WO2012144213A1 - 外圧に対する缶胴部の座屈強度が高く、成形性および成形後の表面性状に優れた缶用鋼板およびその製造方法 - Google Patents
外圧に対する缶胴部の座屈強度が高く、成形性および成形後の表面性状に優れた缶用鋼板およびその製造方法 Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
Definitions
- the present invention relates to a steel plate for a can suitable for a can container material used as a container material for beverages and foods, and a method for producing the same, and in particular, the buckling strength of a can body portion with respect to external pressure is high, and formability and after molding
- the present invention relates to a steel plate for cans having excellent surface properties and a method for producing the same.
- the buckling phenomenon of the can body part is caused by the deterioration of the rigidity of the can body due to the thinning of the thickness of the can body part. Therefore, in order to improve the buckling resistance (sometimes referred to as paneling strength), a method of optimizing the size and design of the can body and increasing the rigidity of the can body can be considered.
- a crystal orientation group ( ⁇ fiber) in which the ⁇ 111> direction is parallel to the normal direction of the plate surface can increase the Young's modulus in the 0, 45, and 90 ° directions to about 230 GPa with respect to the rolling direction.
- the crystal orientation of the steel sheet does not show an orientation in a specific orientation, that is, the Young's modulus of the steel sheet with a random texture is about 205 GPa.
- Patent Document 1 a steel obtained by adding Nb or Ti to ultra-low carbon steel is used, and in the hot rolling process, the reduction ratio between Ar 3 and (Ar 3 + 150 ° C.) is set to 85% or more and non-recrystallized.
- the texture of ferrite becomes ⁇ 311 ⁇ ⁇ 011> and ⁇ 332 ⁇ ⁇ 113> orientations at the hot-rolled sheet stage, and cold rolling and recrystallization annealing are performed using these as initial orientations.
- a technique is disclosed in which the ⁇ 211 ⁇ ⁇ 110> orientation is the main orientation and the Young's modulus in the 90 ° direction with respect to the rolling direction is increased.
- Patent Document 2 by mass%, was added Nb, Mo, and B C weight 0.02 to 0.15% low carbon steel, the rolling reduction at Ar 3 ⁇ 950 ° C. With 50% or more, A method for producing a hot-rolled steel sheet, in which ⁇ 211 ⁇ ⁇ 110> is developed and the Young's modulus in the 90 ° direction with respect to the rolling direction is increased, is disclosed.
- Patent Document 3 after cold rolling and annealing, secondary cold rolling of 50% or more is performed to form a strong rolling texture, that is, ⁇ fiber, and the container has a higher Young's modulus in the 90 ° direction relative to the rolling direction.
- Steel plate manufacturing techniques are disclosed.
- Patent Document 4 a hot-rolled sheet is cold-rolled at a rolling reduction of 60% or more, a strong ⁇ fiber is formed, and the Young's modulus in the 90 ° direction with respect to the rolling direction is increased. Manufacturing techniques are disclosed.
- Patent Document 5 Ti, Nb, Zr, and B are added to ultra-low carbon steel, hot rolled at least 50% or more at a temperature below the Ar 3 transformation point, and after cold rolling, 400 ° C. or more.
- a technique for manufacturing a steel plate for containers in which the Young's modulus in the 90 ° direction is increased by annealing at a recrystallization temperature or lower is disclosed.
- Patent Document 6 performs hot rough rolling on ultra-low carbon steel under the condition that the total reduction amount is 80% or more, of which the final pass is 20% or more.
- the material to be rolled passes through one of the rolling stands in the finish rolling mill row, it is reverse transformed by the heat generated by the rolling process and finished so that the finish rolling temperature becomes Ar3-50 ° C or higher.
- a steel sheet that can efficiently and uniformly refine the structure of a hot-rolled steel sheet and a steel sheet for canning that is a final product, has good workability, and has no rough surface, and a method for producing the same.
- Patent Document 7 the hot rolling conditions such as cooling after finish rolling are appropriately controlled, the crystal grains after hot rolling are made equiaxed, fine grained uniform structure, and the effect is inherited after cold rolling and annealing.
- Patent Document 8 the pinning effect is optimized by adding Nb and controlling the amount and grain size of Nb-based precipitates based on ultra-low carbon steel, and the ferrite grain size is as fine as 6 to 10 ⁇ m. Steel sheets having excellent skin roughness resistance and manufacturing techniques thereof are disclosed.
- Japanese Patent Laid-Open No. 5-255804 Japanese Unexamined Patent Publication No. 8-311541 JP-A-6-212353 JP-A-6-248332 JP-A-6-248339 Japanese Patent Laid-Open No. 10-8142 Japanese Patent Laid-Open No. 10-81919 JP 2010-229486 A
- Patent Documents 1 to 5 only disclose methods for increasing the Young's modulus in the 90 ° direction with respect to the rolling direction.
- this method when the can body part is formed by roll form forming like a three-piece can, it is possible to improve the paneling strength by forming the direction having a high Young's modulus to be the circumferential direction of the can body part.
- the direction having a high Young's modulus is not necessarily the circumferential direction of the can body, and the effect of increasing the rigidity of the can body is not sufficiently exhibited.
- Patent Documents 6 to 8 do not disclose any technology for compensating for the deterioration of the can body rigidity accompanying the thinning of the steel sheet.
- the present invention has been made in view of such circumstances, solves the above-mentioned problems of the prior art, has a high buckling strength of the can body against external pressure, and has excellent formability and surface properties after forming, and its steel plate
- An object is to provide a manufacturing method.
- the present inventors have conducted intensive research to solve the above problems. As a result, by optimizing the chemical composition, hot rolling conditions, cold rolling conditions and annealing conditions based on ultra low carbon steel, the buckling strength of the can body against external pressure is high, and the formability and The present inventors have found that it is possible to produce a steel plate for cans having excellent surface properties, and have completed the present invention based on this finding.
- a steel plate for cans that has a high buckling strength of the can body against an external pressure and that is excellent in formability and surface properties after forming, characterized by being 10.0 ⁇ m.
- the buckling strength of the can body against external pressure is higher than the standard value (about 1.5 kgf / cm 2 ) provided by the can and beverage manufacturers, and it is excellent in DI moldability and deep drawing ironing moldability.
- a steel plate for cans having excellent surface properties after forming can be obtained. Therefore, by using the steel plate for cans of the present invention for food cans, beverage cans, etc., the rigidity of the can body is improved without incurring the surface properties after molding of the two-piece can and the reduction in yield due to the occurrence of earrings. Therefore, it is possible to achieve further resource saving and cost reduction.
- the application range of the steel plate for cans of the present invention can be expected to be applied not only to various metal cans but also to a wide range of dry battery interior cans, various home appliances / electrical parts, automotive parts and the like.
- Such a steel plate for cans is subjected to hot rolling at a reheating temperature of 1150 to 1300 ° C. and a finishing temperature of 850 to 950 ° C. on a steel slab having the above composition, and then rolled at 500 to 640 ° C. Winding at the coiling temperature, pickling, cold rolling at a reduction ratio of 87-93%, recrystallization annealing at a recrystallization temperature of 720 ° C, and temper rolling with an elongation of 0.5-5% Can be manufactured. These are the most important requirements of the present invention.
- the component composition of the steel plate for cans of this invention is demonstrated.
- C 0.0005% or more and 0.0035% or less
- the greater the amount of C dissolved in the steel the greater the yield elongation, which tends to cause age hardening and stretcher strain during processing.
- Use the continuous annealing method In such a case, it is necessary to control so as to keep the C content as low as possible in the steelmaking stage.
- the amount of residual solute carbon increases, cracks occur during stretch flange molding of the tightened portion, which is the final process of can making, and the amount of work hardening also increases, so wrinkles when necking and flange processing are performed. May occur. Therefore, the C content is 0.0035% or less.
- C is an element that affects the recrystallization texture.
- it is less than 0.0005% it is the orientation that decreases the Young's modulus in the 45 ° direction with respect to the rolling direction ⁇ 100 ⁇ ⁇ 110> orientation tends to remain, and rather the average Young's modulus is lowered. From the above, the C content is 0.0005% or more.
- Si 0.05% or less If Si is added in a large amount, the problem of deterioration of the surface treatment property and corrosion resistance of the steel sheet occurs, so 0.05% or less, preferably 0.02% or less.
- Mn 0.1% to 0.6% Mn needs to be added in an amount of 0.1% or more in order to prevent a decrease in hot ductility due to the impurity S contained in the steel.
- Mn is one of the elements that lowers the Ar 3 transformation point, and can further reduce the hot rolling finish rolling temperature. For this reason, the recrystallized grain growth of ⁇ grains can be suppressed during hot rolling, and the ⁇ grains after transformation can be refined. Further, in the present invention, in addition to the effect of refining by adding B described later, Mn is added to achieve further refining, and excellent surface properties after canning are ensured. In order to obtain the above effects, Mn is 0.1% or more.
- Mn is set to 0.6% or less.
- P 0.02% or less
- S Less than 0.02% S combines with Mn in steel to form MnS and precipitates in large quantities, thereby reducing the hot ductility of the steel. Therefore, S is less than 0.02%.
- Al 0.01% or more and less than 0.10%
- Al is an element added as a deoxidizer.
- N and AlN it has the effect of reducing the solute N in the steel.
- Al content is less than 0.01%, a sufficient deoxidizing effect or solute N reducing effect cannot be obtained. Therefore, Al is made 0.01% or more.
- it is 0.10% or more not only is the above effect saturated, but also inclusions such as alumina increase, such being undesirable. Therefore, the Al content is in the range of 0.01 to less than 0.10%.
- N 0.0030% or less N is an unavoidable impurity. As the amount of N increases, the amount of B to be fixed must be increased. Since a large increase in the amount of B added leads to an increase in cost, N should be 0.0030% or less.
- B 0.0010% or more and B / N ⁇ 3.0 B has the effect of preventing age hardening by combining with N dissolved in the steel and precipitating as BN. Moreover, when added more than the amount necessary for precipitation as BN, it is recognized that it has the effect of making the crystal grains of the hot-rolled sheet and the annealed sheet fine. This is considered to be because B added excessively segregates as a solid solution B at the grain boundary and suppresses the grain growth of the crystal grain. In order to exhibit such an effect of refining crystal grains, it is necessary to deposit B as solid solution B after precipitating BN.
- B is set to 0.0010% or more.
- the increase in solid solution B excessively raises the recrystallization completion temperature in the continuous annealing process, and the risk of occurrence of in-furnace breakage and buckling increases. For this reason, B / N ⁇ 3.0.
- B / N (B (mass%)) / 10.81) / (N (mass%) / 14.01).
- the balance is Fe and inevitable impurities.
- Texture Average accumulation strength f in the (111) [1-10] to (111) [-1-12] orientation is 7.0 or more (111) [1-10] to (111) [-1-12 ]
- the Young's modulus in the 0, 45, 90 ° direction relative to the rolling direction can be increased isotropically. Therefore, the (111) It is necessary to set the average accumulated intensity f in the [1-10] to (111) [-1-12] directions to 7.0 or more.
- E AVE 215GPa, E 0 ⁇ 210GPa, E 45 ⁇ 210GPa, E 90 ⁇ 210GPa
- E AVE (E 0 + 2E 45 + E 90 ) / 4
- E 0 , E 45 , and E 90 represent Young's moduli in the 0 , 45 , and 90 ° directions with respect to the rolling direction, respectively.
- E AVE should be 215 GPa or more. By setting it to 215 GPa or more, the paneling strength is remarkably improved, and deformation of the can body due to increase or decrease in pressure outside the can in the heat sterilization treatment of the contents accompanying the thinning of the steel plate can be prevented.
- the anisotropy of the Young's modulus of the steel plate becomes a problem. That is, among E 0 , E 45 , and E 90 , when the Young's modulus in only one direction or two directions is high and the Young's modulus in other directions is low, even if E AVE ⁇ 215 GPa is satisfied, The effect of increasing the rigidity is not sufficiently exhibited. In order to increase the rigidity of the can body, E 0 , E 45 , and E 90 need to be 210 GPa or more, respectively.
- the base steel sheet may be exposed due to film rupture caused by peeling of the film from the steel sheet or stress concentration on the film, and the corrosion resistance may deteriorate. This occurs due to the rough surface of the steel sheet after DI forming or drawing and ironing, and the degree of this rough surface is proportional to the size of the ferrite crystal grain size. Therefore, the ferrite average crystal grain size in the rolling direction cross section of the steel sheet used for the base is 10.0 ⁇ m or less, preferably 9.0 ⁇ m or less. On the other hand, if the crystal grain size is excessively fine, the strength of the steel sheet is greatly increased due to the refinement. For this reason, the average grain size of ferrite in the cross section in the rolling direction is 6.0 ⁇ m or more.
- ⁇ r represented by the following formula is used as an index of earrings.
- ⁇ r (r 0 ⁇ 2r 45 + r 90 ) / 2
- r 0 , r 45 , and r 90 represent Rankford (hereinafter sometimes referred to as r value) in directions of 0 , 45 , and 90 ° in the rolling direction, respectively.
- r value Rankford
- the amount of earrings is large, so the trim margin increases and the yield decreases.
- ⁇ r needs to be in the range of ⁇ 0.4 to 0.4.
- (DELTA) r can be made into a predetermined
- the steel plate for cans according to the present invention is obtained by subjecting a steel slab having the above composition to hot rolling at a reheating temperature of 1150 to 1300 ° C and a finishing temperature of 850 to 950 ° C, and then at a winding temperature of 500 to 640 ° C.
- Slab reheating temperature 1150-1300 ° C If the slab reheating temperature before hot rolling is too high, problems such as product surface defects and increased energy costs occur. On the other hand, if it is too low, it will be difficult to ensure the final finish rolling temperature. Therefore, the slab reheating temperature is 1150-1300 ° C.
- Final finishing rolling temperature 850-950 ° C
- winding temperature 500-640 ° C
- the final finish rolling temperature is 850 to 950 ° C and the coiling temperature is 500 to 640 ° C from the viewpoint of grain refinement and uniformity of precipitate distribution in the hot-rolled steel sheet.
- the final finish rolling temperature is higher than 950 ° C.
- ⁇ grain growth after rolling occurs more violently, and the accompanying coarse ⁇ grains cause coarsening of the ⁇ grains after transformation.
- the temperature is lower than 850 ° C., the rolling is performed below the Ar 3 transformation point, which leads to coarsening of ⁇ grains.
- the coiling temperature is too low, the shape of the hot-rolled sheet deteriorates, and the pickling and cold rolling operations in the next process are hindered.
- the temperature is higher than 640 ° C., the scale thickness of the steel sheet is remarkably increased, and the descaling property at the time of pickling in the next process may be deteriorated.
- 620 ° C. or lower is preferable.
- the pickling conditions are not particularly limited as long as the surface scale can be removed. Pickling can be performed by a commonly performed method.
- the cold rolling rate is an important factor in controlling texture, that is, Young's modulus and ⁇ r.
- Young's modulus and the anisotropy of the r value depend on the texture. Since the texture of the steel sheet after annealing is affected not only by the rolling reduction, but also by the addition amount of Mn and B and the winding temperature, the rolling reduction is determined by the above Mn, B addition amount and the winding in the hot rolling process. It must be set appropriately in relation to temperature. By optimizing the rolling reduction, it is possible to rotate in the (111) [1-10] to (111) [-1-12] directions effective in improving E AVE and reducing
- E AVE ⁇ 215 GPa, E 0 ⁇ 210 GPa, E 45 ⁇ 210 GPa, E 90 ⁇ 210 GPa and ⁇ r within a desired range of ⁇ 0.4 to 0.4 by setting the rolling reduction to 87 to 93%. Can do.
- Annealing temperature Recrystallization temperature ⁇ 720 °C
- the annealing method is preferably a continuous annealing method from the viewpoint of material uniformity and high productivity. It is essential that the annealing temperature in continuous annealing is equal to or higher than the recrystallization temperature, but if the annealing temperature is too high, the crystal grains become coarse and rough after processing, and in thin materials such as steel plates for cans, The risk of furnace breakage and buckling will increase. For this reason, the upper limit of annealing temperature shall be 720 degreeC.
- Elongation rate 0.5-5% (preferred conditions)
- the elongation ratio of temper rolling is appropriately determined depending on the tempering degree of the steel sheet, but it is preferable to perform rolling at an elongation ratio of 0.5% or more in order to suppress the occurrence of stretcher strain.
- rolling at an elongation ratio exceeding 5% or more causes a decrease in workability and elongation due to the hardening of the steel sheet, and further decreases the r value and increases the in-plane anisotropy of the r value.
- the upper limit is preferably 5%. More preferably, it is 4% or less.
- a steel slab was obtained by melting steel containing the component compositions A to H shown in Table 1 and the balance being Fe and inevitable impurities.
- the obtained steel slab was reheated at 1200 ° C., and then hot rolled at a finish rolling temperature of 880 to 890 ° C. and a winding temperature of 560 to 650 ° C.
- the steel sheet was cold-rolled at a reduction ratio of 86 to 93.5% to produce a thin steel sheet having a thickness of 0.225 to 0.260 mm.
- the obtained thin steel sheet was annealed at an annealing temperature of 660 to 730 ° C. and an annealing time of 30 seconds in a continuous annealing furnace, and temper rolled at an elongation of 2.0%. Details are shown in Table 2.
- Average accumulated strength f in the (111) [1-10] to (111) [-1-12] orientations of the plate surface at 1/4 thickness of the steel plate Chemical polishing (oxalic acid etching) was performed to remove the influence of processing strain, and after polishing, the integrated strength f was measured at a position of 1/4 plate thickness.
- An X-ray diffractometer was used for the measurement, and (110), (200), (211), and (222) pole figures were created by the Schulz reflection method.
- the average value of the accumulated intensity at 90 ° ( ⁇ 1 is a value of 5 ° interval from 0 ° to 90 °) is the average in the (111) [1-10] to (111) [-1-12] orientations It was set as the accumulation intensity.
- R 0 is a tensile test in the rolling direction
- r 45 is a tensile test in the 45 ° direction relative to the rolling direction
- r 90 is a tensile test in the 90 ° direction relative to the rolling direction.
- Each r value is shown.
- the ferrite structure of the ferrite average crystal grain size rolling direction cross section was etched with a 3% nital solution to reveal grain boundaries, and photographed at 400 times using an optical microscope. Using the photograph obtained, the ferrite average crystal grain size was measured by a cutting method in accordance with the steel-crystal grain size microscopic test method of JIS G 0551.
- two-piece can molding was performed on the steel sheet. Specifically, the steel plate was subjected to chromium plating (tin-free) treatment as a surface treatment, and then a laminated steel plate coated with an organic film was produced. Next, after punching into a circle, deep drawing, ironing, etc. were applied to form a can body similar to the two-piece can applied in beverage cans. The external pressure strength was measured on the can obtained as described above.
- the method is as follows. The can was placed inside the pressurizing chamber, and pressurization inside the pressurizing chamber was carried out by introducing pressurized air into the chamber at 0.016 MPa / s via an air introduction valve.
- the pressure inside the chamber was confirmed through a pressure gauge, a pressure sensor, an amplifier for amplifying the detection signal, a signal processing device for displaying the detection signal, data processing, and the like.
- the critical buckling pressure that is, the external pressure strength
- the external pressure strength should be 0.14 MPa or more with respect to the pressure change due to the heat sterilization treatment. From this, the case where the external pressure strength was higher than 0.14 MPa was indicated as ⁇ , and the case where the external pressure strength was 0.14 MPa or less was indicated as x.
- the surface roughness of the steel plate surface after can making was measured by measuring the surface roughness of the can body and examining the maximum height Rmax.
- the laminated film of the can body was peeled off with an NaOH solution, and the roughness of the surface of the can body steel plate having the highest degree of processing was measured. It was found that when the maximum height of the steel sheet surface Rmax was less than 7.4 ⁇ m, the steel sheet did not damage the film and the corrosion resistance was maintained.
- the maximum height Rmax is less than 7.4 ⁇ m and the skin roughness is low ( ⁇ )
- the maximum height Rmax is 7.4 to less than 9.5 ⁇ m
- the skin roughness is slightly low ( ⁇ )
- the skin roughness is 9.5 ⁇ m or more and the skin roughness is high ( ⁇ ).
- the examples of the present invention all have an average accumulated strength of 7.0 or more in the (111) [1-10] to (111) [-1-12] orientations of the plate surface at a quarter thickness of the steel plate, E AVE ⁇ 215 GPa, E 0 , E 45 , E 90 ⁇ 210 GPa, ⁇ 0.4 ⁇ ⁇ r ⁇ 0.4 and ferrite average crystal grain size 6.0 to 10.0 ⁇ m, high external pressure strength, excellent moldability and surface properties Recognize.
- the cold pressure ratio is lower than the range of the present invention, and ⁇ r is not less than the upper limit value of the present invention.
- the annealing temperature exceeds the range of the present invention, the crystal grains become coarse, and rough skin is generated.
- the cold pressure ratio exceeds the range of the present invention, and ⁇ r is not more than the lower limit value of the present invention.
- the non-recrystallized structure is observed in part because of annealing at the recrystallization temperature or lower.
- the coiling temperature exceeds the range of the present invention, the effect of fine graining by lowering the coiling temperature cannot be obtained, and the crystal grain size of the pressure adjusting plate is not less than the upper limit of the present invention.
- the comparative example No. 18 is lower than the B / N of the present invention, the effect of suppressing the recrystallization of B is not sufficiently exhibited, and the crystal grain size of the pressure adjusting plate is not less than the upper limit of the present invention.
- the comparative example of No19 exceeds the amount of C of the present invention, and the average in the (111) [1-10] to (111) [-1-12] orientations of the plate surface at the 1/4 plate thickness of the steel plate Is less than the range of the present invention, and a high Young's modulus of the steel sheet is not sufficiently obtained.
- the comparative example of No. 20 exceeds the B / N of the present invention, the recrystallization completion temperature rises, and an unrecrystallized structure is observed in the annealing within the scope of the present invention.
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Abstract
Description
特許文献1~5では、圧延方向に対して90°方向のヤング率を高める方法しか開示されていない。この方法では3ピース缶のようなロールフォーム成形によって缶胴部を成形した場合は、高ヤング率を有する方向を缶胴部周方向になるように成形し、パネリング強度を向上させることは可能であるが、絞り加工によって缶胴部が成形される2ピース缶においては高ヤング率を有する方向が必ずしも缶胴部周方向にはならず、缶体の剛性を高める効果が充分に発現されない。また、αファイバーの集積は圧延方向に対して90°方向のヤング率は高めるが、45°方向のヤング率を著しく低下させることが知られている。したがって、上述の方法で得られた高ヤング率鋼板を2ピース缶に成形した場合、缶体の剛性を高めるどころか、逆に低下させてしまう恐れがある。また、DI成形や深絞りしごき成形で製缶される2ピース缶における成形後のイヤリングを小さくする技術およびフィルムとの密着性を良好に保つために表面に肌荒れが発生しない表面性状に関する技術については全く開示されていない。
[1]成分組成は、質量%で、C:0.0005%以上0.0035%以下、Si:0.05%以下、Mn:0.1%以上0.6%以下、P:0.02%以下、S:0.02%未満、Al:0.01%以上0.10%未満、N:0.0030%以下、B:0.0010%以上かつB/N≦3.0(B/N=(B(質量%))/10.81)/(N(質量%)/14.01))を含有し、残部はFeおよび不可避的不純物からなり、鋼板の1/4板厚における板面の(111)[1-10]~(111)[-1-12]方位における平均の集積強度fが7.0以上である組織を有し、かつ、EAVE≧215GPa、E0≧210GPa、E45≧210GPa、E90≧210GPa、-0.4≦Δr≦0.4、および圧延方向断面のフェライト平均結晶粒径が6.0~10.0μmであることを特徴とする外圧に対する缶胴部の座屈強度が高く成形性および成形後の表面性状に優れた缶用鋼板。
ただし、
EAVE=(E0+2E45+E90)/4
E0、E45、E90:圧延方向に対してそれぞれ0、45、90°方向のヤング率
Δr=(r0-2r45+r90)/2
r0、r45、r90:圧延方向に対してそれぞれ0、45、90°方向のランクフォード値
である。
[2]質量%で、C:0.0005%以上0.0035%、Si:0.05%以下、Mn:0.1%以上0.6%以下、P:0.02%以下、S:0.02%未満、Al:0.01%以上、0.10%未満、N:0.0030%以下、B:0.0010%以上かつB/N≦3.0 (B/N=(B(質量%))/10.81)/(N(質量%)/14.01))を含有し、残部は鉄および不可避的不純物からなる成分組成を有する鋼スラブに、再加熱温度が1150~1300℃、仕上げ温度が850~950℃の熱間圧延を施したのち、500~640℃の巻取り温度で巻取り、酸洗後、87~93%の圧下率で冷間圧延し、再結晶温度~720℃の温度で再結晶焼鈍し、調質圧延を行うことを特徴とする前記[1]の外圧に対する缶胴部の座屈強度が高く成形性および成形後の表面性状に優れた缶用鋼板の製造方法。
なお、本明細書において、鋼の成分を示す%は、すべて質量%である。
したがって、本発明の缶用鋼板を食缶や飲料缶等に使用することで、2ピース缶の成形後表面性状およびイヤリング発生による歩留りの低下を招くことなく、缶体の剛性が向上し、鋼板の更なる薄肉化が可能になり、省資源化および低コスト化を達成することができる。また、本発明の缶用鋼板の適用範囲は、各種金属缶のみならず、乾電池内装缶、各種家電・電気部品、自動車用部品等の幅広い範囲への適用も期待できる。
本発明の缶用鋼板は、成分組成が質量%で、C:0.0005%以上0.0035%以下、Si:0.05%以下、Mn:0.1%以上0.6%以下、P:0.02%以下、S:0.02%未満、Al:0.01%以上0.10%未満、N:0.0030%以下、B:0.0010%以上かつB/N≦3.0(B/N=(B(質量%))/10.81)/(N(質量%)/14.01))を含有し、残部はFeおよび不可避的不純物からなり、鋼板の1/4板厚における板面の(111)[1-10]~(111)[-1-12]方位における平均の集積強度fが7.0以上である組織を有し、かつ、EAVE≧215GPa、E0≧210GPa、E45≧210GPa、E90≧210GPa、-0.4≦Δr≦0.4、および圧延方向断面のフェライト平均結晶粒径が6.0~10.0μmである。そして、このような缶用鋼板は、上記成分組成を有する鋼スラブに、再加熱温度が1150~1300℃、仕上げ温度が850~950℃の熱間圧延を施したのち、500~640℃の巻取り温度で巻取り、酸洗後、87~93%の圧下率で冷間圧延し、再結晶温度~720℃の温度で再結晶焼鈍し、伸長率0.5~5%の調質圧延を行うことで製造可能となる。これらは、本発明の最も重要な要件である。
C:0.0005%以上0.0035%以下
一般に、鋼中に固溶しているCの量が多いほど降伏伸びが大きくなり、時効硬化や加工時のストレッチャーストレインの原因となりやすいため、連続焼鈍法を利用した場合においては、製鋼段階において、Cの含有量を極力低く抑えるように制御する必要がある。また、残存固溶炭素量が増加すると、製缶の最終工程である巻き締め部の伸びフランジ成形時に割れを生じたり、加工硬化量についても大きくなるためネック加工やフランジ加工をする際のしわが発生したりする恐れがある。以上より、C含有量は0.0035%以下とする。また、Cは再結晶集合組織に影響を及ぼす元素である。C量が少ないほど<111>方向が板面法線方向に平行な結晶方位群への集積が高まる。平均ヤング率を高めるためには、この結晶方位群への集積を高めることが必要となるが、0.0005%未満では、圧延方向に対して45°方向のヤング率を下げる方位である{100}<110>方位が残りやすくなり、かえって平均ヤング率を低下させてしまう。以上より、C含有量は0.0005%以上とする。
Siは多量に添加すると、鋼板の表面処理性の劣化および耐食性の低下の問題が発生するため、0.05%以下、好ましくは0.02%以下とする。
Mnは、鋼中に含まれる不純物のSに起因する熱間延性の低下を防止するために0.1%以上添加する必要がある。MnはAr3変態点を低下させる元素の一つであり、熱間圧延仕上圧延温度をより低下させることができる。このために、熱間圧延時にγ粒の再結晶粒成長を抑制し、さらに変態後のα粒を微細化できる。また、本発明では、後述するB添加による細粒化効果に加えて、Mnを添加してさらなる細粒化を達成し、製缶後の優れた表面性状を確保する。以上の効果を得るために、Mnは0.1%以上とする。一方、JIS G 3303に規定されたとりべ分析値やアメリカ合衆国材料試験協会規格(ASTM)のとりべ分析値において、通常の食品容器に用いられるぶりき原板のMnの上限は0.6%以下と規定されている。よって、Mnは0.6%以下とする。
Pは、多量に添加すると、鋼の硬質化、耐食性の低下を引き起こす。よって、Pは0.02%以下とする。
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。よって、Sは0.02%未満とする。
Alは、脱酸剤として添加される元素である。また、NとAlNを形成することにより、鋼中の固溶Nを減少させる効果を有する。しかし、Alの含有量が0.01%未満では、十分な脱酸効果や固溶N低減効果が得られない。よって、Alは0.01%以上とする。一方、0.10%以上になると、上記効果が飽和するだけでなく、アルミナなどの介在物が増加するため好ましくない。よってAlの含有量は0.01以上0.10%未満の範囲とする。
Nは不可避的に混入する不純物である。N量が高くなるほどこれを固定するためのBの添加量を増やさなければならない。B添加量の大幅な増加はコストアップにつながるので、Nは0.0030%以下とする。
Bは、鋼中に固溶したNと結合してBNとして析出することにより、時効硬化を防止する効果がある。また、BNとして析出するために必要な量以上に添加された場合は、熱延板および焼鈍板の結晶粒を微細にする効果を有することが認められている。これは、過剰に添加されたBが結晶粒界に固溶Bとして偏析し、結晶粒の粒成長を抑制するためであると考えられる。このような結晶粒の微細化効果を発揮させるためには、BNを析出させた上でさらに固溶BとしてBを存在させることが必要である。上記の時効硬化を防止する効果と結晶粒の微細化効果の両方を得るためには、本発明者らが行った種々の試験の結果から、Bは0.0010%以上必要であるとの知見を得た。以上より、Bは0.0010%以上とする。一方、固溶Bの増加は連続焼鈍工程における再結晶完了温度を過度に上昇させ、炉内破断やバックリングの発生の危険が大きくなる。このため、B/N≦3.0とする。また、実機製造においてN量は変動するので、確実に固溶Bを存在させるためにはB/N≧1.1とすることが好ましい。ただし、B/N=(B(質量%))/10.81)/(N(質量%)/14.01)である。
集合組織:(111)[1-10]~(111)[-1-12]方位における平均の集積強度fが7.0以上
(111)[1-10]~(111)[-1-12]方位の集合組織を発達させることで、圧延方向に対して0、45、90°方向のヤング率を等方的に高めることができることから鋼板の1/4板厚における板面の(111)[1-10]~(111)[-1-12]方位における平均の集積強度fを7.0以上とすることが必要となる。
ただし、EAVE=(E0+2E45+E90)/4であり、E0、E45、E90は圧延方向に対してそれぞれ0、45、90°方向のヤング率を表す。
缶胴部の剛性を高める観点から、EAVEは215GPa以上とする。215GPa以上とすることでパネリング強度が顕著に向上し、鋼板の薄肉化に伴う、内容物の加熱殺菌処理等における缶外部の圧力の増減による缶胴部の変形を防ぐことができる。
一方で、絞り加工によって成形される2ピース缶では、鋼板のヤング率の異方性が問題となる。すなわち、E0、E45、E90の内、一方向ないし二方向だけのヤング率が高く、その他の方向のヤング率が低い場合、EAVE≧215GPaを満足していても、缶胴部の剛性を高める効果が十分に発揮されない。缶胴部の剛性を高めるためにはE0、E45、E90をそれぞれ210GPa以上にする必要がある。
ラミネート鋼板においては、フィルムと鋼板の剥離やフィルムへの応力集中で発生するフィルム破断により下地鋼板が露出し耐食性が劣化する場合がある。これは、DI成形や絞りしごき成形後の鋼板表面の肌荒れを起因として起こるものであり、この肌荒れの程度は、フェライト結晶粒径の大きさに比例する。そのため、下地に用いる鋼板の圧延方向断面のフェライト平均結晶粒径は10.0μm以下、望ましくは9.0μm以下とする。一方、結晶粒径が過度に微細であると、細粒化強化により鋼板強度が大幅に増大する。このため圧延方向断面のフェライト平均結晶粒径は6.0μm以上とする。
本発明では、イヤリングの指標として、下記式にて表されるΔrを用いることにする。
Δr=(r0-2r45+r90)/2
ただし、r0、r45、r90は、それぞれ圧延方向に0、45、90°の方向のランクフォード(以下、r値と称することがある)を表す。
Δrが0.4より大きい、または-0.4より小さい鋼板では、DI成形や絞りしごき成形した際、イヤリング発生が大きいためトリム代が大きくなり歩留りが低下する。歩留りの観点からイヤリング発生量を抑制するために、Δrは-0.4~0.4の範囲にする必要がある。
なお、Δrは、冷間圧延の圧下率を調整することで、所定の範囲とすることができる。
本発明の缶用鋼板は、上記組成からなる鋼スラブに、再加熱温度が1150~1300℃、仕上げ温度が850~950℃の熱間圧延を施したのち、500~640℃の巻取り温度で巻取り、酸洗後、87~93%の圧下率で冷間圧延し、再結晶温度~720℃の温度で再結晶焼鈍し、伸長率0.5~5%の調質圧延を行うことで製造される。
熱間圧延前のスラブ再加熱温度は、高すぎると製品表面の欠陥やエネルギーコストが上昇するなどの問題が発生する。一方、低すぎると、最終仕上圧延温度の確保が難しくなる。よって、スラブ再加熱温度は1150~1300℃とする。
熱延鋼板の結晶粒微細化や析出物分布の均一性の観点から、最終仕上圧延温度は850~950℃、巻取温度は500~640℃とする。
最終仕上圧延温度が、950℃よりも高くなると、圧延後のγ粒粒成長がより激しく起こり、それに伴う粗大γ粒により変態後のα粒の粗大化を招く。また、850℃より低い場合は、Ar3変態点以下の圧延となり、α粒の粗大化を招く。
巻取り温度が低すぎると熱延板の形状が劣化し、次工程の酸洗、冷間圧延の操業に支障をきたすため、500℃以上とする。一方、640℃よりも高くなると、鋼板のスケール厚みが顕著に増大し、次工程の酸洗時の脱スケール性が劣化する可能性がある。上記問題を一層改善するためには、620℃以下が好ましい。
冷間圧延率は集合組織制御即ちヤング率およびΔrを制御する上で重要な因子である。
一般的に、ヤング率およびr値の異方性は集合組織に依存することが知られている。焼鈍後の鋼板の集合組織は圧下率のみではなく、Mn、Bの添加量および巻取り温度にも影響を受けるので、圧下率は、上記Mn、B添加量および熱間圧延工程での巻取温度との関係で適切に設定されなければならない。その圧下率を最適化することで、EAVEの向上および|Δr|の低減に有効な(111)[1-10]~(111)[-1-12]方位に回転させることができる。具体的には、圧下率を87~93%とすることでEAVE≧215GPa、E0≧210GPa、E45≧210GPa、E90≧210GPaかつΔrを所望の-0.4~0.4の範囲内にすることができる。
焼鈍方法は、材質の均一性と高い生産性の観点から連続焼鈍法が好ましい。連続焼鈍における焼鈍温度は、再結晶温度以上であることが必須であるが、焼鈍温度が高すぎると結晶粒が粗大化し、加工後の肌荒れが大きくなるほか、缶用鋼板などの薄物材では、炉内破断やバックリングの発生の危険が大きくなる。このため、焼鈍温度の上限は720℃とする。
調質圧延の伸張率は、鋼板の調質度により適宜決定されるが、ストレッチャーストレインの発生を抑えるために、0.5%以上の伸張率で圧延するのが好ましい。一方、伸張率5%以上を超える伸張率で圧延すると、鋼板が硬質化することによる加工性の低下と伸びの低下、さらにはr値の低下およびr値の面内異方性の増大を引き起こす場合がある。よって、上限は5%が好ましい。さらに好ましくは4%以下である。
加工歪みの影響を除去するため化学研磨(シュウ酸エッチング)を行い、研磨後、1/4板厚の位置にて集積強度fを測定した。測定にはX線回折装置を使用し、Schulzの反射法により(110)、(200)、(211)、(222)極点図を作成した。これらの極点図から結晶方位分布関数(ODF:Orientation Distribution Function)を算出し、Euler空間(Bunge方式)のφ2=45°、Φ=55°において、φ1=0°、5°、10°・・・90°(φ1は0°から90°まで5°間隔の値とした)のときの集積強度の平均値を(111)[1-10]~(111)[-1-12]方位における平均の集積強度とした。
圧延方向に対して0°、45°および90°方向を長手方向として10×35mmの試験片を切り出し、横振動型の共振周波数測定装置を用いて、American Society for Testing Materialsの基準(C1259)に従い、圧延方向に対して0°、45°および90°方向のヤング率E0、E45、E90(GPa)を測定し、平均ヤング率EAVE[=(E0+2E45+E90)/4]を求めた。
r値の測定はJIS13号Bハーフサイズの引張試験片(幅12.5mm、平行部35mm、標点間距離20mm)を用いて測定を行い、JIS Z 2254の薄板金属材料の塑性ひずみ比試験方法に準拠して、r値を算出し、Δr[=(r0+r90-2r45)/2]を求めた。なお、r0は圧延方向に引張試験を行った時、r45は圧延方向に対して45°方向に引張試験を行った時、r90は圧延方向に対して90°方向に引張試験を行った時の各々のr値を示す。
圧延方向断面のフェライト組織を3%ナイタール溶液でエッチングして粒界を現出させ、光学顕微鏡を用いて400倍で撮影した。得られた写真を用いて、JIS G 0551の鋼-結晶粒度の顕微鏡試験方法に準拠して、切断法によりフェライト平均結晶粒径を測定した。
以上により得られた缶体に対して、外圧強度の測定を行った。方法は以下のとおりである。
缶体を加圧チャンバーの内部に設置し、加圧チャンバー内部の加圧は、空気導入バルブを介してチャンバーに0.016MPa/sで加圧空気を導入することで行った。チャンバーの内部の圧力の確認は、圧力ゲージ、圧力センサ、その検出信号を増幅するアンプ、検出信号の
表示、データ処理などを行う信号処理装置を介して行った。限界座屈圧力、つまり外圧強度は座屈に伴う圧力変化点の圧力とした。一般的に、加熱殺菌処理による圧力変化に対して、外圧強度は0.14MPa以上を有すればよいとされている。これより、外圧強度が0.14MPaより高いのものを○、外圧強度が0.14MPa以下のものを×としてそれぞれ表示した。
結果を表3に示す。
Claims (2)
- 成分組成は、質量%で、C:0.0005%以上0.0035%以下、Si:0.05%以下、Mn:0.1%以上0.6%以下、P:0.02%以下、S:0.02%未満、Al:0.01%以上0.10%未満、N:0.0030%以下、B:0.0010%以上かつB/N≦3.0(B/N=(B(質量%))/10.81)/(N(質量%)/14.01))を含有し、残部はFeおよび不可避的不純物からなり、
鋼板の1/4板厚における板面の(111)[1-10]~(111)[-1-12]方位における平均の集積強度fが7.0以上である組織を有し、
かつ、EAVE≧215GPa、E0≧210GPa、E45≧210GPa、E90≧210GPa、-0.4≦Δr≦0.4、および圧延方向断面のフェライト平均結晶粒径が6.0~10.0μmであることを特徴とする外圧に対する缶胴部の座屈強度が高く成形性および成形後の表面性状に優れた缶用鋼板。
ただし、
EAVE=(E0+2E45+E90)/4
E0、E45、E90:圧延方向に対してそれぞれ0、45、90°方向のヤング率
Δr=(r0-2r45+r90)/2
r0、r45、r90:圧延方向に対してそれぞれ0、45、90°方向のランクフォード値
である。 - 質量%で、C:0.0005%以上0.0035%、Si:0.05%以下、Mn:0.1%以上0.6%以下、P:0.02%以下、S:0.02%未満、Al:0.01%以上0.10%未満、N:0.0030%以下、B:0.0010%以上かつB/N≦3.0(B/N=(B(質量%))/10.81)/(N(質量%)/14.01))を含有し、残部は鉄および不可避的不純物からなる成分組成を有する鋼スラブに、
再加熱温度が1150~1300℃、仕上げ温度が850~950℃の熱間圧延を施したのち、500~640℃の巻取り温度で巻取り、
酸洗後、87~93%の圧下率で冷間圧延し、
再結晶温度~720℃の温度で再結晶焼鈍し、
調質圧延を行うことを特徴とする請求項1に記載の外圧に対する缶胴部の座屈強度が高く成形性および成形後の表面性状に優れた缶用鋼板の製造方法。
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EP12774346.6A EP2700731A4 (en) | 2011-04-21 | 2012-04-19 | STEEL PLATE FOR CANS WITH HIGH RUMP NICKNESS STRENGTH UNDER EXTERNAL PRINTING AND WITH EXCELLENT FORMABILITY AND EXCELLENT SURFACE PROPERTIES AFTER FORMING, AND METHOD FOR THE PRODUCTION THEREOF |
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Citations (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH05255804A (ja) | 1992-03-11 | 1993-10-05 | Nippon Steel Corp | 成形性および剛性の優れた冷延鋼板およびその製造方法 |
JPH0641683A (ja) * | 1992-04-06 | 1994-02-15 | Kawasaki Steel Corp | 缶用鋼板およびその製造方法 |
JPH06212353A (ja) | 1993-01-11 | 1994-08-02 | Nippon Steel Corp | 高剛性容器用鋼板及びその製造方法 |
JPH06248332A (ja) | 1993-02-26 | 1994-09-06 | Nippon Steel Corp | 容器用鋼板の製造方法 |
JPH06248339A (ja) | 1993-02-26 | 1994-09-06 | Nippon Steel Corp | 高剛性容器用鋼板の製造方法 |
JPH08311541A (ja) | 1995-05-18 | 1996-11-26 | Sumitomo Metal Ind Ltd | 高ヤング率鋼板の製造方法 |
JPH09227947A (ja) * | 1996-02-26 | 1997-09-02 | Nkk Corp | 極低炭素缶用鋼板の製造方法 |
JPH108142A (ja) | 1996-06-26 | 1998-01-13 | Kawasaki Steel Corp | 加工性が良好でかつ肌荒れのない製缶用鋼板の製造方 法 |
JPH1081919A (ja) | 1996-09-05 | 1998-03-31 | Kawasaki Steel Corp | ノンイヤリング性および耐肌荒れ性に優れる2ピース缶用鋼板の製造方法 |
JPH10280094A (ja) * | 1997-04-10 | 1998-10-20 | Nippon Steel Corp | イヤリングが小さく耐ネックしわ性に優れた2ピース容器用鋼板およびその製造方法 |
JP2005320633A (ja) * | 2005-06-20 | 2005-11-17 | Jfe Steel Kk | 2ピース変形缶用鋼板およびその製造方法 |
JP2007239035A (ja) * | 2006-03-09 | 2007-09-20 | Jfe Steel Kk | 耐ひずみ時効性および耐肌荒れ性に優れ、面内異方性の小さい冷延鋼板およびその製造方法 |
JP2010229486A (ja) | 2009-03-27 | 2010-10-14 | Jfe Steel Corp | 絞りおよびしごき加工後の表面性状に優れた缶用鋼板およびその製造方法 |
WO2011021646A1 (ja) * | 2009-08-19 | 2011-02-24 | Jfeスチール株式会社 | 高加工性3ピース溶接缶用鋼板およびその製造方法 |
Family Cites Families (21)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0565066B1 (en) * | 1992-04-06 | 1997-07-02 | Kawasaki Steel Corporation | A tin mill black plate for canmaking, and method of manufacturing |
JPH073334A (ja) | 1993-06-18 | 1995-01-06 | Nippon Steel Corp | 低イヤリング容器用鋼板の製造方法 |
JPH07188854A (ja) | 1993-12-28 | 1995-07-25 | Nkk Corp | 面内異方性の小さい冷延鋼板 |
US5587027A (en) | 1994-02-17 | 1996-12-24 | Kawasaki Steel Corporation | Method of manufacturing canning steel sheet with non-aging property and superior workability |
JPH08246060A (ja) * | 1995-03-10 | 1996-09-24 | Kawasaki Steel Corp | 缶用鋼板の製造方法 |
JP3695048B2 (ja) | 1997-03-04 | 2005-09-14 | Jfeスチール株式会社 | 変形3ピース缶用鋼板およびその製造方法 |
JPH10330844A (ja) | 1997-05-28 | 1998-12-15 | Nippon Steel Corp | 成形性に優れた冷延鋼板の製造方法 |
JP3548390B2 (ja) | 1997-07-29 | 2004-07-28 | 新日本製鐵株式会社 | イヤリングが著しく小さい硬質2ピース容器用鋼板およびその製造方法 |
AU4164599A (en) * | 1998-05-29 | 1999-12-20 | Toyo Kohan Co. Ltd. | Resin-coated steel sheet suitable for use in thin-walled deep-drawn ironed can and steel sheet therefor |
JP3707260B2 (ja) * | 1998-09-11 | 2005-10-19 | Jfeスチール株式会社 | 面内異方性および面内異方性のコイル内均一性に優れた2ピース缶用極薄鋼板の製造方法 |
JP2001247917A (ja) * | 2000-03-06 | 2001-09-14 | Nkk Corp | 極低炭素缶用鋼板の製造方法 |
JP2002212673A (ja) | 2001-01-19 | 2002-07-31 | Toyo Kohan Co Ltd | 異方性の優れた電池外筒缶用鋼板及びその製造法 |
JP3756779B2 (ja) * | 2001-04-20 | 2006-03-15 | Jfeスチール株式会社 | 加工性に優れた薄肉化深絞りしごき缶用鋼板 |
KR100627430B1 (ko) | 2001-10-04 | 2006-09-25 | 신닛뽄세이테쯔 카부시키카이샤 | 용기용 강판 및 이를 제조하는 방법 |
JP4835015B2 (ja) | 2004-03-25 | 2011-12-14 | Jfeスチール株式会社 | 軟質缶用鋼板およびその製造方法 |
WO2006100796A1 (ja) * | 2005-03-24 | 2006-09-28 | Jfe Steel Corporation | 軟質缶用鋼板およびその製造方法 |
JP4604883B2 (ja) | 2005-06-30 | 2011-01-05 | Jfeスチール株式会社 | 異方性の小さい鋼板およびその製造方法 |
JP4867256B2 (ja) * | 2005-09-29 | 2012-02-01 | Jfeスチール株式会社 | 剛性に優れた高強度薄鋼板およびその製造方法 |
KR101030207B1 (ko) | 2006-03-16 | 2011-04-22 | 제이에프이 스틸 가부시키가이샤 | 냉연 강판 및 그 제조 방법, 전지 및 그 제조 방법 |
JP5076872B2 (ja) | 2007-12-21 | 2012-11-21 | Jfeスチール株式会社 | 缶用鋼板およびその製造方法 |
JP5272714B2 (ja) | 2008-12-24 | 2013-08-28 | Jfeスチール株式会社 | 製缶用鋼板の製造方法 |
-
2012
- 2012-04-16 JP JP2012092556A patent/JP5958038B2/ja active Active
- 2012-04-19 TW TW101113992A patent/TWI450981B/zh active
- 2012-04-19 CN CN201280027406.8A patent/CN103597110B/zh active Active
- 2012-04-19 CA CA2833452A patent/CA2833452C/en not_active Expired - Fee Related
- 2012-04-19 WO PCT/JP2012/002709 patent/WO2012144213A1/ja active Application Filing
- 2012-04-19 US US14/112,717 patent/US10174393B2/en active Active
- 2012-04-19 EP EP12774346.6A patent/EP2700731A4/en not_active Withdrawn
Patent Citations (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH05255804A (ja) | 1992-03-11 | 1993-10-05 | Nippon Steel Corp | 成形性および剛性の優れた冷延鋼板およびその製造方法 |
JPH0641683A (ja) * | 1992-04-06 | 1994-02-15 | Kawasaki Steel Corp | 缶用鋼板およびその製造方法 |
JPH06212353A (ja) | 1993-01-11 | 1994-08-02 | Nippon Steel Corp | 高剛性容器用鋼板及びその製造方法 |
JPH06248332A (ja) | 1993-02-26 | 1994-09-06 | Nippon Steel Corp | 容器用鋼板の製造方法 |
JPH06248339A (ja) | 1993-02-26 | 1994-09-06 | Nippon Steel Corp | 高剛性容器用鋼板の製造方法 |
JPH08311541A (ja) | 1995-05-18 | 1996-11-26 | Sumitomo Metal Ind Ltd | 高ヤング率鋼板の製造方法 |
JPH09227947A (ja) * | 1996-02-26 | 1997-09-02 | Nkk Corp | 極低炭素缶用鋼板の製造方法 |
JPH108142A (ja) | 1996-06-26 | 1998-01-13 | Kawasaki Steel Corp | 加工性が良好でかつ肌荒れのない製缶用鋼板の製造方 法 |
JPH1081919A (ja) | 1996-09-05 | 1998-03-31 | Kawasaki Steel Corp | ノンイヤリング性および耐肌荒れ性に優れる2ピース缶用鋼板の製造方法 |
JPH10280094A (ja) * | 1997-04-10 | 1998-10-20 | Nippon Steel Corp | イヤリングが小さく耐ネックしわ性に優れた2ピース容器用鋼板およびその製造方法 |
JP2005320633A (ja) * | 2005-06-20 | 2005-11-17 | Jfe Steel Kk | 2ピース変形缶用鋼板およびその製造方法 |
JP2007239035A (ja) * | 2006-03-09 | 2007-09-20 | Jfe Steel Kk | 耐ひずみ時効性および耐肌荒れ性に優れ、面内異方性の小さい冷延鋼板およびその製造方法 |
JP2010229486A (ja) | 2009-03-27 | 2010-10-14 | Jfe Steel Corp | 絞りおよびしごき加工後の表面性状に優れた缶用鋼板およびその製造方法 |
WO2011021646A1 (ja) * | 2009-08-19 | 2011-02-24 | Jfeスチール株式会社 | 高加工性3ピース溶接缶用鋼板およびその製造方法 |
Non-Patent Citations (1)
Title |
---|
See also references of EP2700731A4 * |
Cited By (4)
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WO2015182360A1 (ja) * | 2014-05-30 | 2015-12-03 | Jfeスチール株式会社 | 缶用鋼板およびその製造方法 |
JPWO2015182360A1 (ja) * | 2014-05-30 | 2017-04-20 | Jfeスチール株式会社 | 缶用鋼板 |
US10301702B2 (en) | 2014-05-30 | 2019-05-28 | Jfe Steel Corporation | Steel sheet for cans and manufacturing method thereof |
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