EP0747496B1 - 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
EP0747496B1
EP0747496B1 EP96401006A EP96401006A EP0747496B1 EP 0747496 B1 EP0747496 B1 EP 0747496B1 EP 96401006 A EP96401006 A EP 96401006A EP 96401006 A EP96401006 A EP 96401006A EP 0747496 B1 EP0747496 B1 EP 0747496B1
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EP
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Prior art keywords
sheet
temperature
point
subjected
rate
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Revoked
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EP96401006A
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English (en)
French (fr)
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EP0747496A1 (de
Inventor
Pascal Teracher
Jean-Pierre Porcet
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Sollac SA
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Sollac SA
Lorraine de Laminage Continu SA SOLLAC
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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 concerns the field hot-rolled steel sheets which should have high strength properties and drawability, especially 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.
  • TRIP transformation Induced Plasticity steels have a microstructure composed of ferrite, bainite and residual austenite. They allow reach very high resistances, 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 ⁇ A1 ⁇ 0.1%; 0.0 2 ⁇ 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 rolled steel sheets with hot products with a very good compromise between resistance levels good formability and good weldability, as well as a flawless surface.
  • the invention also relates to methods of manufacturing such sheets.
  • the sheets according to the invention are distinguished from those known hitherto for the same uses firstly by their substantially lower content in silicon, their ranges of titanium and niobium contents significantly narrowed, and stricter requirements on the distribution of the different phases of the structure. And obtaining the structure, therefore the desired properties for the sheet, involves special conditions during the heat treatment immediately following hot rolling.
  • Their composition and manufacturing method mean that these steels represent, in several respects, a combination of HLE steels and double steels phase.
  • a steel comprising (all percentages are percentages by weight) a lower carbon content or equal to 0.12%, a manganese content of between 0.5 and 1.5%, a content of silicon less than or equal to 0.3%, a phosphorus content less than or equal to 0.1%, sulfur content less than or equal to 0.05%, aluminum content between 0.01 and 0.1%, a chromium content of less than 1%, a content of effective titanium (we will explain below what this term means) 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 gives it a microstructure composed at least 75% ferrite and at least 10% martensite.
  • the ferrite is hardened by a precipitation of titanium carbides or carbonitrides, and also of carbides or niobium carbonitrides if this element is present significantly.
  • the microstructure may optionally also include bainite and austenite residual.
  • 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 likely, at high content, to form a mid-thickness segregation which could cause delamination. Furthermore, it can segregate at grain boundaries, which increases fragility.
  • chromium Although not strictly speaking necessary, an addition of chromium (limited at 1%) is recommended because it promotes the formation of martensite and the ferritic transformation.
  • 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 it is not possible, during preparation and casting, to drastically limit these nitrogen and sulfur contents, a sufficient amount of titanium must be added to the metal bath so that in the solidified metal, after precipitation nitrides and sulfides, the 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 “effective titanium content” and which is shortened to "Ti eff %".
  • Ti eff % Ti total % - 3.4 x N% - 1.5 x S%.
  • This addition of titanium can advantageously be supplemented by an addition niobium to achieve even higher resistance levels.
  • niobium makes the sheet more difficult to laminate.
  • adding titanium and niobium beyond the prescribed amounts is unnecessary, because we would then see 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 previous stay in the air.
  • niobium nitrides and carbonitrides slows down ferritic transformation. It is therefore desirable that the duration of the slow cooling step during which the ferritic transformation is sufficient to ensure the smooth running of this transformation. 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 stage 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 has was carried out according to procedure No. 2.
  • the clear areas are equiaxed ferrite and represent 88% of the structure.
  • the dark beaches are martensite, and represent almost the entire remainder of the structure.
  • Figure 2 shows the structure of a steel corresponding to the grade C with 0.060% titanium.
  • the cooling of the sheet after hot rolling has was carried out according to procedure No. 2
  • the equiaxed ferrite represents 86% of the structure.
  • the steels according to the invention can be used in particular to constitute parts of motor vehicle structures, such as chassis elements, wheel sails, suspension arms, as well as all stamped parts in front have a high resistance to mechanical stress.

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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)

Claims (6)

  1. Warmgewalztes Stahlblech hoher Festigkeit und guter Tiefziehfähigkeit, dadurch gekennzeichnet, dass seine Zusammensetzung, ausgedrückt in Gewichtsprozent
    C ≤ 0,12 %;
    0,5 ≤ Mn ≤ 1,5 %;
    0 ≤ Si 0,3 %;
    0 ≤ P ≤ 0,1 %;
    0 ≤ S ≤ 0,05 %;
    0,01 ≤ Al ≤ 0,1 %;
    0 ≤ Cr ≤ 1 %;
    0,03 ≤ Tieff ≤ 0,15 %, wobei bei Tieff der Gehalt an Titan nicht in Form von Nitriden, Sulfiden oder Oxiden ist;
    0 ≤ Nb ≤ 0,05 %;
    Rest Eisen und unvermeidbare Verunreinigungen ist; und dass seine Struktur wenigstens 75 % Ferrit umfasst, welches durch Fällung von Carbiden oder Carbonitriden von Ti oder von Ti und Nb gehärtet ist, wobei der Rest der Struktur wenigstens 10 % Martensit und ggf. Bainit und restliches Austenit umfaßt.
  2. Stahlblech nach Anspruch 1, dadurch gekennzeichnet, dass sein Gehalt an Nb zwischen 0,02 und 0,05 % beträgt.
  3. Verfahren zur Herstellung eines warmgewalzten Stahlblechs hoher Festigkeit und guter Tiefziehfähigkeit, dadurch gekennzeichnet, dass man
    Stahle erschmilzt und in Form einer Bramme vergießt, der eine Zusammensetzung entsprechend dem Blech nach Anspruch 1 aufweist;
    dann die besagte Bramme zu Blech warmwalzt, wobei das Walzen mit einer Temperatur zwischen dem Ar3-Punkt und 950°C beendet wird;
    dann das besagte Blech einer langsamen Abkühlung mit einer Geschwindigkeit von 2 bis 15°C/s während einer Dauer von weniger als 40 s bis zu einer Temperatur, die zwischen dem Ar1-Punkt und 730°C liegt, unterwirft;
    dann das besagte Blech einer schnellen Abkühlung mit einer Geschwindigkeit von 20 bis 150°C/s bis zu einer Temperatur kleiner oder gleich 300°C unterwirft.
  4. Verfahren zur Herstellung eines warmgewalzten Stahlblechs hoher Festigkeit und guter Tiefziehfähigkeit, dadurch gekennzeichnet, dass
    man Stahl erschmilzt und in Form einer Bramme vergießt, welcher die gleiche Zusammensetzung wie das Blech nach dem Anspruch 1 aufweist;
    dann die besagte Bramme zu Blech warmwalzt, wobei das Walzen bei einer Temperatur, die zwischen dem Ar3-Punkt und 950°C liegt, beendet wird,
    dann das besagte Blech wenigstens 10 s nach der Beendigung des Warmwalzens einer raschen Abkühlung mit einer Geschwindigkeit von 20 bis 150°C/s bis zu einer Temperatur unter dem Ar3-Punkt unterwirft;
    dann das besagte Blech einer langsamen Abkühlung mit einer Geschwindigkeit von 2 bis 15°C/s innerhalb eines Zeitraums von weniger als 40 s bis zu einer Temperatur, die zwischen dem Ar1-Punkt und 730°C liegt, unterwirft;
    dann das besagte Blech einer raschen Abkühlung mit einer Geschwindigkeit von 20 bis 150°C/s bis zu einer Temperatur unterhalb oder gleich 300°C unterwirft.
  5. Verfahren zur Herstellung eines warmgewalzten Stahlblechs hoher Festigkeit und guter Tiefziehfähigkeit, dadurch gekennzeichnet, dass
    man Stahl erschmilzt und in Form einer Bramme vergießt, welcher die gleiche Zusammensetzung wie das Blech nach dem Anspruch 2 aufweist;
    dann die besagte Bramme zu Blech warmwalzt, wobei das Walzen bei einer Temperatur, die zwischen dem Ar3-Punkt und 950°C liegt, beendet wird;
    dann das besagte Blech einer langsamen Abkühlung mit einer Geschwindigkeit von 2 bis 15°C/s während eines Zeitraums, der zwischen 8 und 40 s liegt, bis zu einer Temperatur, die zwischen dem Ar1-Punkt und 730°C, unterwirft;
    dann das besagte Blech einer raschen Abkühlung mit einer Geschwindigkeit von 20 bis 150°C/s bis zu einer Temperatur kleiner oder gleich 300°C unterwirft;
  6. Verfahren zur Herstellung eines warmgewalzten Stahlblechs hoher Festigkeit und guter Tiefziehfähigkeit, dadurch gekennzeichnet, dass
    man Stahl erschmilzt und in Form einer Bramme vergießt, welcher die gleiche Zusammensetzung wie das Blech nach dem Anspruch 2 aufweist;
    dann die Bramme zu einem Blech warmwalzt, wobei das Walzen bei einer Temperatur beendet wird, die zwischen dem Ar3-Punkt und 950°C liegt;
    dann das besagte Blech wenigstens 10 s nach Beendigung des Warmwalzens einer raschen Abkühlung mit einer Geschwindigkeit von 20 bis 150°C bis zu einer Temperatur unterhalb des Ar3-Punktes unterwirft;
    dann das besagte Stahlblech einer langsamen Abkühlung mit einer Geschwindigkeit von 2 bis 15°C/s während eines Zeitraums, der zwischen 5 und 40 Sekunden liegt, bis zu einer Temperatur, die zwischen dem Ar1-Punkt und 730°C liegt, unterwirft; und
    dann das besagte Blech einer schnellen Abkühlung mit einer Geschwindigkeit von 20 bis 150°C/s bis zu einer Temperatur unterhalb oder gleich 300°C unterwirft.
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 EP0747496A1 (de) 1996-12-11
EP0747496B1 true EP0747496B1 (de) 2000-01-19

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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)

Families Citing this family (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2757877B1 (fr) * 1996-12-31 1999-02-05 Ascometal Sa Acier et procede pour la fabrication d'une piece en acier mise en forme par deformation plastique a froid
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
US10053757B2 (en) 2012-08-03 2018-08-21 Tata Steel Ijmuiden Bv Process for producing hot-rolled steel strip
PL2896715T3 (pl) * 2012-09-26 2017-12-29 Nippon Steel & Sumitomo Metal Corporation Dwufazowa blacha stalowa cienka i sposób jej wytwarzania
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
WO2017085841A1 (ja) * 2015-11-19 2017-05-26 新日鐵住金株式会社 高強度熱延鋼板及びその製造方法
DE102016121905A1 (de) * 2016-11-15 2018-05-17 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung von Radschüsseln aus Dualphasenstahl mit verbesserter Kaltumformbarkeit
KR101917469B1 (ko) * 2016-12-23 2018-11-09 주식회사 포스코 재질편차가 적고 표면품질이 우수한 고강도 열연강판 및 그 제조방법

Family Cites Families (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3897280A (en) * 1972-12-23 1975-07-29 Nippon Steel Corp Method for manufacturing a steel sheet and product obtained thereby
US4033789A (en) * 1976-03-19 1977-07-05 Jones & Laughlin Steel Corporation Method of producing a high strength steel having uniform elongation
US4141761A (en) * 1976-09-27 1979-02-27 Republic Steel Corporation High strength low alloy steel containing columbium and titanium
US4398970A (en) * 1981-10-05 1983-08-16 Bethlehem Steel Corporation Titanium and vanadium dual-phase steel and method of manufacture
JPS6126756A (ja) * 1984-07-17 1986-02-06 Kawasaki Steel Corp 良化成処理性を有する極低炭素鋼板
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
JPH0745687B2 (ja) * 1987-12-18 1995-05-17 株式会社神戸製鋼所 伸びフランジ性の優れた高強度熱延薄鋼板の製造方法

Also Published As

Publication number Publication date
JPH08337840A (ja) 1996-12-24
ATE189008T1 (de) 2000-02-15
FR2735147A1 (fr) 1996-12-13
FR2735147B1 (fr) 1997-07-11
EP0747496A1 (de) 1996-12-11
CA2178305A1 (fr) 1996-12-09
DE69606227D1 (de) 2000-02-24
US5759297A (en) 1998-06-02
DE69606227T2 (de) 2000-09-07
ES2143725T3 (es) 2000-05-16

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