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EP1389639B1 - Stahlblech mit guter Biegbarkeit - Google Patents

Stahlblech mit guter Biegbarkeit Download PDF

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Publication number
EP1389639B1
EP1389639B1 EP03254606A EP03254606A EP1389639B1 EP 1389639 B1 EP1389639 B1 EP 1389639B1 EP 03254606 A EP03254606 A EP 03254606A EP 03254606 A EP03254606 A EP 03254606A EP 1389639 B1 EP1389639 B1 EP 1389639B1
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EP
European Patent Office
Prior art keywords
mass
steel sheet
less
retained austenite
ferrite
Prior art date
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EP03254606A
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English (en)
French (fr)
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EP1389639A3 (de
EP1389639A2 (de
Inventor
Shushi c/o Kobe Steel Ltd. Ikeda
Koichi c/o Kobe Steel Ltd. Makii
Hiroshi c/o Kobe Steel Ltd Akamizu
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Kobe Steel Ltd
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Kobe Steel Ltd
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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
    • 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
    • C21D8/0273—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
    • 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
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/20—Isothermal quenching, e.g. bainitic hardening
    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/003—Cementite
    • 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

Definitions

  • the present invention relates to a high-strength steel sheet with excellent bendability, especially tight bendability (ultimate deformability). More particularly, the present invention relates to a high-strength steel sheet which exhibits excellent bendability despite its high or ultra-high strength ranging from 600 to 1400 MPa.
  • a steel sheet in which strength and ductility stand together. It is a steel sheet of ferrite-martensite dual phase (DP) in which the ferrite matrix contains the microstructure composed mainly of martensite which has transformed at low temperatures (disclosed in, for example, Japanese Patent Laid-open No. 122820/1980 ).
  • DP ferrite-martensite dual phase
  • This steel sheet is excellent in ductility as well as shape freezing properties in press working. The latter is attributable to a large number of free dislocations which appear in the region where martensite forms, and such dislocations eliminate yield elongation, thereby reducing yield stress. With a properly controlled microstructure, the steel sheet will have both high tensile strength (TS) and high elongation (El).
  • retained austenite steel sheet (or TRIP steel sheet) with improved ductility. It contains retained austenite in the structure so that it undergoes transformation induced plastic deformation during working.
  • Japanese Patent Laid-open No. 43425/1985 discloses a dual-phase steel sheet with high strength as well as excellent ductility. This steel sheet is composed of no less that 10 vol% of ferrite and no less than 10 vol% of retained austenite, with the remainder being bainite or martensite or a mixture thereof.
  • retained austenite produces the effect of working-induced transformation and soft ferrite produces the effect of high ductility.
  • ferrite and retained austenite contribute to ductility and bainite or martensite contributes to strength.
  • EP 1 201 780 describes a steel sheet excellent in burring workability having a microstructure being a compound structure having ferrite as a main phase and martensite or retained austenite as the second phase, the quotient of the volume percentage of the second phase divided by the average grain size of the second phase being 3 or more and 12 or less, and the quotient of the average hardness of the ferrite being 1.5 or more and 7 or less; or a compound structure steel sheet excellent in burring workability having the microstructure being a compound structure having ferrite as the main phase and martensite or retained austenite mainly as the second phase, the average grain size of the ferrite being 2 ⁇ m or more and 20 ⁇ m or less, the quotient of the average grain size of the second phase divided by the average grain size of the ferrite being 0.05 or more and 0.8 or less, and the carbon concentration in the second phase being 0.2% or more and 3% or less.
  • EP 0 707 087 disclosed a high-strength steel sheet adapted for deep drawing and a process for producing the same.
  • This steel is produced by specifying the inlet side temperature in hot rolling, and controlling the conditions of annealing, cooling, and bainitic transformation.
  • the steel comprises ferrite as the principal phase, and has a composite structure containing at least 3 vol% of austenite, bainite and martensite.
  • JP 11-189839 provides a high strength steel plate exhibiting high impact energy absorptivity at the time of collision of a front side member, etc., and its production.
  • the steel plate as a final product has a structure composed of a microstructure which contains ferrite and bainite and where either of them is used as a principal phase and they form a conjugated structure together with a third phase containing retained austenite by 3-50% by volume fraction.
  • All the steel sheets mentioned above are characterized by excellent elongation properties (especially uniform elongation).
  • TRIP steel sheets benefit from very high elongation and very good formability (for stretching and deep drawing) owing to retained austenite therein.
  • they are generally inferior to solid-solution strengthened steels in local deformation properties (bendability and bore-expandability) and unltimate deformation properties (tight bendability).
  • good bending properties are essential for steel sheets for press forming in the automobile industry, there have been no steel sheets developed so far which meet these requirements.
  • the present invention was completed in view of the foregoing. It is an object of the present invention to provide a high-strength steel sheet with excellent bendability, especially tight bendability, despite its high or ultra-high strength ranging from 600 to 1400 MPa.
  • the present invention provides a steel sheet with excellent bendability comprising:
  • the present invention constructed as mentioned above provides a high-strength steel sheet which exhibits excellent bendability even though its strength as high as 600 to 1400 MPa. This steel sheet is suitable for automobiles.
  • TRIP steel sheets exhibit excellent bendability.
  • the present invention is based on this finding.
  • the condition of quantity of carbide is defined in terms of number of the carbide grains.
  • the steel sheet according to the present invention is characterized by the minimal content of carbide existing between retained austenite and ferrite, which is specified by the number of carbide grains no more than 40 per 2000 ⁇ m 2 . With the number of carbide grains exceeding 40, the resulting steel sheet is poor in bendability (especially tight bendability).
  • the number of carbide grains should preferably be no more than 30.
  • the steel sheet according to the present invention should also have an adequately controlled structure so that it meets requirements for high strength as well as good elongation.
  • the structure should be composed mainly of retained austenite (5-30 area%) and ferrite (no less than 50 area%). This limitation is based on the following.
  • Retained austenite should be present in an amount of 5 area% (preferably no less than 8 area%) so that it helps increase total elongation. With an amount in excess of 30 area%, retained austenite adversely affects bendability. Therefore, the upper limit should be 30 area%, preferably no more than 20 area%.
  • the steel sheet according to the present invention should contain ferrite in an amount no less than 50 area% so that it exhibits good ductility.
  • the steel sheet according to the present invention contains retained austenite and ferrite which constitute the main structure (accounting for no less than 70 area%). It may additionally contain bainite and martensite, which constitute the secondary structure, in an amount not harmful to the function of the present invention. These minor components inevitably remain in the structure during steel production. The amount of martensite should preferably be as small as possible.
  • TRIP steel sheets undergo heat treatment (after hot rolling.and cold rolling) in the following manner.
  • the work is heated and kept at a temperature higher than A 1 point and lower than A 3 point for about 60-180 seconds.
  • the work is cooled to a temperature in the zone for bainite transformation (for example, about 400 ⁇ 50°C) at an average cooling rate in excess of 10°C/s.
  • the work is kept at this temperature for about 300 seconds so as to stabilize the gamma phase with an increased C concentration therein and to ensure a prescribed amount of retained austenite.
  • Heat treatment in this manner causes the C concentration to vary greatly from the inside to the outside of the retained gamma phase. This in turn gives rise to carbide, thereby deteriorating bendability.
  • the steel sheet containing carbide in controlled form may be obtained by the manufacturing method which includes a step of keeping the work at a temperature in the zone for ferrite transformation (for example, about 700 ⁇ 30°C) for a prescribed period of time in the course of cooling from the retention temperature not less than A 1 point and not more than A 3 point to the temperature range of bainite transformation.
  • this method requires that heat treatment be carried out in two stages so as to reduce difference in C concentration in the inside and outside of the retained gamma phase and to suppress formation of carbide between retained austenite and ferrite.
  • the temperature zone for ferrite transformation overlaps with the temperature zone for pearlite transformation and hence keeping the work at that temperature for an excessively long period of time permits the pearlite structure to separate out, thereby deteriorating the characterstic properties. Therefore, it is necessary to keep the work at a heating temperature for an adequate length of time, which is about 10-30 seconds.
  • this heat treatment may be carried out as part of the annealing step that follows hot rolling.
  • the conditions of the hot rolling and cold rolling that precede the heat treatment are not specifically limited. They may be properly selected among ordinary conditions. Also, the cooling rates after the heat treatments may be controlled adequately. For example, the average cooling rate in the case where the work is kept at a temperature in the zone for ferrite transformation for a prescribed period time and then cooled to a temperature in the zone for bainite transformation is preferably larger than 10°C/s so as to prevent the formation of carbide.
  • the retained austenite steel sheet according to the present invention should have the specific structure and the controlled number of carbide grains as mentioned above so that it exhibits the desired properties. It is desirable to control the amount of fundamental components (such as C, Si, Al, Mn, P, and S) as follows.
  • fundamental components such as C, Si, Al, Mn, P, and S
  • C is an essential element for high strength and for ensuring retained austenite.
  • C is an important element for obtaining an adequate amount of C in the austenite phase and for making a desired amount of the austenite phase remain at room temperature.
  • the content of C to produce these effects should be no less than 0.06 mass%.
  • Si + Al from 0.5 mass% to 3 mass%
  • Si and Al effectively prevent the retained austenite from decomposing to form carbide.
  • Si is also useful for solid solution strengthening.
  • the total amount of Si and Al necessary for these effects is no less than 0.5 mass%, preferably no less than 0.7 mass%, more preferably no less than 1 mass%. Total amount of the elements exceeding 3 mass% makes the effects saturated. Excess Si and Al are wasted without any additional effect, and they will cause hot shortness.
  • the upper limit is 3 mass%, preferably 2.5 mass%, more preferably 2 mass%.
  • Mn from 0.5 mass% to 3 mass%
  • Mn stabilizes austenite to give retained austenite as desired.
  • the amount of Mn necessary for this effect is no less than 0.5 mass%, preferably no less than 0.7 mass%, more preferably no less than 1 mass%. Excess Mn produces an adverse effect, such as cracking in cast ingots. Therefore, the upper limit of Mn is 3 mass%, preferably 2.5 mass%, more preferably 2 mass%.
  • P ensures as much retained austenite as desired.
  • the amount of P necessary for this effect is no preferably less than 0.03 mass%, preferably no less than 0.05 mass%. Excess P produces adverse effects in secondary operation. Therefore, the upper limit of P is 0.15 mass%, preferably 0.1 mass%.
  • S deteriorates workability because it forms sulfide inclusions, such as MnS, to bring about cracking.
  • the amount of S should be as small as possible.
  • the amount of S should be below 0.02 mass%, preferably below 0.015 mass%.
  • the steel sheet of the present invention may optionally contain at least one of Mo, Ni, Cu, Cr Ca, and rare earth elements in addition to the above-mentioned fundamental components. They improve the properties of the steel sheet when they are used in an adequate amount as specified in the following.
  • Ca from greater than 0 mass% to 0.003 mass% and/or Rare earth elements: from greater than 0 mass% to 0.003 mass%
  • the rare earth elements used in the present invention include scandium (sc) and yttrium (Y), both belonging to Group III, and lanthanide elements (atomic number 51 to 71). Any of them may be used in an amount no less than 0.0003 mass%, preferably no less than 0.0005 mass%. The upper limit is 0.003 mass%, preferably 0.0025 mass%. Any excess amount is wasted without additional effect.
  • the steel sheet of the present invention is composed of the above-mentioned components, with the remainder being iron. However, it may also contain Ti, Nb, V, etc. in small amounts, and the steel sheet containing such minor components is also covered by the present invention. In addition, the steel sheet of the present invention may contain inevitable impurities, such as Zr and B; they are permissible so long as their amount is small enough (less than 0.001 mass%) to save the effect of the present invention.
  • a sample steel with the chemical composition shown in Table 1 was prepared by vacuum melting.
  • the steel was made into a slab, which was subsequently made into a steel sheet (1.2 mm thick) by hot rolling and continuous annealing.
  • Hot rolling was started at 1300°C and completed at about 900°C (which is higher than the Ar 3 point).
  • the rolled sheet was wound up at a finishing temperature of about 450°C.
  • the thus obtained hot-rolled steel sheet (2-3 mm thick) underwent cold rolling.
  • the cold-rolled steel sheet (1.2 mm thick) underwent heat treatment (continuous annealing) in different patterns as specified below.
  • This heat treatment consists of heating up to 850°C (above A 1 point and below A 3 point) and keeping this temperature for 120 seconds (for annealing), cooling to 700°C at an average rate of 5°C/s and keeping this temperature for 15 seconds, cooling to 420°C at an average rate of 15°C/s and keeping this temperature for 15 seconds (for austempering), and air cooling to room temperature at an average rate of 5°C/s.
  • This heat treatment consists of heating up to 850°C (above A 1 point and below A 3 point) and keeping this temperature for 120 seconds (for annealing), cooling to 700°C at an average rate of 5°C/s and keeping this temperature for 60 seconds, cooling to 420°C at an average rate of 15°C/s and keeping this temperature for 15 seconds (for austempering), and air cooling to room temperature at an average rate of 5°C/s.
  • This heat treatment consists of heating up to 850°C (above A 1 point and below A 3 point) and keeping this temperature for 120 seconds (for annealing), cooling to 420°C at an average rate of 15°C/s and keeping this temperature for 15 seconds (for austempering), and air cooling to room temperature at an average rate of 5°C/s.
  • This heat treatment consists of heating up to 850°C (above A 1 point and below A 3 point) and keeping this temperature for 120 seconds (for annealing), cooling to 420°C at an average rate of 15°C/s and keeping this temperature for 200 seconds (for austempering), and air cooling to room temperature at an average rate of 5°C/s.
  • Each sample undergoes electrolytic polishing (60 V - 0.5 A) with a solution containing 5% perchloric acid and acetic acid and etching (2 V - 20 mA, 2 min) with a solution of 10% acetylacetone and 90% methanol, containing 1 g of tetramethylammonium chloride.
  • each sample (with its surface etched by Repeller corrosion method) is observed and photographed by using an optical microscope and a transmission electron microscope (TEM). The photographs are used to measure the areal ratio of each constituent.
  • the areal ratio of retained austenite is determined by X-ray microanalysis (according to ISIJ Int. vol. 33 (1933), No. 7, p. 776 ).
  • Samples Nos. 2-5 and 7-10 exhibit excellent bendability because they meet all of the requirements prescribed in the present invention.
  • Sample No. 4 gave a TEM photograph (x7500) as shown in Fig. 1 . This photograph indicates that there exist a less number of carbide grains in the between retained austenite and ferrite.
  • samples Nos. 1, 6, 11, 12, and 13 are not satisfactory because they do not meet any of the requirements prescribed in the present invention.
  • Sample No. 1 is poor in strength on account of low carbon content.
  • Sample No. 6 is poor in strength, elongation, and bendability because of insufficient retained austenite and excess pearlite structure which result from the low content of Mn and the low content of (Si+Al) combined together.
  • Sample No. 11 is poor in elongation and bendability on account of excess pearlite structure and insufficient retained austenite, which results from keeping the work at 700°C for a long time during heat treatment.
  • Sample No. 12 is poor in bendability on account of a large number of carbide grains, which results from not keeping the work at 700°C during heat treatment.
  • Sample No. 13 is good in bendability owing to stable retained austenite with a high carbon content but is poor in tight bendability (R 0 ) owing to a large number of carbide grains, which results from not keeping the work at 700°C but keeping the work at 400°C for a long time during heat treatment.
  • Sample No. 13 gave a TEM photograph (x7500) as shown in Fig. 2 . This photograph indicates that the conventional steel sheet has a large number of carbide grains between retained austenite and ferrite.

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

Claims (3)

  1. Stahlblech mit hervorragender Biegbarkeit, das Folgendes umfasst:
    C: von 0,06 Masseprozent bis 0,25 Masseprozent;
    Si und/oder Al: insgesamt 0,5 - 3 Masseprozent;
    Mn: von 0,5 Masseprozent bis 3 Masseprozent;
    P: nicht mehr als 0,15 Masseprozent, ausschließlich 0 Masseprozent;
    S: nicht mehr als 0,02 Masseprozent, ausschließlich 0 Masseprozent; gegebenenfalls mindestens eines der folgenden Elemente:
    Mo: von mehr als 0 Masseprozent bis 1 Masseprozent;
    Ni: von mehr als 0 Masseprozent bis 0,5 Masseprozent;
    Cu: von mehr als 0 Masseprozent bis 0,5 Masseprozent;
    Cr: von mehr als 0,05 Masseprozent bis 0,8 Masseprozent;
    Ca: von mehr als 0 Masseprozent bis 0,003 Masseprozent;
    Sc: von 0,0003 Masseprozent bis 0,003 Masseprozent;
    Y: von 0,0003 Masseprozent bis 0,003 Masseprozent;
    ein Lanthanid-Element: von 0,0003 Masseprozent bis 0,003 Masseprozent;
    Zr: weniger als 0,001 Masseprozent;
    B: weniger als 0,001 Masseprozent;
    wobei der Rest Fe und unvermeidbare Verunreinigungen ist,
    wobei die Hauptstruktur der Stahlplatte Abschreckaustenit von 5 - 30 Flächenprozent und Ferrit von nicht weniger als 50 Flächenprozent umfasst und wobei nicht mehr als 40 Karbidkörner pro 2000 µm2 in der Stahlplatte zwischen Abschreckaustenit und Ferrit vorliegen.
  2. Stahlplatte nach Anspruch 1, wobei die Hauptstruktur der Stahlplatte Abschreckaustenit von 5 - 20 Flächenprozent umfasst.
  3. Stahlplatte nach einem der Ansprüche 1 bis 2, wobei nicht mehr als 30 Karbidkörner pro 2000 µm2 in der Stahlplatte vorliegen.
EP03254606A 2002-07-29 2003-07-24 Stahlblech mit guter Biegbarkeit Expired - Lifetime EP1389639B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2002219662A JP3828466B2 (ja) 2002-07-29 2002-07-29 曲げ特性に優れた鋼板
JP2002219662 2002-07-29

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EP1389639A2 EP1389639A2 (de) 2004-02-18
EP1389639A3 EP1389639A3 (de) 2005-06-08
EP1389639B1 true EP1389639B1 (de) 2011-01-05

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EP1431406A1 (de) * 2002-12-20 2004-06-23 Sidmar N.V. Stahlzusammensetzung zur Herstellung von mehrphasigen kaltgewalzten Stahlprodukten
US7314532B2 (en) * 2003-03-26 2008-01-01 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) High-strength forged parts having high reduction of area and method for producing same
ATE526424T1 (de) * 2003-08-29 2011-10-15 Kobe Steel Ltd Hohes stahlblech der dehnfestigkeit ausgezeichnet für die verarbeitung und proze für die produktion desselben
EP1553202A1 (de) * 2004-01-09 2005-07-13 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Ultrahochfester Stahl mit ausgezeichneter Beständigkeit gegenüber Wasserstoffversprödung und Verfahren zu seiner Herstellung
EP1559798B1 (de) * 2004-01-28 2016-11-02 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Hochfestes kaltgewalztes Stahlblech mit niedrigem Streckgrenzenverhältnis und Verfahren zu seiner Herstellung
EP1589126B1 (de) * 2004-04-22 2009-03-25 Kabushiki Kaisha Kobe Seiko Sho Hochfestes und kaltgewaltzes stahlblech mit hervorragender verformbarkeit und plattiertes stahlblech
JP4288364B2 (ja) * 2004-12-21 2009-07-01 株式会社神戸製鋼所 伸びおよび伸びフランジ性に優れる複合組織冷延鋼板
JP4716359B2 (ja) * 2005-03-30 2011-07-06 株式会社神戸製鋼所 均一伸びに優れた高強度冷延鋼板およびその製造方法
JP4716358B2 (ja) * 2005-03-30 2011-07-06 株式会社神戸製鋼所 強度と加工性のバランスに優れた高強度冷延鋼板およびめっき鋼板
EP1767659A1 (de) * 2005-09-21 2007-03-28 ARCELOR France Herstellungsverfahren eines Stahlwerkstücks mit mehrphasigem Mikrogefüge
KR100985298B1 (ko) 2008-05-27 2010-10-04 주식회사 포스코 리징 저항성이 우수한 저비중 고강도 열연 강판, 냉연강판, 아연도금 강판 및 이들의 제조방법
JP5867436B2 (ja) 2013-03-28 2016-02-24 Ｊｆｅスチール株式会社 高強度合金化溶融亜鉛めっき鋼板およびその製造方法

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US20040159373A1 (en) 2004-08-19
EP1389639A3 (de) 2005-06-08
EP1389639A2 (de) 2004-02-18
JP2004059996A (ja) 2004-02-26

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