EP0750049A1 - Ferritischer Stahl und Verfahren zu seiner Herstellung und Verwendung - Google Patents

Ferritischer Stahl und Verfahren zu seiner Herstellung und Verwendung Download PDF

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Publication number
EP0750049A1
EP0750049A1 EP96107884A EP96107884A EP0750049A1 EP 0750049 A1 EP0750049 A1 EP 0750049A1 EP 96107884 A EP96107884 A EP 96107884A EP 96107884 A EP96107884 A EP 96107884A EP 0750049 A1 EP0750049 A1 EP 0750049A1
Authority
EP
European Patent Office
Prior art keywords
steel
temperature
hot
less
mass
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.)
Withdrawn
Application number
EP96107884A
Other languages
German (de)
English (en)
French (fr)
Inventor
Bertram Ehrhardt
Thomas Heidelauf
Thomas Wilhelm Schaumann
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.)
Thyssen Stahl AG
Original Assignee
Thyssen 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
Priority claimed from DE19605696A external-priority patent/DE19605696C2/de
Application filed by Thyssen Stahl AG filed Critical Thyssen Stahl AG
Publication of EP0750049A1 publication Critical patent/EP0750049A1/de
Withdrawn legal-status Critical Current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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D2211/005—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 ferritic steel, a method for producing this steel with a predominantly polygonal-ferritic structure and one or more carbon-enriched second phases, and a preferred use of this steel.
  • the steel should have high strength and good formability as well as improved surface quality after hot forming in the last production stage.
  • Dual-phase steels which have a structure, e.g. B. from up to 80 vol .-% of polygonal relatively soft ferrite and the rest of carbon-rich martensite.
  • the carbon-rich second phase which is present in smaller quantities, is embedded in the island in the pre-eutectoid ferritic phase.
  • Such a steel has good mechanical properties and favorable cold formability.
  • Known steels with predominantly polygonal ferrite in the structure and martensite embedded therein consist of (in mass%) 0.03 to 0.12% C, up to 0.8% Si and 0.8 to 1.7% Mn (DE 29 24 340 C2) or 0.02 to 0.2% C, 0.05 to 2.0% Si, 0.5 to 2% Mn, 0.3 to 1.5% Cr and up to 1% Cu, Ni and Mo (EP 0 072 867 B1). Both steels are calmed with aluminum and contain soluble residual contents of less than 0.1% Al. Silicon in these steels promotes ferrite transformation. In combination with manganese and if necessary, chromium is suppressed to form pearlite.
  • a steel with (in mass%) 0.05 to 0.3% carbon 0.8 to 3.0% manganese 0.4 to 2.5% aluminum 0.01 to 0.2% silicon less than 0.08% phosphorus less than 0.05% sulfur Balance iron including unavoidable impurities proposed with a structure consisting predominantly of polygonal ferrite and smaller proportions of martensite and / or bainite and / or residual austenite, which with a carbon equivalent (C eq. ) of greater than 0.1 to 0.325 C.
  • equ. % C + 1/20% Mn + 1/20% Cr + 1/15% Mo
  • the desired conversion to bainite or martensite in a previously formed ferrite matrix results in a favorable residual stress state of the structure with a positive influence on the cold forming ability.
  • the level of tensile strength is increased compared to a ferritic-pearlitic structure, as is the case in the known hot-rolled structural steels (St 37 to St 52).
  • the higher strength offers the possibility of reducing the thickness and thus saving weight.
  • Such a steel not only achieves the good strength level of known silicon-alloyed dual-phase steels, but also has improved surface quality after the hot forming, as is e.g. for wheel disks of motor vehicles, which are produced by cold forming the hot-rolled steel.
  • the following additional elements can be added to the steel up to the specified amounts (in mass%): up to 0.05% titanium up to 0.8% chromium up to 0.5% molybdenum up to 0.8% copper up to 0.5% nickel.
  • Characteristic of the steel according to the invention is the aluminum content, which is considerably increased compared to known steels with 0.4-2.5%.
  • the silicon content was limited to less than 0.2% according to the invention.
  • known steels of this type mostly had silicon contents of over 1%.
  • the steels alloyed with aluminum according to the invention have the desired pearlite-free two- or multi-phase structure and have excellent strength properties. Above all, the surface quality of the thermoformed product is much better than that of previously known silicon alloyed steels.
  • Aluminum ensures an extensive formation of globular ferrite with a content in the range of 0.4 to 2.5%. The formation of pearlite is delayed more than that of silicon-alloyed steels and can be safely avoided if the claimed process parameters are observed.
  • the carbon content of 0.05 to 0.3% is within the normal range for generic steels.
  • Manganese is added in an amount of 0.8 to 3.0% in order to avoid the formation of pearlite and to enrich the austenite in addition to carbon. Manganese has a solidifying effect and increases the strength level. The contents of carbon and manganese are interchangeable under the aspects of pearlite avoidance and effects on ferrite formation within the framework set by the carbon equivalent.
  • Carbon equivalence values higher than 0.1% result in higher aluminum contents.
  • the intersection of the carbon equivalent value and the corresponding aluminum value should lie in the shaded area in FIG. 1 in order to ensure a ferrite content of over 70% and suppression of pearlite formation under large-scale production conditions.
  • the carbon equivalent value should ensure a max. 0.325 can be limited.
  • titanium up to 0.05% ensures nitrogen removal and prevents the formation of elongated manganese sulfides.
  • Chromium in an amount of up to 0.8% can be added to improve the martensite resistance and to prevent pearlite formation.
  • molybdenum increases the range of successful cooling rates.
  • Copper and nickel in an amount of up to 0.5% each can help lower the transition temperature and prevent pearlite.
  • the hot rolling end temperature ET should be in the range of Ar3 - 50 ° C ⁇ ET ⁇ Ar3 + 100 ° C lie.
  • the cooling of the hot rolling end temperature to the reel temperature between room temperature and 500 ° C is accelerated with a cooling rate of 15 to 70 K / s.
  • the process according to the invention can further promote the formation of ferrite in the range from Ar3 to Ar3 - 200 ° C. by taking a cooling break of 2 to 30 s, in which the cooling rate is below 15 K / s.
  • Fig. 2 shows a schematic representation of the production of hot strip coupled with the cooling process of the steel according to the invention during and after hot rolling.
  • a steel A according to the invention with the values according to Table 1 was hot-rolled to a final strip thickness of 3.7 mm with a hot-rolling end temperature of 875 ° C.
  • the cooling from this temperature was carried out at 30 K / s to the reel temperatures (HT) given in Table 2.
  • the properties of this steel A according to the invention were determined on flat tensile specimens in accordance with DIN EN 10002.
  • the reel temperature was varied between 80 ° C and 350 ° C.
  • the strength values determined in each case make it clear that the steel according to the invention has very good properties in the entire reel area, which at least correspond to those of the known silicon-alloyed comparison steel B.
  • Table 2 also shows the mechanical properties of a steel C according to the invention of the composition according to Table 1.
  • the results were determined on a round tensile specimen with a diameter of 4 mm.
  • the hot rolling was simulated by a flat compression test.
  • the values were measured in the longitudinal direction (material flow direction).
  • the reel temperature was 200 ° C for the first sample and 400 ° C for the second sample.
  • This steel also has the favorable range of mechanical properties; but also better surface quality than steel B.
  • Table 2 The results reported in Table 2 make it clear that the yield ratio in the entire range of the reel temperature is below 0.8.
  • Table 1 (Chemical composition) stole C% Mn% Si% P% Al% Cr% N% S% C equ A 0.076 1.45 0.053 0.019 1.23 0.35 0.002 ⁇ 0.001 0.16 B * 0.090 0.38 0.71 0.013 0.025 0.62 0.006 0.009 0.14 C. 0.090 1.51 0.03 ⁇ 0.005 1.19 0.50 0.005 0.004 0.19 D 0.20 1.49 0.04 ⁇ 0.005 1.99 0.02 0.005 0.004 0.27 *) Comparative steel

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Cleaning And De-Greasing Of Metallic Materials By Chemical Methods (AREA)
EP96107884A 1995-06-16 1996-05-17 Ferritischer Stahl und Verfahren zu seiner Herstellung und Verwendung Withdrawn EP0750049A1 (de)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
DE19521836 1995-06-16
DE19521836 1995-06-16
DE19605696A DE19605696C2 (de) 1995-06-16 1996-02-16 Ferritischer Stahl und Verfahren zu seiner Herstellung und Verwendung
DE19605696 1996-02-16

Publications (1)

Publication Number Publication Date
EP0750049A1 true EP0750049A1 (de) 1996-12-27

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ID=26016011

Family Applications (1)

Application Number Title Priority Date Filing Date
EP96107884A Withdrawn EP0750049A1 (de) 1995-06-16 1996-05-17 Ferritischer Stahl und Verfahren zu seiner Herstellung und Verwendung

Country Status (10)

Country Link
EP (1) EP0750049A1 (xx)
CN (1) CN1190997A (xx)
AR (1) AR002501A1 (xx)
BR (1) BR9608672A (xx)
CA (1) CA2224817A1 (xx)
CZ (1) CZ402497A3 (xx)
HU (1) HUP9801908A3 (xx)
PL (1) PL324555A1 (xx)
TR (1) TR199701720T1 (xx)
WO (1) WO1997000332A1 (xx)

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
NL1007739C2 (nl) * 1997-12-08 1999-06-09 Hoogovens Staal Bv Werkwijze en inrichting voor het vervaardigen van een stalen band met hoge sterkte.
AU756917B2 (en) * 1996-06-07 2003-01-30 Corus Staal B.V. Process and device for producing a high-strength steel strip
US6616778B1 (en) 1997-12-08 2003-09-09 Corus Staal Bv Process and device for producing a ferritically rolled steel strip
EP1642990A1 (en) * 2003-06-19 2006-04-05 Nippon Steel Corporation High strength steel plate excellent in formability and method for production thereof
DE10327383C5 (de) * 2003-06-18 2013-10-17 Aceria Compacta De Bizkaia S.A. Anlage zur Herstellung von Warmband mit Dualphasengefüge
CN110551878A (zh) * 2019-10-12 2019-12-10 东北大学 一种超高强度超高韧性低密度双相层状钢板及其制备方法
AT525283B1 (de) * 2021-10-29 2023-02-15 Primetals Technologies Austria GmbH Verfahren zur Herstellung eines Dualphasenstahlbands in einer Gieß-Walz-Verbundanlage, ein mit dem Verfahren hergestelltes Dualphasenstahlband und eine Gieß-Walz-Verbundanlage

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
SE506596C2 (sv) 1996-05-17 1998-01-19 Nobel Biocare Ab Självgängande förankringselement för iskruvning i tandben
JP4259347B2 (ja) * 2004-02-19 2009-04-30 住友金属工業株式会社 高強度非調質継目無鋼管の製造方法
EP1832667A1 (fr) 2006-03-07 2007-09-12 ARCELOR France Procédé de fabrication de tôles d'acier à très hautes caractéristiques de résistance, de ductilité et de tenacité, et tôles ainsi produites
CN109266956B (zh) * 2018-09-14 2019-08-06 东北大学 一种汽车b柱加强板用钢及其制备方法

Citations (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2253841A1 (xx) * 1973-12-06 1975-07-04 Centro Speriment Metallurg
US4316753A (en) * 1978-04-05 1982-02-23 Nippon Steel Corporation Method for producing low alloy hot rolled steel strip or sheet having high tensile strength, low yield ratio and excellent total elongation
BE899253A (fr) * 1984-03-27 1984-07-16 Gielen Paul M E L Un nouvel acier hsla, principalement pour l'industrie automobile.
DE2924340C2 (de) 1978-06-16 1985-10-17 Nippon Steel Corp., Tokio/Tokyo Verfahren zur Herstellung zweiphasiger Stahlbleche
EP0072867B1 (en) 1981-02-20 1986-04-16 Kawasaki Steel Corporation Process for manufacturing high-tensile hot-rolled steel strip having a low yield ratio due to its mixed structure
DE3440752C2 (xx) 1984-11-08 1987-08-06 Thyssen Stahl Ag, 4100 Duisburg, De
JPH0559485A (ja) * 1991-08-27 1993-03-09 Sumitomo Metal Ind Ltd 高延性熱延高張力鋼板とその製造方法
EP0586704A1 (en) * 1991-05-30 1994-03-16 Nippon Steel Corporation High-yield-ratio hot-rolled high-strength steel sheet excellent in formability or in both of formability and spot weldability, and production thereof
JPH06264183A (ja) * 1993-03-11 1994-09-20 Sumitomo Metal Ind Ltd 高加工性熱延高張力鋼板とその製造方法
US5470529A (en) * 1994-03-08 1995-11-28 Sumitomo Metal Industries, Ltd. High tensile strength steel sheet having improved formability

Patent Citations (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2253841A1 (xx) * 1973-12-06 1975-07-04 Centro Speriment Metallurg
US4316753A (en) * 1978-04-05 1982-02-23 Nippon Steel Corporation Method for producing low alloy hot rolled steel strip or sheet having high tensile strength, low yield ratio and excellent total elongation
DE2924340C2 (de) 1978-06-16 1985-10-17 Nippon Steel Corp., Tokio/Tokyo Verfahren zur Herstellung zweiphasiger Stahlbleche
EP0072867B1 (en) 1981-02-20 1986-04-16 Kawasaki Steel Corporation Process for manufacturing high-tensile hot-rolled steel strip having a low yield ratio due to its mixed structure
BE899253A (fr) * 1984-03-27 1984-07-16 Gielen Paul M E L Un nouvel acier hsla, principalement pour l'industrie automobile.
DE3440752C2 (xx) 1984-11-08 1987-08-06 Thyssen Stahl Ag, 4100 Duisburg, De
EP0586704A1 (en) * 1991-05-30 1994-03-16 Nippon Steel Corporation High-yield-ratio hot-rolled high-strength steel sheet excellent in formability or in both of formability and spot weldability, and production thereof
JPH0559485A (ja) * 1991-08-27 1993-03-09 Sumitomo Metal Ind Ltd 高延性熱延高張力鋼板とその製造方法
JPH06264183A (ja) * 1993-03-11 1994-09-20 Sumitomo Metal Ind Ltd 高加工性熱延高張力鋼板とその製造方法
US5470529A (en) * 1994-03-08 1995-11-28 Sumitomo Metal Industries, Ltd. High tensile strength steel sheet having improved formability

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 017, no. 373 (C - 1083) 14 July 1993 (1993-07-14) *
PATENT ABSTRACTS OF JAPAN vol. 018, no. 668 (C - 1289) 16 December 1994 (1994-12-16) *

Cited By (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
AU756917B2 (en) * 1996-06-07 2003-01-30 Corus Staal B.V. Process and device for producing a high-strength steel strip
WO1999029444A1 (en) * 1997-12-08 1999-06-17 Corus Staal Bv Process and device for producing a high-strength steel strip
US6616778B1 (en) 1997-12-08 2003-09-09 Corus Staal Bv Process and device for producing a ferritically rolled steel strip
US6773522B1 (en) 1997-12-08 2004-08-10 Corus Staal Bv Process and device for producing a high-strength steel strip
NL1007739C2 (nl) * 1997-12-08 1999-06-09 Hoogovens Staal Bv Werkwijze en inrichting voor het vervaardigen van een stalen band met hoge sterkte.
CZ298363B6 (cs) * 1997-12-08 2007-09-05 Corus Staal B. V. Zpusob výroby vysokopevnostního ocelového pásu a zarízení pro provádení tohoto zpusobu
DE10327383C5 (de) * 2003-06-18 2013-10-17 Aceria Compacta De Bizkaia S.A. Anlage zur Herstellung von Warmband mit Dualphasengefüge
EP1633894B1 (de) 2003-06-18 2017-04-26 SMS group GmbH Verfahren und anlage zur herstellung von warmband mit dualphasengefüge
EP1642990A4 (en) * 2003-06-19 2006-11-29 Nippon Steel Corp HIGH-RESISTANCE STEEL PLATE WITH EXCELLENT DIVISION AND MANUFACTURING METHOD THEREFOR
US8262818B2 (en) 2003-06-19 2012-09-11 Nippon Steel Corporation Method for producing high strength steel sheet excellent in formability
US7922835B2 (en) 2003-06-19 2011-04-12 Nippon Steel Corporation High strength steel sheet excellent in formability
EP1642990A1 (en) * 2003-06-19 2006-04-05 Nippon Steel Corporation High strength steel plate excellent in formability and method for production thereof
CN110551878A (zh) * 2019-10-12 2019-12-10 东北大学 一种超高强度超高韧性低密度双相层状钢板及其制备方法
AT525283B1 (de) * 2021-10-29 2023-02-15 Primetals Technologies Austria GmbH Verfahren zur Herstellung eines Dualphasenstahlbands in einer Gieß-Walz-Verbundanlage, ein mit dem Verfahren hergestelltes Dualphasenstahlband und eine Gieß-Walz-Verbundanlage
AT525283A4 (de) * 2021-10-29 2023-02-15 Primetals Technologies Austria GmbH Verfahren zur Herstellung eines Dualphasenstahlbands in einer Gieß-Walz-Verbundanlage, ein mit dem Verfahren hergestelltes Dualphasenstahlband und eine Gieß-Walz-Verbundanlage

Also Published As

Publication number Publication date
AR002501A1 (es) 1998-03-25
CN1190997A (zh) 1998-08-19
HUP9801908A2 (hu) 1998-11-30
WO1997000332A1 (de) 1997-01-03
CA2224817A1 (en) 1997-01-03
PL324555A1 (en) 1998-06-08
BR9608672A (pt) 1999-05-04
MX9710230A (es) 1998-03-29
TR199701720T1 (xx) 1998-05-21
CZ402497A3 (cs) 1998-06-17
HUP9801908A3 (en) 1998-12-28

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