EP1396549B1 - Procédé pour la fabrication d'une bande d' acier exempt de perlite laminée à chaud et bande à chaud obtenue - Google Patents

Procédé pour la fabrication d'une bande d' acier exempt de perlite laminée à chaud et bande à chaud obtenue Download PDF

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Publication number
EP1396549B1
EP1396549B1 EP02019314A EP02019314A EP1396549B1 EP 1396549 B1 EP1396549 B1 EP 1396549B1 EP 02019314 A EP02019314 A EP 02019314A EP 02019314 A EP02019314 A EP 02019314A EP 1396549 B1 EP1396549 B1 EP 1396549B1
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EP
European Patent Office
Prior art keywords
hot
process according
amounts
cooling
rolled strip
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
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EP02019314A
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German (de)
English (en)
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EP1396549A1 (fr
Inventor
Andreas Nuss
Thomas Dr.-Ing. Heller
Günter Dipl.-Ing. Stich
Udo Van Hasz
Ulrich Dr. Rudolphi
Eberhard Dr.-Ing. Sowka
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel AG
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Priority to AT02019314T priority Critical patent/ATE343649T1/de
Priority to DE50208550T priority patent/DE50208550D1/de
Priority to EP02019314A priority patent/EP1396549B1/fr
Publication of EP1396549A1 publication Critical patent/EP1396549A1/fr
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Publication of EP1396549B1 publication Critical patent/EP1396549B1/fr
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Classifications

    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • C21D8/0215—Rapid solidification; Thin strip casting
    • 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
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C21D2211/009—Pearlite
    • 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
    • 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

Definitions

  • High-strength steels with good elongation characteristics and processability are required in the field of vehicle construction, in general steel construction as well as in mechanical and apparatus engineering for the production of components that absorb high forces and can be optimally adapted in shape to the respective design requirements.
  • a high-strength, readily deformable hot-rolled strip intended for these purposes and a method for its production are known from EP 0 295 500 B1.
  • the steel used for the production of the known hot strip contains, in addition to iron and the inevitable impurities due to the preparation (in% by weight) 0.15 to less than 0.3% C, 0.5 to 2.0% Si, 0.5 to 2.0% Mn.
  • 0.0005 to 0.0100 Ca or 0.005 to 0.050% rare earth metals may be contained in the steel.
  • the known steel is hot rolled according to EP 0 295 500 B1 in a hot rolling scale with a hot rolling end temperature which deviates from the Ar 3 temperature with a maximum of 50 ° C.
  • the hot strip is cooled in a controlled manner on the roller table following the hot rolling scale, with EP 0 295 500 B1 proposing two ways of controlled cooling.
  • the band On the first path, the band is in a first stage at relatively low Cooling rates of 15 to 45 K / s and then cooled in a second stage with a respective increased cooling rate, which was between 35 to 80 K / s.
  • the cooling is carried out in three stages with cooling rates, which was 50 to 85 K / s in the first stage, 10 to 45 K / s in the second stage and 35 to 80 K / s in the third stage.
  • the reel temperatures reached in both variants were between 370 and 520 ° C.
  • a cooling of the hot strip in the coil is carried out according to the method known from EP 0 295 500 B1.
  • the strip is cooled at a cooling rate of at least 30 ° C / h to a temperature below 200 ° C accelerated.
  • Hot rolled strip produced in this way has a structure formed of ferrite, retained austenite and bainite.
  • the formation of perlite and martensite is largely suppressed, so as not to hinder the formation of retained austenite.
  • the hot strip produced according to the known method has a high strength at high ductility. In practice, however, shows that its production is complex. Also, in the case of sudden loads due to high kinetic energies, such as typically occur in motor vehicles in an accident that it is difficult to meet with the known steel, the ever increasing demands for optimized crash behavior. In addition, the conventional production of the known hot strip is expensive.
  • EP-A-0 881 306 discloses a method for producing a steel strip from an iron and unavoidable impurities (in% by weight) 0.05-0.5% C, 0.5 - Alloy containing 2.5% Mn and 0.3 - 0.8% Si, in which such a multiphase steel is cast in conventional slab casting into slabs, then the slabs at temperatures of 1150 ° C - 1300 ° C. are annealed and then hot rolled into a hot strip, cooled and reeled, the cooling is carried out in two stages.
  • a comparable process, also based on conventional slab casting, is known from US-A-5470529.
  • US-B1-6328826 mentions a method for producing a pearlite-free TRIP steel strip containing steel besides Si, Mn also optionally Ti and / or Nb.
  • EP-A-0 789 090 it is also known to desalt a conventionally produced slab as well as from JP 2000 034537 after casting into thin slabs before hot rolling.
  • the object underlying the invention was therefore to provide a cost-effective and practical feasible method, which reliably enables the production of optimized in terms of their strength and deformation properties hot strips.
  • a TRIP-grade hot strip is produced which has a combination of deformation properties and strength values due to optimized tuning of its alloy contents and the manner of its manufacture on the one hand simplifies its processing and on the other hand contributes to an improved force absorption capacity in the event of sudden exposure to high deformation energies.
  • the Si and Mn content of the processed steel are adjusted so that in the resulting hot strip sufficient for the achievement of the TRIP effect amount of retained austenite is guaranteed.
  • Manganese stabilizes retained austenite remaining in the steel after controlled cooling.
  • the presence of silicon on the one hand supports the formation of ferrite and also improves the ductility of the steel.
  • the silicon content has a favorable effect with regard to the enrichment of the austenite not converted with hot strip in the course of hot strip production.
  • the limitation of the Si and Mn contents according to the invention also causes an improvement of the surface quality of the hot strips. These effects are particularly certain when the sum of the contents of silicon and manganese is 1.5-2.5% by weight, in particular 1.8-2.3% by weight.
  • An essential component of the alloy processed according to the invention in addition to the contents of silicon and manganese, is the content of at least one of the elements niobium and titanium.
  • TRIP steels contain retained austenite and as a result have the effect of so-called "TRANSformation Induced Plasticity". What is essential here is the combination of process control via a cast roll mill and the presence of Ti and / or Nb, as prescribed by the invention.
  • micro-alloying elements are deposited in the slab during conventional production via slab casting and only partially dissolve again during the heating of the slab before hot rolling. In the case of the production of a thin slab prescribed according to the invention, however, these elements remain in solution until the start of hot rolling in solution, due to the heat transfer which normally takes place in a tunnel furnace between thin slab production and hot rolling. These precipitations improve the grain refining of the finished hot strip and on the one hand contribute to an increase in the residual austenite content and, on the other hand, to a stabilization of the retained austenite against transformation into martensite. Steel produced and assembled according to the invention is therefore able to bear higher loads.
  • the resulting thin slabs After casting the steel used according to the invention into thin slabs whose thickness is typically 40 to 70 mm, the resulting thin slabs enter a tunnel kiln at temperatures ranging from 850 to 1050 ° C.
  • the inlet temperature is not less than 950 ° C in order to avoid the formation of precipitates at this stage of hot strip production.
  • the thin slabs are annealed at 1000 - 1200 ° C in the run.
  • the tunnel oven temperature is preferably limited to the range of 1000 - 1050 ° C, in order to avoid excessive scale formation. In this way, the lying at about 900 ° C temperature range is safely avoided, in which there is a precipitation maximum in the steel used in the invention. Instead, the micro-alloying elements are kept in solution, with the result that they are finer and more homogeneously distributed in the finished product.
  • the residence time in the tunnel kiln is limited to 10 to 60 minutes, preferably 15 to 35 minutes.
  • the limitation of the annealing time immediately causes an increase in the output of the casting-rolling plant used.
  • the thin slabs are descaled in a targeted manner after annealing in a scale scrubber.
  • the pressure with which the cleaning liquid, usually water, is added to the slabs is, according to the invention, at least 300 bar in order to achieve the greatest possible removal of all residues present on the surfaces of the slab.
  • the amount of fayalite present on the slabs, which otherwise can cause the formation of unwanted red scale in the further process is largely removed in this way.
  • hot rolled strip is rolled from the thin slabs at hot rolling end temperatures of 750 to 1000 ° C, the thickness of which is typically 0.8 - 10 mm.
  • the specific final temperature selected within the given temperature range can influence the fineness and the composition of the structure of the hot-rolled strip obtained.
  • Hot rolling end temperatures above the Ar3 temperature can be adjusted if larger amounts of retained austenite are to be formed.
  • the Formation of a fine-grained microstructure can also be assisted by the fact that, if the finish rolling is carried out in several passes, the deformation in the last pass of the hot rolling is at least 5%, preferably 15-25%.
  • the fine granularity achieved by the various measures of the procedure according to the invention contributes not only to the deformability, but also to the stabilization of the desired residual austenite content, together with the chemical composition of the processed steel.
  • the fine distribution of the individual phases present in the hot strip produced according to the invention also hampers the conversion of the retained austenite into martensite in a mechanical manner.
  • the hot strip according to the invention has not only a high chemical stability but also a high geometric stability with respect to the residual austenite part. This stability of the structure contributes to the fact that residual austenite can still be present in the finished component produced from the hot strip.
  • the controlled cooling which takes place after hot rolling also has a significant influence on the shape of the microstructure and mechanical properties of the finished hot strip.
  • the cooling can specifically influence the proportions of the individual phases as well as the strength and elongation properties.
  • the controlled cooling takes place for this purpose by the hot strip in a first stage, starting from the hot rolling end temperature with a cooling rate of 70 to 500 K / s to a 600 - 750 ° C amounting intermediate temperature is cooled by the hot strip then in a second stage for Cooling in air for 2 to 13 seconds and then cooling the hot strip in a third stage with a 30 to 200 K / s cooling rate to a reeling temperature which is 300 - 530 ° C.
  • the cooling rate in the first stage of cooling is at least 150 K / s, preferably 300 K / s.
  • a cooling pause takes place in the second phase in order to allow the formation of larger amounts of ferrite and the enrichment of the retained austenite with carbon.
  • the duration of the second stage of cooling may preferably be limited to 4 to 8 seconds for this purpose.
  • the accelerated cooling is continued to suppress the formation of pearlite and grain growth.
  • Another variant of the invention provides that the controlled cooling takes place in that the hot strip is cooled continuously from the hot rolling end temperature to the coiler temperature at a cooling rate of 10 to 70 K / s. In this way, a hot strip with the inventively desired microstructure can be produced.
  • the hot strip continues to cool after being coiled in the coil. So that it does not come to the formation of undesirably large amounts of bainite at the expense of Restaustenits, it is advantageous if the hot strip is cooled accelerated after a rest period in the coil. It has been found that the desired distribution of the individual phase components sets when the accelerated cooling of the coil begins after a rest period lying in the range of 2 to 30. In this case, the cooling can be accelerated by applying the coil with a cooling fluid. Depending on the respectively required cooling rates, a liquid, for example water, or an air stream can be used for this purpose.
  • the hot strip produced according to the invention has in each case at least three of the structural constituents ferrite, bainite, retained austenite or martensite.
  • the total content of martensite and retained austenite should be at least 8%.
  • the lowest possible martensite contents are aimed at avoiding carbon loss to the detriment of the retained austenite. Accordingly, the invention provides that the carbon content of the retained austenite should be more than 1%. This carbon content can be determined, for example, by X-ray analysis.
  • hot strips can be produced in which the product RM * A5 of tensile strength Rm and elongation at break A5 is at least 19,000 MPa *% and the product Rm * A80 consists of tensile strength Rm and elongation at break A80 at least 16,000 MPa *%, in particular 17,000 MPa *%, is.
  • Hot rolled strip produced in accordance with the invention is particularly suitable for use in vehicle construction, in steel construction, in general machine and apparatus construction and in shipbuilding.
  • the molten steels S1, S2, S3 were cast in a casting-rolling plant into thin slabs having an average thickness of 55 mm, which, in a continuous casting operation, entered a tunnel kiln in which they were heated at average temperatures of 1050 ° C in the course of an annealing have been subjected. After leaving the furnace, the thin slabs have passed a scale scrubber, in which their surface has been freed from the scale by being exposed to a cleaning liquid which has been sprayed off at more than 300 bar.
  • the thus cleaned thin slabs are then run into a multi-stand hot rolling stand, in which they at a hot rolling end temperature ET in several passes too in each case a hot strip with a thickness d have been finished hot rolled.
  • the hot strips W1-W4 produced from the melts S1 and S2 have been cooled in three stages.
  • the hot strips in question have each been cooled at a cooling rate Ag1 to an intermediate temperature ZT1.
  • the hot strips were cooled to a temperature ZT2 at a cooling rate Ag2.
  • the hot strips are then cooled to the temperature HT with which they have been rewound.
  • the final rolling temperatures ET observed during the production of the hot strips W1-W4 from the melts S1 and S2, the hot strip thicknesses d, the respective cooling rates Ag1, the intermediate temperature ZT1, the time t2 of the intermediate cooling in air, the respective cooling rates Ag2, the intermediate temperatures ZT2 and the reeling temperatures HT are given in Table 2.
  • Table 3 shows the mechanical properties tensile strength Rm, uniform elongation Ag, elongation A80 and elongation A5 and the respective product of Rm * A5 and Rm * A80 determined for the respective hot strips W1 - W4.
  • Table 4 shows the relevant process parameters and the thickness d of the hot strips W5 to W10.
  • Table 5 contains the corresponding information on the respective tensile strength Rm, uniform elongation Ag, elongation A80 and elongation A5 as well as the respective product of Rm * A5 and Rm * A80.

Claims (24)

  1. Procédé de préparation d'un feuillard d'acier laminé à chaud, exempt de perlite, avec propriétés TRIP et une résistance en traction d'au moins 600 MPa, dans lequel on réalise dans un processus de travail continu sur une installation de laminage de coulée continue, au moins les étapes suivantes :
    - coulée d'une masse fondue d'acier, en brames fines, qui en plus du fer et des impuretés inévitables, contient (en % en poids) :
    C : 0,06-0,3%
    Si : 0,1-3,0%
    Mn : 0,3-1,1%
    où la somme des teneurs en Si et en Mn se situe dans l'intervalle allant de 1,5 à 3,5%,
    au moins un des éléments Ti ou Nb est présent en une teneur de chaque fois 0,005-0,15%,
    ainsi qu'au choix, un ou plusieurs des éléments suivants :
    Cr : maximum 0,8%
    Mo : maximum 0,8%
    Cu : maximum 1%
    Ni : maximum 1%
    - recuit des brames fines parcourant un four de recuit à une température d'entrée allant de 850 à 1050°C, à des températures de recuit allant de 1000 à 1200°C pendant une période de 10 à 60 minutes,
    - décalaminage des brames fines dans un laveur de calamine, sous une pression de pulvérisation du liquide utilisé pour le décalaminage d'au moins 300 bar,
    - laminage à chaud terminal des brames fines en une feuillard à chaud à des températures finales de laminage à chaud, qui se situent dans l'intervalle allant de 750 à 1000°C,
    - refroidissement contrôlé du feuillard à chaud obtenu jusqu'à une température de bobineuse,
    - bobinage du feuillard à chaud.
  2. Procédé selon la revendication 1, caractérisé en ce que la somme des teneurs en Si et en Mn se situe dans l'intervalle allant de 1,5 à 2,5% en poids.
  3. Procédé selon la revendication 1, caractérisé en ce que la somme des teneurs en Si et en Mn se situe dans l'intervalle allant de 1,8 à 2,3% en poids.
  4. Procédé selon l'une des revendications précédentes, caractérisé en ce que la température de recuit est inférieure à 1150°C.
  5. Procédé selon l'une des revendications précédentes, caractérisé en ce que la durée du recuit se situe dans l'intervalle allant de 15 à 35 minutes.
  6. Procédé selon l'une des revendications précédentes, caractérisé en ce que la déformation globale obtenue pendant le laminage à chaud final se situe dans l'intervalle allant de 2,8 à 3,7.
  7. Procédé selon la revendication 6, caractérisé en ce la déformation globale est d'au moins 2,5.
  8. Procédé selon l'une des revendications précédentes, caractérisé en ce que le laminage final est réalisé en plusieurs passes et la déformation se situe à au moins 5% dans la dernière passe.
  9. Procédé selon la revendication 8, caractérisé en ce la déformation dans la dernière passe se situe dans l'intervalle allant de 15 à 25%.
  10. Procédé selon l'une des revendications précédentes, caractérisé en ce que la température du laminage final se situe sous la température Ar3.
  11. Procédé selon l'une des revendications précédentes, caractérisé en ce que le refroidissement contrôlé est réalisé en ce que le feuillard à chaud est refroidit dans une première étape, partant de la température de laminage final, avec une vitesse de refroidissement allant de 70 à 500 K/s jusqu'à une température intermédiaire allant de 600 à 750°C, en ce que le feuillard à chaud est ensuite refroidi dans une deuxième étape, pendant 2 à 13 secondes à l'air, et en ce que le feuillard à chaud est refroidi dans une troisième étape, avec une vitesse de refroidissement allant de 30 à 200 K/s jusqu'à la température de bobinage, qui se situe à 300-530°C.
  12. Procédé selon la revendication 11, caractérisé en ce que la vitesse de refroidissement dans la première étape du refroidissement, se situe à au moins 150K/s.
  13. Procédé selon la revendication 12, caractérisé en ce que la vitesse de refroidissement dans la première étape du refroidissement, se situe à au moins 300K/s.
  14. Procédé selon l'une des revendications 11 à 13, caractérisé en ce que la durée de la deuxième étape du refroidissement, se situe dans l'intervalle allant de 4 à 8 secondes.
  15. Procédé selon l'une des revendications 1 à 10, caractérisé en ce que le refroidissement contrôlé est réalisé en ce que le feuillard à chaud est refroidi avec une vitesse de refroidissement allant de 10 à 70 K/s, en continu depuis la température finale de laminage à chaud jusqu'à la température de bobinage.
  16. Procédé selon l'une des revendications 1 à 10, caractérisé en ce que le refroidissement contrôlé est réalisé en ce que le feuillard à chaud est refroidi dans une première étape, en 1 à 7 secondes, jusqu'à une température qui se situe à environ 80°C au-dessus de la température de bobinage et en ce que le feuillard à chaud est ensuite refroidi à l'air jusqu'à la température de bobinage, qui se situe dans l'intervalle allant de 300 à 530°C.
  17. Procédé selon l'une des revendications précédentes, caractérisé en ce que le feuillard à chaud est refroidi de manière accélérée en bobine, après un temps de repos.
  18. Procédé selon la revendication 17, caractérisé en ce que le temps de repos se situe dans l'intervalle allant de 2 à 30 minutes.
  19. Procédé selon la revendication 17 ou 18, caractérisé en ce que le refroidissement accéléré est réalisé en soumettant la bobine à un fluide de refroidissement.
  20. Procédé selon l'une des revendications précédentes, caractérisé en ce que le feuillard à chaud obtenu présente au moins trois des constituants de structure ferrite, bainite, austénite résiduelle ou martensite.
  21. Procédé selon la revendication 20, caractérisé en ce que la somme de la teneur en martensite et en austénite résiduelle est d'au moins 8%.
  22. Procédé selon la revendication 20 ou 21, caractérisé en ce que la teneur en carbone de l'austénite résiduelle est supérieure à 1%.
  23. Procédé selon l'une des revendications précédentes, caractérisé en ce que le produit de la résistance en traction Rm et de l'allongement à la rupture A5 du feuillard à chaud obtenu s'élève à au moins 19 000 MPa*%.
  24. Procédé selon l'une des revendications précédentes, caractérisé en ce que le produit de la résistance en traction Rm et de l'allongement à la rupture A80 du feuillard à chaud obtenu s'élève à au moins 17 000 MPa*%.
EP02019314A 2002-08-28 2002-08-28 Procédé pour la fabrication d'une bande d' acier exempt de perlite laminée à chaud et bande à chaud obtenue Expired - Lifetime EP1396549B1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
AT02019314T ATE343649T1 (de) 2002-08-28 2002-08-28 Verfahren zum herstellen eines perlitfreien warmgewalzten stahlbands und nach diesem verfahren hergestelltes warmband
DE50208550T DE50208550D1 (de) 2002-08-28 2002-08-28 Verfahren zum Herstellen eines perlitfreien warmgewalzten Stahlbands und nach diesem Verfahren hergestelltes Warmband
EP02019314A EP1396549B1 (fr) 2002-08-28 2002-08-28 Procédé pour la fabrication d'une bande d' acier exempt de perlite laminée à chaud et bande à chaud obtenue

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP02019314A EP1396549B1 (fr) 2002-08-28 2002-08-28 Procédé pour la fabrication d'une bande d' acier exempt de perlite laminée à chaud et bande à chaud obtenue

Publications (2)

Publication Number Publication Date
EP1396549A1 EP1396549A1 (fr) 2004-03-10
EP1396549B1 true EP1396549B1 (fr) 2006-10-25

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EP02019314A Expired - Lifetime EP1396549B1 (fr) 2002-08-28 2002-08-28 Procédé pour la fabrication d'une bande d' acier exempt de perlite laminée à chaud et bande à chaud obtenue

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US8444780B2 (en) * 2009-02-20 2013-05-21 Nucor Corporation Hot rolled thin cast strip product and method for making the same
CN101717890B (zh) * 2009-11-26 2012-09-05 三一重工股份有限公司 一种用于平地机刀片的铸造低合金钢及制备方法
CN109536686A (zh) * 2018-12-12 2019-03-29 贵阳市白云区科创生产力促进中心 一种铌微合金化中锰trip钢的制备方法
KR102209552B1 (ko) 2018-12-19 2021-01-28 주식회사 포스코 구멍확장성이 우수한 고강도 열연강판 및 그 제조방법
CN112522595B (zh) * 2019-09-19 2022-10-21 宝山钢铁股份有限公司 高强薄规格耐火耐候钢板/钢带及其生产方法
KR102404770B1 (ko) 2019-12-20 2022-06-07 주식회사 포스코 항복비가 우수한 고강도 열연강판 및 그 제조방법
KR102403648B1 (ko) 2020-11-17 2022-05-30 주식회사 포스코 고강도 열연강판, 열연 도금강판 및 이들의 제조방법
KR102487759B1 (ko) 2020-12-18 2023-01-12 주식회사 포스코 고강도 열연강판, 열연 도금강판 및 이들의 제조방법

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EP0295500B2 (fr) * 1987-06-03 2003-09-10 Nippon Steel Corporation Tôle d'acier laminée à chaud à haute résistance à la traction et à formabilité excellente
JP3390584B2 (ja) * 1995-08-31 2003-03-24 川崎製鉄株式会社 熱延鋼板およびその製造方法
US6190469B1 (en) * 1996-11-05 2001-02-20 Pohang Iron & Steel Co., Ltd. Method for manufacturing high strength and high formability hot-rolled transformation induced plasticity steel containing copper
BE1011149A3 (fr) * 1997-05-12 1999-05-04 Cockerill Rech & Dev Acier ductile a haute limite elastique et procede de fabrication de cet acier.
JP2000034537A (ja) * 1998-07-16 2000-02-02 Nippon Steel Corp 被切削加工性の良好な高強度熱延鋼板およびその製造方法
FR2796966B1 (fr) * 1999-07-30 2001-09-21 Ugine Sa Procede de fabrication de bandes minces en acier de type "trip" et bandes minces ainsi obtenues

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ATE343649T1 (de) 2006-11-15
EP1396549A1 (fr) 2004-03-10
DE50208550D1 (de) 2006-12-07

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