EP1398390B1 - Acier ferritique-martensitique possédant une resistance élevée ayant une fine microstructure - Google Patents

Acier ferritique-martensitique possédant une resistance élevée ayant une fine microstructure Download PDF

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Publication number
EP1398390B1
EP1398390B1 EP02020294A EP02020294A EP1398390B1 EP 1398390 B1 EP1398390 B1 EP 1398390B1 EP 02020294 A EP02020294 A EP 02020294A EP 02020294 A EP02020294 A EP 02020294A EP 1398390 B1 EP1398390 B1 EP 1398390B1
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EP
European Patent Office
Prior art keywords
hot
rolled strip
cooling
process according
temperature
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.)
Revoked
Application number
EP02020294A
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German (de)
English (en)
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EP1398390A1 (fr
Inventor
Andreas Nuss
Thomas Dr.-Ing. Heller
Bernhard Dr.-Ing. Engl
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 Steel AG
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Application filed by ThyssenKrupp Steel AG filed Critical ThyssenKrupp Steel AG
Priority to AT02020294T priority Critical patent/ATE316157T1/de
Priority to ES02020294T priority patent/ES2256378T3/es
Priority to EP02020294A priority patent/EP1398390B1/fr
Priority to DE50205631T priority patent/DE50205631D1/de
Publication of EP1398390A1 publication Critical patent/EP1398390A1/fr
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Classifications

    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following 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
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • 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

Definitions

  • the invention relates to a method for producing a high-strength hot strip which has an ultrafine grain structure.
  • a method for producing hot strips of this type is known from EP 1 001 041 Al.
  • the slabs After re-heating to not more than 1150 ° C, the slabs are hot rolled in several steps to hot strip.
  • the hot rolling is carried out at temperatures at which dynamic recrystallization of the steel occurs.
  • low reduction levels are set, which should be in the last rolling step 13% to 30% and in all the last step preceding rolling steps 4% to 20%.
  • the desired fine-grained austenitic structure of the hot strip to be adjusted, in which the grain diameter of the austenite in the range of less than 4 .mu.m, in particular less than 2 microns.
  • the hot strip obtained is rapidly heated to 350 to 600 ° C temperature cooled to cause the formation of fine-grained ferrite.
  • the cooling rate is not less than 30 ° C / s.
  • the temperature at which the strip is subsequently coiled is, according to the known method, adapted to the most favorable temperature for the respective steel.
  • the steel obtained by the known method is characterized by a good deformability and at the same time comparably high strength.
  • tensile strengths are achieved which regularly exceed 500 MPa and can be up to 763 MPa.
  • the yield point is in the range of at least 420 MPa to 645 MPa.
  • the yield ratio of the known steel is regularly in the range of at least 0.75.
  • steel sheets having a very fine microstructure are produced in the process known from EP-A-0 945 522.
  • C and other optional components up to 1.0 wt% Cr and up to 3.0 wt% Mn.
  • the steel strips produced from such a steel composition using a reeling temperature not specified may, inter alia, have a bainitic, a bainitic / martensitic, a martensitic, a pearlitic or a pearlitic / martensitic structure.
  • the hot strips produced in this way can have ferrite grain sizes of less than 3 ⁇ m with further scattering.
  • a hot strip (W) which in particular continuously cast finished in the form of reheated or used directly from the casting heat slabs, thin slabs or cast strip and then continuously cooled.
  • the cooling takes place in at least two consecutive cooling phases (t CK , t LK ) accelerated cooling to a final temperature.
  • the first cooling phase (t CK ) of accelerated cooling sets in at the latest three seconds after the final rolling pass of finish rolling and the hot strip (W) is cooled during the first cooling phase (t CK ) accelerated cooling at a cooling rate of at least 150 ° C / s.
  • this steel When a TRIP steel containing 0.2% by mass of C, 1.8% by mass of Al and 1.6% by mass of Mn, the remainder of iron and unavoidable impurities is processed in accordance with this process, this steel has a fine microstructure with ferrite grains, whose diameter is less than 3 microns.
  • EP-A-0 969 112 describes a process for producing a dual-phase steel in which a steel containing, in addition to iron and unavoidable impurities, as Compulsory constituents (in% by weight) 0.02-0.25% C and in addition Mn and / or Cr in respective amounts of 0.15-3.5%, Si, Al and / or P in total contents of 0, 02 - 4.0% and other optional constituents, hot rolled at a hot rolling end temperature of 780 - 880 ° C and then cooled at a cooling rate of more than 5 ° C / s to reel temperatures below 350 ° C.
  • Compulsory constituents in% by weight
  • Mn and / or Cr in respective amounts of 0.15-3.5%
  • Si, Al and / or P in total contents of 0, 02 - 4.0% and other optional constituents
  • EP-A-0 969 112 show that high Si contents, high Mn contents and, if present, high Cr contents have been processed there in each case.
  • the hot strips produced from these steels have a structure with ferrite grains whose diameter is regularly above 4 ⁇ m.
  • EP-A-0 969 112 A method comparable to the prior art according to EP-A-0 969 112 is known from EP-A-0 952 235.
  • a steel is processed, which in addition to other alloying elements (in wt .-%) 0.03 - 0.3% C, 0.5 - 3.5% Mn and / or 0.5 -3.5 Cr and optionally 0.5 to 3.0% Si.
  • the concrete examples given in EP-A-0 952 235 either have Si contents of more than 0.9% or contain no chromium. Insofar as the examples in question have a martensite content, this is below 5%.
  • the diameter of the ferrite grains is in each case above 5 ⁇ m.
  • a method is also known from JP 61-034116, with which hot strips can be produced with high strength.
  • a hot strip is hot rolled at a hot rolling end temperature of 700 - 850 ° C, then at a cooling rate of at least 5 ° C / s cooled and finally reeled at a less than 500 ° C to 200 ° C amounting reel temperature.
  • the tapes produced in this way achieve a minimum tensile strength of 700 MPa. Their deformability is low. Thus, they have yield strength ratios which are each above 0.75.
  • the object of the invention was therefore to provide a method with which can reliably produce hot strips, in which the combination of deformability and strength is further optimized.
  • a hot strip is obtained, the structure of which is formed substantially completely martensitic / ferritic and free of pearlite.
  • the hot strip has a microstructure whose ferrite grains are ultrafine. This is achieved by the interaction of the inventively given composition of the processed steel, the comparatively high hot rolling end temperature of 750 ° C to 900 ° C and the following on the hot rolling cooling to a low coiler temperature, the upper limit inventively set to 250 ° C and from this upper limit can reach to room temperature.
  • an average ferrite diameter is set for this purpose, which is as small as possible taking into account the respective required properties. It is in hot strips according to the invention, whose tensile strength is in the range of 700 MPa to 900 MPa, on average preferably at 2.5 microns. In contrast, in the case of higher-strength hot strips according to the invention, the average ferrite grain size is preferably set to less than 2 ⁇ m, in particular less than 1 ⁇ m, in order to ensure optimum deformability even at the high strengths.
  • niobium-containing hot strips produced by the process according to the invention show a significantly finer ferrite grain than hot strips produced in the same way and containing no niobium.
  • niobium in the steel composition used according to the invention has a favorable effect on the strength of the resulting hot strip. According to the invention it is therefore provided that in the steel used at least 0.03% by mass of niobium are present. The positive influences of niobium are particularly noticeable then noticeable when higher carbon steels are processed.
  • the strength of inventively produced hot strip is also decisively influenced by the height of its martensite content.
  • tensile strengths in the range from 700 MPa to 1000 MPa can be obtained.
  • hot strip according to the invention which has a tensile strength of up to 800 MPa, typically has a 60% to 90% ferritic microstructure.
  • the ferrite content is already limited to about 40% to 60%. If strengths of more than 900 MPa are required, the ferrite content is adjusted to 10% to about 45% in accordance with the invention.
  • the martensite content the desired strength can be produced in a targeted manner.
  • the good deformability on the one hand and the high strength on the other hand lead to a particularly good ratio of deformability and tensile strength of the hot strips produced according to the invention.
  • the yield ratio formed in the ratio of the yield strength to the tensile strength of hot strips produced according to the invention is regularly below 0.7, ie significantly below the value which can be ascertained in the hot strips produced by the known method.
  • Characteristic of the optimized combination of properties of inventive hot strips is also that their product of tensile strength (Rm) and elongation at break (AS) measured in the longitudinal direction of the resulting hot strip regularly at least 15,000 MPa *%.
  • hot strips produced according to the invention are particularly suitable for the production of thin-walled components with complex shapes, which nevertheless are capable of absorbing large forces.
  • sheets obtained from hot strips according to the invention can be used particularly well for the production of components and structural elements of vehicle bodies, which are able to withstand high loads at low wall thicknesses, correspondingly low weight and complex design.
  • the expression of ultrafine-grained microstructure inventively produced hot strips can be directly influenced.
  • cooling has a direct influence on the martensite content and, consequently, on the strength of the hot strips.
  • FIGS. 1 and 2 show micrographs of four hot strips produced according to different variants of the method according to the invention.
  • Diagrams 1 and 2 graphically show the results of the experiments described below.
  • the melts S1, S2 were high carbon steels. With the exception of the niobium contents, the alloys of both steels S1, S2 are essentially identical. However, steel S1 does not contain niobium, while steel S2 has niobium contents. On the basis of steels S1 and S2, it was thus possible to demonstrate which positive effects the presence of niobium has in a high-carbon steel alloy processed according to the invention.
  • the slabs were hot rolled in a rolling scale each to 3.5 mm thick hot strips. After leaving the hot rolling stand, the hot strips obtained have been cooled in two stages with interposed cooling pause controlled to the coiler temperature, before they have been coiled into coils. The cooling was carried out in the first section with a first cooling rate K1 up to a cooling stop temperature Ts, was then interrupted for a break with the duration P, before it has been continued in the second cooling section with a second cooling rate K2 to the coiling temperature HT.
  • the Abfihlungsstopptemperatur Ts was placed in the temperature range at which it comes to ferrite formation. In this way, in each case a specific ferrite content was deliberately set in the resulting hot strip.
  • test series V2 and V3 have been carried out.
  • the hot rolling end temperature was lower in the test series V2 than in the test series V1 and in the test series V3 lower than in the test series V2.
  • the hot rolling was finished at the same hot rolling end temperature as in the test series V2.
  • the hot rolling was not followed by a multi-stage cooling, but the cooling to reel temperature was carried out continuously with a single high cooling rate K1 in one go.
  • Fig. 1 the micrograph of a hot strip is shown, which consists of both a high carbon content and a content of niobium-containing melt S2 in the Series V4 with an uninterrupted cooling after hot rolling has been generated.
  • the average size of the ferrite grains determined by a conventional image analysis is 1 ⁇ m in this example.
  • FIG. 2 shows the micrograph of a hot strip produced from the low carbon content and a minimized silicon content melt S4 likewise produced in the test series V4.
  • the average size of the ferrite grains in this example is 1.6 ⁇ m.
  • the invention provides according to an advantageous embodiment, a range of cooling rate, ranging from 10 K / s to 1000 K / s.
  • the invention provides that with cooling rates of at least 50 K / s is working. Compliance with this minimum cooling rate ensures that the respectively desired fineness is always achieved.
  • test series V1 to V4 are in Diag. 1 again shown graphically.
  • FIG. 2 shows the tensile strength of the hot strips produced in accordance with the invention from the melts S1-S4 as a function of the ferrite content. It can be clearly seen that higher tensile strengths are achieved with decreasing ferrite contents in favor of increasing martensite contents. At the same time goes from Diag. 2 shows the potential of each alloy.
  • hot strips can be produced that are in the high tensile strength range of 900 MPa to 1100 MPa.
  • the low-carbon steel compositions S3 and S4 can be used to produce hot strips with tensile strengths of at least 700 MPa.
  • the alloying elements carbon, niobium and silicon are the most important control variables in this order, with which the material properties of the microstructures produced according to the invention can be determined via an ultrafine martensitic / ferritic microstructure with respect to the ferrite grains Allow hot strips to be adjusted.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Catalysts (AREA)

Claims (11)

  1. Procédé de production d'un feuillard à chaud à haute résistance, avec une résistance à la traction d'au moins 700 MPa, avec des rapports d'élasticité qui font au plus 0,65 dans la direction longitudinale et au plus 0,66 dans la direction transversale, et avec une structure de grains ultrafins ferritique/martensitique et exempte de perlite, qui compte au moins 15% de martensite et dans laquelle le diamètre moyen des grains de ferrite fait moins de 2,5 µm, comprenant les étapes suivantes:
    a) couler de l'acier en fusion contenant (en % en masse) C: 0,05 - 0,2 % Si: < 0,9 % P: < 0,06 % Mn: 0,6 - 1,2 % Al: < 0,05 % Cr: 0,02 - 0,6 % Nb: ≤ 0,08 % Ti: ≤ 0,08 % V: ≤ 0,08 % Mo: ≤ 0,4 % Cu: ≤ 1 % Ni: ≤ 1 %
    solde fer et impuretés inévitables, en un matériau brut tel que des brames ou des brames minces,
    b) laminer à chaud le matériau brut en un feuillard à chaud à une température finale de laminage à chaud de 750 °C à 950 °C,
    c) refroidir le feuillard à chaud obtenu à une température de bobinage allant de la température ambiante à 250 °C, avec une vitesse de refroidissement d'au moins 10 K/s
    d) bobiner le feuillard à chaud refroidi.
  2. Procédé selon la revendication 1, caractérisé en ce que le refroidissement du feuillard à chaud à la température de bobinage se fait en une étape.
  3. Procédé selon la revendication 1, caractérisé en ce que, lors du refroidissement jusqu'à la température de bobinage, le feuillard est d'abord refroidi avec une vitesse de refroidissement de 10 à 200 K/s jusqu'à une température intermédiaire de 600 - 700 °C, en ce que le refroidissement est ensuite interrompu pendant 2 à 6 secondes, et en ce que le feuillard à chaud est finalement refroidi avec une vitesse de refroidissement de 10 à 200 K/s jusqu'à la température de bobinage.
  4. Procédé selon la revendication 1, caractérisé en ce que l'acier en fusion contient au moins 0,03 % en masse de Nb
  5. Procédé selon l'une des revendications précédentes, caractérisé en ce que le diamètre moyen des grains de ferrite fait moins de 2 µm.
  6. Procédé selon l'une des revendications précédentes, caractérisé en ce que le diamètre moyen des grains de ferrite fait moins de 0,1 µm.
  7. Procédé selon l'une des revendications précédentes, caractérisé en ce que la vitesse de refroidissement est de 10 K/s à 1000 K/s.
  8. Procédé selon l'une des revendications précédentes, caractérisé en ce que le vitesse de refroidissement est d'au moins 50 K/s.
  9. Feuillard à chaud obtenu par le procédé selon l'une des revendications 1 à 6, caractérisé en ce que le produit de la résistance à la traction (Rm) et de l'allongement à la rupture (A5) fait au moins 15000 MPa*%.
  10. Feuillard à chaud selon la revendication 9, caractérisé en ce que sa résistance à la traction (Rm) est supérieure à 900 MPa.
  11. Feuillard à chaud selon l'une des revendications 9 et 10, caractérisé en ce que sa résistance à la traction va jusqu'à 1100 MPa.
EP02020294A 2002-09-11 2002-09-11 Acier ferritique-martensitique possédant une resistance élevée ayant une fine microstructure Revoked EP1398390B1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
AT02020294T ATE316157T1 (de) 2002-09-11 2002-09-11 Ferritisch/martensitischer stahl mit hoher festigkeit und sehr feinem gefüge
ES02020294T ES2256378T3 (es) 2002-09-11 2002-09-11 Acero ferritico/martensitico altamente resistente con estructura muy fina.
EP02020294A EP1398390B1 (fr) 2002-09-11 2002-09-11 Acier ferritique-martensitique possédant une resistance élevée ayant une fine microstructure
DE50205631T DE50205631D1 (de) 2002-09-11 2002-09-11 Ferritisch/martensitischer Stahl mit hoher Festigkeit und sehr feinem Gefüge

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP02020294A EP1398390B1 (fr) 2002-09-11 2002-09-11 Acier ferritique-martensitique possédant une resistance élevée ayant une fine microstructure

Publications (2)

Publication Number Publication Date
EP1398390A1 EP1398390A1 (fr) 2004-03-17
EP1398390B1 true EP1398390B1 (fr) 2006-01-18

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EP02020294A Revoked EP1398390B1 (fr) 2002-09-11 2002-09-11 Acier ferritique-martensitique possédant une resistance élevée ayant une fine microstructure

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EP (1) EP1398390B1 (fr)
AT (1) ATE316157T1 (fr)
DE (1) DE50205631D1 (fr)
ES (1) ES2256378T3 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101008066B (zh) * 2006-01-27 2010-05-12 宝山钢铁股份有限公司 抗拉强度高于1000MPa的热轧马氏体钢板及其制造方法

Families Citing this family (10)

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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
KR100937809B1 (ko) * 2005-03-31 2010-01-20 제이에프이 스틸 가부시키가이샤 열연강판, 그 제조방법 및 열연강판성형체
ES2325964T3 (es) * 2006-10-30 2009-09-25 Thyssenkrupp Steel Ag Procedimiento para fabricar productos planos de acero a partir de un acero multifasico aleado con silicio.
PL1918403T3 (pl) * 2006-10-30 2009-10-30 Thyssenkrupp Steel Ag Sposób wytwarzania płaskich produktów stalowych ze stali tworzącej strukturę martenzytyczną
DE102006053819A1 (de) * 2006-11-14 2008-05-15 Thyssenkrupp Steel Ag Verfahren zum Herstellen eines Bauteil durch Warmpresshärten und hochfestes Bauteil mit verbesserter Bruchdehnung
PL2553132T3 (pl) * 2010-03-29 2015-10-30 Arcelormittal Investigacion Y Desarrollo Sl Produkt stalowy z ulepszoną charakterystyką nierdzewienia w warunkach zasolonych
WO2011135700A1 (fr) 2010-04-28 2011-11-03 住友金属工業株式会社 Tôle d'acier biphasé laminée à chaud à excellente résistance dynamique, et son procédé de production
JP5610102B2 (ja) 2012-08-21 2014-10-22 新日鐵住金株式会社 鋼材
CN103667651B (zh) * 2013-11-28 2016-03-09 安徽银力铸造有限公司 一种汽车用高强度热轧钢的制备方法
KR102596515B1 (ko) 2014-12-19 2023-11-01 누코 코포레이션 열연 경량 마르텐사이트계 강판 및 이의 제조방법

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US4466842A (en) * 1982-04-03 1984-08-21 Nippon Steel Corporation Ferritic steel having ultra-fine grains and a method for producing the same
JPS6134116A (ja) * 1984-07-24 1986-02-18 Sumitomo Metal Ind Ltd 強靭性熱間圧延コイルの製造法
CA2273334C (fr) * 1996-11-28 2006-03-28 Nippon Steel Corporation Aciers a haute resistance ayant des proprietes d'absorption de chocs de forte energie et une methode pour les produire
WO1998041664A1 (fr) * 1997-03-17 1998-09-24 Nippon Steel Corporation Tole d'acier biphase a haute resistance ayant d'excellentes proprietes de deformation dynamique et son procede de preparation
BR9806204A (pt) * 1997-09-11 2000-02-15 Kawasaki Heavy Ind Ltd Chapa de aço laminada a quente que apresenta grãos finos com formabilidade aperfeiçoada, produção de chapa de aço laminada a quente ou laminada a frio.
DE19911287C1 (de) * 1999-03-13 2000-08-31 Thyssenkrupp Stahl Ag Verfahren zum Erzeugen eines Warmbandes

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101008066B (zh) * 2006-01-27 2010-05-12 宝山钢铁股份有限公司 抗拉强度高于1000MPa的热轧马氏体钢板及其制造方法

Also Published As

Publication number Publication date
ES2256378T3 (es) 2006-07-16
EP1398390A1 (fr) 2004-03-17
DE50205631D1 (de) 2006-04-06
ATE316157T1 (de) 2006-02-15

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