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
• • 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
  • 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

Definitions

• This disclosure relates to a steel sheet used as a material for a crown cap serving as a cap for a glass bottle, a method of manufacturing the same, and a crown cap.
• a cap made of metal which is referred to as a crown cap, is generally used for a narrow-mouthed glass bottle.
• crown caps are manufactured by press forming by using a thin steel sheet as a material.
• a crown cap includes a disk-shaped portion that covers the mouth of a bottle and a pleated portion disposed on the periphery thereof, and by crimping the pleated portion around the mouth of the bottle, the bottle is hermetically sealed.
• Bottles provided with a crown cap are often filled with contents that cause an internal pressure such as beer or a carbonated beverage.
• the material is required to have a strength such that, even when the internal pressure is increased because of a change in temperature or the like, the seal of the bottle is not broken by deformation of the crown cap.
• the strength of the material is sufficient, when the material has poor formability, the shape of pleats may become non-uniform, and sufficient sealing performance cannot be obtained even when the pleated portion is crimped around the mouth of a bottle.
• an SR (Single Reduced) steel sheet is mainly used as the thin steel sheet used as a material for crown caps.
• An SR steel sheet is produced by reducing the thickness of a steel sheet by cold rolling, and then annealing the steel sheet, followed by temper rolling.
• the thickness of the material for crown caps is 0.20 mm or more, it is possible to secure sufficient strength and formability by employing an SR sheet made from mild steel used for cans of food and drinks.
• Japanese Unexamined Patent Application Publication No. 2001-49383 discloses an ultrathin soft steel sheet for a container excellent in can strength and can formability, containing, in percent by weight, N: 0.0040 to 0.0300% and Al: 0.005 to 0.080%, characterized in that the 0.2% proof stress is 430 MPa or less, the total elongation is 15 to 40%, and the internal friction Q ⁇ 1 is 0.0010 or more.
• Japanese Unexamined Patent Application Publication No. 2013-28842 discloses a high-strength high-workability steel sheet for a can, containing, in percent 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%, and B: 0.0002 to 0.0050%, characterized by including, in area fraction, 0.01 to 1.00% of crystal grains whose elongation rate is 5.0 or more in a cross section in the rolling direction.
• the steel sheet described in JP '383 is soft and contains a large amount of N. Therefore, to obtain the required strength, it is necessary to increase the secondary cold rolling reduction. When the secondary cold rolling reduction is increased, anisotropy is also increased, and formability is impaired.
• the steel sheet described in JP '842 has a large N content as in the steel sheet described in JP '383. Therefore, it is difficult to achieve both strength and workability required for the material for crown caps.
• a steel sheet for a crown cap comprising:
• composition containing, in percent by mass, C: 0.010% to 0.025%, Si: 0.10% or less, Mn: 0.05% to 0.50%, P: 0.050% or less, S: 0.005% to 0.050%, Al: 0.020% to 0.070%, N: less than 0.0040%, and the balance being Fe and inevitable impurities,
• a yield strength in a direction 45° from the rolling direction in a rolling plane equal to or less than an average of the yield strength in the rolling direction and a yield strength in a direction 90° from the rolling direction in the rolling plane.
• a secondary cold rolling step of performing secondary cold rolling with a rolling reduction of 25% to 40% after the annealing step is performed.
• a method of manufacturing a steel sheet for a crown cap including:
• a yield strength in a rolling direction is 550 MPa or more
• a yield strength in a direction 45° from the rolling direction in a rolling plane is equal to or less than the average of the yield strength in the rolling direction and a yield strength in a direction 90° from the rolling direction in the rolling plane.
• our steel sheet has a specific composition, and regarding yield strength after heat treatment at 210° C. for 15 minutes, the yield strength in a rolling direction is 550 MPa or more, and the yield strength in a direction 45° from the rolling direction in a rolling plane is equal to or less than the average of the yield strength in the rolling direction and the yield strength in a direction 90° from the rolling direction in the rolling plane.
• the yield strength in a rolling direction is 550 MPa or more
• the yield strength in a direction 45° from the rolling direction in a rolling plane is equal to or less than the average of the yield strength in the rolling direction and the yield strength in a direction 90° from the rolling direction in the rolling plane.
• C is an element that contributes to achieving both strength and workability when its content is in a controlled range.
• the C content is less than 0.010%, the amount of strengthening due to solute C is small and, therefore, strength becomes insufficient.
• the C content exceeds 0.025%, the shape of pleats of a formed crown cap becomes non-uniform, resulting in shape defects. Therefore, the C content is 0.010% to 0.025%.
• the Si content is excessively large, formability is adversely affected. Accordingly, the Si content exceeding 0.10% is not desirable. Therefore, the Si content is 0.10% or less. From the viewpoint of improvement in the strength of the steel sheet, the Si content is preferably 0.02% to 0.10%.
• the Mn content falls below 0.05%, even when the S content is decreased, it becomes difficult to avoid hot brittleness, resulting in problems such as surface cracking during continuous casting.
• the Mn content exceeding 0.50% adversely affects formability, similarly to Si. Therefore, the Mn content is 0.05% to 0.50%.
• the P content exceeds 0.050%, steel is hardened, and corrosion resistance is decreased. Therefore, the P content is 0.050% or less.
• S binds to Mn to form MnS in steel and precipitates a large amount of MnS, thereby degrading the hot ductility of steel.
• S content exceeds 0.050%, this effect becomes noticeable.
• S content is 0.005% to 0.050%
• Al is an element added as a deoxidizer. Furthermore, Al forms AlN with N in steel to decrease solute N in steel. When the Al content is less than 0.020%, the effect as a deoxidizer is insufficient, resulting in solidification defects. On the other hand, when the extent of secondary cold rolling is large, a large Al content will cause degradation in formability. When the Al content exceeds 0.070%, the shape of pleats becomes non-uniform during formation of a crown cap, resulting in shape defects. Therefore, the Al content is 0.020% to 0.070%.
• the N content is 0.0040% or more, the steel sheet is hardened, and formability is degraded. Therefore, the N content is less than 0.0040%, and preferably 0.0035% or less.
• the balance other than the essential components described above includes iron and inevitable impurities.
• a steel sheet for a crown cap is required to have a strength such that the crown cap is not removed under the influence of an internal pressure of the bottle. For this reason, in existing techniques, the thickness of a steel sheet for a crown cap is 0.20 mm or more. However, there has been an increased demand for a reduction in the thickness. When the thickness is reduced to less than 0.20 mm, a larger strength than that of existing materials is required. When the yield strength in a rolling direction of a steel sheet is less than 550 MPa, it is not possible to impart a sufficient strength to a crown cap whose thickness has been reduced, and the pressure resistance becomes insufficient. Therefore, the yield strength in the rolling direction is 550 MPa or more.
• the yield strength differs depending on the direction in the rolling plane.
• the yield strength in a direction 45° from the rolling direction is more than the average of the yield strength in the rolling direction and the yield strength in a direction 90° from the rolling direction, formability is degraded. Therefore, the yield strength in a direction 45° from the rolling direction in a rolling plane is equal to or less than the average of the yield strength in the rolling direction and the yield strength in a direction 90° from the rolling direction in the rolling plane.
• the difference obtained by subtracting the yield strength in a direction 45° from the rolling direction in the rolling plane from the average of the yield strength in the rolling direction and the yield strength in a direction 90° from the rolling direction in the rolling plane is 0 MPa or more, and preferably 10 to 25 MPa.
• a crown cap is formed, often after a steel sheet has been subjected to baking finish and, therefore, it is necessary to evaluate the quality of the material after treatment corresponding to baking finish. Accordingly, the yield strength is measured after heat treatment corresponding to baking finish at 210° C. for 15 minutes, and the tensile testing method for metallic materials according to “JIS Z 2241” can be applied thereto.
• Our method of manufacturing a steel sheet for a crown cap includes a hot rolling step in which a steel slab having the composition described above is subjected to hot rolling, followed by coiling at a coiling temperature of 530° C. to 590° C.; a primary cold rolling step in which cold rolling is performed after the hot rolling step; an annealing step in which annealing is performed at an annealing temperature of 650° C. to 720° C. after the primary cold rolling step; and a secondary cold rolling step in which secondary cold rolling is performed with a rolling reduction of 25% to 40% after the annealing step.
• Molten steel is adjusted to have the chemical composition described above by a known method using a converter or the like, and is formed into a slab by a continuous casting method. Subsequently, the steel slab is subjected to rough rolling.
• the slab heating temperature is preferably 1,200° C. or higher.
• finish rolling is performed.
• the finish rolling temperature is preferably 850° C. or higher from the standpoint of stability of the rolling load.
• finish rolling temperature refers to the temperature of the sheet when it enters the last stand of a finish rolling mill. On the other hand, when the finish rolling temperature is increased more than necessary, manufacturing of a thin steel sheet may become difficult in some cases.
• the finishing temperature is preferably 850° C. to 900° C.
• the coiling temperature in the hot rolling step is lower than 530° C., to perform an operation without impairing efficiency, it is necessary to decrease the finish rolling temperature accordingly, which is inappropriate.
• the coiling temperature exceeds 590° C., the amount of AlN that precipitates after coiling becomes excessively large, leading to a decrease in the grain size after annealing and resulting in a degradation in formability. Therefore, the coiling temperature is 530° C. to 590° C., and preferably 540° C. to 580° C.
• the method of removing surface scale is not particularly limited, and various common methods such as pickling and physical removal can be used.
• Surface scale can be suitably removed by pickling.
• the picking conditions are not particularly limited, and pickling may be performed in the usual manner.
• the rolling reduction in the primary cold rolling is preferably 85% or more to manufacture an ultrathin material.
• the rolling reduction is preferably 94% or less.
• the annealing temperature is higher than 720° C.
• trouble during passing of the sheet such as heat buckling is likely to occur during continuous annealing, which is not desirable.
• the annealing temperature is lower than 650° C.
• recrystallization becomes imperfect, resulting in non-uniform quality of the material. Therefore, the annealing temperature is 650° C. to 720° C.
• the soaking period in the annealing step is not particularly limited, but is preferably 10 seconds or more to surely obtain a recrystallization structure, and is preferably 50 seconds or less to prevent excessive grain growth.
• the strength of the annealed steel sheet is increased by secondary cold rolling.
• the rolling reduction in the secondary cold rolling is less than 25%, it is not possible to obtain strength sufficient to ensure the pressure resistance of a crown cap.
• the rolling reduction in the secondary cold rolling exceeds 40%, the difference of the yield strength in a direction 45° from the rolling direction in the rolling plane from the average of the yield strength in the rolling direction and the yield strength in a direction 90° from the rolling direction in the rolling plane is positively increased, resulting in degradation in formability. Therefore, the rolling reduction in the secondary cold rolling is 25% to 40%.
• a high-strength steel sheet is obtained by the method described above. Even when the resulting steel sheet is subjected to surface treatment such as plating or chemical conversion treatment, the advantageous effects are not impaired.
• Steels having the compositions shown Table 1 and containing the balance being Fe and inevitable impurities were refined by a converter, and steel slabs were obtained by continuous casting.
• the resulting steel slabs were each heated to 1,250° C., then hot-rolled at a rolling start temperature of 1,150° C. and at a finish rolling temperature of 860° C., and coiled at the coiling temperature shown in Table 2.
• primary cold rolling was performed with the primary cold rolling reduction shown in Table 2
• annealing was performed in a continuous annealing furnace at the annealing temperature shown in Table 2
• secondary cold rolling (DR rolling) was performed with the secondary cold rolling reduction shown in Table 2 to obtain steel sheets (levels 1 to 9) with a thickness of 0.15 to 0.18 mm.
• the resulting steel sheets were Cr-plated on both surfaces with a coating weight of 100 mg/m 2 per surface and, thereby, tin-free steel sheets were obtained.
• a tensile test was carried out.
• the tensile test was performed, using a JIS No. 5 tensile test piece, in accordance with “JIS Z 2241” to measure the yield strength in the rolling direction, the yield strength in a direction 45° from the rolling direction in the rolling plane, and the yield strength in a direction 90° from the rolling direction in the rolling plane.
• a crown cap was formed, and crown cap formability was evaluated.
• a circular blank with a diameter of 37 mm was used and formed by press working into a size (outside diameter: 32.1 mm, height: 6.5 mm, number of pleats: 21) of a type 3 crown cap according to “JIS S 9017” (withdrawn standard).
• the evaluation was visually performed. When the pleats all had a uniform size, they were evaluated as being very good ( ⁇ ), when the pleats had a substantially uniform size they were evaluated as being good ( ⁇ ), and when the pleats had a non-uniform size they were evaluated as being poor ( ⁇ ). In the visual determination, when the maximum value of pleat width (breadth) was 1.5 times or more the minimum value was determined to be non-uniform.
• Crown caps were formed by the same method as that described above. A vinyl chloride liner was formed inside each of the crown caps. A commercially available beer bottle was closed with the crown cap, and the internal pressure at which the crown cap was removed was measured by using a Secure Seal Tester manufactured by Glassline Corporation.
• the yield strength in the rolling direction is 550 MPa
• the yield strength in a direction 45° from the rolling direction in the rolling plane is equal to or less than the average of the yield strength in the rolling direction and the yield strength in a direction 90° from the rolling direction in the rolling plane, and both the crown cap formability and the pressure resistance are satisfactory.
• the yield strength in the rolling direction is less than 550 MPa, and the pressure resistance is insufficient.
• the yield strength in a direction 45° from the rolling direction exceeds the average of the yield strength in the rolling direction and the yield strength in a direction 90° from the rolling direction in the rolling plane, and the crown cap formability is poor. Since the shape of the crown cap is poor, sealing performance is insufficient, and the pressure resistance is low.
• the steel sheet of level 9 which is a comparative example since the secondary cold rolling reduction is excessively small, the yield strength in the rolling direction is less than 550 MPa, the crown cap formability is poor, and the pressure resistance is insufficient.

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• Chemical & Material Sciences (AREA)
• Engineering & Computer Science (AREA)
• Mechanical Engineering (AREA)
• Materials Engineering (AREA)
• Metallurgy (AREA)
• Organic Chemistry (AREA)
• Crystallography & Structural Chemistry (AREA)
• Thermal Sciences (AREA)
• Physics & Mathematics (AREA)
• Heat Treatment Of Sheet Steel (AREA)
• Heat Treatment Of Steel (AREA)
• Closures For Containers (AREA)
• Metal Rolling (AREA)
• Heat Treatment Of Articles (AREA)

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• 2015
  • 2015-11-19 KR KR1020177013154A patent/KR101975129B1/ko active IP Right Grant
  • 2015-11-19 CN CN201580062055.8A patent/CN107109559B/zh active Active
  • 2015-11-19 AU AU2015351836A patent/AU2015351836B2/en not_active Ceased
  • 2015-11-19 JP JP2016515154A patent/JP5988012B1/ja active Active
  • 2015-11-19 CA CA2963622A patent/CA2963622C/en active Active
  • 2015-11-19 US US15/527,167 patent/US20170335438A1/en not_active Abandoned
  • 2015-11-19 WO PCT/JP2015/005782 patent/WO2016084353A1/ja active Application Filing
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  • 2015-11-19 BR BR112017010201-3A patent/BR112017010201B1/pt not_active IP Right Cessation
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• 2017
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