DE102004061284A1 - Production of a deformable hot strips made from light gauge steel used in the automobile industry comprises casting the melt in a horizontal strip casting unit close to the final measurements, and further processing - Google Patents
Production of a deformable hot strips made from light gauge steel used in the automobile industry comprises casting the melt in a horizontal strip casting unit close to the final measurements, and further processing Download PDFInfo
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- 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
- B22D11/0605—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two belts, e.g. Hazelett-process
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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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/06—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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
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- Organic Chemistry (AREA)
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- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
Die Erfindung betrifft ein Verfahren zum Erzeugen von Warmbändern aus einem umformbaren, insbesondere gut kalt tiefziehfähigen Leichtbaustahl gemäß dem Oberbegriff des Patentanspruches 1.The The invention relates to a method for producing hot strips a deformable, especially good cold deep drawable lightweight structural steel according to the preamble of claim 1.
Der heiß umkämpfte Automobilmarkt zwingt die Hersteller ständig nach Lösungen zur Senkung des Flottenverbrauches unter Beibehaltung eines höchstmöglichen Komforts zu suchen. Dabei spielt die Gewichtsersparnis eine entscheidende Rolle. Diesem Wunsch versuchen die Lieferanten insbesondere für den Karosseriebereich dadurch Rechnung zu tragen, dass durch den Einsatz höherfester Stähle die Wanddicken reduziert werden können, ohne Einbußen der Beulsteifigkeit sowie der Umformung durch Tief- und/oder Streckziehen und der Beschichtung in Kauf nehmen zu müssen.Of the hotly contested automotive market forces the manufacturers constantly for solutions to reduce fleet consumption while maintaining the highest possible To look for comfort. The weight savings plays a decisive role here Role. Suppliers are trying to fulfill this wish in particular for the bodywork sector take account of the fact that the use of higher-strength steels Wall thicknesses can be reduced without losses the buckling stiffness as well as the forming by deep and / or ironing and the coating to accept.
Ein
Lösungsansatz
dazu ist in der
Der hohe Umformgrad wird dunch TRIP- (Transformation Induced Plasticity) und TWIP- (Twinning Induced Plasticity) Eigenschaften des Stahles erreicht. Stähle mit hohen Mn-Gehalten neigen zu Seigenungen, wie sie beim konventionellen Stranggießen durch Biegung, Ausbauchung des Stranges, Sedimentation und Saugseigerung im Sumpfspitzenbereich vorkommen.Of the high degree of deformation will dunch TRIP (Transformation Induced Plasticity) and TWIP (Twinning Induced Plasticity) achieves properties of the steel. Steels with high Mn levels tend to seige, as in conventional continuous casting Bending, bulging of the strand, sedimentation and suction seeding occur in the swamp tip area.
Die auf diese Weise entstehende Makroseigerung, die auch zu intermetallischen Phasen führen kann, führt zu schwerwiegenden Bandfehlern beim Warmwalzen.The in this way emerging macrosegregation, which is also intermetallic Can lead phases, leads to severe banding during hot rolling.
Hochlegierte Stähle neigen grundsätzlich auch zu Innenrissen, die letztlich Markroseigerungsfehler darstellen. Diese resultieren z. B. aus Biegebeanspruchungen während des Herstellungsprozesses.High-alloy steels basically, too internal cracks, which ultimately represent marrow defects. These result z. B. from bending stresses during the Manufacturing process.
Stähle mit hohen Al-Gehalten lassen sich mit konventionellen Gießpulvern nicht vergießen, da Al im besonderen Maße das SiO2 im Gießpulver reduziert und somit zu einer verschlechterten Reibung zwischen Strangschale und Kokille führt.Steels with high Al contents can not be cast with conventional casting powders, since Al in particular reduces the SiO 2 in the casting powder and thus leads to a reduced friction between the strand shell and mold.
Der Erfindung liegt die Aufgabe zugrunde, ein Verfahren zum Erzeugen von Warmbändern aus einem umformbaren, insbesondere gut kalt tiefziehfähigem Leichtbaustahl anzugeben, das die zuvor geschilderten Nachteile vermeidet.Of the Invention is based on the object, a method for generating of hot tapes from a formable, especially good deep-drawable low-weight steel specify that avoids the disadvantages described above.
Diese Aufgabe wird ausgehend vom Oberbegriff in Verbindung mit den kennzeichnenden Merkmalen des Anspruches 1 gelöst.These Task is based on the generic term in conjunction with the characterizing Characteristics of claim 1 solved.
Nach
der Lehre der Erfindung weist der Stahl Gehalte in Masse % für
C
0,04 bis ≤ 1,0
Al
0,05 bis < 4,0
Si
0,05 bis ≤ 6,0
Mn
9,0 bis ≤ 30,0
auf,
Rest Eisen einschließlich üblicher
Stahlbegleitelemente und bei dem eine Schmelze in einer horizontalen
Bandgießanlage
endabmessungsnah sowie strömungsberuhigt
und biegefrei zu einem Vorband im Bereich zwischen 6 und 15 mm vergossen
und anschließend
einer Weiterbehandlung zugeführt
wird. Optional können
je nach Anforderung Cr, Cu, Ti, Zr, V und Nb der Stahlschmelze zugegeben
werden.According to the teaching of the invention, the steel contents in% by mass
C 0.04 to ≤ 1.0
Al 0.05 to <4.0
Si is 0.05 to ≤ 6.0
Mn 9.0 to ≤ 30.0
on, remainder iron including conventional steel accompanying elements and in which a melt in a horizontal strip casting plant near the final dimensions and flow-smoothed and bend-free cast to a preliminary band in the range between 6 and 15 mm and then fed to a further treatment. Optionally, Cr, Cu, Ti, Zr, V and Nb can be added to the molten steel as required.
Der erfindungsgemäße Stahl ist gefügemäßig entweder als stabilisierter γ-Kristall oder als teilstabilisierter γ-Mischkristall mit definierter Stapelfehlerenergie ausgeprägt, der einen z. T. multiplen TRIP-Effekt zeigt.Of the Steel according to the invention is befitting either as a stabilized γ-crystal or as partially stabilized γ-mixed crystal pronounced with a defined stacking fault energy, the z. T. multiple TRIP effect shows.
Der
letztgenannte Effekt ist die spannungs- oder dehnungsinduzierte
Umwandlung eines flächenzentrierten γ-Mischkristalls
in ein martensitisches ε-Gefüge mit hexagonaler
dichtester Kugelpackung, der dann zum Teil in einen raumzentrierten α-Martensit
und Restaustenit transformiert.
fcc = face centred cubic
bcc
= body centred cubic
hcp = hexogonal closed packedThe latter effect is the stress- or strain-induced transformation of a surface-centered γ-mixed crystal into a martensitic ε-structure with hexagonal close-packed spherical packing, which then partially transforms into a body-centered α-martensite and retained austenite.
fcc = face centric cubic
bcc = body centric cubic
hcp = hexagonal closed packed
Zahlreiche Versuche haben zur Erkenntnis geführt, dass im komplexen Zusammenspiel zwischen Al, Si und Mn dem Kohlenstoffgehalt eine überragende Bedeutung zukommt. Es erhöht zum Einen die Stapelfehlerenergie und erweitert zum Anderen den metastabilen Austenitbereich. Dadurch wird die verformungsinduzierte Martensitbildung und die damit verbundene Verfestigung gehemmt und auch die Duktilität gesteigert.numerous Experiments have led to the realization that in the complex interaction between Al, Si and Mn the carbon content is a superior Meaning. It increases On the one hand, the stacking fault energy and, on the other, expands that metastable austenite area. This will cause the deformation induced Martensite formation and the associated hardening inhibited and also the ductility increased.
Weitere Verbesserungen lassen sich erreichen durch gezielte Zugaben von Kupfer und/oder Chrom. Mit der Zugabe von Kupfer wird der ε-Martensit stabilisiert und die Verzinkbarkeit verbessert. Zudem erhöht Kupfer die Korrosionsbeständigkeit des Stahles. Auch Chrom stabilisiert den ε-Martensit und verbessert die Korrosionsbeständigkeit.Further improvements can be achieved by targeted additions of copper and / or chromium. With the addition of copper, the ε-martensite is stabilized and the galvanic nature is improved. In addition, copper increases the corrosion resistance of the steel. Chromium also stabilizes ε-martensite and improves corrosion resistance.
Der Vorteil des vorgeschlagenen Leichtbaustahles ist darin zu sehen, dass durch gezielte Legierungszusammensetzung und Wahl der Prozessparameter wie Umformgrad und Wärmebehandlung ein breites Spektrum von Festigkeits- und Duktilitätsanforderungen abgedeckt werden kann, wobei Zugfestigkeiten bis 1400 MPa möglich sind. Dabei spielt die Kohlenstoffzugabe eine Schlüsselrolle.Of the Advantage of the proposed lightweight steel figure is to be seen in that through targeted alloy composition and choice of process parameters such as degree of deformation and heat treatment a wide range of strength and ductility requirements can be covered, with tensile strengths up to 1400 MPa are possible. The carbon addition plays a key role.
Bislang wurde in der Fachwelt die Meinung vertreten, den Kohlenstoffgehalt möglichst auf Null zu setzen, um die Bildung von κ-Karbiden zu vermeiden. Die Erfindung überwindet dieses Vorurteil durch den Vorschlag eines ausgewogenen Verhältnisses der Zugabe von Aluminium und Mangan, das auch eine gezielte Zugabe von Kohlenstoff gestattet.So far The opinion was expressed in the professional world, the carbon content preferably to zero in order to avoid the formation of κ-carbides. The Overcomes invention this prejudice by proposing a balanced relationship the addition of aluminum and manganese, which is also a targeted addition allowed by carbon.
Für das Phänomen "delayed fracture", das bei Stählen mit überwiegend TRIP-Eigenschaften auftreten kann, spielt der Wasserstoffgehalt im Stahl eine wichtige Rolle. Das Phänomen äußert sich darin, dass z. B. an tiefgezogenen Näpfen nach einiger Zeit im Kantenbereich Risse auftreten. Der Rissbildungsvorgang kann sich über mehrere Tage hinziehen.For the phenomenon "delayed fracture", which predominantly affects steels TRIP properties can occur, the hydrogen content plays in the steel an important role. The phenomenon manifests itself in that z. B. on deep-drawn cups Cracks appear in the edge area after some time. The cracking process can over drag on for several days.
Aus diesem Grunde wird vorgeschlagen, den Wasserstoffgehalt auf < 20 ppm vorzugsweise auf < 5 ppm zu begrenzen. Dieses lässt sich durch eine sorgfältige Behandlung während der Erschmelzung erreichen, z. B. durch eine spezielle Spül- und Vakuumbehandlung.Out For this reason, the hydrogen content is preferably <20 ppm to <5 ppm limit. This leaves through a careful Treatment during reach the melting, z. B. by a special rinsing and vacuum treatment.
Je nach Anforderung kann es erforderlich sein, den Leichtbaustahl überwiegend mit TRIP oder mit TWIP-Eigenschaften auszustatten. Dies kann man am einfachsten durch Steuerung des Mn-Gehaltes erreichen. Wird der untere Bereich von etwa 9–18% gewählt, dann ist ein Endprodukt mit überwiegend TRIP-Eigenschaften zu erwarten, wird hingegen der obere Bereich mit etwa 22–30% bevorzugt, überwiegen die TWIP-Eigenschaften. Wie schon zuvor erwähnt, ist diese Steuerung auch durch gezielte Zugabe anderer Elemente, insbesondere Kohlenstoff, möglich. In diesem Zusammenhang sei erwähnt, dass unter dem Blickwinkel einer ausreichenden Korrosionsbeständigkeit für den unteren angegebenen Mn-Bereich ein höherer Cr-Gehalt und für den oberen Mn-Bereich ein niedrigerer Cr-Gehalt vorteilhaft ist.ever Upon request, it may be necessary to use the lightweight steel predominantly equipped with TRIP or with TWIP properties. This one can easiest to achieve by controlling the Mn content. Will the lower range of about 9-18% selected then an end product is overwhelming Expect TRIP properties, however, the upper range with about 22-30% preferred, predominate the TWIP properties. As mentioned earlier, this control is too by targeted addition of other elements, in particular carbon, possible. In this context it should be mentioned that from the point of view of adequate corrosion resistance for the lower specified Mn range a higher one Cr content and for the upper Mn range, a lower Cr content is advantageous.
Verfahrenstechnisch wird vorgeschlagen, die Strömungsberuhigung dadurch zu erreichen, dass eine mitlaufende elektromagnetische Bremse eingesetzt wird, die dafür sorgt, dass im Idealfall die Geschwindigkeit des Schmelzenzulaufs gleich der Geschwindigkeit des umlaufenden Förderbandes ist.process engineering it is suggested the flow calming to achieve that a follower electromagnetic brake is used for that ensures that, ideally, the speed of the melt inlet is equal to the speed of the circulating conveyor belt.
Die als nachteilig angesehene Biegung während der Erstarrung wird dadurch vermieden, dass die Unterseite des die Schmelze aufnehmenden Gießbandes sich auf einer Vielzahl von nebeneinander liegenden Rollen abstützt. Verstärkt wird die Abstützung in der Weise, dass im Bereich des Gießbandes ein Unterdruck erzeugt wird, so dass das Gießband fest auf die Rollen gedrückt wird.The considered as disadvantageous bending during solidification is characterized avoided that the underside of the casting tape receiving the melt is supported on a variety of adjacent roles. Reinforced the support in such a way that creates a negative pressure in the region of the casting belt so that the casting tape firmly pressed on the rollers becomes.
Um diese Bedingungen während der kritischen Phase der Erstarrung aufrecht zu erhalten, wird die Länge des Förderbandes so gewählt, dass am Ende des Förderbandes vor dessen Umlenkung das Vorband weitestgehend durcherstarrt ist.Around these conditions during To maintain the critical phase of solidification, the Length of the conveyor belt chosen so that at the end of the conveyor belt before the deflection of the Vorband is largely solidified.
Am Ende des Förderbandes schließt sich eine Homogenisierungszone an, die für einen Temperaturausgleich und möglichen Spannungsabbau genutzt wird. Danach folgt eine Weiterbehandlung, die ein direktes Aufcoilen des Vorbandes sein kann oder aus einem vorgeschalteten Walzprozess besteht, um die erforderliche Umformung von mindestens 50% vorzugsweise von > 70% aufzubringen.At the End of the conveyor belt includes a Homogenisierungszone, which is for a temperature compensation and possible Stress reduction is used. This is followed by a further treatment, the may be a direct Aufcoilen the Vorbandes or from an upstream Rolling process consists of the required deformation of at least 50%, preferably of> 70% applied.
Das direkte Aufcoilen des Vorbandes hat den Vorteil, dass man die Gießgeschwindigkeit hinsichtlich optimaler Erstarrungsbedingungen wählen kann, unabhängig vom Takt des nachfolgenden Walzprozesses.The direct Aufcoilen the Vorbandes has the advantage that one the casting speed in terms of optimum solidification conditions, regardless of Clock of the subsequent rolling process.
Andererseits kann es insbesondere aus wirtschaftlichen Gründen (hohe Produktivität) vorteilhaft sein, den erfindungsgemäßen Werkstoff direkt nach dem Gießen inline ganz oder teilweise bis auf seine endgültige Dicke zu walzen.on the other hand In particular, it may be advantageous for economic reasons (high productivity) the material according to the invention right after pouring inline wholly or partially to roll to its final thickness.
Bei der Bildung der Strangschale zu Beginn der Erstarrung kann es lokal zu Abhebungen der Strangschale vom umlaufenden Band der Bandgießanlage kommen. Dies führt unter Umständen zu unzulässigen Unebenheiten der Unterseite des erzeugten Vorbandes. Um dies zu vermeiden, ist es erforderlich für alle Flächenelemente der sich bildenden Strangschale eines sich über die Breite des Förderbandes erstreckenden Streifens möglichst gleiche Abkühlbedingungen zu gewährleisten. Dies kann man durch eine Konditionierung der Oberseite des umlaufenden Bandes erreichen, z. B. durch eine gezielte Strukturierung oder durch Aufbringen einer thermisch isolierenden Trennschicht.at The formation of the strand shell at the beginning of solidification can be local to withdraw the strand shell from the circulating belt of the strip casting plant come. this leads to in certain circumstances too inadmissible Unevenness of the underside of the produced Vorbandes. To this, too Avoid, it is necessary for all surface elements the forming strand shell one across the width of the conveyor belt extending strip as possible same cooling conditions to ensure. This can be done by conditioning the top of the circulating Reach Bandes, z. B. by a targeted structuring or by applying a thermally insulating separating layer.
Eine der vorgenannten Strukturierungsmaßnahmen ist z. B. ein Sandstrahlen oder Bürsten der Oberseite des umlaufenden Bandes. Ein Beispiel für die thermisch isolierende Trennschicht ist die Beschichtung durch Plasmaspritzen mit beispielsweise Aluminiumoxid oder Zirkonoxid. Ein weiteres Ausführungsbeispiel für eine Strukturierung ist das Aufprägen einer Noppenstruktur, z. B. mit nach oben gerichteten Noppen von einigen 100 μm Höhe und einigen Millimeter Durchmesser sowie einem Abstand der Noppen von einigen Millimetern.One of the aforementioned structuring measures is z. B. sandblasting or brushing the top of the rotating belt. An example of the thermally insulating release layer is the coating by plasma spraying with, for example, aluminum oxide or zirconium oxide. Another embodiment of a structuring is the imprinting of a nub structure, for. B. with upward pimples of some 100 microns in height and some Mm diameter as well as a distance of the pimples of a few millimeters.
Anhand
eines Ausführungsbeispieles
werden die erreichbaren Werte demonstriert. Ausgehend von einem
Stahl mit der Analyse
C = 0,06%
Mn = 15,5%
Al = 2,0%
Si
= 2,6%
H2 = 4 ppm
wurde ein Warmband
mit einer Dicke von 2,5 mm erzeugt.Based on an embodiment, the achievable values are demonstrated. Starting from a steel with the analysis
C = 0.06%
Mn = 15.5%
Al = 2.0%
Si = 2.6%
H 2 = 4 ppm
a hot strip with a thickness of 2.5 mm was produced.
Die in Walzrichtung liegende Zugprobe ergab eine Zugfestigkeit von 1046 MPa und eine Dehnung (A80) von 35%. In Abhängigkeit vom Umformgrad und Wärmebehandlung kann die Zugfestigkeit bis über 1100 MPa und die Dehnung (A80) über 40% gesteigert werden.The in the rolling direction tensile test gave a tensile strength of 1046 MPa and an elongation (A80) of 35%. Depending on the degree of deformation and heat treatment the tensile strength can be up over 1100 MPa and the elongation (A80) over 40% increase.
Ein zweites Beispiel zeigt die Möglichkeit, wie man durch Anhebung des Kohlenstoffgehaltes bei nahezu gleichem Mn-Gehalt die Festigkeits- und Duktilitätseigenschaften gegeneinander verschieben kann.One second example shows the way how one by raising the carbon content at almost the same Mn content the strength and ductility properties can move against each other.
Der
Stahl dieses Ausführungsbeispiels
weist folgende Gehalte auf
C = 0,7%
Mn = 15%
Al =
2,5%
Si = 2,5%
H2 = 3 ppmThe steel of this embodiment has the following contents
C = 0.7%
Mn = 15%
Al = 2.5%
Si = 2.5%
H 2 = 3 ppm
Das aus diesem Stahl hergestellte Kaltband von 1,0 mm wurde unter Schutzgas bei 1050°C und einer Haltezeit von 15 Minuten rekristallisierend geglüht. Die Zugfestigkeit ist auf 817 MPa abgesunken, dafür aber die A80-Dehnung auf 60% gestiegen. Dies bedeutet, dass trotz des niedrigen Mn-Gehaltes durch die höhere Kohlenstoffzugabe der Stahl mehr in den Bereich mit TWIP-Eigenschaften verschoben worden ist.The cold rolled strip of 1.0 mm made from this steel was under protective gas at 1050 ° C and a holding time of 15 minutes, recrystallizing annealed. The Tensile strength has dropped to 817 MPa, but the A80 elongation has dropped 60% up. This means that despite the low Mn content through the higher one Carbon addition of the steel more in the range with TWIP properties has been moved.
Ein
weiteres Beispiel zeigt die Ergebnisse mit hohem Mn-Gehalt und niedrigem
Kohlenstoffgehalt. Die Gehalte betrugen
C = 0,041%
Mn
= 25%
Al = 3,4%
Si = 2,54%
H2 =
4 ppmAnother example shows the results of high Mn content and low carbon content. The contents amounted
C = 0.041%
Mn = 25%
Al = 3.4%
Si = 2.54%
H 2 = 4 ppm
Nach einer vergleichbaren Wärmebehandlung wie zuvor beschrieben, betrug die Zugfestigkeit im Mittel 632 MPa und die A80-Dehnung 57%. Auch dieses Beispiel zeigt deutlich, dass man mit hohen Mn-Gehalten die Dehnung stark steigern kann, dies aber immer zulasten der Festigkeit geht, solange der Kohlenstoffgehalt niedrig ist.To a comparable heat treatment as described above, the average tensile strength was 632 MPa and the A80 stretch 57%. This example also clearly shows that with high Mn contents it is possible to greatly increase the elongation, but this always at the expense of strength, as long as the carbon content is low.
Insgesamt zeigen die drei Beispiele die Variationsbreite hinsichtlich Festigkeit und Dehnung, wobei dem Mn- und C-Gehalt eine Schlüsselrolle zukommt. Überlagert wird der Analyseneinfluss noch durch Behandlungen des Warmbandes in Form von Glühen und/oder durch kombiniertes Kaltumformen (z. B. Walzen, Strecken, Tiefziehen) und Zwischenglühen bzw. Endglühen.All in all The three examples show the variation in strength and elongation, with the Mn and C content a key role due. overlapped the influence of analysis is still due to treatments of the hot strip in the form of glow and / or by combined cold forming (eg rolling, stretching, Thermoforming) and intermediate annealing or final annealing.
Claims (23)
Priority Applications (5)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE102004061284A DE102004061284A1 (en) | 2003-12-23 | 2004-12-14 | Production of a deformable hot strips made from light gauge steel used in the automobile industry comprises casting the melt in a horizontal strip casting unit close to the final measurements, and further processing |
EP04802997.9A EP1699582B1 (en) | 2003-12-23 | 2004-12-22 | Method for the generation of hot strips of light gauge steel |
PCT/DE2004/002817 WO2005061152A1 (en) | 2003-12-23 | 2004-12-22 | Method for the generation of hot strips of light gauge steel |
KR1020067012471A KR101178775B1 (en) | 2003-12-23 | 2004-12-22 | Method for the generation of hot strips of light gauge steel |
US10/596,781 US7806165B2 (en) | 2003-12-23 | 2004-12-22 | Method for making hot strips of lightweight construction steel |
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE10361952.6 | 2003-12-23 | ||
DE10361952 | 2003-12-23 | ||
DE102004061284A DE102004061284A1 (en) | 2003-12-23 | 2004-12-14 | Production of a deformable hot strips made from light gauge steel used in the automobile industry comprises casting the melt in a horizontal strip casting unit close to the final measurements, and further processing |
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Inventor name: FROMMEYER, GEORG, PROF. DR., 40699 ERKRATH, DE Inventor name: KROOS, JOACHIM, DR., 38527 MEINE, DE Inventor name: BRUEX, UDO, 40670 MEERBUSCH, DE Inventor name: SPITZER, KARL-HEINZ, PROF. DR., 38678 CLAUSTHA, DE Inventor name: FLAXA, VOLKER, DR., 38229 SALZGITTER, DE Inventor name: BROKMEIER, KLAUS, 47057 DUISBURG, DE |
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Effective date: 20141022 |