EP1741800A1 - Feuille d'acier pour boîte et sa méthode de production - Google Patents

Feuille d'acier pour boîte et sa méthode de production Download PDF

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Publication number
EP1741800A1
EP1741800A1 EP05736903A EP05736903A EP1741800A1 EP 1741800 A1 EP1741800 A1 EP 1741800A1 EP 05736903 A EP05736903 A EP 05736903A EP 05736903 A EP05736903 A EP 05736903A EP 1741800 A1 EP1741800 A1 EP 1741800A1
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Prior art keywords
weight
steel sheet
steel
less
strength
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EP05736903A
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German (de)
English (en)
Inventor
Yuka IP Dept. JFE Steel Corp. Nishihara
Katsumi IP Dept. JFE Steel Corp. Kojima
Hiroki IP Dept. JFE Steel Corp. Iwasa
Eisuke IP Dept. JFE Steel Corp. Hotta
Teruhiro IP Dept. JFE Steel Corp. Saito
Kazuhiro IP Dept. JFE Steel Corp. Matsumoto
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JFE Steel Corp
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JFE Steel Corp
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Publication of EP1741800A1 publication Critical patent/EP1741800A1/fr
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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
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0278—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment 

Definitions

  • the present invention relates to thin steel sheets (hereinafter also referred to as can steel sheets) suitable for surface-treated steel sheets for can manufacture, such as tinplates and electrically chromium-coated steel sheets, and also to methods for manufacturing the steel sheets.
  • can steel sheets thin steel sheets (hereinafter also referred to as can steel sheets) suitable for surface-treated steel sheets for can manufacture, such as tinplates and electrically chromium-coated steel sheets, and also to methods for manufacturing the steel sheets.
  • can steel sheets are therefore difficult to apply to portions requiring strength, such as bodies of draw-redraw cans (hereinafter also referred to as DRD cans) and welded cans. Accordingly, can steel sheets have been desired to have a smaller thickness with sufficient strength.
  • DR double reduction
  • second cold rolling follows annealing.
  • a steel sheet manufactured by this method has an elongation of only several percent and poor formability.
  • the steel sheet chronically causes, for example, surface flaws and surface dirt which are extremely difficult to completely avoid.
  • Japanese Unexamined Patent Application Publication No. 2001-107186 discloses that large amounts of C and N are added and hardened by baking to achieve can steel sheets having high strength equivalent to that of a steel sheet manufactured by DR.
  • the steel sheet has high yield stress after the baking of coating, namely 550 MPa, and the hardness thereof is adjustable according to the amount of N added and heat-treatment conditions. This method is effective for achieving higher strength, though it may cause yield elongation due to strain aging even after temper rolling, and thus may cause stretcher strains during forming.
  • Japanese Unexamined Patent Application Publication No. 8-325670 proposes a method for manufacturing a steel sheet having a good balance between strength and elongation by a combination of precipitation strengthening with niobium carbide and crystal grain refinement strengthening with the carbonitrides of Nb, Ti, and B.
  • the present inventors produced a steel sheet containing 0.025% by weight of Nb according to this method.
  • the resultant steel sheet however, had low tensile strength, namely 510 MPa, and thus could not reach the strength of a steel sheet manufactured by the currently available method, namely DR.
  • Japanese Unexamined Patent Application Publication No. 5-345926 proposes a method for manufacturing a steel sheet reaching a strength level of 60 to 75 in terms of Rockwell hardness (HR30T) (see JIS G 3303) by solid solution strengthening with P and crystal grain refinement strengthening with the carbonitrides of Nb, Ti, and B.
  • HR30T Rockwell hardness
  • Japanese Unexamined Patent Application Publication No. 2000-119802 proposes a method for manufacturing a high-strength steel sheet having a tensile strength of 540 MPa or more by precipitation strengthening through the addition of alloy elements such as Nb.and Ti. Either method, however, depends on temper rolling at a high reduction rate, namely about 10% to 30%, to achieve high strength, and thus has difficulty in providing strength equivalent to that of a steel sheet manufactured by DR (hereinafter also referred to as DR steel sheets).
  • Japanese Unexamined Patent Application Publication No. 2003-34825 proposes a method in which low-carbon steel is subjected to hot rolling in the ⁇ + ⁇ region, rapid cooling, and annealing at a specified heating temperature.
  • This method can provide a steel sheet having a tensile strength of 600 MPa and a total elongation of 30% or more. Such strengthening by rapid cooling, however, leads to high operating cost.
  • An object of the present invention is to provide a can steel sheet having strength equivalent to that of a DR steel sheet and elongation superior to that of a DR steel sheet, and also to provide a method for manufacturing the can steel sheet.
  • the present invention provides a can steel sheet containing 0.04% to 0.1% by weight of C, 0.002% to 0.012% by weight of N, 0.5% to 1.5% by weight of Mn, 0.01% to 0.15% by weight of P, 0.01% to 0.5% by weight of Si, more than 0.025% to 0.1% by weight of Nb, 0.01% or less by weight of Al, and 0.01% or less by weight of S, and the balance is Fe and incidental impurities.
  • This can steel sheet substantially has a single-phase ferrite structure having an average crystal grain size of 7 ⁇ m or less.
  • the present invention further provides a method for manufacturing a can steel sheet.
  • This method includes hot-rolling a steel at a finish temperature of an Ar 3 transformation point or more, coiling the steel at a coiling temperature of 560°C to 600°C, pickling the steel, cold-rolling the steel at a reduction rate of 80% or more, and annealing the steel at 700°C to 820°C.
  • the steel used contains 0.04% to 0.1% by weight of C, 0.002% to 0.012% by weight of N, 0.5% to 1.5% by weight of Mn, 0.01% to 0.15% by weight of P, 0.01% to 0.5% by weight of Si, more than 0.025% to 0.1% by weight of Nb, 0.01% or less by weight of Al, and 0.01% or less by weight of S, and the balance is Fe and incidental impurities.
  • the present invention further provides a can steel sheet having high strength and high elongation.
  • This can steel sheet contains 0.04% to 0.1% by weight of C, 0.002% to 0.012% by weight of N, 0.5% to 1.5% by weight of Mn, 0.010% to 0.15% by weight of P, 0.01% to 0.5% by weight of Si, 0.025% to 0.1% by weight of Nb, 0.01% or less by weight of Al, and 0.01% or less by weight of S, and the balance is Fe and incidental impurities.
  • the can steel sheet substantially has a single-phase ferrite structure, and has an average ferrite crystal grain size of 7 ⁇ m or less and a thickness of 0.2 mm or less.
  • the present inventors have focused on a combination of solid solution strengthening, precipitation strengthening, and grain refinement strengthening to strengthen a steel sheet. As a result, the inventors have found that higher strength can be achieved with no decrease in elongation by reducing the size of crystal grains through the addition of proper amounts of P and Mn, as solid solution strengthening elements, and a proper amount of Nb, as a precipitation strengthening element and a grain refinement strengthening element. The inventors have further found that the strength and the elongation can be balanced at high levels with a substantial single-phase ferrite structure having a specified average ferrite crystal grain size.
  • a high-strength can steel sheet is a thin steel sheet suitable as, for example, a raw plate for a surface-treated steel sheet such as a tinplate (electrically tin-coated steel sheets) and an electrically chromium-coated steel sheet.
  • a can steel sheet having high strength and high elongation according to the present invention contains specified amounts of elements described below as a solid solution strengthening element, a precipitation strengthening element, and/or a grain refinement strengthening element.
  • the can steel sheet substantially has a single-phase ferrite structure having an average crystal grain size of 7 ⁇ m or less. These conditions are the most important requirements for the present invention which allow the manufacture of a can steel sheet having a tensile strength of 550 MPa or more and an elongation exceeding 10%.
  • Such a high-strength, high-elongation steel sheet may be manufactured by hot rolling at a finish temperature of an Ar 3 transformation point or more, coiling at a coiling temperature of 560°C to 600°C, pickling, cold rolling at a reduction rate of 80% or more, and annealing at 700°C to 820°C.
  • the chemical composition of the steel is specified for the following reasons. In the present application, all percentages for the composition of the steel are expressed in terms of weight. C: 0.04% to 0.1%
  • the steel sheet requires a crystal grain size of 7 ⁇ m or less to achieve a tensile strength of 550 MPa or more and an elongation exceeding 10% after annealing.
  • the amount of C added is important to achieve such properties; C is one of the main requirements for the present invention. In particular, a required amount of carbon must be assigned to precipitation because the strength and the grain size depend largely on the amount and density of carbide. In addition, the amount of C added is 0.04% or more in consideration of strengthening by the solid solution of C. If, on the other hand, the amount of C added exceeds 0.1%, a pearlite phase precipitates in the second phase and decreases the elongation. Accordingly, the content of C is 0.04% to 0.1%.
  • Si 0.01% to 0.5%
  • Si is an element for strengthening the steel sheet by solid solution strengthening, though an excessive amount of Si added significantly impairs corrosion resistance. Accordingly, the content of Si is 0.01% to 0.5%.
  • the content of Si is preferably 0.01% to 0.3% to further inhibit impairment in the corrosion resistance.
  • Mn 0.5% to 1.5%
  • Mn is an element for increasing the strength of the steel sheet by solid solution strengthening, reducing the size of crystal grains, and further increasing the strength of the steel sheet by grain refinement strengthening. Mn is one of the main requirements for the present invention. The above effects appear significantly by adding 0.5% or more of Mn. An excessive amount of Mn added, however, impairs the corrosion resistance. Accordingly, the content of Mn is 0.5% to 1.5%.
  • the content of Mn is preferably 0.5% to 1.0% to inhibit a large increase in recrystallization temperature.
  • P 0.01% to 0.15%
  • P is an element having a high solid solution strengthening ability, and is therefore one of the main requirements for the present invention. This effect appears significantly by adding 0.01% or more of P. An excessive amount of P added, however, impairs the corrosion resistance of the steel sheet. Accordingly, the content of P is 0.01% to 0.15%.
  • the content of P is preferably 0.01% to 0.1% to further inhibit impairment in the corrosion resistance.
  • S 0.01% or less The content of S is preferably minimized because the element occurs in the steel as an inclusion which is disadvantageous in view of the elongation and corrosion resistance of the steel sheet.
  • the content of S is 0.01% or less, usually about 0.0001% to 0.01%.
  • Al 0.01% or less
  • An increase in the content of Al raises the recrystallization temperature, and the annealing temperature must be raised accordingly.
  • a rise in annealing temperature increases the amount of A1N formed and decreases the amount of solid solution of N, thus decreasing the strength of the steel sheet.
  • the annealing temperature must be raised because the recrystallization temperature rises due to other elements added to increase the strength of the steel sheet.
  • the rise in recrystallization temperature due to Al is preferably minimized.
  • the content of Al is 0.01% or less, usually about 0.003% to 0.01%.
  • N 0.002% to 0.012% N is deliberately added because the element has a high solid solution strengthening ability to increase the strength of the steel sheet.
  • the effective amount of N required for increasing the strength is 0.002% or more.
  • An excessive amount of N added causes the problem of strain aging of the steel sheet. Accordingly, the content of N is 0.002% to 0.012% Nb: more than 0.025% to 0.1% Nb is one of the main requirements for the present invention.
  • This element which has a high carbide-forming ability, precipitates fine carbide grains to increase the strength of the steel sheet. In addition, the element refines the carbide grains to increase the strength of the steel sheet.
  • Fig. 1 illustrates the relationship between the amount of Nb added and the strength of the can steel sheet when Nb is added together with Mn as a solid solution element.
  • Fig. 1 shows that the addition of Nb together with Mn as a solid solution element provides a larger increase in the strength of the steel sheet than the intrinsic effect of solid solution strengthening. The possible cause is described below.
  • the addition of the solid solution element (Mn in this example) together with Nb precipitates Nb-C which suppresses the diffusion of the solid solution element (Mn in this example) and thus inhibits the growth of recrystallized grains in annealing. That is, the solid solution element itself achieves the effect of grain refinement strengthening which adds to the effect of solid solution strengthening. This effect starts to appear significantly when the amount of Nb added exceeds 0.025%.
  • Nb raises the recrystallization temperature. If the amount of Nb added exceeds 0.1%, the steel sheet hardens significantly in hot rolling and thus deteriorates in formability in cold rolling.
  • the content of Nb is more than 0.025% to 0.1%.
  • the content of Nb is preferably more than 0.025% to 0.05% in view of formability in cold rolling.
  • the steel sheet according to the present invention substantially has a single-phase ferrite structure. Even a steel sheet containing, for example, about 1% of cementite is determined to substantially have a single-phase ferrite structure as long as the sheet provides the operation and effects of the present invention.
  • the present inventors have studied the balance between the strength and elongation of steel sheets having single-phase ferrite structures with varying average ferrite crystal grain sizes. This study has found that a high-strength steel can be achieved with no decrease in elongation if the average ferrite crystal grain size is 7 ⁇ m or less. The study has also found that an average crystal grain size exceeding 7 ⁇ m results in a poor surface appearance after can manufacture. Such phenomena are associated with extreme variations in surface roughness which occurred particularly on two-piece cans, though the positions and degrees thereof varied. Accordingly, the average ferrite crystal grain size is 7 ⁇ m or less. The average ferrite crystal grain size is measured by, for example, an intercept method according to ASTM.
  • the can steel sheet according to the present invention preferably has a thickness of 0.2 mm or less to achieve a higher cold rolling rate and a tensile strength of 550 MPa or more.
  • a molten steel with the above chemical composition is prepared with, for example, a converter, and is cast into a rolling stock by, for example, continuous casting.
  • the resultant rolling stock is subjected to hot rolling.
  • the finish temperature must be set to an Ar 3 transformation point or more to provide a steel sheet in the single-phase ⁇ region.
  • the rolling stock preferably has a low temperature before the hot rolling to refine crystal grains more readily, though the finish rolling temperature must be set in the single-phase ⁇ region. Accordingly, the temperature of the rolling stock is preferably 1,150°C to 1,300°C at the beginning of the rolling.
  • the coiling temperature must be set to 560°C to 600°C to achieve a crystal grain size of 7 ⁇ m or less and thus enhance the strength of the steel sheet after annealing. If the coiling temperature is more than 600°C, coarse crystal grains are produced. If, on the other hand, the coiling temperature in the hot rolling is less than 560°C, the solid solution of N and C remain in the hot-rolled steel sheet and thus impair the formation of a desired aggregate structure in recrystallization annealing after cold rolling.
  • the steel sheet After subsequent pickling, the steel sheet is subjected to cold rolling at a reduction rate of 80% or more to develop an aggregation texture after annealing and significantly refine crystal grains. Simultaneously, the steel sheet can achieve a more uniform ferrite structure. A tensile strength of 550 MPa or more is difficult to achieve at reduction rates below 80%.
  • the thickness of the steel sheet after the cold rolling is preferably 0.2 mm or less to provide a reduction rate of 80% or more.
  • the steel sheet is then subjected to annealing in the soaking area of 700°C to 820°C.
  • the annealing must be performed at the recrystallization temperature or more of the steel sheet to provide good formability, and must be performed at 700°C or more to provide a more uniform structure.
  • temper rolling is preferably performed to adjust the surface shape of the steel sheet.
  • the temper rolling rate is preferably 1.5% or less, more preferably 0.5% to 1.5%, to prevent a decrease in elongation by excessive work hardening.
  • the tensile strength may be controlled to a target value according to the composition, the coiling temperature in the hot rolling, the annealing temperature, and the cold rolling rate.
  • the steel slabs were reheated at 1,200°C and were subjected to hot rolling at finish rolling temperatures and coiling temperatures shown in Table 2. After subsequent pickling, cold rolling was performed at reduction rates shown in Table 2 to produce thin steel sheets having a thickness of 0.2 mm.
  • the resultant thin steel sheets were subjected to annealing in a continuous annealing furnace for 30 seconds at heating temperatures and soaking temperatures shown in Table 2. The steel sheets were then cooled at about 10°C/s to 15°C/s by a common method to produce can steel sheets.
  • the can steel sheets were subjected to temper rolling at a reduction rate of about 1.5% and were continuously subjected to normal chromium plating to produce electrically chromium-coated steel sheets.
  • the annealing temperatures which were adjusted according to the amount of Nb added, were kept at the values shown in Table 2.
  • test and test method are as follows.
  • the tensile test was performed with JIS No. 5 tensile test pieces to measure the yield points, tensile strength, and elongation thereof. Also, the Rockwell hardness was measured.
  • the crystal structures were examined by polishing samples, corroding the crystal grain boundaries thereof with nital, and observing them by optical microscopy.
  • the average crystal grain sizes of the above crystal structures observed were measured by an intercept method according to ASTM.
  • Table 3 shows that the steels of Examples 1 to 9 had a single-phase ferrite structure with an average crystal grain size of 7 ⁇ m or less, and thus excelled in both strength and elongation.
  • the type of steel used was limited to the steel a of Example 1 shown in Table 1 to examine the effect of differences in production conditions.
  • Example 1 Electrically chromium-coated steel sheets were produced with the steel a under the production conditions of Examples 1, 10, and 11 and Comparative Example 9 shown in Table 2. Other conditions followed the description of Example 1. The same tests as in Example 1 were made on the resultant electrically chromium-coated steel sheets. The results are listed in Table 3.
  • Table 3 shows that a single-phase ferrite structure with an average crystal grain size of 7 ⁇ m or less can be achieved under the production conditions of Invention Examples 1, 10, and 11 to provide a steel sheet having a tensile strength of 550 MPa or more with no decrease in elongation.
  • the steel sheet produced under the conditions of Comparative Example 9 had an average ferrite crystal grain size exceeding 10 ⁇ m. This steel sheet had high elongation, but exhibited lower strength.
  • the steel sheet of Comparative Example 7 had high strength, but requires rapid heating and rapid cooling before and after annealing. This steel sheet is therefore difficult to manufacture with conventional equipment.
  • Example 1 Type of steel C Si Mn P S N Nb Al
  • Example 1 a 0.05 0.01 0.5 0.04 0.01 0.006 0.03 0.01
  • Example 2 b 0.05 0.01 1.0 0.04 0.01 0.006 0.03 0.01
  • Example 3 c 0.05 0.01 0.5 0.075 0.01 0.006 0.03 0.01
  • Example 4 d 0.05 0.01 0.5 0.04 0.01 0.006 0.05 0.01
  • Example 5 e 0.05 0.2 0.5 0.04 0.01 0.006 0.03 0.01
  • Example 6 f 0.04 0.01 1.0 0.075 0.01 0.006 0.03 0.01
  • Example 7 g 0.04 0.01 1.0 0.075 0.01 0.01 0.03 0.01
  • Example 8 h 0.04 0.01 1.0 0.01 0.01 0.006 0.03 0.01
  • Example 9 i 0.04 0.01 1.0 0.075 0.01 0.002 0.05 0.01 Comparative example 1 j 0.05 0.
  • the present invention can provide a can steel sheet having a tensile strength of 550 MPa or more and an elongation exceeding 10% and a method for manufacturing the can steel sheet.
  • This steel sheet can be applied to parts such as bodies of, for example, DRD cans and welded cans.
  • the strength of the steel sheet is enhanced by a combination of solid solution strengthening with many elements and precipitation strengthening with Nb and grain refinement strengthening with Nb.
  • a target tensile strength can therefore be reliably achieved at a reduction rate of 1.5% or less in temper rolling after annealing.
  • the steel sheet which contains low amounts of C and N, causes no yield elongation due to strain aging. Accordingly, the steel sheet can make a significant social contribution as a thin steel sheet suitable for a surface-treated steel sheet such as a tinplate and an electrically chromium-coated steel sheet.

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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)
EP05736903A 2004-04-27 2005-04-26 Feuille d'acier pour boîte et sa méthode de production Withdrawn EP1741800A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2004131537 2004-04-27
PCT/JP2005/008399 WO2005103316A1 (fr) 2004-04-27 2005-04-26 Feuille d'acier pour boîte et sa méthode de production

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EP1741800A1 true EP1741800A1 (fr) 2007-01-10

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EP (1) EP1741800A1 (fr)
CN (1) CN1946866A (fr)
MX (1) MXPA06012304A (fr)
TW (1) TW200540284A (fr)
WO (1) WO2005103316A1 (fr)

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EP2650396A4 (fr) * 2010-12-06 2014-07-23 Nippon Steel & Sumitomo Metal Corp Tôle en acier destinée aux revêtements inférieurs de bombes aérosol et son procédé de fabrication
EP2138596B1 (fr) 2007-04-26 2015-07-29 JFE Steel Corporation Feuille d'acier pour une utilisation dans une boîte métallique, et son procédé de fabrication
EP2128289B1 (fr) 2007-02-28 2016-08-10 JFE Steel Corporation Tôle d'acier pour boîtes de conserve, tôle d'acier laminé à chaud à utiliser comme métal de base et procédés de fabrication des deux types de tôle
US9908566B2 (en) 2012-05-08 2018-03-06 Tata Steel Ijmuiden B.V. Automotive chassis part made from high strength formable hot rolled steel sheet
EP3255168B1 (fr) 2015-03-25 2020-08-19 JFE Steel Corporation Tôle d'acier à haute résistance, et procédé de fabrication de celle-ci
US10941456B2 (en) 2016-02-29 2021-03-09 Jfe Steel Corporation Steel sheet for can and method for manufacturing the same
EP3845678A4 (fr) * 2018-08-30 2022-01-19 JFE Steel Corporation Tôle d'acier de canette et son procédé de production
US11965224B2 (en) 2020-02-17 2024-04-23 Nippon Steel Corporation Steel sheet for can and manufacturing method thereof
US12129535B2 (en) 2018-12-20 2024-10-29 Jfe Steel Corporation Steel sheet for cans and method of producing same

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JP5262242B2 (ja) * 2008-03-31 2013-08-14 Ｊｆｅスチール株式会社 製缶用鋼板の製造方法
CN102766800A (zh) * 2011-05-05 2012-11-07 上海梅山钢铁股份有限公司 一种硬质镀锡基板瓶盖用钢及其生产方法
JP5794004B2 (ja) * 2011-07-12 2015-10-14 Ｊｆｅスチール株式会社 フランジ加工性に優れる高強度缶用鋼板およびその製造方法
MY177004A (en) * 2014-08-29 2020-09-01 Jfe Steel Corp Steel sheets for cans and methods for manufacturing the same
CN105112776A (zh) * 2015-08-25 2015-12-02 上海梅山钢铁股份有限公司 一种含磷低碳冷轧硬质镀锡钢板及其生产方法
KR101899681B1 (ko) * 2016-12-22 2018-09-17 주식회사 포스코 고항복비형 초고강도 냉연강판 및 그 제조방법
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EP2128289B1 (fr) 2007-02-28 2016-08-10 JFE Steel Corporation Tôle d'acier pour boîtes de conserve, tôle d'acier laminé à chaud à utiliser comme métal de base et procédés de fabrication des deux types de tôle
EP2138596B1 (fr) 2007-04-26 2015-07-29 JFE Steel Corporation Feuille d'acier pour une utilisation dans une boîte métallique, et son procédé de fabrication
US9879332B2 (en) 2008-03-19 2018-01-30 Jfe Steel Corporation Method of manufacturing high-strength steel sheet for a can
EP2253729B1 (fr) 2008-03-19 2015-07-29 JFE Steel Corporation Feuille de métal haute résistance pouvant être utilisée dans les boîtes de conserve, et son procédé de fabrication
EP2253729A4 (fr) * 2008-03-19 2014-01-01 Jfe Steel Corp Feuille de métal haute résistance pouvant être utilisée dans les boîtes de conserve, et son procédé de fabrication
US9315877B2 (en) 2010-12-06 2016-04-19 Nippon Steel & Sumitomo Metal Corporation Steel sheet for bottom covers of aerosol cans and method for producing same
EP2650396A4 (fr) * 2010-12-06 2014-07-23 Nippon Steel & Sumitomo Metal Corp Tôle en acier destinée aux revêtements inférieurs de bombes aérosol et son procédé de fabrication
US9908566B2 (en) 2012-05-08 2018-03-06 Tata Steel Ijmuiden B.V. Automotive chassis part made from high strength formable hot rolled steel sheet
EP3255168B1 (fr) 2015-03-25 2020-08-19 JFE Steel Corporation Tôle d'acier à haute résistance, et procédé de fabrication de celle-ci
US10941456B2 (en) 2016-02-29 2021-03-09 Jfe Steel Corporation Steel sheet for can and method for manufacturing the same
EP3845678A4 (fr) * 2018-08-30 2022-01-19 JFE Steel Corporation Tôle d'acier de canette et son procédé de production
US12129535B2 (en) 2018-12-20 2024-10-29 Jfe Steel Corporation Steel sheet for cans and method of producing same
US11965224B2 (en) 2020-02-17 2024-04-23 Nippon Steel Corporation Steel sheet for can and manufacturing method thereof

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WO2005103316A1 (fr) 2005-11-03
MXPA06012304A (es) 2007-01-17
TW200540284A (en) 2005-12-16
CN1946866A (zh) 2007-04-11

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