EP1088905B2 - Stahlblech für ultradünne dosen mit hervorragender anti-falteigenschaften und verfahren zu dessen herstellung - Google Patents

Stahlblech für ultradünne dosen mit hervorragender anti-falteigenschaften und verfahren zu dessen herstellung Download PDF

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Publication number
EP1088905B2
EP1088905B2 EP00915519.3A EP00915519A EP1088905B2 EP 1088905 B2 EP1088905 B2 EP 1088905B2 EP 00915519 A EP00915519 A EP 00915519A EP 1088905 B2 EP1088905 B2 EP 1088905B2
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Prior art keywords
less
diameter
steel sheet
aln
mns
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Expired - Lifetime
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EP00915519.3A
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English (en)
French (fr)
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EP1088905A1 (de
EP1088905B1 (de
EP1088905A4 (de
Inventor
Hidekuni Nippon Steel Corporation Murakami
Masayoshi Nippon Steel Corporation SUEHIRO
Seiichi Nippon Steel Corporation TANAKA
Tetsurou Nippon Steel Corporation TAKESHITA
Hirokazu Nippon Steel Corporation YOKOYA
Toru Nippon Steel Corporation CHICHIKI
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Nippon Steel Corp
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Nippon Steel and Sumitomo Metal Corp
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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
    • C21D8/04—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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0468—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment between cold rolling steps
    • C—CHEMISTRY; METALLURGY
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/041—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 involving a particular fabrication or treatment of ingot or slab
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling

Definitions

  • the present invention relates to a method for producing a steel sheet used as a material for a can produced by drawing, ironing, stretching and succeeding diameter reduction forming as represented by the production of a two-piece can and a method for producing the steel sheet.
  • the present invention provides a steel sheet for an ultra-thin can, capable of being produced with high productivity, small earing and good neck wrinkling resistance and a method for producing the steel sheet.
  • two-piece cans In the field of manufacturing beverage cans and food cans, etc., the production amount of cans wherein bottoms and walls are integrally formed in one body, called two-piece cans, is increasing.
  • a two-piece can In a two-piece can, generally, in order to obtain a required can height, a method for increasing the can wall height by ironing or stretching after drawing process is adopted, as is represented by a method for manufacturing a DI can or a DTR can.
  • JP-A 10 237 550 and JP-A 9 104 920 both relate to the production of thin steel sheets for cams.
  • the present invention provides a method for producing a steel sheet according to claim 1 used for a two-piece can produced by drawing and ironing or stretching, having high drawability and avoiding
  • the anti-wrinkling property is improved, as crystal grain size becomes coarser, as the strength of ⁇ 100 ⁇ plane becomes higher and the strength of ⁇ 111 ⁇ plane becomes lower in crystalline texture, and as precipitates become coarser in size and lower in density.
  • the present invention has been completed by further considering the workability, etc. of a two-piece can annealed at a relatively low temperature for restraining heat-buckle during annealing process.
  • the inventors Based on the finding that the anti-wrinkling property is influenced by the amount and size of AlN and MnS, the inventors have further studied in detail and obtained the result that the anti-wrinkling property can be evaluated by restricting the ratio of N existing as Al nitrides to N content or the size distribution of AlN and MnS. That is, according to the present invention, a steel sheet for a two-piece can with a thickness of 0.19mm or less and having excellent neck wrinkling resistance and anti-earing property can be produced on condition that AlN and MnS satisfy the following requirements:
  • Figure 1 is a graph showing the relationship between the average diameter of MnS, hot-rolling conditions (slab heating temperature and coiling temperature) and a critical diameter reduction ratio.
  • C forms cementite in steel when the content is high.
  • coarse cementite When coarse cementite is exposed on a surface, it may cause the deterioration of the plating properties of a steel sheet. Further, the coarse cementite could be a starting points cracks during ironing, stretching or flange forming in the process for manufacturing a can. It is desirable, therefore, that the upper limit of C content is set to 0.08%.
  • the properties can be markedly improved by setting the upper limit of C to 0.06% or less.
  • a reduction of the carbon content of less than 0.008% for controlling aging property it is not desirable from the aspect of insufficient can strength and the increase of decarburization cost because of the existence of C in solid solution. From these aspects, it is desirable to set C content to at least 0.008%. Further, to obtain a soft material with high ductility desirable for a two-piece can at a low cost without using a vacuum degassing process, it is desirable to limit the C content within the range between 0.02 and 0.04%.
  • N is an important element that controls the formation of nitrides. Too much N generates many nitrides, and hence the object of the present invention is hard to achieve. It is desirable, therefore, the upper limit of N be set to 0.0040%. If N is reduced to 0.0020% or less by sufficiently applying a vacuum degassing treatment, it is further desirable because the amount of nitrides generated is decreased and hence the target properties are improved.
  • the Si content is set to 0.05% or less. Further, more desirably, it should be set to 0.029% or less.
  • the Mn content is set within the range between 0.04 and 0.4%. Further, more desirably, it should be set within the range between 0.15 and 0.25%.
  • the P content is set to 0.04% or less. Further, more desirably, it should be set to 0.010% or less.
  • the S content is set to 0.04% or less. Further, more desirably, it should be set to 0.020% or less.
  • Al is, like N, an important element that controls nitrides, which is an important requirement of the present invention. From this aspect, it is desirable that the Al content is set within the range between 0.02 and 0.10%. Further, more desirably, it should be set within the range between 0.050 and 0.080%.
  • the present invention mainly utilizes Al nitrides as precipitates and does not mainly utilize compounds of B, Ti and V, etc. Therefore, B, Ti and V, etc. are not added intentionally.
  • Nitrides are mainly composed of AlN and hence the following relation must be satisfied; (N existing as AlN)/(N content)> 0.5.
  • N existing as AlN is a value obtained by converting the total amount of AlN into the amount of N, wherein the amount of Al in residuals when a steel sheet is dissolved in an iodine alcohol solution is analyzed and that total amount is regarded as composing AlN.
  • the size distributions of AlN and MnS are important factors for improving neck wrinkling resistance.
  • the present invention is preferable that, for AlN, the ratio of the number of AlN with a diameter of 0.10 ⁇ m or less to the number of AlN with a diameter of at least 0.005 ⁇ m is 10% or less and the average diameter of AlN is 0.01 to 0.10 ⁇ m, and that, for MnS, the ratio of the number of MnS with a diameter of 0.03 ⁇ m or less to the number of MnS with a diameter of at least 0.005 ⁇ m is 50% or less and the average diameter of MnS is 0.03 to 0.40 ⁇ m.
  • the size distribution can also be obtained by photographing the visual field and carrying out image analysis, etc.
  • work hardening behavior of a material including the Bauschinger Effect
  • fine precipitates greatly influence the work hardening behavior of a material.
  • the quantitative and qualitative analyses of fine precipitates are not regarded as perfect even with the latest technologies and could cause large errors. Therefore, the present invention specifies the claims in relation to coarse precipitates in which measuring errors are expected to be reduced.
  • MnS of an elongated shape can occasionally be observed, and for MnS with anisotropic shape, the average of the longest diameter and the shortest diameter is defined as the diameter of the precipitate.
  • the heat history over the overall manufacturing processes is important.
  • the influence of slab heating temperature and coiling temperature is large, and therefore it is necessary to control the slab reheating temperature to within a predetermined range.
  • a slab reheating temperature is determined in combination with a coiling temperature (CT).
  • CT coiling temperature
  • a steel sheet according to the present invention can be obtained without specifying the coiling temperature.
  • the precipitation of MnS during slab heating proceeds by setting a slab reheating temperature at a low temperature of 1150°C or less, the amount of fine MnS, which precipitates with a temperature drop during hot-rolling, is reduced, and thus the same effect as the above-mentioned AlN can be obtained. Further, in this case, it is thought that the coiling temperature need not be specified because the precipitation of AlN is also promoted during slab heating.
  • Cold-rolling reduction ratio is in the range between 82 and 94%, but the claimed range is between 90 and 94%. The figure is defined considering the productivity in producing a thin steel sheet and the suppression of in-plane anisotropy from the aspect of material quality.
  • the productivity of hot rolling goes down and in-plane anisotropy increases because the thickness of a hot band is required to be thinner.
  • the cold-rolling reduction ratio is high, the burden on the cold-rolling process becomes heavy and in-plane anisotropy also increases.
  • Annealing temperature is in the range between the recrystallization temperature and 720°C, but the claimed range is between 650 and 670°C. The reason is that securing recrystallization is necessary for obtaining good ductility and the deterioration of productivity in the annealing process is of concern at a temperature exceeding 720°C.
  • re-cold-rolling reduction ratio (RCR) after annealing is in the range between 1 and 10%. This is because the effect of re-cold-rolling is obtained at a re-cold-rolling reduction ratio of at least 1%, while too high re-cold-rolling reduction ratio causes the deterioration of workability due to the hardening of a material. Further, more desirably, the re-cold-rolling reduction ratio is in the range between 1 and 2%.
  • the effect of the present invention does not disappear even if strengthening elements such as Si, Mn and P, etc. are added in a large quantities, instead of employing 2CR, to increase the strength of a steel sheet.
  • a steel sheet according to the present invention is also used as a substrate for a surface treated steel sheet.
  • the surface treatment does not hurt the effect of the present invention at all.
  • a steel sheet according to the present invention when it is used as a surface treated steel sheet for a can, is usually coated with tin or chromium (tin-free), etc. Further, a steel sheet according to the present invention is also used as a substrate for a laminated steel sheet, which is coated with organic film and has been in use recently, without hurting the effect of the present invention.
  • Cans with a thickness of 125 ⁇ m at the portion where neck-forming is to be performed were produced while maintaining the drawing ratio and ironing ratio constant and the same multi-stage diameter reduction as is applied to conventional actual can manufacturing was applied to the cans and neck wrinkling resistance was evaluated by the value of a critical diameter reduction ratio calculated by the following equation (2) as a threshold of generating wrinkle. Since the allowance of material quality in actual operation becomes larger as the critical diameter reduction ratio becomes higher, wrinkle generation can be suppressed.
  • Critical diameter reduction ratio initial diameter ⁇ diameter at the time of wrinkle generation / initial diameter
  • Heat-buckle was evaluated by the occurrence of heat-buckle when a steel sheet was processed in a continuous annealing line at the temperature of recrystallization temperature + 40°C.
  • Figure 1 shows the relationship between the size distribution of MnS and neck wrinkling resistance for steel sheets with 0.03% of C in weight percent. Steel sheets having MnS size distribution within the range specified by the present invention have good neck wrinkling resistance.
  • the effects of MnS size distribution are separately shown by each slab reheating temperature category. The neck diameter reduction property is improved when slab reheating temperature is 1250°C or less and coiling temperature is at least 690°C even though the size distribution of MnS is almost the same.
  • the rate of wrinkle generation during neck diameter reduction can be reduced. Further, since a steel according to the present invention shows good properties even with an annealing temperature lower than the temperature for a conventional steel, the generation of heat-buckle can be avoided and highly efficient production of a material for an ultra-thin can is made possible.

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

Claims (2)

  1. Verfahren zur Herstellung eines Stahlblechs für eine zweiteilige Dose mit ausgezeichneter Beständigkeit gegen Halsfaltenbildung und ausgezeichneten Zipfelverhinderungseigenschaften, dadurch gekennzeichnet, dass das Stahlblech in Gewichtsprozent enthält:
    C: höchstens 0,08 %,
    Si: höchstens 0,05 %,
    Mn: 0,04 bis 0,4 %,
    P: höchstens 0,04 %,
    S: höchstens 0,04 %,
    Al: 0,02 bis 0,10 % und
    N: höchstens 40 ppm, wobei der Rest Eisen und unvermeidliche Verunreinigungen sind; und durch Durchführen von Warmwalzen bei einer Brammenwiedererwärmungstemperatur im Bereich von 1150 bis 1250 °C und bei einer Wickeltemperatur nach Warmwalzen im Bereich von 690 bis 750 °C, Kaltwalzen mit einem Walzgrad beim Kaltwalzen im Bereich von 90 bis 94 %, Glühen bei einer Temperatur im Bereich von 650 bis 670 °C sowie erneutes Kaltwalzen mit einem Walzgrad beim erneuten Kaltwalzen im Bereich von 1 bis 10 %,
    wobei der mittlere Durchmesser von AlN mit mindestens 0,005 µm Durchmesser von 0,01 bis 0,10 µm beträgt,
    das Verhältnis der Anzahl von AlN mit höchstens 0,01 µm Durchmesser zur Anzahl von AlN mit mindestens 0,005 µm Durchmesser höchstens 10 % beträgt,
    der mittlere Durchmesser von MnS mit mindestens 0,005 µm Durchmesser von 0,03 bis 0,40 µm beträgt,
    das Verhältnis der Anzahl von MnS mit höchstens 0,03 µm Durchmesser zur Anzahl von MnS mit mindestens 0,005 µm Durchmesser höchstens 50 % beträgt,
    die folgende Bedingung erfüllt ist:
    (als AlN vorliegender N)/(N-Gehalt) > 0,5, und
    die Dicke des Stahlblechs höchstens 0,19 mm beträgt.
  2. Verfahren nach Anspruch 1, wobei
    das Stahlblech in Gewichtsprozent enthält:
    C: 0,02 bis 0,04 %,
    Si: höchstens 0,029 %,
    Mn: 0,15 bis 0,25 %,
    P: höchstens 0,010 %,
    S: höchstens 0,020 %,
    Al: 0,050 bis 0,080 % und
    N: höchstens 40 ppm, wobei der Rest Eisen und unvermeidliche Verunreinigungen sind.
EP00915519.3A 1999-04-20 2000-04-13 Stahlblech für ultradünne dosen mit hervorragender anti-falteigenschaften und verfahren zu dessen herstellung Expired - Lifetime EP1088905B2 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP11285299 1999-04-20
JP11285299 1999-04-20
PCT/JP2000/002426 WO2000063453A1 (fr) 1999-04-20 2000-04-13 Tole d'acier tres mince destinee a un contenant en deux morceaux, tres resistante a la formation de plis et cornes d'emboutissage lors de la reduction du diametre du col, et procede de production associe

Publications (4)

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EP1088905A1 EP1088905A1 (de) 2001-04-04
EP1088905A4 EP1088905A4 (de) 2004-12-01
EP1088905B1 EP1088905B1 (de) 2009-10-07
EP1088905B2 true EP1088905B2 (de) 2019-06-05

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EP00915519.3A Expired - Lifetime EP1088905B2 (de) 1999-04-20 2000-04-13 Stahlblech für ultradünne dosen mit hervorragender anti-falteigenschaften und verfahren zu dessen herstellung

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EP (1) EP1088905B2 (de)
JP (1) JP4213870B2 (de)
DE (1) DE60043087D1 (de)
WO (1) WO2000063453A1 (de)

Families Citing this family (1)

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Publication number Priority date Publication date Assignee Title
FR2837500B1 (fr) 2002-03-21 2004-12-03 Usinor Tole ecrouie en acier calme a l'aluminium et procede de fabrication d'un emballage a partir de cette tole

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0521808B1 (de) † 1991-07-04 2002-08-07 Sollac Verfahren zum Herstellen von Tiefziehblechen

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JP2689148B2 (ja) * 1988-11-19 1997-12-10 新日本製鐵株式会社 耳発生の小さい絞り缶用鋼板の製造法
JPH0480345A (ja) * 1990-07-19 1992-03-13 Nippon Steel Corp 加工性、肌荒れ性及びイヤリング性に優れた冷延鋼板及びその製造方法
JP3103268B2 (ja) * 1994-04-22 2000-10-30 新日本製鐵株式会社 耐フルーティング性に優れた容器用鋼板の製造方法
JPH08253820A (ja) * 1995-03-16 1996-10-01 Nisshin Steel Co Ltd 連続焼鈍による耐時効性に優れた缶用薄鋼板の製造方法
JP3975488B2 (ja) * 1995-10-06 2007-09-12 Ｊｆｅスチール株式会社 材質均一性に優れる薄鋼板の製造方法
JP3224732B2 (ja) * 1996-03-28 2001-11-05 川崎製鉄株式会社 耐時効性の良好な冷延鋼板とその製造方法
JP3593235B2 (ja) * 1997-02-26 2004-11-24 新日本製鐵株式会社 成形性に優れた高強度な極薄溶接缶用鋼板の製造方法
JP3740779B2 (ja) * 1997-03-12 2006-02-01 Ｊｆｅスチール株式会社 開蓋性とリベット成形性に優れるイージーオープン缶蓋用鋼板およびその製造方法、ならびにイージーオープン缶蓋
JP3421942B2 (ja) * 1997-07-18 2003-06-30 Ｊｆｅエンジニアリング株式会社 缶用冷間圧延鋼板を製造するための鋳片

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0521808B1 (de) † 1991-07-04 2002-08-07 Sollac Verfahren zum Herstellen von Tiefziehblechen

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
GÉRARD BÉRANGER ET AL, LE LIVRE DE L'ACIER, September 1994 (1994-09-01), PARIS, pages 1298 - 1300 †

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DE60043087D1 (de) 2009-11-19
EP1088905A1 (de) 2001-04-04
JP4213870B2 (ja) 2009-01-21
WO2000063453A1 (fr) 2000-10-26
EP1088905B1 (de) 2009-10-07
EP1088905A4 (de) 2004-12-01

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