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EP0966547B1 - Procede permettant de fabriquer un feuillard d'acier a resistance et a malleabilite elevees - Google Patents

Procede permettant de fabriquer un feuillard d'acier a resistance et a malleabilite elevees Download PDF

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Publication number
EP0966547B1
EP0966547B1 EP98916911A EP98916911A EP0966547B1 EP 0966547 B1 EP0966547 B1 EP 0966547B1 EP 98916911 A EP98916911 A EP 98916911A EP 98916911 A EP98916911 A EP 98916911A EP 0966547 B1 EP0966547 B1 EP 0966547B1
Authority
EP
European Patent Office
Prior art keywords
steel
several
strip
max
hot
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
EP98916911A
Other languages
German (de)
English (en)
Other versions
EP0966547A1 (fr
Inventor
Bernhard Engl
Günter STICH
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.)
ThyssenKrupp Steel Europe AG
Original Assignee
ThyssenKrupp Stahl AG
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 ThyssenKrupp Stahl AG filed Critical ThyssenKrupp Stahl AG
Publication of EP0966547A1 publication Critical patent/EP0966547A1/fr
Application granted granted Critical
Publication of EP0966547B1 publication Critical patent/EP0966547B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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Classifications

    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—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
    • C21D2211/002—Bainite
    • 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

Definitions

  • the invention relates to a method for manufacturing a steel strip with a high strength of at least 900 MPa and good formability.
  • the parameters relevant for the forming can be done with high informative value for the practice from the tensile test be won. Especially the elongation at break and the Set the n-value (measure of the hardening capacity) important metrics.
  • the n-value is characteristic of the deformability under a stretch drawing stress. This is the case for most sheet metal parts in a vehicle prevailing deformation mechanism.
  • the n value stands in relatively good agreement with the Yield strength ratio, which is also a practical one usable measure of the strengthening ability of a Represents material.
  • DE-A-3323255 describes a process for the production of high steel strip Strength and good cold formability.
  • the steel defined in DE-A-3323255 lies within the ranges defined in claim 1.
  • the object of the invention is to develop steel strips, which has a high strength, paired with good Formability and high component strength.
  • the special economic importance of The inventive method consists in Production possibility as a hot strip in thicknesses below 2.0 mm, e.g. 1.5 mm.
  • the manufacturing process requires therefore not necessarily the complex manufacturing process cold strip production with the additional steps cold rolling and final annealing.
  • This material concept also includes the Possibility factory applied Surface finishing. For example, a electrolytically deposited zinc layer applied become. The enormous improvement in corrosion protection through a zinc layer can be a known fact be assumed. It is also known that ultra high strength steels for embrittlement by a Hydrogen absorption in the electrolytic Tending to galvanize. It could be shown that the steel strip according to the invention free of these dreaded galvanizing problems remains.
  • Carbon is required for structural hardening and for the formation of fine precipitates.
  • the content should be limited to 0.1 to 0.2%.
  • Silicon increases the hardness of the mixed crystal, which requires at least 0.3%. For reasons of weldability and to avoid unfavorable scale formation, the content should be limited to 0.6%.
  • Manganese at a content of at least 1.5% delays the conversion and causes the formation of hard conversion products. In order to avoid impermissibly strong micro segregations, the content should be max. Limit 2.0%.
  • Phosphorus can be used to further increase solid-solution strengthening, but should not exceed 0.08% for reasons of weldability.
  • Chromium promotes the formation of a bainite-rich final structure in at least 0.3%. In order not to delay the conversion too much, its content should be limited to max. Be limited to 0.80%.
  • Titanium or zirconium can be used to form fine precipitates with a hardening effect.
  • the effect clearly drops at levels above 0.2%.
  • the maximum value is therefore set at 0.2%.
  • Niobium can also be used for precipitation hardening. At least 0.04% should preferably be added. For reasons of effectiveness, the content is limited to max. 0.08% set.
  • Boron improves hardenability at levels in the range of 0.0005 to 0.005%. According to the current state of knowledge, it is used for this purpose in martensitic steel. It has surprisingly been found that boron in the present case also causes a significant increase in strength in the bainitic basic structure with only a slight reduction in formability.
  • the roller end temperature should be in the range of homogeneous Austenite and therefore not below 800 ° C to a sufficiently low deformation resistance guarantee and secondly deformation-induced Keep excretions low.
  • the cooling conditions should be chosen so that a Conversion to pearlite is avoided and the conversion largely in the bainite stage. Shares of Martensite can contribute to further solidification. Of further solidification by excretion of finest particles can be achieved.
  • This is a cooling of roll end temperature with a cooling rate of at least 30 ° C / s required. This cooling process is to finish at a temperature below 600 ° C by the Tape is wound on a reel and then in Coil cools down.
  • Table 1 shows the chemical compositions of the strip steels 1 and 2 and steel 3, a comparative martensitic steel, produced according to the invention.
  • Table 2 shows the characteristic mechanical properties of the strip steels 1 and 2 produced according to the invention and of the comparison steel 3, which was tempered to the values given in Table 2 by a subsequent heat treatment.
  • Strip steel produced according to the invention clearly. He points a higher elongation at break and a better one Yield strength ratio as a measure of the hardening.
  • Table 3 shows the influence of low reel temperature and a subsequent heat treatment on the properties of a strip steel produced according to the invention of the composition of steel 1 in Table 1.
  • Low reel temperatures of preferably 330 ° C can significantly increase the strength properties, see Example 4 in Table 3.
  • Another object of the invention is Achieving the beneficial effect of a subsequent one Heat treatment. It has surprisingly turned out to be found that the thermal treatment of the Steel strip produced according to the invention in the temperature range between 500 and 850 ° C the forming properties still can be further increased.
  • Examples 4, 5 and 6 in Table 3 show the effect such a heat treatment on the steel 1 with the Composition according to Table 1.
  • This property profile is useful for manufacturing of cold-formed parts with a high Energy absorption capacity (example 5a).
  • higher annealing temperatures can lead to high strengths extraordinarily low yield strength ratios or synonymous high consolidation with good Elongation values can be achieved (Examples 5b, 6a to 6c).

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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 (15)

  1. Procédé pour la fabrication d'un acier en feuillard, calmé à l'aluminium, ayant une résistance mécanique élevée d'au moins 900 MPa et une bonne formabilité, composé de (en % en masse)
    0,10 à 0,20 % de C
    0,30 à 0,60 % de Si
    1,50 à 2,00 % de Mn
    max. 0,08 % de P
    0,30 à 0,80 % de Cr
    jusqu'à 0,40 % de Mo
    jusqu'à 0,20 % de Ti et/ou Zr
    jusqu'à 0,08 % de Nb
    le reste étant constitué de Fe et d'impuretés inévitables, qui est fondu, coulé en brames et ensuite laminé en feuillard laminé à chaud, la température finale de laminage étant supérieure à 880°C, la vitesse de refroidissement sur le train de rouleaux de sortie étant d'au moins 30°C/s et la température du bobinage étant de 300 à 600°C.
  2. Procédé selon la revendication 1, caractérisé en ce que le feuillard laminé à chaud est enroulé à une température d'au maximum 550°C.
  3. Procédé selon la revendication 1, caractérisé en ce que le feuillard laminé à chaud est enroulé à une température d'au maximum 350°C.
  4. Procédé selon l'une quelconque des revendications 1 à 3, caractérisé en ce que le feuillard laminé à chaud est enroulé à une température non inférieure à 330°C.
  5. Procédé selon une ou plusieurs des revendications 1 à 4, caractérisé en ce que le feuillard laminé à chaud est laminé à une épaisseur finale de 2,0 mm au maximum.
  6. Procédé selon une ou plusieurs des revendications 1 à 5, caractérisé en ce que le feuillard laminé à chaud est dressé.
  7. Procédé selon une ou plusieurs des revendications 1 à 6, caractérisé en ce que le feuillard est décapé et muni d'un revêtement métallique.
  8. Procédé selon la revendication 7, caractérisé en ce que le revêtement métallique est appliqué par électrolyse.
  9. Procédé selon la revendication 7, caractérisé en ce que le revêtement métallique est appliqué par le procédé de revêtement métallique à chaud.
  10. Procédé selon une ou plusieurs des revendications 1 à 6, caractérisé en ce que le feuillard laminé à chaud est recuit dans la plage de 500 à 850°C.
  11. Procédé selon une ou plusieurs des revendications 1 à 6, caractérisé en ce qu'après le laminage à chaud, on effectue un laminage à froid d'au moins 30 % et un recuit continu à des températures comprises entre 700 et 900°C.
  12. Procédé selon l'une quelconque des revendications 1 à 11, caractérisé en ce qu'au maximum 0,15 % de Mo est allié à l'acier.
  13. Procédé selon une ou plusieurs des revendications 1 à 12, caractérisé en ce qu'au moins 0,04 % de Ti et/ou Zr est allié à l'acier.
  14. Procédé selon une ou plusieurs des revendications 1 à 13, caractérisé en ce que 0,0005 à 0,005 % de B est allié à l'acier.
  15. Procédé selon une ou plusieurs des revendications 1 à 14, caractérisé en ce qu'au moins 0,04 % de Nb est allié à l'acier.
EP98916911A 1997-03-13 1998-03-10 Procede permettant de fabriquer un feuillard d'acier a resistance et a malleabilite elevees Expired - Lifetime EP0966547B1 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE19710125A DE19710125A1 (de) 1997-03-13 1997-03-13 Verfahren zur Herstellung eines Bandstahles mit hoher Festigkeit und guter Umformbarkeit
DE19710125 1997-03-13
PCT/EP1998/001376 WO1998040522A1 (fr) 1997-03-13 1998-03-10 Procede permettant de fabriquer un feuillard d'acier a resistance et a malleabilite elevees

Publications (2)

Publication Number Publication Date
EP0966547A1 EP0966547A1 (fr) 1999-12-29
EP0966547B1 true EP0966547B1 (fr) 2001-10-04

Family

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Family Applications (1)

Application Number Title Priority Date Filing Date
EP98916911A Expired - Lifetime EP0966547B1 (fr) 1997-03-13 1998-03-10 Procede permettant de fabriquer un feuillard d'acier a resistance et a malleabilite elevees

Country Status (11)

Country Link
EP (1) EP0966547B1 (fr)
CN (1) CN1082549C (fr)
AR (1) AR010130A1 (fr)
AT (1) ATE206472T1 (fr)
CA (1) CA2284124A1 (fr)
CZ (1) CZ290944B6 (fr)
DE (2) DE19710125A1 (fr)
ES (1) ES2165157T3 (fr)
PL (1) PL186831B1 (fr)
WO (1) WO1998040522A1 (fr)
ZA (1) ZA982115B (fr)

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0966090A2 (fr) 1998-06-17 1999-12-22 Black & Decker Inc. Méthode et appareil pour charger des batteries
EP2028282A1 (fr) 2007-08-15 2009-02-25 ThyssenKrupp Steel AG Acier en phase double, produit plat à partir d'un tel acier en phase double et son procédé de fabrication
EP1399598B2 (fr) † 2001-06-26 2011-02-23 ThyssenKrupp Steel Europe AG Procede pour fabriquer des produits en acier de grande resistance et de bonne malleabilite, formes a froid a partir d'un feuillard lamine a chaud
EP2489748A1 (fr) 2011-02-18 2012-08-22 ThyssenKrupp Steel Europe AG Produit plat en acier laminé à chaud fabriqué à partir d'un acier à phase complexe et son procédé de fabrication
EP1577412B2 (fr) † 2002-12-24 2014-11-12 Nippon Steel & Sumitomo Metal Corporation Tole d'acier de haute resistance presentant une excellente aptitude a l'ebarbage et une excellente resistance a l'adoucissement dans une zone affectee par la chaleur et son procede de production

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KR100595947B1 (ko) 1998-09-29 2006-07-03 제이에프이 스틸 가부시키가이샤 고강도 박강판, 고강도 합금화 용융아연도금 강판 및이들의 제조방법
DE29818244U1 (de) * 1998-10-13 1998-12-24 Benteler Werke Ag Stahllegierung
DE19937271C2 (de) 1999-08-06 2003-01-09 Hille & Mueller Gmbh & Co Verfahren zur Herstellung von tiefzieh- oder abstreckziehfähigem, veredeltem Kaltband, sowie Kaltband, vorzugsweise zur Herstellung von zylindrischen Behältern und insbesondere Batteriebehältern
ATE464402T1 (de) * 1999-09-16 2010-04-15 Jfe Steel Corp Verfahren zur herstellung einer dünnen stahlplatte mit hoher festigkeit
RU2156312C1 (ru) * 2000-02-29 2000-09-20 Открытое акционерное общество "НОСТА" Способ производства катаных заготовок
FR2807068B1 (fr) * 2000-03-29 2002-10-11 Usinor Acier lamine a chaud a tres haute limite d'elasticite et resistance mecanique utilisable notamment pour la realisation de piece de vehicules automobiles
JP4085583B2 (ja) 2001-02-27 2008-05-14 Ｊｆｅスチール株式会社 高強度冷延溶融亜鉛メッキ鋼板およびその製造方法
EP1288322A1 (fr) 2001-08-29 2003-03-05 Sidmar N.V. Acier à tres haute résistance mécanique, procédé pour la production de cet acier et le produit obtenu
DE10153234A1 (de) * 2001-10-31 2003-05-22 Thyssenkrupp Stahl Ag Für die Herstellung von nichtkornorientiertem Elektroblech bestimmtes, warmgewalztes Stahlband und Verfahren zu seiner Herstellung
DE10161465C1 (de) * 2001-12-13 2003-02-13 Thyssenkrupp Stahl Ag Verfahren zum Herstellen von Warmband
FR2847270B1 (fr) * 2002-11-19 2004-12-24 Usinor Procede pour fabriquer une tole en acier resistant a l'abrasion et tole obtenue
FR2847271B1 (fr) * 2002-11-19 2004-12-24 Usinor Procede pour fabriquer une tole en acier resistant a l'abrasion et tole obtenue
US9999918B2 (en) 2005-10-20 2018-06-19 Nucor Corporation Thin cast strip product with microalloy additions, and method for making the same
US10071416B2 (en) 2005-10-20 2018-09-11 Nucor Corporation High strength thin cast strip product and method for making the same
US9149868B2 (en) 2005-10-20 2015-10-06 Nucor Corporation Thin cast strip product with microalloy additions, and method for making the same
ES2325962T3 (es) * 2006-10-30 2009-09-25 Thyssenkrupp Steel Ag Procedimiento para fabricar productos planos de acero a partir de un acero multifasico microaleado con boro.
PL1918405T3 (pl) * 2006-10-30 2009-10-30 Thyssenkrupp Steel Ag Sposób wytwarzania płaskich produktów stalowych z wielofazowej stali stopowej z krzemem
EP1918402B1 (fr) * 2006-10-30 2009-05-27 ThyssenKrupp Steel AG Procédé de fabrication de produits plats en acier à partir d'un acier formant une structure de phases complexes
ES2367713T3 (es) * 2007-08-15 2011-11-07 Thyssenkrupp Steel Europe Ag Acero de fase dual, producto plano de un acero de fase dual tal y procedimiento para la fabricación de un producto plano.
CN101555574B (zh) * 2008-04-11 2011-06-15 宝山钢铁股份有限公司 一种高回火抗力耐磨钢
WO2011100798A1 (fr) 2010-02-20 2011-08-25 Bluescope Steel Limited Nitratation d'acier au niobium et produit fabriqué par ce moyen
DE102010056264C5 (de) * 2010-12-24 2020-04-09 Voestalpine Stahl Gmbh Verfahren zum Erzeugen gehärteter Bauteile
CN102864377B (zh) * 2012-09-10 2015-05-20 山西太钢不锈钢股份有限公司 一种热轧带钢及其制造方法
KR102596515B1 (ko) 2014-12-19 2023-11-01 누코 코포레이션 열연 경량 마르텐사이트계 강판 및 이의 제조방법
CN105624570A (zh) * 2016-03-10 2016-06-01 绵阳市联合传动科技有限公司 高强度低碳合金钢制动鼓
CN107653361B (zh) * 2017-10-14 2020-02-18 上海鑫昌众星实业有限公司 一种深加工汽车钢板的制备工艺
DE102018122901A1 (de) * 2018-09-18 2020-03-19 Voestalpine Stahl Gmbh Verfahren zur Herstellung ultrahochfester Stahlbleche und Stahlblech hierfür

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Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0966090A2 (fr) 1998-06-17 1999-12-22 Black & Decker Inc. Méthode et appareil pour charger des batteries
EP1399598B2 (fr) † 2001-06-26 2011-02-23 ThyssenKrupp Steel Europe AG Procede pour fabriquer des produits en acier de grande resistance et de bonne malleabilite, formes a froid a partir d'un feuillard lamine a chaud
EP1577412B2 (fr) † 2002-12-24 2014-11-12 Nippon Steel & Sumitomo Metal Corporation Tole d'acier de haute resistance presentant une excellente aptitude a l'ebarbage et une excellente resistance a l'adoucissement dans une zone affectee par la chaleur et son procede de production
EP2028282A1 (fr) 2007-08-15 2009-02-25 ThyssenKrupp Steel AG Acier en phase double, produit plat à partir d'un tel acier en phase double et son procédé de fabrication
EP2028282B1 (fr) * 2007-08-15 2012-06-13 ThyssenKrupp Steel Europe AG Acier en phase double, produit plat à partir d'un tel acier en phase double et son procédé de fabrication
EP2489748A1 (fr) 2011-02-18 2012-08-22 ThyssenKrupp Steel Europe AG Produit plat en acier laminé à chaud fabriqué à partir d'un acier à phase complexe et son procédé de fabrication
WO2012110165A1 (fr) 2011-02-18 2012-08-23 Thyssenkrupp Steel Europe Ag Produit plat en acier laminé à chaud fabriqué à partir d'un acier à phase complexe et procédé de fabrication correspondant

Also Published As

Publication number Publication date
CZ321999A3 (cs) 2000-07-12
CN1252105A (zh) 2000-05-03
ATE206472T1 (de) 2001-10-15
CZ290944B6 (cs) 2002-11-13
WO1998040522A1 (fr) 1998-09-17
CA2284124A1 (fr) 1998-09-17
CN1082549C (zh) 2002-04-10
PL186831B1 (pl) 2004-03-31
ZA982115B (en) 1998-09-14
DE19710125A1 (de) 1998-09-17
PL335639A1 (en) 2000-05-08
EP0966547A1 (fr) 1999-12-29
AR010130A1 (es) 2000-05-17
ES2165157T3 (es) 2002-03-01
DE59801637D1 (de) 2001-11-08

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