EP1411140B1 - Procédé de fabrication de tôles ou de bandes d'acier laminées à froid ayant une excellente formabilité - Google Patents

Procédé de fabrication de tôles ou de bandes d'acier laminées à froid ayant une excellente formabilité Download PDF

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Publication number
EP1411140B1
EP1411140B1 EP03018184A EP03018184A EP1411140B1 EP 1411140 B1 EP1411140 B1 EP 1411140B1 EP 03018184 A EP03018184 A EP 03018184A EP 03018184 A EP03018184 A EP 03018184A EP 1411140 B1 EP1411140 B1 EP 1411140B1
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Prior art keywords
hot
process according
rolling
leaving
last
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EP03018184A
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German (de)
English (en)
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EP1411140A1 (fr
Inventor
Bernhard Dr.-Ing. Engl
Klaus-Dieter Horn
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel AG
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties 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
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • 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
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0478—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular surface treatment

Definitions

  • the invention relates to a method for producing a cold-rolled steel strip or sheet.
  • such tape or sheet is used for the production of body parts required in vehicle construction.
  • a good formability is characterized by a high n-value characterizing the iron drawability and a likewise high r value characterizing the deep drawability.
  • a method for producing a hot-rolled steel strip having a high r-value in which a not more than 0.015 wt .-% C, 1.0 - 2.0 % By weight of Mn, 0.005 to 0.10% by weight of Al, 0.01 to 0.06% by weight of Nb, 0.01 to 0.1% by weight of Ti and the remainder containing iron and unavoidable impurities Steel in a reheating furnace to a temperature of not less than 1150 ° C is heated.
  • the thus heated steel is pre-rolled, wherein the rough rolling is carried out in a temperature range of 980 ° C to 1100 ° C with a reduction in thickness of not less than 20% per pass.
  • the pre-rolled steel is hot rolled in a temperature range of Ar 3 to 930 ° C while maintaining a total reduction of not less than 90% before being coiled at 600 ° C to 800 ° C.
  • the hot strip thus produced should have a high formability, the essential feature of the known from DE 37 04 828 C2 method is seen in that the developed IF steel has a high Mn content and is free of dissolved C and N and that the steel thus composed undergoes a large reduction within a certain temperature range, then cooled and then rewound within a certain temperature range.
  • a process for the production of fine formable metal sheet with a cold strip final thickness of at most 0.3 mm is known from DE 101 17 118 C1.
  • slabs or thin slabs are then reheated after cooling to a temperature ranging from 1080 ° C to 1150 ° C for a maximum of eight hours holding time.
  • the reheated slabs or slabs are then hot rolled into a hot strip at a number of passes in a hot rolling mill at a final rolling temperature above the Ar 3 temperature and coiled at temperatures ranging from 590 ° C to 660 ° C. After coiling, the hot strip obtained is cold rolled to cold strip and subjected to a continuous annealing.
  • JP 07-018381 A discloses a method for producing an excellent deep-drawable cold-rolled steel sheet in which a steel other than iron (in% by weight) is subjected to an ultra-low C content by Max. 0.015%, a Mn content of max. 0.40%, a P content of max. 0.020%, an Al content of max. 0.080%, an N content of max. 0.005%, a Ti content of 0.005-0.020% and an S content of max. 0.015%.
  • N, S, Mn and Ti must simultaneously satisfy the condition 3.42 N + S / 16 (Mn + 0.10) ⁇ Ti ⁇ 10 N + S / 8 (Mn + 0.10) to obtain the To allow formation of TiN precipitates, which decisively influence the thermoformability of the steel processed in the known manner.
  • the thus composed steel is continuously cast at a certain take-off speed and then hot rolled.
  • a degree of deformation of at least 40% and in the final stage of finish hot rolling a degree of deformation of at least 20% is to be achieved.
  • the hot rolling temperatures are in the known method in each case above the Ar 3 temperature in order to ensure the lowest possible property dispersion in the bands obtained after hot rolling. Hot rolling is followed by targeted cooling of the hot strip, at which cooling rates of at least 30 ° C./s must be achieved.
  • the object of the invention was therefore to provide a method by which can be produced at low production cost effort cold strips or sheets with widely dispersed composition that have a compared to conventionally manufactured products further improved formability.
  • the invention is based on the knowledge that a decisive improvement in the formability of steel strips and steel sheets of the type in question can be achieved not only by a suitable, the finished hot rolling upstream processing of each used precursor, but in particular by the inventive choice of hot rolling.
  • cold sheets produced according to the invention are distinguished by outstanding r values and, correspondingly, excellent deep drawability.
  • an embodiment of the invention provides that a soft steel alloy is processed, each containing (in wt .-%) 0.01 - 0.1% C, 0.1 - 0.5% Mn, up to 0.03% P, up to 0.03% S, 0.01-0.1% Al, less than 0.005% Ti, less than 0.005% Nb and up to 0.01% B, and the remainder iron and unavoidable impurities may contain.
  • an IF steel may typically contain (in% by weight) less than 0.01% C, less than 0.2% Mn, less than 0.02% S, less than 0.02% P less than 0.05% Al, less than 0.005% N, 0.02-0.1% Ti, up to 0.05% Nb, and less than 0.001% B.
  • the individual alloy components can be coordinated with one another within the ranges generally specified by the invention in such a way that an optimum work result is achieved.
  • the suitably alloyed molten steel is poured into a hot-rolling starting material, such as slabs or thin slabs. These are heated to a preheating temperature, which is preferably in the range of 1000 ° C to 1300 ° C. Subsequently, the starting material is fed into a hot rolling mill, where it is rolled into hot strip.
  • This hot rolling comprises a multi-stage finish rolling, which may be preceded by rough rolling if necessary.
  • the improvement sought by the invention is achieved in each case that in the last four stages of Fertigwarmwalzens the remaining, over these four stages to be handled Bacumformgrad as high as possible.
  • the invention requires that over the last four stands of the hot roll stand the Retroformgrad should be at least 80%. In the case of a classic rolling scale comprising seven stands, it is therefore necessary, via the stands 4, 5, 6 and 7, to set a total degree of deformation of at least 80%, preferably 85%, in order to achieve the desired increase in the r value.
  • the division of the individual thickness decreases on the individual last of the hot strip traversed rolling stands is not arbitrary, but follows a precisely graded plan.
  • the invention still stipulates that the overall degree of transformation to be handled over the last three rolling stands is still at least 65%, preferably 75%, which is at least 50% above the last two stands of the rolling scale 60% and the degree of deformation reached over the last frame of the squadron must be at least 25%, preferably at least 30% or even at least 35%.
  • the effect of the procedure according to the invention is all the more favorable, the higher the overall conversion remaining for the last four scaffolds.
  • the temperature at which the hot rolling is carried out in the last four continuous stands of the hot rolling stand is of importance. This should be chosen according to the invention so that the relevant passes of the hot rolling are carried out in deep austenite. Therefore, the invention contemplates rolling the last four passes at temperatures ranging from 950 ° C to 880 ° C in close proximity to the Ar 3 transformation temperature. In this case, roller temperatures which are particularly close to the Ar 3 temperature, which range from 930 ° C. down to the Ar 3 temperature, are advantageous. In this case, the respective hot rolling temperatures are within a range in which the steel being processed is still certainly austenitic, but at the same time is at a level which ensures that work is done in the deep austenite favorable for the effects of the invention.
  • An operating parameter also to be considered according to the invention which is of importance for the properties of the product obtained, is the tape end speed.
  • This is at least 10 m / s, for unalloyed very soft steel, but preferably at least 15 m / s, in order to avoid recrystallization in the finishing scale between the rolling passes.
  • the high rolling or rolling speed is required, so that there is no recrystallization in the finishing scale, especially in very rekristallisationsfreudigem steel after the rolling passes between the individual Walgerüsten. In this way, a high cumulative degree of hot deformation is achieved, whereby the Texture base for the very high r-values on the hot strip produced according to the invention is set.
  • the cold strip is to be recrystallized after cold rolling in a continuous furnace, it has proven to be advantageous in view of the desired high r-values of steel sheets or strips produced according to the invention if the coiling temperature is at least 700 ° C. If, on the other hand, a "pan-cake microstructure" favorable for certain deformation tasks is to be produced in the cold-rolled sheet by a recrystallizing annealing carried out in the bundle under the hood, it is favorable to choose a reel temperature which is as low as possible and which does not exceed 550 ° C. "Pan-cake texture" is characterized by a stretched, relatively coarse grain.
  • the fabric of this nature and the texture associated therewith are particularly favorable if high degrees of deformation must be achieved during the cold forming of the cold sheet into a component.
  • a high reel temperature causes coarse, a low coiler temperature on the other hand fine carbides and nitrides. In principle, a few coarse precipitates are more favorable for cold strip recrystallization than many fine ones, since they have a less disturbing effect on the recrystallization process.
  • hot rolling scale slabs were hot rolled to hot strip W consisting of a 0.025 wt .-% C, 0.15 wt .-% Mn, each less than 0.01 wt .-% P and S, 0.04 wt. % Al, 0.003 wt .-% N, balance iron and unavoidable impurities containing mild steel have been poured.
  • the slabs were thoroughly warmed to a preheat temperature of 1250 ° C before being finish hot rolled in hot roll 8 to hot strip W at a hot rolling end temperature of 900 ° C.
  • the resulting hot strip was then coiled at a reel temperature of 520 ° C and rolled at a cold rolling degree of 75% to cold strip.
  • the cold strip in the coil in the annealing furnace at 700 ° C was annealed recrystallizing.
  • the slabs were heated to a preheating temperature of 1100 ° C, hot rolled in the hot rolling stand 8 at a hot rolling end temperature of 900 ° C to hot strip W.
  • the hot strip W has been coiled at a temperature of 720 ° C., cold-rolled with a cold rolling degree of 75% and recrystallized at 800 ° C. in a continuously passed continuous furnace.
  • the forming degrees ⁇ h1 to ⁇ h7 to be achieved over the individual respective rolling stands 1, 2, 3, 4, 5, 6, 7 are each set such that the for the last four rolling stands 4 , 5,6,7 of the rolling scale remaining remainders were significantly higher than in conventional production.
  • three erfindunsupplementarye hot rolling variants Ea, Eb and Ec have been compared to a conventionally performed hot rolling K compared to setting the highest possible for the last four rolling stands 4,5,6,7 remaining forming effects according to the invention.

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

Claims (25)

  1. Procédé de préparation d'un feuillard ou d'une tôle d'acier laminé à froid, qui comprend les étapes suivantes :
    - coulée d'une masse fondue d'acier contenant (en % en poids) C : ≤ 0,1%, Mn : ≤ 0,5%, P : < 0,03%, S : < 0,03%, Al : ≤ 0,1%, N : < 0,01%, Ti : < 0,1%, Nb : < 0,05%, B : ≤ 0,01%,
    le reste étant du fer et les impuretés usuelles, en un prématériau, comme des brames ou brames minces,
    - réchauffage à coeur du prématériau jusqu'à une température de réchauffage d'au moins 1000°C,
    - laminage à chaud du prématériau dans un train de laminage à chaud comprenant au moins quatre laminoirs, en un feuillard à chaud, où
    - le taux global de déformation εh4 obtenu par les quatre derniers laminoirs avant avoir quitté le train de laminage à chaud est au moins 80%,
    - le taux global de déformation εh3 obtenu par les trois derniers laminoirs avant avoir quitté le train de laminage à chaud est au moins 65%,
    - le taux global de déformation εh2 obtenu par les deux derniers laminoirs avant avoir quitté le train de laminage à chaud est au moins 50%,
    - le taux global de déformation εh1 obtenu par le dernier laminoir avant avoir quitté le train de laminage à chaud est au moins 25%,
    - le laminage à chaud est réalisé dans les quatre derniers laminoirs avant de quitter le train de laminage à chaud, à une température de laminage allant de 880°C à 950°C,
    - le laminage à chaud se termine à une température de laminage à chaud qui est ≥ à la température Ar3, et
    - la vitesse du feuillard obtenu lorsqu'il quitte le train de laminage est d'au moins 10 m/s,
    - le dévidage du feuillard chaud,
    - le laminage à froid du feuillard chaud en un feuillard froid,
    - le recuit de cristallisation du feuillard froid.
  2. Procédé selon la revendication 1, caractérisé en ce que la masse fondue d'acier contient 0,01% en poids de C.
  3. Procédé selon la revendication 1, caractérisé en ce que la masse fondue d'acier contient moins de 0,01% en poids de C.
  4. Procédé selon l'une des revendications précédentes, caractérisé en ce que la masse fondue d'acier contient au moins 0,1% en poids de Mn.
  5. Procédé selon l'une des revendications précédentes, caractérisé en ce que la masse fondue d'acier contient moins de 0,2% en poids de Mn.
  6. Procédé selon l'une des revendications précédentes, caractérisé en ce que la masse fondue d'acier contient moins 0,2% en poids de P et/ou moins de 0,02% en poids de S.
  7. Procédé selon l'une des revendications précédentes, caractérisé en ce que la masse fondue d'acier contient moins de 0,05% en poids de Al.
  8. Procédé selon l'une des revendications précédentes, caractérisé en ce que la masse fondue d'acier contient moins de 0,005% en poids de N.
  9. Procédé selon l'une des revendications précédentes, caractérisé en ce que la masse fondue d'acier contient moins de 0,005% en poids de Ti.
  10. Procédé selon l'une des revendications précédentes, caractérisé en ce que la masse fondue d'acier contient au moins 0,02% en poids de Ti.
  11. Procédé selon l'une des revendications précédentes, caractérisé en ce que la masse fondue d'acier contient moins de 0,005% en poids de Nb.
  12. Procédé selon l'une des revendications précédentes, caractérisé en ce que la masse fondue d'acier contient moins de 0,001% en poids de B.
  13. Procédé selon l'une des revendications précédentes, caractérisé en ce que le laminage à chaud dans les quatre derniers laminoirs avant de quitter le train de laminage à chaud est réalisé à une température de laminage, qui est au moins égale à la température Ar3 et au maximum égale à 930°C.
  14. Procédé selon l'une des revendications précédentes, caractérisé en ce que le taux global de déformation εh4 obtenu dans les quatre derniers laminoirs avant de quitter le train de laminage à chaud s'élève à au moins 85%.
  15. Procédé selon l'une des revendications précédentes, caractérisé en ce que le taux global de déformation εh3 obtenu dans les trois derniers laminoirs avant de quitter le train de laminage à chaud s'élève à au moins 75%.
  16. Procédé selon l'une des revendications précédentes, caractérisé en ce que le taux global de déformation εh2 obtenu dans les deux derniers laminoirs avant de quitter le train de laminage à chaud s'élève à au moins 60%.
  17. Procédé selon l'une des revendications précédentes, caractérisé en ce que le taux global de déformation εh1 obtenu dans le dernier laminoir avant de quitter le train de laminage à chaud s'élève à au moins 35%.
  18. Procédé selon l'une des revendications précédentes, caractérisé en ce que la vitesse de feuillard du feuillard chaud obtenu lorsqu'il quitte le train de laminage à chaud s'élève à au moins 15 m/seconde.
  19. Procédé selon l'une des revendications précédentes, caractérisé en ce que la température de dévidoir est d'au moins 700°C.
  20. Procédé selon l'une des revendications 1 à 18, caractérisé en ce que la température de dévidoir s'élève à moins de 550°C.
  21. Procédé selon l'une des revendications précédentes, caractérisé en ce que le taux de laminage à froid obtenu par la laminage à froid s'élève à au moins 40%.
  22. Procédé selon l'une des revendications précédentes, caractérisé en ce que le recuit de recristallisation est réalisé en continu.
  23. Procédé selon l'une des revendications précédentes, caractérisé en ce que le feuillard recuit par recristallisation est ensuite galvanisé à chaud.
  24. Procédé selon l'une des revendications précédentes, caractérisé en ce que le recuit de recristallisation est réalisé dans un four à cloche.
  25. Procédé selon l'une des revendications 1 à 22 ou 24, caractérisé en ce qu'après le recuit de recristallisation, on réalise une transformation de surface électrolytique.
EP03018184A 2002-10-15 2003-08-09 Procédé de fabrication de tôles ou de bandes d'acier laminées à froid ayant une excellente formabilité Expired - Lifetime EP1411140B1 (fr)

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Application Number Priority Date Filing Date Title
DE10247998 2002-10-15
DE10247998A DE10247998B4 (de) 2002-10-15 2002-10-15 Verfahren zum Herstellen eines besonders gut verformbaren kaltgewalzten Stahlbands oder -blechs

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EP1411140A1 EP1411140A1 (fr) 2004-04-21
EP1411140B1 true EP1411140B1 (fr) 2006-10-25

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EP (1) EP1411140B1 (fr)
AT (1) ATE343657T1 (fr)
DE (2) DE10247998B4 (fr)
DK (1) DK1411140T3 (fr)
ES (1) ES2275046T3 (fr)
PL (1) PL361945A1 (fr)

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CN104831207A (zh) * 2015-04-16 2015-08-12 河北钢铁股份有限公司邯郸分公司 一种薄规格600MPa级热镀锌板生产方法
MX2019002942A (es) 2016-09-20 2019-06-12 Thyssenkrupp Steel Europe Ag Metodo para fabricar productos de acero planos y producto de acero plano.
CN111996463B (zh) * 2020-07-31 2021-12-14 马鞍山钢铁股份有限公司 一种低成本的低合金钢卷及其制造方法

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ATE343657T1 (de) 2006-11-15
DK1411140T3 (da) 2007-02-26
DE10247998B4 (de) 2004-07-15
EP1411140A1 (fr) 2004-04-21
PL361945A1 (en) 2004-04-19
DE50305470D1 (de) 2006-12-07
DE10247998A1 (de) 2004-05-06
ES2275046T3 (es) 2007-06-01

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