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
  • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D6/00—Heat treatment of ferrous alloys
  • C21D6/005—Heat treatment of ferrous alloys containing Mn
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
  • C21D8/0268—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment between cold rolling steps
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • 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
  • C21D8/0468—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment between cold rolling steps
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • 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
  • 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

Definitions

• the present invention relates to a steel sheet for crown cap used as a material of crown caps that serve as caps for glass bottles, and to a method for producing the steel sheet for crown cap.
• Narrow-mouthed glass bottles have a metal cap called a crown cap.
• a crown cap is produced by press-forming using a thin steel sheet as a material.
• Such a crown cap includes a disk-shaped part for closing the mouth of a bottle and a pleated part in the periphery of the disk-shaped part. The pleated part is crimped onto the mouth of the bottle to seal the bottle.
• the properties of thin steel sheets required for use as materials of crown caps include strength and formability.
• the bottles to be capped with crown caps are typically filled with, for example, beer or carbonated drinks, which increase the internal pressure of the bottles after the bottles have been filled.
• Such a crown cap needs to be strong enough to resist an elevated internal pressure resulting from changes in temperature and impacts caused during transportation or the like so as to prevent deformation of the crown cap and subsequent breakage of the seal of the bottle.
• the shapes of the pleats may be uneven, which may cause inadequate sealing performance even after the steel sheet has been crimped onto the mouth of a bottle.
• SR (single reduced) steel sheets are mainly used as thin steel sheets that serve as materials of crown caps.
• Such a SR steel sheet is produced by reducing a steel sheet in gauge by cold rolling, followed by annealing and temper rolling.
• a crown cap material commonly used in the related art has a thickness of 0.22 to 0.24 mm and is made of mild steel used for, for example, food cans and beverage cans.
• crown cap steel sheets as well as can steel sheets have needed to be reduced in gauge for the purpose of cost reduction.
• the thickness of crown cap steel sheets that serve as materials of crown caps is less than 0.20 mm
• sealing performance is not maintained with SR steel sheets known in the art because of their low strength even though the formability is similar.
• the use of a DR (double reduced) steel sheet produced by, after annealing, performing second cold-rolling to ensure strength is conceived easily.
• the use of a DR steel sheet made of low-carbon steel as a crown cap may cause a failure in sealing the bottle because of poor formability.
• Patent Literature 1 discloses an ultra-thin soft steel sheet for containers that achieves high can strength and good can formability.
• the steel sheet for containers includes, in terms of % by mass, N: 0.0040% to 0.0300% and Al: 0.005% to 0.080% and has 0.2% proof stress: 430 MPa or less, total elongation: 15% to 40%, and internal friction Q -1 : 0.0010 or more.
• Patent Literature 2 discloses a highly processable high-strength steel sheet for cans.
• the steel sheet for cans includes C: 0.001% to 0.080%, Si: 0.003% to 0.100%, Mn: 0.10% to 0.80%, P: 0.001% to 0.100%, S: 0.001% to 0.020%, Al: 0.005% to 0.100%, N: 0.0050% to 0.0150%, and B: 0.0002% to 0.0050%.
• the steel sheet for cans includes, in terms of area ratio, 0.01% to 1.00% of crystal grains having an elongation rate of 5.0 or larger.
• Patent Literature 1 and Patent Literature 2 are intended to produce cans which are containers and not to produce crown caps. As described below, the steel sheets described in these patent documents are not suitable for forming crown caps.
• Patent Literature 1 The steel sheet described in Patent Literature 1 is flexible. Thus, the anisotropy of the steel sheet increases as the second cold rolling reduction is increased in order to obtain desired strength, which impairs formability.
• an object of the present invention is to provide a steel sheet for crown that, even when reduced in gauge, has sufficient strength and formability suitable for forming crown caps, and to provide a method for forming the steel sheet for crown cap.
• the inventors of the present invention have diligently carried out studies to solve the aforementioned problems. As a result, it is found that the aforementioned problems can be solved by optimizing the components and controlling the yield strength in the rolling direction and the average Lankford value in particular ranges, completing the present invention. More specifically, the present invention provides the following.
• a steel sheet for crown cap has a composition including, in terms of % by mass, C: 0.002% or more and 0.010% or less, Si: 0.05% or less, Mn: 0.05% or more and 0.30% or less, P: 0.030% or less, S: 0.020% or less, Al: less than 0.0100%, N: 0.0050% or less, and the balance being Fe and unavoidable impurities.
• the C content is more than 0.003% when the Al content is 0.005% or more.
• the yield strength in the rolling direction is 500 MPa or more.
• the average Lankford value is 1.3 or more.
• the absolute value of is preferably 0.40 or less.
• % expressing the amount of each component contained in the steel sheet for crown cap of the present invention denotes “% by mass”.
• the C content is more than 0.010%, the average Lankford value after second cold-rolling is low, which impairs formability as described below and makes the steel sheet unsuitable for forming crown caps.
• the C content is more than 0.010%, the formed crown cap has uneven pleats, that is, a shape defect.
• the C content is set to 0.002% or more and 0.010% or less.
• the C content is preferably 0.002% or more and 0.006% or less, and more preferably 0.003% or more and 0.005% or less.
• a Si content of more than 0.05% is undesirable because Si affects formability because of the same reason as for C. Therefore, the Si content is set to 0.05% or less.
• the Si content is more preferably 0.03% or less.
• the Si content is still more preferably 0.01% or less.
• Mn 0.05% or more and 0.30% or less
• the Mn content is set to 0.05% or more and 0.30% or less.
• the Mn content is more preferably 0.10% or more and 0.30% or less.
• the Mn content is still more preferably 0.15% or more and 0.25% or less.
• a P content of more than 0.030% results in steel being hard or low corrosion resistance. Therefore, the upper limit of the P content is set to 0.030%.
• the upper limit of the P content is more preferably 0.020%.
• the upper limit of the S content is set to 0.020%.
• the upper limit of the S content is more preferably 0.011%.
• the S content is still more preferably 0.007% or less.
• Aluminum is an element to be added as a deoxidizer.
• Aluminum has an effect of reducing the amount of oxygen (0) in molten steel and thus suppressing generation of solidification defects in a steel ingot.
• the Al content is preferably 0.0005% or more.
• a large amount of Al results in reduced formability.
• the Al content is set to less than 0.0100%.
• the Al content is 0.003% or less, an improvement in the solid-solution strengthening ability attributed to C and N is achieved, which eliminates a need to increase the rolling reduction in the second cold-rolling. Specifically, even when a steel sheet for crown cap having a thickness of less than 0.20 mm is produced, desired properties can be achieved by setting the rolling reduction in the second cold-rolling to 10% to 40%. Therefore, the Al content is preferably set to 0.003% or less. The Al content is more preferably 0.002% or less. When the strength is improved by setting the Al content to 0.003% or less as described above, degradation of formability due to C can be avoided by setting the C content to 0.002% to 0.006%.
• the N content is set to 0.0050% or less.
• the N content is preferably less than 0.0040%.
• the C content is more than 0.003% when the Al content is 0.005% or more.
• the unavoidable impurities include components that are unavoidably mixed in the production process and components that are unavoidably added in order to impart desired properties unless the advantageous effects of the present invention are impaired.
• Examples of the unavoidable impurities include at least one of V, B, Ca, Zn, Co, and As in a total amount of 0.02% or less, Cu: 0.10% or less, Ni: 0.10% or less, Cr: 0.09% or less, and 0: 0.0150% or less.
• the steel sheet for crown cap needs to have sufficient strength to avoid detachment of a crown cap from the bottle against the internal pressure of the bottle.
• a typical steel sheet for crown cap has a thickness of about 0.22 to 0.24 mm. If the steel sheet for crown cap is reduced in gauge below this range, the strength of the steel sheet for crown cap needs to be further increased.
• the yield strength of the steel sheet for crown cap in the rolling direction is less than 500 MPa, it is impossible to impart sufficient strength to such a crown cap that has been reduced in gauge, which results in low pressure resistance. Therefore, the yield strength in the rolling direction is set to 500 MPa or more.
• the yield strength is preferably set to 550 MPa or more.
• the yield strength in the rolling direction is more than 650 MPa, it may be difficult to control the press conditions in forming crown caps.
• the yield strength in the rolling direction is thus preferably set to 650 MPa or less.
• the yield strength can be determined by Metallic materials--tensile testing-method described in "JIS Z 2241".
• the steel sheet for crown cap is punched into a circular blank, which is then pressed to form a crown cap.
• the shape of the crown cap after forming is evaluated mainly based on the evenness of the shapes of the pleats. If the shapes of the pleats are uneven, the sealing performance after capping is impaired, which may cause the content of the bottle to be leaked.
• the formability of the steel sheet for crown cap is associated with the composition and the yield strength and more closely associated with the average Lankford value. Specifically, when the average Lankford value is less than 1.3, the shapes of the pleats after forming are uneven. Consequently, the average Lankford value is set to 1.3 or more.
• the average Lankford value is preferably 1.4 or more. A larger average Lankford value is more preferred.
• the average Lankford value can be evaluated by determining the r values by the method described in the attached document JA in "JIS Z 2254".
• the average Lankford value is obtained by determining r L : the r value in the direction parallel to the rolling direction, r D : the r value in the direction at 45° with respect to the rolling direction, and r C : the r value in the direction at 90° with respect to the rolling direction by the method described above, and performing calculation in accordance with (r L + 2 ⁇ r D + r C /4 .
• the absolute value of is preferably 0.40 or less.
• the steel sheet for crown cap is punched into a circular blank, which is then pressed to form a crown cap.
• the shape of the crown cap after forming is evaluated mainly based on the evenness of the shapes of the pleats. If the shapes of the pleats are uneven, the sealing performance after capping is impaired, which may cause the content of the bottle to be leaked.
• the formability of the steel sheet for crown cap is associated with the composition and the yield strength and also closely associated with the absolute value of (Lankford value (r value) for in-plane anisotropy). Specifically, when the absolute value of is more than 0.40, the shapes of the pleats after forming are uneven.
• the absolute value of ⁇ r is set to 0.40 or less. A smaller absolute value of is more preferred.
• the absolute value of is preferably 0.20 or less.
• the absolute value of is obtained by determining r L : the r value in the direction parallel to the rolling direction, r D : the r value in the direction at 45° with respect to the rolling direction, and r C : the r value in the direction at 90° with respect to the rolling direction by the method described above, and performing calculation in accordance with (r L - 2 ⁇ r D + r C )/2.
• Thickness less than 0.20 mm
• the thickness of the steel sheet for crown cap of the present invention is not limited, but the steel sheet for crown cap of the present invention has both good formability and high strength even if it is thin.
• the term “thin” means that the thickness is less than 0.20 mm, and more specifically 0.13 to 0.19 mm.
• the steel sheet for crown cap of the present invention can be produced by a DR method including a hot-rolling step, a coiling step, a pickling step, a first cold-rolling step, an annealing step, and a second cold-rolling step. Each step will be described below.
• the hot-rolling step is a step of rough-rolling a slab having the composition described above and finish-rolling the rough-rolled slab.
• the slab is produced, for example, by controlling the molten steel so as to have the above-mentioned chemical components (composition) by a publicly known method using a converter or the like, followed by continuous casting. Since the composition of the slab is equivalent to the composition of the steel sheet for crown cap, the composition of the steel sheet for crown cap is controlled when the slab is produced.
• the rough-rolling conditions are not limited, but the slab is preferably heated to 1200°C or higher in rough rolling.
• the upper limit of the heating temperature is not limited, but application of significantly high heating temperature causes excess scale formation, which results in defects on the product surface. Therefore, the heating temperature is preferably set to 1300°C or lower.
• the finish-rolling temperature is set to 850°C or higher from the viewpoint of the stability of the rolling load.
• the finish-rolling temperature is preferably 880°C or higher, and more preferably 900°C or higher. Since it difficult to produce a thin steel sheet at a finish-rolling temperature higher than needed, the finish-rolling temperature is preferably set to 960°C or lower.
• the coiling step is a step of coiling the hot-rolled sheet obtained in the hot-rolling step.
• the coiling temperature in the hot-rolling step is set to 750°C or lower.
• the coiling temperature is preferably 740°C or lower and more preferably 700°C or lower.
• the coiling temperature is still more preferably 650°C or lower. In order to lower the coiling temperature to less than 450°C and operate without impairing efficiency, the finish-rolling temperature needs to be lowered accordingly.
• the coiling temperature is set to 450°C or higher.
• the coiling temperature is more preferably 500°C or higher.
• the coiling temperature is still more preferably 550°C or higher.
• the pickling step is a step of pickling the hot-rolled sheet after the coiling step.
• the pickling step involves removing surface scale.
• the pickling conditions are not limited as long as surface scale can be removed.
• the first cold-rolling step is a step of cold-rolling the hot-rolled sheet after the pickling step.
• the rolling reduction in the first cold-rolling step is not limited, but the rolling reduction is preferably set to 85% to 94% in order to produce an ultra-thin material.
• the annealing step is a step of annealing the cold-rolled sheet obtained in the first cold-rolling step.
• the annealing temperature is higher than 790°C, troubles, such heat buckling, that occur during the passage of the sheet tend to occur in continuous annealing.
• the annealing temperature is lower than 650°C, the recrystallization is incomplete, which leads to an uneven material. Therefore, the annealing temperature is set to 650°C to 790°C.
• the second cold-rolling step is a step of cold-rolling the annealed sheet obtained in the annealing step.
• This second cold-rolling imparts desired strength.
• the condition of the rolling reduction to be selected differs with the Al content. Specifically, the rolling reduction is 10% or more and 50% or less when the Al content is 0.003% or less. The rolling reduction is 20% or more and 50% or less when the Al content is more than 0.003%. If the rolling reduction is less than 10% when the Al content is 0.003% or less and if the rolling reduction is less than 20% when the Al content is more than 0.003%, the strength sufficient to ensure the pressure resistance of the crown cap is not obtained.
• the rolling reduction in the second cold-rolling is set in the above-mentioned range in accordance with the Al content.
• the preferred upper limit of the rolling reduction is 40% at any Al content.
• one of the characteristics is that the rolling reduction can be low when the Al content is 0.003% or less.
• the rolling reduction is preferably 40% or less as described below when the Al content is 0.003% or less.
• a process such as a plating process is performed by an ordinary method to produce a steel sheet for crown cap.
• the steel sheet has both high strength and good crown cap formability, which enables gauge reduction of crown caps.
• a steel having the composition described in Table 1 with the balance being Fe and unavoidable impurities was first smelted in an actual converter and continuously cast to obtain a steel slab.
• the steel slab thus obtained was reheated to 1250°C and then hot-rolled in the conditions at a rolling start temperature of 1150°C and at the finish-rolling temperature described in Table 2.
• the resulting sheet was coiled at the coiling temperature described in Table 2 and then pickled after coiling.
• the sheet was subjected to first cold-rolling at the first cold rolling reduction described in Table 2, continuously annealed at the annealing temperature described in Table 2, and subsequently subjected to second cold-rolling at the second cold rolling reduction described in Table 2.
• the obtained steel sheet was continuously subjected to ordinary chromium plating to produce a tin-free steel.
• the steel sheet thus obtained was subjected to a heat treatment corresponding to coating baking at 210°C for 15 minutes.
• the steel sheet was then subjected to tensile testing and measured for its average Lankford value and ⁇ r value.
• Tensile testing was performed by using a JIS No. 5 tensile test piece in accordance with JIS Z 2241 to determine the yield strength in the rolling direction.
• the average Lankford value was determined by using the natural-vibration method described in the attached document JA in "JIS Z 2254.”
• r L was determined by preforming tensile testing in the rolling direction
• r D was determined by performing tensile testing in the direction at 45° with respect to the rolling direction
• r C was determined by performing tensile testing in the direction at 90° with respect to the rolling direction.
• the absolute value of ⁇ r was obtained by calculating (r L -2 x r D + r c )/2 from the measured results.
• the obtained steel sheet was used to form a crown cap and evaluated for crown cap formability.
• a circular blank having a diameter of 37 mm was pressed in the size of the third type of crown cap (outer diameter: 32.1 mm, height: 6.5 mm, number of pleats: 21) described in "JIS S 9017" (withdrawn standard).
• the crown cap formability was evaluated by visual observation and rated "A” for the case where the sizes of the pleats were even and "B" for the case where the sizes of the pleats were uneven.
• the steel sheets of Samples 1 to 5, 13, and 14 which are Invention Examples have a yield strength in the rolling direction of 500 MPa or more, an average Lankford value of 1.3 or more, and an absolute value of ⁇ r of 0.40 or less, which shows both good crown cap formability and high pressure resistance.
• the steel sheet of Sample 6 which is Comparative Example has a yield strength in the rolling direction of less than 500 MPa, namely, low pressure resistance because the Al content is more than 0.005% but the C content is less than 0.003%.
• the steel sheet of Sample 7 has an excessively high C content
• the steel sheet of Sample 8 has an excessively high Mn content
• the steel sheet of Sample 9 has an excessively high Al content
• the steel sheet of Sample 10 has an excessively high N content
• the coiling temperature after hot rolling was too high for the steel sheet of Sample 11. Because of these reasons, all of these steel sheets have an average Lankford value of less than 1.3, namely, poor crown cap formability.
• the second cold rolling reduction was too low, and thus the yield strength in the rolling direction is less than 500 MPa, which shows low pressure resistance.

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• 2015
  • 2015-09-28 JP JP2015189112A patent/JP5958630B2/ja active Active
  • 2015-10-08 TW TW104133241A patent/TWI565812B/zh not_active IP Right Cessation
  • 2015-10-08 BR BR112017007235A patent/BR112017007235A2/pt active Search and Examination
  • 2015-10-08 KR KR1020177009648A patent/KR102020718B1/ko active IP Right Grant
  • 2015-10-08 AU AU2015329455A patent/AU2015329455B2/en not_active Ceased
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  • 2015-10-08 MX MX2017004584A patent/MX2017004584A/es unknown
  • 2015-10-08 US US15/518,190 patent/US20170292176A1/en not_active Abandoned
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• 2017
  • 2017-02-27 PH PH12017500350A patent/PH12017500350A1/en unknown
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