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.

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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
  • 2015-11-19 MY MYPI2017701807A patent/MY177069A/en unknown
  • 2015-11-19 MX MX2017006871A patent/MX2017006871A/es unknown
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  • 2015-11-19 BR BR112017010201-3A patent/BR112017010201B1/pt not_active IP Right Cessation
  • 2015-11-25 TW TW104139167A patent/TWI601830B/zh active
• 2017
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