DE102005062221B3 - Deformable light alloy steel with TRIP) and TWIP properties useful in production of products having decreased crack liability twinning induced plasticity (TWIP) good ductility and tensile strength without increase in hydrogen embrittlement - Google Patents

Deformable light alloy steel with TRIP) and TWIP properties useful in production of products having decreased crack liability twinning induced plasticity (TWIP) good ductility and tensile strength without increase in hydrogen embrittlement Download PDF

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DE102005062221B3
DE102005062221B3 DE102005062221A DE102005062221A DE102005062221B3 DE 102005062221 B3 DE102005062221 B3 DE 102005062221B3 DE 102005062221 A DE102005062221 A DE 102005062221A DE 102005062221 A DE102005062221 A DE 102005062221A DE 102005062221 B3 DE102005062221 B3 DE 102005062221B3
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content
twip
trip
induced plasticity
alloy steel
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German (de)
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Karl-Heinz Prof.Dr. Spitzer
Hellfried Eichholz
Bianca Springub
Rune Dr. Schmidt-Jürgensen
Markus Dr. Schäperkötter
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Salzgitter Flachstahl GmbH
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Salzgitter Flachstahl GmbH
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Application filed by Salzgitter Flachstahl GmbH filed Critical Salzgitter Flachstahl GmbH
Priority to DE102005062221A priority Critical patent/DE102005062221B3/en
Priority to DE202005021771U priority patent/DE202005021771U1/en
Priority to UAA200809270A priority patent/UA88994C2/en
Priority to KR1020087016987A priority patent/KR20080081969A/en
Priority to AU2006332301A priority patent/AU2006332301B2/en
Priority to RU2008129694/02A priority patent/RU2430184C2/en
Priority to EP06818103.1A priority patent/EP1969151B1/en
Priority to US12/158,490 priority patent/US20090196785A1/en
Priority to CNA2006800481734A priority patent/CN101405420A/en
Priority to PCT/DE2006/002081 priority patent/WO2007076748A1/en
Publication of DE102005062221B3 publication Critical patent/DE102005062221B3/en
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Priority to ZA200805306A priority patent/ZA200805306B/en
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    • 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
    • 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
    • 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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Investigating And Analyzing Materials By Characteristic Methods (AREA)

Abstract

Deformable light alloy steel with transformation induced plasticity (TRIP) and twinning induced plasticity (TWIP) properties of composition (wt.%):C (0.05 to =1.0), Al 0.0 to =11.0), Si (0.0 to =6.0), Al+Si greater than 0.05, Mn (9.0 to =25.0, H less than 20 ppm, remainder Fe and usual steel impurities, where alloying composition is present in various phases. Alloy can have decreased Mn content and increased C content or increased content and decreased C content. The C/Mn pair value (sic) lies in C/Mn coordinate system approximating to linear bond line (sic), which is distance from the C/Mn pair value in equilibrium between gamma-austenite and alpha'- martensite phases.

Description

Die Erfindung betrifft einen umformbaren Leichtbaustahl mit TRIP- (Transformation Induced Plasticity) und TWIP- (Twinning Induced Plasticity) Eigenschaften gemäß dem Oberbegriff des Anspruches 1.The The invention relates to a deformable lightweight structural steel with TRIP (transformation Induced Plasticity) and TWIP (Twinning Induced Plasticity) properties according to the generic term of claim 1.

Umformbare Leichtbaustähle dieser Art sind bekannt ( DE 10 2004 061 284 A1 , DE 197 27 759 A1 , DE 101 285 44 A1 ). Bei diesen und vergleichbaren Stählen kann bei Vorliegen von Eigenspannungen im Material in Abhängigkeit vom Gefüge und der Festigkeit eine durch Wasserstoff ausgelöste verzögerte Versprödung und in Folge dessen eine Rissbildung auftreten.Formable lightweight steels of this type are known ( DE 10 2004 061 284 A1 . DE 197 27 759 A1 . DE 101 285 44 A1 ). In the case of these and comparable steels, in the presence of residual stresses in the material, depending on the microstructure and the strength, a hydrogen-induced delayed embrittlement and as a result cracking may occur.

Zur Überwindung dieses Problems ist bereits vorgeschlagen worden, den Wasserstoffgehalt auf < 20 ppm vorzugsweise auf < 5 ppm zu begrenzen ( DE 10 2004 061 284 A1 ).To overcome this problem, it has already been proposed to limit the hydrogen content to <20 ppm, preferably to <5 ppm ( DE 10 2004 061 284 A1 ).

Dieser Vorschlag ist zwar hilfreich aber nicht ausreichend, da selbst bei niedrig eingestellten Wasserstoffgehalten trotzdem noch der Effekt der Wasserstoffversprödung auftreten kann. Außerdem können bei der Stahlherstellung aus verschiedenen Gründen Überschreitungen des festgelegten Maximalwertes für Wasserstoff vorkommen, die legierungsmäßig zwar toleriert werden können, aber die Gefahr des Auftretens einer Wasserstoffversprödung vergrößern.This Suggestion is helpful but not sufficient, even with still low the hydrogen content still the effect the hydrogen embrittlement can occur. Furthermore can in steelmaking for various reasons exceeded the specified Maximum value for Hydrogen occur, although the alloy can be tolerated, but increase the risk of hydrogen embrittlement.

Aufgabe der Erfindung ist es einen Leichtbaustahl der gattungsgemäßen Art anzugeben, der unter Beibehaltung sehr guter mechanischer Eigenschaften (Duktilität, Festigkeit) den Effekt einer verzögerten Wasserstoffversprödung nicht aufweist.task The invention is a lightweight steel of the generic type specify, while maintaining very good mechanical properties (Ductility, Strength) does not effect the effect of retarded hydrogen embrittlement having.

Diese Aufgabe wird ausgehend vom Oberbegriff in Verbindung mit den kennzeichnenden Merkmalen des Anspruches 1 gelöst. Vorteilhafte Weiterbildungen sind Gegenstand von Unteransprüchen.These Task is based on the generic term in conjunction with the characterizing Characteristics of claim 1 solved. Advantageous developments are the subject of dependent claims.

Nach der Lehre der Erfindung wird das in der Aufgabenstellung genannte Problem durch ein neues Legierungskonzept gelöst. Dieses zeichnet sich dadurch aus, dass einem niedrigeren Mn-Gehalt ein höherer C-Gehalt und einem höheren Mn-Gehalt ein niedriger C-Gehalt zugeordnet wird, wobei die C-Mn-Wertepaare in einem C-Mn-Koordinatensystem annähernd auf einer geraden Verbindungslinie liegen, die einen Abstand zur Verbindungslinie von im Gleichgewicht zwischen γ- (Austenit-kfz) und α'-Phasen (Martensit-krz) sich befindenden C-Mn-Wertepaaren aufweist.To The teaching of the invention is called in the task Problem solved by a new alloy concept. This is characterized by from that a lower Mn content has a higher C content and a higher Mn content assigned a low C content, wherein the C-Mn value pairs in a C-Mn coordinate system lie approximately on a straight connecting line, a distance from the line of equilibrium between γ- (austenite-fcc) and α'-phases (martensite-krz) C-Mn value pairs having.

Bei diesem neuen Legierungskonzept macht man sich die Erkenntnis zu Nutze, dass die γ-Austenit(kfz) und die ε-Martensit(hdp)-Phase eine hohe Wasserstofflöslichkeit besitzen während die α'-Martensit(krz)-Phase eine sehr viel geringere Wasserstofflöslichkeit aufweist. Beim Auftreten des TRIP-Effektes kommt es je nach Legierungszusammensetzung zur Bildung der α'-Martensit-Phase, z.T. über die metastabile ε-Martensit-Phase. In Bereichen, in denen der Werkstoff z.B. unter Druckspannung umgeformt wird, kann dabei die dichter gepackte ε-Martensit-Phase nach dem Prinzip des kleinsten Zwanges auch nach der Umformung vorliegen und bei Entlastung in die α'-Martensit-Phase umklappen.at This new alloy concept makes you aware of it Use the γ austenite (fcc) and the ε-martensite (hdp) phase a high hydrogen solubility own during the α'-martensite (krz) phase has a much lower hydrogen solubility. Upon occurrence The TRIP effect depends on the alloy composition Formation of the α'-martensite phase, z.T. about the metastable ε-martensite phase. In areas where the material is e.g. deformed under compressive stress is, can the more densely packed ε-martensite phase on the principle of the smallest constraint even after the forming and at Relief in the α'-martensite phase fold.

Bei diesem Umklappen von der ε-Martensit-Phase in die α'-Martensit-Phase muss der Wasserstoff wegen der niedrigeren Löslichkeit entweichen, und führt entweder atomar oder rekombiniert zur Schwächung des Materials, gegebenenfalls zum Reißen.at this flipping of the ε-martensite phase into the α'-martensite phase The hydrogen must escape because of the lower solubility, and leads either atomic or recombined to weaken the material, optionally to tearing.

Ausgehend von einer Legierung mit C und Mn führt die Zugabe von Al und/oder Si zu einer Destabilisierung der ε-Martensit-Phase. Das verringert die Gefahr einer Wasserstoffversprödung bzw. erhöht den Spielraum für den Stahlwerker auch bei Überschreitung des Maximalwertes des Wasserstoffs die abgegossene Schmelze noch als tolerierbar einzustufen. Weniger Abwertungen erhöhen das Ausbringen und damit die Wirtschaftlichkeit des Verfahrens.outgoing of an alloy with C and Mn, the addition of Al and / or Si destabilization of the ε-martensite phase. This reduces the risk of hydrogen embrittlement or elevated the scope for the steelworker even when exceeded the maximum value of hydrogen, the cast melt still to be considered tolerable. Less devaluations increase that Application and thus the efficiency of the process.

Vorzugsweise ist die Zugabe von Al und Si annähernd gleich groß.Preferably the addition of Al and Si is approximate same size.

Unabhängig von der Wirkung der Zugabe von Al und/oder Si ist der Kohlenstoffgehalt ein entscheidendes Element im vorgeschlagenen Legierungskonzept, da er die Austenit-Phase stabilisiert und den Wasserstoff von den freien Gitterplätzen verdrängt.Independent of the effect of adding Al and / or Si is the carbon content a crucial element in the proposed alloy concept, since it stabilizes the austenite phase and the hydrogen from the free grid places repressed.

Das Streuband um die Verbindungslinie der optimalen C-Mn-Wertepaare für den Gehalt an C sollte = ± 0,15%, vorzugsweise ± 0,1% an für den Gehalt an Mn = ± 2,5%, vorzugsweise ± 1,5% betragen.The Scattering around the connecting line of the optimal C-Mn value pairs for the Content of C should = ± 0.15%, preferably ± 0.1% on for the content of Mn = ± 2.5%, preferably ± 1.5% be.

Beispielsweise weisen Legierungen mit
0,7 % C, 15 % Mn, 2,5 % Al, 2,5 % Si
sowie
0,4 % C, 18 % Mn, 2,5 % Al, 2,5 % Si
neben hervorragenden mechanischen Eigenschaften, wie nachfolgend angegeben, keine verzögerte Rissbildung ("delayed fracture") auf.For example, alloys have
0.7% C, 15% Mn, 2.5% Al, 2.5% Si
such as
0.4% C, 18% Mn, 2.5% Al, 2.5% Si
in addition to excellent mechanical properties, as indicated below, no delayed fracture on.

Nach einer Glühung bei 850°C weist das erste Legierungsbeispiel eine Streckgrenze Rp0,2 von 480 MPa und eine Festigkeit von 850 MPa mit einer Dehnung A von 58 % auf. Diese Werte für das zweite Legierungsbeispiel ebenfalls nach einer Glühung bei 850°C sind Rp0,2 450 MPa; Rm 790 MPa und A 53 %. Eine zweite Kenngröße ist das Produkt aus Festigkeit x Dehnung, das ein Maß für die Leistungsfähigkeit des Werkstoffes ist. Dieser Wert liegt für das Legierungsbeispiel 1 bei 49.300 und für Beispiel 2 bei 41.870 (% x MPa).After annealing at 850 ° C, the first alloy example has a yield strength R p0.2 of 480 MPa and a strength of 850 MPa with an elongation A of 58%. These values for the second alloy example also after annealing at 850 ° C are R p0.2 450 MPa; R m 790 MPa and A 53%. A second parameter is the product of strength x elongation, which is a measure of the material's performance. This value is 49,300 for alloy example 1 and 41,870 (% x MPa) for example 2.

In der einzigen Figur ist in einem Koordinatensystem der C-Gehalt über den Mn-Gehalt aufgetragen. Die durchgezogene gerade Verbindungslinie zeigt die C-Mn-Wertepaare, die sich unter Berücksichtigung einer Al- und/oder Si-Zugabe im Gleichgewicht bezüglich der γ-Austenit- und der α'-Martensit-Phase befinden.In the single figure is in a coordinate system the C content over the Mn content applied. The solid straight connecting line shows the C-Mn value pairs, which take into account an Al and / or Si addition in equilibrium with respect γ-austenite and α'-martensite phases are located.

Die gestrichelte Verbindungslinie, die einen Abstand zur Gleichgewichtslinie aufweist, kennzeichnet Wertepaare des optimalen Legierungskonzeptes, hinsichtlich Werkstoffeigenschaften unter Vermeidung einer verzögerten Rissbildung (delayed fracture). Die über die gestrichelte Verbindungslinie gelegte Schraffierung soll das qualitative Streuband andeuten, innerhalb dessen noch optimale Ergebnisse zu erwarten sind.The dashed connecting line, which is a distance to the equilibrium line features value pairs of the optimal alloy concept, in terms of Material properties while avoiding delayed cracking (delayed fracture). The above the dashed connecting line laid hatching is the indicate qualitative scattering within which are still optimal results are expected.

Claims (4)

Umformbarer Leichtbaustahl mit TRIP- und TWIP-Eigenschaften mit den Elementen in Gew.-% C 0,05 bis ≤ 1,0 Al 0,0 bis ≤ 11,0 Si 0,0 bis ≤ 6,0 Al + Si > 0,05 Mn 9,0 bis ≤ 25,0 H < 20 ppm, Rest Eisen einschließlich üblicher stahlbegleitender Elemente, wobei je nach Legierungszusammensetzung unterschiedliche Phasen vorliegen, dadurch gekennzeichnet, dass einem niedrigeren Mn-Gehalt ein höherer C-Gehalt und einem höheren Mn-Gehalt ein niedriger C-Gehalt zugeordnet wird, wobei die C-Mn-Wertepaare in einem C-Mn-Koordinatensystem annähernd auf einer geraden Verbindungslinie liegen, die einen Abstand zur Verbindungslinie von im Gleichgewicht zwischen γ- (Austenit) und α'-Phasen (Martensit) sich befindenden C-Mn-Wertepaaren aufweist.Convertible lightweight structural steel with TRIP and TWIP properties with the elements in% by weight C 0.05 to ≤ 1.0 Al 0.0 to ≤ 11.0 Si 0.0 to ≤ 6.0 Al + Si> 0, 05 Mn 9.0 to ≤ 25.0 H <20 ppm, the remainder being iron, including conventional steel-supporting elements, different phases being present depending on the alloy composition, characterized in that a lower Mn content means a higher C content and a higher Mn content is assigned a low C content, wherein the C-Mn pairs of values in a C-Mn coordinate system are approximately on a straight connecting line, which is a distance to the line of equilibrium between γ- (austenite) and α'-phases (martensite ) has C-Mn value pairs. Leichtbaustahl nach Anspruch 1, dadurch gekennzeichnet, dass die Zugabe von Al und Si annähernd gleich groß ist.Lightweight steel according to claim 1, characterized that the addition of Al and Si is approximately equal. Leichtbaustahl nach den Ansprüchen 1-2, dadurch gekennzeichnet, dass das Streuband um die Verbindungslinie der optimalen C-Mn-Wertepaare für den Gehalt an C = ± 0,15 % und für den Gehalt an Mn = ± 2,5 % beträgt.Lightweight steel according to claims 1-2, characterized that the scattering band around the connecting line of the optimal C-Mn value pairs for the content at C = ± 0.15 % and for the content of Mn = ± 2.5 % is. Leichtbaustahl nach Anspruch 3, dadurch gekennzeichnet, dass das Streuband für den Gehalt an C = ± 0,1 % und für den Gehalt an Mn = ± 1,5 % beträgt.Lightweight steel according to claim 3, characterized that the scattering for the content of C = ± 0.1 % and for the content of Mn = ± 1.5 % is.
DE102005062221A 2005-12-20 2005-12-20 Deformable light alloy steel with TRIP) and TWIP properties useful in production of products having decreased crack liability twinning induced plasticity (TWIP) good ductility and tensile strength without increase in hydrogen embrittlement Expired - Fee Related DE102005062221B3 (en)

Priority Applications (11)

Application Number Priority Date Filing Date Title
DE102005062221A DE102005062221B3 (en) 2005-12-20 2005-12-20 Deformable light alloy steel with TRIP) and TWIP properties useful in production of products having decreased crack liability twinning induced plasticity (TWIP) good ductility and tensile strength without increase in hydrogen embrittlement
DE202005021771U DE202005021771U1 (en) 2005-12-20 2005-12-20 Formable lightweight steel
EP06818103.1A EP1969151B1 (en) 2005-12-20 2006-11-22 Process for manufacturing a deformable lightweight structural steel
KR1020087016987A KR20080081969A (en) 2005-12-20 2006-11-22 Deformable lightweight structural steel
AU2006332301A AU2006332301B2 (en) 2005-12-20 2006-11-22 Deformable lightweight structural steel
RU2008129694/02A RU2430184C2 (en) 2005-12-20 2006-11-22 Wrought steel for light-weight constructions
UAA200809270A UA88994C2 (en) 2005-12-20 2006-11-22 Deformable steel for manufacturing lightweight DESIGNS
US12/158,490 US20090196785A1 (en) 2005-12-20 2006-11-22 Transformable Lightweight Structural Steel
CNA2006800481734A CN101405420A (en) 2005-12-20 2006-11-22 Deformable lightweight structural steel
PCT/DE2006/002081 WO2007076748A1 (en) 2005-12-20 2006-11-22 Deformable lightweight structural steel
ZA200805306A ZA200805306B (en) 2005-12-20 2008-06-18 Deformable lightweight structural steel

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Application Number Priority Date Filing Date Title
DE102005062221A DE102005062221B3 (en) 2005-12-20 2005-12-20 Deformable light alloy steel with TRIP) and TWIP properties useful in production of products having decreased crack liability twinning induced plasticity (TWIP) good ductility and tensile strength without increase in hydrogen embrittlement

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DE202005021771U Expired - Lifetime DE202005021771U1 (en) 2005-12-20 2005-12-20 Formable lightweight steel

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US (1) US20090196785A1 (en)
EP (1) EP1969151B1 (en)
KR (1) KR20080081969A (en)
CN (1) CN101405420A (en)
AU (1) AU2006332301B2 (en)
DE (2) DE102005062221B3 (en)
RU (1) RU2430184C2 (en)
UA (1) UA88994C2 (en)
WO (1) WO2007076748A1 (en)
ZA (1) ZA200805306B (en)

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WO2012069035A3 (en) * 2010-11-26 2012-07-19 Salzgitter Flachstahl Gmbh Energy-storing container made of lightweight steel
WO2013124283A1 (en) * 2012-02-25 2013-08-29 Technische Universität Bergakademie Freiberg Method for producing high-strength molded parts from high-carbon and high-manganese-containing austenitic cast steel with trip/twip properties

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US8852356B2 (en) 2009-03-11 2014-10-07 Salzgitter Glachstahl GmbH Method for producing a hot rolled strip and hot rolled strip produced from ferritic steel
DE102010034161B4 (en) 2010-03-16 2014-01-02 Salzgitter Flachstahl Gmbh Method for producing workpieces made of lightweight steel with material properties that can be adjusted via the wall thickness
DE102011010040B3 (en) 2011-02-02 2012-08-02 Salzgitter Flachstahl Gmbh Method and device for producing a cast strip of steel with material properties adjustable over the strip cross section and the strip length
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DE102012013425A1 (en) 2012-07-03 2014-01-09 Salzgitter Flachstahl Gmbh Continuous strip casting and rolling plant
WO2014180456A1 (en) 2013-05-06 2014-11-13 Salzgitter Flachstahl Gmbh Method for producing components from lightweight steel
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