EP1163376B1 - Method for continuous casting of highly ductile ferritic stainless steel strips between rolls, and resulting thin strips - Google Patents

Method for continuous casting of highly ductile ferritic stainless steel strips between rolls, and resulting thin strips Download PDF

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EP1163376B1
EP1163376B1 EP00909393A EP00909393A EP1163376B1 EP 1163376 B1 EP1163376 B1 EP 1163376B1 EP 00909393 A EP00909393 A EP 00909393A EP 00909393 A EP00909393 A EP 00909393A EP 1163376 B1 EP1163376 B1 EP 1163376B1
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Prior art keywords
stainless steel
ferritic stainless
less
casting
strips
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EP00909393A
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German (de)
French (fr)
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EP1163376A1 (en
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Frédéric Mazurier
Philippe Paradis
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USINOR SA
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USINOR SA
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • C21D8/0405—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 of ferrous alloys
    • 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
    • C21D8/041—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 fabrication or treatment of ingot or slab
    • C21D8/0415—Rapid solidification; Thin strip casting

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Continuous Casting (AREA)
  • Metal Rolling (AREA)
  • Heat Treatment Of Steel (AREA)
  • Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)
  • Catalysts (AREA)

Abstract

The invention relates to a process for the casting of thin strip having a thickness of less than 10 mm, made of ferritic stainless steel, directly from liquid metal between two rotating cooled rolls having parallel horizontal axes, characterized in that:the said ferritic stainless steel contains (in percentages by weight) from 11 to 18% chromium, less than 1% manganese, less than 1% silicon and less than 2.5% molybdenum;the said ferritic stainless steel has carbon and nitrogen contents, the sum of the contents not exceeding 0.05%;the said ferritic stainless steel contains at least one of the stabilizing elements titanium, niobium, zirconium and aluminium and the sum of their contents is between 0.05 and 1%;the other elements present are iron and the usual impurities resulting from the smelting.The subject of the invention is also thin strip capable of being obtained by the above process.

Description

L'invention concerne la coulée continue des métaux, et plus précisément la coulée continue, directement à partir de métal liquide, de bandes d'acier inoxydable de type ferritique dont l'épaisseur est de l'ordre de quelques mm, par le procédé dit de « coulée entre cylindres ».The invention relates to the continuous casting of metals, and more precisely the casting continuous, directly from liquid metal, of stainless steel strips of the type ferritic whose thickness is of the order of a few mm, by the process known as "casting between cylinders ".

Ces dernières années ont vu s'accomplir des progrès sensibles dans le développement des procédés de coulée de bandes minces d'acier au carbone ou inoxydable directement à partir de métal liquide. Le procédé principalement utilisé aujourd'hui est la coulée dudit métal liquide entre deux cylindres refroidis intérieurement, tournant autour de leurs axes horizontaux dans des sens opposés, et disposés parallèlement l'un à l'autre, la distance minimale entre leurs surfaces étant sensiblement égale à l'épaisseur que l'on désire conférer à la bande coulée (par exemple quelques mm). L'espace de coulée renfermant l'acier liquide est défini par les surfaces latérales des cylindres, sur lesquelles s'initie la solidification de la bande, et par des plaques de fermeture latérale en réfractaire appliquées contre les extrémités des cylindres. Le métal liquide initie sa solidification au contact des surfaces extérieures des cylindres, sur lesquelles il forme des « peaux » solidifiées, dont on fait en sorte qu'elles se rejoignent au niveau du « col », c'est à dire de la zone où la distance entre les cylindres est minimale.The last few years have seen significant progress in development of processes for casting thin strips of carbon or stainless steel directly from liquid metal. The process mainly used today is pouring of said liquid metal between two internally cooled cylinders, rotating around their horizontal axes in opposite directions, and arranged parallel to each other, the minimum distance between their surfaces being substantially equal to the thickness that is desired impart to the cast strip (for example a few mm). The casting space containing liquid steel is defined by the lateral surfaces of the cylinders, on which the solidification of the strip, and by side closing plates in refractory applied against the ends of the cylinders. The liquid metal initiates its solidification on contact with external surfaces of the cylinders, on which it forms solidified "skins", of which ensures that they meet at the "neck", that is to say the area where the distance between cylinders is minimum.

Les bandes minces en acier inoxydable ferritique obtenues par coulée continue entre deux cylindres présentent une fragilité importante, qui rend difficile leur transformation à froid lors des opérations habituelles telles que le débobinage, le cisaillage des rives ou le laminage à froid. On explique la mauvaise ductilité des bandes coulées entre cylindres essentiellement par la structure à très gros grains résultant du mode de solidification rapide entre les cylindres de coulée, associée à un temps de séjour important à température élevée après que la bande solidifiée a quitté l'emprise des cylindres. La dureté élevée de ces grains ferritiques sursaturés en éléments interstitiels tels que le carbone et l'azote constitue un facteur aggravant pour la fragilité des bandes minces.Thin strips of ferritic stainless steel obtained by continuous casting between two cylinders have a significant brittleness, which makes their cold processing during normal operations such as unwinding, shearing edges or cold rolling. We explain the bad ductility of the strips cast between cylinders essentially by the structure with very large grains resulting from the mode of rapid solidification between the casting rolls, associated with a long residence time at high temperature after the solidified strip has left the grip of the cylinders. The high hardness of these ferritic grains supersaturated with interstitial elements such as carbon and nitrogen is an aggravating factor for the fragility of thin strips.

Plusieurs tentatives ont été faites, dans le passé, pour mettre au point un procédé de coulée entre cylindres d'aciers inoxydables ferritiques présentant une bonne ductilité. Elles s'appuyaient largement sur l'addition d'éléments stabilisants connus, tels que le titane et le niobium, et imposaient des limitations analytiques sur le taux maximum d'austénite présent à haute température, désigné par le symbole γp. A ces conditions analytiques, on associait un contrôle de la vitesse de refroidissement, l'application d'un laminage à chaud, ou le contrôle de la température de bobinage des bandes coulées.Several attempts have been made in the past to develop a process of casting between cylinders of ferritic stainless steels having good ductility. They were largely based on the addition of known stabilizing elements, such as titanium and niobium, and imposed analytical limitations on the maximum rate austenite present at high temperature, designated by the symbol γp. Under these conditions analytical, we associated a control of the cooling rate, the application of a hot rolling, or controlling the winding temperature of the cast strips.

Ainsi, le document EP - A - 0 881 305 décrit une nuance ferritique non stabilisée, que l'on obtient par coulée directe d'une bande entre cylindres, la bande étant ensuite bobinée à une température inférieure à 600°C. Elle est ensuite recuite en vase clos, toujours sous forme bobinée. Un bobinage en dessous de 600°C permet de limiter la précipitation des carbures au stade brut de coulée, et ainsi d'éviter leur coalescence sous forme de films continus très fragilisants lors du recuit vase clos.Thus, document EP-A-0 881 305 describes an unstabilized ferritic grade, which is obtained by direct casting of a strip between cylinders, the strip then being wound at a temperature below 600 ° C. It is then annealed in a vacuum, always in coiled form. Winding below 600 ° C limits precipitation carbides in the raw casting stage, and thus avoid their coalescence in the form of films very weakening continuous during closed annealing.

Le document EP - A - 0 638 653 préconise la coulée d'une nuance ferritique à teneur en chrome pouvant être relativement élevée (13-25%) stabilisée au titane, au niobium ou à l'aluminium (0.05% au moins), à basses teneurs en carbone et azote, et présentant un indice γp négatif, γp étant la quantité maximale d'austénite formée à haute température. Cette grandeur est définie par la relation de Tricot et Castro et se calcule par la formule : γp = 420 C% + 470 N% + 23 Ni% + 9 Cu% + 7 Mn% - 11,5 Cr% -11,5 Si% - 12 Mo% - 23 V% - 47 Nb% - 49 Ti% - 52 Al% + 189 Document EP-A-0 638 653 recommends the casting of a ferritic grade with a chromium content which can be relatively high (13-25%) stabilized with titanium, niobium or aluminum (0.05% at least), low carbon and nitrogen contents, and having a negative γp index, γp being the maximum amount of austenite formed at high temperature. This quantity is defined by the relation of Tricot and Castro and is calculated by the formula: γp = 420 C% + 470 N% + 23 Ni% + 9 Cu% + 7 Mn% - 11.5 Cr% -11.5 Si% - 12 Mo% - 23 V% - 47 Nb% - 49 Ti% - 52 Al% + 189

Après la coulée, on procède à un laminage à chaud avec un taux de réduction supérieur à 5% dans l'intervalle 950-1150°C, suivi d'un refroidissement lent à moins de 20°C/s ou d'un maintien à haute température pendant plus de 5 secondes. Le bobinage de la bande a ensuite lieu à moins de 700°C. Selon ce document, on vise à éviter la formation d'austénite à haute température en imposant un indice γp négatif pour empêcher la formation de martensite sur la bande, ce qui la rendrait fragile. La présence de stabilisants conduit, par le fait de la solidification rapide, à de fins précipités fragilisants. Le laminage à chaud avec maintien à haute température et le refroidissement lent favorisent la précipitation, et surtout la coalescence de ces précipités, qui deviennent ainsi inoffensifs. Le bobinage froid permet d'éviter la formation de phases intermétalliques fragiles.After casting, hot rolling is carried out with a reduction rate greater than 5% in the range 950-1150 ° C, followed by slow cooling to less than 20 ° C / s or a high temperature hold for more than 5 seconds. The winding of the strip then takes place at less than 700 ° C. According to this document, we aim to avoid training austenite at high temperature by imposing a negative γp index to prevent formation of martensite on the strip, which would make it fragile. Presence of stabilizers leads, by the fact of rapid solidification, to fine embrittling precipitates. Rolling hot with high temperature maintenance and slow cooling favor the precipitation, and especially the coalescence of these precipitates, which thus become harmless. The cold winding prevents the formation of fragile intermetallic phases.

Le document JP - A - 08283845 préconise un laminage à chaud asynchrone d'une bande coulée à une épaisseur initiale inférieure à 10 mm, ayant pour effet d'améliorer la ductilité en affinant la structure des bandes minces par recristallisation. La coulée est suivie par un laminage à chaud asynchrone et un traitement thermique. On cherche ici à améliorer la ductilité des bandes minces par un traitement de recristallisation.Document JP - A - 08283845 recommends an asynchronous hot rolling of a strip cast at an initial thickness of less than 10 mm, having the effect of improving the ductility by refining the structure of the thin strips by recrystallization. The flow is followed by asynchronous hot rolling and heat treatment. We are trying to improve here the ductility of the thin strips by a recrystallization treatment.

Le document JP - A - 08295943 utilise une autre estimation de la quantité maximale d'austénite formée à chaud, en l'absence d'éléments stabilisants. Cette quantité γ'p est calculée par : γ'p = 420 C% + 470 N% + 23 Ni% + 7 Mn% - 11,5 Cr% -11,5 Si% - 52 Al% + 189 The document JP-A-08295943 uses another estimate of the maximum quantity of austenite formed hot, in the absence of stabilizing elements. This quantity γ'p is calculated by: γ'p = 420 C% + 470 N% + 23 Ni% + 7 Mn% - 11.5 Cr% -11.5 Si% - 52 Al% + 189

On coule entre cylindres une bande dont l'indice γ'p est supérieur à 25%, on la lamine à chaud avec un taux de réduction supérieur à 20% à moins de 1200°C, puis on la met en bobines et on effectue un recuit vase clos des bobines entre 700 et 900°C pendant 4 heures. Le but visé est l'obtention d'une bande à excellente qualité de surface, sans que l'on s'intéresse spécialement à sa ductilité.A band is cast between cylinders whose index γ'p is greater than 25%, it is hot rolled with a reduction rate greater than 20% at less than 1200 ° C, then it is puts in coils and performs a closed annealing of the coils between 700 and 900 ° C for 4 hours. The aim is to obtain a strip with excellent surface quality, without we are particularly interested in its ductility.

Tous ces procédés nécessitent des traitements thermiques particuliers, pouvant nécessiter des installations spéciales, être coûteux en énergie et, dans le cas des recuits vase clos, également en temps. Les avantages économiques procurés par la coulée directe de bandes minces sont donc en grande partie atténués par ces procédés.All these processes require special heat treatments, which can require special installations, be costly in energy and, in the case of vase annealing closed, also in time. The economic benefits of direct casting Thin strips are therefore largely attenuated by these methods.

Le but de l'invention est de procurer aux aciéristes un procédé de fabrication, par coulée entre cylindres, de bandes minces d'acier inoxydable ferritique devant subir ensuite les transformations à froid classiques, sans nécessiter d'opérations complexes ou coûteuses telles qu'un refroidissement contrôlé de la bande ou un recuit vase clos pour conférer auxdites bandes une bonne ductilité.The object of the invention is to provide steelmakers with a manufacturing process, by casting between cylinders, thin strips of ferritic stainless steel to be subjected thereafter conventional cold processing, without requiring complex or costly operations such as controlled strip cooling or closed annealing to provide said strips have good ductility.

Avec cet objectif en vue, l'invention a pour objet un procédé de coulée de bandes minces d'épaisseur inférieure à 10 mm en acier inoxydable ferritique directement à partir de métal liquide entre deux cylindres refroidis en rotation à axes horizontaux parallèles, caractérisé en ce que :

  • ledit acier inoxydable ferritique contient (en pourcentages pondéraux) de 11 à 18% de chrome, moins de 1% de manganèse, moins de 1% de silicium, moins de 2,5% de molybdène ;
  • ledit acier inoxydable ferritique a des teneurs en carbone et azote dont la somme des teneurs ne dépasse pas 0,05%;
  • ledit acier inoxydable ferritique contient au moins l'un des éléments stabilisants titane, niobium, zirconium, aluminium, et la somme de leurs teneurs est comprise entre 0,05 et 1%;
  • les autres éléments présents sont du fer et des impuretés habituelles résultant de l'élaboration ;
  • l'indice γp dudit acier inoxydable ferritique est supérieur ou égal à 30, avec : γp = 420 C% + 470 N% + 23 Ni% + 9 Cu% + 7 Mn% - 11,5 Cr% -11,5 Si% - 12 Mo% - 23 V% - 47 Nb% - 49 Ti% - 52 Al% + 189
  • et en ce qu'après la coulée on effectue un bobinage de la bande mince à une température inférieure à 600°C.
With this objective in view, the invention relates to a process for casting thin strips of thickness less than 10 mm in ferritic stainless steel directly from liquid metal between two cylinders cooled in rotation with parallel horizontal axes, characterized in that than :
  • said ferritic stainless steel contains (in weight percentages) from 11 to 18% of chromium, less than 1% of manganese, less than 1% of silicon, less than 2.5% of molybdenum;
  • said ferritic stainless steel has carbon and nitrogen contents the sum of the contents of which does not exceed 0.05%;
  • said ferritic stainless steel contains at least one of the stabilizing elements titanium, niobium, zirconium, aluminum, and the sum of their contents is between 0.05 and 1%;
  • the other elements present are iron and usual impurities resulting from the production;
  • the γp index of said ferritic stainless steel is greater than or equal to 30, with: γp = 420 C% + 470 N% + 23 Ni% + 9 Cu% + 7 Mn% - 11.5 Cr% -11.5 Si% - 12 Mo% - 23 V% - 47 Nb% - 49 Ti% - 52 Al% + 189
  • and in that, after casting, the thin strip is wound at a temperature below 600 ° C.

L'invention a également pour objet des bandes minces susceptibles d'être obtenues par le procédé précédent.The subject of the invention is also thin strips capable of being obtained by the previous process.

Comme on l'aura compris, l'invention consiste à associer la présence d'un ou plusieurs éléments stabilisants en quantités significatives à des teneurs en autres éléments d'alliage qui maintiennent néanmoins l'indice γp à une valeur élevée, et à un bobinage de la bande à une température relativement basse. La conjonction d'éléments stabilisants et d'un indice γp élevé n'était pas connue dans l'art antérieur, a fortiori son association avec une température de bobinage basse qui permet de concilier ces caractéristiques analytiques avec une très bonne ductilité de la bande, sans, de plus, qu'il soit nécessaire de procéder à un refroidissement contrôlé de la bande ou à un traitement thermique pénalisant en temps et en énergie.As will be understood, the invention consists in associating the presence of one or several stabilizing elements in significant quantities at levels of other elements alloy which nevertheless maintain the index γp at a high value, and at a winding of the strip at a relatively low temperature. The conjunction of stabilizing elements and a high γp index was not known in the prior art, a fortiori its association with a low winding temperature which allows these analytical characteristics to be reconciled with very good ductility of the strip, without, moreover, that it is necessary to proceed with controlled cooling of the strip or a time-consuming heat treatment and in energy.

Les différentes caractéristiques sont motivées par les considérations suivantes. The different features are motivated by the following considerations.

La teneur en chrome supérieure à 11% est conforme aux exigences habituelles rencontrées dans les aciers inoxydables ferritiques. Le maximum de 18% est justifié en ce qu'au-delà de cette limite, la température de transition ductile-fragile des aciers inoxydables augmente sensiblement, et l'invention devient alors inopérante. Le chrome a également tendance à faire fortement baisser la valeur de l'indice γp.Chromium content above 11% meets usual requirements encountered in ferritic stainless steels. The maximum of 18% is justified in this that beyond this limit, the ductile-brittle transition temperature of steels stainless steel increases significantly, and the invention then becomes ineffective. Chromium has also tend to significantly decrease the value of the γp index.

Les teneurs en silicium et molybdène sont respectivement maintenues à 1% et 2,5% au maximum, afin d'éviter la formation de composés intermétalliques ou la formation de phases intermétalliques de type σ ou χ. La teneur maximale en silicium est d'ailleurs ni plus ni moins conforme à celles rencontrées sur les nuances ferritiques classiques, comme la teneur maximale en manganèse de 1%.The silicon and molybdenum contents are maintained respectively at 1% and 2.5% maximum, to avoid the formation of intermetallic compounds or the formation σ or χ type intermetallic phases. The maximum silicon content is also more or less consistent with those encountered on conventional ferritic grades, such as the maximum manganese content of 1%.

La teneur totale en éléments stabilisants, à savoir en titane, niobium, zirconium et aluminium, doit être supérieure ou égale à 0,05% pour qu'ils puissent jouer leur rôle habituel. Au-delà de 1%, on observe des problèmes de coulabilité de l'acier liquide à travers les busettes de l'installation de coulée, ainsi que la présence de défauts de surface sur la bande qui peuvent constituer des amorces de ruptures. Il faut également veiller à ce qu'une présence importante d'éléments stabilisants n'abaisse pas l'indice γp jusqu'à une valeur qui serait excessivement basse, si par ailleurs le silicium, le molybdène et le vanadium sont présents à de fortes teneurs. Simultanément, la teneur totale en carbone et azote ne doit pas dépasser 0,05% pour ne pas former une quantité excessive de carbures ou de carbonitrures fragilisants.The total content of stabilizing elements, namely titanium, niobium, zirconium and aluminum, must be greater than or equal to 0.05% so that they can play their role usual. Above 1%, problems of flowability of the liquid steel are observed. through the nozzles of the casting installation, as well as the presence of surface defects on the strip which can constitute the beginnings of ruptures. We must also ensure that that a significant presence of stabilizing elements does not lower the γp index to a value which would be excessively low, if otherwise silicon, molybdenum and vanadium are present at high contents. At the same time, the total carbon content and nitrogen should not exceed 0.05% to avoid forming an excessive amount of carbides or of embrittling carbonitrides.

Lorsque l'indice γp est inférieur à 30%, le biphasage ferrite-austénite à haute température, après la fin de la solidification, n'est pas suffisant pour permettre un affinement de la structure de la bande et améliorer sensiblement la ductilité du produit coulé. Si l'indice γp est supérieur à 60%, la ductilité se détériore, car la contraction résultant de la transformation de phase ferrite-austénite à haute température risque de conduire à l'apparition de défauts de surface tels que des criques, qui constituent autant d'amorces de ruptures possibles lors des opérations de transformation ultérieures.When the γp index is less than 30%, the high-ferrite-austenite two-phase temperature, after the end of solidification, is not sufficient to allow a refinement of the strip structure and significantly improve the ductility of the product sank. If the index γp is greater than 60%, the ductility deteriorates, because the contraction resulting from the transformation of ferrite-austenite phase at high temperature risk of lead to the appearance of surface defects such as cracks, which constitute as much possible initiations of ruptures during subsequent processing operations.

D'autre part, si la température de bobinage est supérieure à 600°C, il y a formation de précipités fragilisants, et le problème que l'on s'était posé n'est pas résolu.On the other hand, if the winding temperature is higher than 600 ° C, there is formation of weakening precipitates, and the problem that we had posed is not resolved.

On va, à présent, donner des exemples d'application de l'invention, et les confronter à des exemples de référence. Tous ces exemples concernent la coulée d'aciers inoxydables ferritiques à relativement basses teneurs en chrome (11,5% environ), mais il est entendu que des résultats comparables peuvent être obtenus avec des aciers présentant des teneurs en chrome plus élevées, dans la limite de 18% comme spécifié précédemment. Ces aciers ont été coulés en bandes de 3 mm d'épaisseur en sortie des cylindres. Le tableau 1 précise les compositions (en pourcentages pondéraux) des aciers ayant fait l'objet des essais ; les aciers A et B ont des compositions conformes aux exigences de l'invention, l'acier C est donné à titre de référence. Composition chimique des aciers étudiés Nuance C% Mn% P% S% Si% Ni% Cr% Cu% Mo% Nb% V% Ti% N% Al% γp% A 0,012 0,290 0,015 0,001 0,560 0,090 11,497 0,022 0,0006 0,002 0,079 0,178 0,010 0,005 53,6 B 0,014 0,225 0,017 0,002 0,471 0,088 11,514 0,009 0,042 0,288 0,045 0,003 0,011 0,002 50,6 C 0,011 0,282 0,015 0,001 0,688 0,065 11,711 0,028 0,0010 0,354 0,050 0,299 0,010 0,009 26,5 We will now give examples of application of the invention, and compare them with reference examples. All these examples relate to the casting of ferritic stainless steels with relatively low chromium contents (approximately 11.5%), but it is understood that comparable results can be obtained with steels having higher chromium contents, within the limit 18% as previously specified. These steels were cast in strips 3 mm thick at the outlet of the cylinders. Table 1 specifies the compositions (in percentages by weight) of the steels which have been the subject of the tests; steels A and B have compositions in accordance with the requirements of the invention, steel C is given by way of reference. Chemical composition of the steels studied Shade VS% mn% P% S% Yes% Or% Cr% Cu% Mo% No.% V% Ti% NOT% al% γp% AT 0.012 0.290 0,015 0,001 0.560 0.090 11,497 0,022 0.0006 0,002 0.079 0.178 0,010 0.005 53.6 B 0.014 0,225 0,017 0,002 0.471 0.088 11.514 0,009 0,042 0.288 0,045 0,003 0,011 0,002 50.6 VS 0,011 0.282 0,015 0,001 0.688 0,065 11.711 0,028 0.0010 0.354 0,050 0.299 0,010 0,009 26.5

Les nuances A, B et C se distinguent essentiellement en ce que la nuance A est stabilisée au titane, la nuance B est stabilisée au niobium et la nuance C est stabilisée par ces deux éléments à la fois. Dans cette dernière nuance, la présence simultanée à des teneurs assez importantes de ces deux stabilisants, ainsi que la teneur en silicium plus élevée que dans les nuances A et B, ont entraíné un abaissement de l'indice γp en dessous de la limite de 30% exigée par l'invention.The grades A, B and C are essentially distinguished in that the grade A is stabilized with titanium, grade B is stabilized with niobium and grade C is stabilized by these two elements at the same time. In this last nuance, the simultaneous presence of fairly high contents of these two stabilizers, as well as the higher silicon content higher than in grades A and B, resulted in a lowering of the γp index below of the 30% limit required by the invention.

Le tableau 2 regroupe les conditions d'essais particulières auxquelles ont été soumis les aciers précédents, en termes de taux de réduction et de température lors du laminage à chaud éventuel, et en termes de température de bobinage. On y a également reporté les résultats des essais de flexion par choc sur éprouvettes Charpy auxquels ont été soumises les bandes postérieurement à leur bobinage, dans le but de déterminer leur énergie de rupture à une température de 0°C. A cet effet, on a utilisé des éprouvettes entaillées en V. On considère qu'une énergie de rupture inférieure à 40 J/cm2 est insuffisante pour procurer aux bandes des propriétés garantissant un débobinage sans incident et pour autoriser les transformations à froid habituelles. Conditions de traitement des bandes et résultats des essais de flexion par choc effectués sur les éprouvettes Charpy Essai Nuance Taux de réduction au laminage à chaud (%) Température de laminage à chaud (°C) Température de bobinage (°C) Energie de rupture à 0°C (J/cm2) 1 (référence) A - - 800 35 2 (invention) A - - 500 85 3 (référence) B - - 800 20 4 (référence) C - - 500 30 5 (référence) A 10 1000 800 34 6 (invention) A 10 1000 500 185 Table 2 groups together the particular test conditions to which the preceding steels were subjected, in terms of reduction rate and temperature during possible hot rolling, and in terms of winding temperature. The results of the impact bending tests on Charpy specimens to which the strips were subjected after their winding were also reported therein, with the aim of determining their breaking energy at a temperature of 0 ° C. For this purpose, V-notched test pieces were used. It is considered that a breaking energy of less than 40 J / cm 2 is insufficient to provide the strips with properties guaranteeing unwinding without incident and to allow the usual cold transformations. Strip processing conditions and results of impact bending tests carried out on Charpy test pieces Trial Shade Reduction rate in hot rolling (%) Hot rolling temperature (° C) Winding temperature (° C) Breaking energy at 0 ° C (J / cm 2 ) 1 (reference) AT - - 800 35 2 (invention) AT - - 500 85 3 (reference) B - - 800 20 4 (reference) VS - - 500 30 5 (reference) AT 10 1000 800 34 6 (invention) AT 10 1000 500 185

Les essais 1 à 3 ont été effectués sur des aciers dont l'indice γp était supérieur à 30%, conformément à l'invention. Ils illustrent l'effet bénéfique d'un bobinage à basse température sur la ductilité de la bande, en ce que seul l'essai 2 où le bobinage a eu lieu à 500°C a donné lieu à une ductilité satisfaisante de la bande coulée, car on a réussi à éviter la formation de précipités fragilisants dans l'acier bobiné. Cela n'est pas possible lorsque le bobinage est effectué à 800°C (essais 1 et 3), et l'énergie de rupture par essai Charpy se situe alors en deçà de la limite inférieure de 40 J/cm2 que l'on considère comme satisfaisante.Tests 1 to 3 were carried out on steels whose γp index was greater than 30%, in accordance with the invention. They illustrate the beneficial effect of a low temperature winding on the ductility of the strip, in that only test 2 where the winding took place at 500 ° C. gave rise to satisfactory ductility of the cast strip, because we managed to avoid the formation of embrittling precipitates in the coiled steel. This is not possible when the winding is carried out at 800 ° C (tests 1 and 3), and the breaking energy by Charpy test is then below the lower limit of 40 J / cm 2 that we consider satisfactory.

Dans l'essai 4, le bobinage a bien été effectué à une température de 500°C, conformément à l'invention, et on n'a pas observé la formation de précipités fragilisants. Cependant, cet essai portait sur une nuance dont l'indice γp était inférieur aux 30% requis par l'invention, et la quantité d'austénite formée à chaud a été insuffisante pour permettre un affinement très substantiel de la structure à gros grains obtenue après la solidification. En conséquence, et malgré la présence en quantité élevée d'éléments stabilisants, la ductilité de la bande après bobinage n'était pas plus satisfaisante qu'après les essais 1 et 3.In test 4, the winding was indeed carried out at a temperature of 500 ° C., in accordance with the invention, and the formation of embrittling precipitates was not observed. However, this test related to a shade whose γp index was less than the 30% required by the invention, and the amount of hot formed austenite was insufficient to allow a very substantial refinement of the coarse-grained structure obtained after solidification. Consequently, and despite the presence in high quantity of stabilizing elements, the The ductility of the strip after winding was no more satisfactory than after tests 1 and 3.

Au cours des essais 5 et 6, on a examiné l'influence d'un laminage à chaud de la bande, effectué en sortie des cylindres avant le bobinage. Ce laminage a été effectué à une température de 1000°C, avec un taux de réduction de 10% de l'épaisseur de la bande. On constate (essai 5) que l'affinement de la structure initiale procuré par un tel laminage à chaud n'est cependant pas suffisant pour compenser les effets négatifs d'un bobinage à température élevée (800°C) sur la ductilité de la bande. En revanche, si le bobinage de la bande laminée à chaud dans de telles conditions est effectué à une température assez basse pour être conforme à l'invention (500°C, essai 6), on obtient une amélioration considérable de la ductilité par rapport à celle observée sur le même acier lors de l'essai 2 en l'absence de laminage à chaud, alors même que cette ductilité était déjà satisfaisante.During tests 5 and 6, the influence of a hot rolling of the strip, made at the outlet of the cylinders before winding. This lamination was carried out at a temperature of 1000 ° C, with a reduction rate of 10% in the thickness of the strip. We notes (test 5) that the refinement of the initial structure obtained by such rolling to warm is not enough to compensate for the negative effects of high temperature (800 ° C) on the ductility of the strip. On the other hand, if the winding of the hot rolled strip in such conditions is carried out at a fairly low temperature to be in accordance with the invention (500 ° C., test 6), a considerable improvement is obtained ductility compared to that observed on the same steel during test 2 in the absence hot rolling, even though this ductility was already satisfactory.

Claims (4)

  1. Method of casting thin strips of ferritic stainless steel less than 10 mm thick directly from liquid metal between two cooled rotating rollers with parallel horizontal axes, characterised in that:
    said ferritic stainless steel contains (in percent by weight) 11 to 18% of chromium, less than 1% of manganese, less than 1% of silicon, less than 2.5% of molybdenum;
    said ferritic stainless steel has carbon and nitrogen contents which total not more than 0.05%;
    said ferritic stainless steel contains at least one of the stabilising elements titanium, niobium, zirconium and aluminium, and the sum of their contents is between 0.05 and 1%;
    the other elements present are iron and conventional impurities resulting from the production process;
    the index γp of said ferritic stainless steel is greater than or equal to 30, with: γp = 420 C% + 470 N% + 23 Ni% + 9 Cu% + 7 Mn% - 11.5 Cr% - 11.5 Si% - 12 Mo% - 23 V% - 47 Nb% - 49 Ti% - 52 Al% + 189,
    and in that after the casting the thin strip is coiled at a temperature below 600°C.
  2. Method according to claim 1, characterised in that before being coiled said cast strip is subjected to hot rolling at between 1200 and 900°C with a reduction level of more than 5%.
  3. Method according to claim 1 or 2, characterised in that the index γp of said ferritic stainless steel is between 30 and 60%.
  4. Thin strip of highly ductile ferritic stainless steel, characterised in that it is capable of being produced by the method according to one of claims 1 to 3.
EP00909393A 1999-03-05 2000-02-29 Method for continuous casting of highly ductile ferritic stainless steel strips between rolls, and resulting thin strips Expired - Lifetime EP1163376B1 (en)

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FR9902749A FR2790485B1 (en) 1999-03-05 1999-03-05 CONTINUOUS CASTING PROCESS BETWEEN CYLINDERS OF HIGH-DUCTILITY FERRITIC STAINLESS STEEL STRIPS, AND THIN STRIPS THUS OBTAINED
FR9902749 1999-03-05
PCT/FR2000/000498 WO2000053817A1 (en) 1999-03-05 2000-02-29 Method for continuous casting of highly ductile ferritic stainless steel strips between rolls, and resulting thin strips

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KR100848939B1 (en) * 2000-09-29 2008-07-29 누코 코포레이션 Method for production of thin steel strip and thin steel strip produced thereby
US7117925B2 (en) * 2000-09-29 2006-10-10 Nucor Corporation Production of thin steel strip
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ITRM20010584A1 (en) * 2001-09-26 2003-03-26 Acciai Speciali Terni Spa FERRITIC STAINLESS STEEL AND ITS USE IN THE MANUFACTURE OF ITEMS FOR USE AT HIGH TEMPERATURES.
JP2005512759A (en) 2002-01-10 2005-05-12 カタナ テクノロジーズ ゲゼルシャフト ミット ベシュレンクテル ハフツング Refractive laser surgical apparatus and process
US7842434B2 (en) * 2005-06-15 2010-11-30 Ati Properties, Inc. Interconnects for solid oxide fuel cells and ferritic stainless steels adapted for use with solid oxide fuel cells
US8158057B2 (en) * 2005-06-15 2012-04-17 Ati Properties, Inc. Interconnects for solid oxide fuel cells and ferritic stainless steels adapted for use with solid oxide fuel cells
US7981561B2 (en) * 2005-06-15 2011-07-19 Ati Properties, Inc. Interconnects for solid oxide fuel cells and ferritic stainless steels adapted for use with solid oxide fuel cells
DE10339595A1 (en) * 2003-08-26 2005-04-07 Siemens Ag Method for predicting and controlling the pourability of liquid steel
RU2375145C2 (en) * 2003-10-10 2009-12-10 Ньюкор Корпорейшн Casting of steel strip
US7484551B2 (en) * 2003-10-10 2009-02-03 Nucor Corporation Casting steel strip
JP4959937B2 (en) * 2004-12-27 2012-06-27 株式会社日立産機システム Distribution transformer with corrosion diagnostic components
US9999918B2 (en) 2005-10-20 2018-06-19 Nucor Corporation Thin cast strip product with microalloy additions, and method for making the same
US9149868B2 (en) * 2005-10-20 2015-10-06 Nucor Corporation Thin cast strip product with microalloy additions, and method for making the same
US10071416B2 (en) * 2005-10-20 2018-09-11 Nucor Corporation High strength thin cast strip product and method for making the same
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US7975754B2 (en) * 2007-08-13 2011-07-12 Nucor Corporation Thin cast steel strip with reduced microcracking
WO2011100798A1 (en) 2010-02-20 2011-08-25 Bluescope Steel Limited Nitriding of niobium steel and product made thereby
RU2452788C2 (en) * 2010-02-27 2012-06-10 Российская Федерация, от имени которой выступает Министерство образования и науки РФ (Минобрнаука РФ) Rustproof nanostructured ferrite steel
CN102303212B (en) * 2011-06-24 2013-04-10 成都申信达机械有限公司 Process for manufacturing lining board of wet-spraying machine
CN107142364A (en) * 2017-04-27 2017-09-08 酒泉钢铁(集团)有限责任公司 A kind of super-purity ferrite stainless steel double roll strip casting rolling production process
CN109731913B (en) * 2019-02-21 2020-07-24 江苏沙钢集团有限公司 Method for reducing rolling force of rolling mill of double-roller continuous casting production line

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