EP2119803A1 - Plaque d'acier épaisse de haute résistance et son procédé de fabrication - Google Patents

Plaque d'acier épaisse de haute résistance et son procédé de fabrication Download PDF

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Publication number
EP2119803A1
EP2119803A1 EP08721186A EP08721186A EP2119803A1 EP 2119803 A1 EP2119803 A1 EP 2119803A1 EP 08721186 A EP08721186 A EP 08721186A EP 08721186 A EP08721186 A EP 08721186A EP 2119803 A1 EP2119803 A1 EP 2119803A1
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EP
European Patent Office
Prior art keywords
iso
domains
orientation
steel
arrestability
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.)
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Application number
EP08721186A
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German (de)
English (en)
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EP2119803A4 (fr
Inventor
Hiroyuki Shirahata
Masaaki Fujioka
Akihiko Kojima
Yoichi Tanaka
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Nippon Steel Corp
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Nippon Steel Corp
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Publication date
Application filed by Nippon Steel Corp filed Critical Nippon Steel Corp
Publication of EP2119803A1 publication Critical patent/EP2119803A1/fr
Publication of EP2119803A4 publication Critical patent/EP2119803A4/fr
Withdrawn legal-status Critical Current

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    • 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
    • C21D6/001—Heat treatment of ferrous alloys containing Ni
    • 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C21D2201/05—Grain orientation
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the present invention relates to a high-strength thick steel plate (hereafter also referred to as a high-strength high-arrest thick steel plate or a high-arrest steel plate) excellent ability to arrest propagation of brittle cracks (hereafter referred to as arrestability) and method of producing the same.
  • a steel plate according to the present invention may be applied in weld constructions such as shipbuilding, buildings, bridges, tanks, and offshore structures.
  • the steel plate according to the present invention may also be worked to steel pipes, steel columns or the like, and may be distributed in the form of a secondary product.
  • Priority is claimed on Japanese Patent Application, No. 2007-54279 filed on March 5, 2007 , the content of which is incorporated herein by reference.
  • Patent Reference 1 Japanese Unexamined Patent Application, First Publication, No. H02-1293189 ) describes a method (i) of refining the crystal grain size. In this method, steel is subjected to rolling with a reduction of 50% or more at a non-recrystallization region at a temperature of not lower than Ar 3 temperature, and is subsequently subjected to rolling with a reduction of 30 to 50% at two-phase region at 700 to 750°C.
  • Patent Reference 2 Japanese Examined Patent Application, Second Publication No. H06-004903
  • Patent Reference 3 Japanese Unexamined Patent Application, First Publication No. 2003-221619
  • Patent Reference 1 is directed to steel used in low-temperature conditions, where the steel has relatively low strength because of its microstructure mainly composed of ferrite, and the plate thickness is up to about 20 mm. Therefore, if the method is applied to a thick plate with a thickness of 50 mm or more, as designated by the present invention, it is difficult to ensure a sufficient reduction (reduction ratio) in terms of slab thickness. In addition, there is another problem in that prolonged stand-by time before reaching the process temperature reduces the productivity of the steel. In addition, it is difficult to ensure a yield strength of 390MPa or more by the method described in this reference.
  • Patent References 2 and 3 Application of the method described in Patent References 2 and 3 to a production of a thick member having a plate thickness of 50 mm or more, as designated in the present invention, also causes problems. Even though a similar microstructure is obtained, it is difficult to ensure arrestability. The effect of refined ferrite in the surface portion is relatively reduced. Further, the production process itself includes a problem in that thermal control along the plate thickness is further made difficult, and it is impossible to avoid increasing the reduction during the recuperation process, thereby largely disturbing the productivity.
  • Patent Reference 5 If the invention described in Patent Reference 5 is applied to a thick plate, efficiency of rolling is extremely reduced. Thus, such a method is not applicable in industrial production.
  • an object of the present invention is to provide a thick high-strength steel plate having excellent brittle crack propagation arrestability that is sufficient as a steel for large construction, and to provide a production method that enables industrially stable and effective production of the same steel plate.
  • the present invention concerns a thick high-strength steel plate having excellent brittle crack propagation arrestability and a method of producing the same that solve the above-described problems, and includes below-described aspects.
  • the basic structural unit dominating the toughness of bainite steel is not prior-austenite grain size, but the size of a region of a so-called packet or block (With respect to a packet and block, see Non-Patent Reference: Matsuda, Inoue, Mimura, and Okamura, "Toughness and effective grain size of low-alloy heat-treated high-tensile steel", Proc. of Int. Symp. on Towered Improved Ductility and Toughness. Climax Molybdenum Co., Kyoto (1971), p47 ).
  • the toughness is improved as the region has small size.
  • the inventors firstly produced steel plate of 50 mm in plate thickness under various conditions using a steel slab not containing Ni, worked the steel plates to test pieces of 500mm square each notched to a depth of 29 mm, and subjected the test specimens to a temperature-gradient type ESSO test so as to evaluate the arrestability in accordance with the method described in WES 3003. After that, by observing the fracture surface of the test specimens using a scanning electron microscope, and measured the unit (fracture facet size) of cleavage surface surrounded by the fracture portion called a tear-ridge, and confirmed its good correlation with arrestability.
  • FIG. 1 shows an example of the examination. Analysis was carried out on representative points in iso-orientation domains were analyzed based on the orientation map obtained by EBSP. Cubes constituted of ⁇ 100 ⁇ planes (that are regarded as cleavage plane) and the direction of crack propagation assuming that the crack propagates along the ⁇ 100 ⁇ planes were shown in FIG. 1 .
  • the numbers in FIG. 1 denote the angles (crack propagation deviation angles) required to make closest ⁇ 001> axes to coincident with each other, that is, the angles required to make ⁇ 100 ⁇ planes perpendicular to the T-direction coincident with each other by allowing their rotation.
  • orientation of crack propagation appears to change where the crack-propagation deviation angle was 20° or more as shown in (a), (b), (c), and (f).
  • the boundary of the above-described critical conditions actually constituted the boundaries of the fracture facet size.
  • crack-propagation does not change its direction in small-sized domains even when the deviation angle is more than 20°C.
  • Such phenomenon is considered to correspond to wraparound of the crack and ductile fracture surface.
  • Such phenomenon is observed in the domains having a circle equivalent diameter smaller than 8 ⁇ m.
  • apparent boundaries were not constituted by such small domains.
  • the existent domains smaller than 8 ⁇ m may be united to any of the adjacent grains on both sides, and the domain boundaries of iso-crack propagation resisting domain may be determined by examining the deviation angles between the two adjacent domains.
  • the effective grain size can be estimated by excluding the grains smaller than 8 ⁇ m from the result of EBSP analysis, determining the boundaries of domains that show crack-propagation deviation angle of not smaller than 20°, and calculating the mean circle equivalent diameter of domains surrounded by the boundaries.
  • the inventors also examined the influence of microstructural factors other than effective grain size on the arrestability, since it was confirmed that steel plates of fine effective grain size occasionally showed insufficient arrestability.
  • arrestability was also affected by the size of cementite included in the bainite. As shown in FIG. 5 , arrestability is reduced where the mean circle equivalent diameter of cementite exceeds 0.5 ⁇ m. It can be estimated that fine cementites generate microcracks in their grain boundaries in the matrix before propagation of the main crack, thereby decreasing the stress state in the tip of the crack. On the other hand, where the cementite is coarsened, like as pearlite, the cementite acts as an origin for causing the brittle fracture to occur, thereby decreasing the arrestability.
  • the reheating temperature of a slab was controlled to be 950 to 1150°C. Where the reheating temperature is lower than 950°C, homogenization of the alloying elements is insufficient, thereby causing inhomogeneous properties. Where the reheating temperature exceeds 1150°C, the grain sizes of austenite are coarsened. Therefore, there is a possibility that it is difficult to obtain a fine microstructure in the final state.
  • the subsequent rough rolling must be performed at a temperature of 900°C or more with a cumulative reduction of 30% or more. If the above-described conditions are not satisfied, recrystallization of austenite grains does not proceed sufficiently, resulting in mixed grain microstructure which may cause inhomogeneous properties.
  • the following finish-rolling is the most important process for refining the effective grain size that dominates the arrestability.
  • the finish-rolling is performed at a temperature of not lower than Ar 3 (a temperature at which formation of ferrite from austenite starts during cooling of steel) and not higher than the below described T(°C) with a cumulative reduction of 40% or more.
  • T 37 ⁇ Ni + 810 ⁇ 1.1 - t / 500 , where [Ni] denotes Ni content (in mass %) and t denotes a plate thickness (mm).
  • the steel plate After the completion of finish-rolling, the steel plate is subjected to accelerated cooling from the temperature of not lower than Ar 3 to a temperature of 500°C or less with a cooling rate of 8°C/s or more.
  • the starting temperature of cooling is lower than Ar 3
  • the fraction of coarse ferrite in the surface portions exceeds 10%, thereby deteriorating the arrestability.
  • the cooling rate is less than 8°C/s, or where the finish temperature of cooling is higher than 500°C, sufficient strength is not obtained.
  • arrestability is reduced by insufficient refinement of effective grain size, coarsening of cementite that could contribute the improvement of arrestability, or by generation of pearlite exceeding 5%.
  • a tempering treatment may be performed at a temperature of 300 to 600°C so as to control the strength and toughness of the steel plate. Where the tempering temperature is less than 300°C, ductility and toughness are not improved sufficiently. Where the tempering temperature exceeds 600°C, arrestability is reduced by coarsening of cementite.
  • C is an element that contributes to generation of cementite and preventing coarsening of microstructure.
  • carbon is an inevitable element for enhancing the strength of steel at low cost. Therefore, carbon is added in an amount of 0.01 % or more.
  • too much addition of carbon makes it difficult to assure a HAZ (Heat Affected Zone) toughness in the time of large heat input welding, and easily coarsens cementite. Therefore, the upper limit of carbon content is controlled to be 0.14%.
  • Si silicon is an inexpensive deoxidizing element and is added in an amount of 0.03% or more for solid solution-strengthening of matrix.
  • a silicon content exceeding 0.5% deteriorates weldability and HAZ toughness. Therefore, the upper limit of silicon content is controlled to be 0.5%.
  • Mn manganese
  • the upper limit of manganese content is controlled to be 2.0%.
  • the content of P (phosphorus) and S (sulfur) are preferably controlled to be as low as possible, large cost is required to reduce the content of P and S industrially. Therefore, the upper limits are controlled to be 0.02% for P and 0.01 % for S.
  • Ni nickel
  • the content of Ni is controlled to be not more than 4.0% since increasing amounts of Ni result in increasing costs of a slab.
  • Nb niobium
  • Nb is an element that contributes to refining of microstructure, transformation strengthening, and precipitation strengthening, and is effective for ensuring the strength of the matrix. Therefore, Nb is added in an amount of 0.005% or more.
  • the upper limit ofNb is controlled to be 0.050%.
  • Ti titanium
  • Ti titanium
  • the upper limit of Ti is controlled to be 0.050%.
  • Al is an important deoxidizing element and is added in an amount of 0.002% or more.
  • the upper limit of aluminum is controlled to be 0.10%.
  • N nitrogen
  • Ti titanium
  • nitrides that improves HAZ toughness. Therefore, N is added in an amount of 0.0010% or more.
  • excessive addition ofN generates brittleness by soluble N. Therefore, the amount ofNi is controlled to be 0.0080% or less.
  • Optional additional elements are limited for the below described reason.
  • Cu copper
  • Cr chromium
  • Mo mobdenum
  • V vanadium
  • V vanadium
  • its upper limit is controlled to be 0.10% since an addition of V exceeding 0.10% reduces HAZ toughness.
  • B (boron) is an element for improving hardenability and is effective for enhancing the strength of steel by addition thereof in an appropriate amount. On the other hand, excessive addition of B deteriorates weldability. Therefore, boron content is controlled to be 0.0002 to 0.0030%.
  • Mg magnesium
  • Ca calcium
  • REM is controlled to be in a range of 0.0005 to 0.010%.
  • REM denotes a rare earth element (rare earth metal) such as La, Ce, or the like.
  • Ceq C + Mn / 6 + Cu + Ni / 15 + Cr + Mo + V / 5 , where [symbol of element] denotes a content (in mass %) of the element. That is, where X denotes the symbol of an element, [X] denotes the content (in mass %) of the element X.
  • Steel plates each having a thickness of 50 to 80 mm were produced in accordance with the production method shown in Tables 2 and 3 using slabs each having a composition shown in Table 1.
  • the microstructure, base-metal strength, and arrestability of the steel plates are shown in Tables 4 and 5.
  • Fraction of surface coarse ferrite surface coarse a fraction
  • Fraction of pearlite was measured based on an optical micrograph of a T-sections obtained from a portion of 5 mm depth from the plates surface, a portion of 1/4 plate thickness, and central portion of the plate thickness.
  • Replica samples were obtained from the above-described three portions along the plate thickness.
  • Steel plates No. 1 to 22 as Examples according to the present invention had chemical compositions within a predetermined range and were produced under predetermined conditions. Therefore, each of the plates had sufficient strength as a steel of YP: 390 to 460MPa class, and had satisfactory arrestability.
  • the chemical composition or production condition was outside the predetermined range of the present invention. As a result, arrestability was reduced in each case.
  • the finish-rolling temperatures were lower than Ar 3 , and coarse ferrite was generated in large amounts in the surface portions, resulting in reduction of arrestability.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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  • Metallurgy (AREA)
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  • Physics & Mathematics (AREA)
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  • Heat Treatment Of Steel (AREA)
EP08721186.8A 2007-03-05 2008-03-03 Plaque d'acier épaisse de haute résistance et son procédé de fabrication Withdrawn EP2119803A4 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2007054279 2007-03-05
PCT/JP2008/053766 WO2008108333A1 (fr) 2007-03-05 2008-03-03 Plaque d'acier épaisse de haute résistance et son procédé de fabrication

Publications (2)

Publication Number Publication Date
EP2119803A1 true EP2119803A1 (fr) 2009-11-18
EP2119803A4 EP2119803A4 (fr) 2016-07-20

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EP08721186.8A Withdrawn EP2119803A4 (fr) 2007-03-05 2008-03-03 Plaque d'acier épaisse de haute résistance et son procédé de fabrication

Country Status (7)

Country Link
EP (1) EP2119803A4 (fr)
JP (1) JP4309946B2 (fr)
KR (1) KR101024709B1 (fr)
CN (1) CN101622370B (fr)
BR (1) BRPI0808347B1 (fr)
TW (1) TWI335355B (fr)
WO (1) WO2008108333A1 (fr)

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EP2698442A1 (fr) * 2011-04-13 2014-02-19 Nippon Steel & Sumitomo Metal Corporation Feuille d'acier laminé à froid à haute résistance ayant une excellente aptitude au façonnage local et son procédé de fabrication
EP2698442A4 (fr) * 2011-04-13 2015-01-28 Nippon Steel & Sumitomo Metal Corp Feuille d'acier laminé à froid à haute résistance ayant une excellente aptitude au façonnage local et son procédé de fabrication
US9719151B2 (en) 2012-02-17 2017-08-01 Nippon Steel & Sumitomo Metal Corporation Steel sheet, plated steel sheet, and method for producing the same
EP2860276A4 (fr) * 2013-08-13 2015-12-30 Nippon Steel & Sumitomo Metal Corp Plaque d'acier
EP3239332A4 (fr) * 2014-12-24 2017-11-22 Posco Acier à haute résistance ayant une excellente résistance à la propagation de fissures fragiles et procédé de production s'y rapportant
EP3239331A4 (fr) * 2014-12-24 2017-11-08 Posco Acier à haute résistance ayant une excellente résistance à la propagation de fissures fragiles et son procédé de production
EP3239330A4 (fr) * 2014-12-24 2017-11-08 Posco Acier à haute résistance ayant une excellente résistance à la propagation de fissures fragiles et procédé de production s'y rapportant
US10822671B2 (en) 2014-12-24 2020-11-03 Posco High-strength steel having superior brittle crack arrestability, and production method therefor
US10883159B2 (en) 2014-12-24 2021-01-05 Posco High-strength steel having superior brittle crack arrestability, and production method therefor
CN107406951A (zh) * 2015-03-31 2017-11-28 杰富意钢铁株式会社 高强度/高韧性钢板及其制造方法
EP3279351A4 (fr) * 2015-03-31 2018-03-07 JFE Steel Corporation Tôle d'acier laminée à chaud à résistance et ténacité élevées et son procédé de fabrication
CN107406951B (zh) * 2015-03-31 2019-09-24 杰富意钢铁株式会社 高强度和高韧性钢板及其制造方法
US10544478B2 (en) 2015-03-31 2020-01-28 Jfe Steel Corporation High-strength, high-toughness steel plate, and method for producing the same
US10640841B2 (en) 2015-03-31 2020-05-05 Jfe Steel Corporation High-strength, high-toughness steel plate and method for producing the same

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TWI335355B (en) 2011-01-01
KR101024709B1 (ko) 2011-03-24
TW200844240A (en) 2008-11-16
BRPI0808347A2 (pt) 2014-07-29
CN101622370A (zh) 2010-01-06
EP2119803A4 (fr) 2016-07-20
KR20090110384A (ko) 2009-10-21
JP2008248382A (ja) 2008-10-16
CN101622370B (zh) 2011-07-13
WO2008108333A1 (fr) 2008-09-12
BRPI0808347B1 (pt) 2017-07-04
JP4309946B2 (ja) 2009-08-05

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