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WO2016157761A1 - Tôle d'acier pour canette et son procédé de production - Google Patents

Tôle d'acier pour canette et son procédé de production Download PDF

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Publication number
WO2016157761A1
WO2016157761A1 PCT/JP2016/001411 JP2016001411W WO2016157761A1 WO 2016157761 A1 WO2016157761 A1 WO 2016157761A1 JP 2016001411 W JP2016001411 W JP 2016001411W WO 2016157761 A1 WO2016157761 A1 WO 2016157761A1
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steel sheet
steel plate
steel
crystal grain
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PCT/JP2016/001411
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English (en)
Japanese (ja)
Inventor
雄介 木俣
船川　義正
直行 ▲高▼田
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JFE Steel Corp
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JFE Steel Corp
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Priority to JP2017509237A priority Critical patent/JP6210177B2/ja
Priority to CN201680017408.7A priority patent/CN107429348B/zh
Publication of WO2016157761A1 publication Critical patent/WO2016157761A1/fr
Anticipated expiration legal-status Critical
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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
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium

Definitions

  • the present invention relates to a steel plate for cans and a method for producing the same, and more particularly to a steel plate for cans having excellent workability, excellent surface roughness in surface appearance and suppressing striped defects, and a method for producing the same.
  • Patent Document 1 and Patent Document 2 propose a steel sheet in which Ti or Nb is added to an ultra-low carbon steel, yield strength (YP) is lowered, and workability is improved.
  • the steel plate which made small the surface roughness after a process is proposed by using the low carbon steel whose crystal grain is a fine grain.
  • the ultra-low carbon steel in which Ti or Nb is added and solid solution C is completely precipitated and fixed has coarse crystal grains and is excellent.
  • the low carbon steel obtained by patent document 3 has a problem that a crystal grain is fine and yield strength (YP) is high, and it is inferior to workability by the crack at the time of can molding.
  • YP yield strength
  • coarsening of the crystal grain size is effective for workability
  • fine grain size is effective for rough skin resistance.
  • the suppression of stripe defects was not sufficient as the surface appearance.
  • the object of the present invention is to solve the above-mentioned problems, and to provide a steel plate for cans which has excellent processability, excellent surface roughness in surface appearance and suppresses striped defects, and a method for producing the same.
  • the present inventors have intensively studied to develop a steel plate for cans that solves the above-described problems and realizes all of improvement of workability, improvement of rough skin resistance, and suppression of striped defects.
  • a reduction in yield strength (YP) due to coarsening of the crystal grain size is effective for improving workability. Further, it is effective to reduce the crystal grain size in order to improve the rough skin resistance.
  • the crystal grain size that affects the yield strength (YP) is the crystal grain size in the entire region of the steel sheet, whereas the crystal grain size that affects the rough skin resistance is a crystal near the surface layer of the steel sheet.
  • the present inventors have found that it is possible to control the distribution of crystal grain size in the plate thickness direction by controlling the equivalent dislocation density of the surface layer of the original steel plate before annealing (steel plate before annealing). It was.
  • FIG. 1 shows the relationship between the equivalent dislocation density of the steel sheet surface layer before recrystallization by annealing, the surface layer average crystal grain size and the total thickness average crystal grain size of the steel sheet after annealing.
  • the measurement of the equivalent dislocation density of the steel sheet surface layer was performed according to the method described later.
  • the surface average grain size of the steel sheet after annealing in the figure, simply referred to as the surface average grain size
  • the total thickness average grain size of the steel sheet after annealing in the figure, simply referred to as the total thickness average grain size
  • the high equivalent dislocation density on the surface layer of the steel plate promotes recrystallization during annealing, suppresses the remaining non-recrystallized grains that are problematic in the ultra-low carbon steel plate added with Ti and Nb described above, and the steel plate surface after annealing. Suppresses striped defects. Therefore, by increasing the equivalent dislocation density of the steel sheet surface layer, it is possible to obtain a steel sheet having low yield strength (YP), excellent workability, excellent surface roughness in the surface appearance, and having suppressed stripe defects. .
  • the area ratio of the non-recrystallized grains on the steel sheet surface is 0.10% or less, and the average crystal grain diameter d1 and the average crystal grain diameter d2 of the total thickness in the structure from the steel sheet surface to a depth of 50 ⁇ m are d1 ⁇ 0.8 ⁇ .
  • the steel plate for cans that is annealed at 550 ° C. or more and 700 ° C. or less with respect to the steel plate having an equivalent dislocation density ⁇ of 1.0 ⁇ 10 15 m ⁇ 2 or more from the surface of the steel plate before annealing to 50 ⁇ m in the depth direction. Manufacturing method.
  • the equivalent transition density ⁇ is calculated from 14.4 ⁇ 2 / b 2 ( ⁇ represents a non-uniform strain of the steel sheet, and b is 2.5 ⁇ 10 ⁇ 10 m).
  • a steel plate for a can having a low yield strength (YP), excellent workability, and excellent surface roughness in the surface appearance and suppressing striped defects.
  • the steel plate for cans according to the present invention is in mass%, C: 0.0010% or more and 0.0050% or less, Si: 0.03% or less, Mn: 0.3% or less, P: 0.02% or less, S: 0.02% or less, Al: 0.01% or more and 0.10% or less, N: 0.004% or less, Ti: 0.01% or more and 0.06% or less and / or Nb: 0 0.01% or more and 0.04% or less, and the balance is composed of Fe and inevitable impurities, the area ratio of unrecrystallized grains on the steel sheet surface is 0.10% or less,
  • the average crystal grain size d1 and the average crystal grain size d2 of the entire thickness satisfy the relationship of d1 ⁇ 0.8 ⁇ d2, and d2 is 11.0 ⁇ m or more.
  • the steel plate for cans of the present invention will be described.
  • ⁇ C 0.0010% or more and 0.0050% or less> If C is less than 0.0010%, the ferrite crystal grains are excessively coarsened, so the lower limit of the C content is 0.0010%. On the other hand, when the C content exceeds 0.0050%, the yield strength increases and the workability at the time of draw forming decreases, so the upper limit of the C content is set to 0.0050%. Therefore, the C content is set to 0.0010% or more and 0.0050% or less. Preferably, the C content is 0.0015% or more. Preferably, the C content is 0.0040% or less.
  • Si 0.03% or less> Even if Si is not intentionally contained, it is an element that remains in the steel as an impurity component and degrades the corrosion resistance and plating adhesion of the steel sheet.
  • the Si content is 0. 0.03% or less.
  • the Si content is 0.02% or less.
  • Mn prevents hot cracking of the slab by precipitating S in the steel as MnS.
  • MnS precipitating S in the steel
  • Mn is a solid solution strengthening element, and the workability at the time of drawing is reduced by increasing the yield strength, so the upper limit of the Mn content is 0.3%.
  • P is a solid solution strengthening element, and decreases the workability at the time of drawing by increasing the yield strength. Moreover, it is an element which reduces the adhesiveness of Ni plating, P content shall be 0.02% or less.
  • S is preferably as small as possible from the viewpoint of preventing hot cracking of the slab, and the S content is 0.02% or less.
  • Al 0.01% or more and 0.10% or less>
  • Al When Al is contained in an amount of 0.01% or more, it combines with N in the steel to form AlN, and by reducing the solid solution N, an increase in yield strength (YP) due to aging of the steel sheet is suppressed.
  • the Al content exceeds 0.10%, inclusions such as alumina are likely to occur, and the defect occurrence rate after processing increases. Therefore, it is 0.10% or less. Therefore, the Al content is set to 0.01% or more and 0.10% or less.
  • the Al content is preferably 0.02% or more.
  • Al content 0.08% or less is preferable and 0.07% or less is more preferable.
  • N forms a nitride with Al or B and tends to be harmless, but the N content is preferably as low as possible, and is 0.004% or less. Preferably, the N content is 0.003% or less.
  • Ti precipitates and fixes C and N in the steel and improves the aging resistance of the steel sheet. If the content is less than 0.01%, the effect is not sufficient, and aging deterioration is caused. If the content exceeds 0.06%, the recrystallization temperature is remarkably increased, so that unrecrystallized grains tend to remain. Therefore, when Ti is contained, the Ti content is 0.01% or more and 0.06% or less. When Ti is contained, the Ti content is preferably 0.01% or more and 0.05% or less, and more preferably 0.01% or more and 0.04% or less.
  • Nb precipitates and fixes C in the steel and improves the aging resistance of the steel sheet. If it is less than 0.01%, the effect is not sufficient, and aging deterioration is caused. If it exceeds 0.04%, the recrystallization temperature is remarkably increased, so that unrecrystallized grains tend to remain. Therefore, when Nb is contained, the Nb content is set to 0.01% or more and 0.04% or less. When Nb is contained, the Nb content is preferably 0.01% or more and 0.03% or less, and more preferably 0.01% or more and 0.02% or less.
  • the balance other than the above components is Fe and inevitable impurities.
  • B is not an essential component, but can be contained in the following range as required.
  • B like Al, binds to N in steel to form BN, and reduces the amount of solid solution N, thereby suppressing an increase in yield strength (YP) due to aging. Moreover, it has the effect
  • the B content is preferably 0.0003% or more and 0.0030% or less.
  • the B content is more preferably 0.0005% or more.
  • the B content is more preferably 0.0020% or less.
  • Non-recrystallized grains are harder than recrystallized grains, and due to their different deformability, striped surface defects (hereinafter also referred to as stripe defects) are generated after press working. Since the presence of non-recrystallized grains on the steel sheet surface becomes a problem for striped defects, the area ratio of the non-recrystallized grains on the steel sheet surface after recrystallization annealing is reduced to 0.10% or less, A steel plate for cans having an excellent appearance after processing can be obtained.
  • the surface of the steel sheet is observed and the ratio (area ratio) of the non-recrystallized structure to the entire structure is obtained.
  • the area ratio occupied by crystal grains may be used.
  • the non-recrystallized grains present inside the steel sheet do not specifically define because they do not affect the surface appearance, but if they are excessively present, the yield strength (YP) increases remarkably and causes molding defects such as cracks during press molding. It is preferable that the amount is as small as possible.
  • the area ratio which the non-recrystallized grain accounts on the steel plate surface after recrystallization annealing can be adjusted by controlling the equivalent dislocation density from the steel plate surface before recrystallization by annealing to a depth of 50 ⁇ m.
  • the average crystal grain size (d1) and the total thickness average crystal grain size (d2) in the structure from the steel sheet surface to a depth of 50 ⁇ m satisfy the relationship of d1 ⁇ 0.8 ⁇ d2 and d2 is 11.0 ⁇ m or more>
  • the larger the crystal grain size of the steel sheet surface layer the more likely it is that the surface becomes rough after press working, and the poor surface roughness resistance.
  • the average crystal grain size (d1) in the structure from the steel sheet surface to the depth of 50 ⁇ m representing the crystal grain size of the steel sheet surface layer, and the average crystal grain size of the total thickness of the steel sheet (d2, hereinafter referred to as total thickness average crystal grain) In the case of d1 ⁇ 0.8 ⁇ d2, the crystal grain size in the vicinity of the steel plate surface layer is made fine, and the crystal grain size in the region other than the steel plate surface layer is made coarse so that the workability is improved. And excellent resistance to rough skin.
  • d2 When the total thickness average crystal grain size (d2) of the steel sheet is less than 11.0 ⁇ m, the yield strength (YP) is high and the workability is inferior, so d2 is set to 11.0 ⁇ m or more.
  • the upper limit of the average crystal grain size of the steel sheet surface layer that is, the average crystal grain size (d1) in the structure from the steel sheet surface to the depth of 50 ⁇ m is not particularly specified, when the crystal grains are coarse, D1 is preferably 10 ⁇ m or less because it is difficult to satisfy the definition of the surface roughness Ra.
  • the lower limit of d1 / d2 is not particularly limited, but is preferably 0.3 or more from the viewpoint of surface peeling due to a difference in hardness.
  • the average crystal grain size is obtained by measuring the average crystal grain size by a cutting method based on JIS G0551.
  • the above average crystal grain size is obtained by measuring the ferrite average crystal grain size by a cutting method based on JIS G0551.
  • the average crystal grain size (d1) in the structure from the steel sheet surface to a depth of 50 ⁇ m can be adjusted by controlling the equivalent dislocation density from the steel sheet surface before the recrystallization by annealing to a depth of 50 ⁇ m.
  • the total thickness average crystal grain size (d2) can be adjusted by changing the annealing temperature and the steel plate components.
  • plating film When a plating film is applied to the steel plate for cans of the present invention, Sn plating, Ni plating, Cr plating, or the like may be applied as the surface treatment of the steel plate. Furthermore, chemical conversion treatment may be performed, or an organic film such as a laminate may be formed.
  • the plate thickness is preferably set to 0.1 mm or more and 0.6 mm or less. More preferably, the plate thickness is 0.1 mm or more and 0.4 mm or less. In the present invention, the desired plate thickness can be adjusted by changing the cold rolling rate.
  • a slab having the above-described component composition is heated at a heating temperature of 1000 ° C. to 1300 ° C. and hot-rolled at a finish rolling temperature of 800 ° C. to 1000 ° C., 600
  • the equivalent dislocation density ⁇ up to 50 ⁇ m in the depth direction from the steel sheet surface of the steel sheet after annealing, pickling, cold rolling, and before annealing at a temperature of ⁇ 700 ° C. is 1.0 ⁇ 10 15 m ⁇ 2 or more.
  • a certain steel plate is annealed at 550 ° C. or more and 700 ° C. or less.
  • the method for melting the steel material is not particularly limited, and a known melting method such as a converter or an electric furnace can be employed. Moreover, after melting, it is preferable to use a slab (steel material) by a continuous casting method because of problems such as segregation, but a slab can also be formed by a known casting method such as an ingot-bundling rolling method or a thin slab continuous casting method. good.
  • Slab heating temperature shall be 1000 degreeC or more from a viewpoint of ensuring the finishing rolling temperature mentioned later.
  • slab heating temperature exceeds 1300 ° C., a large amount of nitride is generated, causing unrecrystallized grains to remain after annealing, and yield strength is increased. Therefore, slab heating temperature shall be 1300 degrees C or less.
  • finish rolling temperature 800 ° C to 1000 ° C>
  • finish rolling temperature 800 ° C. or higher and 1000 ° C. or lower.
  • finish rolling temperature 800 ° C. or higher.
  • finish rolling temperature shall be 1000 degrees C or less.
  • ⁇ Winding at a temperature of 600 ° C to 700 ° C> When the coiling temperature is lower than 600 ° C., precipitates are not sufficiently precipitated, so that solid solution C and solid solution N increase and yield strength increases. Furthermore, a further increase in yield strength occurs due to aging deterioration. For this reason, the coiling temperature is set to 600 ° C. or higher. On the other hand, when the coiling temperature exceeds 700 ° C., the scale of the surface layer grows and tends to cause surface defects. For this reason, winding temperature shall be 700 degrees C or less.
  • the equivalent dislocation density from the surface of the steel sheet before annealing to 50 ⁇ m in the depth direction is 1.0 ⁇ 10 15 m ⁇ 2 or more.
  • the equivalent dislocation density from the surface of the steel plate before annealing to 50 ⁇ m in the depth direction is 1.0 ⁇ 10 15 m ⁇ 2 or more.
  • the crystal grain of the steel plate surface layer after annealing can be made fine. More preferably, it is 1.0 ⁇ 10 16 m ⁇ 2 or more.
  • the upper limit of the equivalent dislocation density is not particularly limited, but is preferably 1.0 ⁇ 10 18 m ⁇ 2 or less from the viewpoint of preventing surface peeling.
  • the method for setting the equivalent dislocation density from the surface of the steel sheet before annealing to 50 ⁇ m in the depth direction to 1.0 ⁇ 10 15 m ⁇ 2 or more is not particularly specified. However, it is difficult to obtain an equivalent dislocation density of 1.0 ⁇ 10 15 m ⁇ 2 or more in the surface layer of the steel sheet in the range of the cold rolling reduction ratio of about 50 to 95% that is normally performed when manufacturing a cold rolled steel sheet. .
  • Examples of a method of setting the equivalent dislocation density from the surface of the steel sheet before annealing to 50 ⁇ m in the depth direction to 1.0 ⁇ 10 15 m ⁇ 2 or more include shot blasting or high strength on a cold-rolled steel sheet after cold rolling.
  • a method of applying a strain imparting process with a brush can be mentioned. Further, as another method for setting the equivalent dislocation density to 1.0 ⁇ 10 15 m ⁇ 2 or more, a cold rolling steel sheet after the cold rolling final stage or after cold rolling is applied at a low pressure ratio by a high roughness roll. The method of performing additional rolling is mentioned.
  • the high roughness roll for example, a roll having a roll roughness Ra of 2.0 to 10.0 ⁇ m can be used.
  • the additional rolling at the low pressure reduction rate can be performed, for example, at a reduction rate of 0.1 to 10%.
  • the equivalent dislocation density can be measured by the following method. A 10 mm ⁇ 10 mm test piece is sampled from each steel plate before annealing, polished from the back surface of the test piece to a plate thickness of 50 ⁇ m, and then the polishing strain layer on the back surface layer is removed with hydrofluoric acid. An X-ray diffraction experiment is performed using this test piece, and the half width of the peak of the (110), (211), (220) crystal plane of the steel sheet is obtained. Using this half width, the non-uniform strain ⁇ of the test piece is obtained by the Williamson-Hall method.
  • the annealing may be performed by a method using either a continuous annealing furnace or a box annealing furnace.
  • the annealing temperature is less than 550 ° C., unrecrystallized grains may remain even if a high equivalent dislocation density is introduced into the steel sheet surface layer.
  • annealing temperature shall be 550 degreeC or more and 700 degrees C or less.
  • the annealing temperature is more preferably 570 ° C. or higher and 680 ° C. or lower.
  • a plating process After annealing, a plating process may be performed.
  • chemical conversion treatment may be performed, or an organic film such as a laminate may be formed.
  • temper rolling it is preferable to perform temper rolling for adjusting the surface roughness.
  • the rolling rate (elongation rate) of temper rolling is preferably about 0.5% to 1.5%.
  • the steel sheet for cans of the present invention described above has low yield strength, excellent workability, excellent surface roughness resistance in surface appearance, and striped defects are suppressed.
  • the steel plate for cans of the present invention can be applied, for example, for a two-piece can.
  • the molten steel having the component composition shown in Table 1 was made into a slab by continuous casting after vacuum degassing treatment.
  • the slab was heated at 1250 ° C., and after the scale was removed, it was roughly rolled to a plate thickness of 40 mm.
  • the steel sheet surface layer was cooled with a scale removing device, and then finish-rolled to a thickness of 3.2 mm and wound around a coil at a predetermined temperature.
  • the wound steel sheet was pickled and cold-rolled.
  • another part of the sample was subjected to shot blasting (shot condition: steel shot (average particle size 0.5 mm) was sprayed at a pressure of 0.5 MPa for 300 seconds).
  • shot blasting shot condition: steel shot (average particle size 0.5 mm) was sprayed at a pressure of 0.5 MPa for 300 seconds).
  • shot blasting shot condition: steel shot (average particle size 0.5 mm) was sprayed at a pressure of 0.5 MPa for 300 seconds.
  • shot blasting shot condition: steel shot (average particle size 0.5 mm) was sprayed at a pressure of 0.5 MPa for 300 seconds.
  • shot blasting shot condition: steel shot (average particle size 0.5
  • the above-mentioned equivalent transition density was measured according to the method described above.
  • the obtained steel sheet was subjected to mechanical property evaluation and crystal grain size measurement.
  • Table 2 also shows the surface roughness Ra ( ⁇ m) of the steel sheet obtained.
  • yield strength (YP), tensile strength (TS) and elongation (El) were evaluated by a tensile test.
  • Tensile properties were measured according to the test method described in JIS Z2241, after being processed into a No. 5 test piece described in JIS Z2201.
  • the crystal grain size the ferrite average crystal grain size was measured by a cutting method based on JIS G0551.
  • a 100 mm diameter circular blank is sampled from the steel sheet, formed into a 14 mm diameter cylindrical shape by five-stage multistage drawing, and then the surface roughness of the can body using a stylus type roughness measuring instrument.
  • Ra was measured, and the evaluation of workability (formability) and the evaluation of surface appearance were evaluated for the rough skin resistance and the suppression of stripe defects.
  • the evaluation of workability was performed by drawing 200 pieces, and the case where no defects such as cracks and wrinkles occurred was evaluated as ⁇ , and the case where the defects were generated was evaluated as ⁇ .
  • the evaluation of the rough skin resistance was evaluated as ⁇ when the surface roughness Ra of the can body portion was less than 0.5 ⁇ m, ⁇ when 0.5 ⁇ m or more and 0.7 ⁇ m or less, and ⁇ when 0.7 ⁇ m or more.
  • the evaluation of the suppression of striped defects those in which defects such as stripes occurred on the processed surface were evaluated as x, and the others were evaluated as ⁇ .
  • Table 2 shows the manufacturing conditions and evaluation results.
  • the examples of the present invention were excellent in workability, had excellent surface roughness resistance in the surface appearance, and were able to suppress striped defects and had performance suitable as steel plates for cans.
  • the comparative example at least one of workability and surface appearance was inferior.
  • the area ratio of unrecrystallized grains on the steel sheet surface exceeds 0.10%, and the average crystal grain size (d1) in the structure from the steel sheet surface to a depth of 50 ⁇ m Since d1 / d2 exceeded 0.8 with respect to the total thickness average crystal grain size (d2), the surface appearance was inferior in skin roughness resistance, and striped defects were generated.
  • Sample C3 had an area ratio of non-recrystallized grains on the steel sheet surface exceeding 0.10%, and the total thickness average crystal grain size (d2) was less than 11.0 ⁇ m. Striped defects occurred.
  • the C content of the steel used exceeds 0.0050 mass%, the area ratio occupied by unrecrystallized grains on the steel sheet surface exceeds 0.10%, and the total thickness average crystal grain size ( Since d2) was less than 11.0 ⁇ m, the workability was poor.
  • Sample E1 had a C content of less than 0.0010 mass% of the steel used, and the area ratio of non-recrystallized grains on the steel sheet surface exceeded 0.10%, so that workability and rough skin resistance were increased. It was inferior to both.
  • Sample F1 the Mn content of the steel used exceeded 0.3% by mass, and the area ratio of non-recrystallized grains on the steel plate surface exceeded 0.10%, so that the workability was poor.

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Abstract

L'invention concerne : une tôle d'acier pour canette qui présente une faible limite d'élasticité, une excellente aptitude au façonnage, et une excellente résistance à la rugosification superficielle en ce qui concerne l'aspect de surface, et dans laquelle les défauts de bande sont supprimés ; et un procédé de fabrication de celle-ci. La tôle d'acier pour canette présente une composition comprenant, en % en masse, 0,0010 à 0,0050 % de C, 0,03 % ou moins de Si, 0,3 % ou moins de Mn, 0,02 % ou moins de P, 0,02 % ou moins de S, 0,01 à 0,10 % d'Al, 0,004 % ou moins de N, 0,01 à 0,06 % de Ti et/ou 0,01 à 0,04 % de Nb, et le reste étant du Fe et des impuretés inévitables. Le rapport de superficie occupé par des grains non recristallisés dans la surface de la tôle d'acier est inférieur ou égal à 0,10 %. La taille moyenne des grains cristallins (d1) dans la structure à partir de la surface de la tôle d'acier jusqu'à une profondeur de 50 µm et la taille moyenne des grains cristallins (d2) dans l'épaisseur globale satisfont la relation d1 ≤ 0,8 × d2, et d2 est supérieur ou égal à 11,0 µm.
PCT/JP2016/001411 2015-03-27 2016-03-14 Tôle d'acier pour canette et son procédé de production Ceased WO2016157761A1 (fr)

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