EP0747495A1 - Niob enthaltendes warmgewalztes, hochfestes Stahlblech mit gute Tiefziehfähigkeit, und Verfahren zu ihrer Herstellung - Google Patents

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

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Publication number
EP0747495A1
EP0747495A1 EP96401007A EP96401007A EP0747495A1 EP 0747495 A1 EP0747495 A1 EP 0747495A1 EP 96401007 A EP96401007 A EP 96401007A EP 96401007 A EP96401007 A EP 96401007A EP 0747495 A1 EP0747495 A1 EP 0747495A1
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EP
European Patent Office
Prior art keywords
sheet
temperature
hot
point
speed
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Granted
Application number
EP96401007A
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English (en)
French (fr)
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EP0747495B1 (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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Application filed by Sollac SA, Lorraine de Laminage Continu SA SOLLAC filed Critical Sollac SA
Publication of EP0747495A1 publication Critical patent/EP0747495A1/de
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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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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 are distinguished from those known hitherto for the same uses by their substantially lower silicon content, their ranges of niobium and titanium contents significantly tightened, and more stringent requirements 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.
  • FIG. 1 shows a micrograph of a sheet 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 between 0.01 and 0.1%, a chromium content less than or equal to 1%, a niobium content between 0.01 and 0.10%, and a effective titanium content (we will explain below what this term means) 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.
  • the ferrite is hardened by precipitation of niobium carbides or carbonitrides, and also of titanium 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.
  • Niobium and titanium are micro-alloying elements that form precipitates of carbide and carbonitride hardening ferrite. Their addition, which for titanium is only optional, aims to obtain, thanks to this hardening, a high level of resistance.
  • niobium increases the temperature of non-recrystallization of the steel, which results in a strong hardening of the austenite, and can cause a heterogeneity of grain size.
  • the precipitation of niobium carbides and carbonitrides slows down ferritic transformation. This is why, in order to obtain in the presence of niobium a sufficient formation of suitably hardened equiaxed ferrite, it is imperative to comply with one of the cooling schemes for hot-rolled sheet which will be described.
  • the hardening effect of the ferrite it provides is however only obtained if the 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.
  • the quantities of nitrides and sulphides formed they depend on the nitrogen and sulfur contents of the liquid steel.
  • titanium If it is not possible, during production 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 at most 0.05%. 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%.
  • 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.
  • the fixing of a minimum duration for the slow air cooling step of operation 3) of the two operating modes that have just been described is no longer imperative, the niobium not being sufficiently present to very significantly slow down the ferritic transformation.
  • Grade B considered during these two tests is particularly sensitive to this factor because its silicon content is not very high, and its phosphorus content is low, and this does not promote ferritic transformation, therefore the formation of martensite.
  • the hard phase is then formed of bainite and / or perlite.
  • the micrograph in FIG. 1 shows the structure of a steel corresponding to grade B with 0.050% niobium and 0.010% 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 85% of the structure.
  • the dark areas are martensite, and represent almost the entire rest 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 that must be highly resistant 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)
EP96401007A 1995-06-08 1996-05-10 Niob enthaltendes warmgewalztes, hochfestes Stahlblech mit gute Tiefziehfähigkeit, und Verfahren zu ihrer Herstellung Revoked EP0747495B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR9506746A FR2735148B1 (fr) 1995-06-08 1995-06-08 Tole d'acier laminee a chaud a haute resistance et haute emboutissabilite renfermant du niobium, et ses procedes de fabrication.
FR9506746 1995-06-08

Publications (2)

Publication Number Publication Date
EP0747495A1 true EP0747495A1 (de) 1996-12-11
EP0747495B1 EP0747495B1 (de) 2000-01-19

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ID=9479730

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EP96401007A Revoked EP0747495B1 (de) 1995-06-08 1996-05-10 Niob enthaltendes warmgewalztes, hochfestes Stahlblech mit gute Tiefziehfähigkeit, und Verfahren zu ihrer Herstellung

Country Status (9)

Country Link
US (1) US5817196A (de)
EP (1) EP0747495B1 (de)
JP (1) JPH093609A (de)
AT (1) ATE189007T1 (de)
BR (1) BR9602713A (de)
CA (1) CA2178306A1 (de)
DE (1) DE69606226T2 (de)
ES (1) ES2143726T3 (de)
FR (1) FR2735148B1 (de)

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2000005422A1 (de) * 1998-07-24 2000-02-03 Sms Schloemann-Siemag Aktiengesellschaft Verfahren und anlage zur herstellung von dualphasen-stählen
EP1002884A1 (de) * 1998-04-27 2000-05-24 Nkk Corporation Kaltgewalzte stahlplatte exzellenter formbarkeit, flachförmigen eigenschaften und eindellwiderstand, feuerverzinkte stahlplatte und verfahren zur deren herstellung
NL1016042C2 (nl) * 2000-08-29 2001-07-24 Corus Technology B V Warmgewalste stalen band, werkwijze voor het vervaardigen ervan, en een daarmee vervaardigde wielschijf.
WO2001071047A1 (fr) * 2000-03-22 2001-09-27 Centre De Recherches Metallurgiques, Association Sans But Lucratif Procede pour la fabrication d'une bande en acier multiphase laminee a chaud.
WO2004111279A2 (de) * 2003-06-18 2004-12-23 Sms Demag Aktiengesellschaft Verfahren und anlage zur herstellung von warmband mit dualphasengefüge
EP3658692B1 (de) 2017-07-25 2021-11-10 Tata Steel IJmuiden B.V. Stahlband, folie oder rohling zur herstellung eines warmgeschmiedeten teils, teil und verfahren zum warmumformen eines rohlings in ein teil

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0952233B1 (de) * 1998-04-21 2003-03-19 KABUSHIKI KAISHA KOBE SEIKO SHO also known as Kobe Steel Ltd. Walzdraht oder Stabstahl mit guter Kaltverformbarkeit und daraus hergestellte Maschinenteile
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
DE19910582A1 (de) 1999-03-10 2000-09-28 Mahle Gmbh Gebauter Kolben
EP1662014B1 (de) * 2003-06-12 2018-03-07 JFE Steel Corporation Stahlpatte und geschweisstes stahlrohr mit kleinem streckgrenzenverhältnis und hoher zähigkeit und herstellungsverfahren dafür
KR101619786B1 (ko) * 2010-01-08 2016-05-13 삼성디스플레이 주식회사 바텀 샤시의 제조 방법, 이에 따라 제조된 바텀 샤시, 액정 표시 장치의 제조 방법 및 이에 따라 제조된 액정 표시 장치
DE112015005690T8 (de) * 2014-12-19 2018-04-19 Nucor Corporation Warmgewalztes martensitisches Leichtbau-Stahlblech und Verfahren zum Herstellen desselben
EP3378961B1 (de) * 2015-11-19 2021-12-29 Nippon Steel Corporation Hochfestes warmgewalztes stahlblech und herstellungsverfahren dafür

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2037350A1 (de) * 1969-07-30 1971-02-11 Armco Steel Corp , Middletown, Ohio (VStA) Verfahren zur Verbesserung der Zähigkeit und Schweißbarkeit von hochfestem niedrig legiertem Elsengrobblech
DE2362658A1 (de) * 1972-12-23 1974-07-18 Nippon Steel Corp Stahlblech mit hervorragender pressverformbarkeit und verfahren zu dessen herstellung
FR2240960A1 (en) * 1973-08-13 1975-03-14 Albright & Wilson Low carbon steel containing niobium - coated with chromium to give good corrosion resistance
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
JPH05179397A (ja) * 1991-12-31 1993-07-20 Sumitomo Metal Ind Ltd 疲労強度の優れた熱延鋼板およびその製造方法

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE236258C (de) *
US4033789A (en) * 1976-03-19 1977-07-05 Jones & Laughlin Steel Corporation Method of producing a high strength steel having uniform elongation

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2037350A1 (de) * 1969-07-30 1971-02-11 Armco Steel Corp , Middletown, Ohio (VStA) Verfahren zur Verbesserung der Zähigkeit und Schweißbarkeit von hochfestem niedrig legiertem Elsengrobblech
DE2362658A1 (de) * 1972-12-23 1974-07-18 Nippon Steel Corp Stahlblech mit hervorragender pressverformbarkeit und verfahren zu dessen herstellung
FR2240960A1 (en) * 1973-08-13 1975-03-14 Albright & Wilson Low carbon steel containing niobium - coated with chromium to give good corrosion resistance
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
JPH05179397A (ja) * 1991-12-31 1993-07-20 Sumitomo Metal Ind Ltd 疲労強度の優れた熱延鋼板およびその製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 17, no. 597 (C - 1127) 2 November 1993 (1993-11-02) *

Cited By (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1002884A1 (de) * 1998-04-27 2000-05-24 Nkk Corporation Kaltgewalzte stahlplatte exzellenter formbarkeit, flachförmigen eigenschaften und eindellwiderstand, feuerverzinkte stahlplatte und verfahren zur deren herstellung
EP1002884A4 (de) * 1998-04-27 2006-04-05 Nippon Kokan Kk Kaltgewalzte stahlplatte exzellenter formbarkeit, flachförmigen eigenschaften und eindellwiderstand, feuerverzinkte stahlplatte und verfahren zur deren herstellung
WO2000005422A1 (de) * 1998-07-24 2000-02-03 Sms Schloemann-Siemag Aktiengesellschaft Verfahren und anlage zur herstellung von dualphasen-stählen
KR100578823B1 (ko) * 1998-07-24 2006-05-11 에스엠에스 데마그 악티엔게젤샤프트 복합 조직강을 제조하기 위한 방법 및 장치
WO2001071047A1 (fr) * 2000-03-22 2001-09-27 Centre De Recherches Metallurgiques, Association Sans But Lucratif Procede pour la fabrication d'une bande en acier multiphase laminee a chaud.
BE1013359A3 (fr) * 2000-03-22 2001-12-04 Centre Rech Metallurgique Procede pour la fabrication d'une bande en acier multiphase laminee a chaud.
US6821364B2 (en) 2000-03-22 2004-11-23 Centre De Recherches Metallurgiques A.S.B.L. Method of making a multiphase hot-rolled steel strip
NL1016042C2 (nl) * 2000-08-29 2001-07-24 Corus Technology B V Warmgewalste stalen band, werkwijze voor het vervaardigen ervan, en een daarmee vervaardigde wielschijf.
WO2004111279A2 (de) * 2003-06-18 2004-12-23 Sms Demag Aktiengesellschaft Verfahren und anlage zur herstellung von warmband mit dualphasengefüge
WO2004111279A3 (de) * 2003-06-18 2005-05-06 Sms Demag Ag Verfahren und anlage zur herstellung von warmband mit dualphasengefüge
CN100381588C (zh) * 2003-06-18 2008-04-16 Sms迪马格股份公司 双相组织结构热轧带的生产方法和设备
EP3658692B1 (de) 2017-07-25 2021-11-10 Tata Steel IJmuiden B.V. Stahlband, folie oder rohling zur herstellung eines warmgeschmiedeten teils, teil und verfahren zum warmumformen eines rohlings in ein teil

Also Published As

Publication number Publication date
ATE189007T1 (de) 2000-02-15
EP0747495B1 (de) 2000-01-19
ES2143726T3 (es) 2000-05-16
DE69606226T2 (de) 2000-09-07
CA2178306A1 (fr) 1996-12-09
FR2735148A1 (fr) 1996-12-13
JPH093609A (ja) 1997-01-07
BR9602713A (pt) 1998-04-22
DE69606226D1 (de) 2000-02-24
US5817196A (en) 1998-10-06
FR2735148B1 (fr) 1997-07-11

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