EP0835945A1 - Warmgewalztes Stahlblech zum Tiefziehen - Google Patents

Warmgewalztes Stahlblech zum Tiefziehen Download PDF

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Publication number
EP0835945A1
EP0835945A1 EP97402089A EP97402089A EP0835945A1 EP 0835945 A1 EP0835945 A1 EP 0835945A1 EP 97402089 A EP97402089 A EP 97402089A EP 97402089 A EP97402089 A EP 97402089A EP 0835945 A1 EP0835945 A1 EP 0835945A1
Authority
EP
European Patent Office
Prior art keywords
temperature
nickel
boron
steel sheet
titanium
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
Application number
EP97402089A
Other languages
English (en)
French (fr)
Other versions
EP0835945B1 (de
Inventor
Xavier Bano
Christian Giraud
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 EP0835945A1 publication Critical patent/EP0835945A1/de
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Publication of EP0835945B1 publication Critical patent/EP0835945B1/de
Anticipated expiration legal-status Critical
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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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0421—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper

Definitions

  • the present invention relates to a hot rolled steel sheet for deep drawing, from a band train.
  • steels with the best stamping properties are steels called 3C and 3C Ti.
  • These steels have compositions containing carbon, manganese, titanium and have very high levels of additives weak to soften the mechanical properties. They own nevertheless gamagenic elements like carbon and manganese whose contents are high enough to have a temperature of relatively low ferritic transformation, such as, for example, AR3 transformation temperature of 840 ° C for a thickness of 4.5 mm. It is necessary to laminate above this temperature, i.e. in the austenitic area to avoid laminating in the area two-phase austenite-ferrite, rolling domain which degrades the properties steel shaping.
  • the sheets made with these steels can be coated continuously on a galvanizing line to protect them against corrosion.
  • This coating method results in the sheets being subjected to a cycle thermal which causes in the steel of said sheets, by diffusion of carbon and nitrogen, an increase in the yield strength of steel and a decrease in its elongation.
  • the object of the invention is to provide a steel sheet having a on the other hand, high shaping properties for deep drawing, and on the other hand, comparable mechanical properties after rolling to hot and after continuous galvanizing.
  • FIG. 1 shows the influence of the carbon element contents, boron, copper plus nickel on the lowering of the AR3 transformation point.
  • Figure 2 shows the evolution of AR3 as a function of temperature for a steel containing 0.002% boron and a steel not containing no boron.
  • FIG. 3 shows the evolution of sheet metal processing in its production process.
  • the transformation point is lowered by the copper, nickel elements and boron without the hardening of the structure.
  • FIG. 1 shows the influence of the carbon element contents, boron, copper plus nickel on the lowering of the AR3 transformation point.
  • Copper and nickel provide sheet steel with improved corrosion resistance.
  • Carbon at a content of less than 0.08%, makes it possible to obtain good formatting properties.
  • Low carbon content ensures a limitation of the hardening of the matrix due to a low rate of carburetted phases.
  • titanium in over-stoichiometry (3.4 ⁇ Ti / N ⁇ 10) precipitates during cooling in the form of titanium carbide and thus traps part of the carbon in the steel.
  • the Ti / N ratio must remain less than 10 to avoid precipitation hardening of carbide titanium.
  • titanium content must therefore be limited to avoid hardening by the precipitates.
  • titanium precipitated in the form of TIC can be an advantage for steels for enameling because it allows the conservation of the mechanical properties after the sheet metal shaping and thermal enamelling treatment.
  • boron in particular is to control the germination and growth of ferrite and thus obtain good setting properties shape, properties which are characterized by an elongation of the steel improved.
  • Boron on the other hand precipitates with carbon in the form of borocarbons or segregations at grain boundaries.
  • the starting point of ferritic transformation decreases with increasing temperature rolling.
  • two-phase rolling leads to type defects orange peel on the surface linked to the magnification of the ferritic grain with degraded formatting properties.
  • Figure 2 shows the evolution of AR3 as a function of temperature for a steel containing 0.002% boron and a steel not containing no boron.
  • boron helps control the ferritic transformation start temperature in association with end of rolling temperature.
  • titanium and boron allows their precipitation to keep the mechanical properties obtained after hot rolling at during heat treatment on the galvanizing line.
  • the rolling temperature is chosen so that it is 10 ° C to 120 ° C higher than the point value AR3 transformation to avoid rolling in the austenite domain ferrite unfavorable for shaping properties.
  • Figure 3 shows the evolution of the heat treatment of the sheet in its manufacturing process.
  • a time of less than 10 seconds is necessary before the first cooling heat treatment, the cooling being carried out with a speed of between 3 ° C / s and 80 ° C / s depending on the thickness of the laminated sheet, which ensures controlled and homogeneous germination of ferrite.
  • the structure final composed of cementite ferrite ensures, on the one hand, resistance mechanical between 250 MPa and 370 MPa and, on the other hand, a limit elasticity between 180 MPa and 280 MPa as well as an elongation more than 30%.
  • the hot rolling temperature is chosen at the point value transformation AR3 plus 20 ° C. Cooling started 1.5 second after hot rolling is performed at 30 ° C per second until a temperature of 680 ° C. Elongations of hot rolled sheet according to the invention can reach 36% for sheet thicknesses between 1.8 and 2.8 mm and values greater than 40% for sheet thicknesses between 3 and 8 mm.
  • Table 1 shows two other compositions of the steel sheet according to the invention.
  • the temperature at the start of the ferritic transformation AR3, respectively for sheet A and sheet B, is 818 ° C and 842 ° C.
  • thermomechanical treatment of the two sheets according to the invention involves rolling at a temperature of 900 ° C, winding at a temperature of 700 ° C., the cooling of the sheets having been carried out at a speed of 25 ° C per second.
  • Table 2 presents the mechanical characteristics of the two examples of sheets A and B. Re (MPA) Rm (MPa) AT (%) Sheet A 246 344 43 Sheet B 244 328 43.4
  • Table 3 presents, for a sheet A, the so-called raw mechanical characteristics obtained before thermal galvanizing treatment and the mechanical characteristics after thermal galvanizing treatment at 700 ° C. and 600 ° C.
  • Raw sheet metal 700 ° C 600 ° C Re (MPa) 246 262 246 Rm (MPa) 344 350 348 AT (%) 43 43.3 36.3
  • the rate of temperature rise is between 3 ° C / s and 20 ° C / s, speed generally being 8 ° C / s.
  • the holding temperature is between 550 ° C and 850 ° C, the current temperature being 700 ° C, with a holding time of 20 s to 120 s and preferably 60 s.
  • This temperature rise is followed by cooling at a rate between 3 ° C / s and 25 ° C / s, the typical speed value cooling being 10 ° C / s. Cooling is carried out until temperature of the galvanizing bath, at 450 ° C.
  • the steel sheet according to the invention comprises, for a thickness between 1.5 mm and 8 mm of the mechanical characteristics comparable between the raw state of hot rolling and the galvanized state.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)
  • Laminated Bodies (AREA)
  • Adhesives Or Adhesive Processes (AREA)
  • Lining Or Joining Of Plastics Or The Like (AREA)
EP97402089A 1996-09-19 1997-09-08 Warmgewalztes Stahlblech zum Tiefziehen Expired - Lifetime EP0835945B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR9611413 1996-09-19
FR9611413A FR2753399B1 (fr) 1996-09-19 1996-09-19 Tole d'acier lamine a chaud pour emboutissage profond

Publications (2)

Publication Number Publication Date
EP0835945A1 true EP0835945A1 (de) 1998-04-15
EP0835945B1 EP0835945B1 (de) 2003-03-19

Family

ID=9495878

Family Applications (1)

Application Number Title Priority Date Filing Date
EP97402089A Expired - Lifetime EP0835945B1 (de) 1996-09-19 1997-09-08 Warmgewalztes Stahlblech zum Tiefziehen

Country Status (11)

Country Link
US (1) US5873957A (de)
EP (1) EP0835945B1 (de)
JP (1) JPH10102198A (de)
KR (1) KR19980024716A (de)
AT (1) ATE234944T1 (de)
CA (1) CA2215570A1 (de)
DE (1) DE69719898T2 (de)
DK (1) DK0835945T3 (de)
ES (1) ES2193338T3 (de)
FR (1) FR2753399B1 (de)
PT (1) PT835945E (de)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3524790B2 (ja) * 1998-09-30 2004-05-10 株式会社神戸製鋼所 塗膜耐久性に優れた塗装用鋼材およびその製造方法
EP2166121A1 (de) * 1999-09-16 2010-03-24 JFE Steel Corporation Dünne Stahlplatte mit höher Festigkeit und Verfahren zu deren Herstellung
FR2798676B1 (fr) * 1999-09-20 2001-10-26 Lorraine Laminage Tole d'acier lamine a chaud pour emaillage une ou deux faces
US7005016B2 (en) * 2000-01-07 2006-02-28 Dofasco Inc. Hot rolled steel having improved formability

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2133744A1 (de) * 1971-07-07 1973-01-25 Thyssen Huette Ag Die verwendung eines vollberuhigten stahles fuer bauteile aus warmgewalztem band
US4080225A (en) * 1976-10-08 1978-03-21 Alan Wood Steel Company Low temperature, weldable, low alloy steel
EP0320003A1 (de) * 1987-12-11 1989-06-14 Nippon Steel Corporation Verfahren zur Herstellung von Stahl mit niedrigem Verhältnis der Elastizitätsgrenze zur Bruchfestigkeit
EP0620289A1 (de) * 1992-10-30 1994-10-19 JAPAN CASTING & FORGING CORPORATION Hochfester warmgewalstes stahlblech mit hervorragender gleichmässiger dehmung nach der kaltverformung und herstellungsverfahren
JPH07316649A (ja) * 1994-05-20 1995-12-05 Sumitomo Metal Ind Ltd 加工性と耐食性に優れた熱延鋼板の製造方法

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5454883A (en) * 1993-02-02 1995-10-03 Nippon Steel Corporation High toughness low yield ratio, high fatigue strength steel plate and process of producing same

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2133744A1 (de) * 1971-07-07 1973-01-25 Thyssen Huette Ag Die verwendung eines vollberuhigten stahles fuer bauteile aus warmgewalztem band
US4080225A (en) * 1976-10-08 1978-03-21 Alan Wood Steel Company Low temperature, weldable, low alloy steel
EP0320003A1 (de) * 1987-12-11 1989-06-14 Nippon Steel Corporation Verfahren zur Herstellung von Stahl mit niedrigem Verhältnis der Elastizitätsgrenze zur Bruchfestigkeit
EP0620289A1 (de) * 1992-10-30 1994-10-19 JAPAN CASTING & FORGING CORPORATION Hochfester warmgewalstes stahlblech mit hervorragender gleichmässiger dehmung nach der kaltverformung und herstellungsverfahren
JPH07316649A (ja) * 1994-05-20 1995-12-05 Sumitomo Metal Ind Ltd 加工性と耐食性に優れた熱延鋼板の製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 096, no. 004 30 April 1996 (1996-04-30) *

Also Published As

Publication number Publication date
DE69719898D1 (de) 2003-04-24
DK0835945T3 (da) 2003-06-23
ES2193338T3 (es) 2003-11-01
FR2753399A1 (fr) 1998-03-20
JPH10102198A (ja) 1998-04-21
DE69719898T2 (de) 2004-03-04
CA2215570A1 (fr) 1998-03-19
PT835945E (pt) 2003-06-30
US5873957A (en) 1999-02-23
FR2753399B1 (fr) 1998-10-16
EP0835945B1 (de) 2003-03-19
KR19980024716A (ko) 1998-07-06
ATE234944T1 (de) 2003-04-15

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