EP1067203A1 - Process of manufacturing iron-carbon-manganese alloy strips and strips obtained thereby - Google Patents

Process of manufacturing iron-carbon-manganese alloy strips and strips obtained thereby Download PDF

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Publication number
EP1067203A1
EP1067203A1 EP00401860A EP00401860A EP1067203A1 EP 1067203 A1 EP1067203 A1 EP 1067203A1 EP 00401860 A EP00401860 A EP 00401860A EP 00401860 A EP00401860 A EP 00401860A EP 1067203 A1 EP1067203 A1 EP 1067203A1
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Prior art keywords
strip
annealing
casting
rolling
carried out
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EP00401860A
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German (de)
French (fr)
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EP1067203B1 (en
Inventor
Nicolas Guelton
Michel Faral
Odile Faral
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USINOR SA
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USINOR SA
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Classifications

    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/04Ferrous alloys, e.g. steel alloys containing manganese
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021Modifying 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
    • C21D8/0215Rapid solidification; Thin strip casting
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236Cold rolling
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273Final recrystallisation annealing

Definitions

  • the invention relates to the manufacture of ferrous alloy strips. More specifically, it relates to the manufacture of iron-carbon-manganese alloy strips by direct casting in the form of thin strips.
  • Hadfield Fe-Mn steels (11 to 14%) - C (1.1 to 1.4%) which can be described as “steels with a high manganese content”. They present the particularity of having a very high resistance and a hardening capacity under the effect repeated shocks or friction.
  • austenitic steels of the type Fe-Mn (15 to 35%) - Al (0 to 10%) - Cr (0 to 20%) - C (0 to 1.5%) which derive simultaneously from Hadfield steels and Fe-Cr-Ni austenitic stainless steels which are gradually replaced nickel with manganese and chromium with aluminum.
  • These steels with strong manganese content are characterized by a high work hardening capacity which allows them to associate a high level of resistance with excellent ductility.
  • the object of the invention is to propose a method of manufacturing strips ferrous alloys with a high manganese content faster and less expensive than conventionally known method, and making it possible to obtain products of at least also good quality only by this previous method.
  • the invention also relates to a strip capable of being produced by this process.
  • the invention is primarily based on the use of a method of casting liquid metal directly in the form of a weak strip thickness. This can optionally undergo in-line hot rolling by means of a small installation, the cost of manufacture and use is much lower to that of a band train.
  • the elimination of hot rolling on a train bands eliminates the risks of hot cracking during the heating which we have spoken about. Then follow cold rolling, annealing and possibly skin-pass operations, including execution according to the methods which will be specified makes it possible to obtain the properties of the desired product.
  • austenitic steels with a high manganese content are characterized by the absence of phase transformation during their cooling.
  • one of the functions conventional hot rolling of ferritic, carbon or stainless steels is refinement of the microstructure just before the phase transformation occurs.
  • steels with high manganese content which offer the best strength-ductility compromise at the shaping temperature are completely austenitic, at least before deformation, from their solidification until the end of their cooling. So the hot rolling of austenitic steels with a high manganese content is not of interest important metallurgical. Its function is limited to a simple reduction in thickness of the product to obtain a strip capable of being cold rolled. In their case, there is therefore no inconvenience to obtain by casting thin strips a thick strip relatively close to its final thickness, provided that said strip is free of central porosities after pouring. A slight in-line hot rolling, as described, is sufficient to close these possible porosities.
  • a steel with a very high manganese content having a composition as previously defined (a typical example of such a composition is Fe - C: 0.55% - Mn: 21.5%) is cast in the form of thin strips of thickness 1.5 to 10 mm, directly from liquid metal.
  • a typical example of such a composition is Fe - C: 0.55% - Mn: 21.5%
  • the casting between cylinders of strips of thickness of the order of 3 to 4 mm is particularly suitable for implementation of the method according to the invention.
  • the strip At its exit from the cylinders, the strip preferably crosses an area such as an enclosure inerted by gas blowing, where it is subjected to a non-oxidizing environment (neutral atmosphere of nitrogen or argon, or even an atmosphere containing a certain proportion of hydrogen to make it reducing), in order to avoid or limit the formation of scale on its surface.
  • a non-oxidizing environment neutral atmosphere of nitrogen or argon, or even an atmosphere containing a certain proportion of hydrogen to make it reducing
  • the role essential of this hot rolling is to close the porosities likely to have been formed at the heart of the strip during its solidification, and to improve its surface condition by crushing any roughness peaks present on the surface of the strip, in particular when high roughness casting cylinders have been used.
  • the reduction rate minimum to apply to the strip during this hot rolling is 10% if we want to close the porosities correctly, typically 20%.
  • a rate of up to 60% (obtained in one or more stages) is however possible, in particular if we are dealing with a strip with high surface roughness, or if you want to obtain a final product having a very small thickness.
  • the temperature at which this rolling is carried out at hot is of no great importance from a metallurgical point of view, since, as we have says, steel has an austenitic structure at all temperatures and therefore does not undergo phase transformation which could influence the qualitative result of hot rolling.
  • the strip can possibly be wound, again at a temperature which hardly matters otherwise than practical, since no significant metallurgical transformation other than growth grains are not likely to occur during the period when the wound strip is cools at low speed.
  • the growth of the grains will, however, only have a magnitude limited, the effects of which will be easy to reverse by cold rolling and annealing that will follow.
  • the stay of the strip in the form of a reel can be the opportunity to complete the precipitation of carbides, nitrides and carbonitrides.
  • the cast strip then possibly hot rolled then undergoes (directly or after a winding-unwinding operation) cold rolling, preferably preceded by an acid pickling (for example with hydrochloric acid) to ensure obtaining a good surface condition of the strip.
  • the reduction rate applied during this cold rolling is 10 to 90%, typically of the order of 75%. It is obtained in one or many stages. If we started with a 3 to 4 mm thick cast strip, that we have reduced to 2.5 to 3 mm thick after hot rolling, we typically end up with a cold rolled strip whose thickness is of the order of 0.6-0.8 mm.
  • a grain size is obtained recrystallized less than 10 ⁇ m.
  • steels with high manganese content concerned by the invention tolerate a wide variation in conditions annealing, due to their high content of alloying elements which slows the growth of grains.
  • the strip development process may stop after annealing (after a pickling of the annealed strip), or be supplemented in a conventional manner by a passage to the skin-pass carried out according to usual methods.

Abstract

1.5-10 mm-thick strip is cast from molten metal containing (in wt. %) C 0.001-1.6; Mn 6-30, Ni ≤ 10 and (Mn+Ni) 16-30; Si ≤ 2.5; Al ≤ 6; Cr ≤ 10; (P+Sn+Sb+As) ≤ 0.2; (S+Se+Te) ≤ 0.5; (V+Ti+Nb+B+Zr+rare earths) ≤ 0.3%; (Mo+W) ≤ 0.5%; N ≤ 0.3%; Cu ≤ 5%; and Fe and production impurities. After cold rolling to 10-90% reduction in one or more stages, recrystallization annealing is carried out. Preferably, the content of carbon in the molten metal is 0.2-0.8 wt.%. The strip is obtained by rolling between two closely located, horizontal cylinders which rotate in opposite directions and are internally cooled. Between the casting and rolling stages the strip is hot rolled to 10-60 % reduction in one or more stages, and between the casting and hot rolling stages the strip is passed through a non-oxidizing zone. Before the hot rolling stage the strip is subjected to decarbonization. The strip is coiled after casting or hot rolling and uncoiled before cold rolling. Acidic pickling of the strip is preferably carried out before cold rolling. Recrystallization annealing comprises a high density annealing process carried out at 900-1100 degrees C, immediately followed by cooling at a rate of 100-6000 degrees C/second. The strip is pickled after the annealing stage, followed by a skin-pass stage. An Independent claim is given for the an iron-carbon-manganese strip produced by the above process.

Description

L'invention concerne la fabrication de bandes d'alliages ferreux. Plus précisément, elle concerne la fabrication de bandes en alliage fer-carbone-manganèse par coulée directe sous forme de bandes minces.The invention relates to the manufacture of ferrous alloy strips. More specifically, it relates to the manufacture of iron-carbon-manganese alloy strips by direct casting in the form of thin strips.

On connaít depuis longtemps les aciers Hadfield Fe-Mn (11 à 14%)-C (1,1 à 1,4%) qui peuvent être qualifiés d'« aciers à forte teneur en manganèse ». Ils présentent la particularité d'avoir une résistance très élevée et une capacité de durcissement sous l'effet de chocs ou de frottements répétés. On connaít également les aciers austénitiques du type Fe-Mn (15 à 35%)-Al (0 à 10%)-Cr (0 à 20%)-C (0 à 1,5%) qui dérivent simultanément des aciers Hadfield et des aciers inoxydables austénitiques Fe-Cr-Ni dont on a progressivement remplacé le nickel par du manganèse et le chrome par de l'aluminium. Ces aciers à forte teneur en manganèse se caractérisent par une forte capacité d'écrouissage qui leur permet d'associer un haut niveau de résistance à une excellente ductilité. On peut donc les utiliser avec profit pour la fabrication d'éléments de renfort fabriqués par emboutissage pour l'industrie automobile. C'est au maclage mécanique, assisté éventuellement par la transformation martensitique γ → ε que ces aciers doivent leur grande capacité d'écrouissage. En se propageant, les macles facilitent la déformation plastique, mais en se faisant mutuellement obstacle, elles contribuent aussi à l'augmentation de la contrainte d'écoulement.Hadfield Fe-Mn steels (11 to 14%) - C (1.1 to 1.4%) which can be described as “steels with a high manganese content”. They present the particularity of having a very high resistance and a hardening capacity under the effect repeated shocks or friction. We also know austenitic steels of the type Fe-Mn (15 to 35%) - Al (0 to 10%) - Cr (0 to 20%) - C (0 to 1.5%) which derive simultaneously from Hadfield steels and Fe-Cr-Ni austenitic stainless steels which are gradually replaced nickel with manganese and chromium with aluminum. These steels with strong manganese content are characterized by a high work hardening capacity which allows them to associate a high level of resistance with excellent ductility. So we can use them profitably for the manufacture of reinforcing elements produced by stamping for automobile industry. It is mechanical twinning, possibly assisted by martensitic transformation γ → ε that these steels owe their high capacity hardening. By propagating, twins facilitate plastic deformation, but by mutually impeding, they also contribute to the increase of the constraint of flow.

Divers documents traitent de la composition et de la fabrication de tels aciers à très forte teneur en manganèse, par exemple WO 93/13233, WO 95/26423, WO 97/24467. Ces aciers ont toujours, jusqu'à présent, été fabriqués par la filière classique coulée continue de brames d'épaisseur 200 mm environ - laminage à chaud - laminage à froid - recuit - décapage - skin-pass. Cette filière présente essentiellement trois inconvénients. D'abord son coût, lié à l'utilisation d'un train à bandes qui est une installation nécessitant un investissement très élevé et consommant beaucoup d'énergie, puisqu'il est nécessaire de fortement réchauffer les brames avant de les laminer. Ensuite l'existence d'un risque de fissuration à chaud de la bande lors de ce réchauffage, pendant lequel se forme également une épaisse couche de calamine qui est défavorable aussi bien à la qualité de surface du produit qu'au rendement métallurgique du process de fabrication. Enfin, dans l'ensemble, il s'agit d'une filière de fabrication longue, ne permettant pas toujours de réagir promptement à une demande pressante de la part d'un client.Various documents deal with the composition and manufacture of such steels very high manganese content, for example WO 93/13233, WO 95/26423, WO 97/24467. These steels have always, until now, been manufactured by the conventional die casting continuous slab thickness around 200 mm - hot rolling - cold rolling - annealing - pickling - skin-pass. This sector has essentially three drawbacks. First, its cost, linked to the use of a band train, which is an installation requiring a very high investment and consuming a lot of energy, since it is necessary to strongly warm the slabs before rolling them. Then the existence of a risk of hot cracking of the strip during this reheating, during which also forms a thick layer of scale which is detrimental both to the surface quality of the product that metallurgical efficiency of the manufacturing process. Finally, overall, it is a long manufacturing process, not always making it possible to react promptly upon an urgent request from a client.

Le but de l'invention est de proposer une méthode de fabrication de bandes d'alliages ferreux à forte teneur en manganèse plus rapide et moins coûteuse que la méthode classiquement connue, et permettant d'obtenir des produits d'au moins aussi bonne qualité que par cette précédente méthode. The object of the invention is to propose a method of manufacturing strips ferrous alloys with a high manganese content faster and less expensive than conventionally known method, and making it possible to obtain products of at least also good quality only by this previous method.

A cet effet, l'invention a pour objet un procédé de production de bandes en alliage fer-carbone-manganèse, selon lequel :

  • on coule sur une machine de coulée une bande mince d'épaisseur 1,5 à 10 mm directement à partir d'un métal liquide de composition en pourcentages pondéraux : C compris entre 0,001 et 1,6% ; Mn compris entre 6 et 30%, Ni ≤ 10% et avec (Mn + Ni) compris entre 16 et 30%; Si ≤ 2,5% ; Al ≤ 6% ; Cr ≤ 10% ; (P + Sn + Sb + As) ≤ 0,2% ; (S + Se + Te) ≤ 0,5% ; (V + Ti + Nb + B + Zr + terres rares) ≤ 3% ; (Mo + W) ≤ 0,5% ; N ≤ 0,3% ; Cu ≤ 5% ; le reste étant du fer et des impuretés résultant de l'élaboration ;
  • on lamine à froid ladite bande à un taux de réduction compris entre 10 et 90% en une ou plusieurs étapes ;
  • et on effectue un recuit de recristallisation de ladite bande.
To this end, the subject of the invention is a process for producing strips of iron-carbon-manganese alloy, according to which:
  • a thin strip 1.5 to 10 mm thick is poured onto a casting machine directly from a liquid metal with a composition in weight percentages: C of between 0.001 and 1.6%; Mn between 6 and 30%, Ni ≤ 10% and with (Mn + Ni) between 16 and 30%; If ≤ 2.5%; Al ≤ 6%; Cr ≤ 10%; (P + Sn + Sb + As) ≤ 0.2%; (S + Se + Te) ≤ 0.5%; (V + Ti + Nb + B + Zr + rare earths) ≤ 3%; (Mo + W) ≤ 0.5%; N ≤ 0.3%; Cu ≤ 5%; the remainder being iron and impurities resulting from processing;
  • said strip is cold rolled at a reduction rate of between 10 and 90% in one or more stages;
  • and an recrystallization annealing of said strip is carried out.

L'invention concerne également une bande susceptible d'être produite par ce procédé.The invention also relates to a strip capable of being produced by this process.

Comme on l'aura compris, l'invention repose en premier lieu sur l'utilisation d'un procédé de coulée du métal liquide directement sous forme d'une bande de faible épaisseur. Celle-ci peut éventuellement subir un laminage à chaud en ligne au moyen d'une installation de faible dimension, dont le coût de fabrication et d'utilisation est très inférieur à celui d'un train à bandes. De plus, la suppression du laminage à chaud sur un train à bandes élimine les risques de fissuration à chaud lors du réchauffage dont on a parlé. Suivent ensuite des opérations de laminage à froid, recuit et éventuellement skin-pass, dont l'exécution selon les modalités qui seront précisées permet d'obtenir les propriétés du produit souhaitées.As will be understood, the invention is primarily based on the use of a method of casting liquid metal directly in the form of a weak strip thickness. This can optionally undergo in-line hot rolling by means of a small installation, the cost of manufacture and use is much lower to that of a band train. In addition, the elimination of hot rolling on a train bands eliminates the risks of hot cracking during the heating which we have spoken about. Then follow cold rolling, annealing and possibly skin-pass operations, including execution according to the methods which will be specified makes it possible to obtain the properties of the desired product.

L'invention sera mieux comprise à la lecture de la description qui suit.The invention will be better understood on reading the description which follows.

Le procédé de coulée directe de bandes minces d'acier de 1,5 à 10 mm d'épaisseur est aujourd'hui bien connu, notamment sous sa forme dite « coulée entre cylindres ». L'acier liquide se solidifie contre les parois latérales de deux cylindres horizontaux rapprochés, refroidis intérieurement et mis en rotation en sens inverses, et ressort sous les cylindres sous forme d'une bande solidifiée. Celle-ci peut être directement bobinée, puis envoyée aux installations de traitement à froid, ou subir un laminage à chaud en ligne avant le bobinage. Selon l'invention, l'utilisation d'un tel procédé permet de raccourcir la filière de fabrication des bandes d'acier à haute teneur en manganèse grâce à la suppression du passage au train à bandes, alors que ce passage est nécessaire dans la filière classique débutant par la coulée de brames. Cette suppression est d'autant plus avantageuse que les aciers austénitiques à forte teneur en manganèse se caractérisent par l'absence de transformation de phase au cours de leur refroidissement. En effet, l'une des fonctions classiques du laminage à chaud des aciers ferritiques, au carbone ou inoxydables, est l'affinement de la microstructure juste avant que ne se produise la transformation de phase. Mais les aciers à haute teneur en manganèse qui offrent le meilleur compromis résistance-ductilité à la température de mise en forme sont complètement austénitiques, du moins avant déformation, depuis leur solidification jusqu'à la fin de leur refroidissement. Donc le laminage à chaud des aciers austénitiqües à forte teneur en manganèse n'a pas un intérêt métallurgique important. Sa fonction se limite à une simple réduction d'épaisseur du produit pour obtenir une bande susceptible d'être laminée à froid. Dans leur cas, il n'y a donc pas d'inconvénient à obtenir par coulée de bandes minces une bande d'épaisseur relativement proche de son épaisseur finale, sous réserves que ladite bande soit exempte de porosités centrales après sa coulée. Un léger laminage à chaud en ligne, tel qu'on le décrit, est suffisant pour refermer ces éventuelles porosités.The process of direct casting of thin steel strips from 1.5 to 10 mm thick is well known today, in particular in its form known as "casting between cylinders". Liquid steel solidifies against the side walls of two horizontal cylinders close together, internally cooled and rotated in opposite directions, and comes out under the cylinders in the form of a solidified strip. This can be directly wound, then sent to cold processing facilities, or undergo online hot rolling before the winding. According to the invention, the use of such a method makes it possible to shorten the sector for manufacturing high-manganese steel strips by eliminating the changeover to the band train, whereas this changeover is necessary in the conventional sector starting with the casting of slabs. This removal is all the more advantageous since the austenitic steels with a high manganese content are characterized by the absence of phase transformation during their cooling. Indeed, one of the functions conventional hot rolling of ferritic, carbon or stainless steels, is refinement of the microstructure just before the phase transformation occurs. But steels with high manganese content which offer the best strength-ductility compromise at the shaping temperature are completely austenitic, at least before deformation, from their solidification until the end of their cooling. So the hot rolling of austenitic steels with a high manganese content is not of interest important metallurgical. Its function is limited to a simple reduction in thickness of the product to obtain a strip capable of being cold rolled. In their case, there is therefore no inconvenience to obtain by casting thin strips a thick strip relatively close to its final thickness, provided that said strip is free of central porosities after pouring. A slight in-line hot rolling, as described, is sufficient to close these possible porosities.

L'invention s'applique à la fabrication d'aciers à haute teneur en manganèse qui ont la composition suivante, les pourcentages étant des pourcentages pondéraux :

  • leur teneur en carbone est comprise entre 0,001 et 1,6%, préférentiellement comprise entre 0,2 et 0,8% ; une teneur inférieure à 0,2% oblige à procéder à une décarburation du bain d'acier liquide qui peut être coûteuse à réaliser, en particulier lorsque le manganèse est déjà présent en quantité importante ; de plus, cette teneur minimale de 0,2% permet d'obtenir une interaction entre le carbone et les dislocations : le carbone, en bloquant les dislocations, permet un durcissement supplémentaire par rapport au maclage, et permet d'améliorer la résistance à la traction de 50 à 100 Mpa ; une teneur supérieure à 0,8% rend plus délicate l'optimisation des teneurs en autres éléments d'alliage en vue de l'obtention des propriétés mécaniques les plus favorables ;
  • leur teneur en manganèse est comprise entre 6 et 30%, sachant que le total de leurs teneurs en manganèse et nickel est compris entre 16 et 30% et que leur teneur en nickel peut aller jusqu'à 10% ;
  • leur teneur en silicium peut aller jusqu'à 2,5%, sachant que cet élément n'est qu'optionnel ;
  • leur teneur en aluminium est inférieure à 6% sachant que cet élément n'est qu'optionnel ;
  • si du chrome est présent, la teneur en chrome est au maximum de 10% ;
  • leur teneur en phosphore peut aller jusqu'à 0,2%, sachant que l'étain, l'antimoine et l'arsenic éventuellement présents sont, de ce point de vue, assimilables au phosphore et comptabilisés avec lui dans la composition de l'acier ; au-delà, on risque d'obtenir des défauts dans les zones ségrégées de la bande ; ces défauts seraient provoqués par des retards à la solidification là où se trouvent des ségrégations ; si on lamine à chaud alors que du métal à l'état liquide est encore présent par endroits dans le produits, il y a, de ce fait, un risque de décohésion de la microstructure ;
  • le total de leurs teneurs en soufre, sélénium et tellure peut aller jusqu'à 0,5% ;
  • le total de leurs teneurs en vanadium, titane, niobium, bore, tantale et zirconium et terres rares, qui précipitent les nitrures et carbonitrures, peut aller jusqu'à 3% ;
  • le total de leurs teneurs en molybdène et tungstène peut aller jusqu'à 0,5% ;
  • leur teneur en azote peut aller jusqu'à 0,3%.
The invention applies to the manufacture of steels with a high manganese content which have the following composition, the percentages being percentages by weight:
  • their carbon content is between 0.001 and 1.6%, preferably between 0.2 and 0.8%; a content of less than 0.2% makes it necessary to decarburize the bath of liquid steel which can be costly to produce, in particular when the manganese is already present in large quantity; moreover, this minimum content of 0.2% makes it possible to obtain an interaction between the carbon and the dislocations: the carbon, by blocking the dislocations, allows an additional hardening compared to twinning, and makes it possible to improve the resistance to traction from 50 to 100 Mpa; a content greater than 0.8% makes it more difficult to optimize the contents of other alloying elements with a view to obtaining the most favorable mechanical properties;
  • their manganese content is between 6 and 30%, knowing that the total of their manganese and nickel contents is between 16 and 30% and that their nickel content can range up to 10%;
  • their silicon content can go up to 2.5%, knowing that this element is only optional;
  • their aluminum content is less than 6% knowing that this element is only optional;
  • if chromium is present, the chromium content is at most 10%;
  • their phosphorus content can go up to 0.2%, knowing that the tin, antimony and arsenic possibly present are, from this point of view, comparable to phosphorus and counted with it in the composition of the steel; beyond, there is a risk of obtaining faults in the segregated zones of the strip; these defects would be caused by delays in solidification where there are segregations; if it is hot rolled while metal in the liquid state is still present in places in the products, there is, therefore, a risk of decohesion of the microstructure;
  • the total of their sulfur, selenium and tellurium contents can go up to 0.5%;
  • the total of their contents of vanadium, titanium, niobium, boron, tantalum and zirconium and rare earths, which precipitate nitrides and carbonitrides, can range up to 3%;
  • the total of their molybdenum and tungsten contents may be up to 0.5%;
  • their nitrogen content can range up to 0.3%.

Selon l'invention, un acier à très forte teneur en manganèse présentant une composition telle que précédemment définie (un exemple typique d'une telle composition est Fe - C : 0,55% - Mn : 21,5%) est coulé sous forme de bandes minces d'épaisseur 1,5 à 10 mm, directement à partir de métal liquide. A cet effet, la coulée entre cylindres de bandes d'épaisseur de l'ordre de 3 à 4 mm est particulièrement adaptée à la mise en oeuvre du procédé selon l'invention.According to the invention, a steel with a very high manganese content having a composition as previously defined (a typical example of such a composition is Fe - C: 0.55% - Mn: 21.5%) is cast in the form of thin strips of thickness 1.5 to 10 mm, directly from liquid metal. For this purpose, the casting between cylinders of strips of thickness of the order of 3 to 4 mm is particularly suitable for implementation of the method according to the invention.

A sa sortie des cylindres, la bande traverse, de préférence, une zone telle qu'une enceinte inertée par une insufflation de gaz, où elle est soumise à un environnement non oxydant (atmosphère neutre d'azote ou d'argon, voire une atmosphère comportant une certaine proportion d'hydrogène pour la rendre réductrice), afin d'éviter ou de limiter la formation de calamine à sa surface. On a vu que les aciers du type coulé étaient particulièrement sensibles à la formation de calamine, et il est moins difficile de limiter cette formation sur des bandes minces coulées directement à partir de métal liquide que sur des brames épaisses devant être coulées sur une installation de coulée continue classique, puis réchauffées avant leur laminage à chaud. En sortie de cette zone d'inertage on peut également placer un dispositif de décalaminage de la bande par projection de grenailles ou de CO2 solide sur sa surface ou par brossage, afin d'éliminer la calamine qui aurait pu se former malgré les précautions prises. On peut également choisir de laisser se former la calamine de façon naturelle sans chercher à inerter l'atmosphère environnant la bande, puis d'éliminer cette calamine par un dispositif tel qu'on vient de le décrire.At its exit from the cylinders, the strip preferably crosses an area such as an enclosure inerted by gas blowing, where it is subjected to a non-oxidizing environment (neutral atmosphere of nitrogen or argon, or even an atmosphere containing a certain proportion of hydrogen to make it reducing), in order to avoid or limit the formation of scale on its surface. It has been seen that steels of the cast type are particularly sensitive to the formation of scale, and it is less difficult to limit this formation on thin strips cast directly from liquid metal than on thick slabs to be cast on an installation for conventional continuous casting, then reheated before hot rolling. At the exit from this inerting zone, it is also possible to place a device for descaling the strip by spraying shot or solid CO 2 onto its surface or by brushing, in order to eliminate the scale which could have formed despite the precautions taken. . One can also choose to allow the scale to form naturally without seeking to inert the atmosphere surrounding the strip, then to eliminate this scale by a device as just described.

Autant que possible immédiatement après la sortie de la bande de l'installation d'inertage ou de décalaminage a lieu, de préférence, un laminage à chaud en ligne de cette même bande. Il n'est, cependant, pas obligatoire dans le cas où la bande serait d'emblée satisfaisante en termes de porosités et d'état de surface. C'est en grande partie ce laminage qui justifie les mesures prises préférentiellement pour éviter ou limiter la formation de calamine, et/ou pour éliminer la calamine qui aurait pu se former. En effet, effectuer ce laminage à chaud sur une bande calaminée pourrait conduire à des incrustations de calamine dans la surface de la bande, qui détérioreraient sa qualité de surface. Le rôle essentiel de ce laminage à chaud est de refermer les porosités susceptibles d'avoir été formées au coeur de la bande lors de sa solidification, et d'améliorer son état de surface en écrasant les pics de rugosité éventuellement présents à la surface de la bande, en particulier lorsque des cylindres de coulée à rugosité élevée ont été utilisés. Le taux de réduction minimal à appliquer à la bande lors de ce laminage à chaud est de 10% si on veut refermer correctement les porosités, typiquement de 20%. Un taux allant jusqu'à 60% (obtenu en une ou plusieurs étapes) est cependant envisageable, en particulier si on a affaire à une bande présentant une forte rugosité de surface, ou si on désire obtenir un produit final présentant une très faible épaisseur. La température à laquelle est effectuée ce laminage à chaud est sans grande importance du point de vue métallurgique, puisque, comme on l'a dit, l'acier a une structure austénitique à toute température et ne subit donc pas de transformation de phase qui pourrait influer sur le résultat qualitatif du laminage à chaud.As much as possible immediately after the tape leaves the facility Inerting or descaling takes place, preferably an in-line hot rolling of this same band. It is not, however, compulsory in the event that the band is immediately satisfactory in terms of porosity and surface condition. It’s largely this rolling which justifies the measures taken preferentially to avoid or limit the formation of scale, and / or to remove scale which may have formed. Indeed, perform this hot rolling on a burnt strip could lead to encrustations of scale in the surface of the strip, which would deteriorate its surface quality. The role essential of this hot rolling is to close the porosities likely to have been formed at the heart of the strip during its solidification, and to improve its surface condition by crushing any roughness peaks present on the surface of the strip, in particular when high roughness casting cylinders have been used. The reduction rate minimum to apply to the strip during this hot rolling is 10% if we want to close the porosities correctly, typically 20%. A rate of up to 60% (obtained in one or more stages) is however possible, in particular if we are dealing with a strip with high surface roughness, or if you want to obtain a final product having a very small thickness. The temperature at which this rolling is carried out at hot is of no great importance from a metallurgical point of view, since, as we have says, steel has an austenitic structure at all temperatures and therefore does not undergo phase transformation which could influence the qualitative result of hot rolling.

Après ce laminage à chaud éventuel mais préférentiel, la bande peut éventuellement être bobinée, là encore à une température qui n'a guère d'importance autre que pratique, puisqu'aucune transformation métallurgique notable autre qu'une croissance des grains n'est susceptible de se produire pendant la période où la bande bobinée se refroidit à faible vitesse. La croissance des grains n'aura, de toute façon, qu'une ampleur limitée, dont les effets seront faciles à annuler par les opérations de laminage à froid et de recuit qui suivront. Eventuellement, le séjour de la bande sous forme de bobine peut être l'occasion de parachever la précipitation des carbures, nitrures et carbonitrures.After this possible but preferential hot rolling, the strip can possibly be wound, again at a temperature which hardly matters otherwise than practical, since no significant metallurgical transformation other than growth grains are not likely to occur during the period when the wound strip is cools at low speed. The growth of the grains will, however, only have a magnitude limited, the effects of which will be easy to reverse by cold rolling and annealing that will follow. Optionally, the stay of the strip in the form of a reel can be the opportunity to complete the precipitation of carbides, nitrides and carbonitrides.

La bande coulée puis éventuellement laminée à chaud subit ensuite (directement ou après une opération de bobinage-débobinage) un laminage à froid, préférentiellement précédé d'un décapage acide (par exemple à l'acide chlorhydrique) permettant d'assurer l'obtention d'un bon état de surface de la bande. Le taux de réduction appliqué lors de ce laminage à froid est de 10 à 90%, typiquement de l'ordre de 75%. Il est obtenu en une ou plusieurs étapes. Si on est parti d'une bande coulée de 3 à 4 mm d'épaisseur, que l'on a réduite à 2,5 à 3 mm d'épaisseur après laminage à chaud, on se retrouve typiquement avec une bande laminée à froid dont l'épaisseur est de l'ordre de 0,6-0,8 mm.The cast strip then possibly hot rolled then undergoes (directly or after a winding-unwinding operation) cold rolling, preferably preceded by an acid pickling (for example with hydrochloric acid) to ensure obtaining a good surface condition of the strip. The reduction rate applied during this cold rolling is 10 to 90%, typically of the order of 75%. It is obtained in one or many stages. If we started with a 3 to 4 mm thick cast strip, that we have reduced to 2.5 to 3 mm thick after hot rolling, we typically end up with a cold rolled strip whose thickness is of the order of 0.6-0.8 mm.

La bande subit ensuite un recuit de recristallisation qui doit lui conférer des caractéristiques de résistance à la traction et de ductilité élevées. Ce recuit peut être effectué de différentes manières, à savoir par exemple :

  • un recuit dit « recuit compact » où la bande est chauffée jusqu'à une température de 900 à 1000°C, voire 1100°C, à une vitesse d'environ 500°C/s, puis est immédiatement refroidie à une vitesse comprise entre 100 et 6000°C/s, qui est fonction de l'épaisseur de la bande et des caractéristiques du fluide de refroidissement ; typiquement, une bande de 0,8 mm d'épaisseur chauffée à 1000°C se refroidit à 200°C/s si elle est trempée à l'hélium et à 5000°C/s si elle est trempée à l'eau ;
  • un recuit continu où la bande est portée entre 800 et 850 °C, et maintenue à cette température pendant 60 à 120 s environ ;
  • un recuit base où la bande est maintenue entre 700 et 750°C pendant 10 à 90 mn environ ;
The strip then undergoes recrystallization annealing which must give it characteristics of high tensile strength and ductility. This annealing can be carried out in different ways, for example:
  • annealing called "compact annealing" where the strip is heated to a temperature of 900 to 1000 ° C, or even 1100 ° C, at a speed of about 500 ° C / s, then is immediately cooled to a speed between 100 and 6000 ° C / s, which is a function of the thickness of the strip and the characteristics of the cooling fluid; typically, a 0.8 mm thick strip heated to 1000 ° C cools to 200 ° C / s if it is quenched with helium and to 5000 ° C / s if it is quenched with water;
  • continuous annealing in which the strip is brought to between 800 and 850 ° C, and maintained at this temperature for approximately 60 to 120 s;
  • base annealing where the strip is maintained between 700 and 750 ° C for approximately 10 to 90 minutes;

Dans tous les cas, on obtient, dans l'exemple considéré, une taille des grains recristallisés inférieure à 10 µm. De manière générale, on peut dire que les aciers à haute teneur en manganèse concernés par l'invention tolèrent une grande variation des conditions de recuit, en raison de leur forte teneur en éléments d'alliage qui freine la croissance des grains.In all cases, in the example considered, a grain size is obtained recrystallized less than 10 µm. In general, it can be said that steels with high manganese content concerned by the invention tolerate a wide variation in conditions annealing, due to their high content of alloying elements which slows the growth of grains.

On a regroupé dans le tableau 1 les caractéristiques de traction obtenues sur un acier de composition C = 0,57%, Mn = 21,47%, Si = 0,038%, Ni = 0,03%, Cr = 0,005%, Cu = 0 003%, P = 0,009%, N = 0,034%, S = 0,005%, Al = 0,003%, Mo = 0,003%, ayant subi un traitement selon l'invention tel qu'exposé précédemment, comprenant la coulée entre cylindres d'une bande de 4 mm d'épaisseur, un laminage à chaud de cette bande jusqu'à 2,6 mm d'épaisseur, un laminage à froid jusqu'à 1 mm d'épaisseur, et enfin un recuit continu de 90 s à 800°C. A titre de comparaison, figurent également dans le tableau 1 les caractéristiques de traction d'un acier de référence obtenu par un procédé classique de fabrication de bandes d'acier à haute teneur en manganèse de composition C = 0,53%, Mn = 26,4%, Si = 0,045%, P = 0,013%, Al = 1,6%, N = 0,074%, comparable à celles décrites dans le document WO 93/13233. Les caractéristiques de traction ont été mesurées parallèlement à la direction de laminage.

Figure 00060001
The tensile properties obtained on a steel of composition C = 0.57%, Mn = 21.47%, Si = 0.038%, Ni = 0.03%, Cr = 0.005%, Cu =, have been grouped together in Table 1. 0 003%, P = 0.009%, N = 0.034%, S = 0.005%, Al = 0.003%, Mo = 0.003%, having undergone a treatment according to the invention as described above, comprising the casting between cylinders of a strip of 4 mm thick, hot rolling of this strip up to 2.6 mm thick, cold rolling up to 1 mm thick, and finally continuous annealing from 90 s to 800 ° C. For comparison, also appear in Table 1 the tensile characteristics of a reference steel obtained by a conventional method of manufacturing steel strips with a high manganese content of composition C = 0.53%, Mn = 26 , 4%, Si = 0.045%, P = 0.013%, Al = 1.6%, N = 0.074%, comparable to those described in document WO 93/13233. The tensile characteristics were measured parallel to the rolling direction.
Figure 00060001

Ce tableau montre notamment que la résistance mécanique est améliorée de plus de 30% sur l'acier de l'invention par rapport à l'acier de référence. La dispersion des résultats est inférieure à 4%. Cette amélioration de la résistance mécanique ne s'accompagne pas d'une diminution de la ductilité, bien au contraire, puisque l'allongement à la rupture est, lui aussi, considérablement augmenté.This table shows in particular that the mechanical strength is further improved 30% on the steel of the invention compared to the reference steel. The dispersion of results is less than 4%. This improvement in mechanical strength does not not accompanied by a decrease in ductility, on the contrary, since the elongation at break is also considerably increased.

Le process d'élaboration de la bande peut s'arrêter après le recuit (après un éventuel décapage de la bande recuite), ou être complété de manière classique par un passage au skin-pass effectué selon des modalités habituelles.The strip development process may stop after annealing (after a pickling of the annealed strip), or be supplemented in a conventional manner by a passage to the skin-pass carried out according to usual methods.

Claims (14)

Procédé de production de bandes en alliage fer-carbone-manganèse, selon lequel : on coule sur une machine de coulée une bande mince d'épaisseur 1,5 à 10 mm directement à partir d'un métal liquide de composition en pourcentages pondéraux : C compris entre 0,001 et 1,6% ; Mn compris entre 6 et 30%, Ni ≤ 10% et avec (Mn + Ni) compris entre 16 et 30% ; Si ≤ 2,5% ; Al ≤ 6% ; Cr ≤ 10% ; (P + Sn + Sb + As) ≤ 0,2% ; (S + Se + Te) ≤ 0,5% ; (V + Ti + Nb + B + Zr + terres rares) ≤ 3% ; (Mo + W) ≤ 0,5% ; N ≤ 0,3% ; Cu ≤ 5%, le reste étant du fer et des impuretés résultant de l'élaboration ; on lamine à froid ladite bande à un taux de réduction compris entre 10 et 90% en une ou plusieurs étapes ; et on effectue un recuit de recristallisation de ladite bande. Process for the production of iron-carbon-manganese alloy strips, according to which: a thin strip 1.5 to 10 mm thick is poured onto a casting machine directly from a liquid metal with a composition in weight percentages: C of between 0.001 and 1.6%; Mn between 6 and 30%, Ni ≤ 10% and with (Mn + Ni) between 16 and 30%; If ≤ 2.5%; Al ≤ 6%; Cr ≤ 10%; (P + Sn + Sb + As) ≤ 0.2%; (S + Se + Te) ≤ 0.5%; (V + Ti + Nb + B + Zr + rare earths) ≤ 3%; (Mo + W) ≤ 0.5%; N ≤ 0.3%; Cu ≤ 5%, the rest being iron and impurities resulting from processing; said strip is cold rolled at a reduction rate of between 10 and 90% in one or more stages; and an recrystallization annealing of said strip is carried out. Procédé selon la revendication 1, caractérisé en ce que la teneur en carbone dudit métal liquide est comprise entre 0,2 et 0,8%.Process according to claim 1, characterized in that the carbon content of said liquid metal is between 0.2 and 0.8%. Procédé selon la revendication 1 ou 2, caractérisé en ce que ladite bande est obtenue par coulée entre deux cylindres horizontaux rapprochés, refroidis intérieurement et mis en rotation en sens inverses.Method according to claim 1 or 2, characterized in that said strip is obtained by casting between two close horizontal cylinders, internally cooled and rotated in opposite directions. Procédé selon l'une des revendications 1 à 3, caractérisé en ce qu'entre la coulée de la bande et le laminage à froid, on lamine à chaud ladite bande à un taux de réduction compris entre 10 et 60% en une ou plusieurs étapes.Method according to one of claims 1 to 3, characterized in that between the casting the strip and cold rolling, said strip is hot rolled at a rate of reduction between 10 and 60% in one or more stages. Procédé selon la revendication 4, caractérisé en ce que ladite bande traverse une zone sous atmosphère non oxydante entre sa coulée et son laminage à chaud.Method according to claim 4, characterized in that said strip passes through a zone in a non-oxidizing atmosphere between its casting and its hot rolling. Procédé selon l'une des revendications 4 ou 5, caractérisé en ce que ladite bande subit une opération de décalaminage avant son laminage à chaud.Method according to one of claims 4 or 5, characterized in that said strip undergoes a descaling operation before its hot rolling. Procédé selon l'une des revendications 1 à 6, caractérisé en ce que la bande est bobinée après sa coulée ou son laminage à chaud et débobinée avant son laminage à froid.Method according to one of claims 1 to 6, characterized in that the strip is coiled after casting or hot rolling and unwound before cold rolling. Procédé selon l'une des revendications 1 à 7, caractérisé en ce que ladite bande subit un décapage acide avant son laminage à froid.Method according to one of claims 1 to 7, characterized in that said strip undergoes acid pickling before cold rolling. Procédé selon l'une des revendications 1 à 8 caractérisé en ce que ledit recuit de recristallisation est un recuit compact effectué à une température de 900 à 1100°C, immédiatement suivi par un refroidissement de la bande à une vitesse de 100 à 6000°C/s.Method according to one of claims 1 to 8 characterized in that said annealing of recrystallization is a compact annealing carried out at a temperature of 900 to 1100 ° C., immediately followed by cooling of the strip at a speed of 100 to 6000 ° C / s. Procédé selon l'une des revendications 1 à 8, caractérisé en ce que ledit recuit de recristallisation est un recuit continu effectué à une température de 800 à 850°C pendant 60 à 120 s.Method according to one of claims 1 to 8, characterized in that said annealing recrystallization is a continuous annealing carried out at a temperature of 800 to 850 ° C for 60 to 120 s. Procédé selon l'une des revendications 1 à 8, caractérisé en ce que ledit recuit de recristallisation est un recuit base effectué à une température de 700 à 750°C pendant 10 à 90 mn. Method according to one of claims 1 to 8, characterized in that said annealing recrystallization is a basic annealing carried out at a temperature of 700 to 750 ° C for 10 90 mins. Procédé selon l'une des revendications 1 à 11, caractérisé en ce que ladite bande est décapée après ledit recuit de recristallisation.Method according to one of claims 1 to 11, characterized in that said strip is pickled after said recrystallization annealing. Procédé selon l'une des revendications 1 à 12, caractérisé en ce que ladite bande subit un passage au skin-pass après le recuit de recristallisation ou le décapage.Method according to one of claims 1 to 12, characterized in that said strip undergoes a passage to the skin-pass after recrystallization annealing or pickling. Bande en alliage fer-carbone-manganèse, caractérisée en ce qu'elle est susceptible d'être produite par le procédé selon l'une des revendications 1 à 13.Iron-carbon-manganese alloy strip, characterized in that it is capable of being produced by the method according to one of claims 1 to 13.
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