WO2016084353A1 - Steel sheet for crown cap, manufacturing method therefor, and crown cap - Google Patents

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

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Publication number
WO2016084353A1
WO2016084353A1 PCT/JP2015/005782 JP2015005782W WO2016084353A1 WO 2016084353 A1 WO2016084353 A1 WO 2016084353A1 JP 2015005782 W JP2015005782 W JP 2015005782W WO 2016084353 A1 WO2016084353 A1 WO 2016084353A1
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WO
WIPO (PCT)
Prior art keywords
rolling
less
yield strength
crown
annealing
Prior art date
Application number
PCT/JP2015/005782
Other languages
French (fr)
Japanese (ja)
Inventor
田中　匠
智也 平口
克己 小島
裕樹 中丸
房亮 假屋
Original Assignee
Ｊｆｅスチール株式会社
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority to KR1020177013154A priority Critical patent/KR101975129B1/en
Priority to CN201580062055.8A priority patent/CN107109559B/en
Priority to NZ730832A priority patent/NZ730832A/en
Priority to CA2963622A priority patent/CA2963622C/en
Priority to BR112017010201-3A priority patent/BR112017010201B1/en
Priority to MX2017006871A priority patent/MX2017006871A/en
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 JP2016515154A priority patent/JP5988012B1/en
Priority to US15/527,167 priority patent/US20170335438A1/en
Priority to AU2015351836A priority patent/AU2015351836B2/en
Publication of WO2016084353A1 publication Critical patent/WO2016084353A1/en
Priority to PH12017500676A priority patent/PH12017500676A1/en
Priority to CONC2017/0004922A priority patent/CO2017004922A2/en

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • 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
    • B65D41/12—Caps or cap-like covers adapted to be secured in position by permanent deformation of the wall-engaging parts made of relatively stiff metallic materials, e.g. crown caps
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
    • 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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • 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

Definitions

  • the present invention relates to a steel plate used as a material for a crown as a stopper of a glass bottle, a manufacturing method thereof, and a crown.
  • 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.
  • Strength and formability are listed as the properties required for thin steel sheets used as crown materials. Bottles in which crowns are used are often filled with contents that generate internal pressure, such as beer and carbonated drinks. Even when the internal pressure increases due to changes in temperature, etc., the strength is required so that the crown is not deformed and the seal of the bottle is not broken. Further, even if the strength of the material is sufficient, the shape of the bag becomes non-uniform if the moldability is poor, and sufficient sealing performance may not be obtained even if it is caulked on the mouth of the bottle.
  • SR (Single Reduced) steel plate is mainly used for the thin steel plate as the crown material.
  • the SR steel sheet is manufactured by performing annealing and temper rolling after thinning the steel sheet by cold rolling.
  • the plate thickness of the crown material is 0.20 mm or more, and it is possible to ensure sufficient strength and formability by applying SR material made of mild steel used for food and beverage cans, etc. there were.
  • Patent Document 1 contains N: 0.0040 to 0.0300%, Al: 0.005 to 0.080% by weight%, 0.2% proof stress: 430 MPa or less, and total elongation: 15 to 40. %, Q ⁇ 1 due to internal friction: 0.0010 or more, disclosed is an ultrathin soft steel sheet for containers excellent in can strength and can moldability.
  • 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% Discloses a steel sheet 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 grain elongation of 5.0 or more in the cross section in the rolling direction. Has been.
  • Patent Document 1 Since the steel sheet described in Patent Document 1 is soft and contains a large amount of N, it is necessary to increase the secondary cold rolling rate in order to obtain a required strength. If the secondary cold rolling rate is increased, the anisotropy also increases and the workability is impaired.
  • the steel sheet described in Patent Document 2 has a large N content, so it is difficult to achieve both strength and workability required for the crown material.
  • the present invention has been made in view of such circumstances, and provides a crown steel plate having sufficient strength and formability even when thinned and used, and a method for producing the same, and a crown. For the purpose.
  • the present inventors have conducted intensive research to solve the above problems. As a result, it was found that a steel plate for a crown having sufficient strength and formability can be obtained by optimizing steel components, hot rolling conditions, annealing conditions, and secondary cold rolling conditions (DR conditions). .
  • a steel plate for a crown that is equal to or less than the average yield strength in the direction of 90 ° from the rolling direction.
  • C 0.010% or more and 0.025% or less
  • Si 0.10% or less
  • Mn 0.05% or more and 0.50% or less
  • P 0.050% or less
  • S Slab containing 0.005% or more and 0.050% or less
  • Al 0.020% or more and 0.070% or less
  • N less than 0.0040%, with the balance being composed of Fe and inevitable impurities
  • the yield strength in the rolling direction is A steel plate for a crown having a yield strength in the direction of 45 ° from the rolling direction in the rolling surface that is 50 MPa or more and less than the average value of the yield strength in the rolling direction and the yield strength in the direction of 90 ° from the rolling direction in the rolling surface. Manufacturing method.
  • a crown steel plate having sufficient strength and formability can be obtained even if it is used after being thinned. Both the strength of the steel sheet and the crown formability can be achieved, and the crown can be made thinner.
  • the steel sheet of the present invention has a specific component composition, and the yield strength after heat treatment at 210 ° C. for 15 minutes has a yield strength in the rolling direction of 550 MPa or more, and is 45 ° from the rolling direction in the rolling surface.
  • the yield strength is equal to or less than the average value of the yield strength in the rolling direction and the yield strength in the direction of 90 ° from the rolling direction in the rolling plane.
  • Component composition The component composition of this invention is demonstrated.
  • C 0.010% or more and 0.025% or less C is an element that contributes to both strength and workability by regulating the content within an optimum range. If the C content is less than 0.010%, the amount of strengthening due to the solid solution C is small, so that the strength is insufficient. On the other hand, if the C content exceeds 0.025%, the shape of the crown of the molded crown becomes uneven and the shape becomes poor. Therefore, the C content is 0.010% or more and 0.025% or less.
  • Si 0.10% or less Since an excessive Si content adversely affects the moldability, the content exceeding 0.10% is not desirable. Therefore, the Si content is set to 0.10% or less. From the point of strength improvement of a steel plate, it is preferably 0.02% or more and 0.10% or less.
  • Mn 0.05% or more and 0.50% or less
  • Mn content is less than 0.05%, it becomes difficult to avoid hot brittleness even when the S content is reduced, and surface cracks occur during continuous casting. Problems arise.
  • Mn is contained in excess of 0.50%, similarly to Si, the moldability is adversely affected. Therefore, the Mn content is 0.05% or more and 0.50% or less.
  • the P content is 0.050% or less.
  • S 0.005% or more and 0.050% or less S combines with Mn in steel to form MnS, and precipitates in a large amount to lower the hot ductility of the steel. This effect becomes significant when the S content exceeds 0.050%. On the other hand, desulfurization cost becomes excessive to make the S content less than 0.005%. Therefore, the S content is set to 0.005% or more and 0.050% or less.
  • Al 0.020% to 0.070%
  • Al is an element added as a deoxidizer. Moreover, N and AlN in steel are formed, and solid solution N in steel is reduced. If the Al content is less than 0.020%, the effect as a deoxidizer is insufficient, and solidification defects are generated. On the other hand, when secondary cold rolling is large, a large amount of Al becomes a cause of a decrease in formability. When the Al content exceeds 0.070%, the shape of the ridge becomes non-uniform at the time of crown molding, causing a shape defect. Therefore, the Al content is set to 0.020% or more and 0.070% or less.
  • N Less than 0.0040%
  • the content of N is 0.0040% or more, the steel sheet becomes hard and formability deteriorates. Therefore, the N content is less than 0.0040%. Preferably it is 0.0035% or less.
  • the balance other than the above essential components is iron and inevitable impurities.
  • the steel plate for the crown is required to have such strength that the crown does not come off against the internal pressure of the bottle.
  • the steel plate for crowns that has been used conventionally has a thickness of 0.20 mm or more.
  • the yield strength in the rolling direction of the steel sheet is less than 550 MPa, it is impossible to give sufficient strength to the thinned crown as described above, and the pressure strength is insufficient. Therefore, the yield strength in the rolling direction is 550 MPa or more.
  • the yield strength of a DR steel sheet varies depending on the direction in the rolling plane. If the yield strength in the direction of 45 ° from the rolling direction exceeds the average value of the yield strength in the rolling direction and the yield strength in the direction of 90 ° from the rolling direction, the formability deteriorates. Therefore, in the present invention, the yield strength in the direction of 45 ° from the rolling direction in the rolling surface is set to be equal to or less than the average value of the yield strength in the rolling direction and the yield strength in the direction of 90 ° from the rolling direction in the rolling surface.
  • the difference obtained by subtracting the yield strength in the direction of 45 ° from the rolling direction in the rolling surface from the average value of the yield strength in the rolling direction and the yield strength in the direction of 90 ° from the rolling direction in the rolling surface is 0 MPa or more. . Preferably, it is 10 MPa or more and 25 MPa or less.
  • each yield strength shall be measured after 210 degreeC and the heat processing equivalent to a coating baking for 15 minutes, and the metallic material tension test method shown by "JISZ2241" can be applied.
  • the method for producing a crown steel plate according to the present invention includes a hot rolling step in which a steel slab having the above component composition is hot rolled and wound at a winding temperature of 530 ° C. or higher and 590 ° C. or lower, and after the hot rolling step.
  • a secondary cold rolling process for performing secondary cold rolling will be described.
  • the molten steel is adjusted to the above chemical components by a known method using a hot rolling process converter or the like, and is made into a slab by a continuous casting method. Subsequently, the steel slab is roughly rolled hot.
  • the method of rough rolling is not limited, but the heating temperature of the slab is preferably 1200 ° C. or higher.
  • finish rolling is performed.
  • the finish rolling temperature is preferably 850 ° C. or higher from the viewpoint of rolling load stability.
  • the finish rolling temperature here is a plate temperature when entering the final stand of the finish rolling mill. On the other hand, raising the finish rolling temperature more than necessary may make it difficult to produce a thin steel sheet.
  • the finishing temperature is preferably 850 ° C. or higher and 900 ° C. or lower. If the coiling temperature in the hot rolling process is less than 530 ° C., it is not suitable to operate without impairing the efficiency because the finish rolling temperature needs to be lowered accordingly. On the other hand, when the coiling temperature is higher than 590 ° C., the amount of AlN precipitated after the coiling becomes excessive, which leads to fine graining after annealing and lowers the formability. Accordingly, the coiling temperature is set to 530 ° C. or more and 590 ° C. or less. Preferably they are 540 degreeC or more and 580 degrees C or less.
  • the method for removing the surface scale is not particularly limited, and various conventional methods such as pickling and physical removal can be applied, but it can be suitably removed by pickling.
  • the conditions for pickling are not particularly limited, and may be pickled by a conventional method.
  • the rolling ratio of primary cold rolling is preferably 85% or more in order to produce an ultrathin material.
  • a rolling rate shall be 94% or less.
  • Annealing Step If the annealing temperature is higher than 720 ° C., it is not preferable because troubles such as a heat buckle are likely to occur during continuous annealing. When the annealing temperature is less than 650 ° C., recrystallization becomes incomplete and the material becomes non-uniform. Therefore, annealing temperature shall be 650 degreeC or more and 720 degrees C or less.
  • the soaking time in the annealing step is not particularly limited, but it is preferably 10 seconds or more in order to reliably obtain a recrystallized structure, and 50 seconds or less in order to prevent excessive grain growth. .
  • Secondary cold rolling (DR rolling) step The steel sheet after annealing is strengthened by secondary cold rolling. If the rolling ratio of secondary cold rolling is less than 25%, sufficient strength cannot be obtained to ensure the pressure resistance of the crown. Also, when the rolling ratio of secondary cold rolling exceeds 40%, the yield strength in the direction of 45 ° from the rolling direction in the rolling surface, the yield strength in the rolling direction, and the direction of 90 ° from the rolling direction in the rolling surface The difference in the average value of the yield strengths of the steels becomes positively large and the formability is impaired. Therefore, the rolling rate of secondary cold rolling is set to 25% or more and 40%.
  • the high-strength steel plate of the present invention is obtained. Even if the steel sheet obtained here is subjected to surface treatment such as plating or chemical conversion, the effects of the invention are not lost.
  • a steel slab was obtained by melting a steel having the composition shown in Table 1 with the balance being Fe and inevitable impurities in a converter and continuously casting the steel. After the obtained steel slab was heated to 1250 ° C., it was hot-rolled at a rolling start temperature of 1150 ° C. and a finish rolling temperature of 860 ° C., and wound at the winding temperature shown in Table 2. Next, after removing the scale by pickling, primary cold rolling is performed at the primary cold rolling rate shown in Table 2, annealing is performed at the annealing temperature shown in Table 2 in a continuous annealing furnace, and secondary cooling shown in Table 2 is performed.
  • Yield strength After performing a heat treatment equivalent to baking at 210 ° C. for 15 minutes, a tensile test was conducted. The tensile test is performed according to “JIS Z 2241” using a JIS No. 5 size tensile test piece, the yield strength in the rolling direction, the yield strength in the direction of 45 ° from the rolling direction in the rolling surface, and the rolling direction in the rolling surface. The yield strength in the direction of 90 ° was measured.
  • Crown formability A crown was formed using the obtained steel sheet, and the crown formability was evaluated. Using 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 evaluation was performed visually, and the case where all the sizes of the wrinkles were aligned was evaluated as ⁇ , the case where the sizes of the wrinkles were almost aligned was evaluated as ⁇ , and the case where the sizes of the wrinkles were not aligned was evaluated as ⁇ . In addition, in the above visual determination, it was determined that the case where the maximum value of the width (spread) of the wrinkles was 1.5 times the minimum value was not uniform.
  • the steel sheets of levels 1 to 6 which are examples of the present invention have a yield strength in the rolling direction of 550 MPa, and the yield strength in the direction of 45 ° from the rolling direction in the rolling surface is the yield strength in the rolling direction. It is below the average value of the yield strength in the direction of 90 ° from the rolling direction in the rolling surface, and both the crown formability and the pressure strength are good.
  • the steel sheet of level 7 as a comparative example has too little C content, so the yield strength in the rolling direction is less than 550 MPa, and the pressure strength is insufficient.
  • the steel plate of level 8 as a comparative example has an annealing temperature too low, the yield strength in the direction of 45 ° from the rolling direction is the average value of the yield strength in the rolling direction and the yield strength in the direction of 90 ° from the rolling direction in the rolling plane.
  • the crown formability is inferior. Since the crown has a poor shape, the sealing performance is insufficient, and the pressure resistance is low.
  • the steel plate of level 9 as a comparative example has a secondary cold rolling rate that is too small, the yield strength in the rolling direction is less than 550 MPa, the crown formability is inferior, and the pressure strength is insufficient.

Abstract

Provided are: a steel sheet for a crown cap that has adequate strength and moldability even when used after being made thin; a manufacturing method therefor; and a crown cap. The steel sheet has a composition containing, in mass%, C: 0.010% to 0.025%, Si: not more than 0.10%, Mn: 0.05% to 0.50%, P: not more than0.050%, S: 0.005% to 0.050%, Al: 0.020% to 0.070%, and N: less than 0.0040%, the balance being obtained from Fe and unavoidable impurities. Regarding yield strength after heat treatment for fifteen minutes at 210°C, yield strength in the rolling direction is at least 550 MPa and yield strength in the rolling plane in a direction that is 45° from the rolling direction is not more than the mean of the yield strength in the rolling direction and the yield strength in the rolling plane in a direction that is 90° from the rolling direction.

Description

王冠用鋼板およびその製造方法ならびに王冠Crown steel plate, method for producing the same, and crown
　本発明は、ガラス瓶の栓としての王冠の材料に用いられる鋼板およびその製造方法ならびに王冠に関するものである。 The present invention relates to a steel plate used as a material for a crown as a stopper of a glass bottle, a manufacturing method thereof, and a crown.
　清涼飲料水や酒類などの飲料用の容器には古くからガラス瓶が多く用いられており、細口のガラス瓶には王冠と呼ばれる金属製の栓が広く用いられている。一般的に、王冠は薄鋼板を素材としてプレス成形によって製造され、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からなり、襞状の部分を瓶の口にかしめることによって瓶を密封する。 Glass bottles for drinks such as soft drinks and liquors have long been used for glass bottles, and metal stoppers called crowns have been widely used for narrow-mouth glass bottles. In general, 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.
　王冠の素材となる薄鋼板に必要とされる特性として、強度と成形性が挙げられる。王冠が用いられる瓶には、ビールや炭酸飲料など、内圧を生じる内容物が充填されることが多い。温度の変化などで内圧が高まった場合にも、王冠が変形して瓶の密封が破られることの無い様な強度が必要である。また、素材の強度が十分であっても、成形性に乏しい場合は襞の形状が不均一になり、瓶の口にかしめても十分な密封性が得られない場合が生じる。 Strength and formability are listed as the properties required for thin steel sheets used as crown materials. Bottles in which crowns are used are often filled with contents that generate internal pressure, such as beer and carbonated drinks. Even when the internal pressure increases due to changes in temperature, etc., the strength is required so that the crown is not deformed and the seal of the bottle is not broken. Further, even if the strength of the material is sufficient, the shape of the bag becomes non-uniform if the moldability is poor, and sufficient sealing performance may not be obtained even if it is caulked on the mouth of the bottle.
　王冠の素材としての薄鋼板には、主にＳＲ（Ｓｉｎｇｌｅ　Ｒｅｄｕｃｅｄ）鋼板が用いられている。ＳＲ鋼板は、冷間圧延により鋼板を薄くした後に、焼鈍を施し、調質圧延を行うことで製造される。従来は、王冠の素材の板厚は０．２０ｍｍ以上であり、食品や飲料の缶などに用いる軟鋼を素材としたＳＲ材を適用することで十分な強度と成形性を確保することが可能であった。 SR (Single Reduced) steel plate is mainly used for the thin steel plate as the crown material. The SR steel sheet is manufactured by performing annealing and temper rolling after thinning the steel sheet by cold rolling. Conventionally, the plate thickness of the crown material is 0.20 mm or more, and it is possible to ensure sufficient strength and formability by applying SR material made of mild steel used for food and beverage cans, etc. there were.
　しかしながら、近年、缶用鋼板同様、王冠の素材についてもコストダウンを目的とした薄肉化の要求が高まっている。王冠の素材の板厚が０．２０ｍｍ未満になると、従来のＳＲ鋼板では強度不足となる。強度確保のためには焼鈍のあとに二次冷間圧延を施すＤＲ（Ｄｏｕｂｌｅ　Ｒｅｄｕｃｅｄ）鋼板の適用が考えられる。しかし、二次冷間圧延率を大きくすると成形性が低下し、瓶の密封不良を生じる。 However, in recent years, as with steel plates for cans, there is an increasing demand for thinning the crown material to reduce costs. If the thickness of the crown material is less than 0.20 mm, the conventional SR steel sheet will have insufficient strength. In order to ensure the strength, it is conceivable to apply a DR (Double Reduced) steel sheet that is subjected to secondary cold rolling after annealing. However, when the secondary cold rolling rate is increased, the formability is lowered, resulting in poor sealing of the bottle.
　上記を受けて、これまで、強度と成形性の両者に優れる鋼板を得るために、以下のような技術が提案されている。 In response to the above, the following techniques have been proposed so far in order to obtain a steel sheet excellent in both strength and formability.
　特許文献１には、重量％で、Ｎ：０．００４０～０．０３００％、Ａｌ：０．００５～０．０８０％を含有し、０．２％耐力：４３０ＭＰａ以下、全伸び：１５～４０％、内部摩擦によるＱ－１：０．００１０以上であることを特徴とする缶強度、缶成形性に優れる容器用極薄軟質鋼板が開示されている。 Patent Document 1 contains N: 0.0040 to 0.0300%, Al: 0.005 to 0.080% by weight%, 0.2% proof stress: 430 MPa or less, and total elongation: 15 to 40. %, Q −1 due to internal friction: 0.0010 or more, disclosed is an ultrathin soft steel sheet for containers excellent in can strength and can moldability.
　特許文献２には、質量％で、Ｃ：０．００１～０．０８０％、Ｓｉ：０．００３～０．１００％、Ｍｎ：０．１０～０．８０％、Ｐ：０．００１～０．１００％、Ｓ：０．００１～０．０２０％、Ａｌ：０．００５～０．１００％、Ｎ：０．００５０～０．０１５０％、Ｂ：０．０００２～０．００５０％を含有し、圧延方向断面にて結晶粒の展伸度が５．０以上である結晶粒を面積率にして０．０１～１．００％含むことを特徴とする高強度高加工性缶用鋼板が開示されている。 In 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% Discloses a steel sheet 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 grain elongation of 5.0 or more in the cross section in the rolling direction. Has been.
特開２００１－４９３８３号公報JP 2001-49383 A 特開２０１３－２８８４２号公報JP 2013-28842 A
　しかし、上記従来技術には下記に示す問題が挙げられる。 However, the above-mentioned prior art has the following problems.
　特許文献１に記載の鋼板は、軟質かつＮを多く含有するため、必要な強度を得るためには二次冷間圧延率を大きくする必要がある。二次冷間圧延率を大きくすると異方性も大きくなり、加工性が損なわれる。 Since the steel sheet described in Patent Document 1 is soft and contains a large amount of N, it is necessary to increase the secondary cold rolling rate in order to obtain a required strength. If the secondary cold rolling rate is increased, the anisotropy also increases and the workability is impaired.
　特許文献２に記載の鋼板も特許文献１に記載の鋼板と同様に、Ｎの含有量が多いため、王冠の素材に求められる強度と加工性を両立することは難しい。 Similarly to the steel sheet described in Patent Document 1, the steel sheet described in Patent Document 2 has a large N content, so it is difficult to achieve both strength and workability required for the crown material.
　本発明は、かかる事情に鑑みなされたもので、上述した従来技術の問題を解決し、薄肉化して使用しても十分な強度と成形性を備える王冠用鋼板およびその製造方法ならびに王冠を提供することを目的とする。 The present invention has been made in view of such circumstances, and provides a crown steel plate having sufficient strength and formability even when thinned and used, and a method for producing the same, and a crown. For the purpose.
　本発明者らは、上記課題を解決するために鋭意研究を行った。その結果、鋼成分、熱間圧延条件、焼鈍条件、および二次冷間圧延条件（ＤＲ条件）を最適化することで、十分な強度と成形性を備える王冠用鋼板が得られることを見出した。 The present inventors have conducted intensive research to solve the above problems. As a result, it was found that a steel plate for a crown having sufficient strength and formability can be obtained by optimizing steel components, hot rolling conditions, annealing conditions, and secondary cold rolling conditions (DR conditions). .
　本発明は以上の知見に基づいてなされたものであり、以下を要旨とするものである。
［１］質量％で、Ｃ：０．０１０％以上０．０２５％以下、Ｓｉ：０．１０％以下、Ｍｎ：０．０５％以上０．５０％以下、Ｐ：０．０５０％以下、Ｓ：０．００５％以上０．０５０％以下、Ａｌ：０．０２０％以上０．０７０％以下、Ｎ：０．００４０％未満を含有し、残部はＦｅおよび不可避的不純物からなる成分組成を有し、２１０℃、１５分の熱処理後の降伏強度について、圧延方向の降伏強度が５５０ＭＰａ以上であり、圧延面内における圧延方向から４５°の方向の降伏強度が、圧延方向の降伏強度と圧延面内における圧延方向から９０°の方向の降伏強度の平均値以下である王冠用鋼板。
［２］上記［１］に記載の王冠用鋼板の製造方法であって、スラブを、熱間圧延し、巻取り温度５３０℃以上５９０℃以下で巻取る熱間圧延工程と、前記熱間圧延工程後、冷間圧延する一次冷間圧延工程と、前記一次冷間圧延工程後、焼鈍温度６５０℃以上７２０℃以下で焼鈍する焼鈍工程と、前記焼鈍工程後、圧延率２５％以上４０％以下で二次冷間圧延を行う二次冷間圧延工程と、を有する王冠用鋼板の製造方法。
［３］上記［１］に記載の王冠用鋼板からなる王冠。
［４］質量％で、Ｃ：０．０１０％以上０．０２５％以下、Ｓｉ：０．１０％以下、Ｍｎ：０．０５％以上０．５０％以下、Ｐ：０．０５０％以下、Ｓ：０．００５％以上０．０５０％以下、Ａｌ：０．０２０％以上０．０７０％以下、Ｎ：０．００４０％未満を含有し、残部はＦｅおよび不可避的不純物からなる成分組成を有するスラブを、熱間圧延し、巻取り温度５３０℃以上５９０℃以下で巻取る熱間圧延工程と、前記熱間圧延工程後、冷間圧延する一次冷間圧延工程と、前記一次冷間圧延工程後、焼鈍温度６５０℃以上７２０℃以下で焼鈍する焼鈍工程と、前記焼鈍工程後、圧延率２５％以上４０％以下で二次冷間圧延を行う二次冷間圧延工程と、を有する、２１０℃、１５分の熱処理後の降伏強度について、圧延方向の降伏強度が５５０ＭＰａ以上であり、圧延面内における圧延方向から４５°の方向の降伏強度が、圧延方向の降伏強度と圧延面内における圧延方向から９０°の方向の降伏強度の平均値以下である王冠用鋼板の製造方法。 This invention is made | formed based on the above knowledge, and makes the following a summary.
[1] By mass%, C: 0.010% or more and 0.025% or less, Si: 0.10% or less, Mn: 0.05% or more and 0.50% or less, P: 0.050% or less, S : 0.005% or more and 0.050% or less, Al: 0.020% or more and 0.070% or less, N: containing less than 0.0040%, the balance having a component composition composed of Fe and inevitable impurities With regard to the yield strength after heat treatment at 210 ° C. for 15 minutes, the yield strength in the rolling direction is 550 MPa or more, and the yield strength in the direction of 45 ° from the rolling direction in the rolling plane is the yield strength in the rolling direction and in the rolling plane. A steel plate for a crown that is equal to or less than the average yield strength in the direction of 90 ° from the rolling direction.
[2] The method for manufacturing a crown steel plate according to [1] above, wherein the slab is hot-rolled and wound at a winding temperature of 530 ° C. or higher and 590 ° C. or lower, and the hot rolling After the step, a primary cold rolling step for cold rolling, an annealing step for annealing at an annealing temperature of 650 ° C. to 720 ° C. after the primary cold rolling step, and a rolling rate of 25% to 40% after the annealing step. And a secondary cold rolling step of performing secondary cold rolling at a step.
[3] A crown made of the crown steel plate according to [1].
[4] In mass%, C: 0.010% or more and 0.025% or less, Si: 0.10% or less, Mn: 0.05% or more and 0.50% or less, P: 0.050% or less, S : Slab containing 0.005% or more and 0.050% or less, Al: 0.020% or more and 0.070% or less, N: less than 0.0040%, with the balance being composed of Fe and inevitable impurities , Hot rolling step of winding at a winding temperature of 530 ° C. or more and 590 ° C. or less, a primary cold rolling step of cold rolling after the hot rolling step, and after the primary cold rolling step An annealing step of annealing at an annealing temperature of 650 ° C. to 720 ° C., and a secondary cold rolling step of performing secondary cold rolling at a rolling rate of 25% to 40% after the annealing step, 210 ° C. About the yield strength after heat treatment for 15 minutes, the yield strength in the rolling direction is A steel plate for a crown having a yield strength in the direction of 45 ° from the rolling direction in the rolling surface that is 50 MPa or more and less than the average value of the yield strength in the rolling direction and the yield strength in the direction of 90 ° from the rolling direction in the rolling surface. Manufacturing method.
　本発明によれば、薄肉化して使用しても十分な強度と成形性を備える王冠用鋼板が得られる。鋼板の強度と王冠成形性の両立が可能となり、王冠の薄肉化が実現できる。 According to the present invention, a crown steel plate having sufficient strength and formability can be obtained even if it is used after being thinned. Both the strength of the steel sheet and the crown formability can be achieved, and the crown can be made thinner.
　以下、本発明について詳細に説明する。なお、以下の％は、特に断らない限り質量％を意味するものとする。 Hereinafter, the present invention will be described in detail. In addition, the following% shall mean the mass% unless there is particular notice.
　本発明の鋼板は、特定の成分組成を有し、２１０℃、１５分の熱処理後の降伏強度について、圧延方向の降伏強度が５５０ＭＰａ以上であり、圧延面内における圧延方向から４５°の方向の降伏強度が、圧延方向の降伏強度と圧延面内における圧延方向から９０°の方向の降伏強度の平均値以下である。その結果、十分な強度と成形性を備え、薄肉化して使用可能な王冠が得られる。 The steel sheet of the present invention has a specific component composition, and the yield strength after heat treatment at 210 ° C. for 15 minutes has a yield strength in the rolling direction of 550 MPa or more, and is 45 ° from the rolling direction in the rolling surface. The yield strength is equal to or less than the average value of the yield strength in the rolling direction and the yield strength in the direction of 90 ° from the rolling direction in the rolling plane. As a result, a crown that has sufficient strength and moldability and can be used after being thinned is obtained.
　成分組成
　本発明の成分組成について説明する。 Component composition The component composition of this invention is demonstrated.
　Ｃ：０．０１０％以上０．０２５％以下
Ｃは含有量を最適な範囲に規定することにより、強度と加工性の両立に寄与する元素である。Ｃ含有量が０．０１０％未満であると固溶Ｃによる強化量が小さいため、強度不足となる。一方、Ｃ含有量が０．０２５％を超えると、成形した王冠の襞の形状が不均一になり、形状不良となる。よって、Ｃ含有量は０．０１０％以上０．０２５％以下とする。 C: 0.010% or more and 0.025% or less C is an element that contributes to both strength and workability by regulating the content within an optimum range. If the C content is less than 0.010%, the amount of strengthening due to the solid solution C is small, so that the strength is insufficient. On the other hand, if the C content exceeds 0.025%, the shape of the crown of the molded crown becomes uneven and the shape becomes poor. Therefore, the C content is 0.010% or more and 0.025% or less.
　Ｓｉ：０．１０％以下
Ｓｉ含有量が過剰であると成形性に悪影響を及ぼすため、０．１０％を超える含有は望ましくない。よって、Ｓｉ含有量は０．１０％以下とする。鋼板の強度向上の点から、好ましくは０．０２％以上０．１０％以下である。 Si: 0.10% or less Since an excessive Si content adversely affects the moldability, the content exceeding 0.10% is not desirable. Therefore, the Si content is set to 0.10% or less. From the point of strength improvement of a steel plate, it is preferably 0.02% or more and 0.10% or less.
　Ｍｎ：０．０５％以上０．５０％以下
Ｍｎ含有量が０．０５％を下回ると、Ｓ含有量を低下させた場合で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も、Ｓｉと同様に、０．５０％超えの含有は成形性に悪影響を及ぼす。よって、Ｍｎ含有量は０．０５％以上０．５０％以下とする。 Mn: 0.05% or more and 0.50% or less When the Mn content is less than 0.05%, it becomes difficult to avoid hot brittleness even when the S content is reduced, and surface cracks occur during continuous casting. Problems arise. On the other hand, if Mn is contained in excess of 0.50%, similarly to Si, the moldability is adversely affected. Therefore, the Mn content is 0.05% or more and 0.50% or less.
　Ｐ：０．０５０％以下
Ｐ含有量が０．０５０％を超えると、鋼の硬質化や耐食性の低下が引き起こされる。よって、Ｐ含有量は０．０５０％以下とする。 P: 0.050% or less When the P content exceeds 0.050%, hardening of the steel and deterioration of corrosion resistance are caused. Therefore, the P content is 0.050% or less.
　Ｓ：０．００５％以上０．０５０％以下
Ｓは、鋼中でＭｎと結合してＭｎＳを形成し、多量に析出することで鋼の熱間延性を低下させる。Ｓの含有量が０．０５０％を超えるとこの影響が顕著となる。一方、Ｓ含有量を０．００５％未満とするには脱硫コストが過大となる。よって、Ｓ含有量は０．００５％以上０．０５０％以下とする。 S: 0.005% or more and 0.050% or less S combines with Mn in steel to form MnS, and precipitates in a large amount to lower the hot ductility of the steel. This effect becomes significant when the S content exceeds 0.050%. On the other hand, desulfurization cost becomes excessive to make the S content less than 0.005%. Therefore, the S content is set to 0.005% or more and 0.050% or less.
　Ａｌ：０．０２０％以上０．０７０％以下
Ａｌは、脱酸剤として添加される元素である。また、鋼中のＮとＡｌＮを形成し、鋼中の固溶Ｎを減少させる。Ａｌ含有量が０．０２０％未満であると脱酸剤としての効果が不十分であり、凝固欠陥の発生を招く。一方、二次冷間圧延が大きい場合には、多量のＡｌは成形性低下の要因となる。Ａｌ含有量が０．０７０％を超えると王冠成形時に襞の形状が不均一になり、形状不良を引き起こす。よって、Ａｌ含有量は０．０２０％以上０．０７０％以下とする。 Al: 0.020% to 0.070% Al is an element added as a deoxidizer. Moreover, N and AlN in steel are formed, and solid solution N in steel is reduced. If the Al content is less than 0.020%, the effect as a deoxidizer is insufficient, and solidification defects are generated. On the other hand, when secondary cold rolling is large, a large amount of Al becomes a cause of a decrease in formability. When the Al content exceeds 0.070%, the shape of the ridge becomes non-uniform at the time of crown molding, causing a shape defect. Therefore, the Al content is set to 0.020% or more and 0.070% or less.
　Ｎ：０．００４０％未満
Ｎの含有量が０．００４０％以上であると鋼板が硬質化し、成形性を悪化させる。よって、Ｎの含有量は０．００４０％未満とする。好ましくは０．００３５％以下である。 N: Less than 0.0040% When the content of N is 0.0040% or more, the steel sheet becomes hard and formability deteriorates. Therefore, the N content is less than 0.0040%. Preferably it is 0.0035% or less.
　上記必須成分以外の残部は鉄および不可避的不純物である。 The balance other than the above essential components is iron and inevitable impurities.
　機械的性質
　次に、本発明に係る王冠用鋼板の機械的性質について説明する。 Mechanical Properties Next, the mechanical properties of the crown steel plate according to the present invention will be described.
　王冠用鋼板には、瓶の内圧に対して王冠が外れる事が無いような強度が求められる。これを受けて、従来、用いられてきた王冠用鋼板の板厚は０．２０ｍｍ以上であった。しかし、薄肉化の要求が高まってきており、板厚０．２０ｍｍを下回るような薄肉化にあたっては従来より大きな強度が必要となる。鋼板の圧延方向の降伏強度が５５０ＭＰａ未満では、上記のような薄肉化した王冠に十分な強度を付与することが不可能であり、耐圧強度が不足する。したがって、圧延方向の降伏強度は５５０ＭＰａ以上とする。 The steel plate for the crown is required to have such strength that the crown does not come off against the internal pressure of the bottle. In response, the steel plate for crowns that has been used conventionally has a thickness of 0.20 mm or more. However, there is an increasing demand for thinning, and in order to reduce the thickness so that the thickness is less than 0.20 mm, higher strength than before is required. If the yield strength in the rolling direction of the steel sheet is less than 550 MPa, it is impossible to give sufficient strength to the thinned crown as described above, and the pressure strength is insufficient. Therefore, the yield strength in the rolling direction is 550 MPa or more.
　また、一般的にＤＲ鋼板においては圧延面内の方向によって降伏強度に差が生じる。圧延方向から４５°の方向の降伏強度が圧延方向の降伏強度と圧延方向から９０°の方向の降伏強度の平均値を超えると成形性が低下する。よって、本発明では、圧延面内における圧延方向から４５°の方向の降伏強度が、圧延方向の降伏強度と圧延面内における圧延方向から９０°の方向の降伏強度の平均値以下とする。すなわち、圧延方向の降伏強度と圧延面内における圧延方向から９０°の方向の降伏強度の平均値から、圧延面内における圧延方向から４５°の方向の降伏強度を引いた差は０ＭＰａ以上とする。好ましくは、１０ＭＰａ以上２５ＭＰａ以下である。 In general, the yield strength of a DR steel sheet varies depending on the direction in the rolling plane. If the yield strength in the direction of 45 ° from the rolling direction exceeds the average value of the yield strength in the rolling direction and the yield strength in the direction of 90 ° from the rolling direction, the formability deteriorates. Therefore, in the present invention, the yield strength in the direction of 45 ° from the rolling direction in the rolling surface is set to be equal to or less than the average value of the yield strength in the rolling direction and the yield strength in the direction of 90 ° from the rolling direction in the rolling surface. That is, the difference obtained by subtracting the yield strength in the direction of 45 ° from the rolling direction in the rolling surface from the average value of the yield strength in the rolling direction and the yield strength in the direction of 90 ° from the rolling direction in the rolling surface is 0 MPa or more. . Preferably, it is 10 MPa or more and 25 MPa or less.
　なお、後述の製造方法によって上記のような降伏強度の鋼板を製造することができる。
また、王冠を成形する際は、鋼板に焼付け塗装してから成形されることが多いため、塗装焼付けに相当する処理後の材質を評価する必要がある。よって、本発明では、各降伏強度は２１０℃、１５分の塗装焼付け相当の熱処理後に測定を行うものとし、「ＪＩＳ　Ｚ　２２４１」に示される金属材料引張試験方法が適用できる。 In addition, the steel plate of the above yield strengths can be manufactured with the manufacturing method mentioned later.
Further, when the crown is formed, since it is often formed after being baked and coated on a steel plate, it is necessary to evaluate a material after processing corresponding to the coating and baking. Therefore, in this invention, each yield strength shall be measured after 210 degreeC and the heat processing equivalent to a coating baking for 15 minutes, and the metallic material tension test method shown by "JISZ2241" can be applied.
　王冠用鋼板の製造方法
　以下、本発明の王冠用鋼板の製造方法の一例について説明する。 Hereinafter, an example of a method for manufacturing a crown steel plate according to the present invention will be described.
　本発明の王冠用鋼板の製造方法は、上記成分組成を有する鋼スラブを、熱間圧延し、巻取り温度５３０℃以上５９０℃以下にて巻取る熱間圧延工程と、前記熱間圧延工程後、冷間圧延する一次冷間圧延工程と、前記一次冷間圧延工程後、焼鈍温度６５０℃以上７２０℃以下で焼鈍する焼鈍工程と、前記焼鈍工程後、圧延率２５％以上４０％以下の二次冷間圧延を行う二次冷間圧延工程と、を有する。以下、各工程について説明する。 The method for producing a crown steel plate according to the present invention includes a hot rolling step in which a steel slab having the above component composition is hot rolled and wound at a winding temperature of 530 ° C. or higher and 590 ° C. or lower, and after the hot rolling step. A primary cold rolling step for cold rolling, an annealing step for annealing at an annealing temperature of 650 ° C. to 720 ° C. after the primary cold rolling step, and a rolling rate of 25% to 40% after the annealing step. A secondary cold rolling process for performing secondary cold rolling. Hereinafter, each step will be described.
　熱間圧延工程
転炉などを用いた公知の方法により、溶鋼を上記の化学成分に調整し、連続鋳造法によりスラブとする。続いて、鋼スラブを熱間で粗圧延する。粗圧延の方法は限定しないが、スラブの加熱温度は１２００℃以上であることが好ましい。次いで、仕上圧延を行う。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。なお、ここでの仕上圧延温度とは、仕上圧延機の最終スタンドに入る時の板温である。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。すなわち、板厚が薄い場合には圧延中の板温低下が大きいため、高い板温を保ったまま仕上圧延を行うことが難しく制御しにくくなる。よって、仕上温度は８５０℃以上９００℃以下が好ましい。
熱間圧延工程の巻取温度が５３０℃未満であると、能率を損なわずに操業するためには、これに応じて仕上圧延温度を低くする必要があるため、適さない。一方、巻取温度が５９０℃より高くなると、巻取り後に析出するＡｌＮ量が過大となり、焼鈍後の細粒化につながり成形性が低下する。従って、巻取温度は５３０℃以上５９０℃以下とする。好ましくは５４０℃以上５８０℃以下である。 The molten steel is adjusted to the above chemical components by a known method using a hot rolling process converter or the like, and is made into a slab by a continuous casting method. Subsequently, the steel slab is roughly rolled hot. The method of rough rolling is not limited, but the heating temperature of the slab is preferably 1200 ° C. or higher. Next, finish rolling is performed. The finish rolling temperature is preferably 850 ° C. or higher from the viewpoint of rolling load stability. In addition, the finish rolling temperature here is a plate temperature when entering the final stand of the finish rolling mill. On the other hand, raising the finish rolling temperature more than necessary may make it difficult to produce a thin steel sheet. That is, when the plate thickness is thin, the plate temperature drop during rolling is large, so that it is difficult to perform finish rolling while maintaining a high plate temperature and it is difficult to control. Therefore, the finishing temperature is preferably 850 ° C. or higher and 900 ° C. or lower.
If the coiling temperature in the hot rolling process is less than 530 ° C., it is not suitable to operate without impairing the efficiency because the finish rolling temperature needs to be lowered accordingly. On the other hand, when the coiling temperature is higher than 590 ° C., the amount of AlN precipitated after the coiling becomes excessive, which leads to fine graining after annealing and lowers the formability. Accordingly, the coiling temperature is set to 530 ° C. or more and 590 ° C. or less. Preferably they are 540 degreeC or more and 580 degrees C or less.
　一次冷間圧延工程
一次冷間圧延工程の前に表層スケールを除去することが好ましい。表層スケールの除去方法は特に限定するものではなく、酸洗や物理的な除去等、各種の常法が適用できるが、酸洗により好適に除去できる。酸洗の場合の条件も特に限定するものではなく、常法により酸洗すればよい。 Primary cold rolling process It is preferable to remove the surface scale before the primary cold rolling process. The method for removing the surface scale is not particularly limited, and various conventional methods such as pickling and physical removal can be applied, but it can be suitably removed by pickling. The conditions for pickling are not particularly limited, and may be pickled by a conventional method.
　一次冷間圧延の圧延率は、極薄材を製造するためには８５％以上が好ましい。しかし、圧延率が大きくなりすぎると、圧延機への負荷が過大となり、圧延そのものが困難になる場合がある。このため、圧延率は９４％以下とすることが好ましい。 The rolling ratio of primary cold rolling is preferably 85% or more in order to produce an ultrathin material. However, if the rolling rate becomes too large, the load on the rolling mill becomes excessive, and rolling itself may be difficult. For this reason, it is preferable that a rolling rate shall be 94% or less.
　焼鈍工程
　焼鈍温度が７２０℃超であると、連続焼鈍においてヒートバックルなどの通板トラブルが発生しやすくなり、好ましくない。焼鈍温度が６５０℃未満であると、再結晶が不完全となり、材質が不均一になる。従って、焼鈍温度は６５０℃以上７２０℃以下とする。なお、焼鈍工程での均熱時間は特に限定されないが、確実に再結晶組織を得るためには１０秒以上であることが好ましく、過大な粒成長を防ぐためには５０秒以下であることが好ましい。 Annealing Step If the annealing temperature is higher than 720 ° C., it is not preferable because troubles such as a heat buckle are likely to occur during continuous annealing. When the annealing temperature is less than 650 ° C., recrystallization becomes incomplete and the material becomes non-uniform. Therefore, annealing temperature shall be 650 degreeC or more and 720 degrees C or less. The soaking time in the annealing step is not particularly limited, but it is preferably 10 seconds or more in order to reliably obtain a recrystallized structure, and 50 seconds or less in order to prevent excessive grain growth. .
　二次冷間圧延（ＤＲ圧延）工程
　焼鈍後の鋼板は、二次冷間圧延により高強度化される。二次冷間圧延の圧延率が２５％未満であると、王冠の耐圧性を確保するのに十分な強度が得られない。また、二次冷間圧延の圧延率が４０％を超えると、圧延面内における圧延方向から４５°の方向の降伏強度と、圧延方向の降伏強度と圧延面内における圧延方向から９０°の方向の降伏強度の平均値の差が正に大きくなり、成形性を損なう。よって、二次冷間圧延の圧延率は２５％以上４０％とする。 Secondary cold rolling (DR rolling) step The steel sheet after annealing is strengthened by secondary cold rolling. If the rolling ratio of secondary cold rolling is less than 25%, sufficient strength cannot be obtained to ensure the pressure resistance of the crown. Also, when the rolling ratio of secondary cold rolling exceeds 40%, the yield strength in the direction of 45 ° from the rolling direction in the rolling surface, the yield strength in the rolling direction, and the direction of 90 ° from the rolling direction in the rolling surface The difference in the average value of the yield strengths of the steels becomes positively large and the formability is impaired. Therefore, the rolling rate of secondary cold rolling is set to 25% or more and 40%.
　以上により、本発明の高強度鋼板が得られる。ここで得られた鋼板にめっきや化成処理などの表面処理をしても発明の効果が失われることは無い。 Thus, the high-strength steel plate of the present invention is obtained. Even if the steel sheet obtained here is subjected to surface treatment such as plating or chemical conversion, the effects of the invention are not lost.
　表１に示す成分組成を有し、残部がＦｅ及び不可避的不純物からなる鋼を転炉で溶製し、連続鋳造することにより鋼スラブを得た。得られた鋼スラブを１２５０℃に加熱した後、圧延開始温度１１５０℃、仕上圧延温度８６０℃で熱間圧延し、表２に示す巻取り温度で巻取った。次いで、酸洗にてスケールを除去した後、表２に示す一次冷間圧延率で一次冷間圧延し、連続焼鈍炉にて表２に示す焼鈍温度で焼鈍し、表２に示す二次冷間圧延率で二次冷間圧延（ＤＲ圧延）を行い、板厚０．１５～０．１８ｍｍの鋼板（水準１～９）を得た。得られた鋼板の両面に片面あたり１００ｍｇ／ｍ２のＣｒめっきを施し、ティンフリースチールを得た。 A steel slab was obtained by melting a steel having the composition shown in Table 1 with the balance being Fe and inevitable impurities in a converter and continuously casting the steel. After the obtained steel slab was heated to 1250 ° C., it was hot-rolled at a rolling start temperature of 1150 ° C. and a finish rolling temperature of 860 ° C., and wound at the winding temperature shown in Table 2. Next, after removing the scale by pickling, primary cold rolling is performed at the primary cold rolling rate shown in Table 2, annealing is performed at the annealing temperature shown in Table 2 in a continuous annealing furnace, and secondary cooling shown in Table 2 is performed. Secondary cold rolling (DR rolling) was performed at a hot rolling rate to obtain steel plates (levels 1 to 9) having a thickness of 0.15 to 0.18 mm. 100 mg / m 2 Cr plating was applied to both sides of the obtained steel plate to obtain tin-free steel.
　以上により得られた鋼板に対して、以下の方法で特性評価を行った。 The characteristics of the steel sheet obtained as described above were evaluated by the following method.
　降伏強度
　２１０℃、１５分の塗装焼付け相当の熱処理を行った後、引張試験を行った。引張試験は、ＪＩＳ５号サイズの引張試験片を用いて、「ＪＩＳ　Ｚ　２２４１」に従って行い、圧延方向の降伏強度、圧延面内における圧延方向から４５°の方向の降伏強度、圧延面内における圧延方向から９０°の方向の降伏強度を測定した。 Yield strength After performing a heat treatment equivalent to baking at 210 ° C. for 15 minutes, a tensile test was conducted. The tensile test is performed according to “JIS Z 2241” using a JIS No. 5 size tensile test piece, the yield strength in the rolling direction, the yield strength in the direction of 45 ° from the rolling direction in the rolling surface, and the rolling direction in the rolling surface. The yield strength in the direction of 90 ° was measured.
　王冠成形性
　得られた鋼板を用いて王冠を成形し、王冠成形性を評価した。直径３７ｍｍの円形ブランクを使用し、プレス加工により「ＪＩＳ　Ｓ　９０１７」（廃止規格）に記載の３種王冠の寸法（外径３２．１ｍｍ、高さ６．５ｍｍ、襞の数２１）に成形した。評価は目視で行い、襞の大きさが全て揃っている場合を◎、襞の大きさがほぼ揃っている場合を○、襞の大きさが不揃いな場合を×と評価した。なお、上記は目視判定では、襞の幅（広がり）の最大値が最小値の１．５倍以上の場合を不揃いと判断した。 Crown formability A crown was formed using the obtained steel sheet, and the crown formability was evaluated. Using 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 evaluation was performed visually, and the case where all the sizes of the wrinkles were aligned was evaluated as ◎, the case where the sizes of the wrinkles were almost aligned was evaluated as ○, and the case where the sizes of the wrinkles were not aligned was evaluated as ×. In addition, in the above visual determination, it was determined that the case where the maximum value of the width (spread) of the wrinkles was 1.5 times the minimum value was not uniform.
　成形した王冠を用いての耐圧試験
　上記と同様の方法にて王冠を成形した。次いで、王冠の内側に塩化ビニル製ライナーを成形し、市販ビール瓶に打栓してＧｌａｓｓｌｉｎｅ　Ｃｏｒｐｏｒａｔｉｏｎ製Ｓｅｃｕｒｅ　Ｓｅａｌ　Ｔｅｓｔｅｒを用いて王冠が外れる内圧を測定した。
従来の王冠と同等以上の耐圧強度を示した場合を○、従来の王冠の耐圧強度に至らなかった場合を×と評価した。 Pressure resistance test using molded crown A crown was molded in the same manner as described above. Next, a vinyl chloride liner was molded inside the crown, plugged into a commercial beer bottle, and the internal pressure at which the crown was released was measured using a Secure Seal Tester manufactured by Glassline Corporation.
The case where the pressure strength equal to or higher than that of the conventional crown was shown was evaluated as ◯, and the case where the pressure strength of the conventional crown was not reached was evaluated as x.
　以上により得られた結果を表３に示す。 Table 3 shows the results obtained as described above.
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000002
Figure JPOXMLDOC01-appb-T000002
Figure JPOXMLDOC01-appb-T000003
Figure JPOXMLDOC01-appb-T000003
　表３より、本発明例である水準１～６の鋼板は、圧延方向の降伏強度が５５０ＭＰａであり、かつ圧延面内における圧延方向から４５°の方向の降伏強度が、圧延方向の降伏強度と圧延面内における圧延方向から９０°の方向の降伏強度の平均値以下であり、王冠成形性および耐圧強度のいずれも良好である。 From Table 3, the steel sheets of levels 1 to 6 which are examples of the present invention have a yield strength in the rolling direction of 550 MPa, and the yield strength in the direction of 45 ° from the rolling direction in the rolling surface is the yield strength in the rolling direction. It is below the average value of the yield strength in the direction of 90 ° from the rolling direction in the rolling surface, and both the crown formability and the pressure strength are good.
　一方、比較例である水準７の鋼板はＣの含有量が少なすぎるため、圧延方向の降伏強度が５５０ＭＰａ未満となり、耐圧強度が不足している。比較例である水準８の鋼板は焼鈍温度が低すぎるため、圧延方向から４５°の方向の降伏強度が圧延方向の降伏強度と圧延面内における圧延方向から９０°の方向の降伏強度の平均値を超えており、王冠成形性が劣っている。王冠の形状が不良であるため密封性が不足し、耐圧強度も小さくなっている。比較例である水準９の鋼板は二次冷間圧延率が小さすぎるため、圧延方向の降伏強度が５５０ＭＰａ未満となり、王冠成形性が劣り、耐圧強度が不足している。 On the other hand, the steel sheet of level 7 as a comparative example has too little C content, so the yield strength in the rolling direction is less than 550 MPa, and the pressure strength is insufficient. Since the steel plate of level 8 as a comparative example has an annealing temperature too low, the yield strength in the direction of 45 ° from the rolling direction is the average value of the yield strength in the rolling direction and the yield strength in the direction of 90 ° from the rolling direction in the rolling plane. The crown formability is inferior. Since the crown has a poor shape, the sealing performance is insufficient, and the pressure resistance is low. Since the steel plate of level 9 as a comparative example has a secondary cold rolling rate that is too small, the yield strength in the rolling direction is less than 550 MPa, the crown formability is inferior, and the pressure strength is insufficient.

Claims (4)

  1. 　質量％で、Ｃ：０．０１０％以上０．０２５％以下、Ｓｉ：０．１０％以下、Ｍｎ：０．０５％以上０．５０％以下、Ｐ：０．０５０％以下、Ｓ：０．００５％以上０．０５０％以下、Ａｌ：０．０２０％以上０．０７０％以下、Ｎ：０．００４０％未満を含有し、残部はＦｅおよび不可避的不純物からなる成分組成を有し、
    ２１０℃、１５分の熱処理後の降伏強度について、
    圧延方向の降伏強度が５５０ＭＰａ以上であり、
    圧延面内における圧延方向から４５°の方向の降伏強度が、圧延方向の降伏強度と圧延面内における圧延方向から９０°の方向の降伏強度の平均値以下である王冠用鋼板。     In mass%, C: 0.010% or more and 0.025% or less, Si: 0.10% or less, Mn: 0.05% or more and 0.50% or less, P: 0.050% or less, S: 0.00. 005% or more and 0.050% or less, Al: 0.020% or more and 0.070% or less, N: containing less than 0.0040%, the balance having a component composition consisting of Fe and inevitable impurities,
    About yield strength after heat treatment at 210 ° C for 15 minutes,
    The yield strength in the rolling direction is 550 MPa or more,
    A steel plate for a crown whose yield strength in the direction of 45 ° from the rolling direction in the rolling surface is equal to or less than the average value of the yield strength in the rolling direction and the yield strength in the direction of 90 ° from the rolling direction in the rolling surface.
  2. 　請求項１に記載の王冠用鋼板の製造方法であって、
    スラブを、熱間圧延し、巻取り温度５３０℃以上５９０℃以下で巻取る熱間圧延工程と、
    前記熱間圧延工程後、冷間圧延する一次冷間圧延工程と、
    前記一次冷間圧延工程後、焼鈍温度６５０℃以上７２０℃以下で焼鈍する焼鈍工程と、
    前記焼鈍工程後、圧延率２５％以上４０％以下で二次冷間圧延を行う二次冷間圧延工程と、を有する王冠用鋼板の製造方法。     It is a manufacturing method of the steel plate for crowns according to claim 1,
    A hot rolling step in which the slab is hot-rolled and wound at a winding temperature of 530 ° C. or higher and 590 ° C. or lower;
    After the hot rolling step, a primary cold rolling step for cold rolling,
    After the primary cold rolling step, an annealing step of annealing at an annealing temperature of 650 ° C. or higher and 720 ° C. or lower;
    A secondary cold rolling step of performing secondary cold rolling at a rolling rate of 25% to 40% after the annealing step.
  3. 　請求項１に記載の王冠用鋼板からなる王冠。 A crown made of the steel plate for a crown according to claim 1.
  4. 　質量％で、Ｃ：０．０１０％以上０．０２５％以下、Ｓｉ：０．１０％以下、Ｍｎ：０．０５％以上０．５０％以下、Ｐ：０．０５０％以下、Ｓ：０．００５％以上０．０５０％以下、Ａｌ：０．０２０％以上０．０７０％以下、Ｎ：０．００４０％未満を含有し、残部はＦｅおよび不可避的不純物からなる成分組成を有するスラブを、熱間圧延し、巻取り温度５３０℃以上５９０℃以下で巻取る熱間圧延工程と、
    前記熱間圧延工程後、冷間圧延する一次冷間圧延工程と、
    前記一次冷間圧延工程後、焼鈍温度６５０℃以上７２０℃以下で焼鈍する焼鈍工程と、
    前記焼鈍工程後、圧延率２５％以上４０％以下で二次冷間圧延を行う二次冷間圧延工程と、を有する、
    ２１０℃、１５分の熱処理後の降伏強度について、
    圧延方向の降伏強度が５５０ＭＰａ以上であり、
    圧延面内における圧延方向から４５°の方向の降伏強度が、圧延方向の降伏強度と圧延面内における圧延方向から９０°の方向の降伏強度の平均値以下である王冠用鋼板の製造方法。     In mass%, C: 0.010% or more and 0.025% or less, Si: 0.10% or less, Mn: 0.05% or more and 0.50% or less, P: 0.050% or less, S: 0.00. 005% or more and 0.050% or less, Al: 0.020% or more and 0.070% or less, N: containing less than 0.0040%, the balance being heat-treated slab having a composition composed of Fe and inevitable impurities A hot rolling process in which the steel sheet is rolled at a winding temperature of 530 ° C. or higher and 590 ° C. or lower;
    After the hot rolling step, a primary cold rolling step for cold rolling,
    After the primary cold rolling step, an annealing step of annealing at an annealing temperature of 650 ° C. or higher and 720 ° C. or lower;
    A secondary cold rolling step of performing secondary cold rolling at a rolling rate of 25% or more and 40% or less after the annealing step,
    About yield strength after heat treatment at 210 ° C for 15 minutes,
    The yield strength in the rolling direction is 550 MPa or more,
    A method for producing a crown steel plate, wherein the yield strength in the direction of 45 ° from the rolling direction in the rolling surface is equal to or less than the average value of the yield strength in the rolling direction and the yield strength in the direction of 90 ° from the rolling direction in the rolling surface.
PCT/JP2015/005782 2014-11-28 2015-11-19 Steel sheet for crown cap, manufacturing method therefor, and crown cap WO2016084353A1 (en)

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CN201580062055.8A CN107109559B (en) 2014-11-28 2015-11-19 Bottle cap steel plate and its manufacturing method and bottle cap
NZ730832A NZ730832A (en) 2014-11-28 2015-11-19 Steel sheet for crown cap, manufacturing method therefor, and crown cap
CA2963622A CA2963622C (en) 2014-11-28 2015-11-19 Steel sheet for crown cap, manufacturing method therefor, and crown cap
BR112017010201-3A BR112017010201B1 (en) 2014-11-28 2015-11-19 STEEL SHEET FOR CROWN TYPE COVER, MANUFACTURING METHOD AND CROWN TYPE COVER
MX2017006871A MX2017006871A (en) 2014-11-28 2015-11-19 Steel sheet for crown cap, manufacturing method therefor, and crown cap.
KR1020177013154A KR101975129B1 (en) 2014-11-28 2015-11-19 Steel sheet for crown cap, manufacturing method therefor, and crown cap
JP2016515154A JP5988012B1 (en) 2014-11-28 2015-11-19 Crown steel plate, method for producing the same, and crown
US15/527,167 US20170335438A1 (en) 2014-11-28 2015-11-19 Steel sheet for crown cap, manufacturing method therefor, and crown cap
AU2015351836A AU2015351836B2 (en) 2014-11-28 2015-11-19 Steel sheet for crown cap, manufacturing method therefor, and crown cap
PH12017500676A PH12017500676A1 (en) 2014-11-28 2017-04-10 Steel sheet for crown cap, manufacturing method therefor, and crown cap
CONC2017/0004922A CO2017004922A2 (en) 2014-11-28 2017-05-17 Steel blade for crown cap, manufacturing method, and crown cap

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