WO2008006346A2 - Procédé de fabrication d'un demi-produit en tôle adapté pour le formage à chaud - Google Patents

Procédé de fabrication d'un demi-produit en tôle adapté pour le formage à chaud Download PDF

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Publication number
WO2008006346A2
WO2008006346A2 PCT/DE2007/001217 DE2007001217W WO2008006346A2 WO 2008006346 A2 WO2008006346 A2 WO 2008006346A2 DE 2007001217 W DE2007001217 W DE 2007001217W WO 2008006346 A2 WO2008006346 A2 WO 2008006346A2
Authority
WO
WIPO (PCT)
Prior art keywords
temperature
starting material
recrystallization
sheet metal
ferrite
Prior art date
Application number
PCT/DE2007/001217
Other languages
German (de)
English (en)
Other versions
WO2008006346A3 (fr
Inventor
Kurt Steinhoff
Ursula Weidig
Klaudia Bergmann
Alexander Elsner
Original Assignee
Universität Kassel
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Universität Kassel filed Critical Universität Kassel
Publication of WO2008006346A2 publication Critical patent/WO2008006346A2/fr
Publication of WO2008006346A3 publication Critical patent/WO2008006346A3/fr

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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
    • 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
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • 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
    • 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
    • C21D8/04—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
    • 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
    • C21D8/0447—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 heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working

Definitions

  • the modified heat treatment step is that the time / temperature course of the heat treatment is controlled so that a complete degradation of the fine-grained, elongated in the rolling direction microstructure is deliberately avoided.
  • the heat treatment is carried out according to this proposal so that only a partial recrystallization occurs and z. B. a degree of recrystallization of 25% to 45% is achieved.
  • the technical problem underlying the invention is to propose a method for producing a sheet-metal semi-finished product suitable for molding, which not only leads to a preselected degree of recrystallization, but also to a further increase in ductility and requires no additional process step.
  • a sheet metal semi-finished product is created, which can be efficiently used in a subsequent step of mold hardening to form a component which simultaneously has a high strength and a high elongation at break through a gefeintes microstructure.
  • the hot rolling train first contains a furnace 4 for the starting material, the so-called slab furnace, followed by different, the starting material reducing nips, which are not shown in detail and usually in a so-called “roughing” and in although this is less significant for the purposes of the present invention.
  • the locations within the hot rolling mill to which a rolling operation, i. a so-called roll pass takes place, are indicated in Fig. 1 by serrated regions 5 in a line 6 representing the temperature profile.
  • Fig. 1 along the T-axis different temperatures are given, which here have the following meaning throughout.
  • T AUSS temperature of the precipitation of the micro-alloying elements added to the starting material (eg 1100 0 C ⁇ 200 0 C);
  • Ar3 transformation temperature at which the transformation of austenite to ferrite begins (eg 800 ° C ⁇ 100 ° C);
  • TRX ⁇ recrystallization temperature of ferrite (for example, 600 0 C ⁇ 100 0C.);
  • ferrite with rapid cooling below the martensite start temperature Ms, a microstructure variant is formed, which is called martensite and is characterized by a hardened structure with high strength
  • step a the micro-alloying elements Nb and / or V and / or Ti present as a result of the expanded analysis of the tempering steel are first deliberately brought into a solution in the metal grid in the region of the solution temperature.
  • step b At a temperature slightly below T AUSS then a precipitation of a portion of the micro-alloying elements is achieved.
  • T AUSS a temperature slightly below T AUSS
  • steps a. and b. preferably without forming operations, although this is not mandatory.
  • the rolling step in the austenite region above TRX ⁇ and Ar3 achieves a dynamic reformation of the austenite with grain formation, which is brought about by deformation and a static re-heating of the austenite by grain formation, and thus further refining of the microstructure.
  • the second rolling step effects a refining of the microstructure by a dynamic recrystallization of the ferrite.
  • the semi-finished sheet is now at a temperature below
  • the semi-finished sheet metal is now transferred, possibly in the reeled state, to the coating plant 2 and in this first to an above
  • step h. is due to a targeted heating of the rolls in the ferrite area obtained, fine, a high dislocation density deformation structure to a above TRX ⁇ , but below ArI temperature partial recrystallization to the value a - RX 0PT and thus obtaining a high seed density for subsequent grain refinement by static recrystallization during mold curing achieved.
  • the partially recrystallized sheet metal semifinished product is then passed through the coating installation 2 at a temperature below TRX ⁇ and then cooled to the ambient temperature, whereby the final sheet metal semi-finished product which is particularly well-suited for form hardening is obtained. This step ends at about one
  • a precursor material provided with micro-alloying elements is used, and second, by successively rolling this primary material in different hot-rolling zones and at respectively selected temperature / time values, i. ensured by the combination of metallurgical and thermo-mechanical influences for grain and Gehegef entry that the semi-finished sheet produced by hot rolling has a high grain fineness and a preselected degree of recrystallization.
  • a particularly significant advantage is further that when using this sheet metal semi-finished products for molding components with an improved strength to toughness ratio can be obtained.
  • these components are characterized in comparison to those which are manufactured with conventionally produced sheet-metal semi-finished, characterized in that they have after hardening of the mold by more than 60% improved elongation at break with comparable strength.
  • Fig. 2 shows a second embodiment of the method according to the invention.
  • step c is shown in the method according to FIG. 2. replacing step cl, which starts at point B and ends at point Cl (in each case Fig. 2).
  • step c1 the first rolling step takes place at a temperature which is above Ar3 but below both T OFFS and below the temperature TRX ⁇ .
  • the degree of recrystallization a - RX 0PT is set in a process step which is carried out after the reeling and optionally after cooling of the starting material to the ambient temperature and, if required, only in the coating plant 2.
  • Fig. 3 shows an embodiment of the inventive method in which the desired degree of recrystallization ⁇ - RX 0PT is already obtained immediately before or after the coiling, so that in the subsequent coating system 2 no additional measures must be taken.
  • the semi-finished sheet metal in this case has the desired degree of partial recrystallization a - RX OPT after step gl, it can if necessary also be processed without coating in the mold-hardening system.
  • a heating step H1 (instead of h in FIG. 1) is carried out according to FIG. 3, which heats the semifinished sheet metal only to a temperature slightly below the recrystallization temperature TRX ⁇ , thereby avoiding unwanted further recrystallization. This step ends approximately at a point H 1 in FIG. 3, whereupon the coating and the shape hardening follow in analogy to FIG. 1.
  • a first rolling step c2 (eg in the roughing stand) takes place at a temperature lying in the temperature interval between Ar3 and ArI until approximately a point C2 in FIG.
  • the exemplary embodiment according to FIG. 5 differs with regard to method steps a. to e. of the exemplary embodiment according to FIG. 1 only in that it includes the method step c2 according to FIG. 4 instead of the method step c. contains according to FIG. 1.
  • step e. close after step e. the method steps fl to hl and then the method step i. to, as it corresponds to the embodiment of FIG. 3.
  • Figs. 6 and 7 show two embodiments in which a casting obtained by casting is used as the starting material. Accordingly, the method according to the invention is carried out here in a cast roll mill 8 instead of in a hot rolling mill.
  • the various procedural and rolling steps correspond, however, largely to the steps described above, so that they need not be explained again.
  • the starting material is obtained by melting, casting and solidifying a cast body is produced in which by applying a high solidification rate has already entered a certain refining of the microstructure.
  • the casting is here z. B. at a speed of 3.5 m / min to 5.5 m / min in a thickness range of z. B. 40 mm to 65 mm, then followed by the cooling below Ts followed.
  • micro-alloying elements in the form of niobium, vanadium and / or titanium are added to the molten tempering steel.
  • step a. 1 the heating or holding of the starting material at a temperature which is smaller than Ts and greater than the solution temperature for the micro-alloying elements used is analogous to FIG.
  • step b. joins step c2 according to Fig. 4 and 5, which ends at point C2.
  • This step can be carried out in the finishing scale of a conventional cast roll mill.
  • Fig. 7 shows an embodiment of the method according to the invention, in which the production of the starting material takes place as shown in Fig. 6 by casting rollers.
  • step a heating and maintaining a temperature which is below Ts and in the range of the solution temperature, close the process steps c2, d., e., Fl, gl, hl and i. at.
  • step a heating and maintaining a temperature which is below Ts and in the range of the solution temperature, close the process steps c2, d., e., Fl, gl, hl and i. at.
  • the setting of the desired degree of recrystallization a - RX 0PT as in FIGS . 3 and 5, in turn, takes place until reeling, so that the coiled sheet semifinished product, if a coating is not required, can be transported directly to the mold hardening system.
  • the semi-finished sheet metal products obtained with the method according to FIGS.
  • cooling steps may preferably each involve continuous cooling.
  • the invention includes not only the described methods, but also semi-finished products produced by these methods and components produced with the sheet metal semi-finished products, in particular motor vehicle components such. B. body parts.
  • the sheet semifinished products described can of course also be used for purposes other than for form hardening.
  • the term "tempering steel” other than boron-alloyed steels and in particular also the so-called “case-hardened steels” fall, with which the invention in the same manner as described can be realized.
  • preferred amounts of added micro-alloying elements are therefore only preferred examples of which can be deviated depending on the purpose and purpose of use.

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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 Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Articles (AREA)

Abstract

Procédé de fabrication d'un demi-produit en tôle adapté pour le formage à chaud, qui présente un meilleur rapport entre solidité et ductilité, demi-produit en tôle fabriqué selon ledit procédé et pièce fabriquée à partir de ce demi-produit en tôle, en particulier pièce pour carrosserie de véhicule automobile. Ledit procédé comporte les étapes suivantes : fabrication d'une matière de départ en acier revenu auquel sont ajoutés des éléments de microalliage en quantités prédéterminées, traitement de la matière de départ dans un train de laminage continu à chaud ou de laminage de coulée continue pour obtenir le demi-produit en tôle, traitement de la matière de départ d'abord à une température se trouvant dans la plage de la température de dissolution des éléments de microalliage, refroidissement de la matière de départ jusqu'à une température située au-dessous de la température de précipitation (TAUSS) pour précipiter au moins une partie des éléments de microalliage, laminage de la matière de départ pour former le demi-produit en tôle et commande de la température et des intervalles de temps dans diverses zones de laminage et éventuellement ensuite de manière telle que le demi-produit fini présente une grande finesse des grains et un degré de recristallisation (α ± RX) présélectionné.
PCT/DE2007/001217 2006-07-12 2007-07-05 Procédé de fabrication d'un demi-produit en tôle adapté pour le formage à chaud WO2008006346A2 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102006032617.2 2006-07-12
DE200610032617 DE102006032617B4 (de) 2006-07-12 2006-07-12 Verfahren zur Herstellung eines zum Formhärten geeigneten Blechhalbzeugs

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WO2008006346A2 true WO2008006346A2 (fr) 2008-01-17
WO2008006346A3 WO2008006346A3 (fr) 2008-06-26

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WO (1) WO2008006346A2 (fr)

Families Citing this family (5)

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Publication number Priority date Publication date Assignee Title
EP2287343B1 (fr) * 2008-08-28 2012-12-26 Hyundai Steel Company Procédé et appareil de durcissement par pressage continu
DE102009016027A1 (de) * 2009-04-02 2010-10-07 Volkswagen Ag Verfahren zur Herstellung eines Bauteils, insbesondere eines Karosserieteiles, sowie Fertigungsstraße zur Durchführung des Verfahrens
DE102009050997B4 (de) 2009-10-28 2017-07-13 Volkswagen Ag Verfahren und Umformvorrichtung zur Herstellung eines formgehärteten Bauteils
DE102010055148B4 (de) * 2010-12-18 2016-10-27 Tu Bergakademie Freiberg Verfahren zur Herstellung formgehärteter Bauteile
DE102013017798A1 (de) 2013-10-25 2015-04-30 GM Global Technology Operations LLC (n. d. Ges. d. Staates Delaware) Verbundstahlblech

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JPS58144422A (ja) * 1982-02-20 1983-08-27 Kobe Steel Ltd 非調質高張力鋼板の製造法
US4466842A (en) * 1982-04-03 1984-08-21 Nippon Steel Corporation Ferritic steel having ultra-fine grains and a method for producing the same
WO1993021351A1 (fr) * 1991-02-08 1993-10-28 Mcgill University Aciers depourvus d'elements interstitiels
US6221179B1 (en) * 1997-09-11 2001-04-24 Kawasaki Steel Corporation Hot rolled steel plate to be processed having hyper fine particles, method of manufacturing the same, and method of manufacturing cold rolled steel plate
WO2001029272A1 (fr) * 1999-10-19 2001-04-26 Aspector Oy Procede de production d'une structure de grains ultra-fine pour acier non allie ou faiblement allie
KR20040059579A (ko) * 2002-12-27 2004-07-06 주식회사 포스코 동적변태를 이용한 페라이트 초세립강의 제조방법
US20050115649A1 (en) * 2003-03-27 2005-06-02 Tokarz Christopher A. Thermomechanical processing routes in compact strip production of high-strength low-alloy steel
WO2007033711A1 (fr) * 2005-09-22 2007-03-29 Volkswagen Aktiengesellschaft Procede de traitement d'un feuillard en acier

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US3826691A (en) * 1973-02-05 1974-07-30 Bethlehem Steel Corp Rolled ferrite-pearlite alloy plate and method of processing same
JPS58144422A (ja) * 1982-02-20 1983-08-27 Kobe Steel Ltd 非調質高張力鋼板の製造法
US4466842A (en) * 1982-04-03 1984-08-21 Nippon Steel Corporation Ferritic steel having ultra-fine grains and a method for producing the same
WO1993021351A1 (fr) * 1991-02-08 1993-10-28 Mcgill University Aciers depourvus d'elements interstitiels
US6221179B1 (en) * 1997-09-11 2001-04-24 Kawasaki Steel Corporation Hot rolled steel plate to be processed having hyper fine particles, method of manufacturing the same, and method of manufacturing cold rolled steel plate
WO2001029272A1 (fr) * 1999-10-19 2001-04-26 Aspector Oy Procede de production d'une structure de grains ultra-fine pour acier non allie ou faiblement allie
KR20040059579A (ko) * 2002-12-27 2004-07-06 주식회사 포스코 동적변태를 이용한 페라이트 초세립강의 제조방법
US20050115649A1 (en) * 2003-03-27 2005-06-02 Tokarz Christopher A. Thermomechanical processing routes in compact strip production of high-strength low-alloy steel
WO2007033711A1 (fr) * 2005-09-22 2007-03-29 Volkswagen Aktiengesellschaft Procede de traitement d'un feuillard en acier

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Publication number Publication date
WO2008006346A3 (fr) 2008-06-26
DE102006032617B4 (de) 2008-04-03
DE102006032617A1 (de) 2008-01-24

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