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EP0521808B1 - Procédé de fabrication de tôles minces destinées à l'emboutissage - Google Patents

Procédé de fabrication de tôles minces destinées à l'emboutissage Download PDF

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Publication number
EP0521808B1
EP0521808B1 EP92470020A EP92470020A EP0521808B1 EP 0521808 B1 EP0521808 B1 EP 0521808B1 EP 92470020 A EP92470020 A EP 92470020A EP 92470020 A EP92470020 A EP 92470020A EP 0521808 B1 EP0521808 B1 EP 0521808B1
Authority
EP
European Patent Office
Prior art keywords
proportion
steel
less
thin sheet
thickness
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.)
Expired - Lifetime
Application number
EP92470020A
Other languages
German (de)
English (en)
Other versions
EP0521808A1 (fr
Inventor
Daniel Lafontaine
Georges Van Hoecke
Partrick Zimmer
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Sollac SA
Original Assignee
Sollac SA
Lorraine de Laminage Continu SA SOLLAC
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 Sollac SA, Lorraine de Laminage Continu SA SOLLAC filed Critical Sollac SA
Publication of EP0521808A1 publication Critical patent/EP0521808A1/fr
Application granted granted Critical
Publication of EP0521808B1 publication Critical patent/EP0521808B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

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
    • 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
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • 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
    • C21D8/0436—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
    • C21D8/04—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
    • C21D8/0468—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 between cold rolling steps
    • 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

Definitions

  • the invention relates to steels for packaging intended to be stamped. More particularly it relates to a process for manufacturing steel sheets, intended for manufacturing by shrinking stamping boxes or containers such as so-called boxes two pieces ", including boxes called” DRD "(that is to say obtained by stamping-re-stamping), as well as the product obtained.
  • these products are usually obtained by a process including in particular a base annealing phase.
  • stamping irons tend to have a thickness of more and more weak. Indeed the improvement of mechanical characteristics of steels for packaging authorizes the manufacture of boxes or containers of very thin without affecting the mechanical strength of these. On the other hand, these small thicknesses induce special constraints for stamping such irons, for which we are looking for a coefficient high anisotropy and low plane anisotropy.
  • the subject of the invention is a process for manufacturing thin steel sheets for deep drawing packaging improved, as claimed in claim 1.
  • the steel is produced in converter with bottom blowing of oxygen and with argon blowing.
  • the invention also relates to a thin sheet in steel, for stamping, obtained by the process above and claimed in claim 2.
  • This steel is not subjected to vacuum degassing.
  • This steel is then continuously cast so classic, then hot rolled with a temperature of end of rolling 870 °, and wound at a temperature of 710 ° C.
  • the thin sheet obtained is subjected to annealing in continuous at a temperature below 700 ° C, for example 660 ° C, then re-rolled to a thickness of 0.18 mm.
  • the manganese and sulfur contents are optimized to simultaneously guarantee good forgeability during hot rolling, and good stampability of the thin sheet finally obtained.
  • a reduction in the manganese content is favorable with regard to the final texture of the sheet metal, but if this content is too low, it may pose forgeability problems.
  • the reduced carbon content obtained through development in LWS converter with blowing of argon, associated with a high temperature winding promotes the stampability of the thin sheet ultimately obtained.
  • the low aluminum content allows to avoid its precipitation during annealing, which is also favorable for stampability.
  • the table below indicates, for different steel compositions and rolling and hot-winding conditions, the values of the anisotropy coefficient "r" and the value of " ⁇ C" of the thin sheet obtained after cold rolling and annealing.
  • the value " r” is determined by uniaxial tensile tests after annealing.
  • the value” ⁇ C " which expresses the level of drawing horns, is measured by magnetic method after re-rolling. This value is correlated with the value of the plane anisotropy" ⁇ r ".
  • Steel according to the invention continuously annealed Classic steel with base annealing Classic steel in continuous annealing ex. 1 ex.
  • the anisotropy coefficient of the thin steel sheet according to the invention is at least as high, and especially that the plane anisotropy (correlated to " ⁇ C") is considerably reduced, which corresponds to markedly improved stampability.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Blow-Moulding Or Thermoforming Of Plastics Or The Like (AREA)
  • Press Drives And Press Lines (AREA)
  • Forging (AREA)
  • Mounting, Exchange, And Manufacturing Of Dies (AREA)
  • Heat Treatment Of Steel (AREA)

Description

L'invention concerne les aciers pour emballages destinés à être emboutis. Plus particulièrement elle concerne un procédé de fabrication de tôles en acier, destinées à la fabrication par emboutissage par retreint de boítes ou récipients tels que des boítes dites "boítes deux pièces", notamment des boítes dites "DRD" (c'est-à-dire obtenues par emboutissage-réemboutissage), ainsi que le produit obtenu.
L'utilisation croissante du procédé d'emboutissage dans la fabrication d'emballages métalliques nécessite le développement de tôles d'acier de très faibles épaisseurs, ou fers minces (fer-blanc ou fer chromé) toujours plus performants du point de vue formabilité et résistance mécanique de l'emballage, récipient ou boíte, embouti.
Selon les techniques courantes actuelles, ces produits sont habituellement obtenus par un procédé comportant notamment une phase de recuit sur base.
Cependant l'emboutissabilité des produits ainsi obtenus est insuffisante pour les mises en oeuvre les plus sévères c'est-à-dire lorsque les fers doivent être très fortement déformés par emboutissage.
Ce problème est d'autant plus important que les fers pour emboutissage tendent à avoir une épaisseur de plus en plus faible. En effet l'amélioration des caractéristiques mécaniques des aciers pour emballage autorise la fabrication de boítes ou récipients de très faible épaisseur sans nuire à la tenue mécanique de ceux-ci. Par contre ces épaisseurs faibles induisent des contraintes particulières pour l'emboutissage de tels fers, pour lesquels on recherche un coefficient d'anisotropie élevé et un anisotropie plane faible.
Dans le but d'obtenir ces caractéristiques l'invention a pour objet un procédé de fabrication de tôles minces en acier pour emballage à emboutissabilité amélioré, tel que revendiqué à la revendication 1.
Préférentiellement, l'acier est élaboré en convertisseur avec soufflage d'oxygène par le fond et avec soufflage d'argon.
L'invention a aussi pour objet une tôle mince en acier, destinée à l'emboutissage, obtenue par le procédé ci-dessus et revendiquée à la revendication 2.
D'autres caractéristiques et avantages apparaítront dans la description qui va suivre, donnée uniquement à titre d'exemple.
On élabore en convertisseur du type LWS, c'est-à-dire avec soufflage d'oxygène par le fond, et avec soufflage d'argon, un acier de composition :
  • C = 11 10-3 %
  • Mn = 187   "
  • P = 4   "
  • N = 4,5   "
  • Al = 8   "
  • S = 6   "
    • le reste étant du fer.
    Cet acier n'est pas soumis à un dégazage sous vide.
    Cet acier est ensuite coulé en continu de manière classique, puis laminé à chaud avec une température de fin de laminage de 870°, et bobiné à une température de 710°C.
    Après laminage à froid jusqu'à une épaisseur de 0,23 mm, la tôle mince obtenue est soumise à un recuit en continu à une température inférieure à 700°C, par exemple 660°C, puis relaminée jusqu'à une épaisseur de 0,18 mm.
    On notera que les teneurs en manganèse et en soufre sont optimisées pour garantir simultanément une bonne forgeabilité lors du laminage à chaud, et une bonne emboutissabilité de la tôle mince finalement obtenue. En effet, une réduction de la teneur en manganèse est favorable pour ce qui concerne la texture finale de la tôle, mais si cette teneur est trop faible, il peut se poser des problèmes de forgeabilité.
    La teneur en carbone réduite, obtenue grâce à l'élaboration en convertisseur LWS avec soufflage d'argon, associée à un bobinage à haute température favorise l'emboutissabilité de la tôle mince finalement obtenue.
    Par ailleurs la faible teneur en aluminium permet d'éviter sa précipitation lors du recuit, ce qui est également favorable pour l'emboutissabilité.
    La combinaison de ces différents facteurs permet l'obtention d'une bonne emboutissabilité de la tôle mince, avec un recuit à basse température, laquelle est exigée pour un recuit continu de tôles très minces, dont l'épaisseur peut être inférieur à 0,20 mm. En effet les techniques actuelles de recuit continu ne permettent pas de traiter à haute température de telles tôles qui, sous l'effet de températures élevées et de la grande vitesse de défilement, risqueraient de fluer et former des plis, perturbant ainsi le processus de recuit et dégradant la qualité de la tôle.
    Le tableau ci-dessous indique pour différentes compositions d'acier et conditions de laminage et bobinage à chaud les valeurs du coefficient d'anisotropie " r " et de la valeur de "ΔC" de la tôle mince obtenue après laminage à froid et recuit. La valeur "r" est déterminée par des essais de traction uniaxiale après recuit. La valeur "ΔC", qui exprime le niveau de cornes d'emboutissage, est mesurée par méthode magnétique après relaminage. Cette valeur est corrélée à la valeur de l'anisotropie plane "Δr".
    Acier selon l'invention recuit en continu Acier classique avec recuit base Acier classique en recuit continu
    ex. 1 ex. 2 ex 3
    Composition (en 10-3%)
       C 10 11 7 60 43
       Mn 167 187 231 310 271
       P 6 4 6 11 8
       N 4,5 4,2 4,2 5,5 4,5
       Al 8 14 13 55 53
       S 7 6 10 18 15
    Température de fin de laminage (°C) 890 870 885 860 860
    Température de bobinage (°C) 715 710 720 570 710
    r 1,65 1,62 1,61 1,61 1,30
    ΔC -0,18 -0,18 - 0,20 - 0,39 -0,35
    On constate que par rapport aux aciers classique selon l'Art antérieur, le coefficient d'anisotropie de la tôle mince en acier selon l'invention est au moins aussi élevé, et surtout que l'anisotropie plane (corrélée à "ΔC") est considérablement réduite, ce qui correspond à une emboutissabilité nettement améliorée.

    Claims (2)

    1. Procédé de fabrication de tôles minces en acier pour emballage destinées à l'emboutissage, caractérisé en ce que, en vue d'obtenir des tôles minces d'épaisseur inférieure à 0,20 mm présentant un coefficient d'anisotropie r élevé et une anisotropie plane Δr faible, il comporte les opérations suivantes prises dans cet ordre:
      élaboration en convertisseur de préférence du type LWS avec soufflage d'argon, d'un acier contenant du carbone dans une proportion inférieure à 0,015%, du manganèse dans une proportion 0,15 à 0,25%, du soufre dans une proportion inférieure à 0,012% et de l'aluminium dans une proportion inférieure ou égale à 0,014%, ces proportions étant pondérales, le solde étant du fer et des impuretés habituelles inévitables; cet acier n'étant pas ensuite soumis à un dégazage sous vide,
      coulée en continu;
      laminage à chaud entièrement en domaine austénitique;
      bobinage à une température supérieure à 650°C;
      laminage à froid jusqu'à une épaisseur supérieure à l'épaisseur finale;
      recuit continu à une température inférieure à 700°C;
      relaminage jusqu'à l'épaisseur finale.
    2. Tôle mince en acier pour emballage destinée à l'emboutissage, caractérisée en ce qu'elle est obtenue par le procédé selon la revendication 1 et qu'elle présente un coefficient d'anisotropie r supérieur ou égal à 1,6 et une valeur Δ C, corrélée à l'anisotropie plane Δr, supérieure ou égale à -0,20.
    EP92470020A 1991-07-04 1992-06-11 Procédé de fabrication de tôles minces destinées à l'emboutissage Expired - Lifetime EP0521808B1 (fr)

    Applications Claiming Priority (2)

    Application Number Priority Date Filing Date Title
    FR9108565A FR2678641B1 (fr) 1991-07-04 1991-07-04 Acier a emboutissabilite amelioree et procede de fabrication de toles destinees a l'emboutissage.
    FR9108565 1991-07-04

    Publications (2)

    Publication Number Publication Date
    EP0521808A1 EP0521808A1 (fr) 1993-01-07
    EP0521808B1 true EP0521808B1 (fr) 2002-08-07

    Family

    ID=9414844

    Family Applications (1)

    Application Number Title Priority Date Filing Date
    EP92470020A Expired - Lifetime EP0521808B1 (fr) 1991-07-04 1992-06-11 Procédé de fabrication de tôles minces destinées à l'emboutissage

    Country Status (11)

    Country Link
    US (1) US5232524A (fr)
    EP (1) EP0521808B1 (fr)
    JP (1) JPH05195147A (fr)
    KR (1) KR100244363B1 (fr)
    AT (1) ATE221922T1 (fr)
    CA (1) CA2073131C (fr)
    DE (1) DE69232717T2 (fr)
    DK (1) DK0521808T3 (fr)
    ES (1) ES2180532T3 (fr)
    FR (1) FR2678641B1 (fr)
    PT (1) PT521808E (fr)

    Cited By (1)

    * Cited by examiner, † Cited by third party
    Publication number Priority date Publication date Assignee Title
    EP1088905B2 (fr) † 1999-04-20 2019-06-05 Nippon Steel & Sumitomo Metal Corporation Tole d'acier ultra mince pour boite boisson ayant une résistance à la formation de pli et procede de production associe

    Families Citing this family (8)

    * Cited by examiner, † Cited by third party
    Publication number Priority date Publication date Assignee Title
    FR2723964B1 (fr) * 1994-08-29 1997-03-14 Lorraine Laminage Procede d'elaboration d'un acier pour emballage apte a un emboutissage profond et acier obtenu par ce procede
    FR2724946B1 (fr) * 1994-09-23 1996-12-13 Lorraine Laminage Procede de fabrication d'un acier presentant une bonne aptitude a la mise en forme et une bonne resistance a l'indentation
    FR2730942B1 (fr) * 1995-02-24 1997-05-16 Lorraine Laminage Procede d'elaboration d'une tole ou d'une bande en acier pour la realisation d'une boite et tole ou bande en acier obtenue par ce procede
    NL1000696C2 (nl) * 1995-06-29 1996-12-31 Hoogovens Staal Bv Werkwijze en inrichting voor het vervaardigen van een dunne warmgewalste stalen band.
    FR2739105B1 (fr) * 1995-09-21 1998-04-30 Lorraine Laminage Procede de fabrication d'une bande metallique pour emballages et emballages metalliques obtenus par ce procede
    US6109336A (en) * 1996-06-28 2000-08-29 Hoogovens Staal Bv Method of manufacturing a deep-drawing steel strip or sheet
    FR2767078B1 (fr) 1997-08-07 1999-10-22 Lorraine Laminage Procede d'elaboration d'une tole mince en acier a ultra bas carbone pour la realisation de produits emboutis pour emballage et tole mince obtenue
    JP4559918B2 (ja) * 2004-06-18 2010-10-13 新日本製鐵株式会社 加工性に優れたブリキおよびテインフリースチール用鋼板およびその製造方法

    Family Cites Families (7)

    * Cited by examiner, † Cited by third party
    Publication number Priority date Publication date Assignee Title
    SE405984B (sv) * 1969-12-27 1979-01-15 Nippon Kokan Kk Sett for framstellning av kallvalsat stal, lempligt for djupdragning
    JPS5338691B2 (fr) * 1972-12-28 1978-10-17
    DE3271669D1 (en) * 1981-09-18 1986-07-17 Nippon Steel Corp Method for producing a cold rolled steel sheet
    JPS58136721A (ja) * 1982-02-09 1983-08-13 Nippon Steel Corp 加工性のすぐれた冷間圧延鋼板の製造方法
    JPH0830215B2 (ja) * 1986-09-16 1996-03-27 新日本製鐵株式会社 コイル内材質の均一性に優れた深絞り用鋼板の製造方法
    JPS63277724A (ja) * 1987-05-08 1988-11-15 Nippon Steel Corp 深絞り性の優れた冷延鋼板の製造方法
    BE1002517A6 (fr) * 1988-09-28 1991-03-12 Centre Rech Metallurgique Procede de fabrication d'un acier pour emboutissage.

    Cited By (1)

    * Cited by examiner, † Cited by third party
    Publication number Priority date Publication date Assignee Title
    EP1088905B2 (fr) † 1999-04-20 2019-06-05 Nippon Steel & Sumitomo Metal Corporation Tole d'acier ultra mince pour boite boisson ayant une résistance à la formation de pli et procede de production associe

    Also Published As

    Publication number Publication date
    US5232524A (en) 1993-08-03
    DK0521808T3 (da) 2002-12-02
    EP0521808A1 (fr) 1993-01-07
    KR100244363B1 (ko) 2000-03-02
    CA2073131A1 (fr) 1993-01-05
    DE69232717D1 (de) 2002-09-12
    JPH05195147A (ja) 1993-08-03
    ES2180532T3 (es) 2003-02-16
    PT521808E (pt) 2002-12-31
    KR930002004A (ko) 1993-02-22
    CA2073131C (fr) 2003-04-29
    DE69232717T2 (de) 2003-04-30
    FR2678641A1 (fr) 1993-01-08
    ATE221922T1 (de) 2002-08-15
    FR2678641B1 (fr) 1998-11-20

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