EP1067203A1 - "Procédé de fabrication de bandes en alliage fer-carbonne-manganese, et bandes ainsi produites" - Google Patents
"Procédé de fabrication de bandes en alliage fer-carbonne-manganese, et bandes ainsi produites" Download PDFInfo
- 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
- Authority
- EP
- European Patent Office
- Prior art keywords
- strip
- annealing
- casting
- rolling
- carried out
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
- C21D8/0215—Rapid solidification; Thin strip casting
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final 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.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Continuous Casting (AREA)
- Metal Rolling (AREA)
- Catalysts (AREA)
Abstract
Description
- 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.
- 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%.
- 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 ;
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.
- Procédé selon la revendication 1, caractérisé en ce que la teneur en carbone dudit métal liquide est comprise entre 0,2 et 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.
- 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.
- 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.
- 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.
- 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.
- Procédé selon l'une des revendications 1 à 7, caractérisé en ce que ladite bande subit un décapage acide avant son laminage à froid.
- 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.
- 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.
- 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.
- Procédé selon l'une des revendications 1 à 11, caractérisé en ce que ladite bande est décapée après ledit recuit de recristallisation.
- 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.
- 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.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR9908758A FR2796083B1 (fr) | 1999-07-07 | 1999-07-07 | Procede de fabrication de bandes en alliage fer-carbone-manganese, et bandes ainsi produites |
FR9908758 | 1999-07-07 |
Publications (2)
Publication Number | Publication Date |
---|---|
EP1067203A1 true EP1067203A1 (fr) | 2001-01-10 |
EP1067203B1 EP1067203B1 (fr) | 2004-03-03 |
Family
ID=9547798
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP00401860A Expired - Lifetime EP1067203B1 (fr) | 1999-07-07 | 2000-06-29 | "Procédé de fabrication de bandes en alliage fer-carbone-manganèse, et bandes ainsi produites" |
Country Status (9)
Country | Link |
---|---|
US (1) | US6358338B1 (fr) |
EP (1) | EP1067203B1 (fr) |
JP (2) | JP4713709B2 (fr) |
AT (1) | ATE260992T1 (fr) |
BR (1) | BR0002544A (fr) |
CA (1) | CA2314624C (fr) |
DE (1) | DE60008641T2 (fr) |
ES (1) | ES2215008T3 (fr) |
FR (1) | FR2796083B1 (fr) |
Cited By (16)
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WO2002101109A1 (fr) | 2001-06-13 | 2002-12-19 | Thyssenkrupp Stahl Ag | Acier et feuillard ou tole d'acier a resistance tres elevee, pouvant etre forme a froid, procede pour produire un feuillard d'acier et utilisations d'un tel acier |
GB2385862A (en) * | 2002-02-27 | 2003-09-03 | Edgar Allen Ltd | A Cast Austenitic Manganese-Nickel Steel |
FR2857980A1 (fr) * | 2003-07-22 | 2005-01-28 | Usinor | Procede de fabrication de toles d'acier austenitique fer-carbone-manganese, a haute resistance, excellente tenacite et aptitude a la mise en forme a froid, et toles ainsi produites |
WO2005061152A1 (fr) * | 2003-12-23 | 2005-07-07 | Salzgitter Flachstahl Gmbh | Procede pour produire des feuillards a chaud a partir d'un acier leger |
FR2876708A1 (fr) * | 2004-10-20 | 2006-04-21 | Usinor Sa | Procede de fabrication de toles d'acier austenitique fer-carbone-manganese laminees a froid a hautes caracteristiques mecaniques, resistantes a la corrosion et toles ainsi produites |
WO2006048034A1 (fr) * | 2004-11-03 | 2006-05-11 | Thyssenkrupp Steel Ag | Bande ou tole d'acier extremement resistante a proprietes twip et procede de fabrication de ladite bande a l'aide de la 'coulee directe de bandes' |
FR2878257A1 (fr) * | 2004-11-24 | 2006-05-26 | Usinor Sa | Procede de fabrication de toles d'acier austenitique, fer-carbone-manganese a tres hautes caracteristiques de resistance et d'allongement, et excellente homogeneite |
WO2006077301A1 (fr) * | 2005-01-21 | 2006-07-27 | Arcelor France | Procede de fabrication de toles d'acier austenitique fer-carbone-manganese et toles ainsi produites |
WO2007074994A1 (fr) | 2005-12-24 | 2007-07-05 | Posco | Tole d'acier a forte teneur en mn, presentant une grande resistance a la corrosion et procede de galvanisation de la tole d'acier |
EP2208803A1 (fr) | 2009-01-06 | 2010-07-21 | ThyssenKrupp Steel Europe AG | Acier à résistance élevée, formable à froid, produit plat en acier, procédé de fabrication d'un produit plat en acier et utilisation du produit plat en acier |
CN101956134A (zh) * | 2010-11-01 | 2011-01-26 | 福州大学 | 一种高强度、高塑性含铜高碳twip钢及其制备工艺 |
WO2012052626A1 (fr) | 2010-10-21 | 2012-04-26 | Arcelormittal Investigacion Y Desarrollo, S.L. | Tole d'acier laminee a chaud ou a froid, don procede de fabrication et son utilisation dans l'industrie automobile |
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KR100711361B1 (ko) * | 2005-08-23 | 2007-04-27 | 주식회사 포스코 | 가공성이 우수한 고망간형 고강도 열연강판 및 그 제조방법 |
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US10071416B2 (en) * | 2005-10-20 | 2018-09-11 | Nucor Corporation | High strength thin cast strip product 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 |
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KR100742823B1 (ko) * | 2005-12-26 | 2007-07-25 | 주식회사 포스코 | 표면품질 및 도금성이 우수한 고망간 강판 및 이를 이용한도금강판 및 그 제조방법 |
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Also Published As
Publication number | Publication date |
---|---|
FR2796083B1 (fr) | 2001-08-31 |
DE60008641T2 (de) | 2005-02-03 |
JP2011068997A (ja) | 2011-04-07 |
FR2796083A1 (fr) | 2001-01-12 |
CA2314624C (fr) | 2009-04-07 |
JP2001049348A (ja) | 2001-02-20 |
CA2314624A1 (fr) | 2001-01-07 |
BR0002544A (pt) | 2001-03-13 |
US6358338B1 (en) | 2002-03-19 |
EP1067203B1 (fr) | 2004-03-03 |
JP4713709B2 (ja) | 2011-06-29 |
DE60008641D1 (de) | 2004-04-08 |
ES2215008T3 (es) | 2004-10-01 |
ATE260992T1 (de) | 2004-03-15 |
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