 / m 2.
- the impact resistance is inferior to conventional crowns and DRD cans.
- No. No. 35 has a Mn content of less than 0.10%, and the dislocation density at the 1/2 depth position of the plate thickness from the surface in the plate thickness direction is out of the range of the present invention to be 2.0 ⁇ 10 14 / m.
- the impact resistance is inferior to that of conventional crowns and DRD cans.
- the S content is over 0.20%, the formability of the steel sheet is lowered, and in the case of crown molding, a shape defect in which wrinkles are generated from the top surface of the crown occurs, and in the case of DRD can molding, the flange portion is wrinkled. It produces defects and is inferior to conventional crowns and DRD cans.
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Abstract
Description
C:0.006%超0.012%以下、
Si:0.02%以下、
Mn:0.10%以上0.60%以下、
P:0.020%以下、
S:0.020%以下、
Al:0.01%以上0.07%以下および
N:0.0080%以上0.0200%以下
を含有し、残部はFeおよび不可避的不純物の成分組成を有し、鋼板表面から板厚の1/2深さ位置における転位密度が2.0×1014/m2以上1.0×1015/m2以下である鋼板。
鋼素材を1200℃以上で加熱し、仕上げ圧延後に670℃以下の温度域にて巻取る熱間圧延工程と、
前記熱間圧延後の熱延板に酸洗を行う酸洗工程と、
前記酸洗後の熱延板に冷間圧延する一次冷間圧延工程と、
前記一次冷間圧延後の冷延板に、650℃以上750℃以下の温度域で焼鈍する焼鈍工程と、
前記焼鈍後の焼鈍板に、2台以上のスタンドを有する圧延設備にて各スタンド間の平均張力を98MPa以上として、10%以上30%以下の圧下率での冷間圧延を行う二次冷間圧延工程と、
を有する鋼板の製造方法。
まず、鋼板の成分組成における各成分量の限定理由から順に説明する。なお、成分に関する「%」表示は、特に断らない限り「質量%」を示す。
Cは、侵入型元素であり、微量の添加で大きな固溶強化が得られる。この固溶強化により鋼板素地の摩擦力を向上させる結果、後述の二次冷間圧延中の転位の移動速度が低下し、低い圧下率でも材料に多量の転位が導入され、転位密度が向上する。すなわち、C含有量が0.006%以下では鋼板表面から板厚の1/2深さ位置における転位密度が2.0×1014/m2未満となり、鋼板を例えば王冠用に供して薄肉の王冠とした場合に、従来の王冠と同等の耐衝撃性が得られない。同様に、鋼板を例えばDRD缶用に供して薄肉のDRD缶とした場合に、従来のDRD缶と同等の耐衝撃性が得られない。一方、C含有量が0.012%を超えると、鋼板表面から板厚の1/2深さ位置における転位密度が1.0×1015/m2超えとなり、鋼板の成形性が低下し、鋼板を例えば王冠用に供した場合、王冠成形時に襞が王冠上面から発生する形状不良をまねく。同様に、鋼板を例えばDRD缶用に供した場合、DRD缶成形時にフランジ部にしわが発生する形状不良をまねく。以上より、C含有量は0.006%超0.012%以下とする。好ましくは、0.007%以上0.01%以下である。
Siの含有量が0.02%を超えると、鋼板の成形性が低下し、鋼板を例えば王冠成形時に襞が王冠上面から発生する形状不良をまねく。同様に、鋼板を例えばDRD缶用に供した場合、DRD缶成形時にフランジ部にしわが発生する形状不良をまねく。さらに、鋼板の表面処理性の劣化および耐食性の低下を招く。以上より、Siの含有量は0.02%以下とする。好ましくは、0.01%以下とする。なお、過剰にSiを低下させることは製鋼コストの増大を招くため、Siの含有量は0.004%以上とすることが好ましい。
Mnは侵入型元素であり、微量の添加で大きな固溶強化が得られる。この固溶強化により鋼板素地の摩擦力を向上させる結果、後述の二次冷間圧延中の転位の移動速度が低下し、低い圧下率でも材料に多量の転位が導入され、転位密度が向上する。すなわち、Mnの含有量が0.10%未満では、鋼板表面から板厚の1/2深さ位置における転位密度が2.0×1014/m2未満となり、鋼板を例えば王冠用に供して薄肉化の王冠とした場合に、従来の王冠と同等の耐衝撃性が得られない。同様に、鋼板を例えばDRD缶用に供して薄肉のDRD缶とした場合に、従来のDRD缶と同等の耐衝撃性が得られない。さらに、Mnの含有量が0.10%未満では、Sの含有量を低下させても熱間脆性を回避することが困難になり、連続鋳造時に表面割れなどの問題が生じる。一方、Mn含有量が0.60%を超えると、鋼板の成形性が低下し、鋼板を例えば王冠用に供した場合、王冠成形時に襞が王冠上面から発生する形状不良をまねく。同様に、鋼板を例えばDRD缶用に供した場合、DRD缶成形時にフランジ部にしわが発生する形状不良をまねく。以上より、Mn含有量は0.10%以上0.60%以下とする。好ましくは、Mnの含有量は0.15%以上0.50%以下である。
Pの含有量が0.020%を超えると、鋼板の成形性が低下し、鋼板を例えば王冠用に供した場合に、王冠成形時に襞が王冠上面から発生する形状不良をまねく。同様に、鋼板を例えばDRD缶用に供した場合、DRD缶成形時にフランジ部にしわが発生する形状不良をまねく。さらには、耐食性が低下する。以上より、Pの含有量は0.020%以下とする。好ましくは、0.015%以下とする。なお、Pを0.001%未満とするには脱Pコストが過大となるため、Pの含有量は0.001%以上とすることが好ましい。
Sの含有量が0.020%を超えると、鋼板中で介在物を形成し、鋼板の熱間延性の低下並びに耐食性の劣化をもたらす上、鋼板の成形性が低下し、鋼板を例えば王冠用に供した場合に、王冠成形時に襞が王冠上面から発生する形状不良をまねく。同様に、鋼板を例えばDRD缶用に供した場合、DRD缶成形時にフランジ部にしわが発生する形状不良をまねく。したがって、Sの含有量は0.020%以下とする。好ましくは、0.015%以下とする。なお、Sを0.005%未満とするには脱Sコストが過大となるため、Sの含有量は0.004%以上とすることが好ましい。
Alは、製鋼時の脱酸剤として必要な元素であるが、Al含有量が0.01%未満では、脱酸が不十分となり介在物が増加し、鋼板の成形性が低下し、鋼板を例えば王冠用に供した場合に、王冠成形時に襞が王冠上面から発生する形状不良をまねく。同様に、鋼板を例えばDRD缶用に供した場合、DRD缶成形時にフランジ部にしわが発生する形状不良をまねく。一方、Alが0.07%を超えると、AlNが多量に形成されるため、鋼中のNが減少し後述するNの効果を得られなくなる。以上より、Al含有量は0.01%以上0.07%以下とする。好ましくは、0.15%以上0.55%以下とする。
Nは、侵入型元素であり、Cと同様に、微量の添加で大きな固溶強化が得られる。この固溶強化により鋼板素地の摩擦力を向上させる結果、後述の二次冷間圧延中の転位の移動速度が低下し、低い圧下率でも材料に多量の転位が導入され、転位密度が向上する。すなわち、N含有量が0.0080%未満では、鋼板表面から板厚の1/2深さ位置における転位密度が2.0×1014/m2未満となり、鋼板を例えば王冠用に供して薄肉の王冠とした場合に、従来の厚肉の王冠と同等の耐衝撃性が得られない。同様に、鋼板を例えばDRD缶用に供して薄肉のDRD缶とした場合に、従来のDRD缶と同等の耐衝撃性が得られない。一方、N含有量が0.0200%を超えると、鋼板表面から板厚の1/2深さ位置における転位密度が1.0×1015/m2超えとなり、鋼板の成形性が低下し、鋼板を例えば王冠用に供した場合、王冠成形時に襞が王冠上面から発生する形状不良をまねく。同様に、鋼板を例えばDRD缶用に供した場合、DRD缶成形時にフランジ部にしわが発生する形状不良をまねく。以上より、N含有量は0.0080%以上0.0200%以下とする。好ましくは、0.0090%以上0.019%以下である。
以上の成分以外の残部はFeおよび不可避的不純物である。
さて、本発明者らが鋭意研究を重ねた結果、鋼板の強度は鋼板を例えば王冠用に供した場合の王冠の耐衝撃性で評価することができ、あるいは、鋼板を例えばDRD缶用に供した場合のDRD缶の耐衝撃性で評価することができ、これらの耐衝撃性は転位密度の増加で向上することを見出した。ここで、鋼板表面から板厚の1/2深さ位置における転位密度が2.0×1014/m2以上であれば、薄肉化しても従来の厚肉の王冠やDRD缶と同等の耐衝撃性を得ることができる。この理由は明確ではないが、転位密度が増加すると転位同士によるピン止めにより変形抵抗が増加するものと考えられる。そのために、王冠に例えば瓶内圧が高い状態で外部から衝撃が加わったときにも王冠がはずれにくくなる。あるいは、例えばDRD缶に外部から衝撃が加わったときにも、缶は変形しづらくなる。従って、鋼板表面から板厚の1/2深さ位置における転位密度を2.0×1014/m2以上とする。
製造工程としては、熱間圧延工程と、酸洗工程と、一次冷間圧延工程と、焼鈍工程と、二次冷間圧延工程とを有する。なお、以下の説明において、温度の規定は鋼板(素材)の表面温度とする。
得られた鋼素材を、熱間圧延工程に供する。この熱間圧延工程は、上記成分組成を有する鋼素材を、1200℃以上で加熱し、仕上げ圧延後に670℃以下の温度域にて巻取る工程である。
鋼素材を再加熱する場合、鋼素材再加熱温度が1200℃未満では、AlNを十分に溶解できず、二次冷間圧延工程時に固溶Nが確保できないため、転位密度向上の効果が得られず、鋼板表面から板厚の1/2深さ位置における転位密度が2.0×1014/m2未満となり、鋼板を例えば王冠用に供して薄肉の王冠とした場合に、従来の厚肉の王冠と同等の耐衝撃性が得られない。あるいは、鋼板を例えばDRD缶用に供して薄肉のDRD缶とした場合に、従来のDRD缶と同等の耐衝撃性が得られない。なお、酸化重量の増加にともなうスケールロスの増大などから、スラブ加熱温度は1300℃以下とすることが望ましい。なお、スラブ加熱温度を低くしても熱間圧延時のトラブルを防止するといった観点から、シートバーを加熱する、いわゆるシートバーヒーターを活用してもよい。
熱間圧延工程の仕上圧延温度は、圧延荷重の安定性の観点から850℃以上であることが好ましい。一方、必要以上に仕上圧延温度を高くすることは薄鋼板の製造を困難にする場合がある。具体的には、仕上圧延温度は850~960℃の温度範囲内とすることが好ましい。
巻取り温度が670℃を超えると、巻取り後に鋼中に析出するAlN量が多くなり、二次冷間圧延工程時に固溶Nが十分に確保できないため、転位密度向上の効果が得られず、板厚方向で表面から板厚の1/2深さ位置における転位密度が2.0×1014/m2未満となる。従って、巻取り温度は670℃以下とする。好ましくは、640℃以下とする。一方、巻取り温度の下限は特に限定されないが、巻取り温度が過度に低下すると、熱間圧延工程で得た熱延鋼板の強度が増加し、一次冷間圧延工程での圧延荷重が増大し圧延の制御が困難となるため、巻取り温度は500℃以上が好ましい。
次いで、酸洗を行う。酸洗工程は、熱延工程で得た熱延鋼板の表面の酸化スケールを酸洗により除去する工程である。酸洗条件は特に限定されず、適宜設定すればよい。
前記酸洗後に、一次冷間圧延を行う。一次冷間圧延工程は、酸洗工程後の酸洗板に冷間圧延を施す工程である。冷間圧延条件は特に限定されず、例えば所望の板厚等の観点から圧下率等の条件を決定すればよい。二次冷間圧延後の鋼板の板厚を0.20mm以下にするためには、圧下率85~94%とすることが好ましい。
次に、一次冷間圧延板に、焼鈍を行う。焼鈍工程は、一次冷間圧延工程で得た冷延鋼板を、650℃以上750℃以下の温度域で焼鈍する工程である。焼鈍温度が650℃未満では、焼鈍中にAlNが析出し、続く二次冷間圧延工程時に固溶Nが確保できないため、転位密度向上の効果が得られず、鋼板表面から板厚の1/2深さ位置における転位密度が2.0×1014/m2未満となる。さらに、焼鈍温度が650℃未満では、未再結晶組織の面積率が5%を超えて成形性が悪化する。
前記焼鈍後の焼鈍板に二次冷間圧延を行う。二次冷間圧延工程は、前記焼鈍工程で得た焼鈍板に、2台以上のスタンドを有する圧延設備にて各スタンド間の平均張力を98MPa以上として、かつ10%以上30%以下の圧下率での冷間圧延を行う工程である。
各スタンド間の平均張力が98MPa未満の場合、鋼板表面から板厚の1/2深さ位置における転位密度が2.0×1014/m2未満となる。各スタンド間の平均張力は127.4MPa以上であることが好ましい。一方、各スタンド間の平均張力の上限は特に限定されず、操業性の観点から決定すればよい。例えば、鋼板が破断しない程度の張力であればよい。具体的には392MPa以下が好ましい。
二次冷間圧延の圧下率が10%未満の場合、鋼板表面から板厚の1/2深さ位置における転位密度が2.0×1014/m2未満となる。一方、二次冷間圧延の圧下率が30%を超えると、鋼板表面から板厚の1/2深さ位置における転位密度が1.0×1015/m2を超え、鋼板の成形性が低下する。以上より、二次冷間圧延の圧下率は10%以上30%以下とする。二次冷間圧延の圧下率は12%以上28%以下が好ましい。
王冠は、主に瓶の口を塞ぐ円盤状の部分と、その周囲に設けられた襞状の部分とから構成され、上述した鋼板を円形のブランクに打ち抜いた後、プレス成形により成形することができる。本発明の鋼板を素材とする王冠は、王冠として優れた成形形状を呈し、耐衝撃性に優れており、使用に伴う廃棄物の排出量を減らす効果も有する。
No.12は二次冷間圧延工程の各スタンド間の平均張力が本発明の範囲をはずれて98MPa未満であり、板厚方向で表面から板厚の1/2深さ位置における転位密度が本発明の範囲をはずれて2.0×1014/m2未満であり、耐衝撃性が従来の王冠とDRD缶より劣っている。
Claims (5)
- 質量%で、
C:0.006%超0.012%以下、
Si:0.02%以下、
Mn:0.10%以上0.60%以下、
P:0.020%以下、
S:0.020%以下、
Al:0.01%以上0.07%以下および
N:0.0080%以上0.0200%以下
を含有し、残部はFeおよび不可避的不純物の成分組成を有し、鋼板表面から板厚の1/2深さ位置における転位密度が2.0×1014/m2以上1.0×1015/m2以下である鋼板。 - 板厚が0.20mm以下である請求項1に記載の鋼板。
- 請求項1または2に記載の鋼板からなる王冠。
- 請求項1または2に記載の鋼板からなるDRD缶。
- 請求項1または2に記載の鋼板の製造方法であって、
鋼素材を1200℃以上で加熱し、仕上げ圧延後に670℃以下の温度域にて巻取る熱間圧延工程と、
前記熱間圧延後の熱延板に酸洗を行う酸洗工程と、
前記酸洗後の熱延板に冷間圧延する一次冷間圧延工程と、
前記一次冷間圧延後の冷延板に、650℃以上750℃以下の温度域で焼鈍する焼鈍工程と、
前記焼鈍後の焼鈍板に、2台以上のスタンドを有する圧延設備にて各スタンド間の平均張力を98MPa以上として、10%以上30%以下の圧下率での冷間圧延を行う二次冷間圧延工程と、
を有する鋼板の製造方法。
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