EP1918405B1 - Process for manufacturing steel flat products from silicon alloyed multi phase steel - Google Patents

Process for manufacturing steel flat products from silicon alloyed multi phase steel Download PDF

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Publication number
EP1918405B1
EP1918405B1 EP06123141A EP06123141A EP1918405B1 EP 1918405 B1 EP1918405 B1 EP 1918405B1 EP 06123141 A EP06123141 A EP 06123141A EP 06123141 A EP06123141 A EP 06123141A EP 1918405 B1 EP1918405 B1 EP 1918405B1
Authority
EP
European Patent Office
Prior art keywords
hot
rolled strip
strip
cold
rolled
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.)
Not-in-force
Application number
EP06123141A
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German (de)
French (fr)
Other versions
EP1918405A1 (en
Inventor
Brigitte Dr.-Ing. Hammer
Thomas Dr.-Ing. Heller
Johann Wilhelm Dr. Schmitz
Jochen Dr. Wans
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel AG
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Priority to EP06123141A priority Critical patent/EP1918405B1/en
Application filed by ThyssenKrupp Steel AG filed Critical ThyssenKrupp Steel AG
Priority to PL06123141T priority patent/PL1918405T3/en
Priority to AT06123141T priority patent/ATE432375T1/en
Priority to ES06123141T priority patent/ES2325964T3/en
Priority to DE502006003833T priority patent/DE502006003833D1/en
Priority to PCT/EP2007/061392 priority patent/WO2008052921A1/en
Priority to CN2007800400604A priority patent/CN101528968B/en
Priority to KR1020097007487A priority patent/KR101461585B1/en
Priority to JP2009533824A priority patent/JP5350255B2/en
Priority to US12/447,625 priority patent/US20100065161A1/en
Publication of EP1918405A1 publication Critical patent/EP1918405A1/en
Application granted granted Critical
Publication of EP1918405B1 publication Critical patent/EP1918405B1/en
Not-in-force legal-status Critical Current
Anticipated expiration legal-status Critical

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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
    • C21D8/04—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
    • 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
    • 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
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • 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
    • 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
    • C21D8/0421—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 characterised by the working steps
    • C21D8/0426—Hot 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
    • C21D8/04—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
    • C21D8/0421—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 characterised by the working steps
    • C21D8/0436—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
    • C21D8/04—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
    • C21D8/0447—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 characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • 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
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a method for producing flat steel products, such as strips or sheet metal blanks, from high-strength martensitic steels.
  • Such MS steels belong to the group of multiphase steels. These are usually steels whose properties are determined by the type, amount and arrangement of the phases of the structure. The structure therefore has at least two phases (eg ferrite, martensite, bainite). This gives them a strength / formability combination that is superior to conventional steels.
  • This preparation route presents problems in particular when casting peritectically solidifying compositions.
  • These steel grades there is the danger of the formation of longitudinal cracks during continuous casting.
  • the formation of such longitudinal cracks can reduce the quality of the hot strips produced from the cast slabs or thin slabs so much that they become unusable.
  • extensive measures such as increased insulation costs, are required, which can go so far that the processing of such steel grades becomes uneconomical.
  • multiphase steels are of particular interest for the automotive industry because of their high strength, they permit the use of lower material thicknesses and concomitantly a reduction in vehicle weight and, secondly, the safety of the vehicle body in the event of a collision (crash behavior) .
  • multiphase steels with at least constant strength of the overall body allow a reduction in the sheet thickness of a component produced from such multiphase steels compared to a body produced from conventional steels.
  • multiphase steels are melted in the converter steelworks and cast on a continuous casting plant into slabs or thin slabs, which are then hot rolled into hot strip and coiled.
  • the mechanical properties of the hot strip can be varied.
  • the hot strips can be cold rolled to cold strip to provide thinner sheet thicknesses ( EP 0 910 675 B1 . EP 0 966 547 B1 . EP 1 169 486 B1 . EP 1 319 725 B1 . EP 1 398 390 A1 ).
  • a problem in the production of flat products made of high-strength multiphase steels with tensile strengths of more than 800 MPa is that high rolling forces must be applied when rolling such steels.
  • high-strength hot strips made of steels of the type normally used in the currently available production plants are generally used Speech standing type often only in a width and thickness can be made available that are no longer fully meet the demands made in the field of automotive engineering today.
  • tapes of small thicknesses with sufficient widths can be poorly represented on conventional systems. It also turns out in conventional practice in practice difficult to produce multiphase steels cold strips with strengths of more than 800 MPa.
  • the cast strip is then hot rolled in-line in one or more passes of between 25% and 70% strain to a hot strip.
  • the final temperature of hot rolling is above the Ar 3 temperature.
  • the hot strip obtained is then cooled in two stages. In the first stage of this cooling, a cooling rate of 5 - 100 ° C / s is maintained until a temperature between 400 - 550 ° C is reached. At this temperature, the hot-rolled strip is left to rest for a period of time required to allow bainitic transformation of the steel with a residual austenite content greater than 5%.
  • the Perlite formation should be avoided.
  • the conversion process is stopped by the beginning of the second stage of cooling, in which the hot strip is brought to a temperature below 400 ° C, then at a lying below 350 ° C reel to a Wind coil.
  • the object of the invention was therefore to provide a method by means of which high-strength steel flat products can be produced over a wide range of geometric dimensions with reduced manufacturing outlay.
  • this object has been achieved by a method according to AI for producing steel flat products, in which a multi-phase structure forming steel, the (in wt .-%) 0.10 - 0.15% C , 0.80 - 1.20% Mn, up to 0.030% P, up to 0.004% S, 1.10 - 1.30% Si, 0.0 - 0.05% Al, up to 0.0060% N , 0.30-0.60% Cr, 0.080-0.120% Ti, 0.040-0.060% Nb, 0.150-0.250% Mo and balance iron and unavoidable impurities, to one cast strip with a thickness of 1 - 4 mm, in which the cast strip in a continuous operation with a degree of deformation of more than 20% in-line lying in the range of 850 - 1000 ° C hot rolling to a hot strip with a Hot rolled at a coil temperature of 450-700 ° C to obtain a hot strip whose tensile strength R m is at least 880 MP
  • the invention makes use of the possibility of strip casting to process a particularly high-strength, peritectically solidifying multiphase steel into a hot strip. Since the cast strip itself already has a small thickness, in the course of hot rolling of this strip only relatively low degrees of deformation must be maintained in order to produce flat products with small thicknesses, as are needed in particular in the automotive industry. Thus, by specifying a corresponding output thickness of the cast strip, it is easily possible to produce hot strips with the method according to the invention, which have a maximum property distribution of at most 1.5 mm and from which, for example, elements for the support structure of an automobile can be produced.
  • the invention makes it possible to manufacture high-strength hot strips consisting of a martensitic steel of the specified composition processed according to the invention, whose width is more than 1,200 mm, in particular more than 1,600 mm.
  • the use according to the invention of the strip casting method in the processing of high-strength steels of the type assembled according to the invention offers the possibility, in addition to the above-mentioned advantages due to its process-specific properties and manipulated variables (eg hot rolling end temperature, cooling, coiling temperature), of also critical steel compositions according to the invention with regard to their solidification behavior to safely shed processed species.
  • process-specific properties and manipulated variables eg hot rolling end temperature, cooling, coiling temperature
  • critical steel compositions according to the invention with regard to their solidification behavior to safely shed processed species.
  • the very rapid solidification of the cast strip which is characteristic of strip casting, leads to a significantly reduced risk of the formation of center segregations compared with conventional production, with the result that the hot strip produced according to the invention has a particularly uniform distribution of properties and microstructure over its cross section and its length.
  • the hot strip produced according to the invention has high strengths of at least 880 MPa, without having to observe a special cooling cycle of the hot strip between the end of the hot rolling and the reeling, as described in US Pat EP 1 072 689 B1 is prescribed by the need for a cooling break.
  • the method according to the invention merely has to ensure that the hot rolling ends in a relatively narrow temperature window and that the reeling is also carried out in a precisely defined temperature range. In between there is a one-stage cooling down.
  • a further advantage of the procedure according to the invention is that an extension of the range of mechanical properties of the strip produced according to the invention based on only one steel analysis can be achieved by varying the cooling and rolling conditions.
  • Hot strips produced according to the invention are particularly suitable for further processing into cold rolled strip. Accordingly, a practice-oriented embodiment of the invention provides that the hot strip is cold rolled to a cold strip having a thickness of 0.5-1.4 mm, in particular 0.7 mm to 1.3 mm, as is required for the construction of automobile bodies.
  • the cold strip can be annealed at an annealing temperature of 750-850 ° C.
  • tensile strengths of at least 800 MPa can be reliably ensured.
  • the breaking elongation A 50 of the cold strip is just as safe at least 5%.
  • elongation at break values for which a tensile strength of at least 800 MPa can still be guaranteed, can be reliably produced by limiting the annealing temperatures to a range of 810-850 ° C.
  • the cold strip is provided in a conventional manner with a metallic coating, which may be, for example, a galvanizing.
  • the strength and elongation values according to the invention produced hot strips can be adjusted over a wide range by an appropriate vote of the Hotwalzend- and reel temperatures. If, for example, hot strips are to be produced which have a tensile strength R m of at least 880 MPa at an elongation at break A 80 of the resulting hot strip of at least 10%, this can be achieved by setting the hot rolling end temperature in the range from 850 to 1000 ° C. and the coiler temperature be varied in the range of 550 - 700 ° C.
  • the hot rolling end temperature in the range of 900-1000 ° C and the coiling temperature in the range of 450-550 ° C selected.
  • the cast strip was hot-rolled immediately after in-line strip casting at a hot rolling end temperature WET to a hot strip whose thickness was 1.25 mm. Subsequently, each hot strip obtained has been cooled directly in a cooling step to a coiler temperature HT and coiled. After coiling, the hot rolled strip obtained had a tensile strength R m and an elongation at break A 80 , which, like the hot rolling end temperature WET and reel temperature HT observed in its manufacture, are given in Table 2.
  • Table 2 WET [° C] HT [° C] R m [MPa]
  • the hot strip produced in this way has been cold rolled to a 0.7 mm thick cold strip after unreeling and pickling.
  • Such a cold strip A was annealed at a temperature of 840 ° C to recrystallize the strip.
  • Another cold strip B was recrystallized annealed at a temperature of 800 ° C. This cold-rolled strip B had an elongation at break A 50 of 8.6% and a tensile strength R m of 1003 Mpa.

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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)
  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
  • Coating With Molten Metal (AREA)
  • Chemical Vapour Deposition (AREA)

Abstract

The method for the production of flat steel products useful for automotive industry, comprises casting a steel into a cast strip having a thickness of 1-4 mm, hot-rolling the cast strip in-line into a hot-rolled strip having a thickness of greater than 1.5 mm in a continuous process at a final hot-rolling temperature at 850-1000[deg] C, and coiling the hot-rolled strip at a coiling temperature of 450-700[deg] C to obtain a hot-rolled strip, which has a minimum tensile strength R m of 880 MPa and a minimum breaking elongation A 8 0 of 5%. The steel forms a complex phase structure. The method for the production of flat steel products useful for automotive industry, comprises casting a steel into a cast strip having a thickness of 1-4 mm, hot-rolling the cast strip in-line into a hot-rolled strip having a thickness of greater than 1.5 mm in a continuous process at a final hot-rolling temperature at 850-1000[deg] C, and coiling the hot-rolled strip at a coiling temperature of 450-700[deg] C to obtain a hot-rolled strip, which has a minimum tensile strength R m of 880 MPa and a minimum breaking elongation A 8 0 of 5%. The steel forms a complex phase structure. The shaping degree is greater than 20%. The width of the hot-rolled strip is more than 1.600 mm. The hot-rolled strip is cold-rolled with a thickness of 0.5-1.4 mm at 750-805[deg] C to obtain a cold-rolled strip, which has a minimum tensile strength of more than 800 MPa and a minimum breaking elongation A 5 0 of 5%. The coiling temperature of the cold-rolled strip is 810-850[deg] C. The cold- or hot-rolled strip is provided with a metallic coating, which is galvanizing. The coiling temperature is 550-700[deg] C, when a minimum breaking elongation A 8 0 of the obtained hot-rolled strip is 10%. The hot-rolled temperature is 900-1000[deg] C and the coiling temperature is 450-550[deg] C, when a minimum tensile strength R m of the obtained hot-rolled strip is 1000 MPa.

Description

Die Erfindung betrifft ein Verfahren zur Herstellung von Stahl-Flachprodukten, wie Bändern oder Blechzuschnitten, aus hochfesten martensitischen Stählen. Derartige MS-Stähle gehören zur Gruppe der Mehrphasenstähle. Bei diesen handelt es sich üblicherweise um Stähle, deren Eigenschaften durch Art, Menge und Anordnung der Phasen des Gefüges bestimmt werden. Im Gefüge liegen daher mindestens zwei Phasen vor (z. B. Ferrit, Martensit, Bainit). Dadurch haben sie eine gegenüber konventionellen Stählen überlegene Festigkeits-/ Umformbarkeitskombination.The invention relates to a method for producing flat steel products, such as strips or sheet metal blanks, from high-strength martensitic steels. Such MS steels belong to the group of multiphase steels. These are usually steels whose properties are determined by the type, amount and arrangement of the phases of the structure. The structure therefore has at least two phases (eg ferrite, martensite, bainite). This gives them a strength / formability combination that is superior to conventional steels.

Probleme bereitet diese Herstellungsroute insbesondere beim Vergießen von peritektisch erstarrenden Zusammensetzungen. Bei diesen Stahlgüten besteht die Gefahr der Bildung von Längsrissen beim Stranggießen. Die Entstehung von derartigen Längsrissen kann die Qualität der aus den gegossenen Brammen bzw. Dünnbrammen erzeugten Warmbänder so stark herabsetzen, dass sie unbrauchbar werden. Um dieser Gefahr vorzubeugen, sind umfangreiche Maßnahmen, wie ein erhöhter Flämmaufwand, erforderlich, der so weit gehen kann, dass die Verarbeitung derartiger Stahlgüten unwirtschaftlich wird. Beim Vergießen von Stählen mit hohen Al-Gehalten kommt es darüber hinaus zu unerwünschten Wechselwirkungen mit dem Gießpulver, durch die die Qualität eines aus diesen Stählen gefertigten Flachprodukts ebenfalls negativ beeinflusst wird.This preparation route presents problems in particular when casting peritectically solidifying compositions. With these steel grades there is the danger of the formation of longitudinal cracks during continuous casting. The formation of such longitudinal cracks can reduce the quality of the hot strips produced from the cast slabs or thin slabs so much that they become unusable. In order to prevent this danger, extensive measures, such as increased insulation costs, are required, which can go so far that the processing of such steel grades becomes uneconomical. When casting steels with high Al contents, there are also undesirable interactions with the casting powder, which also adversely affect the quality of a flat product made from these steels.

Aufgrund dieser Besonderheiten sind Mehrphasenstähle insbesondere für den Automobilbau von großem Interesse, da sie aufgrund ihrer hohen Festigkeit zum einen die Verwendung geringerer Materialstärken und damit einhergehend eine Reduzierung des Fahrzeuggewichts erlauben und zum anderen die Sicherheit der Fahrzeugkarosserie im Fall eines Zusammenstoßes (Crash-Verhalten) verbessern. So ermöglichen Mehrphasenstähle bei mindestens gleich bleibender Festigkeit der Gesamtkarosse eine Reduzierung der Blechdicke eines aus solchen Mehrphasenstählen hergestellten Bauteils gegenüber einer aus konventionellen Stählen hergestellten Karosserie.Because of these peculiarities, multiphase steels are of particular interest for the automotive industry because of their high strength, they permit the use of lower material thicknesses and concomitantly a reduction in vehicle weight and, secondly, the safety of the vehicle body in the event of a collision (crash behavior) , Thus, multiphase steels with at least constant strength of the overall body allow a reduction in the sheet thickness of a component produced from such multiphase steels compared to a body produced from conventional steels.

Üblicherweise werden Mehrphasenstähle im Konverterstahlwerk erschmolzen und auf einer Stranggießanlage zu Brammen oder Dünnbrammen vergossen, die dann zu Warmband warmgewalzt und gehaspelt werden. Durch eine gezielt gesteuerte Abkühlung des Warmbands nach dem Warmwalzen mit dem Ziel einer Einstellung bestimmter Gefügeanteile können dabei die mechanischen Eigenschaften des Warmbandes variiert werden. Die Warmbänder können darüber hinaus zu Kaltband kaltgewalzt werden, um auch dünnere Blechdicken zur Verfügung zu stellen ( EP 0 910 675 B1 , EP 0 966 547 B1 , EP 1 169 486 B1 , EP 1 319 725 B1 , EP 1 398 390 A1 ).Usually, multiphase steels are melted in the converter steelworks and cast on a continuous casting plant into slabs or thin slabs, which are then hot rolled into hot strip and coiled. By a controlled controlled cooling of the hot strip after hot rolling with the aim of adjusting certain microstructures, the mechanical properties of the hot strip can be varied. In addition, the hot strips can be cold rolled to cold strip to provide thinner sheet thicknesses ( EP 0 910 675 B1 . EP 0 966 547 B1 . EP 1 169 486 B1 . EP 1 319 725 B1 . EP 1 398 390 A1 ).

Ein Problem bei der Fertigung von Flachprodukten aus hochfesten Mehrphasenstählen mit Zugfestigkeiten von mehr als 800 MPa besteht darin, dass beim Walzen derartiger Stähle hohe Walzkräfte aufgebracht werden müssen. Diese Anforderung hat zur Folge, dass in der Regel mit den derzeit üblicherweise zur Verfügung stehenden Fertigungsanlagen hochfeste Warmbänder aus Stählen der in Rede stehenden Art vielfach nur in einer Breite und Dicke zur Verfügung gestellt werden können, die den heute im Bereich des Automobilbaus gestellten Anforderungen nicht mehr in vollem Umfang gerecht werden. Vor allem Bänder geringer Dicken bei ausreichenden Breiten lassen sich auf konventionellen Anlagen schlecht darstellen. Auch erweist es sich bei konventioneller Vorgehensweise in der Praxis als schwierig, aus Mehrphasenstählen Kaltbänder mit Festigkeiten von mehr als 800 MPa herzustellen.A problem in the production of flat products made of high-strength multiphase steels with tensile strengths of more than 800 MPa is that high rolling forces must be applied when rolling such steels. As a consequence of this requirement, high-strength hot strips made of steels of the type normally used in the currently available production plants are generally used Speech standing type often only in a width and thickness can be made available that are no longer fully meet the demands made in the field of automotive engineering today. Above all, tapes of small thicknesses with sufficient widths can be poorly represented on conventional systems. It also turns out in conventional practice in practice difficult to produce multiphase steels cold strips with strengths of more than 800 MPa.

Ein alternativer Weg der Herstellung von Stahlbändern aus einem Mehrphasenstahl ist in der EP 1 072 689 B1 ( DE 600 09 611 T2 ) vorgeschlagen worden. Gemäß diesem bekannten Verfahren wird zur Herstellung von dünnen Stahlbändern zunächst eine Stahlschmelze, die (in Gew.-%) 0,05 und 0,25 % C, in Summe 0,5 - 3 % Mn, Cu und Ni, in Summe 0,1 - 4 % Si und Al, in Summe bis zu 0,1 % P, Sn, As und Sb, in Summe weniger als 0,3 % Ti, Nb, V, Zr und REM sowie jeweils weniger als 1 % Cr, Mo und V, Rest Eisen und unvermeidbare Verunreinigungen enthält, zu einem gegossenen Band mit einer Dicke von 0,5 - 10 mm, insbesondere 1 - 5 mm, vergossen. Das gegossene Band wird anschließend in-Line in ein oder mehreren Stichen mit einem zwischen 25 % und 70 % liegenden Umformgrad zu einem Warmband warmgewalzt. Die Endtemperatur des Warmwalzens liegt dabei oberhalb der Ar3-Temperatur. Nach dem Ende des Warmwalzens wird das erhaltene Warmband dann zweistufig abgekühlt. In der ersten Stufe dieser Abkühlung wird eine Abkühlgeschwindigkeit von 5 - 100 °C/s eingehalten, bis eine zwischen 400 - 550 °C liegende Temperatur erreicht ist. Bei dieser Temperatur lässt man dann das Warmband für eine Pausenzeit verweilen, die benötigt wird, um eine bainitische Umwandlung des Stahls mit einem Restaustenitanteil von mehr als 5 % zu ermöglichen. Die Bildung von Perlit soll dabei vermieden werden. Nach einer für die Einstellung der geforderten Gefügestruktur ausreichenden Pausenzeit wird der Umwandlungsvorgang durch den Beginn der zweiten Stufe der Abkühlung abgebrochen, bei der das Warmband auf eine Temperatur unter 400 °C gebracht wird, um es anschließend bei einer unter 350 °C liegenden Haspeltemperatur zu einem Coil zu wickeln.An alternative way of producing steel strip from a multiphase steel is in the EP 1 072 689 B1 ( DE 600 09 611 T2 ) has been proposed. According to this known method, for the production of thin steel strips, first of all a molten steel containing (in% by weight) 0.05 and 0.25% C, in total 0.5-3% Mn, Cu and Ni, in total 0, 1 to 4% Si and Al, in total up to 0.1% P, Sn, As and Sb, in total less than 0.3% Ti, Nb, V, Zr and REM and in each case less than 1% Cr, Mo and V, balance iron and unavoidable impurities, cast into a cast strip having a thickness of 0.5 - 10 mm, especially 1 - 5 mm. The cast strip is then hot rolled in-line in one or more passes of between 25% and 70% strain to a hot strip. The final temperature of hot rolling is above the Ar 3 temperature. After the end of the hot rolling, the hot strip obtained is then cooled in two stages. In the first stage of this cooling, a cooling rate of 5 - 100 ° C / s is maintained until a temperature between 400 - 550 ° C is reached. At this temperature, the hot-rolled strip is left to rest for a period of time required to allow bainitic transformation of the steel with a residual austenite content greater than 5%. The Perlite formation should be avoided. After a sufficient for the adjustment of the required microstructure pause time, the conversion process is stopped by the beginning of the second stage of cooling, in which the hot strip is brought to a temperature below 400 ° C, then at a lying below 350 ° C reel to a Wind coil.

Mit der in der EP 1 072 689 B1 beschriebenen Vorgehensweise soll eine einfache Herstellung von Warmband mit bainitischen Gefügeanteilen aus einem Mehrphasenstahl möglich sein, das TRIP-Eigenschaften ("TRIP" = "Transformation Induced Plasticity") aufweist. Derartige Stähle weisen relativ hohe Festigkeiten bei guter Verformbarkeit auf. Allerdings reichen die Festigkeiten für viele Anwendungsfälle insbesondere im Bereich des Automobilbaus nicht aus.With the in the EP 1 072 689 B1 described procedure is a simple production of hot strip with bainitic microstructural parts of a multi-phase steel is possible, the TRIP properties ("TRIP =" T ransformation I nduced P lasticity ") has. Such steels have relatively high strengths with good ductility. However, the strength is not sufficient for many applications, especially in the field of automotive engineering.

Die Aufgabe der Erfindung bestand daher darin, ein Verfahren zur Verfügung zu stellen, mit dem sich hochfeste Stahl-Flachprodukte über eine große Bandbreite von geometrischen Abmessungen bei vermindertem Herstellaufwand erzeugen lassen.The object of the invention was therefore to provide a method by means of which high-strength steel flat products can be produced over a wide range of geometric dimensions with reduced manufacturing outlay.

Ausgehend von dem voranstehend erläuterten Stand der Technik ist diese Aufgabe durch ein Verfahren gemäß A.I zum Herstellen von Stahl-Flachprodukten gelöst worden, bei dem ein ein Mehrphasengefüge bildender Stahl, der (in Gew.-%) 0,10 - 0,15 % C, 0,80 - 1,20 % Mn, bis zu 0,030 % P, bis zu 0,004 % S, 1,10 - 1,30 % Si, 0,0 - 0,05 % Al, bis zu 0,0060 % N, 0,30 - 0,60 % Cr, 0,080 - 0,120 % Ti, 0,040 - 0,060 % Nb, 0,150 - 0,250 % Mo und als Rest Eisen und unvermeidbare Verunreinigungen enthält, zu einem gegossenen Band mit einer Dicke von 1 - 4 mm vergossen wird, bei dem das gegossene Band in einem kontinuierlichen Arbeitsablauf mit einem Umformgrad von mehr als 20 % in-Line bei einer im Bereich von 850 - 1000 °C liegenden Warmwalzendtemperatur zu einem Warmband mit einer Dicke von 0,5 - 3,2 mm warmgewalzt wird und bei dem das Warmband bei einer 450 - 700 °C betragenden Haspeltemperatur gehaspelt wird, so dass ein Warmband erhalten wird, dessen Zugfestigkeit Rm mindestens 880 MPa bei einer Bruchdehnung A80 von mindestens 5 % beträgt.Based on the above-described prior art, this object has been achieved by a method according to AI for producing steel flat products, in which a multi-phase structure forming steel, the (in wt .-%) 0.10 - 0.15% C , 0.80 - 1.20% Mn, up to 0.030% P, up to 0.004% S, 1.10 - 1.30% Si, 0.0 - 0.05% Al, up to 0.0060% N , 0.30-0.60% Cr, 0.080-0.120% Ti, 0.040-0.060% Nb, 0.150-0.250% Mo and balance iron and unavoidable impurities, to one cast strip with a thickness of 1 - 4 mm, in which the cast strip in a continuous operation with a degree of deformation of more than 20% in-line lying in the range of 850 - 1000 ° C hot rolling to a hot strip with a Hot rolled at a coil temperature of 450-700 ° C to obtain a hot strip whose tensile strength R m is at least 880 MPa with an ultimate elongation A 80 of at least 5%.

Die Erfindung nutzt die Möglichkeit des Bandgießens dazu, einen besonders hochfesten, peritektisch erstarrenden Mehrphasenstahl zu einem Warmband zu verarbeiten. Da das gegossene Band dabei selbst schon eine geringe Dicke besitzt, müssen im Zuge des Warmwalzens dieses Bandes nur relativ geringe Umformgrade eingehalten werden, um Flachprodukte mit geringen Dicken zu erzeugen, wie sie insbesondere im Bereich der Automobilindustrie benötigt werden. So ist es durch Vorgabe einer entsprechenden Ausgangsdicke des gegossenen Bandes problemlos möglich, mit dem erfindungsgemäßen Verfahren Warmbänder herzustellen, die bei einer optimalen Eigenschaftsverteilung eine Dicke von höchstens 1,5 mm aufweisen und aus denen sich beispielsweise Elemente für die Tragstruktur eines Automobils fertigen lassen.The invention makes use of the possibility of strip casting to process a particularly high-strength, peritectically solidifying multiphase steel into a hot strip. Since the cast strip itself already has a small thickness, in the course of hot rolling of this strip only relatively low degrees of deformation must be maintained in order to produce flat products with small thicknesses, as are needed in particular in the automotive industry. Thus, by specifying a corresponding output thickness of the cast strip, it is easily possible to produce hot strips with the method according to the invention, which have a maximum property distribution of at most 1.5 mm and from which, for example, elements for the support structure of an automobile can be produced.

Aufgrund der geringen Umformgrade während des Warmwalzens sind die dazu erforderlichen Walzkräfte verglichen mit den beim Warmwalzen von Brammen oder Dünnbrammen bei der konventionellen Vorgehensweise erforderlichen Kräften gering, so dass mit dem erfindungsgemäßen Verfahren problemlos Warmbänder von großer Breite erzeugt werden können, die deutlich über der Breite von in konventioneller Weise erzeugbaren Warmbändern derselben Festigkeits- und Dickenklasse liegen. So erlaubt es die Erfindung, hochfeste, aus einem martensitischen Stahl der angegebenen erfindungsgemäß verarbeiteten Zusammensetzung bestehende Warmbänder sicher zu fertigen, deren Breite mehr als 1.200 mm, insbesondere mehr als 1.600 mm beträgt.Due to the low degrees of deformation during hot rolling, the required rolling forces are low compared to the forces required in the hot rolling of slabs or thin slabs in the conventional approach, so that can be easily produced by the inventive method hot strips of large width, well above the width of in conventionally producible hot strips of the same strength and thickness class. Thus, the invention makes it possible to manufacture high-strength hot strips consisting of a martensitic steel of the specified composition processed according to the invention, whose width is more than 1,200 mm, in particular more than 1,600 mm.

Die erfindungsgemäße Anwendung des Bandgießverfahrens bei der Verarbeitung von hochfesten Stählen der erfindungsgemäß zusammengesetzten Art bietet neben den voranstehend genannten Vorteilen auf Grund seiner verfahrensspezifischen Eigenschaften und Stellgrößen (z. B. Warmwalzendtemperatur, Abkühlung, Haspeltemperatur) die Möglichkeit, auch hinsichtlich ihres Erstarrungsverhaltens kritische Stahlzusammensetzungen der erfindungsgemäß verarbeiteten Art sicher zu vergießen. So führt die für das Bandgießen charakteristische sehr rasche Erstarrung des gegossenen Bandes zu gegenüber einer konventionellen Fertigung deutlich verminderten Gefahr der Entstehung von Mittenseigerungen mit der Folge, dass das erfindungsgemäß erzeugte Warmband über seinen Querschnitt und seine Länge eine besonders gleichmäßige Eigenschaftsverteilung und Gefügestruktur aufweist.The use according to the invention of the strip casting method in the processing of high-strength steels of the type assembled according to the invention offers the possibility, in addition to the above-mentioned advantages due to its process-specific properties and manipulated variables (eg hot rolling end temperature, cooling, coiling temperature), of also critical steel compositions according to the invention with regard to their solidification behavior to safely shed processed species. Thus, the very rapid solidification of the cast strip, which is characteristic of strip casting, leads to a significantly reduced risk of the formation of center segregations compared with conventional production, with the result that the hot strip produced according to the invention has a particularly uniform distribution of properties and microstructure over its cross section and its length.

Ein weiterer besonderer Vorteil der erfindungsgemäßen Vorgehensweise besteht darin, dass erfindungsgemäß erzeugtes Warmband hohe Festigkeiten von mindestens 880 MPa aufweist, ohne dass dazu ein besonderer Abkühlzyklus des Warmbands zwischen dem Ende des Warmwalzens und des Haspelns eingehalten werden muss, wie dies in der EP 1 072 689 B1 durch die Notwendigkeit einer Kühlpause vorgeschrieben ist. Bei der Durchführung des erfindungsgemäßen Verfahrens muss lediglich sichergestellt sein, dass das Warmwalzen in einem relativ eng umgrenzten Temperaturfenster beendet und auch das Haspeln in einem exakt definierten Temperaturbereich durchgeführt wird. Dazwischen findet eine einstufige Abkühlung statt.Another particular advantage of the procedure according to the invention is that the hot strip produced according to the invention has high strengths of at least 880 MPa, without having to observe a special cooling cycle of the hot strip between the end of the hot rolling and the reeling, as described in US Pat EP 1 072 689 B1 is prescribed by the need for a cooling break. In carrying out the The method according to the invention merely has to ensure that the hot rolling ends in a relatively narrow temperature window and that the reeling is also carried out in a precisely defined temperature range. In between there is a one-stage cooling down.

Ein weiterer Vorteil der erfindungsgemäßen Vorgehensweise besteht darin, dass eine Erweiterung der Spannbreite der mechanischen Eigenschaften des erfindungsgemäß erzeugten Bandes basierend auf nur einer Stahlanalyse durch eine Variation der Abkühl- und Walzbedingungen erreicht werden kann.A further advantage of the procedure according to the invention is that an extension of the range of mechanical properties of the strip produced according to the invention based on only one steel analysis can be achieved by varying the cooling and rolling conditions.

Erfindungsgemäß erzeugte Warmbänder eignen sich besonders zur Weiterverarbeitung zu kaltgewalztem Band. Dementsprechend sieht eine praxisgerechte Ausgestaltung der Erfindung vor, dass das Warmband zu einem Kaltband mit einer Dicke von 0,5 - 1,4 mm, insbesondere 0,7 mm bis 1,3 mm kaltgewalzt wird, wie es zum Bau von Automobilkarosserien benötigt wird. Um während des Kaltwalzens entstehende Verfestigungen zu beseitigen, kann das Kaltband bei einer Glühtemperatur von 750 - 850 °C geglüht werden. Für auf diese Weise aus dem erfindungsgemäß hergestellten Warmband erzeugtes Kaltband können Zugfestigkeiten von mindestens 800 MPa sicher gewährleistet werden. Die Bruchdehnung A50 des Kaltbands beträgt dabei ebenso sicher mindestens 5 %. Indem dabei die Glühtemperaturen auf einen Bereich von 750 - 805 °C beschränkt werden, lassen sich Kaltbänder mit Zugfestigkeiten von mindestens 1000 MPa erzeugen. Trotz dieser hohen Festigkeiten kann für derart geglühte Bänder immer noch eine Bruchdehnung A50 von mindestens 5 % gewährleistet werden. Kaltbänder mit verbesserten Bruchdehnungswerten, für die immer noch eine Zugfestigkeit von mindestens 800 MPa gewährleistet werden kann, lassen sich dagegen auf sichere Weise dadurch erzeugen, dass die Glühtemperaturen auf einen Bereich von 810 - 850 °C beschränkt werden.Hot strips produced according to the invention are particularly suitable for further processing into cold rolled strip. Accordingly, a practice-oriented embodiment of the invention provides that the hot strip is cold rolled to a cold strip having a thickness of 0.5-1.4 mm, in particular 0.7 mm to 1.3 mm, as is required for the construction of automobile bodies. In order to eliminate solidification during cold rolling, the cold strip can be annealed at an annealing temperature of 750-850 ° C. For cold rolled strip produced in this way from the hot strip produced according to the invention, tensile strengths of at least 800 MPa can be reliably ensured. The breaking elongation A 50 of the cold strip is just as safe at least 5%. By limiting the annealing temperatures to a range of 750 - 805 ° C, cold strips with tensile strengths of at least 1000 MPa can be produced. Despite these high strengths, an elongation at break A 50 of at least 5% can still be ensured for such annealed strips. Cold tapes with improved On the other hand, elongation at break values, for which a tensile strength of at least 800 MPa can still be guaranteed, can be reliably produced by limiting the annealing temperatures to a range of 810-850 ° C.

Gemäß einer weiteren vorteilhaften Ausgestaltung der Erfindung wird das Kaltband in an sich bekannter Weise mit einer metallischen Beschichtung versehen, bei der es sich beispielsweise um eine Verzinkung handeln kann.According to a further advantageous embodiment of the invention, the cold strip is provided in a conventional manner with a metallic coating, which may be, for example, a galvanizing.

Die Festigkeits- und Dehnwerte erfindungsgemäß erzeugter Warmbänder können über eine große Bandbreite durch eine entsprechende Abstimmung der Warmwalzend- und Haspeltemperaturen eingestellt werden. Sollen beispielsweise Warmbänder erzeugt werden, die bei einer Bruchdehnung A80 des erhaltenen Warmbands von mindestens 10 % eine Zugfestigkeit Rm von mindestens 880 MPa aufweisen, so kann dies dadurch erreicht werden, dass die Warmwalzendtemperatur im Bereich von 850 - 1000 °C und die Haspeltemperatur im Bereich von 550 - 700 °C variiert werden. Soll dagegen ein Warmband mit garantiert höherer Zugfestigkeit Rm von mindestens 1000 MPa bei einer Bruchdehnung A80 von mindestens 5 % erzeugt werden, so werden dazu die Warmwalzendtemperatur im Bereich von 900 - 1000 °C und die Haspeltemperatur im Bereich von 450 - 550 °C gewählt.The strength and elongation values according to the invention produced hot strips can be adjusted over a wide range by an appropriate vote of the Hotwalzend- and reel temperatures. If, for example, hot strips are to be produced which have a tensile strength R m of at least 880 MPa at an elongation at break A 80 of the resulting hot strip of at least 10%, this can be achieved by setting the hot rolling end temperature in the range from 850 to 1000 ° C. and the coiler temperature be varied in the range of 550 - 700 ° C. If, on the other hand, a hot strip with guaranteed higher tensile strength R m of at least 1000 MPa is produced at an elongation at break A 80 of at least 5%, then the hot rolling end temperature in the range of 900-1000 ° C and the coiling temperature in the range of 450-550 ° C selected.

Nachfolgend wird die Erfindung anhand von Ausführungsbeispielen näher erläutert.The invention will be explained in more detail by means of exemplary embodiments.

In einem zum Nachweis der Wirkung der Erfindung durchgeführten Versuch ist ein erfindungsgemäß zusammengesetzter Stahl mit der in Tabelle 1 angegebenen Zusammensetzung erschmolzen und in einer konventionellen Zweiwalzengieß-Maschine zu gegossenem Band vergossen worden, das 1,6 mm dick war. Tabelle 1 (Angaben in Gew.-%) C Mn P S Si Al N Cr Ti Nb Mo 0,11 1,09 0,006 0,004 1,17 0,013 0,0054 0,44 0,112 0,057 0,200 In an experiment carried out to demonstrate the effect of the invention, a composite steel according to the invention having the composition given in Table 1 was melted and cast in a conventional two-roll casting machine into cast strip 1.6 mm thick. Table 1 (in% by weight) C Mn P S Si al N Cr Ti Nb Not a word 0.11 1.09 0,006 0,004 1.17 0,013 0.0054 0.44 0.112 0.057 0,200

Das gegossene Band ist im unmittelbaren Anschluss an das Bandgießen in-Line bei einer Warmwalzendtemperatur WET zu einem Warmband warmgewalzt worden, dessen Dicke 1,25 mm betrug. Anschließend ist das jeweils erhaltene Warmband direkt in einem Kühlschritt auf eine Haspeltemperatur HT abgekühlt und gehaspelt worden. Nach dem Haspeln wies das erhaltene Warmband eine Zugfestigkeit Rm und eine Bruchdehnung A80 auf, die wie die bei ihrer Herstellung eingehaltene Warmwalzendtemperatur WET und Haspeltemperatur HT in Tabelle 2 angegeben sind. Tabelle 2 WET [°C] HT [°C] Rm [MPa] A80 [%] 880 640 895 13,1 The cast strip was hot-rolled immediately after in-line strip casting at a hot rolling end temperature WET to a hot strip whose thickness was 1.25 mm. Subsequently, each hot strip obtained has been cooled directly in a cooling step to a coiler temperature HT and coiled. After coiling, the hot rolled strip obtained had a tensile strength R m and an elongation at break A 80 , which, like the hot rolling end temperature WET and reel temperature HT observed in its manufacture, are given in Table 2. Table 2 WET [° C] HT [° C] R m [MPa] A 80 [%] 880 640 895 13.1

Das so erzeugte Warmband ist nach dem Haspeln und Beizen zu einem 0,7 mm dicken Kaltband kaltgewalzt worden.The hot strip produced in this way has been cold rolled to a 0.7 mm thick cold strip after unreeling and pickling.

Ein solches Kaltband A wurde bei einer Temperatur von 840 °C geglüht, um das Band zu rekristallisieren. Dieses Kaltband A wies bei einer Bruchdehnung von A50 = 12,7 % eine Zugfestigkeit Rm von 851 MPa auf.Such a cold strip A was annealed at a temperature of 840 ° C to recrystallize the strip. This cold-rolled strip A had a tensile strength R m of 851 MPa at an elongation at break of A 50 = 12.7%.

Ein weiteres Kaltband B wurde bei einer Temperatur von 800 °C rekristallisierend geglüht. Dieses Kaltband B hatte eine Bruchdehnung A50 von 8,6 % und eine Zugfestigkeit Rm von 1003 Mpa.Another cold strip B was recrystallized annealed at a temperature of 800 ° C. This cold-rolled strip B had an elongation at break A 50 of 8.6% and a tensile strength R m of 1003 Mpa.

Claims (14)

  1. Method for manufacturing flat steel products,
    - wherein a steel that forms a multi-phase microstructure with the following composition (in wt. %) C: 0.10 - 0.15 % Mn: 0.80 - 1.20 % P: ≤ 0.030 % S: ≤ 0.004 % Si: 1.10 - 1.30 % Al: 0.0 - 0.05 % N: ≤ 0.0060% Cr: 0.30 - 0.60 % Ti: 0.080 - 0.120 % Nb: 0.040 - 0.060 % Mo: 0.150 - 0.250 %
    remainder iron and unavoidable impurities
    is cast into a cast strip having a thickness of 1 - 4 mm,
    - wherein the cast strip is hot-rolled in-line into a hot-rolled strip having a thickness ranging from 0.5 to 3.2 mm in a continuous process at a final hot-rolling temperature ranging from 850 to 1000 °C, the deformation degree being greater than 20 %, cooled in one step and
    - wherein the hot-rolled strip is coiled at a coiling temperature ranging from 450 to 700 °C,
    - so as to obtain a hot-rolled strip, which has a minimum tensile strength Rm of 880 MPa at a minimum breaking elongation A80 of 5 %.
  2. Method according to Claim 1, characterized in that the width of the hot-rolled strip is greater than 1,200 mm, in particular greater than 1,600 mm.
  3. Method according to any one of the preceding claims, characterized in that the thickness of the hot-rolled strip is 1.5 mm at most.
  4. Method according to any one of the preceding claims, characterized in that the hot-rolled strip is cold-rolled into cold-rolled strip having a thickness of 0.5 - 1.4 mm.
  5. Method according to Claim 4, characterized in that the cold-rolled strip is annealed at an annealing temperature of 750 - 805 °C.
  6. Method according to Claim 4 or 5, characterized in that the minimum tensile strength of the cold-rolled strip is 1000 MPa.
  7. Method according to any one of Claims 4 to 6, characterized in that the cold-rolled strip has a minimum breaking elongation A50 of 5 %.
  8. Method according to Claim 4, characterized in that the cold-rolled strip is annealed at an annealing temperature of 810 - 850 °C.
  9. Method according to Claim 4 or 8, characterized in that the tensile strength of the cold-rolled strip is more than 800 MPa.
  10. Method according to Claim 4, 8 or 9, characterized in that the cold-rolled strip has a minimum breaking elongation A50 of 5 %.
  11. Method according to any one of the preceding claims, characterized in that the hot-rolled strip or cold-rolled strip is provided with a metallic coating.
  12. Method according to Claim 11, characterized in that the metallic coating is a zinc coating.
  13. Method according to any one of the preceding claims, characterized in that with a minimum breaking elongation A80 of the obtained hot-rolled strip of 10 %, the coiling temperature is 550 - 700 °C.
  14. Method according to any one of Claims 1 to 12, characterized in that with a minimum tensile strength Rm of the obtained hot-rolled strip of 1000 MPa, the final hot-rolling temperature is 900 - 1000 °C and the coiling temperature is 450 - 550 °C.
EP06123141A 2006-10-30 2006-10-30 Process for manufacturing steel flat products from silicon alloyed multi phase steel Not-in-force EP1918405B1 (en)

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PL06123141T PL1918405T3 (en) 2006-10-30 2006-10-30 Process for manufacturing steel flat products from silicon alloyed multi phase steel
AT06123141T ATE432375T1 (en) 2006-10-30 2006-10-30 METHOD FOR PRODUCING FLAT STEEL PRODUCTS FROM A MULTIPHASE STEEL ALLOYED WITH SILICON
ES06123141T ES2325964T3 (en) 2006-10-30 2006-10-30 PROCEDURE FOR MANUFACTURING STEEL FLAT PRODUCTS FROM A MULTIPHASIC STEEL ALLOYED WITH SILICON.
DE502006003833T DE502006003833D1 (en) 2006-10-30 2006-10-30 Method for producing steel flat products from a silicon-alloyed multiphase steel
EP06123141A EP1918405B1 (en) 2006-10-30 2006-10-30 Process for manufacturing steel flat products from silicon alloyed multi phase steel
CN2007800400604A CN101528968B (en) 2006-10-30 2007-10-24 Method for manufacturing flat steel products from a multiphase steel alloyed with silicon
PCT/EP2007/061392 WO2008052921A1 (en) 2006-10-30 2007-10-24 Method for manufacturing flat steel products from a multiphase steel alloyed with silicon
KR1020097007487A KR101461585B1 (en) 2006-10-30 2007-10-24 Method for manufacturing flat steel products from a multiphase steel alloyed with silicon
JP2009533824A JP5350255B2 (en) 2006-10-30 2007-10-24 Process for producing flat steel products from silicon alloyed multiphase steels
US12/447,625 US20100065161A1 (en) 2006-10-30 2007-10-24 Method for manufacturing flat steel products from silicon alloyed multi-phase steel

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EP1918405B1 true EP1918405B1 (en) 2009-05-27

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ATE432375T1 (en) 2009-06-15
EP1918405A1 (en) 2008-05-07
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WO2008052921A1 (en) 2008-05-08
US20100065161A1 (en) 2010-03-18

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