EP1682686B1 - Feuillard acier a phase duale convenant pour la galvanisation - Google Patents

Feuillard acier a phase duale convenant pour la galvanisation Download PDF

Info

Publication number
EP1682686B1
EP1682686B1 EP04752656.1A EP04752656A EP1682686B1 EP 1682686 B1 EP1682686 B1 EP 1682686B1 EP 04752656 A EP04752656 A EP 04752656A EP 1682686 B1 EP1682686 B1 EP 1682686B1
Authority
EP
European Patent Office
Prior art keywords
strip
temperature
steel
soak
max
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
Application number
EP04752656.1A
Other languages
German (de)
English (en)
Other versions
EP1682686A1 (fr
EP1682686A4 (fr
Inventor
David P. Hoydick
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
UEC Technologies LLC
Original Assignee
UEC Technologies LLC
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority claimed from PCT/US2003/035095 external-priority patent/WO2004048634A1/fr
Application filed by UEC Technologies LLC filed Critical UEC Technologies LLC
Priority to PL04752656T priority Critical patent/PL1682686T3/pl
Publication of EP1682686A1 publication Critical patent/EP1682686A1/fr
Publication of EP1682686A4 publication Critical patent/EP1682686A4/fr
Application granted granted Critical
Publication of EP1682686B1 publication Critical patent/EP1682686B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

Classifications

    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C23C2/29—Cooling or quenching
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • 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
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment

Definitions

  • Dual phase galvanized steel strip is made utilizing a thermal profile involving a two-tiered isothermal soaking and holding sequence.
  • the strip is at a temperature close to that of the molten metal when it enters the coating bath.
  • a cold rolled steel sheet is used as the base for hot dip galvanizing, the steel sheet having a particular composition which is said to be beneficial for the formation, under the conditions of the process, of a microstructure composed mainly of ferrite and martensite.
  • the Omiya et al patent describes a galvanized dual phase product.
  • a dual phase galvanized steel sheet is made by soaking the cold rolled steel sheet at a temperature of 780°C (1436°F) or above, typically for 10 to 40 seconds, and then cooling it at a rate of at least 5°C per second, more commonly 20-40°C per second, before entering the galvanizing bath, which is at a temperature of 460°C (860°F).
  • the steel should have a composition as follows, in weight percent: Carbon: 0.02-0.20 Aluminum: 0.010-0.150 Titanium: 0.01 max Silicon: 0.04 max Phosphorous: 0.060 max Sulfur: 0.030 max Manganese: 1.5-2.40 Chromium: 0.03-1.50 Molybdenum:0.03-1.50 with the provisos that the amounts of manganese, chromium and molybdenum should have the relationship: 3Mn + 6Cr + Mo: 8.1% max, and Mn + 6Cr + 10 Mo: at least 3.5%
  • the plated sheet After plating, cooling at a rate of at least 5°C/second will achieve the desired microstructure of predominantly ferrite and martensite.
  • the plated sheet may be heated prior to cooling, in an alloying procedure (often called galvannealing) after metal coating but prior to the final cooling.
  • the soak temperature of (A C 1 +45°F) to 1425°F, usually 1340-1420°F must be coupled with a subsequent substantially isothermal heat treatment, termed the holding step, in the range of 850-920°F (454-493°C).
  • the holding step the sheet is maintained at 850-920°F (454-493°C), sometimes herein expressed as 885°F ⁇ 35°F, for a period of 20 to 100 seconds, before cooling to room (ambient) temperature.
  • Cooling to ambient temperature should be conducted at a rate of at least 5°C per second. It is important to note, once again, that the Omiya et al patent says nothing about a holding step at any temperature or for any time in their thermal process. Furthermore, my work has shown that if a steel as defined in the Omiya et al patent is soaked within Omiya's defined, higher, soaking range (for example 1475°F) and further processed through a thermal cycle including a holding step as described herein (850-920F), the resultant steel will not achieve the desired predominantly ferrite-martensite microstructure but will contain a significant amount of bainite and/or pearlite.
  • the steel sheet should have a composition similar to that of the Omiya et al patent: Carbon: 0.02-0.20 Aluminum: 0.010-0.150 Titanium: 0.01 max Silicon: 0.04 max Phosphorous: 0.060 max Sulfur: 0.030 max Manganese: 1.5-2.40 Chromium: 0.03-1.50 Molybdenum:0.03-1.50 with the provisos that the amounts of manganese, chromium and molybdenum could have the relationship: Mn + 6Cr + 10 Mo: at least 3.5%
  • the silicon content may be as much as 0.5%, and, preferably, carbon content is 0.03-0.12% although the Omiya et al carbon range may also be used.
  • This composition, as modified, may be referred to hereafter as Composition A.
  • my invention is a method of making a dual phase steel sheet comprising soaking a steel sheet at a temperature of in the range from A C 1 +45°F, but at least 1340°F (727°C), to A C 1 +135°F, but no more than 1425°F (775°C), for a period of 20 to 90 seconds, cooling the sheet at a rate no lower than 1°C/second to a temperature of 454-493°C, and holding the sheet at temperatures in the range of 850-920°F (454-493°C) for a period of 20 to 100 seconds.
  • the holding step may be prior to the hot dip or may begin with the hot dip, as the galvanizing pot will be at a temperature also in the range 454-493°C (850-920°F).
  • the sheet can be cooled to ambient temperature at a rate of at least 5°C/second.
  • the sheet may be galvannealed in the conventional manner - that is, the sheet is heated for about 5-20 seconds to a temperature usually no higher than about 960°F and then cooled at a rate of at least 5°C/second.
  • My galvannealed and galvanized thermal cycles are shown for comparison in Figure 6 .
  • the actual hot dip step is conducted more or less conventionally - that is, the steel is contacted with the molten galvanizing metal for about 5 seconds; while a shorter time may suffice in some cases, a considerably longer time may be used but may not be expected to result in an improved result.
  • the steel strip is generally about 0.7 mm thick to about 2.5 mm thick, and the coating will typically be about 10 ⁇ m.
  • the coated steel may be either cooled to ambient temperature as described elsewhere herein or conventionally galvannealed, as described above. When the above protocol is followed, a product having a microstructure comprising mainly ferrite and martensite will be obtained.
  • my invention comprises feeding a cold rolled coil of steel strip of Composition A to a heating zone in the galvanizing line, passing the strip through a heating zone continuously to heat the strip to within the range of A C 1 +45°F, but at least 1340°F (727°C), to A C 1 +135°F, but no more than 1425°F (775°C), passing the strip through a soaking zone to maintain the strip within the range of A C 1 +45°F, but at least 1340°F (727°C), to A C 1 +135°F, but no more than 1425°F (775°C), for a period of 20 to 90 seconds, passing the strip through a cooling zone to cool the strip at a rate greater than 1°C/second, discontinuing cooling the strip when the temperature of the strip has been reduced to a temperature in the range 885°F ⁇ 35°F, but also ⁇ 30 degrees F of the temperature of the
  • the galvanizing bath is typically at about 870°F (850-920°F), and may be located at the beginning of the holding zone, or near the end of the hold zone, or anywhere else in the holding zone, or immediately after it. Residence time in the bath is normally 3-6 seconds, but may vary somewhat, particularly on the high side, perhaps up to 10 seconds. As indicated above, after the steel is dipped into and removed from the zinc bath, the sheet can be heated in the conventional way prior to cooling to room temperature to form a galvanneal coating, if desired.
  • Samples of steel sheet were processed, with various "soak" temperatures according to the general thermal cycle depicted in Figure 1 - one set of samples followed the illustrated curve with a 35 second "hold” at 880°F and the other set of samples were held at 880°F for 70 seconds.
  • the samples were cold rolled steel of composition A as described above - in particular, the carbon was 0.67, Mn was 1.81, Cr was 0.18 and Mo was 0.19, all in weight percent.
  • the other elemental ingredients were typical of low carbon, A1 killed steel. Soak temperatures were varied in increments of 20°F within the range of 1330 to 1510°F. After cooling, the mechanical properties and microstructures of the modified samples were determined.
  • UTS Ultimate tensile strength
  • a goal of Example 1 was to achieve a predominantly ferrite-martensite microstructure.
  • the yield ratio i.e. the ratio of yield strength to ultimate tensile strength, is an indication whether or not a dual phase ferrite-martensite microstructure is present.
  • a ferrite-martensite microstructure is indicated when the yield ratio is 0.5 or less. If the yield ratio is greater than about 0.5, a significant volume fraction of other deleterious constituents such as bainite, pearlite, and/or Fe 3 C may be expected in the microstructure.
  • Figure 3 shows the yield ratio as a function of soak temperature for both the 35 and 70 second holding zones for the samples.
  • the necessary annealing range for ferrite-martensite microstructures is from about 1350 to 1430°F.
  • Table 1 summarizes the relationships between the thermal process, yield ratio and microstructural constituents for this example at the different soak temperature regimes.
  • a different cold rolled sheet steel of Composition A was subjected to the same set of thermal cycles a described in Example 1 and shown in Figure 1 .
  • This steel also lay within the stated composition range, in this case specifically containing the following, in weight percent: 0.12%C, 1.96%Mn, 0.24%Cr, and 0.18%Mo, and the balance of the composition typical for a low carbon Al-killed steel.
  • the effect of soak temperature on yield ratio for this steel for the 70 second holding sequence at 880°F is shown in Figure 4 .
  • This curve exhibits a shape similar to the curves in Figure 3 , with metallographic analyses revealing identical metallogical phenomena occurring at the different soak temperature regimes as in the previous example.
  • the annealing soak temperature range necessary for a predominantly ferrite-martensite microstructure to be obtained is from about 1350 to 1425°F when a hold step is conducted at about 880°F.
  • a third cold-rolled steel of Composition A was processed according to the set of thermal cycles shown in Figure 1 .
  • This steel contained, in weight percent, 0.076C, 1.89 Mn, 0.10Cr, 0.094 Mo, and 0.34 Si, the balance of which is typical for a low carbon steel.
  • Figure 5 shows the yield ratio of this material as a function of soak temperature for the holding time of 70 seconds.
  • the soak temperature range necessary for dual phase production depends on the specific steel composition - that is, it should lie within the range from A C 1 +45°F, but at least 1340°F (727°C), to A C 1 +135°F, but no more than 1425°F (775°C) when a holding step in the vicinity of 880° (885°F ⁇ 35°F) is present in the thermal cycle.
  • Table 3 shows the resultant mechanical properties of two additional steels having carbon contents lower than shown previously. They were processed as described in Figure 1 utilizing the individual soak temperatures of 1365, 1400, and 1475°F, respectively and a hold time of 70 seconds at 880°F. Also shown within the table are the expected necessary soak temperature ranges for dual phase steel production for each steel as calculated from A c1 as described in Example 3. Note that for the 1365 and 1400°F soak temperatures, which reside within the desired soak temperature range for both respective steels, low yield ratios characteristic of ferrite-martensite microstructures are observed. Furthermore, for the steels soaked at 1475°F, which is outside the range present invention, the yield ratio is significantly higher due to the presence of bainite in the microstructure.
  • Table 3a displays data collected in a manner similar to that of Table 3: Table 3a C Mn Mo Cr Ac1 A C1 +45 -A C1 +135 Soak° F YS UTS YS/U TS .058 1.23 0.4 0.2 1316 1361 - 1451 1400 251 524 0.48 .058 1.23 0.4 0.2 1316 1361 - 1451 1500 304 520 0.58 .121 1.22 0.4 0.2 1316 1361 - 1451 1400 291 619 0.47 .121 1.22 0.4 0.2 1316 1361 - 1451 1500 328 614 0.53
  • my invention includes the use of a soak temperature in the range of A C1 +45°F to A C1 +135°F for the defined compositions, without caps.
  • steels 1 through 4 were soaked within the soaking range of the invention and exhibited the expected yield ratio of less than 0.5.
  • Metallographic examination revealed the presence of ferrite martensite microstructures for steels 1 through 4 with martensite contents of about 15%.
  • Steel 5 was processed outside of the preferred soaking range and exhibited a relatively high yield ratio of about 0.61.
  • Metallographic analysis showed a bainite content of 11% in this material. Similar results have been shown for galvanize as well as galvanneal processing.
  • the hold temperature may be within the range of 850-940°F (that is, 895°F ⁇ 45°F), and need not be limited to 850-920°F as previously stated.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Oil, Petroleum & Natural Gas (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Coating With Molten Metal (AREA)

Claims (4)

  1. Procédé de fabrication d'un feuillard d'acier galvanisé présentant de manière prédominante une microstructure martensitique et ferritique, dans lequel ledit acier comporte comme ingrédients, en pourcentage massique, du carbone : 0,02 % à 0,20 % ; de l'aluminium : 0,010 % à 0,150 % ; du titane : ≤ 0,01 % ; du silicium : ≤ 0,5 % ; du phosphore : ≤ 0,060 % ; du soufre : ≤ 0.030 % ; du manganèse : 0,8 % à 2,40 % ; du chrome : 0,03 % à 1,50 % ; du molybdène : 0,03 % à 1,50 %, comprenant le trempage dudit feuillard d'acier à une température de 727°C (1340°F) à 775°C (1425°F) durant au moins 20 secondes, le refroidissement dudit feuillard à un taux d'au moins 1°C par seconde, le passage dudit feuillard à travers une cuve de galvanisation durant un temps de séjour compris entre 2 et 9 secondes pour revêtir ledit feuillard à tout moment tout en maintenant ledit feuillard à une température de 455°C à 505°C (895°F ± 45°F) durant 20 à 100 secondes, et le refroidissement du feuillard ainsi revêtu jusqu'à température ambiante ;
    dans le cas où un procédé de fabrication d'un feuillard d'acier galvanisé présentant de manière prédominante une microstructure martensitique et ferritique est exclu, dans lequel ledit acier comporte comme ingrédients, en pourcentage massique, du carbone : 0,02 % à 0,20 % ; de l'aluminium : 0,010 % à 0,150 % ; du titane : ≤ 0,01 % ; du silicium : ≤ 0,5 % ; du phosphore : ≤ 0,060 % ; du soufre : ≤ 0,030 % ; du manganèse : 1,5 % à 2,40 % ; du chrome : 0,03 % à 1,50 % ; du molybdène : 0,03 % à 1,50 %, comprenant le trempage dudit feuillard d'acier à AC1+45°F, mais au moins à 727°C (1340°F), jusqu'à AC1+135°F, mais au plus à 775°C (1425°F), durant au moins 20 secondes, le refroidissement dudit feuillard à un taux d'au moins 1°C par seconde, le passage dudit feuillard par une cuve de galvanisation avec un temps de séjour compris entre 2 et 9 secondes pour revêtir ledit feuillard à tout moment tout en maintenant ledit feuillard à une température de 455°C à 494°C (885°F ± 35°F) durant 20 à 100 secondes, et le refroidissement du feuillard ainsi revêtu jusqu'à température ambiante.
  2. Procédé selon la revendication 1, comprenant le recuit après galvanisation dudit feuillard avant le refroidissement jusqu'à température ambiante.
  3. Procédé selon la revendication 1, dans lequel la différence de température entre ledit feuillard et la cuve de galvanisation durant ledit temps de séjour est inférieure ou égale à 30°F.
  4. Procédé selon la revendication 1, dans lequel la différence de température entre ledit feuillard et la cuve de galvanisation durant ledit temps de séjour est inférieure ou égale à 20°F.
EP04752656.1A 2003-11-04 2004-05-17 Feuillard acier a phase duale convenant pour la galvanisation Expired - Lifetime EP1682686B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
PL04752656T PL1682686T3 (pl) 2003-11-04 2004-05-17 Taśma z dwufazowej stali odpowiednia do galwanizacji

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
PCT/US2003/035095 WO2004048634A1 (fr) 2002-11-26 2003-11-04 Procede de production de tole biphasee
PCT/US2004/015675 WO2005047550A1 (fr) 2003-11-04 2004-05-17 Feuillard acier a phase duale convenant pour la galvanisation pour

Publications (3)

Publication Number Publication Date
EP1682686A1 EP1682686A1 (fr) 2006-07-26
EP1682686A4 EP1682686A4 (fr) 2007-06-27
EP1682686B1 true EP1682686B1 (fr) 2014-11-12

Family

ID=34589294

Family Applications (1)

Application Number Title Priority Date Filing Date
EP04752656.1A Expired - Lifetime EP1682686B1 (fr) 2003-11-04 2004-05-17 Feuillard acier a phase duale convenant pour la galvanisation

Country Status (6)

Country Link
EP (1) EP1682686B1 (fr)
AU (1) AU2004289949B2 (fr)
CA (1) CA2544382C (fr)
ES (1) ES2530066T3 (fr)
PL (2) PL1682686T3 (fr)
WO (1) WO2005047550A1 (fr)

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5223360B2 (ja) * 2007-03-22 2013-06-26 Ｊｆｅスチール株式会社 成形性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法

Family Cites Families (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1981002900A1 (fr) * 1980-03-31 1981-10-15 Kawasaki Steel Co Plaque d'acier a haute resistance, laminee a froid presentant une excellente formabilite et procede de production de celle-ci ainsi que plaque d'acier galvanise a haute resistance, presentant une excellente formabilite, et procede de production de celle-ci
EP1160346B1 (fr) * 1999-02-22 2006-03-08 Nippon Steel Corporation Plaque d'acier galvanise a haute resistance, d'excellent comportement pour l'adhesion des placages de metal et la mise en forme sous presse, et plaque d'acier allie galvanise a haute resistance, et procede de production correspondant
US6312536B1 (en) * 1999-05-28 2001-11-06 Kabushiki Kaisha Kobe Seiko Sho Hot-dip galvanized steel sheet and production thereof
EP1443124B1 (fr) * 2000-01-24 2008-04-02 JFE Steel Corporation Bande d'acier galvanisée à chaud et son procédé de fabrication
WO2002044434A1 (fr) * 2000-11-28 2002-06-06 Kawasaki Steel Corporation Tole d'acier laminee a froid presentant une resistance elevee a la traction du type structure composite
US6586117B2 (en) * 2001-10-19 2003-07-01 Sumitomo Metal Industries, Ltd. Steel sheet having excellent workability and shape accuracy and a method for its manufacture
US6811624B2 (en) * 2002-11-26 2004-11-02 United States Steel Corporation Method for production of dual phase sheet steel

Also Published As

Publication number Publication date
AU2004289949B2 (en) 2011-04-28
CA2544382A1 (fr) 2005-05-26
CA2544382C (fr) 2010-04-06
ES2530066T3 (es) 2015-02-26
WO2005047550A1 (fr) 2005-05-26
EP1682686A1 (fr) 2006-07-26
EP1682686A4 (fr) 2007-06-27
AU2004289949A1 (en) 2005-05-26
PL379761A1 (pl) 2006-11-13
PL1682686T3 (pl) 2015-04-30
PL210446B3 (pl) 2012-01-31

Similar Documents

Publication Publication Date Title
US6811624B2 (en) Method for production of dual phase sheet steel
EP3164512B1 (fr) Procédé permettant de produire une tôle d'acier revêtue à haute résistance présentant une résistance et une ductilité améliorées, et tôle ainsi obtenue
CA2954146C (fr) Procede de production d'une tole d'acier revetue a haute resistance presentant une resistance, une ductilite et une aptitude au formage ameliorees
JP2019178428A (ja) 超高強度被覆または非被覆鋼板を製造する方法および得られる鋼板
EP3177749B1 (fr) Procédé de fabrication d'une tôle d'acier ayant une résistance, une ductilité et une aptitude au formage améliorées
CA2954132C (fr) Procede de fabrication d'une tole d'acier a haute resistance presentant une aptitude au formage amelioree, et tole ainsi obtenue
US20110223441A1 (en) Very high mechanical strength steel and method for producing a sheet of this steel coated with zinc or zinc alloy
EP3164519B1 (fr) Procédé de production d'une tôle d'acier revêtue à haute résistance ayant une résistance et une aptitude au formage améliorées
US7311789B2 (en) Dual phase steel strip suitable for galvanizing
EP1682686B1 (fr) Feuillard acier a phase duale convenant pour la galvanisation
EP3889277B1 (fr) Tôle en acier à haute résistance et procédé de fabrication de celle-ci
JP3777049B2 (ja) 耐デント性ならびに耐面ひずみ性に優れた深絞り用ｂｈ冷延鋼板の製造方法

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20060512

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PL PT RO SE SI SK TR

DAX Request for extension of the european patent (deleted)
A4 Supplementary search report drawn up and despatched

Effective date: 20070531

RIC1 Information provided on ipc code assigned before grant

Ipc: C21D 6/00 20060101AFI20050601BHEP

Ipc: C23C 2/06 20060101ALI20070524BHEP

17Q First examination report despatched

Effective date: 20100924

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20140530

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PL PT RO SE SI SK TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 695815

Country of ref document: AT

Kind code of ref document: T

Effective date: 20141115

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602004046123

Country of ref document: DE

Effective date: 20141224

REG Reference to a national code

Ref country code: RO

Ref legal event code: EPE

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2530066

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20150226

REG Reference to a national code

Ref country code: NL

Ref legal event code: VDEP

Effective date: 20141112

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 695815

Country of ref document: AT

Kind code of ref document: T

Effective date: 20141112

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141112

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141112

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150312

REG Reference to a national code

Ref country code: PL

Ref legal event code: T3

REG Reference to a national code

Ref country code: SK

Ref legal event code: T3

Ref document number: E 18017

Country of ref document: SK

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 12

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150213

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141112

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141112

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141112

REG Reference to a national code

Ref country code: HU

Ref legal event code: AG4A

Ref document number: E023388

Country of ref document: HU

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141112

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141112

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602004046123

Country of ref document: DE

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20150813

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

REG Reference to a national code

Ref country code: DE

Ref legal event code: R082

Ref document number: 602004046123

Country of ref document: DE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150517

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20150531

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20150531

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141112

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141112

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 13

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 14

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141112

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: CZ

Payment date: 20170519

Year of fee payment: 14

Ref country code: SK

Payment date: 20170519

Year of fee payment: 14

Ref country code: FR

Payment date: 20170525

Year of fee payment: 14

Ref country code: RO

Payment date: 20170522

Year of fee payment: 14

Ref country code: DE

Payment date: 20170530

Year of fee payment: 14

Ref country code: GB

Payment date: 20170530

Year of fee payment: 14

Ref country code: IE

Payment date: 20170530

Year of fee payment: 14

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141112

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: ES

Payment date: 20170601

Year of fee payment: 14

Ref country code: PL

Payment date: 20170518

Year of fee payment: 14

Ref country code: IT

Payment date: 20170524

Year of fee payment: 14

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141112

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: HU

Payment date: 20170524

Year of fee payment: 14

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 602004046123

Country of ref document: DE

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20180517

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: RO

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180517

Ref country code: HU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180518

Ref country code: SK

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180517

Ref country code: CZ

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180517

REG Reference to a national code

Ref country code: SK

Ref legal event code: MM4A

Ref document number: E 18017

Country of ref document: SK

Effective date: 20180517

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180517

Ref country code: DE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20181201

Ref country code: IT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180517

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180517

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180531

REG Reference to a national code

Ref country code: ES

Ref legal event code: FD2A

Effective date: 20190913

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: ES

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180518

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PL

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180517