EP1453984B1 - Method for the production of hot strip or sheet from a micro-alloyed steel - Google Patents
Method for the production of hot strip or sheet from a micro-alloyed steel Download PDFInfo
- Publication number
- EP1453984B1 EP1453984B1 EP01270630A EP01270630A EP1453984B1 EP 1453984 B1 EP1453984 B1 EP 1453984B1 EP 01270630 A EP01270630 A EP 01270630A EP 01270630 A EP01270630 A EP 01270630A EP 1453984 B1 EP1453984 B1 EP 1453984B1
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- EP
- European Patent Office
- Prior art keywords
- temperature
- hot strip
- hot
- weight
- raw material
- 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.)
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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
- C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
Definitions
- the invention relates to a method for producing Hot strip or sheet of micro-alloyed steel.
- the hot strips are made of a steel that is in % By weight not more than 0.3% C, not more than 0.5% Si, 0.3 2.0% Mn, ⁇ 0.05% Al, 0.01-0.02% Nb, 0.01-0.2% V and optionally 0.01-0.2% Mo and 0.01-0.2% Ti, balance Contains iron and unavoidable impurities.
- This raw material produced in this steel is used in a Roll end temperature of at least 750 ° C to hot strip finish rolled, which immediately afterwards on a cooled to a maximum of 650 ° C reel temperature becomes. Subsequently, the hot strip is a final Subjected to heat treatment.
- the object of the invention is, starting from the above-explained prior art cost-effective method for producing hot strips indicate that even with larger thicknesses a high Possess strength.
- a microalloyed steel is produced which, in addition to micro-alloying elements (in% by weight) 0, 05-0.12% C, 0.2-0.5% Si, 1.5-2.2% Mn, ⁇ 0.025% P, ⁇ 0.01% S, balance iron and unavoidable impurities, to a starting material like slabs, thin slabs or blooms, potted; the starting material is heated to a temperature of 1300-1350 ° C; the heated starting material is pre-rolled at a degree of deformation of 36% to 43%; the pre-rolled starting material is thermo-mechanically hot rolled to a hot strip at a rolling end temperature above the Ac 3 temperature; the hot strip is cooled at a cooling rate of at least 15 ° C / s to a coiler temperature of at least 590 ° C and at most 630 ° C, and finally
- the inventive dimensioning of the contents of the individual alloying elements and the targeted tuning of the rolling end temperature, the cooling rate and the coiling temperature hot strips which have the highest strengths even at thicknesses of more than 8 mm.
- the yield strength is still at least 700 N / mm 2 .
- a yield strength of at least 760 N / mm 2 can be achieved.
- a supplementary heat treatment following the cooling in the coil is not required.
- the high strength of steel produced according to the invention is due to the combined use of the elimination, Fine grain and solid solution hardening achieved. there lead the selected contents of the alloying elements C and Mn to the desired solid solution hardening.
- the Precipitates of micro-alloying elements Ti, V and Nb completely dissolved.
- the at the subsequent pre-deformation set Deformations lead to a fine, even dispersed and recrystallized austenite grain.
- the excellent strength values make According to the invention produced hot strip in particular suitable for the production of load-bearing components Motor vehicles, such as heavily loaded Longitudinal beams of trucks.
- the steel contains at least one of Micro-alloying elements V, Mo, Ti, Nb in the following Held (in weight%) 0.08 - 0.12% V, 0.1 - 0.2% Mo, 0.08 - 0.11% Ti and 0.05 - 0.06% Nb.
- the Al content should be between 0.02 and 0.05% by weight.
- the micro-alloying element niobium hinders this Austenite grain. In addition, it hinders the Recrystallization of the austenite grains during the Hot rolling.
- Recrystallization during hot rolling is also avoided by hot rolling according to the invention at temperatures above the Ac 3 temperature.
- the austenite / ferrite transformation occurs during strip cooling behind the last stand of the hot rolling mill. In this way, a recrystallized, fine-grained microstructure with low Perlitan turnover is obtained.
- the ferrite grains have a size of 11 to 14 ASTM.
- the cooling rate of at least 15 ° C / s is chosen to the hot strip of the preferably at least 840 ° C hot rolling end temperature sufficient cool down to the reel temperature quickly.
- the precipitation hardness maximum by the Microalloying Ti and V and Nb achieved. This effect can be achieved particularly reliably if the reel temperature in the range of 600 ° C to 620 ° C lies.
- Hot strips whose yield strength is at least 700 N / mm 2 even with a thickness of 16 mm, can be produced particularly reliably with the method according to the invention if the steel (in weight%) is 0.06-0.08% C, 0, 2 - 0.3% Si, 1.95 - 2.1% Mn, ⁇ 0.02% P and ⁇ 0.005% S contains. In this case, if present, the Ti content should not be more than 0.1% by weight.
- hot strips whose yield strength is at least 760 N / mm 2 at a thickness of 13 mm can thereby be reliably produced by the steel (in weight%) being 0.10-0.12% C, 0 , 4 - 0.5% Si, 1.95 - 2.1% Mn, ⁇ 0.02% P, ⁇ 0.005% S.
- the steel preferably has at least one of the micro-alloying elements V, Mo, Ti, Nb in the following contents (in% by weight): 0.08-0.10% V, 0.1-0.2% Mo, 0.09 0.11% Ti, 0.05-0.06% Nb.
- the steel used in the invention can production-related or to the expression of certain Properties optionally one or more of the elements N, Cu, Ni, Sn, B or As, where the sum of the Content of these elements not more than 0.1 wt .-% is.
- the Holding time during heating of slabs at least 135 minutes to ensure a safe warmth of the To ensure starting material.
- the hot strip A emerging from the finish rolling scale was immediately after a reel temperature of 610 ° C water cooled and reeled. In the course of Water cooling were cooling rates of at least 15 ° C / s achieved.
- the emerging from the finishing roll scale hot strip B was just like the hot strip A immediately after water cooled to a reel temperature of 610 ° C and coiled. In the course of the water cooling were again Cooling speeds of 15 ° C / s achieved.
Abstract
Description
Die Erfindung betrifft ein Verfahren zum Herstellen von Warmband oder -blech aus mikrolegiertem Stahl.The invention relates to a method for producing Hot strip or sheet of micro-alloyed steel.
Aus dem Patent Abstract of Japan zur JP 61-281814 A ist ein Verfahren zum Herstellen von hochfesten Warmbändern bekannt. Die Warmbänder bestehen aus einem Stahl, der in Gewichts-% höchstens 0,3 % C, höchstens 0,5 % Si, 0,3 - 2,0 % Mn, ≤ 0,05 % Al, 0,01 - 0,02 % Nb, 0,01 - 0,2 % V sowie ggf. 0,01 - 0,2 % Mo und 0,01 - 0,2 % Ti, Rest Eisen und unvermeidbare Verunreinigungen enthält. Ein aus diesem Stahl erzeugtes Vormaterial wird bei einer Walzendtemperatur von mindestens 750 °C zu Warmband fertiggewalzt, welches unmittelbar anschließend auf eine höchstens 650 °C betragende Haspeltemperatur abgekühlt wird. Anschließend wird das Warmband einer abschließenden Wärmebehandlung unterzogen.From the Patent Abstract of Japan to JP 61-281814 A is a method for producing high-strength hot strips known. The hot strips are made of a steel that is in % By weight not more than 0.3% C, not more than 0.5% Si, 0.3 2.0% Mn, ≤ 0.05% Al, 0.01-0.02% Nb, 0.01-0.2% V and optionally 0.01-0.2% Mo and 0.01-0.2% Ti, balance Contains iron and unavoidable impurities. On off This raw material produced in this steel is used in a Roll end temperature of at least 750 ° C to hot strip finish rolled, which immediately afterwards on a cooled to a maximum of 650 ° C reel temperature becomes. Subsequently, the hot strip is a final Subjected to heat treatment.
Praktische Versuche haben ergeben, daß die Festigkeit der nach dem bekannten Verfahren erzeugten Warmbänder bei größeren Dicken von 8 mm und mehr nicht die Anforderungen erfüllt, die sich beispielsweise beim Bau von tragenden Konstruktionselementen von Kraftfahrzeug-Chassis ergeben.Practical experiments have shown that the strength of hot strips produced by the known method larger thicknesses of 8 mm and more does not meet the requirements met, for example, in the construction of load-bearing Design elements of motor vehicle chassis result.
Die Aufgabe der Erfindung besteht darin, ausgehend von dem voranstehend erläuterten Stand der Technik ein kostengünstiges Verfahren zur Herstellung von Warmbändern anzugeben, die auch bei größeren Dicken eine hohe Festigkeit besitzen.The object of the invention is, starting from the above-explained prior art cost-effective method for producing hot strips indicate that even with larger thicknesses a high Possess strength.
Diese Aufgabe wird erfindungsgemäß gelöst durch ein Verfahren gemäß Anspruch 1. Zum Herstellen von bei einer Dicke von 8 mm eine Mindeststreckgrenze von 700 N/mm2 besitzenden Warmbändern oder -blechen wird ein mikrolegierter Stahl, welcher neben Mikrolegierungselementen (in Gewichts-%) 0,05 - 0,12 % C, 0,2 - 0,5 % Si, 1,5 - 2,2 % Mn, ≤ 0,025 % P, ≤ 0,01 % S, Rest Eisen und unvermeidbare Verunreinigungen enthält, zu einem Vormaterial wie Brammen, Dünnbrammen oder Vorblöcken, vergossen; das Vormaterial wird auf eine Temperatur von 1300 - 1350 °C erwärmt; das erwärmte Vormaterial wird mit einem Verformungsgrad von 36 % bis 43 % vorgewalzt; das vorgewalzte Vormaterial wird thermomechanisch bei einer oberhalb der Ac3 -Temperatur liegenden Walzendtemperatur zu einem Warmband warmgewalzt; das Warmband wird mit einer Abkühlgeschwindigkeit von mindestens 15 °C/s auf eine mindestens 590 °C und höchstens 630 °C betragende Haspeltemperatur gekühlt und das abgekühlte Warmband schließlich gehaspelt.This object is achieved according to the invention by a method according to claim 1. For producing hot strips or sheets possessing a minimum yield strength of 700 N / mm 2 at a thickness of 8 mm, a microalloyed steel is produced which, in addition to micro-alloying elements (in% by weight) 0, 05-0.12% C, 0.2-0.5% Si, 1.5-2.2% Mn, ≤ 0.025% P, ≤ 0.01% S, balance iron and unavoidable impurities, to a starting material like slabs, thin slabs or blooms, potted; the starting material is heated to a temperature of 1300-1350 ° C; the heated starting material is pre-rolled at a degree of deformation of 36% to 43%; the pre-rolled starting material is thermo-mechanically hot rolled to a hot strip at a rolling end temperature above the Ac 3 temperature; the hot strip is cooled at a cooling rate of at least 15 ° C / s to a coiler temperature of at least 590 ° C and at most 630 ° C, and finally the cooled hot strip is coiled.
Überraschend hat sich gezeigt, daß sich durch die erfindungsgemäße Bemessung der Gehalte der einzelnen Legierungselemente und die gezielte Abstimmung der Walzendtemperatur, der Abkühlungsgeschwindigkeit und der Haspeltemperatur Warmbänder erzeugen lassen, die auch bei Dicken von mehr als 8 mm höchste Festigkeiten besitzen. So liegt bei einem erfindungsgemäß zusammengesetzten und hergestellten Warmband mit einer Dicke von 16 mm die Streckgrenze immer noch bei mindestens 700 N/mm2. Für Dicken von 13 mm läßt sich eine Streckgrenze von mindestens 760 N/mm2 erreichen. Einer ergänzenden Wärmebehandlung im Anschluß an die im Coil erfolgende Abkühlung bedarf es dazu nicht.Surprisingly, it has been shown that can be produced by the inventive dimensioning of the contents of the individual alloying elements and the targeted tuning of the rolling end temperature, the cooling rate and the coiling temperature hot strips, which have the highest strengths even at thicknesses of more than 8 mm. Thus, in a hot strip composed and manufactured according to the invention with a thickness of 16 mm, the yield strength is still at least 700 N / mm 2 . For thicknesses of 13 mm, a yield strength of at least 760 N / mm 2 can be achieved. A supplementary heat treatment following the cooling in the coil is not required.
Die hohe Festigkeit von erfindungsgemäß erzeugtem Stahl wird durch die kombinierte Anwendung der Ausscheidungs-, Feinkorn- und Mischkristallverfestigung erzielt. Dabei führen die gewählten Gehalte der Legierungselemente C und Mn zu der angestrebten Mischkristallverfestigung. Indem das Vormaterial vor dem Vorwalzen auf eine Temperatur von 1300 °C bis 1350 °C gebracht wird, werden die Ausscheidungen der Mikrolegierungselemente Ti, V und Nb vollständig in Lösung gebracht. Die bei der anschließenden Vorverformung eingestellten Verformungsgrade führen zu einem feinen, gleichmäßig verteilten und rekristallisierten Austenitkorn.The high strength of steel produced according to the invention is due to the combined use of the elimination, Fine grain and solid solution hardening achieved. there lead the selected contents of the alloying elements C and Mn to the desired solid solution hardening. By doing the raw material before roughing to a temperature of 1300 ° C is brought to 1350 ° C, the Precipitates of micro-alloying elements Ti, V and Nb completely dissolved. The at the subsequent pre-deformation set Deformations lead to a fine, even dispersed and recrystallized austenite grain.
Die hervorragenden Festigkeitswerte machen erfindungsgemäß erzeugtes Warmband insbesondere geeignet zur Herstellung von tragenden Bauelementen an Kraftfahrzeugen, wie beispielsweise stark belasteten Längsträgern von LKW.The excellent strength values make According to the invention produced hot strip in particular suitable for the production of load-bearing components Motor vehicles, such as heavily loaded Longitudinal beams of trucks.
Der Stahl enthält mindestens eines der Mikrolegierungselemente V, Mo, Ti, Nb in folgenden Gehalten (in Gewichts-%) 0,08 - 0,12 % V, 0,1 - 0,2 % Mo, 0,08 - 0,11 % Ti und 0,05 - 0,06 % Nb. Der Al-Gehalt sollte dabei zwischen 0,02 - 0,05 Gewichts-% liegen. Das Mikrolegierungselement Niob behindert das Austenitkornwachstum. Zusätzlich behindert es die Rekristallisation der Austenitkörner während des Warmwalzens.The steel contains at least one of Micro-alloying elements V, Mo, Ti, Nb in the following Held (in weight%) 0.08 - 0.12% V, 0.1 - 0.2% Mo, 0.08 - 0.11% Ti and 0.05 - 0.06% Nb. The Al content should be between 0.02 and 0.05% by weight. The The micro-alloying element niobium hinders this Austenite grain. In addition, it hinders the Recrystallization of the austenite grains during the Hot rolling.
Vermieden wird die Rekristallisation während des Warmwalzens auch dadurch, daß erfindungsgemäß bei oberhalb der Ac3-Temperatur liegenden Temperaturen warmgewalzt wird. Die Austenit/Ferrit-Umwandlung erfolgt während der Bandabkühlung hinter dem letzten Gerüst der Warmwalzfertigstraße. Auf diese Weise wird ein rekristallisiertes, feinkörniges Gefüge mit geringen Perlitanteilen erhalten. Die Ferritkörner haben dabei eine Größe von 11 bis 14 ASTM.Recrystallization during hot rolling is also avoided by hot rolling according to the invention at temperatures above the Ac 3 temperature. The austenite / ferrite transformation occurs during strip cooling behind the last stand of the hot rolling mill. In this way, a recrystallized, fine-grained microstructure with low Perlitanteilen is obtained. The ferrite grains have a size of 11 to 14 ASTM.
Die Abkühlgeschwindigkeit von mindestens 15 °C/s wird gewählt, um das Warmband von der vorzugsweise mindestens 840 °C betragenden Warmwalzendtemperatur ausreichend schnell auf die Haspeltemperatur abzukühlen. Bei der von dieser Haspeltemperatur ausgehenden Abkühlung im Coil wird das Ausscheidungshärtemaximum durch die Mikrolegierungselemente Ti und V sowie Nb erreicht. Besonders sicher läßt sich dieser Effekt erzielen, wenn die Haspeltemperatur im Bereich von 600 °C bis 620 °C liegt.The cooling rate of at least 15 ° C / s is chosen to the hot strip of the preferably at least 840 ° C hot rolling end temperature sufficient cool down to the reel temperature quickly. At the of this reel temperature outgoing cooling in the coil is the precipitation hardness maximum by the Microalloying Ti and V and Nb achieved. This effect can be achieved particularly reliably if the reel temperature in the range of 600 ° C to 620 ° C lies.
Warmbänder, deren Streckgrenze auch bei einer Dicke von 16 mm mindestens 700 N/mm2 beträgt, lassen sich bei erfindungsgemäßer Vorgehensweise dann besonders zuverlässig erzeugen, wenn der Stahl (in Gewichts-%) 0,06 - 0,08 % C, 0,2 - 0,3 % Si, 1,95 - 2,1 % Mn, ≤0,02 % P und ≤ 0,005 % S enthält. Dabei sollte, sofern vorhanden, der Ti-Gehalt nicht mehr als 0,1 Gewichts-% betragen. Hot strips, whose yield strength is at least 700 N / mm 2 even with a thickness of 16 mm, can be produced particularly reliably with the method according to the invention if the steel (in weight%) is 0.06-0.08% C, 0, 2 - 0.3% Si, 1.95 - 2.1% Mn, ≤ 0.02% P and ≤ 0.005% S contains. In this case, if present, the Ti content should not be more than 0.1% by weight.
Gemäß einer anderen Variante der Erfindung lassen sich Warmbänder, deren Streckgrenze bei einer Dicke von 13 mm mindestens 760 N/mm2 beträgt, dadurch sicher erzeugen, daß der Stahl (in Gewichts-%) 0,10 - 0,12 % C, 0,4 - 0,5 % Si, 1,95 - 2,1 % Mn, ≤ 0,02 % P, ≤ 0,005 % S enthält. Dabei weist der Stahl vorzugsweise mindestens eines der Mikrolegierungselemente V, Mo, Ti, Nb in folgenden Gehalten (in Gewichts-%) auf: 0,08 - 0,10 % V, 0,1 - 0,2 % Mo, 0,09 - 0,11 % Ti, 0,05 - 0,06 % Nb.According to another variant of the invention, hot strips whose yield strength is at least 760 N / mm 2 at a thickness of 13 mm can thereby be reliably produced by the steel (in weight%) being 0.10-0.12% C, 0 , 4 - 0.5% Si, 1.95 - 2.1% Mn, ≤ 0.02% P, ≤ 0.005% S. In this case, the steel preferably has at least one of the micro-alloying elements V, Mo, Ti, Nb in the following contents (in% by weight): 0.08-0.10% V, 0.1-0.2% Mo, 0.09 0.11% Ti, 0.05-0.06% Nb.
Der erfindungsgemäß verwendete Stahl kann herstellungsbedingt oder zur Ausprägung bestimmter Eigenschaften wahlweise eines oder mehrere der Elemente N, Cu, Ni, Sn, B oder As enthalten, wobei die Summe der Gehalte an diesen Elementen nicht mehr als 0,1 Gew.-% beträgt.The steel used in the invention can production-related or to the expression of certain Properties optionally one or more of the elements N, Cu, Ni, Sn, B or As, where the sum of the Content of these elements not more than 0.1 wt .-% is.
Werden als Vormaterial Brammen verarbeitet, so sollte die Haltezeit während der Erwärmung der Brammen mindestens 135 Minuten betragen, um eine sichere Durchwärmung des Vormaterials zu gewährleisten.If slabs are processed as starting material, then the Holding time during heating of slabs at least 135 minutes to ensure a safe warmth of the To ensure starting material.
Nachfolgend wird die Erfindung anhand von Ausführungsbeispielen erläutert:The invention is based on Embodiments explained:
Eine Stahlschmelze mit (in Gew.-%)
- C:
- 0,075 %
- Si:
- 0,254 %
- Mn:
- 2,011 %
- P:
- 0,015 %
- S:
- 0,003 %
- Al:
- 0,02 %
- N:
- 0,007 %
- Cu:
- 0,017 %
- Cr:
- 0,039 %
- Ni:
- 0,021 %
- Sn:
- 0,004 %
- V:
- 0,098 %
- Mo:
- 0,121 %
- Ti:
- 0,080 %
- Nb:
- 0,060 %
- B:
- 0,0003 %
- As:
- 0,002 %
wurde zu Brammen vergossen. Die Brammen wurden anschließend bei einer Temperatur von 1350 °C für 135 Minuten vorgewärmt und dann bei einem zwischen 36 % und 43 % liegenden Verformungsgrad auf eine Dicke von 55 mm vorgewalzt. Die vorgewalzten Brammen wurden in einer Fertigwalzstaffel auf eine Dicke von 16 mm thermomechanisch fertig warmgewalzt. Im Zuge dieses Warmwalzens wurden die Temperaturführung und Umformgrade so aufeinander abgestimmt, daß das fertig warmgewalzte Warmband A eine für den Verwendungszweck optimale Gefügestruktur aufweist. Die Walzendtemperatur betrug dabei 840 °C.A molten steel with (in% by weight)
- C:
- 0.075%
- Si:
- 0.254%
- Mn:
- 2.011%
- P:
- 0.015%
- S:
- 0.003%
- al:
- 0.02%
- N:
- 0.007%
- Cu:
- 0.017%
- Cr:
- 0.039%
- Ni:
- 0.021%
- Sn:
- 0.004%
- V:
- 0.098%
- Not a word:
- 0.121%
- Ti:
- 0.080%
- Nb:
- 0.060%
- B:
- 0,0003%
- As:
- 0.002%
was shed to slabs. The slabs were then preheated at a temperature of 1350 ° C for 135 minutes and then pre-rolled to a thickness of 55 mm with a degree of deformation between 36% and 43%. The pre-rolled slabs were hot rolled to a thickness of 16 mm thermomechanically finished in a finishing roll. In the course of this hot rolling, the temperature control and degrees of deformation were coordinated so that the finished hot-rolled hot strip A has an optimum for the intended use microstructure. The rolling end temperature was 840 ° C.
Das aus der Fertigwalzstaffel austretende Warmband A wurde unmittelbar anschließend auf eine Haspeltemperatur von 610 °C wassergekühlt und gehaspelt. Im Zuge der Wasserkühlung wurden Abkühlgeschwindigkeiten von mindestens 15 °C/s erzielt. The hot strip A emerging from the finish rolling scale was immediately after a reel temperature of 610 ° C water cooled and reeled. In the course of Water cooling were cooling rates of at least 15 ° C / s achieved.
An aus dem derart erzeugten Warmband A gewonnenen Proben
A1 - A8 wurden Zugversuche durchgeführt, deren Ergebnisse
in Tabelle 1 angegeben sind:
An Proben A9 - A12 des Warmbands wurden darüber hinaus
Kerbschlagbiegeversuche durchgeführt. Deren Ergebnisse
sind in Tabelle 2 angegeben:
Eine aus (in Gew.-%)
- C:
- 0,115 %
- Si:
- 0,449 %
- Mn:
- 1,988 %
- P:
- 0,019 %
- S:
- 0,003 %
- Al:
- 0,03 %
- N:
- 0,007 %
- Cu:
- 0,017 %
- Cr:
- 0,037 %
- Ni:
- 0, 02 %
- Sn:
- 0,003 %
- V:
- 0,092 %
- Mo:
- 0,108 %
- Ti:
- 0,101 %
- Nb:
- 0,055 %
- B:
- 0,0003 %
- As:
- 0,003 %
zusammengesetzte Stahlschmelze wurde zu Brammen vergossen. Die Brammen wurden wie beim Beispiel des Warmbands A bei einer Temperatur von 1350 °C für 135 Minuten vorgewärmt, anschließend auf eine Dicke von 55 mm vorgewalzt und in einer Fertigwalzstaffel bei einer Walzendtemperatur von 840 °C warmgewalzt. Die Dicke des fertig gewalzten Warmbandes betrug 13 mm.One out of (in% by weight)
- C:
- 0,115%
- Si:
- 0.449%
- Mn:
- 1,988%
- P:
- 0.019%
- S:
- 0.003%
- al:
- 0.03%
- N:
- 0.007%
- Cu:
- 0.017%
- Cr:
- 0.037%
- Ni:
- 0, 02%
- Sn:
- 0.003%
- V:
- 0.092%
- Not a word:
- 0.108%
- Ti:
- 0.101%
- Nb:
- 0.055%
- B:
- 0,0003%
- As:
- 0.003%
composite molten steel was poured into slabs. The slabs were preheated as in the example of the hot strip A at a temperature of 1350 ° C for 135 minutes, then pre-rolled to a thickness of 55 mm and hot rolled in a finishing roll at a rolling finish temperature of 840 ° C. The thickness of the finished rolled hot strip was 13 mm.
Das aus der Fertigwalzstaffel austretende Warmband B wurde ebenso wie das Warmband A unmittelbar anschließend auf eine Haspeltemperatur von 610 °C wassergekühlt und gehaspelt. Im Zuge der Wasserkühlung wurden wiederum Abkühlgeschwindigkeiten von 15 °C/s erzielt.The emerging from the finishing roll scale hot strip B was just like the hot strip A immediately after water cooled to a reel temperature of 610 ° C and coiled. In the course of the water cooling were again Cooling speeds of 15 ° C / s achieved.
An aus dem derart erzeugten Warmband B gewonnenen Proben
B1 - B8 wurden Zugversuche durchgeführt, deren Ergebnisse
in Tabelle 3 angegeben sind:
Die Ergebnisse der an Proben B9 - B12 des Warmbands B
ebenfalls durchgeführten Kerbschlagbiegeversuche sind in
Tabelle 4 angegeben:
Die durchgeführten Versuche bestätigten klar die hervorragenden mechanischen Eigenschaften der erfindungsgemäß erzeugten Warmbänder A, B.The tests clearly confirmed that excellent mechanical properties of the hot strips A, B produced according to the invention.
Claims (10)
- A method for producing hot strip or hot platein which a microalloyed steel which, apart from at least one of the microalloying elements V, Mo, Ti, Nb in the following contents (in weight %) V: 0,08 - 0,12 %, Mo: 0,1 - 0,2 %, Ti: 0,08 - 0,11 %, Nb: 0,05 - 0,06 % comprises the following elements (in weight %)
- C:
- 0.05 - 0.12 %;
- Si:
- 0.2 - 0.5 %;
- Mn:
- 1.5 - 2.2 %;
- Al:
- 0.02 - 0.05 %;
- P:
- ≤ 0.025 %;
- S:
- ≤ 0.01 %
in which the raw material is heated to a temperature of 1300 - 1350 °C;in which the heated raw material is rough rolled at a degree of deformation of 36 % to 43 %;in which the rough rolled raw material is thermomechanically hot rolled at a finish roll temperature which exceeds the Ac3 temperature so as to form a hot strip;in which the hot strip is cooled at a cooling rate of at least 15 °C/s to a coiling temperature of at least 590 °C and at most 630 °C;at which temperature the cooled hot strip is finally coiled. - The method according to claim 1, characterised in that at a thickness exceeding 8 mm, the hot strip or hot plate has a minimum yield point of 700 N/mm2.
- The method according to one of claims 1 or 2, characterised in that the steel comprises (in weight %):
- C:
- 0.06 - 0.08 %;
- Si:
- 0.2 - 0.3 %;
- Mn:
- 1.95 - 2.1 %;
- Al:
- 0.02 - 0.05 %;
- P:
- ≤ 0.02 %;
- S:
- ≤ 0.005 %.
- The method according to claim 3, characterised in that the Ti content does not exceed 0.1 weight %.
- The method according to any one of claims 1 or 2, characterised in that the steel comprises (in weight %):
- C:
- 0.10 - 0.12 %;
- Si:
- 0.4 - 0.5 %;
- Mn:
- 1.95 - 2.1 %;
- Al:
- 0.02 - 0.05 %;
- S:
- ≤ 0.005 %.
- The method according to claim 5, characterised in that the steel comprises at least one of the microalloying elements V, Mo, Ti, Nb in the following percentages (in weight %):
- V:
- 0.08 - 0.10 %;
- Mo:
- 0.1 - 0.2 %;
- Ti:
- 0.09 - 0.11 %;
- Nb:
- 0.05 - 0.06 %.
- The method according to claim 5 or 6, characterised in that at a thickness of 13 mm, the hot strip or hot plate has a minimum yield point of 760 N/mm2.
- The method according to any one of the preceding claims, characterised in that slabs are used as raw material, with the holding time during heating of the slabs being at least 135 minutes.
- The method according to any one of the preceding claims, characterised in that the final rolling temperature is at least 840 °C.
- The method according to any one of the preceding claims, characterised in that the coiling temperature is at least 600 °C and at most 620 °C.
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE10062919 | 2000-12-16 | ||
DE10062919A DE10062919A1 (en) | 2000-12-16 | 2000-12-16 | Process for producing hot strip or sheet from a microalloyed steel |
PCT/EP2001/014829 WO2002048410A1 (en) | 2000-12-16 | 2001-12-15 | Method for the production of hot strip or sheet from a micro-alloyed steel |
Publications (3)
Publication Number | Publication Date |
---|---|
EP1453984A1 EP1453984A1 (en) | 2004-09-08 |
EP1453984B1 true EP1453984B1 (en) | 2005-04-13 |
EP1453984B8 EP1453984B8 (en) | 2005-07-27 |
Family
ID=7667534
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP01270630A Expired - Lifetime EP1453984B8 (en) | 2000-12-16 | 2001-12-15 | Method for the production of hot strip or sheet from a micro-alloyed steel |
Country Status (6)
Country | Link |
---|---|
US (1) | US20040040633A1 (en) |
EP (1) | EP1453984B8 (en) |
AT (1) | ATE293175T1 (en) |
DE (2) | DE10062919A1 (en) |
ES (1) | ES2240337T3 (en) |
WO (1) | WO2002048410A1 (en) |
Families Citing this family (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1396550A1 (en) * | 2002-08-28 | 2004-03-10 | ThyssenKrupp Stahl AG | Method for manufacturing hot strip |
ES2325962T3 (en) * | 2006-10-30 | 2009-09-25 | Thyssenkrupp Steel Ag | PROCEDURE FOR MANUFACTURING STEEL FLAT PRODUCTS FROM A MICROALEATED MULTIPHASIC STEEL WITH BORO. |
DE502006003830D1 (en) * | 2006-10-30 | 2009-07-09 | Thyssenkrupp Steel Ag | A method for producing steel flat products from a complex phase structure forming steel |
FI20095528A (en) * | 2009-05-11 | 2010-11-12 | Rautaruukki Oyj | Process for producing a hot rolled strip steel product and hot rolled strip steel product |
FI122143B (en) * | 2009-10-23 | 2011-09-15 | Rautaruukki Oyj | Procedure for the manufacture of a high-strength galvanized profile product and profile product |
JP5365673B2 (en) * | 2011-09-29 | 2013-12-11 | Jfeスチール株式会社 | Hot rolled steel sheet with excellent material uniformity and method for producing the same |
JP5578288B2 (en) | 2012-01-31 | 2014-08-27 | Jfeスチール株式会社 | Hot-rolled steel sheet for generator rim and manufacturing method thereof |
MX2017008027A (en) | 2014-12-19 | 2017-10-20 | Nucor Corp | Hot rolled light-gauge martensitic steel sheet and method for making the same. |
CN111519105B (en) * | 2020-05-12 | 2021-06-15 | 首钢集团有限公司 | Automobile component steel, preparation method thereof and automobile component |
Family Cites Families (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE2133744B2 (en) * | 1971-07-07 | 1973-07-12 | August Thyssen-Hütte AG, 4100 Duisburg | THE USE OF A FULLY KILLED STEEL FOR ARTICLES FROM HOT-ROLLED STRIP |
IT1002387B (en) * | 1972-12-31 | 1976-05-20 | Nippon Steel Corp | PROCEDURE FOR MANUFACTURING STEEL SHEETS FOR CONSTRUCTION WITH HIGH BREAKING LOAD |
JPS58136719A (en) * | 1982-02-05 | 1983-08-13 | Nippon Kokan Kk <Nkk> | Manufacture of high strength hot rolled steel plate |
JPS61281814A (en) * | 1985-06-06 | 1986-12-12 | Kobe Steel Ltd | Production of high-strength hot rolled steel sheet having low sensitivity to bauschinger effect |
JPS63223130A (en) * | 1987-03-13 | 1988-09-16 | Kawasaki Steel Corp | Manufacture of high-tensile hot-rolled steel plate excellent in workability |
JPH059572A (en) * | 1991-07-08 | 1993-01-19 | Sumitomo Metal Ind Ltd | Production of hot rolled steel plate excellent in workability |
FR2688009B1 (en) * | 1992-02-28 | 1994-05-27 | Lorraine Laminage | PROCESS FOR THE PREPARATION OF A STEEL SHEET AND STEEL SHEET OBTAINED BY THIS PROCESS. |
JP3767132B2 (en) * | 1997-11-11 | 2006-04-19 | Jfeスチール株式会社 | Method for producing high-strength hot-rolled steel sheet having high ductility and excellent material uniformity |
-
2000
- 2000-12-16 DE DE10062919A patent/DE10062919A1/en not_active Withdrawn
-
2001
- 2001-12-15 US US10/398,795 patent/US20040040633A1/en not_active Abandoned
- 2001-12-15 WO PCT/EP2001/014829 patent/WO2002048410A1/en active IP Right Grant
- 2001-12-15 ES ES01270630T patent/ES2240337T3/en not_active Expired - Lifetime
- 2001-12-15 EP EP01270630A patent/EP1453984B8/en not_active Expired - Lifetime
- 2001-12-15 DE DE50105924T patent/DE50105924D1/en not_active Expired - Lifetime
- 2001-12-15 AT AT01270630T patent/ATE293175T1/en active
Also Published As
Publication number | Publication date |
---|---|
EP1453984B8 (en) | 2005-07-27 |
ATE293175T1 (en) | 2005-04-15 |
EP1453984A1 (en) | 2004-09-08 |
WO2002048410A1 (en) | 2002-06-20 |
DE50105924D1 (en) | 2005-05-19 |
US20040040633A1 (en) | 2004-03-04 |
DE10062919A1 (en) | 2002-06-27 |
ES2240337T3 (en) | 2005-10-16 |
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