EP0747496A1 - Titan enthaltendes warmgewalztes, hochfestes Stahlblech mit gute Tiefziehfähigkeit, und Verfahren zu ihrer Herstellung - Google Patents

Titan enthaltendes warmgewalztes, hochfestes Stahlblech mit gute Tiefziehfähigkeit, und Verfahren zu ihrer Herstellung Download PDF

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Publication number
EP0747496A1
EP0747496A1 EP96401006A EP96401006A EP0747496A1 EP 0747496 A1 EP0747496 A1 EP 0747496A1 EP 96401006 A EP96401006 A EP 96401006A EP 96401006 A EP96401006 A EP 96401006A EP 0747496 A1 EP0747496 A1 EP 0747496A1
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EP
European Patent Office
Prior art keywords
sheet
temperature
hot
point
speed
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
EP96401006A
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English (en)
French (fr)
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EP0747496B1 (de
Inventor
Pascal Teracher
Jean-Pierre Porcet
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
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Application filed by Sollac SA, Lorraine de Laminage Continu SA SOLLAC filed Critical Sollac SA
Publication of EP0747496A1 publication Critical patent/EP0747496A1/de
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    • 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
    • C21D8/0426—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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • 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
    • C21D8/0463—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 following hot rolling

Definitions

  • the invention relates to the steel industry. More specifically, it relates to the field of hot-rolled steel sheets which must have high strength and stampability properties, intended in particular for the automotive industry to form parts of vehicle structures.
  • HLE steels are steels microalloyed with niobium, titanium or vanadium. They have a high elastic limit, the minimum according to the grade can range from approximately 300 MPa to approximately 700 MPa, obtained thanks to a refinement of the ferritic grain and a fine hardening precipitation. However, their formability is limited, especially for the highest grades. They have a high elastic limit / tensile strength (R e / R m ) ratio.
  • the so-called “double phase” or “dual phase” steels have a microstructure composed of ferrite and martensite. Ferritic transformation is favored by rapid cooling of the sheet, from the end of the hot rolling, to a temperature below Ar 3 , followed by slow cooling in air. The martensitic transformation is then obtained by rapid cooling to a temperature below M s . For a given resistance level, these steels have excellent formability, but this degrades for resistances greater than 650 MPa, due to the large proportion of martensite that they contain.
  • the so-called "very low carbon bainitic structure"("ULCB) steels have an extremely fine low carbon bainite microstructure composed of ferrite in the form of slats and carbides. To obtain it, the ferritic transformation is inhibited by a micro-addition of boron, or even niobium. These steels make it possible to achieve very high strengths, greater than 750 MPa, but with fairly low formability and ductility.
  • TRIP transformation Induced Plasticity steels have a microstructure composed of ferrite, bainite and residual austenite. They allow very high resistances to be reached, but their weldability is very low due to their high carbon content.
  • hot-rolled sheet steels whose structure essentially contains ferrite hardened by precipitates of titanium carbide and / or niobium and martensite, or even residual austenite. These steels have the composition, expressed in weight percentages: C ⁇ 0.18%; 0.5 ⁇ If ⁇ 2.5%; 0.5 ⁇ Mn ⁇ 2.5%; P ⁇ 0.05%; S ⁇ 0.02%; 0.01 ⁇ Al ⁇ 0.1%; 0.02 ⁇ Ti ⁇ 0.5% and / or 0.03 ⁇ Nb ⁇ 1%, with C% ⁇ 0.05 + Ti / 4 + Nb / 8.
  • the object of the invention is to provide users of hot-rolled steel sheets with products which offer a very good compromise between high resistance levels, satisfactory formability and good weldability, as well as an integrity surface appearance.
  • the invention also relates to methods of manufacturing such sheets.
  • the sheets according to the invention differ from those known hitherto for the same uses first by their significantly lower silicon content, their ranges of titanium and niobium contents significantly tightened, and requirements more strict on the distribution of the different phases of the structure. And obtaining the structure, therefore the desired properties for the sheet, implies special conditions during the heat treatment which immediately follows the hot rolling.
  • Their composition and manufacturing method mean that these steels represent, in several respects, a combination of HLE steels and double phase steels.
  • FIGS. 1 and 2 show micrographs of sheets according to the invention.
  • a steel comprising (all the percentages are percentages by weight) a carbon content of less than or equal to 0, 12%, a manganese content between 0.5 and 1.5%, a silicon content less than or equal to 0.3%, a phosphorus content less than or equal to 0.1%, a lower sulfur content or equal to 0.05%, an aluminum content of between 0.01 and 0.1%, a chromium content of less than 1%, an effective titanium content (we will explain what this term means below) between 0 , 03 and 0.15% and a niobium content of between 0 and 0.05%.
  • the slab is then hot rolled on a strip train to form a sheet a few mm thick.
  • the sheet undergoes a heat treatment which makes it possible to give it a microstructure composed at least of 75% ferrite and at least 10% martensite.
  • Ferrite is hardened by precipitation of titanium carbides or carbonitrides, and also niobium carbides or carbonitrides if this element is present significantly.
  • the microstructure may optionally also include bainite and residual austenite.
  • the limited carbon content makes it possible to maintain good weldability of the steel, and to obtain the desired proportion of martensite.
  • Silicon is an alpha-element, which therefore promotes ferritic transformation. It is also hardening in solid solution.
  • the invention is based, among other things, on a very significant drop in the silicon content of the steel compared to the prior art illustrated by document EP 0 548 950.
  • the advantage of a significant drop in the content of silicon is that the surface appearance problems encountered on steels of the prior art arise, in fact, from an appearance on the surface of the slab, in the reheating furnace, of oxide Fe 2 SiO 4 which forms with FeO oxide a low melting eutectic. This eutectic penetrates into the grain boundaries and promotes the anchoring of the scale, which can therefore only be imperfectly removed during pickling.
  • Another advantage of this lowering of the silicon content is the improvement in the weldability of the steel.
  • the steels of the invention provided that the other specifications on their composition and method of manufacture are respected, tolerate having only low, or even very low, silicon contents.
  • phosphorus is alphagene and hardens. But its content should be limited to 0.1%, and may be as low as possible. Indeed, it would be likely, at high content, to form a mid-thickness segregation which could cause delamination. Furthermore, it can segregate at grain boundaries, which increases fragility.
  • Titanium is a micro-alloying element which forms precipitates of carbide and carbonitride hardening ferrite. Its addition is intended to obtain, thanks to this hardening, a high level of resistance. However, this effect is only obtained if titanium has the possibility of combining with carbon.
  • account must therefore be taken of the possibilities of titanium oxides, nitrides and sulfides. The significant formation of oxides can be easily avoided by adding aluminum during the deoxidation of the liquid steel. As for the quantities of nitrides and sulphides formed, they depend on the nitrogen and sulfur contents of the liquid steel.
  • titanium content not in the form of nitrides, sulfides or oxides (and therefore available to form carbides and carbonitrides) is between 0.03 and 0.15%. It is this content which is called “titanium content efficient "and which is shortened to" Ti eff % ".
  • Ti total % means the total titanium content of the steel
  • Ti eff % Ti total % - 3.4 x N% - 1.5 x S%.
  • This addition of titanium can advantageously be supplemented by an addition of niobium to achieve even higher resistance levels.
  • niobium makes the sheet more difficult to laminate.
  • adding titanium and niobium beyond the prescribed amounts is useless, as there would then be a saturation of the hardening effect.
  • the sheet can be wound, either immediately or after a stay in the air.
  • the sheet metal can then be wound, again with or without a prior stay in the air.
  • niobium nitrides and carbonitrides slows down the ferritic transformation. It is therefore desirable that the duration of the slow cooling step during which the ferritic transformation takes place is sufficient to ensure that this transformation takes place correctly. For procedure No. 1 which was previously described, we therefore recommend that step 1 last at least 8 s. For procedure No. 2, a minimum duration of step 2 of 5 s is recommended.
  • the micrograph in Figure 1 shows the structure of a steel corresponding to grade B with 0.030% titanium.
  • the cooling of the sheet after hot rolling was carried out according to procedure No. 2.
  • the clear areas are of equiaxed ferrite and represent 88% of the structure.
  • the dark areas are martensite, and represent almost the entire rest of the structure.
  • Figure 2 shows the structure of a steel corresponding to grade C with 0.060% titanium.
  • the cooling of the sheet after hot rolling was carried out according to procedure No. 2
  • the steels according to the invention can be used in particular to constitute parts of motor vehicle structures, such as chassis elements, wheel linings, suspension arms, as well as all stamped parts which must have a high resistance to mechanical stresses. .

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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)
EP96401006A 1995-06-08 1996-05-10 Titan enthaltendes warmgewalztes, hochfestes Stahlblech mit gute Tiefziehfähigkeit, und Verfahren zu ihrer Herstellung Revoked EP0747496B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR9506745A FR2735147B1 (fr) 1995-06-08 1995-06-08 Tole d'acier laminee a chaud a haute resistance et haute emboutissabilite renfermant du titane, et ses procedes de fabrication.
FR9506745 1995-06-08

Publications (2)

Publication Number Publication Date
EP0747496A1 true EP0747496A1 (de) 1996-12-11
EP0747496B1 EP0747496B1 (de) 2000-01-19

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ID=9479729

Family Applications (1)

Application Number Title Priority Date Filing Date
EP96401006A Revoked EP0747496B1 (de) 1995-06-08 1996-05-10 Titan enthaltendes warmgewalztes, hochfestes Stahlblech mit gute Tiefziehfähigkeit, und Verfahren zu ihrer Herstellung

Country Status (8)

Country Link
US (1) US5759297A (de)
EP (1) EP0747496B1 (de)
JP (1) JPH08337840A (de)
AT (1) ATE189008T1 (de)
CA (1) CA2178305A1 (de)
DE (1) DE69606227T2 (de)
ES (1) ES2143725T3 (de)
FR (1) FR2735147B1 (de)

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0851038A1 (de) * 1996-12-31 1998-07-01 Ascometal Stahl und Verfahren zur Formung eines Stahlwerkstückes durch kalte plastische Verarbeitung
WO2014019844A1 (en) * 2012-08-03 2014-02-06 Tata Steel Ijmuiden Bv A process for producing hot-rolled steel strip and a steel strip produced therewith
US9863026B2 (en) 2012-09-26 2018-01-09 Nippon Steel & Sumitomo Metal Corporation Dual phase steel sheet and manufacturing method thereof
WO2018091039A1 (de) * 2016-11-15 2018-05-24 Salzgitter Flachstahl Gmbh Verfahren zur herstellung von radschüsseln aus dualphasenstahl mit verbesserter kaltumformbarkeit
CN110100033A (zh) * 2016-12-23 2019-08-06 Posco公司 材质偏差小且表面质量优异的高强度热轧钢板及其制造方法

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
BE1013359A3 (fr) * 2000-03-22 2001-12-04 Centre Rech Metallurgique Procede pour la fabrication d'une bande en acier multiphase laminee a chaud.
US6669789B1 (en) 2001-08-31 2003-12-30 Nucor Corporation Method for producing titanium-bearing microalloyed high-strength low-alloy steel
US6837235B2 (en) * 2002-03-14 2005-01-04 Ssw Holdings Company, Inc. Porcelain oven rack
JP4470701B2 (ja) * 2004-01-29 2010-06-02 Ｊｆｅスチール株式会社 加工性および表面性状に優れた高強度薄鋼板およびその製造方法
US20070272231A1 (en) * 2006-05-25 2007-11-29 Ssw Holding Company, Inc. Oven rack having an integral lubricious, dry porcelain surface
CN103334057A (zh) * 2013-06-18 2013-10-02 首钢总公司 一种热轧马氏体钢及其生产方法
MX2018006061A (es) * 2015-11-19 2018-09-21 Nippon Steel & Sumitomo Metal Corp Lamina de acero laminada en caliente de alta resistencia y metodo de fabricacion de la misma.

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2362658A1 (de) * 1972-12-23 1974-07-18 Nippon Steel Corp Stahlblech mit hervorragender pressverformbarkeit und verfahren zu dessen herstellung
US4141761A (en) * 1976-09-27 1979-02-27 Republic Steel Corporation High strength low alloy steel containing columbium and titanium
EP0228756A1 (de) * 1984-07-17 1987-07-15 Kawasaki Steel Corporation Stahlbleche mit sehr niedrigem Kohlenstoffgehalt
JPS63118012A (ja) * 1986-11-07 1988-05-23 Sumitomo Metal Ind Ltd 低降伏比高張力厚鋼板の製造法
JPH01162723A (ja) * 1987-12-18 1989-06-27 Kobe Steel Ltd 伸びフランジ性の優れた高強度熱延薄鋼板の製造方法

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4033789A (en) * 1976-03-19 1977-07-05 Jones & Laughlin Steel Corporation Method of producing a high strength steel having uniform elongation
US4398970A (en) * 1981-10-05 1983-08-16 Bethlehem Steel Corporation Titanium and vanadium dual-phase steel and method of manufacture

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2362658A1 (de) * 1972-12-23 1974-07-18 Nippon Steel Corp Stahlblech mit hervorragender pressverformbarkeit und verfahren zu dessen herstellung
US4141761A (en) * 1976-09-27 1979-02-27 Republic Steel Corporation High strength low alloy steel containing columbium and titanium
EP0228756A1 (de) * 1984-07-17 1987-07-15 Kawasaki Steel Corporation Stahlbleche mit sehr niedrigem Kohlenstoffgehalt
JPS63118012A (ja) * 1986-11-07 1988-05-23 Sumitomo Metal Ind Ltd 低降伏比高張力厚鋼板の製造法
JPH01162723A (ja) * 1987-12-18 1989-06-27 Kobe Steel Ltd 伸びフランジ性の優れた高強度熱延薄鋼板の製造方法

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 12, no. 365 (C - 532) 29 September 1988 (1988-09-29) *
PATENT ABSTRACTS OF JAPAN vol. 13, no. 423 (C - 638) 20 September 1989 (1989-09-20) *

Cited By (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0851038A1 (de) * 1996-12-31 1998-07-01 Ascometal Stahl und Verfahren zur Formung eines Stahlwerkstückes durch kalte plastische Verarbeitung
FR2757877A1 (fr) * 1996-12-31 1998-07-03 Ascometal Sa Acier et procede pour la fabrication d'une piece en acier mise en forme par deformation plastique a froid
US5919415A (en) * 1996-12-31 1999-07-06 Ascometal Steel and process for the manufacture of a steel component formed by cold plastic deformation
WO2014019844A1 (en) * 2012-08-03 2014-02-06 Tata Steel Ijmuiden Bv A process for producing hot-rolled steel strip and a steel strip produced therewith
CN104520449A (zh) * 2012-08-03 2015-04-15 塔塔钢铁艾默伊登有限责任公司 一种用于生产热轧钢带的方法以及由此生产的钢带
CN104520449B (zh) * 2012-08-03 2016-12-14 塔塔钢铁艾默伊登有限责任公司 一种用于生产热轧钢带的方法以及由此生产的钢带
US10053757B2 (en) 2012-08-03 2018-08-21 Tata Steel Ijmuiden Bv Process for producing hot-rolled steel strip
US9863026B2 (en) 2012-09-26 2018-01-09 Nippon Steel & Sumitomo Metal Corporation Dual phase steel sheet and manufacturing method thereof
WO2018091039A1 (de) * 2016-11-15 2018-05-24 Salzgitter Flachstahl Gmbh Verfahren zur herstellung von radschüsseln aus dualphasenstahl mit verbesserter kaltumformbarkeit
CN110100033A (zh) * 2016-12-23 2019-08-06 Posco公司 材质偏差小且表面质量优异的高强度热轧钢板及其制造方法
CN110100033B (zh) * 2016-12-23 2021-04-20 Posco公司 材质偏差小且表面质量优异的高强度热轧钢板及其制造方法

Also Published As

Publication number Publication date
JPH08337840A (ja) 1996-12-24
EP0747496B1 (de) 2000-01-19
CA2178305A1 (fr) 1996-12-09
ATE189008T1 (de) 2000-02-15
FR2735147B1 (fr) 1997-07-11
US5759297A (en) 1998-06-02
ES2143725T3 (es) 2000-05-16
FR2735147A1 (fr) 1996-12-13
DE69606227D1 (de) 2000-02-24
DE69606227T2 (de) 2000-09-07

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