US20220025475A1 - Impact and wear resistant component, and method for producing the same - Google Patents

Impact and wear resistant component, and method for producing the same Download PDF

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US20220025475A1
US20220025475A1 US17/311,886 US201917311886A US2022025475A1 US 20220025475 A1 US20220025475 A1 US 20220025475A1 US 201917311886 A US201917311886 A US 201917311886A US 2022025475 A1 US2022025475 A1 US 2022025475A1
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mass
less
steel
impact
wear resistant
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Eiji Amada
Kouji Kitamura
Kazuo Maeda
Naomi Kobayashi
Takashi Noda
Mamoru Hatano
Takafumi Amata
Yutaka Neishi
Kei Miyanishi
Ryoji Nishijima
Daisuke Takiguchi
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Komatsu Ltd
Nippon Steel Corp
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Komatsu Ltd
Nippon Steel Corp
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Assigned to KOMATSU LTD., NIPPON STEEL CORPORATION reassignment KOMATSU LTD. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: NODA, TAKASHI, AMADA, Eiji, HATANO, MAMORU, KITAMURA, KOUJI, KOBAYASHI, NAOMI, MAEDA, KAZUO, AMATA, Takafumi, MIYANISHI, KEI, NEISHI, YUTAKA, NISHIJIMA, RYOJI, TAKIGUCHI, Daisuke
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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation
    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—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
    • C22C38/04—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
    • C22C38/18—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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • E—FIXED CONSTRUCTIONS
    • E02—HYDRAULIC ENGINEERING; FOUNDATIONS; SOIL SHIFTING
    • E02F—DREDGING; SOIL-SHIFTING
    • E02F9/00—Component parts of dredgers or soil-shifting machines, not restricted to one of the kinds covered by groups E02F3/00 - E02F7/00
    • E02F9/28—Small metalwork for digging elements, e.g. teeth scraper bits
    • E02F9/2808—Teeth
    • E02F9/285—Teeth characterised by the material used
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • E—FIXED CONSTRUCTIONS
    • E02—HYDRAULIC ENGINEERING; FOUNDATIONS; SOIL SHIFTING
    • E02F—DREDGING; SOIL-SHIFTING
    • E02F5/00—Dredgers or soil-shifting machines for special purposes
    • E02F5/30—Auxiliary apparatus, e.g. for thawing, cracking, blowing-up, or other preparatory treatment of the soil
    • E02F5/32—Rippers

Definitions

  • the present invention relates to a component (impact and wear resistant component) that is subjected to repeated impact and wears by contact with earth and sand, such as a ground engaging tool (hereinafter, GET) component used in construction or mining equipment, and to a method for producing the same.
  • a component impact and wear resistant component
  • GET ground engaging tool
  • a ripper device is a rear attachment of a work vehicle such as a bulldozer, and is used to scrape up earth, sand, and bedrock. Ripping work can be performed as the work machine is advanced with a ripper point attached to the distal end of the ripper shank being penetrated into the ground. While the ripper shank is a strength member of the ripper device, it is an impact and wear resistant component that suffers wear and deformation. Although SCrB steel, JIS SNCM431H steel, etc. have conventionally been used as the steel material constituting the ripper shank, a material having even better durability is desired.
  • Patent Literature 1 Japanese Patent Application Laid-Open No. S61-166954
  • Patent Literature 2 Japanese Translation of PCT International Publication No. 2014/185337
  • Patent Literature 1 Japanese Patent Application Laid-Open No. S61-166954
  • Patent Literature 2 Japanese Translation of PCT International Publication No. 2014/185337
  • the resultant component When an impact and wear resistant component, particularly a GET component, is produced using the steel disclosed in Patent Literature 1 or 2, the resultant component will have a high strength. Further, a steel having an improved 0.2% proof stress will be able to, for example, suppress deformation (plastic flow) of the contact surface with the ripper point in the ripper shank. However, when the steel material disclosed in Patent Literature 1 is used to produce a large ripper shank having a wall thickness of 100 mm and a mass of about 1 ton, for example, the component will suffer a decrease in strength (insufficient hardenability) at the center in its wall thickness.
  • a component produced using the steel disclosed in Patent Literature 2 through a common production process tends to exhibit a small reduction of area in a tensile test.
  • the smaller reduction of area in the tensile test leads to lower resistance to breakage. That is, further improvement in durability is desired for the impact and wear resistant component produced through a common production process using the steel disclosed in Patent Literature 2.
  • One of the objects of the present invention is to provide an impact and wear resistant component excellent in durability and a method for producing the same.
  • An impact and wear resistant component according to the present invention is made of a steel containing not less than 0.41 mass % and not more than 0.44 mass % C, not less than 0.2 mass % and not more than 0.5 mass % Si, not less than 0.2 mass % and not more than 1.5 mass % Mn, not less than 0.0005 mass % and not more than 0.0050 mass % S, not less than 0.6 mass % and not more than 2.0 mass % Ni, not less than 0.7 mass % and not more than 1.5 mass % Cr, not less than 0.1 mass % and not more than 0.6 mass % Mo, not less than 0.02 mass % and not more than 0.03 mass % Nb, not less than 0.01 mass % and not more than 0.04 mass % Ti, not less than 0.0005 mass % and not more than 0.0030 mass % B, and not less than 20 mass ppm and not more than 60 mass ppm N, with the balance consisting of iron and unavoidable impurities, and having a hardness
  • the steel includes a matrix including a martensite phase and a residual austenite phase, and first nonmetallic particles dispersed in the matrix and including at least one species selected from the group consisting of MnS, TiCN, and NbCN.
  • the steel does not include a carbide represented as M 23 C 6 (where M represents the metallic elements constituting the steel).
  • a method for producing an impact and wear resistant component according to the present invention includes the steps of: preparing a steel material made of a steel containing not less than 0.41 mass % and not more than 0.44 mass % C, not less than 0.2 mass % and not more than 0.5 mass % Si, not less than 0.2 mass % and not more than 1.5 mass % Mn, not less than 0.0005 mass % and not more than 0.0050 mass % S, not less than 0.6 mass % and not more than 2.0 mass % Ni, not less than 0.7 mass % and not more than 1.5 mass % Cr, not less than 0.1 mass % and not more than 0.6 mass % Mo, not less than 0.02 mass % and not more than 0.03 mass % Nb, not less than 0.01 mass % and not more than 0.04 mass % Ti, not less than 0.0005 mass % and not more than 0.0030 mass % B, and not less than 20 mass ppm and not more than 60 mass ppm N, with the balance consisting of iron and
  • FIG. 1 is a schematic view showing the structure of a ripper device including a ripper shank and a ripper point;
  • FIG. 2 is a schematic perspective view showing the state of connection between the ripper shank and the ripper point;
  • FIG. 3 is a schematic cross-sectional view showing the structure of the ripper shank
  • FIG. 4 is a flowchart schematically illustrating the steps of producing a ripper shank
  • FIG. 5 shows optical micrographs of a microstructure of the steel
  • FIG. 6 shows SEM photographs of nonmetallic particles
  • FIG. 7 shows observation results using an optical microscope and SEM, and elemental mapping results
  • FIG. 8 shows a result of identification of a product present at a grain boundary
  • FIG. 9 shows a relationship between heating temperature and reduction of area.
  • An impact and wear resistant component of the present application is made of a steel containing not less than 0.41 mass % and not more than 0.44 mass % C, not less than 0.2 mass % and not more than 0.5 mass % Si, not less than 0.2 mass % and not more than 1.5 mass % Mn, not less than 0.0005 mass % and not more than 0.0050 mass % S, not less than 0.6 mass % and not more than 2.0 mass % Ni, not less than 0.7 mass % and not more than 1.5 mass % Cr, not less than 0.1 mass % and not more than 0.6 mass % Mo, not less than 0.02 mass % and not more than 0.03 mass % Nb, not less than 0.01 mass % and not more than 0.04 mass % Ti, not less than 0.0005 mass % and not more than 0.0030 mass % B, and not less than 20 mass ppm and not more than 60 mass ppm N, with the balance consisting of iron and unavoidable impurities, and having a hardness of
  • the steel includes a matrix including a martensite phase and a residual austenite phase, and first nonmetallic particles dispersed in the matrix and including at least one species selected from the group consisting of MnS, TiCN, and NbCN.
  • the steel does not include a carbide represented as M 23 C 6 (where M represents the metallic elements constituting the steel).
  • the steel may further contain at least one species selected from the group consisting of not less than 0.05 mass % and not more than 0.20 mass % V, not less than 0.01 mass % and not more than 0.15 mass % Zr, and not less than 0.1 mass % and not more than 2.0 mass % Co.
  • Carbon is an element that greatly affects the hardness of the steel. If the carbon content is less than 0.41 mass %, it will be difficult to obtain a hardness of HRC 53 or more in a portion having a wall thickness of about 100 mm, for example, with quenching and tempering. On the other hand, the carbon content exceeding 0.44 mass % will decrease the reduction of area and reduce the breakage resistance. The carbon content is thus necessary to be within the above-described range. From the standpoint of readily securing a sufficient hardness, the carbon content is preferably 0.42 mass % or more.
  • Silicon is an element that has the effects of improving the hardenability of the steel, enhancing the matrix of the steel, and improving the resistance to temper softening, and also has a deoxidizing effect in the steelmaking process. If the silicon content is 0.2 mass % or less, the above effects cannot be obtained sufficiently. If the silicon content exceeds 0.5 mass %, however, the reduction of area tends to decrease. The silicon content is thus necessary to be within the above-described range.
  • Manganese is an element effective in improving the hardenability of the steel, and also having a deoxidizing effect in the steelmaking process. If the manganese content is 0.2 mass % or less, the above effects cannot be obtained sufficiently. If the manganese content exceeds 1.5 mass %, however, the hardness before quench hardening will increase, leading to degradation in workability. From the standpoint of securing sufficient hardenability of the steel, the manganese content is preferably 0.4 mass % or more. Further, focusing on the workability, the manganese content is preferably 0.9 mass % or less, and more preferably 0.8 mass % or less.
  • Sulfur is an element that improves the machinability of the steel. Sulfur is also an element that is mixed during the steelmaking process even if not added intentionally. If the sulfur content is less than 0.0005 mass %, the machinability will decrease, and the production cost of the steel will increase. On the other hand, according to the investigations of the present inventors, in the component composition of the steel of the present application, the sulfur content greatly affects the reduction of area. If the sulfur content exceeds 0.0050 mass %, the reduction of area will decrease, making it difficult to obtain sufficient breakage resistance. The sulfur content is thus necessary to be within the above-described range. The sulfur content of 0.0040 mass % or less can further improve the breakage resistance.
  • Nickel is an effective element in improving the toughness of the matrix of the steel. If the nickel content is less than 0.6 mass %, such an effect cannot be exerted sufficiently. If the nickel content exceeds 2.0 mass %, however, nickel becomes more likely to segregate in the steel. This may cause variation in the mechanical properties of the steel. The nickel content is thus necessary to be within the above-described range. Further, with the nickel content exceeding 1.5 mass %, the improvement in toughness will become moderate, and the production cost of the steel will increase. From these standpoints, the nickel content is preferably 1.5 mass % or less. On the other hand, in the case of a steel having a hardness of HRC 53 or more, in order to sufficiently exert the effect of improving the toughness of the matrix of the steel, the nickel content is preferably 1.0 mass % or more.
  • Chromium improves the hardenability of the steel and also enhances the resistance to temper softening.
  • chromium being added in combination with molybdenum, niobium, vanadium, and the like considerably enhances the resistance to temper softening of the steel. If the chromium content is less than 0.7 mass %, the above effects cannot be exerted sufficiently. If the chromium content exceeds 1.5 mass %, however, the improvement of the resistance to temper softening will become moderate, and the production cost of the steel will increase. The chromium content is thus necessary to be within the above-described range.
  • Molybdenum improves the hardenability of the steel and enhances the resistance to temper softening. Molybdenum also has the function of improving the high temperature tempering brittleness. If the molybdenum content is less than 0.1 mass %, the above effects cannot be exerted sufficiently. If the molybdenum content exceeds 0.6 mass %, however, the above effects will be saturated. The molybdenum content is thus necessary to be within the above-described range.
  • Niobium is effective in improving the strength and toughness of the steel.
  • niobium is a highly effective element in improving the toughness because it makes the crystal grains of the steel extremely fine when added in combination with chromium and molybdenum.
  • the niobium content should be 0.02 mass % or more. If the niobium content exceeds 0.03 mass %, however, the crystallization of coarse eutectic NbC and the formation of a large amount of NbC cause a decrease in the amount of carbon in the matrix, leading to degradation in strength and toughness of the steel. Further, the niobium content exceeding 0.03 mass % will increase the production cost of the steel. The niobium content is thus necessary to be within the above-described range.
  • Titanium is effective in improving the toughness of the steel. Further, the addition of Ti can form Ti(C,N) and refine the crystal grains of the steel. If the titanium content is less than 0.01 mass %, such effects are small. If the titanium content exceeds 0.04 mass %, however, the toughness of the steel may rather deteriorate. The titanium content is thus necessary to be within the above-described range.
  • Boron is an element that considerably improves the hardenability of the steel.
  • the addition of boron can decrease the addition amounts of the other elements added for the purpose of improving the hardenability, and can reduce the production cost of the steel.
  • boron is more likely to segregate in the prior austenite grain boundary, and it particularly expels sulfur from the grain boundary, thereby improving the grain boundary strength. If the boron content is 0.0005 mass % or less, the above effects cannot be exerted sufficiently. The boron content exceeding 0.0030 mass %, however, may decrease the toughness of the steel. The boron content is thus necessary to be within the above-described range.
  • Nitrogen may deteriorate the toughness of the steel, except the case where nitrogen together with carbon forms carbonitrides with Ti or Nb to refine the crystal grains.
  • the nitrogen content is thus necessary to be 60 mass ppm or less.
  • the nitrogen content of less than 20 mass ppm, however, will increase the production cost of the steel.
  • the nitrogen content is thus necessary to be within the above-described range.
  • Vanadium is not an indispensable element. Vanadium, however, forms fine carbides, contributing to the refinement of crystal grains. If the vanadium content is less than 0.05 mass %, the above effect cannot be obtained sufficiently. If the vanadium content exceeds 0.20 mass %, however, the above effect will be saturated. Vanadium is a relatively expensive element, so it is preferably added in a minimum required amount. Thus, in the case of adding vanadium, the addition amount within the above-described range is appropriate.
  • Zirconium is not an indispensable element, but it has the effect of further improving the toughness of the steel by making carbides in the form of fine spherical particles dispersed in the steel. If the zirconium content is less than 0.01 mass %, its effect cannot be obtained sufficiently. If the zirconium content exceeds 0.15 mass %, however, the toughness of the steel may rather deteriorate. Thus, in the case of adding zirconium, the addition amount within the above-described range is appropriate.
  • Cobalt is not an indispensable element, but it increases the solid solubility of chromium, molybdenum, and other carbide-forming elements to the matrix, and also improves the resistance to temper softening of the steel.
  • the addition of cobalt thus achieves finer carbides and a higher tempering temperature, thereby improving the strength and toughness of the steel. If the cobalt content is less than 0.1 mass %, the above effects cannot be obtained sufficiently. On the other hand, because of its expensiveness, cobalt added in a large amount will increase the production cost of the steel. These problems become prominent with a cobalt content exceeding 2.0 mass %. Thus, in the case of adding cobalt, the addition amount within the above-described range is appropriate.
  • Phosphorus (P) as an unavoidable impurity is preferably contained in an amount of 0.010 mass % or less.
  • Copper (Cu) as an unavoidable impurity is contained in an amount of preferably 0.1 mass % or less and more preferably 0.05 mass % or less.
  • Aluminum (Al) as an unavoidable impurity is contained in an amount of preferably 0.04 mass % or less.
  • the impact and wear resistant component of the present application is made of a steel having the above-described appropriate component composition. Further, in the impact and wear resistant component of the present application, the steel constituting the impact and wear resistant component does not include a carbide represented as M 23 C 6 (where M represents the metallic elements constituting the steel, mainly at least one of Cr and Mo; hereinafter, referred to as “M 23 C 6 carbide”).
  • M represents the metallic elements constituting the steel, mainly at least one of Cr and Mo; hereinafter, referred to as “M 23 C 6 carbide”.
  • the present inventors have obtained findings that adopting a steel having the above-described appropriate component composition and eliminating the M 23 C 6 carbides from the steel structure can obtain an impact and wear resistant component improved in breakage resistance and excellent in durability.
  • the steel having the above-described appropriate component composition is adopted as the steel constituting the impact and wear resistant component, and no M 23 C 6 carbides are included in the steel structure.
  • the impact and wear resistant component of the present application is thus an impact and wear resistant component excellent in durability.
  • the state where the steel includes no M 23 C 6 carbides means a state where M 23 C 6 carbides are not found when the cross section of the impact and wear resistant component is observed using a field-emission scanning electron microscope (FE-SEM) and an area of 80 ⁇ m 2 including the grain boundary of the steel is examined for 10 or more fields of view.
  • the M 23 C 6 carbide can be identified, when a possible product of M 23 C 6 carbide is found for example in the above-described manner, by detecting the product in a bright-field image of a scanning transmission electron microscope (STEM) and then confirming the selected area diffraction (SAD) pattern of the product.
  • STEM scanning transmission electron microscope
  • the matrix may have a grain size number of 5 or more and 8 or less. With this configuration, excellent toughness can readily be imparted to the impact and wear resistant component.
  • the martensite phase constituting the matrix may be a low temperature-tempered martensite phase. With this configuration, excellent toughness can readily be imparted to the impact and wear resistant component.
  • the low temperature-tempered martensite phase means a phase made up of a structure (obtained through low temperature tempering) which is obtained when a steel that has been quenched is tempered at a temperature not lower than 150° C. and not higher than 250° C.
  • the phase being the low temperature-tempered martensite phase can be confirmed through investigation of the hardness, carbide precipitation state, etc. of the phase.
  • a method for producing an impact and wear resistant component of the present application includes the steps of: preparing a steel material made of a steel containing not less than 0.41 mass % and not more than 0.44 mass % C, not less than 0.2 mass % and not more than 0.5 mass % Si, not less than 0.2 mass % and not more than 1.5 mass % Mn, not less than 0.0005 mass % and not more than 0.0050 mass % S, not less than 0.6 mass % and not more than 2.0 mass % Ni, not less than 0.7 mass % and not more than 1.5 mass % Cr, not less than 0.1 mass % and not more than 0.6 mass % Mo, not less than 0.02 mass % and not more than 0.03 mass % Nb, not less than 0.01 mass % and not more than 0.04 mass % Ti, not less than 0.0005 mass % and not more than 0.0030 mass % B, and not less than 20 mass ppm and not more than 60 mass ppm N, with the balance consisting of iron and un
  • the steel may further contain at least one species selected from the group consisting of not less than 0.05 mass % and not more than 0.20 mass % V, not less than 0.01 mass % and not more than 0.15 mass % Zr, and not less than 0.1 mass % and not more than 2.0 mass % Co.
  • the steel material is hot forged or hot rolled to obtain a formed body.
  • M 23 C 6 carbides are generated at the grain boundaries of the steel.
  • normalizing treatment is performed on the entirety of the formed body in which the formed body is cooled from a temperature not lower than 945° C. and not higher than 1000° C. to a temperature not higher than the temperature corresponding to the M s point of the steel. With the normalizing treatment of heating to a temperature range of not lower than 945° C.
  • FIG. 1 is a schematic view showing the structure of a ripper device including a ripper shank and a ripper point.
  • FIG. 2 is an exploded perspective view of the ripper shank and the ripper point.
  • FIG. 3 is a schematic cross-sectional view showing the structure of the ripper shank.
  • the ripper device 1 of the present embodiment is, for example, a ripper device attached to a bulldozer.
  • the ripper device 1 is attached to the rear (opposite the side on which a blade (soil removal plate) is disposed) of the vehicle body of the bulldozer.
  • the ripper device 1 includes an arm 31 , a lift cylinder 32 , a tilt cylinder 33 , a ripper support member 34 , a ripper shank 10 , and a ripper point 20 .
  • the arm 31 has a rod shape.
  • the arm 31 has one end connected to a bracket (not shown) mounted on the vehicle body of the bulldozer, and the other end connected to the ripper support member 34 .
  • the ripper support member 34 is pivotably connected to the other end of the arm 31 .
  • the lift cylinder 32 and the tilt cylinder 33 have their one ends connected to the bracket (not shown) mounted on the vehicle body of the bulldozer.
  • the lift cylinder 32 and the tilt cylinder 33 have their other ends connected to the ripper support member 34 .
  • the lift cylinder 32 and the tilt cylinder 33 are hydraulic cylinders that can be extended and contracted in the longitudinal direction.
  • the ripper support member 34 is pivotably connected to the other ends of the lift cylinder 32 and the tilt cylinder 33 . Of the ripper support member 34 , the region connected to the lift cylinder 32 is located between the region connected to the arm 31 and the region connected to the tilt cylinder 33 .
  • the ripper shank 10 is made of steel.
  • the ripper shank 10 includes a distal end 15 as one end and a proximal end 14 as the other end in the longitudinal direction.
  • the region including the distal end of the ripper shank 10 is bent toward the side approaching the vehicle body of the bulldozer.
  • the region of the ripper shank 10 between its distal end 15 and proximal end 14 is supported by the ripper support member 34 .
  • the ripper point 20 is attached to the distal end 15 of the ripper shank 10 .
  • the region connected to the arm 31 is positioned closer to the ripper point 20 as compared to the region connected to the tilt cylinder 33 and the region connected to the lift cylinder 32 .
  • the extension and contraction of the lift cylinder 32 cause the ripper shank 10 to move up and down.
  • the extension and contraction of the tilt cylinder 33 cause the ripper shank 10 to tilt.
  • the ripper shank 10 has a through hole, a ripper shank through hole 11 , formed therein.
  • the ripper point 20 has a through hole, a ripper point through hole 25 , formed therein.
  • the ripper point through hole 25 and the ripper shank through hole 11 form a continuous through hole.
  • a pin 51 inserted into the continuous through hole secures the ripper point 20 to the ripper shank 10.
  • the ripper point 20 has a recess 22 formed to recess from its proximal end 23 side toward its distal end 21 side.
  • the ripper shank 10 includes a body portion 12 including its proximal end 14 and an insert portion 13 including its distal end 15 on the side to be inserted into the recess 22 .
  • the recess 22 formed in the ripper point 20 has its bottom region 22 A not in contact with the distal end 15 of the ripper shank 10 . There is a space 29 between the bottom region 22 A of the recess 22 and the distal end 15 .
  • the ripper shank 10 as the impact and wear resistant component is made of a steel containing not less than 0.41 mass % and not more than 0.44 mass % C, not less than 0.2 mass % and not more than 0.5 mass % Si, not less than 0.2 mass % and not more than 1.5 mass % Mn, not less than 0.0005 mass % and not more than 0.0050 mass % S, not less than 0.6 mass % and not more than 2.0 mass % Ni, not less than 0.7 mass % and not more than 1.5 mass % Cr, not less than 0.1 mass % and not more than 0.6 mass % Mo, not less than 0.02 mass % and not more than 0.03 mass % Nb, not less than 0.01 mass % and not more than 0.04 mass % Ti, not less than 0.0005 mass % and not more than 0.0030 mass % B, and not less than 20 mass ppm and not more than 60 mass ppm N, with the balance consisting of iron and
  • the steel includes a matrix including a martensite phase and a residual austenite phase, and first nonmetallic particles dispersed in the matrix and including at least one species selected from the group consisting of MnS, TiCN, and NbCN.
  • the steel does not include a carbide represented as M 23 C 6 (where M represents the metallic elements constituting the steel).
  • the amount of the residual austenite included in the matrix is 10 vol % or less, for example, and preferably 5 vol % or less.
  • the steel constituting the ripper shank 10 may further contain at least one species selected from the group consisting of not less than 0.05 mass % and not more than 0.20 mass % V, not less than 0.01 mass % and not more than 0.15 mass % Zr, and not less than 0.1 mass % and not more than 2.0 mass % Co.
  • the ripper shank 10 as the impact and wear resistant component of the present embodiment adopts the steel having the above-described appropriate component composition as the material, and the steel structure does not include M 23 C 6 carbides. Accordingly, the ripper shank 10 as the impact and wear resistant component of the present embodiment is an impact and wear resistant component excellent in durability.
  • the matrix of the steel constituting the ripper shank 10 preferably has the grain size number (ASTM) of 5 or more and 8 or less. This facilitates imparting excellent toughness to the ripper shank 10 .
  • the martensite phase constituting the matrix of the steel is preferably a low temperature-tempered martensite phase. This facilitates imparting excellent toughness to the ripper shank 10 .
  • a steel material preparing step is performed as a step S 10 .
  • a steel material made of the steel having the above-described appropriate component composition is prepared.
  • a hot working step is performed as a step S 20 .
  • the steel material prepared in the step S 10 is subjected to hot forging or hot rolling and forming processing. With this, a formed body having an approximate shape of the ripper shank 10 is obtained.
  • Hot forging or hot rolling is performed by, for example, heating the steel material prepared in the step S 10 to a temperature not lower than 1200° C., such as 1250° C. In the cooling process following the hot forging or hot rolling, M 23 C 6 carbides are formed at the grain boundaries of the steel.
  • a normalizing step is performed as a step S 30 .
  • the formed body obtained in the step S 20 is subjected to normalizing treatment. Specifically, the formed body is firstly heated to a temperature range of not lower than 945° C. and not higher than 1000° C., and then cooled from the temperature range to a temperature not higher than the temperature corresponding to the M s point of the steel. In this manner, the entirety of the formed body is normalized. Performing the normalizing treatment of heating to the temperature range of 945° C. or higher and 1000° C. or lower and then cooling causes the M 23 C 6 carbides generated in the step S 20 to dissolve into the matrix of the steel and disappear.
  • a hardening treatment step is performed as a step S 40 .
  • the formed body having undergone the normalizing treatment in the step S 30 is firstly heated to a temperature range of 840° C. or higher and 920° C. or lower, for example, and then cooled from the temperature range to a temperature not higher than the M s point of the steel. In this manner, the entirety of the formed body is quench hardened.
  • the cooling to the temperature not higher than the M s point of the steel can be performed, for example, by water cooling or oil cooling adopting water or oil as a cooling medium. The water cooling or oil cooling is continued until, for example, the surface temperature of the formed body becomes a temperature not lower than 50° C. and not higher than 100° C.
  • the formed body is heated to a temperature range of not lower than 150° C. and not higher than 250° C. and then cooled to a room temperature (low temperature tempering). With this, the hardness of the steel constituting the formed body is adjusted to a range of HRC 53 or more and HRC 57 or less.
  • a finishing step is performed as a step S 50 as required.
  • the formed body obtained through the steps S 10 to S 40 is subjected to any necessary finishing or other treatment.
  • the ripper shank 10 in the present embodiment can be produced through the above-described process.
  • the obtained ripper shank 10 is combined with a separately prepared ripper point 20 , to obtain a ripper device 1 .
  • the M 23 C 6 carbides, generated along the grain boundaries of the steel during hot forging or hot rolling and forming the steel material made of the steel having the above-described appropriate component composition are made to disappear by the normalizing treatment in the step S 30 , before the hardening treatment in the step S 40 .
  • the ripper shank 10 as the impact and wear resistant component excellent in durability can be produced.
  • Samples corresponding to the impact and wear resistant component of the present application were prepared using four types of steel materials, including one made of a steel having the above-described appropriate component composition, and experiments for evaluating their properties were conducted.
  • the experimental procedures were as follows.
  • Table 1 shows chemical compositions of the steels used in the experiments. The values in Table 1 are in mass %.
  • the steel material A has a component composition corresponding to the steel constituting the impact and wear resistant component of the present invention (Inventive Example).
  • the steel materials B, C, and D have component compositions falling outside the scope of the present invention (Comparative Examples).
  • the steel materials B, C, and D correspond to SCrB430H, JIS standard SNCM431H, and the steel disclosed in the aforementioned Patent Literature 1, respectively.
  • the steel materials in Table 1 were used to prepare samples through a process similar to the steps S 10 to S 40 in the above embodiment. From the obtained samples, tensile test specimens and Charpy impact test specimens (2 mm U-notch) were produced, and a tensile test, an impact test, and a Rockwell hardness measurement were conducted.
  • the Inventive Example when comparing the Inventive Example with the Comparative Examples, the Inventive Example has achieved high values for the 0.2% proof stress, tensile strength, and impact value, while maintaining the reduction of area comparable to those of the Comparative Examples. Further, for the steel material A as the Inventive Example, as compared to the steel material D, the tensile strength has improved considerably despite their comparable 0.2% proof stress. The above demonstrates that the impact and wear resistant component of the present application is excellent in durability.
  • the steel material A in Table 1 (the steel material corresponding to the example of the present invention) was used to prepare a sample of a ripper shank in a similar procedure as in the above embodiment.
  • a test specimen was taken from the sample.
  • the surface of the obtained test specimen was polished and then etched with a nitric acid alcohol solution, and a microstructure was observed using an optical microscope.
  • FIG. 5 shows optical micrographs showing the microstructure of the steel.
  • the matrix includes a low temperature-tempered martensite phase.
  • the presence of some residual austenite (of 10 vol % or less) is acceptable.
  • the amount of residual austenite was measured using an X ray, and it was found that the residual austenite of 1 vol % to 3 vol % was present. The above demonstrates that the matrix of the steel includes the martensite phase and the residual austenite phase.
  • FIG. 6 shows photographs indicating the results of analysis by energy dispersive X-ray spectroscopy (EDX) of products that were found through observation of the steel structure with SEM.
  • EDX energy dispersive X-ray spectroscopy
  • the steel material A (the steel material corresponding to the example of the present invention) in Table 1 was used to prepare a test specimen (as quenched; sample A) by performing the process of the above embodiment up to the step S 20 (with the forging temperature of 1250° C.), not performing the step S 30 , and performing quenching treatment in the step S 40 after heating the material to 870° C.
  • a test specimen (as quenched; sample B) was also prepared, by similarly performing the process up to the step S 20 , performing normalizing treatment in the step S 30 by heating the material to 970° C., and further performing quenching treatment in the step S 40 after heating the material to 870° C.
  • the microstructures were observed with an optical microscope and SEM, and for products present along the grain boundaries, elemental mapping was conducted with EDX. The experimental results are shown in FIG. 7 .
  • FIG. 8 An example of the identification of carbides present in the sample A is shown in FIG. 8 , in which a carbide was detected in a bright-field image of STEM and then the selected area diffraction (SAD) pattern of the carbide was confirmed.
  • SAD selected area diffraction
  • the steel material A in Table 1 was used to prepare test specimens which were quench hardened by rapid cooling from various temperatures and then tempered at high temperature.
  • the test specimens were subjected to a tensile test. At this time, the heating temperature upon quenching was varied to investigate the effect of the heating temperature on the reduction of area in the tensile test.
  • the experimental results are shown in FIG. 9 .
  • the impact and wear resistant component of the present application is applicable to a variety of impact and wear resistant components made of a steel having a hardness of HRC 53 or more and HRC 57 or less, such as bucket teeth, bucket adapters, bucket shrouds, ripper points, protectors, cutting edges, end bits, crusher teeth, sprocket teeth, springs, shoe plates, shoe bolts, and the like.
  • ripper device 10 : ripper shank; 11 : ripper shank through hole; 12 : body portion; 13 : insert portion; 14 : proximal end; 15 : distal end; 20 : ripper point; 21 : distal end; 22 : recess; 22 A: bottom region; 23 : proximal end; 25 : ripper point through hole; 29 : space; 31 : arm; 32 : lift cylinder; 33 : tilt cylinder; 34 : ripper support member; and 51 : pin.

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