EP3492610A1 - Tôle d'acier à haute résistance - Google Patents

Tôle d'acier à haute résistance Download PDF

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Publication number
EP3492610A1
EP3492610A1 EP16910563.2A EP16910563A EP3492610A1 EP 3492610 A1 EP3492610 A1 EP 3492610A1 EP 16910563 A EP16910563 A EP 16910563A EP 3492610 A1 EP3492610 A1 EP 3492610A1
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Prior art keywords
steel plate
content
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case
high strength
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EP16910563.2A
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German (de)
English (en)
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EP3492610A4 (fr
EP3492610B1 (fr
Inventor
Masahide Yoshimura
Masanori Minagawa
Norimasa Kawabata
Takeshi Tsuzuki
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Nippon Steel Corp
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Nippon Steel and Sumitomo Metal Corp
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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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/60—Aqueous agents
    • 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
    • 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
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • 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
    • 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
    • C21D2211/003—Cementite
    • 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 present invention relates to a high strength steel plate.
  • the total elongation is reduced in a case where the plate thickness of a steel plate is limited while increasing the strength of the steel plate to suppress the increase in the weight of members.
  • the plate thickness is limited to 25 mm or less
  • the plate thickness is limited to 8 mm or less
  • the steel plate is required to have not only a strength, but also ductility such as a total elongation.
  • low temperature toughness is also required to prevent brittle fracture.
  • a high strength steel plate having a tensile strength of 780 MPa or greater, or further 950 MPa, and a method of manufacturing the high strength steel plate are proposed.
  • Patent Document 1 proposes a high strength steel plate having excellent toughness which is obtained by hot-rolling and rapidly cooling a steel containing an alloy added thererto and reducing the C content and to obtain appropriate hardenability, and a method of manufacturing the steel plate.
  • Patent Document 1 does not consider the workability of the steel plate.
  • Patent Documents 2 to 4 propose a high strength hot rolled steel sheet which is manufactured by coiling a steel in a coil after hot rolling as a steel sheet which is used for construction machines or the like, and a method of manufacturing the hot rolled steel sheet.
  • Patent Documents 2 to 4 disclose a method of manufacturing a hot rolled steel sheet having a martensitic phase or a tempered martensitic phase as a primary phase by performing hot rolling, rapid cooling to near a martensitic transformation start temperature (Ms), holding for a predetermined period of time, and coniling in a coil.
  • Ms martensitic transformation start temperature
  • tempering heat treatment
  • tempering is preferably performed after the accelerated cooling to transform the microstructure to tempered martensite.
  • the tempering is omitted from the viewpoint of shortening the construction period or suppressing an increase in the manufacturing cost, the microstructure is transformed to martensite, and thus ductility or toughness is reduced although a high strength is obtained.
  • Patent Document 5 proposes a high strength steel plate in which a Mn content and a Ni content are suppressed and a Mo content and a V content are increased to suppress the formation of martensite and to provide a microstructure consisting mainly of lower bainite, and a method of manufacturing the high strength steel plate.
  • Patent document 5 since the technology described in Patent document 5 is based on the premise that the microstructure is obtained by setting a cooling stop temperature to 300°C to 450°C, a sufficient total elongation is not obtained.
  • the inventors produced a steel plate in accordance with the disclosure of Patent Document 5 and performed a test, but a total elongation of 12% or greater was not obtained.
  • a tensile strength (joint strength) thereof is required to be not less than a value required for a base metal in view of reliability of the structure.
  • a welding joint may have a lower tensile strength (joint strength) than a base metal due to softening of a heat-affected zone, and a required value may not be satisfied.
  • the inventors examined the relationship between the ductility of a steel plate and the accelerated cooling stop temperature. As a result, the inventors found that the ductility is reduced in a case where the accelerated cooling stop temperature is 300°C or higher or higher than a martensitic transformation completion temperature (Mf). The inventors further proceeded the examination, and found that in a case where the accelerated cooling is stopped at a temperature of 300°C or higher or a temperature higher than Mf, untransformed austenite transforms to bainite in a microstructure, voids starting from a coarse carbide (cementite) formed caused by the bainite are excessively generated, and thus the ductility is reduced.
  • Mf martensitic transformation completion temperature
  • the inventors studied ways to suppress such a reduction in the ductility.
  • the inventors designed a component capable of increasing hardenability to suppress the above-described bainitic transformation, and found new knowledge that in a case where accelerated cooling to a temperature which is lower than 300°C and not higher than Mf is performed after hot rolling, the microstructure can be allowed to consist mainly of martensite, and thus the ductility of a high strength steel plate can be secured.
  • the invention is contrived based on such knowledge, and the gist thereof is as follows.
  • a tensile strength of 950 MPa or greater can be secured at a welding joint where a high strength steel plate according to the invention is a base metal with a predetermined heat input or less in welding.
  • a high strength steel plate according to an embodiment of the invention (hereinafter, may be referred to as a high strength steel plate according to this embodiment) will be described in detail.
  • the C content is a useful element for increasing a strength of steel, and is a very important element for determining a total elongation of steel having a martensite structure.
  • the C content is required to be 0.050% or greater to obtain a sufficient strength.
  • the C content is preferably 0.060% or greater, 0.065% or greater, or 0.070% or greater.
  • the C content is required to be 0.100% or less to obtain a good total elongation and good toughness.
  • the C content is preferably adjusted to be 0.095% or less, 0.090% or less, or 0.085% or less.
  • the Si content is limited to 0.50% or less. It is not necessary to particularly determine the lower limit of the Si content, and the lower limit of the Si content is 0%. However, in a case where Si is used for deoxidation, the Si content is preferably adjusted to be 0.03% or greater to obtain a sufficient effect. In addition, Si is also an element which suppresses the generation of a carbide, and in order to obtain this effect, the Si content is preferably adjusted to be 0.10% or greater, and more preferably 0.20% or greater. In a case where it is not necessary to obtain the effects, the upper limit of the Si content may be adjusted to be 0.45%, 0.40%, or 0.35%.
  • Mn is an important element for improving the hardenability of steel.
  • the Mn content is adjusted to be 1.20% or greater to obtain a high strength by increasing a martensite area fraction in a microstructure.
  • the Mn content is preferably adjusted to be greater than 1.20%, 1.25% or greater, or 1.30% or greater, and more preferably 1.35% or greater or 1.39% or greater. In a case where the Mn content is too high, ductility and toughness may be reduced. Accordingly, the Mn content is adjusted to be 1.70% or less. More preferably, the Mn content is adjusted to be 1.60% or less, 1.55% or less, or 1.50% or less.
  • P and S are elements inevitably contained as impurities in steel, and deteriorate the toughness of steel.
  • P and S are elements which deteriorate the toughness of a heat-affected zone in a case where welding is performed. Therefore, the P content is limited to 0.020% or less, and the S content is limited to 0.0050% or less.
  • the P content may be adjusted to be 0.015% or less, and the S content may be adjusted to be 0.0030% or less. Since the P content and the S content are preferably low, and thus preferably reduced as much as possible. Accordingly, it is not necessary to particularly determine the lower limits of the P content and the S content, and the lower limits of the P content and the S content are 0%.
  • the P content may be adjusted to be 0.001% or greater, and the S content may be adjusted to be 0.0001% or greater.
  • the B is an element which is segregated in the grain boundary to increase the hardenability of steel, and is a useful element for exhibiting the effect even in a case where the amount thereof is very small.
  • the B content is adjusted to be 0.0003% or greater to increase martensite in a microstructure.
  • the B content is adjusted to be 0.0005% or greater.
  • the B content is adjusted to be 0.0030% or less.
  • the B content is preferably adjusted to be 0.0020% or less or 0.0015% or less.
  • Total Content of One or Both of Cr and Mo is 0.20% or Greater, and In Case Where Mo Content is Greater Than 0.50%, Cr Content is 0.80% or Less
  • the Cr content and the Mo content are adjusted to be 2.00% or less and 0.90% or less, respectively.
  • the Cr content is preferably adjusted to be 1.50% or less or 1.00% or less, and more preferably 0.90% or less or 0.80%.
  • the Mo content is preferably adjusted to be 0.70% or less, and more preferably 0.60% or less or 0.50%.
  • N is inevitably contained as impurities. N forms BN and inhibits the hardenability improving effect of B. Accordingly, the N content is limited to 0.0080% or less. The N content is preferably limited to 0.0060% or less, and more preferably 0.0050% or less. The N content is preferably reduced as much as possible, and the lower limit thereof is 0%. However, from the viewpoint of cost of denitrification, the N content may be adjusted to be 0.0001% or greater. The N content may be adjusted to be 0.0020% or greater for refining of a microstructure by a nitride.
  • the high strength steel plate according to this embodiment may further contain, other than the above-described components, one or more of 0.100% or less of Al, 0.50% or less of Cu, 0.50% or less of Ni, 0.100% or less of V, 0.50% or less of W, 0.0030% or less of Ca, 0.0030% or less of Mg, and 0.0030% or less of REM instead of a part of Fe. Since these elements are not essential elements, the contents of the elements may be 0%.
  • Al is a deoxidizing element.
  • the Al content is preferably adjusted to be 0.010% or greater to obtain a sufficient effect.
  • the Al content is limited to 0.100% or less even in a case where Al is contained.
  • the Al content is preferably limited to 0.080% or less, more preferably 0.050% or less, and even more preferably 0.030% or less.
  • Cu and Ni are elements which improve the hardenability of steel.
  • the Cu content and the Ni content are preferably adjusted to be 0.10% or greater, respectively. Since Cu and Ni are expensive elements, the Cu content and the Ni content are preferably adjusted to be 0.50% or less, respectively, even in a case where Cu and Ni are contained.
  • the Cu content and the Ni content are more preferably adjusted to be 0.40% or less, and even more preferably 0.30% or less, respectively.
  • V is an element which forms a carbide or a nitride.
  • the V content is preferably adjusted to be 0.005% or greater in a case where toughness is increased by grain refining by a carbide or a nitride. In a case where the V content is too high, ductility or toughness is reduced. However, since V has less adverse effects than Nb or Ti, the upper limit of the V content is limited to 0.100% in a case where V is contained.
  • the V content is preferably adjusted to be 0.050% or less.
  • W is an element which improves the hardenability of steel.
  • the W content is preferably adjusted to be 0.05% or greater.
  • the W content is adjusted to be 0.50% or less or 0.30% or less even in a case where W is contained. If necessary, the W content may be adjusted to be 0.02% or less or 0.01% or less.
  • Ca is an element which controls the form of an oxide or a sulfide.
  • the Ca content is preferably adjusted to be 0.0001% or greater.
  • the Ca content is more preferably adjusted to be 0.0005% or greater, and even more preferably 0.0010% or greater.
  • the Ca content is adjusted to be 0.0030% or less even in a case where Ca is contained.
  • Mg is an element which acts to increase the toughness of steel by refining the microstructure.
  • the Mg content is preferably adjusted to be 0.0005% or greater. In a case where the Mg content is too high, the effect is saturated, and ductility or toughness may be reduced due to the formation of inclusions. Therefore, the Mg content is adjusted to be 0.0030% or less even in a case where Mg is contained.
  • REM rare earth metal
  • MnS a sulfide
  • the REM content is preferably adjusted to be 0.0001 % or greater. In a case where the REM content is too high, inclusions including REM may become coarse, and thus ductility or toughness may be reduced. Therefore, the REM content is adjusted to be 0.0030% even in a case where REM is contained.
  • DI and Pcm which are determined by a chemical composition, are required to satisfy the following ranges, respectively.
  • a structure mainly including martensite in which 90% or more of a microstructure is martensite is preferably provided.
  • the martensite area fraction in the microstructure is preferably adjusted to be 90% or greater, more preferably 92% or greater, and even more preferably 94% or greater.
  • both the martensite and the bainite are continuous cooling transformation structures, and it may be difficult to accurately distinguish the martensite and the bainite by observing the microstructures. In such a case, it can be judged that the formation of bainite causing the formation of coarse cementite is suppressed in a case where the total area fraction of martensite and bainite is 99% or greater and the total elongation is 12% or greater.
  • the total area fraction of one or both of martensite and bainite is adjusted to be 99% or greater, and the total elongation as a structure index is adjusted to be 12% or greater.
  • the martensite area fraction is preferably 90% or greater.
  • the martensite of the microstructure is as quenched, and is different from tempered martensite obtained after tempering treatment. Tempered martensite is not preferable since cementite grows by tempering for a long period of time.
  • the remainder other than the above microstructures may include one or more of ferrite, pearlite, and residual austenite.
  • the distinguishment of the microstructure and the measurement of the martensite area fraction are performed using an optical microscope. Specifically, near a 1/4 t-portion in a cross-section parallel to a rolling direction (a portion at a depth of 1/4 of a plate thickness t from a steel plate surface in a plate thickness direction) is subjected to nital etching, and two regions within a range of 120 ⁇ m ⁇ 100 ⁇ m are photographed at 500-fold magnification using an optical microscope to measure an area fraction of a microstructure in which an acicular lath structure is developed.
  • the cross-section of the steel plate is subjected to electrolytic polishing, and then a portion near the 1/4 t-portion in the cross-section of the steel plate is observed by a scanning electron microscope (SEM).
  • SEM scanning electron microscope
  • the magnification is 5,000 times, and the photographing is performed within a range of 50 ⁇ m ⁇ 40 ⁇ m.
  • the acicular structure is defined as martensite, and an area fraction of the region is obtained.
  • the product of the acicular structure area fraction measured using the optical microscope and the martensite area fraction measured using SEM is an area fraction of the martensite structure of this steel.
  • the orientation of the long axis direction of cementite in two or more directions in the block may not be clearly distinguished.
  • the area fraction of a microstructure in which an acicular lath structure is developed is defined as the total area fraction of martensite and bainite.
  • the inventors found that by controlling an accelerated cooling stop temperature, the number fraction of the coarse carbide (particularly, cementite) having a length of 1.0 ⁇ m or greater in a long axis direction can be reduced, and as a result, the generation of voids can be suppressed and the total elongation can be improved. Specifically, the inventors found that the total elongation can be improved by adjusting the number fraction of cementite having a length of 1.0 ⁇ m or greater in a long axis direction in cementite having a length of 0.1 ⁇ m or greater in a long axis direction to be 5% or less.
  • the invention by stopping accelerated cooling at a temperature which is not higher than Mf and lower than 300°C, it is possible to provide a structure mainly including martensite in which the generation of a coarse carbide is suppressed. That is, the generation of voids starting from coarse cementite having a length of 1.0 ⁇ m in a long axis direction can be suppressed by controlling an accelerated cooling stop temperature.
  • the number of cementite having an aspect ratio of 2.0 or greater and a length of 1.0 ⁇ m or greater in a long axis direction is counted.
  • the obtained number of precipitates of 1.0 ⁇ m or greater is divided by the number of cementite of 0.1 ⁇ m or greater, and thus the number fraction (%) of cementite of 1.0 ⁇ m or greater is obtained.
  • the shape of the carbide is not particularly limited. However, in a case where the carbide has an ellipsoidal shape, the "length in a long axis direction" refers to a major axis.
  • the aspect ratio of prior austenite grains is adjusted to be 2.0 or greater. In a case where the aspect ratio is less than 2.0, toughness may be reduced.
  • a high strength steel plate which is used for cranes or the like has a plate thickness of 4.5 to 20 mm. Therefore, the high strength steel plate according to this embodiment has a plate thickness of 4.5 to 20 mm. However, the thickness is preferably 4.5 to 15 mm in view of contribution to a reduction in the weight.
  • the total elongation is adjusted to be 12% or greater.
  • the total elongation may be a structure index indicating whether the formation of bainite, which causes the formation of coarse cementite is suppressed.
  • the high strength steel plate may be required to have low temperature toughness. Therefore, the Charpy absorbed energy at -20°C is preferably 59 J/cm 2 . More preferably, the Charpy absorbed energy at -40°C is preferably 59 J/cm 2 or greater.
  • a heated slab is hot-rolled. After the hot rolling, it is necessary to start accelerated cooling at a temperature at which the microstructure is austenite in order to provide a microstructure mainly including martensite through the accelerated cooling. Accordingly, the hot rolling should be ended at a temperature at which the microstructure is austenite.
  • the hot rolling finishing temperature is adjusted to be Ar3 (°C) or higher.
  • Ar3 (°C) is a temperature at which transformation from austenite to ferrite starts during cooling, and can be obtained from thermal expansion behavior.
  • Ar3 (°C) can be simply obtained by (Formula b).
  • Ar 3 868 ⁇ 396 ⁇ C + 24.6 ⁇ Si ⁇ 68.1 ⁇ Mn ⁇ 36.1 ⁇ Ni ⁇ 20.7 ⁇ Cu ⁇ 24.8 ⁇ Cr + 29.6 ⁇ Mo
  • the hot rolling may be performed in the usual manner, and it is preferable that recrystallization region rolling be performed with a cumulative rolling reduction of 50% to 80% within a temperature range not lower than 1,050°C, or non-recrystallization region rolling be performed with a cumulative rolling reduction of 50% to 90% within a temperature range of Ar3 to 950°C.
  • the cooling rate of the accelerated cooling is required to be 30 °C/s or higher to increase a martensite area fraction. A sufficient martensite area fraction is not obtained when the cooling rate is lower than 30 °C/s.
  • the cooling rate is preferably increased, but there is a restriction caused by a plate thickness or facility. Accordingly, the upper limit may be 200 °C/s or lower.
  • the cooling rate is calculated as follows: a temperature variation of a steel plate surface after hot rolling is measured, and a difference between a surface temperature before the water cooling is started and a surface temperature immediately after the water cooling is stopped is divided by a time required for cooling.
  • cooling to at least Ms (°C) or lower is required, and in a case where cooling (rapid cooling) to Mf (°C) or lower is performed, 90% or more of the microstructure transforms to martensite.
  • the cooling stop temperature is 300°C or higher, the cooling may become unstable and a part of the microstructure transforms to not martensite but bainite. Accordingly, the cooling stop temperature is adjusted to be not higher than Mf (°C) and lower than 300°C.
  • the accelerated cooling stop temperature is very important, and a precondition is set that the accelerated cooling is stopped at a temperature lower than the martensitic transformation start temperature Ms (°C).
  • the microstructure transforms to a structure mainly including martensite in which the generation of a carbide is suppressed.
  • the ductility of a high strength steel plate is influenced by hardenability. That is, in a case where the hardenability is increased, the formation of bainite is suppressed, and the generation of a coarse cementite-based carbide is suppressed. Accordingly, the total elongation is improved, and the variation is also reduced.
  • FIG. 1 The relationship between the accelerated cooling stop temperature Tcf and Mf and the total elongation, and the influence of DI and the C content on the total elongation are qualitatively summarized as schematically shown in FIG. 1 .
  • the vertical axis represents a total elongation
  • the horizontal axis represents accelerated cooling stop temperature Tcf
  • DI represents a hardenability index which is obtained by (Formula 1).
  • microstructure and the mechanical properties were evaluated.
  • the distinguishment of a microstructure and the measurement of a martensite area fraction and a bainite area fraction were performed by the following method.
  • a cross-section of a steel plate was subjected to mirror polishing, and then near a 1/4 t-portion in the cross-section parallel to a rolling direction was subjected to nital etching.
  • Two regions within a range of 120 ⁇ m ⁇ 100 ⁇ m were photographed at 500-fold magnification using an optical microscope to measure an area fraction of a microstructure in which an acicular lath structure was developed.
  • the cross-section of the steel plate was subjected to electrolytic polishing, and then a portion near the 1/4 t-portion in the cross-section of the steel plate was observed by a scanning electron microscope (SEM).
  • the magnification was 5,000 times, and the photographing was performed within a range of 50 ⁇ m ⁇ 40 ⁇ m.
  • the acicular structure was defined as martensite, and an area fraction of the region was obtained.
  • the product of the acicular structure area fraction measured using the optical microscope and the martensite area fraction measured using SEM was an area fraction of the martensite structure of this steel.
  • An acicular structure other than the martensite was determined as bainite.
  • a microstructure (remainder) other than the "martensite and bainite" described in Table 3 includes one or more of ferrite, pearlite, bainite, and residual austenite.
  • a cross-section of the steel plate was subjected to electrolytic polishing, and then a portion near a 1/4 t-portion in the cross-section of the steel plate was observed by a scanning electron microscope (SEM) to measure the number density of cementite.
  • SEM scanning electron microscope
  • a cross-section of the steel plate was subjected to electrolytic polishing, and then a portion near a 1/4 t-portion in the cross-section of the steel plate was photographed within a range of 50 ⁇ m ⁇ 40 ⁇ m at 5,000-fold magnification by a scanning electron microscope (SEM).
  • the number of precipitates as cementite having an aspect ratio of 2.0 or greater and a length of 0.1 ⁇ m or greater in a long axis direction was counted using image analysis software.
  • the number of cementite having an aspect ratio of 2.0 or greater and a length of 1.0 ⁇ m or greater in a long axis direction was counted.
  • the obtained number of precipitates of 1.0 ⁇ m or greater was divided by the number of cementite of 0.1 ⁇ m or greater, and thus the number fraction (%) of cementite of 1.0 ⁇ m or greater was obtained. In a case where the number fraction of cementite of 1.0 ⁇ m or greater was 5% or less, this was judged as a good result.
  • the aspect ratio of prior austenite grains was measured. Specifically, near a 1/4 t-portion in a cross-section parallel to a rolling direction was etched with nital, and two regions within a range of 120 ⁇ m ⁇ 100 ⁇ m were photographed at 500-fold magnification using an optical microscope. From the obtained image, long axis lengths and short axis lengths of at least 50 prior austenite grains were measured, and the long axis length was divided by the short axis length to obtain an aspect ratio of each grain. An average of the aspect ratios of the prior austenite grains was obtained and defined as an aspect ratio of the prior austenite grains. In a case where the aspect ratio of the prior austenite grains was 2.0 or greater, this was judged as a good result.
  • a test piece (overall thickness) was collected from the steel plate, and a tensile strength, a yield strength, and a total elongation were measured based on JIS Z 2241. In addition, a Charpy absorbed energy at -20°C and a Charpy absorbed energy at -40 °C were measured based on JIS Z 2242.
  • the tensile test piece is a No. 5 test piece (overall thickness) collected such that a longitudinal direction is perpendicular to the rolling direction, and the yield strength is 0.2% proof stress.
  • the Charpy test piece is a sub-sized test piece of 10 mm ⁇ 5 mm collected from a thickness middle portion such that a longitudinal direction is the rolling direction.
  • the mechanical properties were evaluated to be good in a case where the yield strength was 885 MPa or greater, the tensile strength was 950 MPa or greater, the total elongation was 12% or greater, and the absorbed energy value at -20°C (vE -20 ) was 59 J/cm 2 or greater as a result of the tests.
  • Welding joints were produced using steel plates having good mechanical properties (steel plate Nos. 1 to 16) and a steel plate No. 32 in which Pcm was less than 0.189%.
  • the welding method was MAG welding, and the weld heat input was 7.0 kJ/cm or 10.0 kJ/cm.
  • the welding conditions were set as follows: a current of 280 A, a voltage of 27 V, and a welding rate of 65 cm/min.
  • the welding conditions were set as follows: a current of 305 A, a voltage of 29 V, and a welding rate of 53 cm/min.
  • the tensile strength (joint strength) of the welding joint was evaluated by a tensile test specified in JIS Z 3121, and evaluated to be good in a case where the tensile strength was 950 MPa or greater.
  • Steel plate Nos. 1 to 16 are invention examples, and an excellent strength, excellent ductility, and excellent toughness are obtained.
  • the joint strength is 950 MPa or greater.
  • Mo/Cr is 0.20 or higher, excellent toughness is obtained even at a test temperature of -40°C.
  • Steel plate Nos. 17 to 35 are comparative examples, and one or more of the yield strength, the tensile strength, the total elongation, and vE -20 does not satisfy a target value.
  • a steel plate No. 31 had a high Cr content and a high Mo content, and DI was too high. Accordingly, the toughness and the total elongation were low.

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