EP1067203B1 - Verfahren zum Herstellen von Eisen-Kohlenstoff-Mangan-Legierungbändern und also hergestellte Bändern - Google Patents

Verfahren zum Herstellen von Eisen-Kohlenstoff-Mangan-Legierungbändern und also hergestellte Bändern Download PDF

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Publication number
EP1067203B1
EP1067203B1 EP00401860A EP00401860A EP1067203B1 EP 1067203 B1 EP1067203 B1 EP 1067203B1 EP 00401860 A EP00401860 A EP 00401860A EP 00401860 A EP00401860 A EP 00401860A EP 1067203 B1 EP1067203 B1 EP 1067203B1
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EP
European Patent Office
Prior art keywords
strip
rolling
annealing
casting
hot
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
Application number
EP00401860A
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English (en)
French (fr)
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EP1067203A1 (de
Inventor
Nicolas Guelton
Michel Faral
Odile Faral
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USINOR SA
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USINOR SA
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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 production 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 an in-line hot rolling by means of a small installation, the cost of manufacture and use of which is much lower to that of a band train.
  • the elimination of hot rolling on a train bands eliminates the risk 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 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 so 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 use of the process 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 reductive), 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 reductive
  • the role essential of this hot rolling is to close the porosities which may have been formed at the heart of the strip during its solidification, and to improve its surface condition by crushing the roughness peaks possibly 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 steps) 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 the 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 that does not matter much else than practical, since no significant metallurgical transformation other than growth grain is 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 optionally 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, which 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)

Claims (14)

  1. Verfahren zur Herstellung von Bändern aus einer Eisen-Kohlenstoff-Mangan-Legierung, bei dem :
    man ein dünnes Band mit einer Dicke zwischen 1,5 und 10 mm direkt auf einer Gussmaschine aus einem flüssigen Metall mit folgender gewichtsprozentualen Zusammensetzung giesst: C zwischen 0,001 und 1,6% ; Mn zwischen 6 und 30%, Ni ≤ 10% mit (Mn + Ni) zwischen 16 und 30% ; Si ≤ 2,5 % ; Al ≤ 6% ; Cr ≤ 10% ; (P + Sn + Sb + As) ≤ 0,2% ; (S + Se + Te ) ≤ 0,5 % ; (V + Ti + Nb + Zr + seltene Erden) ≤ 3% ; (Mo + W) ≤ 0, 5 % ; N ≤ 0,3% ; Cu ≤ 5% , wobei der Rest Eisen und aus der Zubereitung herrührende Unreinheiten sind;
    das besagte Band bei einem Reduktionsgrad zwischen 10 und 90% in einem oderer mehrereren Schritten kaltgewalzt wird;
    ein Rekristallisationsglühen des besagten Bandes ausgeführt wird.
  2. Verfahren nach Anspruch 1, dadurch gekennzeichnet, dass der Kohlenstoffgehalt des besagten flüssigen Metalls zwischen 0,2 und 0,8 % liegt.
  3. Verfahren nach Anspruch 1 oder 2, dadurch gekennzeichnet, dass das besagte Band durch Giessen zwischen zwei einander angenäherten, von innen gekühlten und in umgekehrter Richtung rotierender Zylinder erhalten wird.
  4. Verfahren nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass zwischen dem Giessen des Bandes und dem Kaltwalzen das besagte Band bei einem Reduktionsgrad zwischen 10 und 60 % in einem oder mehren Schritten warmgewalzt wird.
  5. Verfahren nach Anspruch 4, dadurch gekennzeichnet, dass das besagte Band zwischen seinem Guss und seinem Warmwalzen einen Bereich mit nicht oxydierender Atmosphäre durchquert.
  6. Verfahren nach einem der Ansprüche 4 oder 5, dadurch gekennzeichnet, dass das besagte Band vor seinem Warmwalzen einem Entzunderungsvorgang unterzogen wird.
  7. Verfahren nach einem der Ansprüche 1 bis 6, dadurch gekennzeichnet, dass das Band nach seinem Guss und seinem Warmwalzen aufgerollt und nach seinem Kaltwalzen entrollt wird.
  8. Verfahren nach einem der Ansprüche 1 bis 7, dadurch gekennzeichnet, dass das besagte Band vor dem Kaltwalzen einem Säurebeizen unterzogen wird.
  9. Verfahren nach einem der Ansprüche 1 bis 8, dadurch gekennzeichnet, dass das besagte Rekristallisationsglühen ein bei einer Temperatur zwischen 900 und 1100 °C ausgeführtes Kompaktglühen ist, welches unmittelbar von einer Abkühlung des Bandes mit einer Geschwindigkeit zwischen 100 und 600 °C/ Sekunde gefolgt wird.
  10. Verfahren nach einem der Ansprüche 1 bis 8, dadurch gekennzeichnet, dass das besagte Rekristallisationsglühen ein kontinuierliches Glühen ist, welches während 60 bis 120 Sekunden bei einer Temperatur zwischen 800 und 850 °C ausgeführt wird.
  11. Verfahren nach einem der Ansprüche 1 bis 8, dadurch gekennzeichnet, dass das besagte Rekristallisationsglühen ein Basisglühen ist, welches während 10 bis 90 Minuten bei einer Temperatur zwischen 700 und 750 °C ausgeführt wird.
  12. Verfahren nach einem der Ansprüche 1 bis 11, dadurch gekennzeichnet, dass das besagte Band nach dem besagten Rekristallisationsglühen gebeizt wird.
  13. Verfahren nach einem der Ansprüche 1 bis 12, dadurch gekennzeichnet, dass das besagte Band nach dem besagten Rekristallisationsbeizen oder dem Beizen einem "skin-pass"-Durchgang unterzogen wird.
  14. Band aus einer Eisen-Kohlenstoff-Mangan-Legierung, dadurch gekennzeichnet, dass es nach einem Verfahren nach einem der Ansprüche 1 bis 13 hergestellt wird.
EP00401860A 1999-07-07 2000-06-29 Verfahren zum Herstellen von Eisen-Kohlenstoff-Mangan-Legierungbändern und also hergestellte Bändern Expired - Lifetime EP1067203B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR9908758 1999-07-07
FR9908758A FR2796083B1 (fr) 1999-07-07 1999-07-07 Procede de fabrication de bandes en alliage fer-carbone-manganese, et bandes ainsi produites

Publications (2)

Publication Number Publication Date
EP1067203A1 EP1067203A1 (de) 2001-01-10
EP1067203B1 true EP1067203B1 (de) 2004-03-03

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Country Status (9)

Country Link
US (1) US6358338B1 (de)
EP (1) EP1067203B1 (de)
JP (2) JP4713709B2 (de)
AT (1) ATE260992T1 (de)
BR (1) BR0002544A (de)
CA (1) CA2314624C (de)
DE (1) DE60008641T2 (de)
ES (1) ES2215008T3 (de)
FR (1) FR2796083B1 (de)

Cited By (5)

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CN101090982B (zh) * 2004-11-24 2010-09-08 阿塞洛法国公司 生产具有非常高强度和伸长性能以及良好均匀性的铁-碳-锰奥氏体钢板的方法
EP1399598B2 (de) † 2001-06-26 2011-02-23 ThyssenKrupp Steel Europe AG Verfahren zum herstellen von hochfesten, aus einem warmband kaltverformten stahlprodukten mit guter dehnbarkeit
CN101107377B (zh) * 2005-01-21 2011-03-23 阿塞洛法国公司 铁-碳-锰奥氏体钢板的制造方法和由此制造的板材
US9677146B2 (en) 2008-11-12 2017-06-13 Voestalpine Stahl Gmbh Manganese steel strip having an increased phosphorous content and process for producing the same
WO2018036918A1 (de) 2016-08-23 2018-03-01 Salzgitter Flachstahl Gmbh Verfahren zur herstellung eines höchstfesten stahlbandes mit verbesserten eigenschaften bei der weiterverarbeitung und ein derartiges stahlband

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JP6703608B2 (ja) * 2015-12-22 2020-06-03 ポスコＰｏｓｃｏ 耐水素脆化性に優れたオーステナイト系鋼材
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FR2796083B1 (fr) 2001-08-31
JP2001049348A (ja) 2001-02-20
BR0002544A (pt) 2001-03-13
JP4713709B2 (ja) 2011-06-29
ES2215008T3 (es) 2004-10-01
CA2314624A1 (fr) 2001-01-07
ATE260992T1 (de) 2004-03-15
JP2011068997A (ja) 2011-04-07
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DE60008641T2 (de) 2005-02-03
CA2314624C (fr) 2009-04-07

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