EP1200635B1 - Höherfestes stahlband oder -blech und verfahren zu seiner herstellung - Google Patents

Höherfestes stahlband oder -blech und verfahren zu seiner herstellung Download PDF

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Publication number
EP1200635B1
EP1200635B1 EP00956356A EP00956356A EP1200635B1 EP 1200635 B1 EP1200635 B1 EP 1200635B1 EP 00956356 A EP00956356 A EP 00956356A EP 00956356 A EP00956356 A EP 00956356A EP 1200635 B1 EP1200635 B1 EP 1200635B1
Authority
EP
European Patent Office
Prior art keywords
steel
steel sheet
steel band
band
sheet
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
EP00956356A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP1200635A1 (de
Inventor
Bernhard Engl
Thomas Gerber
Klaus Horn
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 EP1200635A1 publication Critical patent/EP1200635A1/de
Application granted granted Critical
Publication of EP1200635B1 publication Critical patent/EP1200635B1/de
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
    • C22C38/04—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
    • 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
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12785—Group IIB metal-base component
    • Y10T428/12792—Zn-base component
    • Y10T428/12799—Next to Fe-base component [e.g., galvanized]

Definitions

  • the invention relates to a high-strength steel strip or sheet with a predominantly ferritic-martensitic Structure and a process for its production.
  • a well-formable steel band or sheet stands out due to high r-values, which stand for good deep drawability, high n-values for good stretchability and high, positive plane-strain properties indicating elongation values. Also characteristic of good stretchability is low Yield strength ratio, which is the quotient of Yield strength and tensile strength is formed.
  • DE 30 07 560 A describes a method for Manufacture of essentially ferrite and Known martensite existing hot-rolled sheet. The aim is to use a sheet steel with a lower one Yield strength, high tensile strength and excellent Deformability.
  • the object of the invention is a one High-strength steel strip made of dual-phase steel to create or sheet, which also after passage an annealing process including one Aging treatment good mechanical-technological Possesses properties. It is also intended to be a procedure for the production of such a strip or sheet can be specified.
  • a steel strip or sheet steel according to the invention has high strengths of at least 500 N / mm 2 with good formability at the same time, without the need for particularly high contents of certain alloying elements.
  • the invention makes use of the conversion-influencing effect of the element boron, which is already known per se in steels for hot-rolled strips and forgings.
  • the strength-increasing effect of boron is ensured by adding at least one alternative nitride former, preferably Al and additionally Ti, to the steel material according to the invention.
  • the effect of the addition of titanium and aluminum is that they bind the nitrogen contained in the steel, so that boron is available for the formation of hardness-increasing carbides. Supported by the necessary Cr content, a higher level of strength is achieved in this way than with comparable steels, which are composed in a conventional manner.
  • the yield strengths of a strip or sheet according to the invention are between 250 N / mm 2 and 350 N / mm 2 .
  • the tensile strengths are 500 N / mm 2 to more than 600 N / mm 2 , in particular up to 650 N / mm 2 .
  • a steel strip or sheet according to the invention thus has properties and features that could not previously be achieved for low-alloy steels.
  • steels according to the invention are their resistance to tempering effects. That in particular with conventionally composed two-phase steels existing problem that the martensite share in a Aging treatment is left on and on it Way to a decrease in strength comes at steels according to the invention composed by the Avoid presence of chrome.
  • the Al content can be limited to a range of 0.02-0.05 mass%.
  • the nitrogen contained in the steel is not only offered as Al as a nitride former, but there is also a sufficient amount of Ti for the stoichiometric setting of the nitrogen. If, on the other hand, there is no Ti in the steel, the Al content of the steel strip or sheet should be from 0.1 to 0.4% by mass. The presence of aluminum and / or titanium initially results in the formation of relatively coarse-grained TiN and / or AlN.
  • One way of producing an inventive Steel strip or sheet consists of the steel strip or sheet by cold rolling a hot strip produce.
  • a thin hot strip can also be used without further cold rolling to an inventive Steel strip can be processed, provided its thickness for the Further processing is sufficiently reduced.
  • Such one Hot strip can, for example, on a casting and rolling line are produced in which a cast steel strand immediately rolled into a hot strip of small thickness becomes.
  • the above task with regard to Manufacturing process solved in that the steel strip or - subjected to an annealing treatment in the continuous furnace at which the annealing temperature is between 750 ° C and 870 ° C, preferably between 750 ° C and 850 ° C, and that the annealed steel strip or sheet is then from the annealing temperature with a cooling rate of cooled at least 20 ° C / s and at most 100 ° C / s becomes.
  • the method according to the invention can be based on a C-Mn steel, the boron and at least Al and possibly in addition, Ti is added as a nitride former Manufacture steel band, which also under the specified Annealing and cooling conditions the desired high Has a martensite content of around 5% to 20%.
  • a nitride former Manufacture steel band which also under the specified Annealing and cooling conditions the desired high Has a martensite content of around 5% to 20%.
  • the boron freely dissolved in the lattice ensures that the formation of martensite even at low Cooling rates set in such a way that a predominant ferrite / martensite structure with the dual-phase characteristic combinations are created.
  • Table 1 shows the alloy contents and the technological-mechanical parameters A RE (yield strength), R eL (lower yield strength), R m (tensile strength), R eL / R m (yield strength ratio ) and A 80 (elongation at break) for steel strips A1 according to the invention. A4 specified. In the same table, the corresponding information on comparative steel strips B1 - B5, C1 - C5, D1 - D4 and E1 are compared.
  • Comparative steel strips B1 - B5 are the Mn content of 1.5 - 2.4 mass% to influence the Conversion behavior has been used.
  • Comparative steel strips C1 - C5 is one for the same purpose Element combinations of Si (around 0.4 mass%) and Mn (1.5 - 2.4 mass%) and in the case of the comparative steel strips D1 - D4 a combination of the Si contents (up to 0.7 Mass%), Mn (1.2 - 1.6 mass%) and Cr (0.5 mass%) been used.
  • the comparison steel strip is E1 additional Mo provided.
  • the respective cold-rolled steel strip became one Continuous annealing, which takes place at a Standard procedure with aging for low-alloy, oriented towards soft steels.
  • Essential characteristics of this Glow and aging treatments were one Annealing temperature during continuous annealing of 800 ° C and a two-part cooling with final Pass through the aging zone. The cooling took place initially to 550 - 600 ° C with a cooling rate of approx. 20 ° C / s. Then with one Cooling rate from approx. 50 ° C / s to 400 ° C cooled.
  • the final aging treatment consisted of holding in the temperature range of 400-300 ° C for 150 s.
  • the mechanical-technological characteristic values given in Table 1 for the steel strips A1 to A4 produced according to the invention after conventional continuous annealing in the undressed state demonstrate the advantageous properties of the steel strips or sheets produced according to the invention in comparison with the additionally stated high-strength alloy concepts of the comparative steel strips.
  • the absence of an elongation limit in the undressed state in the steel strips according to the invention clearly indicates the favorable ferrite / martensite structure.
  • the yield strengths are below 300 N / mm 2 and the strength values between 530 N / mm 2 and 630 N / mm 2 .
  • the respective steel strip A1 - A4 exhibits good hardening behavior in the case of plastic deformation, which is also manifested in a very low yield strength ratio (R e / R m ⁇ 0.5).
  • the elongation at break values for strengths of 540 - 580 N / mm 2 are between 27 and 30%; for approx. 630 N / mm 2 with a still good 25%.
  • the overall mechanical properties are isotropic.
  • Table 2 shows the alloy contents and the technological-mechanical parameters A RE (yield strength), R eL (lower yield strength), R m (tensile strength), R eL / R m (yield strength ratio ) and A 80 (elongation at break) for a steel strip F1 according to the invention specified.
  • a RE yield strength
  • R eL lower yield strength
  • R m tensile strength
  • R eL / R m yield strength ratio
  • a 80 elongation at break
  • the cold-rolled steel strip F1 is then annealed and passed through a hot dip galvanizing line.
  • the annealing was carried out at 870 ° C. Connected to it a hold phase at 480 ° C for 60 seconds.
  • the Zinc bath temperature was 460 ° C.
  • the operating conditions are given in detail in Table 3.
  • the Properties of the so hot-dip coated, finally trained steel strips F1 are in the range the properties of the invention, in Table 1 specified values.
  • Table 4 also shows the alloy contents and the technological-mechanical parameters A RE (yield strength), R eL (lower yield strength), R m (tensile strength), R eL / R m (yield strength ratio ) and A for steel strips G1 1 -G1 4 according to the invention 80 (elongation at break) for steel strips A1-A4 according to the invention.
  • the steel strips G1 1 -G1 4 are each produced based on a steel of identical composition and have been subjected to a conventional hot and cold rolling process.
  • the cold-rolled steel strips G1 1 and G1 2 have undergone a continuous annealing treatment, while the steel strips G1 3 and G1 4 have been subjected to a hot-dip galvanizing treatment.
  • the respective operating conditions are given in Table 5.
  • annealing temperatures of 780 - 800 ° C the tensile strengths of the steel strips G1 1 -G1 4 are around 500 N / mm 2 .
  • the start of the flow is largely free of yield stress (A RE ⁇ 1.0%).

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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)
  • Laminated Bodies (AREA)
  • Coating With Molten Metal (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
EP00956356A 1999-07-31 2000-07-31 Höherfestes stahlband oder -blech und verfahren zu seiner herstellung Expired - Lifetime EP1200635B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE19936151A DE19936151A1 (de) 1999-07-31 1999-07-31 Höherfestes Stahlband oder -blech und Verfahren zu seiner Herstellung
DE19936151 1999-07-31
PCT/EP2000/007377 WO2001009396A1 (de) 1999-07-31 2000-07-31 Höherfestes stahlband oder -blech und verfahren zu seiner herstellung

Publications (2)

Publication Number Publication Date
EP1200635A1 EP1200635A1 (de) 2002-05-02
EP1200635B1 true EP1200635B1 (de) 2003-10-01

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EP00956356A Expired - Lifetime EP1200635B1 (de) 1999-07-31 2000-07-31 Höherfestes stahlband oder -blech und verfahren zu seiner herstellung

Country Status (19)

Country Link
US (1) US6743307B1 (zh)
EP (1) EP1200635B1 (zh)
JP (1) JP4745572B2 (zh)
KR (1) KR100796819B1 (zh)
CN (1) CN1180096C (zh)
AT (1) ATE251226T1 (zh)
AU (1) AU777321B2 (zh)
BR (1) BR0012906A (zh)
CA (1) CA2380969A1 (zh)
CZ (1) CZ299072B6 (zh)
DE (2) DE19936151A1 (zh)
ES (1) ES2208410T3 (zh)
MX (1) MXPA02001073A (zh)
PL (1) PL194945B1 (zh)
RU (1) RU2246552C2 (zh)
SK (1) SK1472002A3 (zh)
TR (1) TR200200259T2 (zh)
WO (1) WO2001009396A1 (zh)
ZA (1) ZA200200898B (zh)

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CN108411207B (zh) * 2018-04-11 2020-01-07 东北大学 一种抗拉强度600MPa级薄规格热轧双相钢及其制造方法
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CN111733366B (zh) * 2020-07-08 2021-06-22 马鞍山钢铁股份有限公司 一种含铝冷轧超高强钢及其制备方法、应用
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JPS5684443A (en) * 1979-12-14 1981-07-09 Nippon Kokan Kk <Nkk> High tensile cold rolled steel plate excellent in press moldability and denting resistance and its manufacture
JPS5850300B2 (ja) * 1979-12-15 1983-11-09 新日本製鐵株式会社 加工性に優れ且つ加工後人工時効硬化性の高い高強度低降伏比高延性複合組織鋼板の製造方法
DE3007560A1 (de) * 1980-02-28 1981-09-03 Kawasaki Steel Corp., Kobe, Hyogo Verfahren zum herstellen von warmgewalztem blech mit niedriger streckspannung, hoher zugfestigkeit und ausgezeichnetem formaenderungsvermoegen
JPS5927370B2 (ja) * 1980-07-05 1984-07-05 新日本製鐵株式会社 プレス加工用高強度冷延鋼板
JPS57126924A (en) * 1981-01-29 1982-08-06 Sumitomo Metal Ind Ltd Production of cold-rolled steel sheet having delayed aging property by continuous annealing
JPS57137426A (en) * 1981-02-20 1982-08-25 Kawasaki Steel Corp Production of low yield ratio, high tensile hot rolled steel plate by mixed structure
JPH03264645A (ja) * 1982-03-29 1991-11-25 Kobe Steel Ltd 伸びフランジ性等にすぐれた高強度鋼板
SE442545B (sv) * 1985-03-11 1986-01-13 Tore J Hedbeck Ab Anordning for reglering av rokgasernas utloppshastighet i en skorsten
JPS637337A (ja) * 1986-06-26 1988-01-13 Nippon Steel Corp 開缶性と製蓋性のすぐれたイ−ジ−オ−プンエンド用鋼板の製造方法
JPH04268016A (ja) * 1991-02-20 1992-09-24 Kobe Steel Ltd 圧壊特性に優れたドアガードバー用高張力鋼板の製造方法
JP3219820B2 (ja) * 1991-12-27 2001-10-15 川崎製鉄株式会社 低降伏比高強度熱延鋼板およびその製造方法
JPH05255799A (ja) * 1992-03-11 1993-10-05 Nippon Steel Corp 加工性に優れた溶融めっき熱延高強度鋼板およびその製造方法
JP3132338B2 (ja) * 1995-05-10 2001-02-05 日本鋼管株式会社 耐側壁破断性の優れたｄｔｒ缶適合鋼板の製造方法
DE19719546C2 (de) * 1996-07-12 1998-12-03 Thyssen Stahl Ag Warmband aus Stahl und Verfahren zu seiner Herstellung
EP2314729B2 (en) * 1997-03-17 2017-03-08 Nippon Steel & Sumitomo Metal Corporation Dual-phase type high-strength steel sheets having high impact energy absorption properties
US6312536B1 (en) * 1999-05-28 2001-11-06 Kabushiki Kaisha Kobe Seiko Sho Hot-dip galvanized steel sheet and production thereof

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ES2208410T3 (es) 2004-06-16
TR200200259T2 (tr) 2002-05-21
WO2001009396A1 (de) 2001-02-08
CZ299072B6 (cs) 2008-04-16
CN1367846A (zh) 2002-09-04
EP1200635A1 (de) 2002-05-02
MXPA02001073A (es) 2002-11-04
CA2380969A1 (en) 2001-02-08
PL353858A1 (en) 2003-12-01
RU2002105012A (ru) 2004-01-20
AU777321B2 (en) 2004-10-14
JP2003505604A (ja) 2003-02-12
ZA200200898B (en) 2003-07-30
DE19936151A1 (de) 2001-02-08
SK1472002A3 (en) 2002-10-08
ATE251226T1 (de) 2003-10-15
KR100796819B1 (ko) 2008-01-22
AU6833200A (en) 2001-02-19
KR20020037339A (ko) 2002-05-18
PL194945B1 (pl) 2007-07-31
BR0012906A (pt) 2002-06-04
RU2246552C2 (ru) 2005-02-20
JP4745572B2 (ja) 2011-08-10
US6743307B1 (en) 2004-06-01
CZ2002317A3 (cs) 2002-07-17
DE50003922D1 (de) 2003-11-06

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