WO2007024092A1 - Tole en acier laminee a chaud de grande resistance ayant une teneur elevee en mn et presentant une excellente maniabilite, et son procede de fabrication - Google Patents

Tole en acier laminee a chaud de grande resistance ayant une teneur elevee en mn et presentant une excellente maniabilite, et son procede de fabrication Download PDF

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Publication number
WO2007024092A1
WO2007024092A1 PCT/KR2006/003303 KR2006003303W WO2007024092A1 WO 2007024092 A1 WO2007024092 A1 WO 2007024092A1 KR 2006003303 W KR2006003303 W KR 2006003303W WO 2007024092 A1 WO2007024092 A1 WO 2007024092A1
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WO
WIPO (PCT)
Prior art keywords
steel sheet
steel
hot rolled
content
rolled steel
Prior art date
Application number
PCT/KR2006/003303
Other languages
English (en)
Inventor
Sung-Kyu Kim
Kwang-Geun Chin
Seong-Ju Kim
Original Assignee
Posco
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 Posco filed Critical Posco
Priority to JP2008527844A priority Critical patent/JP4850908B2/ja
Priority to CN2006800310158A priority patent/CN101248203B/zh
Priority to EP06798530A priority patent/EP1937861A4/fr
Priority to US12/064,145 priority patent/US20080240969A1/en
Publication of WO2007024092A1 publication Critical patent/WO2007024092A1/fr

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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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • 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
    • C21D8/0405—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 of ferrous alloys
    • 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
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C21D2211/001—Austenite

Definitions

  • the present invention relates to a hot rolled steel sheet used for a bumper reinforcing material or for an impact absorption material in a door of automobiles. More particularly, the present invention relates to a high strength hot rolled steel sheet containing a high Mn content with high elongation which ensures excellent formability, and to a method for manufacturing the same.
  • bumper reinforcing materials or impact absorption material inside doors are directly related to safety of passengers upon collision of the automobiles, and generally formed of super strength hot rolled steel sheets having a tensile strength of 780 MPa or more.
  • high strength steel has been increasingly used in the automobiles to increase fuel efficiency, and investigations have progressed more and more for commercial application of the high strength steel having the tensile strength of 780 MPa or more.
  • a method for manufacturing a hot rolled steel sheet for the automobiles comprises reheating a steel slab for allowing steel components to form a solid solution again, hot rolling the steel slab to a steel sheet having a predetermined thickness, cooling the hot rolled steel sheet at room temperature, and coiling the cooled steel sheet.
  • the dual phase steel is produced in such a way of hot rolling the reheated slab at a temperature in an austenite region, and cooling the hot rolled steel sheet to a cooling finish temperature below Ms-temperature for transformation from austenite to martensite.
  • an increase in ratio of the martensite structure causes an increase in strength of the steel
  • an increase in ratio of the ferrite structure causes an increase in elongation of the steel.
  • the dual phase steel has a disadvantage in that a high cooling rate is required to form the martensite at low temperatures.
  • the TRIP steel refers to steel which has further enhanced workability by forming retained austenite in a portion of the steel structure. Since the TRIP steel has excellent uniform elongation by transformation through work hardening, and typically has an elongation of 30% for 800 MPa, which is excellent compared with that of other super strength steel, it has a high tensile strength-elongation balance value. However, high strength steel having a higher level of strength has been required to satisfy higher requirement for a light automotive body. Furthermore, machining of more complicated components with the steel is required for integration of the components, thereby requ iring the steel to have an elongation 30% higher than those for the same strength level.
  • the multi-phase steel refers to steel which is further increased in strength and elongation at the same time than the TRIP steel by forming the austenite during hot rolling, and controlling the cooling rate and the cooling finish temperature during cooling the coiled steel sheet to form ferrite, martensite, a small fraction of bainite, and a mixed phase of martensite and austenite at room temperature.
  • the multi-phase steel has superior weldability and high yield strength due to its smaller added amount of alloy element.
  • the multi-phase steel has a disadvantage in view of formability due to a low elongation. Disclosure of Invention Technical Problem
  • the present invention has been made to solve the above problems, and it is an object of the present invention to provide a high strength hot rolled steel sheet containing a high Mn content with excellent workability, which is controlled in Mn content to 8 ⁇ 15 wt% to form a single phase austenite structure, ensuring an excellent elongation, and to form twins upon deformation, preventing necking which causes cracks.
  • a high strength hot rolled steel sheet containing a high Mn content with excellent workability comprising, by weight%: C: 0.2% - 1%, Mn: 8 ⁇ 15%, S: 0.05% or less, P: 0.03% or less, and the balance of Fe and other unavoidable impurities, wherein a product of tensile strength and total elongation (TS x ToLEl) of the steel sheet is 24,000 MPa% or more.
  • a method for manufacturing a high strength hot rolled steel sheet containing a high Mn content with excellent workability comprises: reheating a steel slab at a temperature of 1,180 ⁇ 1,220 °C, the steel slab comprising by weight%: by weight%: C: 0.2% ⁇ 1%, Mn: 8 ⁇ 15%, S: 0.05% or less, P: 0.03% or less, and the balance of Fe and other unavoidable impurities finish hot rolling the reheated steel slab at a temperature of 800 °C or more and cooling the hot rolled steel sheet at a temperature of 600 °C or more, followed by coiling the cooled steel sheet, wherein a product of tensile strength and total elongation (TS x ToLEl) of the steel sheet is 24,000 MPa% or more.
  • the present invention provides a high strength hot rolled steel sheet containing a high Mn content with excellent workability, which has a higher strength-elongation balance value than that of TRIP steel known as having excellent elongation in the art. Best Mode for Carrying Out the Invention
  • the present invention is provided in order to solve such a typical problem of the high strength steel, and characterized by controlling an Mn content to 8 ⁇ 15 wt% to form a single phase austenite structure in order to ensure excellent elongation, and by create twins to prevent generation of necking which forms cracks upon deformation.
  • the steel of the present invention has a different deformation characteristic from that of the conventional high strength steel.
  • the steel according to the present invention is twin-induced plasticity steel, which has a high content of Mn so as to have the austenite structure and is formed with the twins upon application of stress to the steel.
  • the twins cause little deformation concentration upon work hardening, providing the excellent elongation.
  • TRIP steel is subjected to transformation upon deformation, the deformation is concentrated on martensite.
  • the TWIP steel of the present invention is not subjected to the transformation upon the deformation, and maintains the austenite structure, thereby providing excellent elongation.
  • Carbon (C) is the most important component in steel.
  • C has a close relationship with all physical and chemical properties of the steel, such as strength, toughness, corrosion resistance, and the like, and provides the most influential effect on the properties of the steel. If C content is less than 0.2%, not only stability of austenite but also a fraction of a secondary phase are reduced, thereby providing a problem of lowered strength. If the C content exceeds 1%, not only weldability of the steel is deteriorated, but also the fraction of the secondary phase is rapidly increased, thereby rapidly deteriorating workability. Thus, the C content is preferably in the range of 0.2 - 1%.
  • Manganese (Mn) is an austenite stabilization element, which increases the strength of steel by improving hardenability. According to the present invention, it is necessary to contain 8% or more of Mn in order to obtain a stable austenite structure. If Mn is excessively added above 15%, there are problems, such as excessive load during steel manufacturing, deterioration in weldability, formation of inclusions, and increase in manufacturing costs. Thus, the Mn content is preferably in the range of 8 ⁇ 15%.
  • S Sulfur
  • the S content is preferably 0.05% or less.
  • Phosphorus (P) is an impurity element in the steel. If P content exceeds 0.03%, the toughness of steel becomes deteriorated. Thus, the P content is preferably 0.03% or less.
  • the steel of the present invention may further comprise at least one of
  • Aluminum (Al) is a ferrite stabilization element, which resides in a solid solution state in ferrite.
  • Al serves to enhance the strength of steel, and is generally added to the steel as a deoxidation agent.
  • Al is effective to continuously generate twins during deformation by increasing stacking fault energy. If Al content is less than 0.3%, the effect of increasing the stacking fault energy is small. If the Al content exceeds 3%, there can be problems of increasing nozzle clogging and inclusions during the steel manufacturing or continuous casting process.
  • the Al content is preferably in the range of 0.3 ⁇ 3%.
  • Nickel (Ni) is the austenite stabilization element, and advantageous in terms of properties of the steel when it is added to the steel as much as possible. If Ni content is less than 2%, the effect by addition of Ni cannot be obtained. If the Al content exceeds 7%, there is a problem of significantly increasing the manufacturing costs. Thus, the Ni content is preferably in the range of 2 ⁇ 7%.
  • Copper (Cu) is an element which is solid-soluted in the austenite or forms a precipitation phase, thereby decreasing an amount of crystal grains of the austenite and refining crystal grains of the ferrite.
  • Cu content is 2% or more. If the Cu content exceeds 5%, there are problems of significantly increasing a reheating temperature while increasing the manufacturing costs.
  • the Cu content is preferably in the range of 2 ⁇ 5%.
  • the hot rolled steel sheet of the present invention has a single phase austenite structure, and exhibits an elongation of 30% or more.
  • a tensile strength-total elongation balance value (TS X Tot.El) is of 24,000 MPa% or more. Such a balance value is very high when considering that the TRIP steel known as having excellent elongation has a tensile strength-total elongation balance value less than 24,000 MPa%.
  • a method of manufacturing a steel sheet according to the present invention comprises reheating a steel slab having the composition as described above for allowing components segregated during casting to form a solid solution thereof again, hot rolling the reheated steel slab to a steel sheet having a desired thickness, cooling and coiling the hot rolled steel sheet to ensure desired properties of the steel.
  • the steel slab having the composition described as above is reheated. Reheating of the steel slab is performed for the purpose of solid solutioning the components segregated during the casting, and preferably at a temperature of 1,180 ⁇ 1,220 °C. If a reheating temperature is less than 1,180 °C, the components segregated during the casting are not solid soluted again. If the reheating temperature exceeds 1,220 °C, the grain size of austenite increases, and grains of ferrite become coarsened, thereby decreasing the strength of steel.
  • the reheated steel slab is subjected to hot rolling, preferably, at a finish hot rolling temperature of 800 °C or more. If the finish hot rolling temperature is less than 800 °C, a great amount of dislocations are induced in the ferrite formed during the hot rolling, and the ferrite is grown during cooling or coiling, forming coarse surface grains.
  • the hot rolled steel sheet is cooled, and coiled. Since a final structure of the hot rolled steel sheet according to the present invention is a single phase austenite, the hot rolled steel sheet does not suffer from phase transformation during the cooling.
  • the present invention is not limited to a specific cooling rate, and may have a typical cooling pattern including air cooling and water cooling. In this regard, if a cooling finish temperature is less than 600 °C, there is a problem of generating excessive retained stress. Thus, the cooling finish temperature is preferably 600 °C or more.
  • Inventive steel CS Comparative steel [53] As can be appreciated from Table 2, Inventive Samples 1 - 7 satisfying the conditions of the present invention have excellent strength, elongation, and strength- elongation balance value. In particular, the Inventive Samples 1 - 7 have strength- elongation balance values of 24,000 MPa% or more, thereby securing excellent workability along with high strength.
  • Comparative Samples 1 and 2 do not satisfy the condition of the present invention in terms of Mn content, and have low strength-elongation balance values.

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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 Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)
  • Metal Rolling (AREA)

Abstract

L’invention concerne une tôle en acier laminée à chaud utilisée en tant que matériau de renfort de pare-chocs ou en tant que matériau absorbant les impacts pour des portières d'automobiles, et un procédé de fabrication de ladite tôle. La tôle en acier comprend, en % massique, C : 0,2 % ~ 1 %, Mn : 8 ~ 15 %, S : 0,05 % ou moins, P : 0,03 % ou moins, le reste étant du Fe et d’autres impuretés inévitables. Le produit de la résistance à la traction et de l’allongement total (TS x ToLEl) de la tôle en acier est d’au moins 24 000 MPa%. Ce procédé permet d’obtenir une tôle en acier laminée à chaud de grande résistance, présentant une valeur élevée d’équilibre résistance-allongement, conférant ainsi une excellente maniabilité.
PCT/KR2006/003303 2005-08-23 2006-08-23 Tole en acier laminee a chaud de grande resistance ayant une teneur elevee en mn et presentant une excellente maniabilite, et son procede de fabrication WO2007024092A1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
JP2008527844A JP4850908B2 (ja) 2005-08-23 2006-08-23 加工性に優れた高マンガン形高強度熱延鋼板及びその製造方法
CN2006800310158A CN101248203B (zh) 2005-08-23 2006-08-23 含高Mn含量的可加工性优异的高强度热轧钢板及其制造方法
EP06798530A EP1937861A4 (fr) 2005-08-23 2006-08-23 Tole en acier laminee a chaud de grande resistance ayant une teneur elevee en mn et presentant une excellente maniabilite, et son procede de fabrication
US12/064,145 US20080240969A1 (en) 2005-08-23 2006-08-23 High Strength Hot Rolled Steel Sheet Containing High Mn Content with Excellent Workability and Method for Manufacturing the Same

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR1020050077371A KR100711361B1 (ko) 2005-08-23 2005-08-23 가공성이 우수한 고망간형 고강도 열연강판 및 그 제조방법
KR10-2005-0077371 2005-08-23

Publications (1)

Publication Number Publication Date
WO2007024092A1 true WO2007024092A1 (fr) 2007-03-01

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PCT/KR2006/003303 WO2007024092A1 (fr) 2005-08-23 2006-08-23 Tole en acier laminee a chaud de grande resistance ayant une teneur elevee en mn et presentant une excellente maniabilite, et son procede de fabrication

Country Status (6)

Country Link
US (1) US20080240969A1 (fr)
EP (1) EP1937861A4 (fr)
JP (1) JP4850908B2 (fr)
KR (1) KR100711361B1 (fr)
CN (1) CN101248203B (fr)
WO (1) WO2007024092A1 (fr)

Cited By (8)

* Cited by examiner, † Cited by third party
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EP2128293A1 (fr) * 2008-05-27 2009-12-02 Posco Feuilles d'acier de faible densité et grande résistance doté d'une excellente résistance à la formation de rides et leur procédé de fabrication
DE102008056844A1 (de) * 2008-11-12 2010-06-02 Voestalpine Stahl Gmbh Manganstahlband und Verfahren zur Herstellung desselben
WO2013179115A1 (fr) 2012-05-31 2013-12-05 ArcelorMittal Investigación y Desarrollo, S.L. Acier lamine a chaud ou a froid a faible densite, son procede de mise en oeuvre et son utilisation
EP2799582A4 (fr) * 2011-12-28 2016-02-24 Posco Acier austénitique résistant à l'usure et présentant une usinabilité et une ductilité améliorées, et procédé de production correspondant
EP2799581A4 (fr) * 2011-12-28 2016-02-24 Posco Acier austénitique résistant à l'usure et présentant une usinabilité et une résistance améliorées dans des zones affectées par la température de soudage, et procédé de production correspondant
EP2883974A4 (fr) * 2012-08-09 2016-04-27 Posco Fil machine ayant une résistance et une ductilité correctes et procédé pour produire celui-ci
US20180030567A1 (en) * 2015-02-16 2018-02-01 Easyforming Steel Technology Co., Ltd. Steel plate used for hot stamping forming, forming process of hot stamping and hot-stamped component
EP3686310A4 (fr) * 2018-05-23 2020-08-19 Manchao He Matériau d'acier de tige d'ancrage npr et son procédé de production

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RU2401877C2 (ru) 2005-02-02 2010-10-20 Корус Стал Бв Аустенитная сталь, имеющая высокую прочность и формуемость, способ получения упомянутой стали и ее применение
KR100955203B1 (ko) * 2007-11-05 2010-04-29 한국기계연구원 연성이 우수한 고망간형 초고강도 냉연강판 및 그 제조방법
US20120128524A1 (en) * 2010-11-22 2012-05-24 Chun Young Soo Steel wire rod having excellent cold heading quality and hydrogen delayed fracture resistance, method of manufacturing the same, and mehod of manufacturing bolt using the same
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US10655196B2 (en) 2011-12-27 2020-05-19 Posco Austenitic steel having excellent machinability and ultra-low temperature toughness in weld heat-affected zone, and method of manufacturing the same
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US20140261918A1 (en) * 2013-03-15 2014-09-18 Exxonmobil Research And Engineering Company Enhanced wear resistant steel and methods of making the same
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EP1937861A1 (fr) 2008-07-02
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KR100711361B1 (ko) 2007-04-27
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CN101248203A (zh) 2008-08-20
US20080240969A1 (en) 2008-10-02

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