EP2154262B1 - Abriebfestes stahlblech mit hervorragender verarbeitbarkeit und herstellungsverfahren dafür - Google Patents

Abriebfestes stahlblech mit hervorragender verarbeitbarkeit und herstellungsverfahren dafür Download PDF

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EP2154262B1
EP2154262B1 EP08764952.1A EP08764952A EP2154262B1 EP 2154262 B1 EP2154262 B1 EP 2154262B1 EP 08764952 A EP08764952 A EP 08764952A EP 2154262 B1 EP2154262 B1 EP 2154262B1
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steel
abrasion
abrasion resistant
test
phase
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French (fr)
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EP2154262A4 (de
EP2154262A1 (de
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Yasuhiro Murota
Misao Ishikawa
Yoshinori Watanabe
Shinichi Suzuki
Nobuo Shikanai
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JFE Steel Corp
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JFE 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
    • 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
    • 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
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys 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
    • 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
    • C22C38/14—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
    • C22C38/18—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
    • 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
    • C21D1/06—Surface hardening
    • 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
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

Definitions

  • the present invention relates to an abrasion resistant steel suitable for members, which have issues in wear or abrasion resulting from contact with earth and sand, of industrial machines and transporting machines, e.g., power shovels, bulldozers, hoppers, and buckets, used in the fields of construction, civil engineering, mining, and the like and a production method thereof.
  • industrial machines and transporting machines e.g., power shovels, bulldozers, hoppers, and buckets, used in the fields of construction, civil engineering, mining, and the like and a production method thereof.
  • an abrasion resistant steel excellent in bending formability e.g., power shovels, bulldozers, hoppers, and buckets
  • Steels having an excellent abrasion resistant property are used for members which are worn and abraded by earth and sand, in order to obtain its prolonged service life. It is known that the abrasion resistant property of the steel is improved by increasing hardness. Therefore, steels having a hardness increased by subjecting the steel containing large amounts of alloy elements, e.g., Cr and Mo, to a heat treatment, e.g., quenching, has been used for a member required to have the abrasion resistant property.
  • alloy elements e.g., Cr and Mo
  • Japanese Unexamined Patent Application Publication No. 62-142726 proposes a method for producing an abrasion resistant steel plate, wherein a steel containing 0.10% to 0.19% of C and appropriate amounts of Si and Mn and having Ceq limited to 0.35% to 0.44% is hot rolled and, thereafter, is quenched directly or is reheated to 900°C to 950°C and quenched, followed by tempering at 300°C to 500°C so as to have a steel surface hardness of 300 HV (Vickers hardness) or more.
  • HV Vander hardness
  • Japanese Unexamined Patent Application Publication No. 63-169359 proposes a method for producing an abrasion resistant thick steel plate, wherein a steel containing 0.10% to 0.20% of C and appropriately adjusted amounts of Si, Mn, P, S, N, and Al, or further containing at least one element of Cu, Ni, Cr, Mo, and B is hot rolled, followed directly by quenching or above steel is hot rolled, cooled through standing, reheated, and quenched, so as to be provided with a hardness of 340 HB (Brinell hardness) or more.
  • a steel containing 0.10% to 0.20% of C and appropriately adjusted amounts of Si, Mn, P, S, N, and Al, or further containing at least one element of Cu, Ni, Cr, Mo, and B is hot rolled, followed directly by quenching or above steel is hot rolled, cooled through standing, reheated, and quenched, so as to be provided with a hardness of 340 HB (Brinell hard
  • Japanese Unexamined Patent Application Publication No. 1-142023 proposes a method for producing an abrasion resistant steel, wherein a steel containing 0.07% to 0.17% of C and appropriately adjusted amounts of Si, Mn, P, S, N, and Al, or further containing at least one element of Cu, Ni, Cr, Mo, and B is hot rolled, followed directly by quenching or above steel is hot rolled, air cooled to the room temperature, reheated, and quenched, so as to produce a steel having a surface hardness of 321 HB or more and exhibiting excellent bending formability.
  • the hardness is increased taking advantage of solid solution hardening, transformation hardening, precipitation hardening, and the like by addition of large amounts of alloy elements and, thereby, the abrasion resistant characteristic is improved.
  • the hardness is increased taking advantage of solid solution hardening, transformation hardening, precipitation hardening, and the like by addition of large amounts of alloy elements, the weldability and the formability deteriorate and, furthermore, the production cost increases.
  • the member required to have the abrasion resistant property in some cases, merely an increase in hardness of only a surface and the vicinity of surface to improve the abrasion resistant property is good enough depending on the use condition.
  • the steel used in such a case it is believed that addition of large amounts of alloy elements, e.g., Cr, Mo, and the like is not necessary, but a heat treatment, e.g., quenching, is conducted so as to allow only a surface and the vicinity of surface to have a hardened structure.
  • an increase in the amount of solid solution C in the steel is required to increase the hardness of the hardened structure.
  • the increase in the amount of solid solution C causes deterioration of the weldability, deterioration of the bending formability, and the like.
  • the deterioration of the bending formability limits the bending which is required of the member and, therefore, the use condition is limited.
  • Japanese Patent No. 3089882 proposes an abrasion resistant steel containing 0.10% to 0.45% of C, appropriately adjusted amounts of Si, Mn, P, S, and N, and 0.10% to 1.0% of Ti, including 400 particles/mm 2 or more of TiC precipitates or complex precipitates of TiC and TiN or TiS, which have an average particle diameter of 0.5 ⁇ m or more, having 0.05% or more, and less than 0.4% of Ti*, and exhibiting improved surface properties.
  • Japanese Unexamined Patent Application Publication No. 4-41616 proposes a method for producing an abrasion resistant steel, wherein 0.05% to 0.45% of C, 0.1% to 1.0% of Si, 0.1% to 1.0% of Mn, and 0.05% to 1.5% of Ti are contained and the bending formability is improved by specifying a surface hardness to be 401 or less on a Brinell hardness basis.
  • the surface hardness is specified to be 401 or less on a Brinell hardness basis in order to ensure the bending formability.
  • the tensile strength exceeds 780 MPa. Therefore, satisfactory bending formability is not achieved from the viewpoint of reduction in a load during forming.
  • an object of the present invention to provide an abrasion resistant steel which can be produced by hot rolling without conducting a heat treatment and which is excellent in abrasion resistant property and bending formability, as well as a production method thereof.
  • the inventors of the present invention conducted intensive research on various factors having influences on the abrasion resistant property and the bending formability. As a result, it was found that a forming load in the bending was able to be reduced, i.e. the bending formability was able to be improved, while the abrasion resistant property was ensured, by including a chemical composition containing Ti and C, allowing a microstructure of base metal to include a complex structure of a ferrite and pearlite structure, which remained unchanged after rolling, as a base phase, and dispersing a second phase (hard phase: Ti based carbide) in a matrix.
  • a chemical composition containing Ti and C allowing a microstructure of base metal to include a complex structure of a ferrite and pearlite structure, which remained unchanged after rolling, as a base phase, and dispersing a second phase (hard phase: Ti based carbide) in a matrix.
  • the present invention has been made on the basis of the obtained findings and additional research. That is, the present invention relates to the followings.
  • the above-described hard phase is specified to be a Ti based carbide, e.g., TiC.
  • TiC a Ti based carbide
  • examples thereof can include TiC, (NbTi)C, (VTi)C, and a TiC which Mo and/or W is dissolved in.
  • the abrasion resistant steel exhibiting the bending formability improved without impairing the abrasion resistant property can be obtained without conducting a heat treatment after hot rolling. Therefore, rational production, e.g., a reduction in heat treatment cost and a reduction in production time, can be conducted, so that remarkable industrial effects are exerted.
  • An element C is effective for increasing the hardness of the matrix in the microstructure of base metal so as to improve the abrasion resistant property, as well as for forming Ti carbide serving as a hard second phase (hereafter may be referred to as a hard phase) so as to improve the abrasion resistant property.
  • a hard phase Ti carbide serving as a hard second phase
  • C is specified to be within the range of 0.05% to 0.35%.
  • C is 0.15% to 0.32%.
  • Ti and C are important in the present invention, and Ti is an indispensable element which forms Ti carbide serving as a hard phase contributing to improvement of the abrasion resistant property. In order to obtain such effects, it is necessary that the content is 0.1% or more.
  • Fig. 1 shows an effect of the amount of addition of Ti on the abrasion resistant property.
  • Fig. 2 shows an effect of the amount of addition of Ti on the tensile properties (yield strength: YS, tensile strength: TS).
  • the vertical axis indicates the abrasion resistance ratio, where the amount of abrasion in a rubber wheel abrasion test is compared with the abrasion weight loss of a mild steel (SS400) .
  • the amount of addition of Ti is 0.1% or more, characteristics in which the abrasion resistant property is higher than or equal to that of a common abrasion resistant steel are obtained and TS is reduced to 800 MPa or less. That is, the formability can be improved while the abrasion characteristics equal to the known abrasion resistant steel, which has been subjected to a quenching heat treatment, is maintained.
  • the test steel in the rubber wheel abrasion test was produced by rolling a steel slab containing 0.33%C-0.35%Si-0.82%Mn-0.05% to 1.2%Ti to 19 mmt and, thereafter, conducting air-cooling at a cooling rate of 0.5°C/s.
  • the resulting steel was subjected to tensile tests and abrasion tests.
  • a JIS No. 5 test piece was taken on the basis of the stipulation of JIS Z2201, and the tensile test was conducted so as to determine the tensile properties (yield strength: YS, tensile strength: TS).
  • the rubber wheel abrasion test was conducted on the basis of ASTM G65, and the test results were organized in terms of the abrasion resistance ratio that is the ratio of the amount of abrasion weight loss of the mild steel (SS400) to the amount of abrasion weight loss of each test steel.
  • the larger abrasion resistance ratio corresponds to better abrasion characteristics.
  • the common abrasion resistant steel refers to a steel which is a material produced by hot rolling a steel having a composition of 0.15 mass%C-0.35 mass%Si-1.50 mass%Mn-0.13 mass%Cr-0.13 mass%Mo-0.01 mass%Ti-0.0010 mass%B, conducting reheating to 900°C and, thereafter, conducting a quenching heat treatment, and which has a Brinell hardness of about 400 HB.
  • Ti is limited within the range of 0.1% to 1.2%, and preferably 0.1% to 0.8%.
  • Si is effective as a deoxidizing element. In order to obtain such an effect, it is necessary that the content is 0.05% or more. Furthermore, Si is an element which forms a solid solution in a steel so as to contribute to an increase in hardness because of solid solution strengthening. However, if the content exceeds 1.0%, problems occur in that, for example, the ductility and the toughness deteriorate and the inclusion content increases. Therefore, preferably, Si is limited within the range of 0.05% to 1.0%. More preferably, Si is 0.05% to 0.40%.
  • Mn contributes to an increase in hardness because of solid solution strengthening. In order to obtain such an effect, it is necessary that the content is 0.1% or more. On the other hand, if the content exceeds 2.0%, the weldability deteriorates. Therefore, preferably, Mn is limited within the range of 0.1% to 2.0%. More preferably, Mn is 0.1% to 1.60%.
  • An element Al acts as a deoxidizing element. Such an effect is observed if the content is 0.0020% or more. However, a large content exceeding 0.1% allows the cleanness of the steel to deteriorate. Therefore, preferably, Al is limited to 0.1% or less.
  • An element Cu improve the hardenability because of solid solution. In order to obtain this effect, it is necessary that the content is 0.1% or more. On the other hand, if the content exceeds 1.0%, the hot formability deteriorates. Therefore, preferably, Cu is limited within the range of 0.1% to 1.0%. More preferably, Cu is 0.1% to 0.5%.
  • Ni improve the hardenability because of solid solution. Such an effect becomes remarkable if the content is 0.1% or more. On the other hand, if the content exceeds 2.0%, the material cost increases significantly. Therefore, preferably, Ni is limited within the range of 0.1% to 2.0%. More preferably, Ni is 0.1% to 1.0%.
  • An element Cr exerts an effect of improving the hardenability. In order to obtain such an effect, it is necessary that the content is 0.1% or more. However, if the content exceeds 1.0%, the weldability deteriorates. Therefore, preferably, Cr is limited within the range of 0.1% to 1.0%. More preferably, Cr is 0.1% to 0.8%. Further preferably, Cr is 0.4% to 0.7%.
  • Mo improves the hardenability. In order to obtain such an effect, it is necessary that the content is 0.05% or more. On the other hand, if the content exceeds 1.0%, the weldability deteriorates. Therefore, Mo is limited within the range of 0.05% to 1.0%. Preferably Mo is 0.05% to 0.40%.
  • An element W improves the hardenability. In order to obtain such an effect, it is necessary that the content is 0.05% or more. On the other hand, if the content exceeds 1.0%, the weldability deteriorates. Therefore, preferably, W is limited within the range of 0.05% to 1.0%. More preferably, W is 0.05% to 0.40%. Since Mo and W form solid solutions in TiC, an effect of increasing the amount of hard phase is also exerted.
  • An element B segregates at grain boundaries, strengthen grain boundaries, and contributes to improvement of the toughness effectively. In order to obtain such effects, it is necessary that the content is 0.0003% or more. On the other hand, if the content exceeds 0.0030%, the weldability deteriorates. Therefore, preferably, B is limited within the range of 0.0003% to 0.0030%. More preferably, B is 0.0003% to 0.0015%.
  • DI* hardenability index
  • Fig. 3 shows an effect of DI* on the abrasion resistant property.
  • Fig. 4 shows an effect of DI* on the tensile properties (yield strength: YS, tensile strength: TS).
  • the vertical axis indicates the abrasion resistance ratio, where the amount of abrasion in the rubber wheel abrasion test is compared with the amount of abrasion of the mild steel (SS400). The larger abrasion resistance ratio corresponds to better abrasion characteristics.
  • the amount of abrasion is at a level equal to that of a common abrasion resistant steel regardless of low strength, that is, TS is 800 MPa or less.
  • DI* is 60 or more
  • excellent abrasion resistant property is exhibited, however, the tensile strength is 800 MPa or more and the formability is poor.
  • the reason is estimated that in the case where DI* is 60 or more, a ferrite and bainite structure results.
  • the test steel in the rubber wheel abrasion test was produced by rolling a steel slab containing 0.34%C-0.22%Si-0.55%Mn-0.22%Ti on a percent by mass basis and at least one element of Cu, Ni, Cr, Mo, and W, where DI* is 40 to 120, to 8 mmt and, thereafter, conducting air-cooling (cooling rate: 1.2°C/s) .
  • the resulting steel was subjected to tensile tests and abrasion tests.
  • a JIS No. 5 test piece was taken on the basis of the stipulation of JIS Z2201, and the tensile test was conducted so as to determine the tensile properties (yield strength: YS, tensile strength: TS).
  • the rubber wheel abrasion test was conducted on the basis of ASTM G65, and the test results were organized in terms of the abrasion resistance ratio that is the ratio of the amount of abrasion of the mild steel (SS400) to the amount of abrasion of each test steel.
  • Nb and V which are elements contributing to the abrasion resistant property, can be included as selective elements in order to further improve the abrasion resistant property.
  • Nb is added in combination with Ti, forms a complex carbide ((NbTi)C) of Ti and Nb, and disperses as a hard second phase, so as to contribute to an improvement of the abrasion resistant property effectively.
  • the content is 0.005% or more.
  • the hard second phase complex carbide of Ti and Nb
  • the hard second phase complex carbide of Ti and Nb
  • Nb is limited within the range of 0.005% to 1.0%. More preferably, Nb is 0.1% to 0.5%.
  • V 0.005% to 1.0%
  • an element V is added in combination with Ti, forms a complex carbide ((VTi)C) of Ti and V, and disperses as a hard second phase, so as to contribute to an improvement of the abrasion resistant property effectively.
  • the content is 0.005% or more.
  • V is limited within the range of 0.005% to 1.0%. More preferably, V is 0.1% to 0.5%.
  • Nb and V are added in combination, the same effect of improving the abrasion resistant property is exerted merely except that the hard second phase becomes (NbVTi)C.
  • a carbonitride may be formed in addition to a carbide, but the same effect is obtained.
  • the amount of addition of N exceeds 0.01%, the proportion of N in the carbonitride increases, the hardness of the hard second phase decreases, and deterioration of the abrasion resistant property is concerned. Therefore, it is preferable that the amount of addition of N is specified to be 0.01% or less.
  • a microstructure of base metal is specified to be a microstructure in which a base phase is a ferrite and pearlite structure, and a hard phase (hard second phase) is dispersed in the base phase.
  • the base phase means that the volume fraction thereof is 90% or more.
  • two phases, i.e. ferrite and pearlite, constitute 90% or more of the whole.
  • the volume fraction of the ferrite phase is 70% or more, among them, and the ferrite phase has an average particle diameter of 20 ⁇ m in terms of an equivalent circle diameter.
  • the base phase has a Brinell hardness of 300 HB or less in consideration of the formability.
  • the hard phase is a Ti based carbide, e.g., TiC.
  • TiC Ti based carbide
  • examples thereof can include TiC, (NbTi)C, (VTi)C, and TiC which Mo and/or W is dissolved in.
  • the size of the hard phase is not specifically limited. However, from the viewpoint of the abrasion resistant property, about 0.5 ⁇ m or more, and 50 ⁇ m or less is preferable. Furthermore, it is preferable that the dispersion density of the hard phase is 400 particles/mm 2 or more from the viewpoint of the abrasion resistant property.
  • the area of each hard phase is measured, an equivalent circle diameter is calculated from the area, the resulting equivalent circle diameters are arithmetically averaged, and the average value is assumed to be the size (average particle diameter) of the hard phase in the steel.
  • a molten steel having the above-described composition is melted by a known melting method and steel materials, e.g., a slab, having a predetermined dimension is produced by a continuous casting method or an ingot making-blooming method.
  • the cooling is adjusted in such a way that the cooling rate of a cast slab having a thickness of 200 to 400 mm in a temperature range of 1,500°C to 1,200°C becomes 0.2°C/s to 10°C/s.
  • the steel material (cast slab or ingot) is hot rolled immediately without cooling or the above material is cooled, reheated to 950°C to 1,250°C, and hot rolled, so as to produce a steel having a predetermined sheet thickness. After the hot rolling, cooling is conducted at an average cooling rate of 2°C/s or less without a heat treatment.
  • the cooling rate exceeds 2°C/s, the ferrite and pearlite structure is not obtained, the tensile strength becomes 800 MPa or more, the forming load in the steel bending increases, and the formability deteriorates. Therefore, the cooling rate is specified to be 2°C/s or less.
  • the hot rolling condition is not specifically limited, insofar as the steel having predetermined size and shape can be produced. However, in consideration of the toughness which is a performance necessary to the steel, it is necessary that the rolling reduction rate at a steel surface temperature of 920°C or lower is specified to be 30% or more and the rolling finishing temperature is specified to be 900°C or lower.
  • the abrasion resistant steel according to the present invention can be used for various purposes in which bending is required to the hot-rolled steel with no need to conduct a heat treatment after the hot rolling.
  • a molten steel having the composition shown in Table 1 was melted in a vacuum melting furnace so as to produce a small steel ingot (50 kg) (steel material). Thereafter, heating to 1,050°C to 1,250°C and hot rolling were conducted so that a test steel having a sheet thickness of 6 to 100 mm was produced. Regarding each test steel, a microstructure observation, a tensile test, an abrasion test, a Charpy impact test, and a bend test were conducted.
  • a test piece for the microstructure observation was polished and etched with nital. Regarding the site at a position 1 mm under the surface layer, the microstructure was identified by using an optical microscope (magnification ratio: 400 times), and the ferrite grain diameter and the size and the number of the hard phase were measured. The microstructure constituting 90% or more of the observation field of view was assumed to be a base phase, and an average particle diameter determined by the above-described method was assumed to be the size of hard phase.
  • a JIS No. 5 test piece was taken on the basis of the stipulation of JIS Z2201, and the tensile test was conducted on the basis of the stipulation of JIS Z2241, so as to determine the tensile properties (yield strength: YS, tensile strength: TS).
  • the present invention is specified to be within the range of a tensile strength (TS) of less than 800 MPa and a yield strength (YS) of less than 600 MPa.
  • test piece was t (sheet thickness) ⁇ 20 ⁇ 75 (mm) and the rubber wheel abrasion test was conducted by using abrasion sand on the basis of the stipulation of ASTM G65. After the test, the amount of abrasion of the test piece was measured.
  • the larger abrasion resistance ratio corresponds to better abrasion property.
  • the range of the present invention is specified to be an abrasion resistance ratio of 4.0 or more.
  • a V notch impact test piece was taken from the position at 1/4 in the plate thickness direction toward an L direction on the basis of the stipulation of JIS Z2202.
  • the Charpy impact test was conducted at a test temperature of 0°C on the basis of the stipulation of JIS Z2242, so as to determine Charpy absorbed energy.
  • the number of test pieces was three, and an average value was determined.
  • Test pieces were taken on the basis of the stipulation of JIS Z2204.
  • the width was 50 mm and in the case where the plate thickness of the test steel was 45 mm or more, the thickness was reduced to 25 mm by cutting from one surface side. In the case where the plate thickness of the test steel was less than 45 mm, the plate thickness was not changed.
  • the bend test was conducted on the basis of the stipulation of JIS Z2248. The bend test was conducted by a pressing bend method at a pressing bend radius r of 1.5t.
  • Table 2 shows the results of the microstructure observation, the tensile test, and the abrasion test.
  • Invention examples (Steel Nos. 1 to 6 and Steel Nos. 8 and 9) are steels having a very excellent abrasion resistant property in spite of the tensile strength (TS) ⁇ 800 MPa and the yield strength (YS) ⁇ 600 MPa.
  • Comparative examples are inferior in the abrasion resistant property to Invention examples, or inferior in the bending formability because YS and TS are high even if the abrasion resistant property is at an equal level.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
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  • Metallurgy (AREA)
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  • Heat Treatment Of Steel (AREA)
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Claims (5)

  1. Abriebfester Stahl, bestehend aus, basierend auf Massenprozent, 0,05 % bis 0,35 % C, 0,05 % bis 1,0 % Si, 0,1 % bis 2,0 % Mn, 0,1 % bis 1,2 % Ti, 0,1 % oder weniger Al, 0,05 % bis 1,0 % Mo, mindestens einem Element aus 0,1 % bis 1,0 % Cu, 0,1 % bis 2,0 % Ni, 0,1 % bis 1,0 % Cr, 0,05 % bis 1,0 % W und 0,0003 % bis 0,0030 % B, und optional
    mindestens einem Element aus 0,005 % bis 1,0 % Nb und 0,005 % bis 1,0 % V auf Massenprozentbasis, und/oder
    nicht mehr als 0,015 % P, und/oder
    nicht mehr als 0,012 % S; und/oder 0,01 % oder weniger N,
    wobei der Rest Fe und zufällige Verunreinigungen sind;
    wobei DI*, repräsentiert durch die Formel (1), weniger als 60 ist. DI * = 33,85 × 0,1 × C * 0.5 × 0,7 × Si + 1 × 3,33 × Mn + 1 × 0,35 × Cu + 1 × 0,36 × Ni + 1 × 2,16 × Cr + 1 × 3 × Mo * + 1 × 1,5 × W * + 1
    Figure imgb0003
     wobei C* = C - 1/4 x (Ti - (48/14)N), Mo* = Mo x (1 - 0,5 x (Ti - (48/14)N), W* = W x (1 - 0,5 x (Ti - (48/14)N), und C, Si, Mn, Cu, Ni, Cr, Mo, W, Ti und N Inhalte repräsentieren (Massenprozent), und
    wobei das Stahlblech eine Zugfestigkeit < 800 MPa und eine Streckgrenze < 600 MPa aufweist.
  2. Abriebfester Stahl nach Anspruch 1, wobei eine Mikrostruktur eines Basismetalls eine Ferrit- und eine Perlitphase als eine Basisphase mit einem Volumenanteil von 90 % oder mehr aufweist, und eine Ti-basierte Carbid-Hartphase in der Basisphase verteilt ist.
  3. Abriebfester Stahl nach Anspruch 2, wobei die Verteilungsdichte der Hartphase 400 Partikel/mm2 oder mehr beträgt.
  4. Herstellungsverfahren für einen abriebfesten Stahl, wobei das Verfahren die Schritte zum Warmwalzen einer Stahlbramme mit der Zusammensetzung nach Anspruch 1 und das Durchführen von Abkühlen auf 400 °C oder weniger bei einer Abkühlungsgeschwindigkeit von 2 °C/s oder weniger nach dem Warmwalzen umfasst.
  5. Herstellungsverfahren für einen abriebfesten Stahl mit hervorragender Umformbarkeit nach Anspruch 4, wobei die Warmwalz-Reduzierungsrate bei 920 °C oder weniger auf 30 % oder mehr spezifiziert ist und die Fertigwalztemperatur auf 900 °C oder weniger spezifiziert ist.
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CA2685710C (en) 2012-07-31
EP2154262A1 (de) 2010-02-17
MX2009012820A (es) 2009-12-15
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