EP1725347A1 - Process and installation for producing a lightweight structural steel with a high manganese content - Google Patents

Process and installation for producing a lightweight structural steel with a high manganese content

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Publication number
EP1725347A1
EP1725347A1 EP06723198A EP06723198A EP1725347A1 EP 1725347 A1 EP1725347 A1 EP 1725347A1 EP 06723198 A EP06723198 A EP 06723198A EP 06723198 A EP06723198 A EP 06723198A EP 1725347 A1 EP1725347 A1 EP 1725347A1
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EP
European Patent Office
Prior art keywords
casting
slab
slabs
casting powder
furnace
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Granted
Application number
EP06723198A
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German (de)
French (fr)
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EP1725347B1 (en
Inventor
Jens Kempken
Markus Reifferscheid
Albrecht Girgensohn
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SMS Siemag AG
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SMS Demag AG
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Classifications

    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
    • B21B1/466—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting in a non-continuous process, i.e. the cast being cut before rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel
    • 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
    • B22D11/10—Supplying or treating molten metal
    • B22D11/11—Treating the molten metal
    • B22D11/111—Treating the molten metal by using protecting powders
    • 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
    • B22D11/12—Accessories for subsequent treating or working cast stock in situ
    • B22D11/1213—Accessories for subsequent treating or working cast stock in situ for heating or insulating strands
    • 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
    • B22D11/14—Plants for continuous casting
    • B22D11/142—Plants for continuous casting for curved 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
    • C21D6/00—Heat treatment 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • 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

Definitions

  • the invention relates to a method and a plant for producing a hot strip of a good cold-workable, high-strength, austenitic lightweight steel with increased levels of manganese (Mn), aluminum (AI) and SiIi- zium (Si) with TWIP properties (Twinning-induced Plasticity) in which the steel is first cast on a continuous casting plant to a continuous strand, divided into slabs and then rolled to the final thickness.
  • Mn manganese
  • AI aluminum
  • TWIP properties winning-induced Plasticity
  • Austenitic lightweight steels with TWIP properties for use in, for example, body panel parts, stiffening body elements, as well as cryo gen-containers and pipes have, for example, according to EP 0889144 B1 a chemical composition of 10 to 30% Mn, 1 to 6% Si 1 1 up to 8% Al (with Si + Al ⁇ 12%), balance Fe.
  • a high-strength lightweight steel with 7 to 30% Mn, 1 to 10% Al, 0.7 to 4% Si, ⁇ 10% Cr, ⁇ 10% Ni, ⁇ 3% Cu and ⁇ 0, 5% C and optionally with the other alloying elements N 1 Va 1 Nb 1 Ti, P described, which in addition to good mechanical properties also has good corrosion and stress corrosion cracking resistance.
  • This steel is to be cast in a continuous casting process and hot rolled or slotted close to the final dimensions by thin strip casting.
  • WO 02/101109 A1 discloses a process according to which, by increasing the possible carbon content (C ⁇ 1%) and by adding further elements, here in particular B, also Ni, Cu, N, Nb, Ti, V, P, a significant reduction of the yield strength and thus an improvement in ductility during hot and cold rolling is achieved.
  • a starting material (slab, thin slab or strip) is heated and hot rolled and coiled under consideration of certain temperature limits.
  • EP 1 341 937 B1 describes a process in which a 12 to 30% Mn-containing steel is cast with a two-roll casting machine into a thin pre-strip having a thickness of less than 1 mm to 6 mm, which is vertical From the casting gap emerging pre-strip is cooled by applied to its surface coolant and then rolled in a single hot roll pass to the final thickness. The total time between exit from the casting gap and entry into the rolling stand is about 8 seconds.
  • EP 1 067 203 B1 discloses a process for the production of strips of an Fe-C-Mn alloy, in which initially a thin steel strip having a thickness of between 1.5 and 10 mm and having the composition: 6 to 30% Mn, 0.001 to 1, 6% C, ⁇ 2.5% Si, ⁇ 6% Al 1 ⁇ 10% Cr and other elements produced on a two-roller casting machine and this then with a degree of reduction between 10 and 60% in one or several steps hot rolled.
  • the stated object is procedurally achieved with the characterizing features of claim 1, characterized in that by successively arranged process steps a lightweight steel with the predetermined chemical composition of 15 to 27% Mn, 1 to 6% Al 1 1 to 6% Si, ⁇ 0.8 % C, 5 remainder Fe and accompanying elements
  • An installation for carrying out the method is characterized by the features of claim 7.
  • roller hearth furnace of a CSP plant due to the short lead times greater depletion of the alloying elements or the oxidation of the grain boundaries avoided, which is difficult, for example, in the longer heating phases in the blast furnace of a conventional hot strip mill in the prior art can lead.
  • a suitable casting powder is required.
  • Such a suitable casting powder according to the invention has the property of achieving equilibrium very quickly and then no longer changing its lubricating behavior.
  • the casting powder according to the invention contains an increased proportion of Al 2 O 3 of> 10%.
  • the SiO 2 proportion of the casting powder is alternatively or additionally increased, this increase being carried out up to a basicity (ratio CaOZSiO 2 ) of 0.5-0.7.
  • MnO 2 is more easily reduced by the Al of the steel than SiO 2 and thereby the SiO 2 is protected from this reduction (from burnup), it is possible to add MnO 2 to the casting powder as a further measure of the invention. Even a partial replacement of the SiO 2 by TiO 2 , which acts like SiO 2 glass-forming, but is not attacked (reduced) by the Al of the steel, may be added to the casting powder according to the invention.
  • the plant used is a known CSP plant in which, according to the invention, the distances between the individual plant components have been changed so far that the method of the invention with the requirements, directly after the solidification in an intermediate furnace in the course of a temperature compensation bring about and then hot roll the slab directly without interim cooling, is feasible.
  • the plant shown in the drawing figure therefore consists of a thin slab caster 1 and a downstream intermediate furnace 4, in which the divided from the endless strand 2 after its solidification slab 3 is introduced.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Metal Rolling (AREA)
  • Continuous Casting (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

For various reasons, in the prior art it is considered difficult or impossible to produce steels with high manganese (Mn), aluminium (AI) and silicon (Si) contents and with TWIP (Twinning Induced Plasticity) properties by continuous casting. The reasons cited include low strength of the strand shell during solidification on account of extensive micro-segregation of Mn, high strength at lower temperatures, reactions of the aluminium in the steel with the casting powder, macro-segregations, depletion of the alloying elements in the surface region and oxidation of the grain boundaries during the reheating of slabs in the pusher furnace. Therefore, the invention proposes that, by successive process steps, lightweight structural steel with a predetermined chemical composition of up to 27% Mn, 1 to 6% AI, 1 to 6% Si, < 0.8% C, remainder Fe and accompanying elements, be cast on a thin-slab casting machine (1 ) (d ≤ 120 mm) using suitable casting powders, then immediately after the solidification slabs (3) be severed from the endless strand (2) and that temperature equalization be carried out during continuous passage through an intermediate furnace (4) and then the slab (3) be directly hot-rolled without intervening cooling.

Description

Verfahren und Anlage zur Herstellung eines Leichtbaustahls mit einem hohen Mangan-GehaltMethod and plant for producing a lightweight steel with a high manganese content
Die Erfindung betrifft ein Verfahren und eine Anlage zur Herstellung eines Warmbandes aus einem gut kaltumformbaren, hochfesten, austenitischen Leichtbaustahl mit erhöhten Gehalten an Mangan (Mn), Aluminium (AI) und SiIi- zium (Si) mit TWIP-Eigenschaften (Twinning jnduced Plasticity), wobei der Stahl zunächst auf einer Stranggießanlage zu einem Endlosstrang vergossen, in Brammen unterteilt und dann auf die Enddicke gewalzt wird.The invention relates to a method and a plant for producing a hot strip of a good cold-workable, high-strength, austenitic lightweight steel with increased levels of manganese (Mn), aluminum (AI) and SiIi- zium (Si) with TWIP properties (Twinning-induced Plasticity) in which the steel is first cast on a continuous casting plant to a continuous strand, divided into slabs and then rolled to the final thickness.
Austenitische Leichtbaustähle mit TWIP-Eigenschaften zur Verwendung für bei- spielsweise Karosserieblechteile, versteifende Karosserieelemente sowie Cryo- gen-Behälter und Rohrleitungen besitzen beispielsweise entsprechend der EP 0 889 144 B1 eine chemische Zusammensetzung von 10 bis 30 % Mn, 1 bis 6 % Si1 1 bis 8 % AI (mit Si + AI < 12 %), Rest Fe.Austenitic lightweight steels with TWIP properties for use in, for example, body panel parts, stiffening body elements, as well as cryo gen-containers and pipes have, for example, according to EP 0889144 B1 a chemical composition of 10 to 30% Mn, 1 to 6% Si 1 1 up to 8% Al (with Si + Al <12%), balance Fe.
In der DE 199 00 199 A1 wird ein hochfester Leichbaustahl mit 7 bis 30 % Mn, 1 bis 10 % AI, 0,7 bis 4 % Si, < 10 % Cr, < 10 % Ni, < 3 % Cu und < 0,5 % C sowie optional mit den weiteren Legierungselementen N1 Va1 Nb1 Ti, P beschrieben, der neben guten mechanischen Eigenschaften auch gute Korrosions- und Spannungsrisskorrosionsbeständigkeit besitzt. Dieser Stahl soll im Stranggießverfahren vergossen und warmgewalzt oder durch Dünnbandgießen endabmessungsnah vergossen werden.In DE 199 00 199 A1, a high-strength lightweight steel with 7 to 30% Mn, 1 to 10% Al, 0.7 to 4% Si, <10% Cr, <10% Ni, <3% Cu and <0, 5% C and optionally with the other alloying elements N 1 Va 1 Nb 1 Ti, P described, which in addition to good mechanical properties also has good corrosion and stress corrosion cracking resistance. This steel is to be cast in a continuous casting process and hot rolled or slotted close to the final dimensions by thin strip casting.
Die Herstellung von hochmanganhaltigen Stählen durch Strangguss wird nach dem Stand der Technik aus verschiedenen Gründen als schwierig bzw. unmög- lieh angesehen. Die genannten Gründe sind: geringe Festigkeit der Strangschale bei der Erstarrung wegen starker Mikroseigerung von Mn (Durchbruchgefahr bei Mn > 15 %), hohe Festigkeit bei niedrigeren Temperaturen (Anlagenüberlastung, Rissprobleme), Reaktionen des Aluminium im Stahl mit dem Gießpulver (Einschränkung der Funktion), Makroseigerungen, Wasserstoff- und/oder Sauerstoffaufnahme durch die Spritzwasserkühlung, vermehrtes Auftreten von nichtmetallischen Einschlüssen, Abreicherung der Legierungselemente im Randbereich sowie Oxidation der Korngrenzen bei der Wiedererwärmung von Brammen im Stoßofen.The production of high manganese steels by continuous casting is regarded as difficult or impossible according to the prior art for various reasons. The reasons given are: low strength of the strand shell during solidification due to strong micro segregation of Mn (breakthrough risk at Mn> 15%), high strength at lower temperatures (system overload, cracking problems), reactions of the aluminum in the steel with the casting powder (restriction of function), macrosegregations, hydrogen and / or oxygen uptake by spray water cooling, increased occurrence of non-metallic inclusions, Depletion of the alloying elements in the edge area and oxidation of the grain boundaries during the reheating of slabs in the pusher furnace.
In einer Veröffentlichung von Spitzer et al.: "Innovative Stahlprodukte - Herausforderung für die Prozessentwicklung"1; Konferenz-Einzelbericht: Barbara 2001 , S. 71 - 84 wird hierzu ausgesagt, dass Stähle mit steigendem Mangangehalt zunehmend schwieriger zu vergießen sind. Sie weisen zum einen bei hohen Temperaturen nach der Erstarrung eine geringe Festigkeit auf, da sich Mangan bei hohen Gehalten in der Restschmelze stark anreichert und in den interdendritischen Bereichen den Schmelzpunkt absenkt. Hierdurch steigt die Nei- gung zu Kleberdurchbrüchen, die bei Mn-Gehalten von 15 % und mehr nach heutiger Einschätzung ein Stranggießverfahren unmöglich machen. Die Stähle weisen andererseits bei niedrigeren Temperaturen eine hohe Festigkeit auf, so dass beim Biegen des Stranges Anlagenüberlastungen auftreten und mit Rissbildung gerechnet werden muss. Des Weiteren erfolgen bei Aluminiumgehalten von mehreren Prozenten, wie sie bei diesen Stählen u. a. zur Absenkung der Dichte eingestellt werden, Reaktionen mit dem Gießpulver, die dessen Funktion gravierend beeinträchtigen.In a publication by Spitzer et al .: "Innovative steel products - a challenge for process development"1; Conference Report: Barbara 2001, pp. 71-84 states that steels are increasingly difficult to shed with increasing manganese content. On the one hand, they have a low strength at high temperatures after solidification, since manganese accumulates strongly at high levels in the residual melt and lowers the melting point in the interdendritic areas. As a result, the tendency for adhesive breakthroughs increases, which make a continuous casting at Mn levels of 15% and more impossible according to current estimates. The steels, on the other hand, exhibit high strength at lower temperatures, so that when the strand is bent, system overloads occur and crack formation must be expected. Furthermore, with aluminum contents of several percent, as set in these steels, among other things, to lower the density, reactions with the casting powder, which seriously affect its function.
In einer anderen Veröffentlichung von Gigacher et al.: "Eigenschaften hoch- manganhaltiger Stähle unter stranggießähnlichen Bedingungen"; BHM 149 (2004), Heft 3, S. 112 - 117 wird hierzu zusammenfassend festgestellt, dass das Vergießen der vorgestellten Legierungskonzepte zur Erzeugung von TWIP- Stählen für Verfahren mit Gießpulver nicht vorteilhaft ist.In another publication by Gigacher et al .: "Properties of high-manganese steels under continuous casting-like conditions"; BHM 149 (2004), No. 3, pp. 112-117, it is stated in summary that the casting of the presented alloying concepts for the production of TWIP steels is not advantageous for methods with casting powder.
Das vorherrschende Problem beim Gießen von Stählen mit einem hohen AI- Gehalt (> 1 %) ist die Reaktion des AI aus dem Stahl mit den oxidischen Be- standteilen des Gießpulvers. Durch die Reduktion des SiO2 in der Schlacke durch das AI aus dem Stahl entsteht AI2O3, das von der Schlacke aufgenommen wird, wodurch die Basizität (Verhältnis CaO/SiO2) der Schlacke zunimmt. Die Folge ist, dass sich Viskosität und Schmierverhältnisse in der Kokille sehr stark verändern.The predominant problem when casting steels with a high Al content (> 1%) is the reaction of Al from the steel with the oxide constituents of the casting powder. The reduction of the SiO 2 in the slag by the Al from the steel produces Al 2 O 3 , which is taken up by the slag, whereby the basicity (ratio CaO / SiO 2 ) of the slag increases. The consequence is that viscosity and lubricating conditions in the mold change very much.
Auf Grund dieser Schwierigkeiten wurden in der Vergangenheit verschiedene Verfahrenswege zur Herstellung von TWIP-Stählen beschriften:Because of these difficulties, in the past, various ways of producing TWIP steels have been described:
Aus der WO 02/101109 A1 ist ein Verfahren bekannt, nach dem durch Erhö- hung des möglichen Kohlenstoffgehalts (C ≤ 1 %) und durch Zugabe weiterer Elemente, hier besonders B, auch Ni, Cu, N, Nb, Ti, V, P, eine deutliche Verminderung der Streckgrenze und damit eine Verbesserung der Verformbarkeit beim Warm- und Kaltwalzen erreicht wird. Für die Herstellung dieses Stahls wird ein Vormaterial (Bramme, Dünnbramme oder Band) erwärmt und unter Beachtung bestimmter Temperaturgrenzen warmgewalzt und gehaspelt.WO 02/101109 A1 discloses a process according to which, by increasing the possible carbon content (C ≦ 1%) and by adding further elements, here in particular B, also Ni, Cu, N, Nb, Ti, V, P, a significant reduction of the yield strength and thus an improvement in ductility during hot and cold rolling is achieved. For the production of this steel, a starting material (slab, thin slab or strip) is heated and hot rolled and coiled under consideration of certain temperature limits.
In der EP 1 341 937 B1 wird ein Verfahren beschrieben, bei dem ein 12 bis 30 % Mn enthaltender Stahl mit einer Zwei-Rollen-Gießmaschine zu einem dünnen Vorband mit einer Dicke von weniger als 1 mm bis 6 mm vergossen, das verti- kal aus dem Gießspalt austretende Vorband durch auf seine Oberfläche aufgebrachte Kühlmittel gekühlt und dann in einem einzigen Warmwalzstich auf die Enddicke gewalzt wird. Die Gesamtzeitspanne zwischen Austritt aus dem Gießspalt und Eintritt in das Walzgerüst beträgt etwa 8 Sekunden.EP 1 341 937 B1 describes a process in which a 12 to 30% Mn-containing steel is cast with a two-roll casting machine into a thin pre-strip having a thickness of less than 1 mm to 6 mm, which is vertical From the casting gap emerging pre-strip is cooled by applied to its surface coolant and then rolled in a single hot roll pass to the final thickness. The total time between exit from the casting gap and entry into the rolling stand is about 8 seconds.
Aus der EP 1 067 203 B1 ist ein Verfahren zur Herstellung von Bändern aus einer Fe-C-Mn Legierung bekannt, bei dem zunächst ein dünnes Stahlband mit einer Dicke zwischen 1,5 bis 10 mm mit der Zusammensetzung: 6 bis 30 % Mn, 0,001 bis 1 ,6 % C, < 2,5 % Si, < 6 % Al1 < 10 % Cr sowie weiteren Elementen auf einer Zwei-Rollen-Gießmaschine erzeugt und dieses dann mit einem Re- duktionsgrad zwischen 10 und 60 % in einem oder mehreren Schritten warmgewalzt wird. Ausgehend von diesem Stand der Technik ist es Aufgabe der Erfindung, ein möglichst einfach zu realisierendes Verfahren und eine Anlage anzugeben, mit der hochmanganhaltige Stähle mit einer vorgegebenen chemischen Zusammensetzung durch Stranggießen hergestellt werden können. oEP 1 067 203 B1 discloses a process for the production of strips of an Fe-C-Mn alloy, in which initially a thin steel strip having a thickness of between 1.5 and 10 mm and having the composition: 6 to 30% Mn, 0.001 to 1, 6% C, <2.5% Si, <6% Al 1 <10% Cr and other elements produced on a two-roller casting machine and this then with a degree of reduction between 10 and 60% in one or several steps hot rolled. Based on this prior art, it is an object of the invention to provide a method and a system which is as simple as possible to realize by means of continuous casting high-manganese steels having a predetermined chemical composition. O
Die gestellte Aufgabe wird verfahrensmäßig mit den kennzeichnenden Merkmalen des Anspruchs 1 dadurch gelöst, dass durch hintereinander angeordnete Verfahrensschritte ein Leichtbaustahl mit der vorgegebenen chemischen Zusammensetzung von 15 bis 27 % Mn, 1 bis 6 % Al1 1 bis 6 % Si, < 0,8 % C, 5 Rest Fe und BegleitelementeThe stated object is procedurally achieved with the characterizing features of claim 1, characterized in that by successively arranged process steps a lightweight steel with the predetermined chemical composition of 15 to 27% Mn, 1 to 6% Al 1 1 to 6% Si, <0.8 % C, 5 remainder Fe and accompanying elements
• auf einer Dünnbrammengießmaschine (d ≤ 120 mm) unter Verwendung von geeigneten Gießpulvern, die sehr schnell ein Gleichgewicht erreichen und anschließend ihr Schmierverhalten nicht mehr verändern, vergossen und in Brammen unterteilt wird, 0 • direkt anschließend an die Erstarrung und Abtrennung einer Bramme in einem Zwischenofen im Durchlauf ein Temperaturausgleich stattfindet und dann• on a thin slab caster (d ≤ 120 mm), using suitable casting powders which reach equilibrium very quickly and then no longer change their lubricating behavior, potting and subdividing them into slabs, 0 immediately after the solidification and separation of a slab in one slab Intermediate furnace in the pass a temperature compensation takes place and then
• die Bramme ohne zwischenzeitliche Abkühlung direkt warmgewalzt wird.• The slab is directly hot rolled without intermediate cooling.
5 Eine Anlage zur Durchführung des Verfahrens ist durch die Merkmale des Anspruchs 7 gekennzeichnet.An installation for carrying out the method is characterized by the features of claim 7.
Bei der Herstellung von Dünnbrammen auf beispielsweise CSP-Gießmaschinen (CSP = Compact Strip Production) wird der Strang senkrecht ausgefördert, im 0 Anschluss an die Erstarrung in die Horizontale gebogen und anschließend in Brammen unterteilt. Deshalb können hier keine Probleme mit Innenrissen auftreten. Die Herstellung von hochfesten austenitischen Stählen ist ohne Anlagenüberlastung möglich und inzwischen Stand der Technik. Mikroseigerungen, die direkt nach der Erstarrung noch im Strang vorhanden sind, verschwinden wieder beim Durchlauf durch den Zwischenofen, beispielsweise durch einen Rollenherdofen, noch vor der nachfolgenden Walzumformung zu einem großen Teil durch Diffusion. Die Makroseigerungen in der Brammenmitte werden dabei ähnlich wie bei austenitischen Edelstahlen bei der starken Umformung im Warmwalzwerk ausreichend ausgeglichen.In the production of thin slabs on, for example, CSP casters (CSP = Compact Strip Production), the strand is conveyed vertically, bent in the 0 connection to the solidification in the horizontal and then divided into slabs. Therefore, there can be no problems with internal cracks here. The production of high-strength austenitic steels is possible without equipment overload and is now state of the art. Micro segregations, which are still present in the strand directly after solidification, disappear again during the passage through the intermediate furnace, for example through a roller hearth furnace, before the subsequent roll forming to a large extent by diffusion. The macrosegregations in the middle of the slab are, as with austenitic stainless steels, adequately compensated during the heavy forming in the hot rolling mill.
Mit Vorteil wird bei der erfindungsgemäßen Verwendung des Rollenherdofens einer CSP-Anlage wegen der kurzen Durchlaufzeiten eine stärkere Abreiche- rung der Legierungselemente bzw. die Oxidation der Korngrenzen vermieden, was beispielsweise bei den längeren Aufheizphasen im Stoßofen einer konventionellen Warmbreitbandstraße nach dem Stand der Technik zu Schwierigkeiten führen kann.Advantageously, in the inventive use of the roller hearth furnace of a CSP plant due to the short lead times greater depletion of the alloying elements or the oxidation of the grain boundaries avoided, which is difficult, for example, in the longer heating phases in the blast furnace of a conventional hot strip mill in the prior art can lead.
Um die Technik des Vergießens von TWIP- Leichtbaustählen mit hohem Mn- und AI-Gehalt auf einer Dünnbrammengießmaschine erfindungsgemäß nutzen zu können, ist die Verwendung eines geeigneten Gießpulvers erforderlich. Ein solches geeignetes Gießpulver weist entsprechend der Erfindung die Eigenschaft auf, sehr schnell ein Gleichgewicht zu erreichen und danach sein Schmierverhalten nicht mehr zu verändern.In order to be able to use the technique of potting TWIP lightweight construction steels with a high Mn and Al content on a thin slab casting machine according to the invention, the use of a suitable casting powder is required. Such a suitable casting powder according to the invention has the property of achieving equilibrium very quickly and then no longer changing its lubricating behavior.
Um beispielsweise die Reaktionsgeschwindigkeit der SiO2-Reduktion durch das AI des Stahls zu verkleinern, enthält das Gießpulver entsprechend der Erfindung einen erhöhten Anteil an AI2O3 von >10 %. Um im Gleichgewichtszustand mehr SiO2 zur Verfügung zu haben, ist alternativ oder zusätzlich der SiO2-Anteil des Gießpulvers erhöht, wobei diese Erhöhung bis zu einer Basizi- tät (Verhältnis CaOZSiO2) von 0,5 - 0,7 durchgeführt wird.For example, in order to reduce the reaction rate of the SiO 2 reduction by the Al of the steel, the casting powder according to the invention contains an increased proportion of Al 2 O 3 of> 10%. In order to have more SiO 2 available in the equilibrium state, the SiO 2 proportion of the casting powder is alternatively or additionally increased, this increase being carried out up to a basicity (ratio CaOZSiO 2 ) of 0.5-0.7.
Da MnO2 vom AI des Stahls leichter reduziert wird als SiO2 und dadurch das SiO2vor dieser Reduktion (vor Abbrand) geschützt wird, ist als weitere Maß- nähme der Erfindung ein Zusatz von MnO2 zum Gießpulver möglich. Auch ein teilweiser Ersatz des SiO2 durch TiO2, das wie SiO2 glasbildend wirkt, aber vom AI des Stahls nicht angegriffen (reduziert) wird, kann dem Gießpulver erfindungsgemäß zugemischt sein.Since MnO 2 is more easily reduced by the Al of the steel than SiO 2 and thereby the SiO 2 is protected from this reduction (from burnup), it is possible to add MnO 2 to the casting powder as a further measure of the invention. Even a partial replacement of the SiO 2 by TiO 2 , which acts like SiO 2 glass-forming, but is not attacked (reduced) by the Al of the steel, may be added to the casting powder according to the invention.
Schließlich besteht noch die Möglichkeit, die Viskosität des Gießpulvers in der Kokille zu erniedrigen. Hierdurch wird der Gießpulver-Verbrauch erhöht und mehr gebildetes AI2O3 abgeführt, so dass sich ein Gleichgewicht mit niedrigeren AI2O3-Gehalten einstellt. Erreicht wird diese Viskositätserniedrigung durch Zugabe von B2O3 (Borat), Na2O und/oder LiO2 zum Gießpulver.Finally, there is the possibility of lowering the viscosity of the casting powder in the mold. As a result, the consumption of casting powder is increased and more formed Al 2 O 3 dissipated, so that an equilibrium with lower Al 2 O 3 contents is established. This viscosity reduction is achieved by adding B 2 O 3 (borate), Na 2 O and / or LiO 2 to the casting powder.
Nachfolgend wird das in einer schematischen Zeichnungsfigur dargestellte Verfahrensschema einer erfindungsgemäßen Anlage zur Herstellung eines Warmbandes näher erläutert.The process schematic of a plant according to the invention for producing a hot strip, which is shown in a schematic drawing figure, is explained in greater detail below.
Im Prinzip handelt es sich bei der verwendeten Anlage um eine bekannte CSP- Anlage, bei der erfindungsgemäß die Abstände zwischen den einzelnen Anlagenteilen soweit verändert wurden, dass das Verfahren der Erfindung mit den Forderungen, direkt anschließend an die Erstarrung in einem Zwischenofen im Durchlauf einen Temperaturausgleich herbeizuführen und dann die Bramme ohne zwischenzeitliche Abkühlung direkt warmzuwalzen, durchführbar ist.In principle, the plant used is a known CSP plant in which, according to the invention, the distances between the individual plant components have been changed so far that the method of the invention with the requirements, directly after the solidification in an intermediate furnace in the course of a temperature compensation bring about and then hot roll the slab directly without interim cooling, is feasible.
Die in der Zeichnungsfigur dargestellte Anlage besteht demnach aus einer Dünnbrammengießmaschine 1 und einem nachgeordneten Zwischenofen 4, in den die vom Endlosstrang 2 nach seiner Erstarrung abgeteilte Bramme 3 eingeführt wird. Diesem Zwischenofen 4 wiederum ist ein Walzwerk 5 nachgeordnet, in dem die Bramme 3 nach erfolgtem Temperaturausgleich im Zwischenofen 4 direkt, d. h. ohne Zwischenkühlung zum Warmband 6 ausgewalzt wird. The plant shown in the drawing figure therefore consists of a thin slab caster 1 and a downstream intermediate furnace 4, in which the divided from the endless strand 2 after its solidification slab 3 is introduced. This intermediate furnace 4, in turn, a rolling mill 5 is arranged downstream, in which the slab 3 directly after temperature compensation in the intermediate furnace 4, d. H. without intermediate cooling to the hot strip 6 is rolled out.

Claims

Patentansprüche claims
1. Verfahren zur Herstellung eines Warmbandes (6) aus einem gut kaltum- formbaren, hochfesten, austenitischen Leichtbaustahl mit erhöhten Gehalten an Mangan (Mn), Aluminium (AI) und Silizium (Si) mit TWIP- Eigenschaften (Iwinning Jnduced Plasticity), wobei der Leichtbaustahl zunächst auf einer Stranggießanlage (1) zu einem Endlosstrang (2) vergossen, in Brammen (3) unterteilt und dann auf die Enddicke gewalzt wird, dadurch gekennzeichnet, dass durch hintereinander angeordnete Verfahrensschritte ein Leichtbau- stahl mit der vorgegebenen chemischen Zusammensetzung von 15 bis 271. A process for the production of a hot strip (6) from a good cold formable, high strength, austenitic lightweight steel with increased levels of manganese (Mn), aluminum (AI) and silicon (Si) with TWIP properties (Iwinning Jnduced Plasticity), wherein the lightweight steel is first cast on a continuous casting line (1) into an endless strand (2), subdivided into slabs (3) and then rolled to the final thickness, characterized in that a lightweight steel with the predetermined chemical composition of 15 to 27
% Mn, 1 bis 6 % AI, 1 bis 6 % Si, < 0,8 % C, Rest Fe und Begleitelemente% Mn, 1 to 6% Al, 1 to 6% Si, <0.8% C, remainder Fe and accompanying elements
• auf einer Dünnbrammengießmaschine (1 ) (d < 120 mm) unter Verwendung von Gießpulvern, die sehr schnell ein Gleichgewicht erreichen und anschließend ihr Schmierverhalten nicht mehr verän- dem, vergossen und in Brammen (3) unterteilt wird,On a thin-slab caster (1) (d <120 mm) using casting powders which reach equilibrium very quickly and then no longer change their lubricating behavior, potting and subdividing them into slabs (3),
• direkt anschließend an die Erstarrung und Abtrennung einer Bramme (3) in einem Zwischenofen (4) im Durchlauf ein Temperaturausgleich stattfindet und dann• immediately after the solidification and separation of a slab (3) in an intermediate furnace (4) takes place in the course of temperature compensation takes place and then
• die Bramme (3) ohne zwischenzeitliche Abkühlung direkt warm- gewalzt wird.• The slab (3) is rolled directly without intermediate cooling.
2. Verfahren nach Anspruch 1 , dadurch gekennzeichnet, dass das Gießpulver einen erhöhten AI2O3- Gehalt von > 10 % aufweist 5 3. Verfahren nach Anspruch 1 oder 2, dadurch gekennzeichnet, dass das Gießpulver einen erhöhten SiO2 - Gehalt mit einer Basizität (Verhältnis CaO/SiO2) zwischen 0,5 bis 0,7 aufweist.2. The method according to claim 1, characterized in that the casting powder has an increased Al2O3 content of> 10% 5 3. The method of claim 1 or 2, characterized in that the casting powder has an increased SiO 2 - content with a basicity (ratio CaO / SiO 2 ) between 0.5 to 0.7.
oO
4. Verfahren nach Anspruch 1 , 2 oder 3, dadurch gekennzeichnet, dass das Gießpulver MnO2 und/oder TiO2 enthält.4. The method according to claim 1, 2 or 3, characterized in that the casting powder contains MnO 2 and / or TiO 2 .
5. Verfahren nach Anspruch 1 , 2, 3 oder 4, L5 dadurch gekennzeichnet, dass zur Erniedrigung der Viskosität des Gießpulvers in der Kokille das Gießpulver Anteile an B2θ3 (Borat), Na2O und/oder LiO2 enthält.5. The method of claim 1, 2, 3 or 4, L5 characterized in that to lower the viscosity of the casting powder in the mold, the casting powder contains proportions of B 2 θ 3 (borate), Na 2 O and / or LiO 2 .
6. Verfahren nach einem oder mehreren der Ansprüche 1 bis 5, 0 dadurch gekennzeichnet, dass der Zwischenofen (4) ein Rollenherdofen ist.6. The method according to one or more of claims 1 to 5, 0, characterized in that the intermediate furnace (4) is a roller hearth furnace.
7. Anlage zur Herstellung eines Warmbandes aus einem gut kaltumformba- ren, hochfesten, austenitischen Leichtbaustahl mit erhöhten Gehalten an 5 Mangan (Mn), Aluminium (AI) und Silizium (Si) mit TWIP-Eigenschaften7. Plant for the production of a hot strip made of a cold-formable, high-strength, austenitic lightweight steel with increased contents of 5 manganese (Mn), aluminum (AI) and silicon (Si) with TWIP properties
(Twinning Jnduced Plasticity), zur Durchführung des Verfahrens nach einem oder mehreren der Ansprüche 1 bis 6, gekennzeichnet durch, die unmittelbar hintereinander angeordneten Anlagenteile Dünnbrammen- 0 gießmaschine (1 ), Zwischenofen (4), Warmwalzanlage (5). (Twinning Jnduced Plasticity), for carrying out the method according to one or more of claims 1 to 6, characterized by, immediately after one another arranged plant parts Dünnbrammen- 0 casting machine (1), intermediate furnace (4), hot rolling plant (5).
EP06723198A 2005-03-05 2006-03-03 Process for producing a lightweight structural steel with a high manganese content Active EP1725347B1 (en)

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