EP1070148B1 - Verfahren zum herstellen eines warmgewalzten stahlbleches zum tiefziehen - Google Patents

Verfahren zum herstellen eines warmgewalzten stahlbleches zum tiefziehen Download PDF

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Publication number
EP1070148B1
EP1070148B1 EP00900991A EP00900991A EP1070148B1 EP 1070148 B1 EP1070148 B1 EP 1070148B1 EP 00900991 A EP00900991 A EP 00900991A EP 00900991 A EP00900991 A EP 00900991A EP 1070148 B1 EP1070148 B1 EP 1070148B1
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EP
European Patent Office
Prior art keywords
steel
temperature
rolling
ferritic
hot
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Expired - Lifetime
Application number
EP00900991A
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English (en)
French (fr)
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EP1070148A1 (de
Inventor
Annick De Paepe
Jean-Claude Herman
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Centre de Recherches Metallurgiques CRM ASBL
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Centre de Recherches Metallurgiques CRM ASBL
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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
    • 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
    • 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
    • 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
    • C21D8/0431—Warm rolling

Definitions

  • the present invention relates to a method of manufacturing a hot-rolled steel strip for stamping.
  • the steel strips for stamping operations are generally cold rolled steel strips, which have very favorable properties in this respect.
  • the manufacture of these cold bands includes various thickness reduction and heat treatment operations that increase the cost.
  • steels for stamping are mild steels, that is to say steels whose carbon content is less than 0.2% by weight, and preferably less than 0.1%. in weight.
  • the mild steels are hot-rolled in the austenitic range and the end-of-rolling temperature is higher than the transformation temperature Ar 3.
  • the possibilities of using these conventional hot runners are very limited because of their random texture and poor stamping ability.
  • the rough rolling is carried out in the austenitic field, while the Finishing rolling is done in the ferritic field, ie at lower temperature.
  • the Finishing rolling is done in the ferritic field, ie at lower temperature.
  • DE-A-196 00 990 a finishing lamination is possible for ULC, ELC or IF steels in the austenitic and ferritic domains.
  • ferritic rolling must be carried out at a sufficiently low temperature to prevent recrystallization in the finishing mill. Higher rolling forces in a low temperature rolling mill can therefore be a limiting factor for rolling hot thin strips.
  • Hot-rolled thin tapes made of ferrite-lined Ti + S-IF steel and recrystallized, with increased titanium and sulfur contents, have a high Lankford coefficient, with r ⁇ 1.6-1.7 , but their planar anisotropy remains too important ( ⁇ r ⁇ 1) to allow deep drawing.
  • the present invention provides a method of manufacturing a hot rolled steel strip having a reduced titanium content and an improved drawing ability compared to the steel strips discussed in the introduction.
  • a hot-rolled steel strip produced by the process of the invention is distinguished in particular by an improved anisotropy coefficient (r average ) and a planar anisotropy ( ⁇ r) significantly reduced compared to the state of the art.
  • a method of manufacturing a hot-rolled steel strip for stamping in which a steel slab is subjected to a coating at a temperature greater than Ac 3 in the area of austenitic and subsequently to finishing rolling, is characterized in that the steel is a Ti-IF type steel containing less than 0.05% by weight of titanium and 0.015% to 0.075% by weight of niobium, in that said finishing rolling is carried out at least partly in the ferritic range of the steel, with a ferritic rolling start temperature of between 875 ° C and 800 ° C, with lubricated rolls and with a reduction ratio of at least 80% thickness during said finishing rolling in the ferritic range, and in that the steel strip is reeled at a temperature of between 750 ° C and 500 ° C.
  • winding in the temperature range between 680 ° C and 750 ° C makes it possible to produce a recrystallized hot strip and for direct application in stamping. Winding between 500 ° C and 680 ° C leads to the formation of a non-recrystallized strip which requires a recrystallization treatment in a continuous annealing or galvanizing line.
  • said finishing rolling is carried out partly in the low-temperature region of the austenitic domain of the steel, without lubrication of the rolls and with a thickness reduction ratio greater than or equal to 30%, preferably included between 30% and 80%, and partly in the ferritic field of steel, with lubricated cylinders and with a ferritic rolling start temperature of between 860 ° C and 800 ° C and a ferritic end-of-rolling temperature included between 750 ° C and 600 ° C, said strip is reeled at a temperature between 650 ° C and 500 ° C and annealed continuously at a temperature between 800 ° C and 850 ° C for a time between 30 seconds and 2 minutes.
  • an ester-based oil is preferably used.
  • the process of the invention is directed to Ti-IF steels, in which the titanium is partially replaced by niobium. It has indeed been observed that the precipitation of niobium carbide (NbC) began at increasing temperatures, in the austenitic domain, when the niobium content increases in the steel. As a result, the carbon in solution is almost completely fixed before the beginning of the deformation in the ferritic domain. It is thus possible to obtain a final product, that is to say a hot rolled strip, which has a substantially continuous tensile curve and which therefore lends itself remarkably to deep drawing.
  • NbC niobium carbide
  • niobium delays recrystallization between the rolling mill stands in the ferritic range.
  • the inlet temperature in the finishing mill may therefore be higher than in prior practice and thus reach a value of 850 ° C to 875 ° C as mentioned above.
  • the rolling forces can thus be lower in the finishing mill; likewise, the waiting time between the roughing mill and the finishing mill can be shortened, in favor of an increase in productivity. This waiting time can also be completely eliminated by applying accelerated cooling of the product to the output of the roughing mill.
  • FIG. 1 shows the comparative evolution of the value of the coefficient r for a conventional Ti + S-IF steel and two Ti + Nb-IF steels according to the invention.
  • the products were heated to 1050 ° C and then hot rolled in six passes to a final thickness of 1.3 mm. During this finishing lamination, the first three passes were made in the region of low temperatures of the austenitic domain, that is to say at temperatures slightly higher than Ac3, with a thickness reduction ratio of 73. % and without lubrication of the cylinders.
  • the other three passes were made in the ferritic field, with cylinders lubricated with an ester-based oil.
  • the product temperature at the inlet of the first ferritic rolling pass was about 840 ° C and the outlet temperature of the last pass was about 620 ° C.
  • the strip was coiled at 500 ° C and then continuously annealed at 820 ° C for 60 seconds.
  • FIG. 1 illustrates this evolution for the three steels of Table 1, as a function of the angle ⁇ with respect to the rolling direction.
  • an Nb + Ti-IF1 steel slab was manufactured, which was heated at high temperature, ie 1250 ° C., and then the rough-rolling was carried out at high temperature in the field. austenitic.
  • the product having a thickness of 20 mm, was cooled from its roughing end-milling temperature of 1040 ° C. to a temperature of 900 ° C., with a cooling rate of about 40 ° C. C / s.
  • the finishing rolling was carried out in four passes in the ferritic range, with an inlet temperature of 870 ° C, with lubricated cylinders and with a total reduction of thickness, in the ferrite, of 80%.
  • the strip was cooled in calm air and then wound at 730 ° C.
  • Curve 4 of FIG. 1 shows the evolution of the coefficient of anisotropy r; there is still a slight improvement in the average coefficient r, as well as in the planar anisotropy ⁇ r, with respect to curve 3.
  • the method of the invention makes hot rolled steel strip for stamping, which have little risk of surface defects, due to a low titanium content.
  • the presence of niobium substantially raises the temperature of non-recrystallization in the austenite. This results in a finer grain structure after allotropic austenite-ferrite transformation and, hence, an improvement in planar anisotropy.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)
  • Metal Rolling (AREA)

Claims (3)

  1. Herstellungsverfahren für ein warmgewalztes Stahlband zum Tiefziehen, wobei der besagte Stahl ein Stahl vom Typ Ti-IF ist, der weniger als 0,05 Gewichts-% Titan und 0,015-0,075 Gewichts-% Niob enthält, bei dem eine Stahlbramme bei einer höheren Temperatur als Ac3 zuerst im Austenitgebiet vorgewalzt und dann auf Enddicke gewalzt wird, gekennzeichnet durch folgende, aufeinanderfolgende Phasen:
    - nach dem Vorwalzen im Austenitgebiet des Stahls wird der Stahl beim Austritt aus dem Vorwalzwerk einer beschleunigten Abkühlung bis auf eine Temperatur, die nicht unter der Anfangstemperatur für das Endwalzen liegt, unterzogen,
    - das besagte Endwalzen wird teilweise im unteren Temperaturbereich des Austenitgebiets des Stahls ohne Schmierung der Zylinder durchgeführt, und teilweise im Ferritgebiet des Stahls mit geschmierten Zylindern, bei einer Anfangstemperatur des Ferritwalzens zwischen 875°C und 800°C, und mit einem Gesamtgrad der Dickenreduktion von mindestens 80%, und
    - das Stahlband wird bei einer Temperatur zwischen 750°C und 500°C aufgewickelt.
  2. Verfahren nach Anspruch 1, dadurch gekennzeichnet, dass:
    - das besagte Endwalzen teilweise im unteren Temperaturbereich des Austenitgebiets des Stahls mit einem Gesamtgrad der Dickenreduktion von 30% bis 80% durchgeführt wird;
    - das besagte Endwalzen teilweise im Ferritgebiet des Stahls bei einer Anfangstemperatur des Ferritwalzens zwischen 860°C und 800°C und einer Endtemperatur des Ferritwalzens zwischen 750°C und 600°C durchgeführt wird,
    - das besagte Band dann bei einer Temperatur zwischen 650°C und 500°C aufgewickelt wird und
    - das Band im Durchlaufverfahren bei einer Temperatur zwischen 800°C und 850°C für eine Dauer von 30 Sekunden bis 2 Minuten geglüht wird.
  3. Verfahren nach Anspruch 1 oder 2, dadurch gekennzeichnet, dass die Schmierung der Zylinder während des Walzens im Ferritgebiet des Stahls mit einem Öl auf Esterbasis durchgeführt wird.
EP00900991A 1999-02-05 2000-01-24 Verfahren zum herstellen eines warmgewalzten stahlbleches zum tiefziehen Expired - Lifetime EP1070148B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
BE9900078A BE1012462A3 (fr) 1999-02-05 1999-02-05 Procede de fabrication d'une bande d'acier laminee a chaud pour emboutissage.
BE9900078 1999-02-05
PCT/BE2000/000007 WO2000046411A1 (fr) 1999-02-05 2000-01-24 Procede de fabrication d'une bande d'acier laminee a chaud pour emboutissage

Publications (2)

Publication Number Publication Date
EP1070148A1 EP1070148A1 (de) 2001-01-24
EP1070148B1 true EP1070148B1 (de) 2006-06-21

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EP00900991A Expired - Lifetime EP1070148B1 (de) 1999-02-05 2000-01-24 Verfahren zum herstellen eines warmgewalzten stahlbleches zum tiefziehen

Country Status (6)

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EP (1) EP1070148B1 (de)
AU (1) AU2086900A (de)
BE (1) BE1012462A3 (de)
DE (1) DE60028875T2 (de)
ES (1) ES2265908T3 (de)
WO (1) WO2000046411A1 (de)

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
AT509707B1 (de) * 2010-05-04 2011-11-15 Siemens Vai Metals Tech Gmbh Verfahren zum warmwalzen von stahlbändern und warmwalzstrasse
CN106834906B (zh) * 2017-01-10 2019-04-12 首钢京唐钢铁联合有限责任公司 超低碳钢的生产方法

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
LU86509A1 (fr) * 1986-07-10 1988-02-02 Centre Rech Metallurgique Aciers pour laminage de bandes a basse temperature
BE1002093A6 (fr) * 1988-07-11 1990-06-26 Centre Rech Metallurgique Procede de fabrication d'une bande mince en acier par laminage a chaud.
US4973367A (en) * 1988-12-28 1990-11-27 Kawasaki Steel Corporation Method of manufacturing steel sheet having excellent deep-drawability
US5200005A (en) * 1991-02-08 1993-04-06 Mcgill University Interstitial free steels and method thereof
DE19600990C2 (de) * 1996-01-14 1997-12-18 Thyssen Stahl Ag Verfahren zum Warmwalzen von Stahlbändern
BE1010164A6 (fr) * 1996-05-13 1998-02-03 Centre Rech Metallurgique Procede pour la fabrication d'une bande mince d'emboutissage en acier doux lamine a chaud.

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Publication number Publication date
DE60028875T2 (de) 2006-11-30
EP1070148A1 (de) 2001-01-24
WO2000046411A1 (fr) 2000-08-10
BE1012462A3 (fr) 2000-11-07
AU2086900A (en) 2000-08-25
ES2265908T3 (es) 2007-03-01
DE60028875D1 (de) 2006-08-03

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