EP1225235A2 - Procédé de fabrication d'une bande ou tôle d'acier laminée à froid et bande ou tôle pouvant être obtenue par ce procédé - Google Patents

Procédé de fabrication d'une bande ou tôle d'acier laminée à froid et bande ou tôle pouvant être obtenue par ce procédé Download PDF

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Publication number
EP1225235A2
EP1225235A2 EP02000584A EP02000584A EP1225235A2 EP 1225235 A2 EP1225235 A2 EP 1225235A2 EP 02000584 A EP02000584 A EP 02000584A EP 02000584 A EP02000584 A EP 02000584A EP 1225235 A2 EP1225235 A2 EP 1225235A2
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EP
European Patent Office
Prior art keywords
sheet
strip
annealing
steel
temperature
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.)
Granted
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EP02000584A
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German (de)
English (en)
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EP1225235A3 (fr
EP1225235B1 (fr
Inventor
Klaus Dr.-Ing Freier
Volker Dr.-Ing. Flaxa
Birgit Dr.-Ing. Reichert
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Salzgitter AG
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Salzgitter AG
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Publication date
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Publication of EP1225235A2 publication Critical patent/EP1225235A2/fr
Publication of EP1225235A3 publication Critical patent/EP1225235A3/fr
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Publication of EP1225235B1 publication Critical patent/EP1225235B1/fr
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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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • 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
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/663—Bell-type furnaces

Definitions

  • the invention relates to a method for producing a cold-rolled, easily deformable Strip or sheet of steel after hot rolling, reeling and cold rolling a recrystallizing annealing and optionally a skin pass process is subjected and a bake hardening potential after a subsequent one Has deformation for a subsequent heat treatment.
  • the invention further relates to a readily deformable, cold-rolled strip or sheet which can be produced by the process and has a bake hardening potential after a subsequent deformation and for a subsequent temperature treatment (BH 2 potential).
  • BH 2 potential bake hardening potential after a subsequent deformation and for a subsequent temperature treatment
  • Such steel sheets are generally in the form of a Band made by casting a steel slab, hot rolled and at a certain intermediate temperature is coiled. After cooling the coiled At essentially ambient temperature, the sheet is placed on the strip Cold rolled final thickness. To remove the resulting tensions within the material is recrystallized annealing. Subsequently the band generally becomes weak again with a degree of deformation between about 0.5 and 2% rolled (skin pass).
  • the easy deformability of the steels means an increase in the strength values of the Steel type in principle, because the increased strength in principle with an impairment easy deformability goes hand in hand.
  • They are high-strength steel grades have been developed (e.g. ZStE and ZStEi), despite higher strength values are relatively easily deformable.
  • Such steel grades are, for example, a ZStE steel iron material sheet SEW093 and 094 and known as Isotropic Steel ZStEi while the conventional "soft" steel grades as St12 to St15 (corresponding DC01, DC03, DC04, DC05 according to DIN EN 10130) are known.
  • the steel types differ in the addition of microalloying elements and with regard to the conduct of the procedure.
  • a special steel of this type is, for example the isotropic steel ZstEi, as described in DE 38 03 064 C2, EP 0 400 031 B1 or DD 285 298 B5, the disclosure of which is incorporated in this description is described.
  • the bake hardening effect has the effect that hardening, that is to say increasing the yield strength, is brought about when the steel is subjected to temperature treatment, for example when stove-enamelling of body panels. It is an artificial aging of the steel, which causes the additional strength increase. The increase in strength is thus achieved after the sheet metal has been deformed to produce the desired component, so that the increase in strength does not interfere with the sheet metal deformation. It has been found that the previous deformation of the sheet affects the bake hardening effect.
  • the bake hardening effect caused only by the heat treatment without prior deformation is given as the BH 0 value, while a measure of the bake hardening effect after the deformation has been carried out is the BH 2 value after a deformation of the sheet 2% indicates the increase in strength due to a subsequent temperature treatment - standardized at 170 ° C for 20 minutes.
  • the bake hardening effect is based on a content of dissolved carbon in the steel that is above the equilibrium state.
  • the recrystallization annealing is carried out after the cold rolling with a continuous annealing.
  • carbon goes into solution.
  • the sheet is heated for a short time, a significantly higher than A 1 lying temperature is used for the recrystallization.
  • the proportion of dissolved carbon atoms that is several orders of magnitude above the equilibrium state arises.
  • the steel strip remains in equilibrium, so that there is no aging potential (bake hardening potential) if the carbon content ⁇ 0.02%.
  • An aging potential can only be created at lower carbon contents, which can only be adjusted by means of a complex vacuum treatment, since the C atoms in solution are difficult to remove iron carbide (cementite) due to their low density and the associated longer diffusion paths, and therefore occur Part remains saturated in solution.
  • C contents ⁇ 0.02% the carbon is excreted during slow cooling, so that no dissolved carbon is available for the aging potential.
  • the heat treatment diffuses the carbon atoms in the solution into dislocation areas of the matrix. This dislocates the dislocations, so that an increased amount of stress is required to generate a plastic flow in the material again.
  • This effect is considerably increased by a previous deformation of the steel strip, which is oversaturated with dissolved C.
  • the deformation process for example by deep drawing, leads to a significant increase in the dislocation density.
  • the carbon atoms diffuse into the dilated areas of the dislocations.
  • the bake hardening effect after a previous deformation characterized by BH 2
  • BH 2 bake hardening effect after a previous deformation
  • the forming of the sheets leads to one Strain hardening (work hardening).
  • work hardening steels For the application of bake hardening steels is the total strength resulting from the cold forming through the forming and Bake hardening results from the heat treatment, relevant.
  • the well-known bake hardening steels, which are produced with a continuous annealing have the degree of pre-stretch as a variable has an almost constant yield point for the sum of work hardening and bake hardening.
  • the bake hardening effect is therefore due to the vast majority at larger strains Share of work hardening hardly relevant. It is therefore known that the application of bake hardening steels mainly of interest for large components that are only weakly formed, such as fenders, bonnets, Car doors and roofs.
  • the invention is therefore based on the problem of producing tapes or steel sheets of the type mentioned at the outset with a bake hardening potential to enable that does not have the conventional restrictions.
  • a method of the type mentioned at the outset is characterized in that the recrystallizing annealing is carried out in a hood furnace in the collar and that the strip or sheet after the recrystallizing annealing has a temperature T of 200 ° C. ⁇ T ⁇ A 1 Cooling is subjected to a cooling rate ⁇ 1 ° C / s.
  • This method according to the invention thus allows the production of a bake hardening steel strip or sheet, which in a hood furnace, preferably in Fixed bond, has been recrystallized annealed, even if the C content in the steel is ⁇ 0.02%.
  • the short-time annealing according to the invention after cooling the recrystallized annealed strip or sheet to ⁇ 150 ° C., preferably to about room temperature, makes it possible to bring C which has been eliminated as carbides back into solution. Since the temperature of the brief annealing is below the A 1 temperature of the steel, this annealing does not significantly change the technological properties of the steel, in particular its texture. Due to the brief annealing and the subsequent cooling, which can be carried out in the usual way with air, but also with water, part of the dissolved C remains in solution and leads to the aging potential for the subsequent temperature treatment, for example during a stove enamelling.
  • the brief annealing is preferably effected in a continuous annealing furnace.
  • a sufficient bake hardening effect must be at a low one Annealing temperature T can be maintained during a relatively long annealing period higher annealing temperatures significantly reduce the required annealing time. It is therefore preferred to use a temperature T of brief glow ⁇ 450 ° C. It is further preferred that the glow duration of the brief glow between 2 Min. And 5 min.
  • the method according to the invention can also for not at all or electrolytically, i.e. without exposure to heat, to be galvanized Sheets are used.
  • the strip or sheet produced by the process according to the invention differs different from conventional strips or sheets with a bake hardening potential in that the total hardening of the steel (work hardening + bake hardening) increases with greater previous deformation of the sheet.
  • the steel according to the invention contains cementite precipitates in the matrix and on the grain boundaries. Conventional, continuously annealed bake hardening steels are practically free of cementite. If these steels are subjected to an aging treatment, Cementite forms, but with loss of the bake hardening effect. In contrast, the steel according to the invention has cementite precipitates and a bake hardening effect. This also applies if the steel has a C content ⁇ 0.02%. After the stove-enamelling, the sheet shows through the bake hardening effect clearly, i.e. by at least 15 MPa, preferably by at least 30 MPa, increased yield strength.
  • the steel according to the invention can have any analyzes that are suitable for easily deformable, cold rolled strips or sheets are known.
  • the invention Strip or sheet can therefore be made from steel of the steel types St12 to St15, ZStE or ZStEi.
  • the steel according to the invention can have a hot-dip galvanized surface and have been trained after hot-dip galvanizing.
  • the brief annealing according to the invention can be carried out at a constant temperature over the annealing time, but also with different annealing temperatures during the annealing time.
  • the "soft" grades St15 and St14 have no relevant amounts of microalloying elements (Ti, V, Nb, Mo).
  • the isotropic steel grade ZSt220 characterized by a titanium content that is between 0.01 and 0.04% may lie and is set to about 0.02% in the experimental examples.
  • the higher strength Grade ZSt340 has a similar titanium content and also one clear niobium content.
  • All steel grades used are in the usual way at the required temperatures poured into the slab and then hot rolled. After one Reeling at a suitable intermediate temperature is carried out in air Service. The cold rolling steps were then carried out. The steel strip was then subjected to recrystallization annealing in the hood furnace, whereby the usual annealing time is between 20 and 70 hours.
  • the steel strip cooled to about room temperature, was used for the tests carried out here in part, and in part undressed, before the short-time annealing according to the invention is carried out, preferably in a continuous furnace.
  • the material has been pre-stretched.
  • the cooled material is trained after the brief annealing Service.
  • FIG. 1 shows the measurement results for the BH 2 effect for the steel St15 as a function of the annealing temperature and the annealing duration, which was set at 0.5 min., 2 min. And 5 min.
  • the samples that were not trained before the annealing were referred to as "1 x trained" because of the dressing after the annealing, and the pre-addressed samples as "2 x trained”.
  • Figure 2 shows the results for the same tests on the steel ZStE220i.
  • a very large BH 2 effect is achieved at an annealing temperature of 700 ° C and an annealing time of 2 minutes. Extending the annealing time at this temperature leads to a reduction in the BH 2 effect.
  • dressing before the premature glow is rather harmful for the size of the BH 2 effect.
  • the results for the steel grade ZStE340 shown in FIG. 3 clarify that in this case, the skin pass before the short-term annealing is favorable, at least for medium annealing temperatures. At the low annealing temperature of 200 ° C a maximum is formed at the annealing temperature of 2 minutes for the 1 x trained steel. For shorter and longer glow times, the BH 2 effect even goes back to O.
  • Figures 4 to 6 illustrate the dependence of the BH value on the degree of prior stretching of the material. In all cases there is a more or less distinct maximum at about 2% degree of stretching, while conventional bake hardening steels have a BH value that decreases with increasing degree of stretching.
  • FIG. 4 shows the results for undressed samples of the grades ZSt220i, St14 and ZSt340, which were annealed at 500 ° C. for 5 minutes and deformed between 0.5 and 1% during dressing, depending on the steel grade.
  • the bake hardening annealing took place according to the test regulations at 170 ° for 20 minutes.
  • results shown in FIG. 5 relate to the same steels with the same degree of skin pass, but the short-term annealing at 500 ° C. has been carried out for an annealing period of 15 minutes.
  • the results shown in FIG. 6 relate to the steel grades treated in the same way, which were annealed at 700 ° C. for 5 minutes. What is striking is the high bake hardening potential for the isotropic steel grade ZStE220i, which has been pre-stretched with a degree of deformation between 2 and 3%.
  • FIG. 7 shows the sum of the deformation hardening (work hardening WH) and the bake hardening hardening (BH) as a function of the degree of stretching for the three steel grades. While conventional bake hardening steel grades show a substantially constant sum of the yield strength increase over the different degrees of stretching, the steel grades according to the invention have a yield strength increase that increases with the degree of stretching. The steels treated according to the invention therefore differ in their mechanical properties from the conventionally produced bake hardening steels.
  • FIGS. 8 to 10 illustrate the course of the work hardening curve and the bake hardening curve as a function of the degree of pre-expansion for the steel types St 15 (FIG. 8), ZStE 220i (FIG. 9) and ZStE 340 (FIG. 10). While the pure bake hardening effect tends to decrease again with increasing pre-stretching, the work hardening effect increases disproportionately, which results in the increasing total curve for the steel according to the invention.
  • FIG. 11 illustrates the dependence of the sum of the yield strength increase on the annealing temperatures and the annealing times.
  • the highest yield strength increase is achieved at the highest (permissible) annealing temperature of approx. 700 ° C with a long annealing time (5 minutes).
  • a further increase in the annealing temperature is not possible since the A 1 value (approx. 720 ° C) must not be exceeded during the annealing process. Exceeding the A 1 temperature would cause transformations that would negatively change the properties of the steel.
  • Table 2 shows the essential mechanical values for steels treated according to the invention with a BH 2 effect compared with the mechanical properties of the steel grades, as described in the Euronorm EN 10 130, in a material sheet W5 / 94 by the applicant or in the steel iron material sheets SEW 093 and SEW 094 are shown.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Lubricants (AREA)
  • Coating With Molten Metal (AREA)
EP02000584A 2001-01-23 2002-01-10 Procédé de fabrication d'une bande ou tôle d'acier laminée à froid et bande ou tôle pouvant être obtenue par ce procédé Expired - Lifetime EP1225235B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE10102932 2001-01-23
DE10102932A DE10102932C1 (de) 2001-01-23 2001-01-23 Verfahren zur Herstellung eines kalt gewalzten Bandes oder Bleches aus Stahl und nach dem Verfahren herstellbares Band oder Blech

Publications (3)

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EP1225235A2 true EP1225235A2 (fr) 2002-07-24
EP1225235A3 EP1225235A3 (fr) 2002-08-07
EP1225235B1 EP1225235B1 (fr) 2005-08-31

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EP02000584A Expired - Lifetime EP1225235B1 (fr) 2001-01-23 2002-01-10 Procédé de fabrication d'une bande ou tôle d'acier laminée à froid et bande ou tôle pouvant être obtenue par ce procédé

Country Status (7)

Country Link
US (1) US6749696B2 (fr)
EP (1) EP1225235B1 (fr)
JP (1) JP2002302717A (fr)
AT (1) ATE303453T1 (fr)
DE (2) DE10102932C1 (fr)
PL (1) PL351778A1 (fr)
RU (1) RU2002102055A (fr)

Cited By (2)

* Cited by examiner, † Cited by third party
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CN102755992A (zh) * 2012-07-30 2012-10-31 武汉钢铁(集团)公司 一种药芯焊丝用冷轧钢带生产方法
RU2479640C1 (ru) * 2012-02-29 2013-04-20 Открытое акционерное общество "Магнитогорский металлургический комбинат" Способ производства низкоуглеродистой холоднокатаной тонколистовой стали

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DE102005058658A1 (de) * 2005-12-07 2007-06-14 Kermi Gmbh Verfahren zur Wanddickenreduzierung von Stahlheizkörpern
EP1972699A1 (fr) * 2007-03-20 2008-09-24 ArcelorMittal France Procede de revetement d'un substrat et installation de depot sous vide d'alliage metallique
US8876990B2 (en) * 2009-08-20 2014-11-04 Massachusetts Institute Of Technology Thermo-mechanical process to enhance the quality of grain boundary networks
DE102009051673B3 (de) * 2009-11-03 2011-04-14 Voestalpine Stahl Gmbh Herstellung von Galvannealed-Blechen durch Wärmebehandlung elektrolytisch veredelter Bleche
KR101330396B1 (ko) * 2010-06-25 2013-11-15 엘지디스플레이 주식회사 표시장치와 그의 콘트라스트 향상 방법
US9870697B2 (en) * 2013-12-17 2018-01-16 At&T Mobility Ii Llc Method, computer-readable storage device and apparatus for providing a collaborative standalone area monitor
CN104313297A (zh) * 2014-11-10 2015-01-28 芜湖双源管业有限公司 一种冷轧钢带退火炉余热循环再利用方法
RU2623572C1 (ru) * 2016-08-31 2017-06-27 Публичное акционерное общество "Северсталь" (ПАО "Северсталь") Способ термической обработки холоднокатаного проката из низкоуглеродистой стали
RU2755132C1 (ru) * 2020-10-08 2021-09-13 Федеральное Государственное Унитарное Предприятие "Центральный научно-исследовательский институт черной металлургии им. И.П. Бардина" (ФГУП "ЦНИИчермет им. И.П. Бардина") Способ производства холоднокатаного непрерывно отожженного листового проката из if-стали

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WO1989007158A1 (fr) * 1988-01-29 1989-08-10 Stahlwerke Peine-Salzgitter Ag Tole ou feuillard lamines a froid et procede pour leur fabrication
EP0780480A1 (fr) * 1995-12-16 1997-06-25 Fried. Krupp AG Hoesch-Krupp Procédé de fabrication d'un ruban d'acier laminé à froid à haute résistance mécanique apte au formage et à propiétés isotropes
US5795410A (en) * 1997-01-23 1998-08-18 Usx Corporation Control of surface carbides in steel strip
US6143100A (en) * 1998-09-29 2000-11-07 National Steel Corporation Bake-hardenable cold rolled steel sheet and method of producing same

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EP0780480A1 (fr) * 1995-12-16 1997-06-25 Fried. Krupp AG Hoesch-Krupp Procédé de fabrication d'un ruban d'acier laminé à froid à haute résistance mécanique apte au formage et à propiétés isotropes
US5795410A (en) * 1997-01-23 1998-08-18 Usx Corporation Control of surface carbides in steel strip
US6143100A (en) * 1998-09-29 2000-11-07 National Steel Corporation Bake-hardenable cold rolled steel sheet and method of producing same

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MIZUI N ET AL: "RECENT DEVELOPMENT IN BAKE-HARDENABLE SHEET STEEL FOR AUTOMOTIVE BODY PANELS" , INTERNATIONALE TAGUNG STAHL IN AUTOMOBILBAU - INTERNATIONAL CONFERENCE STEEL IN MOTOR VEHICLE MANUFACTURE - CONGRES INTERNATIONAL ACIER POUR CONSTRUCTIONS D AUTOMOBILES, XX, XX, PAGE(S) 85-94 XP002038993 * Absatz [03.3]; Abbildungen 4,6 * *

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2479640C1 (ru) * 2012-02-29 2013-04-20 Открытое акционерное общество "Магнитогорский металлургический комбинат" Способ производства низкоуглеродистой холоднокатаной тонколистовой стали
CN102755992A (zh) * 2012-07-30 2012-10-31 武汉钢铁(集团)公司 一种药芯焊丝用冷轧钢带生产方法
CN102755992B (zh) * 2012-07-30 2015-08-12 武汉钢铁(集团)公司 一种药芯焊丝用冷轧钢带生产方法

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Publication number Publication date
JP2002302717A (ja) 2002-10-18
US6749696B2 (en) 2004-06-15
US20030145919A1 (en) 2003-08-07
DE50204048D1 (de) 2005-10-06
DE10102932C1 (de) 2002-08-22
PL351778A1 (en) 2002-07-29
EP1225235A3 (fr) 2002-08-07
RU2002102055A (ru) 2003-08-10
EP1225235B1 (fr) 2005-08-31
ATE303453T1 (de) 2005-09-15

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