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EP1169486B1 - Procede de production de feuillard a chaud - Google Patents

Procede de production de feuillard a chaud Download PDF

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Publication number
EP1169486B1
EP1169486B1 EP00906372A EP00906372A EP1169486B1 EP 1169486 B1 EP1169486 B1 EP 1169486B1 EP 00906372 A EP00906372 A EP 00906372A EP 00906372 A EP00906372 A EP 00906372A EP 1169486 B1 EP1169486 B1 EP 1169486B1
Authority
EP
European Patent Office
Prior art keywords
cooling
hot strip
cooled
temperature
phase
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.)
Revoked
Application number
EP00906372A
Other languages
German (de)
English (en)
Other versions
EP1169486A1 (fr
Inventor
Rudolf Kawalla
Hans Pircher
Thomas Heller
Bernhard Engl
Pino Tes
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.)
ThyssenKrupp Steel Europe AG
Original Assignee
ThyssenKrupp Stahl AG
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Filing date
Publication date
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Anticipated expiration legal-status Critical
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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
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
    • B21B37/76—Cooling control on the run-out table
    • 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
    • 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
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following 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
    • 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
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • C21D9/573—Continuous furnaces for strip or wire with cooling

Definitions

  • the invention relates to a method for generating a Steel hot strip, in which the hot strip after the Finishing rolling a carried out in several stages Cooling is subjected.
  • the structure can be cooled as such and the proportions of the individual structure types influence this structure. So it is possible through cooling, for example, strength, toughness and To influence the hardness of a hot strip.
  • JP 10-195588 A discloses a method for producing a hot strip from a slab, which (in% by weight) 0.02-0.2% C, 0.1-1, 5% Si, 0.5-3.0% Mn and one or more of the elements Cr and Mo each with 0.1-2.0%, the rest iron.
  • the hot strip is hot-rolled according to the known method at a final temperature corresponding at least to the Ar 3 temperature to thicknesses which are typically in the range from 0.8 to 1.4 mm.
  • the hot strips are continuously cooled in a first stage that begins 0.1 to 5 s after hot rolling with a cooling rate in the temperature range of 680 - 720 ° C that is more than 50 ° C.
  • the first stage of cooling is followed by an intermediate cooling phase, during which the belt cools in air for up to 15 seconds.
  • a third cooling phase then follows, in which cooling is carried out at a cooling rate of at least 30 ° C./s in a temperature range from 300 to 600 ° C. Finally the tape is coiled.
  • a comparable method is known from EP-A-0 719 868 known.
  • a Slab with (in% by weight) 0.001 - 0.1% C, ⁇ 1.5% Si, 0.5 - 3.0% Mn, 0.01-0.1% Al, and one or more of the Elements P (0.05 - 0.15%) and Cr (0.5 - 1.5%), the rest Iron, at a hot rolling end temperature of up to 850 ° C continuously rolled into hot strip.
  • Within A first is carried out 0.5 s after the finish hot rolling Cooling down at temperatures between 650 - 750 ° C lie.
  • the cooling rate is at least 30 ° C / s, typically 42 - 70 ° C / s.
  • the first cooling stage is followed by an intermediate cooling phase at which the belt cools in air for 4 to 60 seconds. This is followed by a third cooling at cooling rates of at least 30 ° C / s to between 100 ° C and 500 ° C lying reel temperature.
  • the object of the invention is to provide a method create with which hot strips can be produced which have high formability and increased strength exhibit.
  • the hot strip is cooled also in at least two consecutive through stages.
  • the hot strip is in the the first cooling phase cooled much faster than the State of the art.
  • This compact cooling during the first cooling phase has the consequence that the ⁇ / ⁇ conversion of effective and targeted in the ⁇ -region of hot-rolled strip is suppressed towards lower temperatures.
  • the tape is then accelerated to the cooling brought desired final temperature.
  • the hardness-increasing second phases of the hot strip structure like martensite, bainite and residual austenite, set. (At the end of the second cooling phase accelerated cooling can reach the final temperature of course, depending on the desired processing results required Act reel temperature.)
  • the hot strip Steel optionally contain additional elements.
  • the proportion (in mass%) of Cu, Ni, Mo not more than 0.8%, that of N, Ti, Nb, V, Zn, B not larger than 0.5%, that of P not larger than 0.09%, that of Cr not greater than 1.5% and that of S should not be greater than 0.02%.
  • the method according to the invention is firstly for generating suitable for hot strips, which are based on steels are manufactured with low carbon contents. So is an advantageous variant of the invention Process characterized in that the steel (in Mass%) not more than 0.07% C, not more than 0.2% Si, not more than 0.6% Mn and not more than 0.08% Al contains the hot strip during finish rolling in Austenite area is rolled, the hot strip in the first Cooling phase of accelerated cooling starting from one Temperature above 850 ° C to a temperature of 680 is cooled to 750 ° C, the hot strip in the second Cooling phase accelerated cooling to a temperature of is cooled to less than 600 ° C and finally coiled becomes.
  • the method of manufacture according to the invention is likewise suitable for DP hot strip steels.
  • a corresponding one Design of the method according to the invention characterized in that the steel (in mass%) 0.04 - 0.09% C, not more than 0.2% Si, 0.5 - 2.0% Mn, 0.02 - Contains 0.09% P and not more than 0.9% Cr, and that the Hot strip after finish rolling in the first cooling phase accelerated cooling based on a temperature above 800 ° C to a temperature of 650 to 730 ° C is cooled that the hot strip in the second cooling phase accelerated cooling cooled to less than 500 ° C and that the hot strip is then coiled.
  • a hot strip which on a steel with (in mass%) 0.25 - 1.05% C, not more than 0.25% Si and not more than 0.6% Mn based, after finishing rolling in the first cooling phase accelerated cooling based on a temperature above 800 ° C to a temperature of 530 to 620 ° C cooled, in the second cooling phase accelerated cooling cooled to less than 500 ° C and then coiled.
  • a hot strip produced in this way has also improved hardness and better Forming properties compared to conventionally produced Tapes.
  • the method is characterized in that the steel (in Mass%) 0.04 - 0.09% C, 0.5 - 1.5% Si, 0.5 - 2.0% Mn, 0.4 - 2.5% Al, no more than 0.09% P and no more than 0.9% Cr contains that the hot strip after Finishing rolls accelerated in the first cooling phase Cooling from a temperature above 800 ° C is cooled to a temperature of 650 to 730 ° C that the hot strip accelerated in the second cooling phase Cooling is cooled to less than 500 ° C and that Hot strip is then coiled.
  • Such one Hot strip has DP and TRIP properties.
  • a structural steel with an increased ferrite content and from it The following particularly good formability can be thereby make the steel (in mass%) 0.07 - 0.22% C, 0.1 - 0.45% Si and 0.2 - 1.5% Mn contains that the Hot strip after finish rolling in the first cooling phase accelerated cooling based on a temperature above 800 ° C to a temperature of 650 to 730 ° C is cooled that the hot strip in the second cooling phase accelerated cooling cooled to less than 500 ° C and that the hot strip is then coiled.
  • a hot strip can be made with the same steel composition with improved hardness, on the other hand, that the hot strip after finish rolling in the first Cooling phase of accelerated cooling starting from one Temperature above 800 ° C to a temperature of 580 is cooled to 650 ° C that the hot strip in the second Cooling phase of accelerated cooling to less than 500 ° C is cooled and that the hot strip is then coiled becomes.
  • the hot strip cooled in this way has one reduced ferrite content, higher bainite and martensite contents on.
  • the Invention passes through the hot strip between the first Cooling phase and the second cooling phase accelerated Cooling an intermediate cooling phase during which the hot strip is exposed to air cooling.
  • This intermediate cooling phase should take at least a second.
  • in the cooling in air takes place the austenite transformation in ferrite faster and reaches one larger scope than in the prior art, wherein at the same time a strong grain-refining effect watch is.
  • the procedure according to the invention can produce a hot strip, which compared to a conventional one Process in two laminar cooling stages with intermediate cooling in air-cooled hot strip same composition an increased hardness and a has a finer grain structure.
  • the tape produced by the method according to the invention high strength and, unlike that after known methods produced tapes, a good one Formability on.
  • the first cooling phase therefore begins at the latest two Seconds after the last pass of finish rolling.
  • a further advantageous embodiment of the method, with which a hot strip of particularly good formability can be produced is characterized in that at least one of the rolling passes is carried out during the finish rolling in the austenite region below a temperature of Ar 3 + 80 ° C and that the total pass decrease during of finish rolling is more than 30%.
  • the hot strip used steel expedient if the in particular as a thin slab primary material steel introduced into the respective rolling mill in the liquid phase with Ca or Ca carrier alloys is treated.
  • the hot strip in the second cooling phase with a cooling rate of is cooled at least 30 ° C / s.
  • Line 1 for producing a hot strip W comprises one Relay of several finishing stands, one of which is here only the last frame 2 is shown. In the Finishing rolling the hot strip W is on its The desired final thickness is rolled.
  • a compact cooling device 3 is arranged.
  • This Compact cooling device 3 includes not shown here Nozzles, via the cooling liquid, preferably water, under increased pressure on the top and bottom of the Hot strip W is brought.
  • the volume flow of the Coolant is adjustable so that within the Compact cooling device 3 cooling speeds of 150 ° C / s to 1000 ° C / s can be achieved.
  • the second cooling device 4 works kind of a conventional laminar cooling, in which the Coolant through several in the conveying direction F arranged one behind the other, also not shown here Fan is brought onto the hot strip W in a fan-like manner.
  • the Number of nozzles acted upon and / or Volume flow in the area of the laminar cooling device 4 applied coolant can be regulated in such a way that in the area of the laminar cooling device 4 Cooling speeds of 30 to 150 ° C / s reached become.
  • a reel device 5 In the conveying direction F of the belt behind the laminar cooling device 4 is a reel device 5 arranged, in which the hot strip W to a coil is wrapped.
  • Hot strip W is used exclusively in the finishing mill in the austenite area with a total decrease of more rolled as 30%. If necessary, the hot strip W during the rolling of a thermomechanical treatment subjected.
  • the hot strip W After the hot strip W has left the last stand 2 of the finished rolling mill, it arrives in the compact cooling device 3 within a transfer phase t 2 , which is shorter than two seconds.
  • the hot strip W Upon entering the compact cooling device 3, the hot strip W becomes a first cooling phase t CK continuously exposed to a compact cooling, during which the hot strip W is cooled from an inlet temperature ET CK to an outlet temperature AT CK .
  • the cooling rates achieved are between 250 and 1000 ° C / s.
  • the ⁇ / ⁇ conversion of the hot strip steel is suppressed by the accelerated cooling of the hot strip W in the compact cooling device 3 within a short time t z after the exit from the finished rolling stack.
  • the hot strip W then runs through a free stretch in which it is cooled in air for an intermediate cooling phase t PAUSE .
  • the duration of the intermediate cooling phase t PAUSE is at least one second. During this time there is a partial conversion of the hot strip steel.
  • the hot strip W arrives in the laminar cooling device 4. In this, it is cooled from an inlet temperature ET LK to an outlet temperature AT LK within a second cooling phase t LK .
  • the set cooling rate is between 30 and 150 ° C / s.
  • second phases bainite, martensite or residual austenite
  • the excretion state of the hot strip W is also controlled in this way.
  • Table 1 compares the structure components and the hardness of hot strips produced from steels "Stahl” - “Stahl2", which were produced according to the method according to the invention explained above, with the structure components and the hardness of hot strips of the same composition, which are produced in a conventional manner have been cooled in air in two laminar cooling devices with intervening cooling.
  • Fig. 3 is for the steel in a solid line the course CLK of that structural change, which occurs when a hot strip is first in the manner according to the invention for the time t CK a compact cooling with a cooling rate of 250 ° C / s, then one Intermediate cooling phase t PAUSE and finally a laminar cooling cycle for the time t LK , contrasted with the LLK course of the structural transformation drawn in dashed lines, which occurs in a conventional combination of two laminar cooling systems with intermediate cooling in air.
  • Table 1 confirms the statement in FIG. 3.
  • Table 1 confirms the statement in FIG. 3.
  • Table 1 confirms the statement in FIG. 3.
  • those manufactured according to the invention Sample a structure with a finer grain structure than that generated by the conventional method. This has to Consequence that the hot strips produced according to the invention a good one despite the increased shares of the hard phases Show formability. This fact has been confirmed also for a TRIP steel ((in mass%) C: 0.2%, Al: 1.8 %, Mn: 1.6%).
  • Such steel pointed to conventional Production method an average ferrite grain diameter from 6 - 7 ⁇ m. With the procedure according to the invention this diameter is reduced to less than 3 ⁇ m.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Metal Rolling (AREA)
  • Heat Treatment Of Steel (AREA)
  • Package Frames And Binding Bands (AREA)
  • Manufacturing Of Electric Cables (AREA)
  • Heating, Cooling, Or Curing Plastics Or The Like In General (AREA)

Claims (14)

  1. Procédé de production d'un feuillard à chaud (W), qui est fabriqué en particulier à partir de brames coulées en continu réchauffées ou directement traitées dans la chaude de coulée, de brames minces ou d'une bande coulée à base d'un acier, qui contient (en % en masse) : C 0,001 - 1,05 %, Si ≤ 1,5 %, Mn 0,05 - 3,5 %, Al ≤ 2,5 %,
    ainsi qu'au choix un ou plusieurs des éléments :
    Cu, Ni, Mo en proportion ≤ 0,8%,
    N, Ti, Nb, V, Zn, B en proportion ≤ 0,5%,
    P en proportion ≤ 0,09%,
    Cr en proportion ≤ 1,5% et/ou
    S en proportion ≤ 0,02%,
    et
    pour le restant, du fer ainsi que les éléments d'accompagnement usuels,
    dans lequel l'acier peut également être traité au choix dans la phase liquide avec du Ca ou des alliages contenant du Ca,
    comprenant les étapes suivantes :
    laminage final en continu du feuillard à chaud (W),
    refroidissement en continu du feuillard à chaud (W) dans au moins deux phases successives (tCK, tLK) de refroidissement accéléré à une température finale,
    dans lequel la première phase (tCK) de refroidissement accéléré commence au plus tard trois secondes après la dernière passe du laminage final, et
    dans lequel le feuillard à chaud (W) est refroidi, pendant la première phase (tCK) de refroidissement accéléré, à une vitesse de refroidissement d'au moins 250°C/s.
  2. Procédé selon la revendication 1, caractérisé en ce que l'acier contient 0,005 à 0,4% en masse de silicium.
  3. Procédé selon la revendication 1, caractérisé en ce que :
    l'acier contient (en % en masse) : C ≤ 0,07 %, Si ≤ 0,2 %, Mn ≤ 0,6 %, Al ≤ 0,08 %,
    le feuillard à chaud (W) est laminé pendant le laminage final dans le domaine austénitique,
    le feuillard à chaud (W) est refroidi, dans la première phase (tCK) de refroidissement accéléré, d'une température supérieure à 850°C à une température de 680 à 750°C,
    le feuillard à chaud (W) est refroidi, dans la seconde phase (tLK) de refroidissement accéléré, à une température de moins de 600°C, et
    le feuillard à chaud (W) est ensuite bobiné.
  4. Procédé selon la revendication 1, caractérisé en ce que l'acier contient (en % en masse) : C 0,04 - 0,09 %, Si ≤ 0,2 %, Mn 0,5 - 2,0 %, P 0,02 - 0,09 %, Cr ≤ 0,9 %,
    le feuillard à chaud (W) est refroidi, après laminage final, dans la première phase (tCK) de refroidissement accéléré, d'une température supérieure à 800°C à une température de 650 à 730°C,
    le feuillard à chaud (W) est refroidi, dans la seconde phase (tLK) de refroidissement accéléré, à une température de moins de 500°C, et
    le feuillard à chaud (W) est ensuite bobiné.
  5. Procédé selon la revendication 1, caractérisé en ce que l'acier contient (en % en masse) : C 0,25 - 1,05 %, Si ≤ 0,25 %, Mn ≤ 0,6 %,
    le feuillard à chaud (W) est refroidi, après laminage final, dans la première phase (tCK) de refroidissement accéléré, d'une température supérieure à 800°C à une température de 530 à 620°C,
    le feuillard à chaud (W) est refroidi, dans la seconde phase (tLK) de refroidissement accéléré, à une température de moins de 500°C, et
    le feuillard à chaud (W) est ensuite bobiné.
  6. Procédé selon la revendication 1, caractérisé en ce que l'acier contient (en % en masse) : C 0.12 - 0.3 %, Mn 1.2 - 3.5 %, Al 1.1 - 2.2 %,
    le feuillard à chaud (W) est refroidi, après laminage final, dans la première phase (tCK) de refroidissement accéléré, d'une température, qui se situe entre la température Ar3 et une température de Ar3+150°C, à une température, qui se situe jusqu'à 50°C en dessous de la température Ar3,
    le feuillard à chaud (W) est refroidi, dans la seconde phase (tLK) de refroidissement accéléré, à une température de 350 à 550°C, et
    le feuillard à chaud (W) est ensuite bobiné.
  7. Procédé selon la revendication 1, caractérisé en ce que l'acier contient (en % en masse) : C 0,04 - 0,09 %, Si 0,5 - 1,5 %, Mn 0,5 - 2,0 %, Al 0,4 - 2,5 %, P ≤ 0,09 %, Cr ≤ 0,9 %,
    le feuillard à chaud (W) est refroidi, après laminage final, dans la première phase (tCK) de refroidissement accéléré, d'une température supérieure à 800°C à une température de 650 à 730°C,
    le feuillard à chaud (W) est refroidi, dans la seconde phase (tLK) de refroidissement accéléré, à une température de moins de 500°C, et
    le feuillard à chaud (W) est ensuite bobiné.
  8. Procédé selon la revendication 1, caractérisé en ce que l'acier contient (en % en masse) : C 0,07 - 0,22 %, Si 0,1 - 0,45 %, Mn 0,2 - 1,5 %,
    le feuillard à chaud (W) est refroidi, après laminage final, dans la première phase (tCK) de refroidissement accéléré, d'une température supérieure à 800°C à une température de 650 à 730°C,
    le feuillard à chaud (W) est refroidi, dans la seconde phase (tLK) de refroidissement accéléré, à une température de moins de 500°C, et
    le feuillard à chaud (W) est ensuite bobiné.
  9. Procédé selon la revendication 1, caractérisé en ce que l'acier contient (en % en masse) : C 0,07 - 0,22 %, Si 0,1 - 0,45 %, Mn 0,2 - 1,5 %,
    le feuillard à chaud (W) est refroidi, après laminage final, dans la première phase (tCK) de refroidissement accéléré, d'une température supérieure à 800°C à une température de 580 à 650°C,
    le feuillard à chaud (W) est refroidi, dans la seconde phase (tLK) de refroidissement accéléré, à une température de moins de 500°C, et
    le feuillard à chaud (W) est ensuite bobiné.
  10. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que le feuillard à chaud (W) parcourt une phase de refroidissement intermédiaire (tPAUSE) entre la première phase (tCK) de refroidissement accéléré et la seconde phase (tLK) de refroidissement accéléré, pendant laquelle le feuillard à chaud (W) est exposé à un refroidissement à l'air.
  11. Procédé selon la revendication 10, caractérisé en ce que la phase de refroidissement intermédiaire (tPAUSE) dure au moins une seconde.
  12. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que la première phase (tCK) de refroidissement accéléré commence au plus tard deux secondes après la dernière passe du laminage final.
  13. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce qu'on effectue au moins l'une des passes de laminage pendant le laminage final dans le domaine austénitique en dessous d'une température de Ar3+80°C et on atteint un taux de réduction total des passes de plus de 30%.
  14. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que le feuillard à chaud (W) est refroidi, dans la seconde phase (tLK) de refroidissement accéléré, à une vitesse de refroidissement d'au moins 30°C/s.
EP00906372A 1999-03-13 2000-02-24 Procede de production de feuillard a chaud Revoked EP1169486B1 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE19911287 1999-03-13
DE19911287A DE19911287C1 (de) 1999-03-13 1999-03-13 Verfahren zum Erzeugen eines Warmbandes
PCT/EP2000/001517 WO2000055381A1 (fr) 1999-03-13 2000-02-24 Procede de production de feuillard a chaud

Publications (2)

Publication Number Publication Date
EP1169486A1 EP1169486A1 (fr) 2002-01-09
EP1169486B1 true EP1169486B1 (fr) 2003-05-02

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Application Number Title Priority Date Filing Date
EP00906372A Revoked EP1169486B1 (fr) 1999-03-13 2000-02-24 Procede de production de feuillard a chaud

Country Status (7)

Country Link
US (1) US6855218B1 (fr)
EP (1) EP1169486B1 (fr)
JP (1) JP2002539330A (fr)
AT (1) ATE239097T1 (fr)
DE (2) DE19911287C1 (fr)
ES (1) ES2195867T3 (fr)
WO (1) WO2000055381A1 (fr)

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2001023625A1 (fr) * 1999-09-29 2001-04-05 Nkk Corporation Tole d'acier et son procede de fabrication
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EP1169486A1 (fr) 2002-01-09
WO2000055381A1 (fr) 2000-09-21
DE19911287C1 (de) 2000-08-31
US6855218B1 (en) 2005-02-15
JP2002539330A (ja) 2002-11-19
DE50001976D1 (de) 2003-06-05
ES2195867T3 (es) 2003-12-16

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