EP3418412B1 - Stahl nützlich als material für ketten - Google Patents

Stahl nützlich als material für ketten Download PDF

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EP3418412B1
EP3418412B1 EP16890566.9A EP16890566A EP3418412B1 EP 3418412 B1 EP3418412 B1 EP 3418412B1 EP 16890566 A EP16890566 A EP 16890566A EP 3418412 B1 EP3418412 B1 EP 3418412B1
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steel
content
quenching
tempering
low
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French (fr)
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EP3418412A4 (de
EP3418412A1 (de
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Shinya Teramoto
Shingo Yamasaki
Atsushi Monden
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Nippon Steel Corp
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Nippon Steel Corp
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    • 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
    • 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
    • C22C38/02—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • 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
    • 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
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/003—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
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and 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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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

Definitions

  • the present invention relates to steel having a high strength and an excellent low-temperature toughness after quenching and tempering.
  • Such chains are manufactured by cutting a hot rolled steel bar having a diameter of ⁇ 50 mm or more to a predetermined length, forming the steel bar to an annular shape, and welding butted end surfaces through flash butt welding. After flash butt welding, there are cases where a stud is press-fitted into the center of the annular chain. After that, the chain is quenched and tempered, thereby imparting a high strength and a high toughness to the chain.
  • Patent Documents 1 to 6 and the like can be exemplified as invention examples of steel for a high strength and high toughness chain.
  • all of the documents aim to provide a chain having a tensile strength of 800 MPa to 1,000 MPa and do not study a case where the strength of steel is set to 1,200 MPa or more.
  • an increase in the strength of steel generally degrades the toughness of steel and thus decreases the impact value of steel.
  • the strength of the steel having the chemical composition proposed by the above described documents is set to 1,200 MPa or more, it is not possible to obtain an intended impact value.
  • An object of the present invention is to provide a steel having a high strength and an excellent low-temperature toughness (particularly, fracture toughness at a low temperature) after quenching and tempering.
  • the object of the invention is to provide a steel in which the Charpy impact value at -20°C reaches 75 J/cm 2 or more, when quenching and tempering are carried out so that the tensile strength reaches 1,200 MPa or more.
  • the present inventors have continued a variety of researches in order to realize steel having a high strength and an excellent low-temperature toughness, as a result, the present inventors obtained the following findings.
  • the present inventors found a structural component having a high strength and a high low-temperature toughness, particularly, steel which can be used for manufacturing chains.
  • steel according to the present embodiment is steel having an effect in which the tensile strength reaches 1,200 MPa or more and the Charpy impact value at - 20°C reaches 75 J/cm 2 or more after quenching and tempering
  • the strength and the impact value before quenching and tempering are not particularly limited.
  • description of mechanical properties such as strength and toughness relates to the steel according to the present embodiment after quenching and tempering.
  • the unit "%" of the amounts of the alloying elements indicates mass%.
  • the C is an important element that determines the strength of the steel.
  • the lower limit of the C content is set to 0.08%.
  • the upper limit of the C content is set to 0.12%.
  • the upper limit of the C content is preferably 0.11%.
  • the lower limit of the C content is preferably 0.09%.
  • Si has an action of ensuring the strength of the steel and also an action as a deoxidizing agent.
  • the Si content is less than 0.05%, the deoxidizing action cannot be sufficiently obtained, the number of non-metallic inclusions in the steel is increased, and the toughness of the steel is degraded.
  • the Si content is more than 0.50%, Si causes the degradation in the toughness of the steel. Therefore, the Si content is set to 0.05% to 0.50%.
  • the upper limit of the Si content is preferably 0.40%, 0.30%, or 0.20%.
  • the lower limit of the Si content is preferably 0.06%, 0.07%, or 0.08%.
  • Mn is an essential element for ensuring required hardenability.
  • the lower limit of the Mn content is set to 1.50%.
  • the upper limit of the Mn content is set to 3.00%.
  • the upper limit of the Mn content is preferably 2.90%, 2.80%, or 2.70%.
  • the lower limit of the Mn content is preferably 1.70%, 1.90%, or 2.00%.
  • P is an impurity that is incorporated into the steel during the manufacturing process of the steel.
  • the upper limit of the P content is preferably 0.030%, 0.025%, or 0.020%.
  • the steel according to the present embodiment does not need P, and thus the lower limit of the P content is 0%; however, when the capability of a refining facility and the like are taken into account, the lower limit of the P content may be set to 0.001 %, 0.002%, or 0.003%.
  • S is, similar to P, an impurity that is incorporated into the steel during the manufacturing process of the steel.
  • S content exceeds 0.020%, S forms a large amount of MnS in the steel, and the toughness of the steel is degraded. Therefore, the S content is limited to 0.020% or less.
  • the upper limit of the S content is preferably 0.015%, 0.012%, or 0.010%.
  • the steel according to the present embodiment does not need S, and thus the lower limit of the S content is 0%; however, when the capability of a refining facility and the like are taken into account, the lower limit of the S content may be set to 0.001%, 0.002%, or 0.003%.
  • the Cr has an action for enhancing the hardenability of the steel.
  • the lower limit of the Cr content is set to 1.00%.
  • the upper limit of the Cr content is set to 2.50%.
  • the upper limit of the Cr content is preferably 2.40%, 2.30%, or 2.20%.
  • the lower limit of the Cr content is preferably 1.30%, 1.40%, or 1.50%.
  • the Cu is an effective element for improving the hardenability and corrosion resistance of the steel.
  • the lower limit of the Cu content is set to 0.01%.
  • the upper limit of the Cu content is set to 0.50%.
  • the upper limit of the Cu content is preferably 0.40%, 0.30%, or 0.20%.
  • the lower limit of the Cu content is preferably 0.02%, 0.03%, or 0.05%.
  • Ni is an extremely effective element for improving the toughness of the steel and an essential element for increasing the toughness of the steel according to the present embodiment after quenching and tempering.
  • the Ni content is less than 0.75%, it is difficult to sufficiently exhibit the effects.
  • the Ni content is excessive, the amount of residual austenite is increased, and thus the low-temperature toughness is, conversely, degraded. Therefore, the upper limit of the Ni content is set to 1.60%.
  • the upper limit of the Ni content is preferably 1.50%, 1.35%, or 1.20%.
  • the lower limit of the Ni content is preferably 0.80%, 0.85%, or 0.90%.
  • Mo has an effect for improving the low-temperature toughness of the steel. Mo miniaturizes cementite which acts as an origin of fracture and makes cementite harmless. In addition, Mo miniaturizes the block size of a martensite, decreases the ductile-brittle transition temperature of the steel, and thus prevents brittle fracture from easily occurring at a low temperature. When the Mo content is less than 0.10%, it is difficult to sufficiently exhibit the effects. On the other hand, when the Mo content exceeds 0.50%, the effect for improving toughness is saturated. Therefore, the Mo content is set to 0.10% to 0.50%. The upper limit of the Mo content is preferably 0.47%, 0.45%, or 0.42%. The lower limit of the Mo content is preferably 0.15%, 0.20%, or 0.25%.
  • Al has an action for adjusting the crystal grain size of a metallographic structure and miniaturizing the metallographic structure when Al is precipitated as AlN.
  • the Al content is less than 0.025%, it is not possible to obtain a sufficient miniaturizing effect, and thus the toughness of the steel is degraded.
  • the Al content in the steel exceeds 0.050%, the amount of AlN precipitated is saturated, the number of alumina based non-metallic inclusions in the steel is increased, and the toughness of the steel is degraded. Therefore, the Al content is set to 0.025% to 0.050%.
  • the upper limit of the Al content is preferably 0.045%, 0.042%, or 0.040%.
  • the lower limit of the Al content is preferably 0.027%, 0.029%, or 0.030%.
  • N has an action for precipitating AlN, which is effective for adjusting the crystal grain size of the metallographic structure, by bonding to Al.
  • the N content is set to 0.0100% to 0.0200%.
  • the upper limit of the N content is preferably 0.0180%, 0.0170%, or 0.0160%.
  • the lower limit of the N content is preferably 0.0110%, 0.0120%, or 0.0130%.
  • V 0.010% or less
  • the V content, the Ti content and the Nb content are preferably small. This is because VN, NbC, and Ti(C, N) which are generated from V, Nb, and Ti degrade the low-temperature toughness of the steel.
  • the present inventors found that, in order to prevent the degradation in the low-temperature toughness of the steel, it is necessary that to the V content is limited to 0.010% or less, the Ti content is limited 0.010% or less, and the Nb content is limited to 0.005% or less.
  • the upper limit of the V content is preferably 0.009%, 0.007%, or 0.005%.
  • the upper limit of the Ti content is preferably 0.009%, 0.007%, or 0.005%.
  • the upper limit of the Nb content is preferably 0.004%, 0.003%, or 0.002%.
  • the lower limits of the V content, the Ti content and the Nb content are 0%.
  • the lower limit of the V content may be set to 0.003%, 0.002%, or 0.001%
  • the lower limit of the Ti content may be set to 0.003%, 0.002%, or 0.001 %
  • the lower limit of the Nb content may be set to 0.0010%, 0.0009%, or 0.0008%.
  • the steel according to the present embodiment does not need Ca, Zr, and Mg. Therefore, the lower limits of the the Ca content, the Zr content, and the Mg content is 0%. However, all of Ca, Zr, and Mg have an effect for forming an oxide, acting as a crystallization nucleus of MnS, and uniformly and finely dispersing MnS so as to improve the impact value of the steel. Therefore, as an optional element, the steel may contain 0.0005% or more, 0.0010% or more, or 0.0015% or more of Ca, may contain 0.0005% or more, 0.0010% or more, or 0.0015% or more of Zr, and may contain 0.0005% or more, 0.0010% or more, or 0.0015% or more of Mg.
  • the upper limits of each of the Ca content, the Zr content, and the Mg content is set to 0.0100% or less.
  • the upper limit of the Ca content is preferably 0.0090%, 0.0070%, or 0.0050%
  • the upper limit of the Zr content is preferably 0.0090%, 0.0070%, or 0.0050%
  • the upper limit of the Mg content is preferably 0.0090%, 0.0070%, or 0.0050%.
  • the remainder of the chemical composition of the steel according to the present embodiment consists of Fe and impurities.
  • the impurities refer to elements which are incorporated by a raw material such as an ore or a scrap, or a variety of causes in the manufacturing process during the industrial manufacturing of the steel, and the impurities are permitted to an extent in which the steel according to the present embodiment is not adversely influenced.
  • Ratio (Y value) of Al content to N content 2.6 or less
  • the ratio (Y value) of the Al content to the N content is defined by the following Equation a.
  • Y Al / N
  • symbols in parentheses represent the amounts of elements relating to the symbols, by unit mass%.
  • AlN has an effect for miniaturizing crystal grains and improving the low-temperature toughness of the steel.
  • the ratio (Y value) of the Al content to the N content in the steel exceeds 2.6, the number of alumina based non-metallic inclusions in the steel is increased, and the steel becomes brittle, and thus, conversely, the low-temperature toughness is degraded. Therefore, the Y value is set to 2.6 or less.
  • the upper limit of the Y value is preferably 2.55, 2.50, or 2.45.
  • the lower limit of the Y value is not particularly limited; however, when the lower limit of the Al content and the upper limit of the N content which are described above are taken into account, the Y value does not become less than 1.25.
  • the present inventors obtained the above described finding from an experiment that will be described below.
  • the present inventors carried out quenching and tempering on a variety of steels having properties other than the Y value which are all in the specification ranges of the steel according to the present embodiment and different Y values under the following conditions and then carried out a Charpy impact test at -20°C.
  • the present inventors obtained a graph showing the relationship between the Y value and the impact value at -20°C ( Fig. 1 ). As shown in Fig. 1 , steels having a Y value of more than 2.6 did not have sufficient low-temperature toughness after quenching and tempering.
  • Ratio (Z value) of Mn content to Ni content 1.5 or more and 3.0 or less
  • the ratio (Z value) of the Mn content to the Ni content is defined by the following Equation b.
  • Z Mn / Ni
  • Ni improves the low-temperature toughness of the steel.
  • the ratio (Z value) of the Mn content to the Ni content in the steel is less than 1.5, the number of residual austenite is increased, and the low-temperature toughness of the steel is impaired.
  • the Z value exceeds 3.0 the ratio of the amount of solute Mn to the Ni content becomes excessive, the effect of Ni for improving low-temperature toughness is negated, the steel becomes brittle, and the low-temperature toughness is degraded. Therefore, the Z value is set to 1.5 or more and 3.0 or less.
  • the upper limit of the Z value is preferably 2.9, 2.8, or 2.7.
  • the lower limit of the Z value is preferably 1.6, 1.7, or 1.8.
  • the present inventors obtained the above described finding from an experiment that will be described below.
  • the present inventors carried out quenching and tempering on a variety of steels having properties other than the Z value which are all in the specification ranges of the steel according to the present embodiment and different Z values under the following conditions and then carried out a Charpy impact test at -20°C.
  • the present inventors obtained a graph showing the relationship between the Z value and the impact value at -20°C ( Fig. 2 ). As shown in Fig. 2 , steels having a Z value of less than 1.5 or more than 3.0 did not have sufficient low-temperature toughness after quenching and tempering.
  • the number density of AlN, the grain diameters, the dispersion state, and the like in the steel change depending on the conditions of a heat treatment (for example, quenching and tempering) that is carried out on the steel.
  • a heat treatment for example, quenching and tempering
  • AlN effectively functions during quenching and tempering under conditions which is selected so as to set a tensile strength of the steel to 1,200 MPa or more, and the toughness of the steel is improved.
  • the object of the steel according to the present embodiment is to set a Charpy impact value at -20°C of the steel to 75 J/cm 2 or more after a heat treatment is carried out on the steel so that the tensile strength reaches 1,200 MPa, but the control of the state of AlN is not necessary to achieve the object of the steel according to the present embodiment. Therefore, in the steel according to the present embodiment, the state of AlN is not particularly specified. Meanwhile, from the result of the experiment, the present inventors assume that, when the steel is heated to 850°C to 900°C, AlN is preferably precipitated regardless of the state of the steel before heating, and, when the steel in this state is cooled, the structure is preferably miniaturized due to AlN.
  • the steel according to the present embodiment is particularly preferably used as steel for quenching.
  • the average grain size of cementite is 0.05 ⁇ m or less
  • the average size of martensite blocks is 5.5 ⁇ m or less
  • the amount of residual austenite is 5% or less.
  • the steel according to the present embodiment contains 0.08% or more of C and thus has a tensile strength of 1,200 MPa or more when the heat treatment under the above described quenching and tempering conditions is carried out thereon.
  • the tensile strength of the steel is 1,200 MPa or more, the low-temperature toughness (particularly, low-temperature toughness) is impaired.
  • the steel according to the present embodiment contains 0.025% to 0.050% of Al, 0.0100% to 0.0200% of N, and 0.10% to 0.50% of Mo, and thus, even when the heat treatment under the above-described quenching and tempering conditions is carried out thereon, martensite blocks and cementite are sufficiently miniaturized, and the steel has the high low-temperature toughness.
  • the steel according to the present embodiment contains 0.75% to 1.60% or Ni and thus has the high low-temperature toughness even when the heat treatment under the above-described quenching and tempering conditions is carried out thereon.
  • the ratio of the Al content to the N content and the ratio of the Ni content and the Mn content are controlled, and thus the low-temperature toughness is not impaired.
  • the V content is controlled to 0.010% or less
  • the Ti content is controlled to 0.010% or less
  • the Nb content is controlled to 0.005% or less, and thus, even when the heat treatment under the above described quenching and tempering conditions is carried out on the steel, the precipitation of inclusions is suppressed, and the steel has the high low-temperature toughness.
  • quenching and tempering treatment according to the above described conditions is simply an example of the use of the steel according to the present embodiment.
  • a heat treatment under random conditions can be carried out on the steel according to the present embodiment.
  • the properties of the steel according to the present embodiment on which the heat treatment is carried out on the basis of an example of the above described quenching and tempering conditions do not limit the technical scope of the steel according to the present embodiment.
  • the object of the steel according to the present embodiment is to obtain a Charpy impact value at -20°C of 75 J/cm 2 or more after a heat treatment is carried out so that the tensile strength reaches 1,200 MPa or more.
  • the steel according to the present embodiment has a high tensile strength and an excellent low-temperature toughness after quenching and tempering and is thus capable of exhibiting particularly excellent effects, when the steel according to the present embodiment is used as a material for chains for mooring offshore oil-drilling rigs.
  • V-notch Charpy impact test pieces were produced from a 1/4D portion (a region at a depth of approximately 1/4 of a diameter D of the round steel bar from the surface of the round steel bar) of a C cross section of this round steel bar.
  • a tensile test was carried out at normal temperature and a rate of 20 mm/min according to JIS Z 2241.
  • a Charpy impact test was carried out at -20°C according to JIS Z 2242.
  • a 10 mm x 10 mm sample was cut out from the 1/4D portion of the C cross section of the quenched and tempered round steel bar, the cross section of the sample was corroded with a nital etching solution, five structural photographs of the cross section of the sample were captured using a scanning electron microscope at a magnification of 5,000 times, and the average grain size of the cementite included in the photographs was obtained by means of an image analysis using Luzex (registered trademark) and considered as the average grain size of cementite in the round steel bar.
  • Luzex registered trademark
  • Table 1-1, Table 1-2, and Table 2 show the chemical compositions of example steels and comparative example steels
  • Table 2 shows the tensile strengths, the impact values, the average grain sizes of cementite, the average sizes of martensite blocks, and the amounts of residual austenite in the example steels and the comparative example steels after quenching and tempering under the above described conditions were carried out.
  • Table 1-2 values outside the specification ranges of the present invention are underlined.
  • Comparative Example No. 24 the C content was insufficient, and thus a necessary tensile strength could not be obtained after quenching and tempering.
  • Comparative Example No. 25 the C content was excessive, and thus the tensile strength became excessively high after quenching and tempering, and the low-temperature toughness was insufficient.
  • Comparative Example No. 26 the Si content was excessive, in Comparative Example No. 27, the Mn content was excessive, and, in Comparative Example No. 34, the Cr content was excessive. These excessive Si, Mn, and Cr degraded the toughness of the steel, and thus the low-temperature toughness was insufficient in Comparative Examples Nos. 26, 27, and 34 after quenching and tempering.
  • Comparative Example No. 35 the Ni content was insufficient, and the effect of Ni for improving low-temperature toughness was small, and thus the low-temperature toughness was insufficient.
  • Comparative Example No. 36 the Ni content was large, and the amount of residual austenite increased after quenching and tempering, and thus the low-temperature toughness was insufficient after quenching and tempering.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Claims (2)

  1. Ein Stahl, umfassend, in der Einheit Massen-%,
    C: 0,08% bis 0,12%;
    Si: 0,05 % bis 0,50 %;
    Mn: 1,50% bis 3,00%;
    P: 0,040% oder weniger;
    S: 0,020% oder weniger;
    V: 0,010% oder weniger;
    Ti: 0,010% oder weniger;
    Nb: 0,005% oder weniger;
    Cr: 1,00 % bis 2,50 %;
    Cu: 0,01% bis 0,50%;
    Ni: 0,75 % bis 1,60 %;
    Mo: 0,10% bis 0,50%,
    Al: 0,025% bis 0,050%;
    N: 0,0100% bis 0,0200%;
    Ca: 0% bis 0,0100%;
    Zr: 0% bis 0,0100%;
    Mg: 0% bis 0,0100%; und
    den Rest bestehend aus Fe und Verunreinigungen,
    wobei ein Y-Wert, definiert durch die Gleichung (a), 2,6 oder weniger beträgt, und
    ein Z-Wert, definiert durch die Gleichung (b), 1,5 oder mehr und 3,0 oder weniger beträgt, Y = Al / N
    Figure imgb0007
     Z = Mn / Ni
    Figure imgb0008
     die Symbole (Al), (N), (Mn) und (Ni) in den Gleichungen Mengen von Elementen, die sich auf die entsprechenden Symbole in dem Stahl beziehen, in Einheit Massen-% darstellen.
  2. Der Stahl nach Anspruch 1, umfassend, in Einheit Massen-%, eines oder mehrere ausgewählt aus der Gruppe bestehend aus
    Ca: 0,0005% bis 0,0100%;
    Zr: 0,0005% bis 0,0100%; und
    Mg: 0,0005% bis 0,0100%.
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WO2017141425A1 (ja) 2017-08-24
US20200165711A1 (en) 2020-05-28
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