EP0400031B2 - Tole ou feuillard lamines a froid et procede pour leur fabrication - Google Patents

Tole ou feuillard lamines a froid et procede pour leur fabrication Download PDF

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Publication number
EP0400031B2
EP0400031B2 EP89901844A EP89901844A EP0400031B2 EP 0400031 B2 EP0400031 B2 EP 0400031B2 EP 89901844 A EP89901844 A EP 89901844A EP 89901844 A EP89901844 A EP 89901844A EP 0400031 B2 EP0400031 B2 EP 0400031B2
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EP
European Patent Office
Prior art keywords
titanium
epsilon
cold
approx
strip
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
EP89901844A
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German (de)
English (en)
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EP0400031B1 (fr
EP0400031A1 (fr
Inventor
Klaus Freier
Walter Zimnik
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.)
Salzgitter AG
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Salzgitter AG
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Publication date
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Application filed by Salzgitter AG filed Critical Salzgitter AG
Priority to AT89901844T priority Critical patent/ATE97169T1/de
Publication of EP0400031A1 publication Critical patent/EP0400031A1/fr
Application granted granted Critical
Publication of EP0400031B1 publication Critical patent/EP0400031B1/fr
Publication of EP0400031B2 publication Critical patent/EP0400031B2/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
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • 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
    • C21D8/0473—Final recrystallisation annealing

Definitions

  • the invention relates to a method for producing a sheet or strip and to Deep-drawing suitable sheet or strip according to the preambles of claims 1 and 5.
  • Texture-free cold-rolled strip is used to deep-draw rotationally symmetrical steel parts or sheet metal is used, so that quasi-isotropic forming is possible and the drawn part is free of corners. This means that a z. B. cylindrical deep-drawn part has no wavy edge.
  • the value for the plane anisotropy is calculated from the anisotropy r for different things Expansion behavior of the material in the rolling direction as well as at 45 degrees and 90 degrees. For Different deep-drawing properties, different r-values can be set.
  • tip-free material can only be obtained by normalizing of the cold-rolled strip in a continuous annealing at about 1000 degrees Celsius, the sheet in the final state a grain size ASTM 8 with a relative tip height of approx. 0.3 to 0.4% and delta r approx. Reach ⁇ 0.1.
  • DE-OS 32 34 574 is a generic cold-rolled steel sheet suitable for deep drawing or steel band known.
  • the titanium content should, depending on the carbon, oxygen, Sulfur and nitrogen, can rise to values up to 0.15%, the reel temperature over 700 degrees Celsius or at least 580 degrees Celsius with subsequent hot strip heating to over 700 degrees Celsius.
  • US Pat. No. 4,125,416 discloses, inter alia, a method in which hot-rolled slabs at temperatures above 830 ° C. made of alloy steel, which 0.06-0.20% C, 0.5-2.0% Mn, 0.30- May contain 0.50% Si as well as Nb and Ti in quantities of 0.01-0.10%, heated to temperatures above 980 ° C, then rolled into hot strip and coiled at 450-650 ° C. C contents of 0.10-0.11%, a Ti content of 0.1% and an Nb content of 0.04% are specified for the production of high-strength cold strip from this hot strip. At 67% degree of deformation, a high-strength cold strip with a yield strength greater than 48.1 kg / mm 2 is produced, which is then recrystallized annealed in a bundle or in a continuous anneal.
  • EP-A1-101 740 recommends a slab heating temperature of less than 1100 degrees Celsius, a final roll temperature of less than Ar 3 , reel temperatures of 320-600 degrees Celsius and cold rolling degrees of 50-95% and recrystallizing continuous annealing for a generic cold-rolled steel.
  • a steel with a maximum of 0.005% carbon, a maximum of 0.004% nitrogen and a maximum of 0.02% niobium is to be used in combination with one or more of the elements aluminum, chromium, boron or tungsten. High average r values above 1.2 are achieved. There are no indications that the material is rough after deep-drawing.
  • Another method for producing deep-drawing steels with a slab annealing temperature lower 1100 degrees Celsius, final rolling temperature max. 780 degrees Celsius and reel temperatures of at least 450 degrees Celsius and cold strip annealing in the hood or continuous annealing furnace are in EP-B1-120 976 disclosed.
  • the method should achieve r values around 2; Values for tip formation are not disclosed.
  • hot strip has good quasi-isotropic formability, but one insufficient surface quality and tolerances, and also not in thicknesses below 1.2 mm is produced.
  • the invention is therefore based on the object of proposing a sheet-free steel sheet which is suitable for deep drawing or at least poor in drawing and a corresponding production process in which continuous annealing at temperatures above A 1 is dispensed with, but can nevertheless be produced inexpensively.
  • the grain size values of at best ASTM 8 corresponding to 490 ⁇ m 2 which are usually achieved in the state of the art for steel St 4 NZ or RSt 14 by normal annealing, can be undercut by recrystallizing annealing using the process according to the invention, with additional low yield strength values being able to be maintained by selecting appropriate ones Cold rolling degrees depending on the titanium content. This has the advantage that high investments for a continuous annealing for a normal annealing treatment can be dispensed with.
  • a particular advantage of the hot strip produced in this way is that, in principle, none There is a restriction regarding the subsequent cold rolling provided that the degree of cold rolling is at least approx. 5 %, i.e. remains above the known critical weak cold deformation that occurs during recrystallization annealing leads to coarse grain. So far, the production of almost strip-free cold strip was on certain degrees of cold rolling are bound, unless normal annealing is used.
  • the variation of the cold rolling degrees depending on the amount of the alloyed titanium is at simultaneous addition of niobium within the specified limits to cold rolling degrees of 45 to 85% limited.
  • niobium does not hinder the early formation of titanium nitride, so that this too Steel alloy according to the invention does not have a pan-cake structure during recrystallizing annealing can arise.
  • a serious technical and economic importance of the invention lies in the use of the Thin sheets for rotationally symmetrical deep-drawn parts such as needle bearing cages, pulley halves etc.
  • the sheet metal according to the invention can in these cases without substantial rework such as cutting the Tip are used.
  • the low-headedness also prevents the emergence of sectoral thermoforming Wall weaknesses, so that the drawn parts do not show any imbalance when rotating. Additional advantages Low-end or corner-free cold strip are known, so that a further description is unnecessary.
  • Figure 1 shows three different cups, which are to define the terms used in the following, pointed (Fig. 1a), low-pointed (Fig. 1b) and free (Fig. 1c), since the measurement of the height with the commercially available corner measuring devices, in particular low-cornered and Tip-free wells with small height differences are problematic even with the smallest deep-drawn burrs on the edge of the well.
  • This definition was adopted for Figure 10 to represent the lobes of wells from the different melts.
  • the finding was confirmed that the steel E coiled at 710 degrees Celsius is free of flakes only at cold rolling degrees of less than approx. 25% and can only be described as low in the range 30 - 50% of cold rolling.
  • cornering was found at cold rolling degrees greater than 30%.
  • the photos in Figures 8 and 9 demonstrate this impressively.
  • Table 2 shows the grain size achieved according to the invention in ASTM units; the achievable grain refinement compared to steels without titanium addition according to the state of the Technology is significant and extends to ASTM 11.
  • the coarsest grain was obtained with a small addition of Ti and a low degree of cold rolling (ASTM 7).
  • ASTM 9-10 the hot strip values for the grain size (ASTM 9-10) were compared in FIG.
  • For a steel C (variants C3 - C5) tests were carried out with variable coiling temperature Th and annealing throughput Pg (Table 3). While fluctuations in the throughput of the bell annealer from 1.1 - 1.9 t / h did not have a negative effect on the grain size or the level anisotropy Delta r, an increase in the reel temperature to 710 degrees Celsius with roughly the same end temperatures resulted in coarsening and deterioration the plane anisotropy.
  • Figures 2a, 2b, 2c show corresponding results on wells made of 180 mm rounds, the with 100 mm stamps with 50 kN retention force were deep drawn.
  • Table 1 also shows the melt analyzes of the process to be used according to the invention
  • Steel G with 0.01% titanium, H with 0.02% titanium and I with 0.03% titanium with 0.05% and 0.06% niobium addition A comparative steel K with 0.05% niobium addition but without titanium content was listed.
  • From the melts G - I according to the invention and the comparative melt K slabs of 220 mm thickness cast in the strand. After heating in the pusher furnace to 1250 degrees Celsius, the slab was Rolled into 4 mm thick hot strip and coiled and cooled to room temperature. The The final roll temperature was 880 degrees Celsius and the reel temperature was 510 degrees Celsius. After this The strips were pickled by cold rolling in different stages from 10 to 80% on thin sheet thickness reduced and reeled.
  • the tightly wrapped coil was placed in the bell annealer of the Ludwig construction type heated to 700 degrees Celsius and with a throughput rate of 1.1 tons or 1.8 Annealed tons per hour recrystallizing, then in the bell annealing furnace to 120 degrees Celsius cooled. After tempering with a degree of deformation of 1.1%, the strip became sheet metal assembled. Sheet rounds of 90 mm in diameter were closed with drawing dies of 50 mm in diameter Cups deep-drawn ( Figures 13 - 16).
  • the yield strength and tensile strength values were found to be more than 50 N / mm 2 above the characteristic values of the only titanium-alloyed material.

Claims (7)

  1. Procédé de fabrication d'une tôle ou d'une bande, laminée à froid, présentant une bonne aptitude à la déformation quasi-isotrope, en un acier présentant la composition suivante, en pourcentages en poids:
    0,03 - 0,08 % de carbone
    au maximum 0,40 % de silicium
    0,10 à 1,0 % de manganèse
    au maximum 0,08 % de phosphore
    au maximum 0,02 % de soufre
    au maximum 0,009 % d'azote
    0,015 à 0,08 % d'aluminium
    0,01 à 0,04 % de titane
    au maximum 0,15 % d'un ou plusieurs des éléments choisis dans le groupe constitué par le cuivre, le vanadium et le nickel
    le reste étant constitué par du fer et par les impuretés inévitables, la teneur en titane correspondant au moins à 3,5 fois la teneur en azote, procédé suivant lequel la brame est chauffée à une valeur dépassant 1120 degrés Celsius, et est laminée à chaud en un feuillard à une température finale de laminage dépassant le point Ar3, et est bobinée à 520 ± 100 degrés Celsius, et, après le laminage à froid, est soumise à un recuit de recristallisation dans la bobine.
  2. Procédé de fabrication d'une tôle ou d'une bande, laminée à froid, selon la revendication 1, caractérisé par le fait qu'elle est laminée à froid en fonction de la teneur en titane avec les taux de déformation ci-après (epsilon). environ 0,01 % de titane epsilon 20 - 60 %, de préférence 30 - 50 %; environ 0,02 % de titane epsilon 5 - 20 %, de préférence 10 - 15 %, ou epsilon 40 - 85 %, de préférence, 50 - 80 %; environ 0,03 % de titane epsilon 5 - 25 %, de préférence 10 - 20 %, ou epsilon 50 - 85 % de préférence 60 - 80 %; environ 0,04 % de titane epsilon 15 - 25 %, de préférence 20 %, ou epsilon 55 - 80 %, de préférence 60 - 70%;
    puis soumise à un recuit de recristallisation à des températures inférieures à A1, et, ensuite, soumise à un dressage avec un taux de déformation d'environ 1 %.
  3. Procédé de fabrication d'une tôle ou d'une bande, laminée à froid, présentant une bonne aptitude à la déformation quasi-isotrope, à partir d'un acier présentant la composition suivante en pourcentages en poids:
    0,03 - 0,08 % de carbone
    au maximum 0,40 % de silicium
    0,10 à 1,0 % de manganèse
    au maximum 0,08 % de phosphore
    au maximum 0,02 % de sofre
    au maximum 0,009 % d'azote
    0,015 à 0,08 % d'aluminium
    0,01 à 0,04 % de titane
    au maximum 0,15 % d'un ou plusieurs des éléments choisis dans le groupe constitué par le cuivre, le vanadium, le nickel
    0,01 à 0,06 % de niobium
    le reste étant constitué par du fer et par les impuretés inévitables, la teneur en titane correspondant au moins à 3,5 fois la teneur en azote, procédé suivant lequel la brame est chauffée à une température dépassant 1120 degrés Celsius et laminée à chaud en un feuillard à une température finale de laminage dépassant le point Ar3 et bobinée à une température de 520 ± 100 degrés Celsius, puis est laminée à froid en fonction de la teneur en titane avec les taux de déformation suivants (epsilon): environ 0,01 % de titane epsilon 45 à 85 % environ 0,02 % de titane epsilon 55 à 85 % environ 0,03 % de titane epsilon 60 à 70 %
    puis soumise à un recuit de recristallisation dans la bobine à des températures inférieures à A1, et ensuite, soumise à un dressage avec un taux de déformation d'environ 1 %.
  4. Procédé selon l'une des revendications 1 à 3, caractérisé par le fait que l'acier est soumis à un recuit dans la bobine serrée après le laminage à froid.
  5. Tôle ou bande appropriée pour l'emboutissage profond, en un acier ayant la composition indiquée et fabriquée conformément à l'un des procédés indiqués dans l'une des revendications 1 à 4, caractérisée par une structure recristallisée présentant une grosseur de grain de ferrite inférieure à ASTM 7 pour une teneur en titane de 0,01 %, et inférieure à ASTM 9 pour des teneurs en titane de 0,015 à 0,04 % et par une teneur en titane correspondant au moins à 3,5 fois la teneur en azote.
  6. Utilisation d'une tôle ou d'une bande fabriquée conformément à l'un des procédés tel que définis à l'une des revendications 1 à 4, pour l'emboutissage profond sans formation d'oreilles, de préférence, de pièces à symétrie de rotation.
  7. Utilisation d'un acier tel que défini à l'une des revendications 1 ou 3, pour la fabrication de pièces ayant été soumises à un emboutissage profond, de préférence à symétrie de rotation.
EP89901844A 1988-01-29 1989-01-27 Tole ou feuillard lamines a froid et procede pour leur fabrication Expired - Lifetime EP0400031B2 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AT89901844T ATE97169T1 (de) 1988-01-29 1989-01-27 Kaltgewalztes blech oder band und verfahren zu seiner herstellung.

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
DE3803064 1988-01-29
DE3803064A DE3803064C2 (de) 1988-01-29 1988-01-29 Kaltgewalztes Blech oder Band und Verfahren zu seiner Herstellung
DE3843732 1988-12-22
DE3843732A DE3843732C2 (de) 1988-01-29 1988-12-22 Kaltgewalztes Blech oder Band und Verfahren zu seiner Herstellung
PCT/DE1989/000057 WO1989007158A1 (fr) 1988-01-29 1989-01-27 Tole ou feuillard lamines a froid et procede pour leur fabrication

Publications (3)

Publication Number Publication Date
EP0400031A1 EP0400031A1 (fr) 1990-12-05
EP0400031B1 EP0400031B1 (fr) 1993-11-10
EP0400031B2 true EP0400031B2 (fr) 2002-01-02

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ID=25864488

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EP89901844A Expired - Lifetime EP0400031B2 (fr) 1988-01-29 1989-01-27 Tole ou feuillard lamines a froid et procede pour leur fabrication

Country Status (8)

Country Link
US (1) US5139580A (fr)
EP (1) EP0400031B2 (fr)
JP (1) JPH0814003B2 (fr)
DD (1) DD285298B5 (fr)
DE (3) DE3803064C2 (fr)
ES (1) ES2018975A6 (fr)
GR (1) GR1000537B (fr)
WO (1) WO1989007158A1 (fr)

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DE4015249A1 (de) * 1989-05-09 1991-02-28 Salzgitter Peine Stahlwerke Verfahren zur herstellung von feuerverzinktem kaltband
US5686194A (en) * 1994-02-07 1997-11-11 Toyo Kohan Co., Ltd. Resin film laminated steel for can by dry forming
US5556485A (en) * 1994-11-07 1996-09-17 Bethlehem Steel Corporation Bake hardenable vanadium containing steel and method of making thereof
DE19543804B4 (de) * 1995-11-24 2004-02-05 Salzgitter Ag Verfahren zur Herstellung von feuerverzinktem Stahlband und damit hergestelltes feuerverzinktes Blech oder Band aus Stahl
DE19547181C1 (de) * 1995-12-16 1996-10-10 Krupp Ag Hoesch Krupp Verfahren zur Herstellung eines kaltgewalzten, höherfesten Bandstahles mit guter Umformbarkeit bei isotropen Eigenschaften
US5656102A (en) * 1996-02-27 1997-08-12 Bethlehem Steel Corporation Bake hardenable vanadium containing steel and method thereof
DE19622164C1 (de) * 1996-06-01 1997-05-07 Thyssen Stahl Ag Verfahren zur Erzeugung eines kaltgewalzten Stahlbleches oder -bandes mit guter Umformbarkeit
BE1011066A3 (fr) * 1997-03-27 1999-04-06 Cockerill Rech & Dev Acier au niobium et procede de fabrication de produits plats a partir de celui-ci.
DE19736509A1 (de) * 1997-08-22 1999-04-22 Krupp Ag Hoesch Krupp Verfahren zur Herstellung eines kaltgewalzten Ti-IF-Bandstahles mit hervorragender Umformbarkeit bei isotropen Eigenschaften
DE19834361A1 (de) * 1998-07-30 2000-02-03 Schaeffler Waelzlager Ohg Bauteil, insbesondere Wälzlager- und Motorenbauteil
DE19840788C2 (de) * 1998-09-08 2000-10-05 Thyssenkrupp Stahl Ag Verfahren zur Erzeugung von kaltgewalzten Bändern oder Blechen
EP1153145A1 (fr) * 1998-12-30 2001-11-14 Hille & Müller GmbH & Co. Feuillard d'acier presentant de bonnes proprietes de formage et son procede de production
DE10020118B4 (de) * 2000-04-22 2009-11-12 Schaeffler Kg Wälzlagerbauteil
DE10055338C1 (de) * 2000-11-08 2002-03-07 Thyssenkrupp Stahl Ag Verfahren zum Herstellen eines bei niedrigen Verformungsgraden kaltverformten Kaltbandes
DE10102932C1 (de) 2001-01-23 2002-08-22 Salzgitter Ag Verfahren zur Herstellung eines kalt gewalzten Bandes oder Bleches aus Stahl und nach dem Verfahren herstellbares Band oder Blech
KR20060028909A (ko) * 2004-09-30 2006-04-04 주식회사 포스코 형상 동결성이 우수한 고강도 냉연강판 및 그 제조방법
DE102012211458B3 (de) * 2012-07-03 2013-11-21 Schaeffler Technologies AG & Co. KG Deckel mit Ölspeicherfunktionalität für ein Gehäuse eines elektrohydraulischen Ventiltriebes eines Verbrennungsmotors
WO2023135550A1 (fr) 2022-01-13 2023-07-20 Tata Steel Limited Acier micro-allié à faible teneur en carbone laminé à froid et son procédé de fabrication

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Also Published As

Publication number Publication date
JPH0814003B2 (ja) 1996-02-14
WO1989007158A1 (fr) 1989-08-10
DE3843732A1 (de) 1990-07-05
DE3843732C2 (de) 2001-05-10
DE3803064C2 (de) 1995-04-20
DE58906176D1 (de) 1993-12-16
US5139580A (en) 1992-08-18
DE3803064C1 (en) 1989-04-06
DD285298A5 (de) 1990-12-12
GR1000537B (el) 1992-08-25
EP0400031B1 (fr) 1993-11-10
ES2018975A6 (es) 1991-05-16
DD285298B5 (de) 1999-01-28
EP0400031A1 (fr) 1990-12-05
JPH03503185A (ja) 1991-07-18

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