US20190226066A1 - Steel plate - Google Patents

Steel plate Download PDF

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US20190226066A1
US20190226066A1 US16/337,261 US201816337261A US2019226066A1 US 20190226066 A1 US20190226066 A1 US 20190226066A1 US 201816337261 A US201816337261 A US 201816337261A US 2019226066 A1 US2019226066 A1 US 2019226066A1
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hardness
steel plate
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steel
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Mitsuru Sawamura
Naoki Saitoh
Yasunori Takahashi
Takumi Miyake
Norimasa Kawabata
Takeshi Tsuzuki
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Nippon Steel Corp
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Nippon Steel and Sumitomo Metal Corp
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Assigned to NIPPON STEEL & SUMITOMO METAL CORPORATION reassignment NIPPON STEEL & SUMITOMO METAL CORPORATION ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: KAWABATA, NORIMASA, MIYAKE, Takumi, SAITOH, NAOKI, SAWAMURA, MITSURU, TAKAHASHI, YASUNORI, TSUZUKI, TAKESHI
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • 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
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    • 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
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    • 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
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    • 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
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    • C—CHEMISTRY; METALLURGY
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    • 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
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    • C21D2211/00—Microstructure comprising significant phases
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips

Definitions

  • the present invention relates to a steel plate (wear-resistant steel plate) having excellent wear resistance.
  • a wear-resistant steel plate that can be used over a long period of time is required even under a severe wear environment, and from the viewpoint of securing, a wear margin due to an increase in steel thickness, an improvement in wear resistance is required.
  • an improvement in wear resistance is required.
  • an object thereof is to secure not only the hardness in the vicinity of the surface of the steel plate (hereinafter, sometimes referred to as “hardness at a surface layer portion”, and a surface layer portion is a region of 1 mm to 5 mm from the surface of the steel plate in the through-thickness direction) but also the hardness in the center portion in the through-thickness direction (hereinafter, sometimes referred to as “hardness at a thickness center portion”, and the center portion is a region of ⁇ 5 mm (10 mm in total thickness) from a position (that is, the center of the steel thickness) away from the surface of the steel plate by 1 ⁇ 2 of the steel thickness T (that is, T/2) in the through-thickness direction) in which it is difficult to obtain hardness.
  • wear-resistant steel plates are locally exposed to a temperature higher than a room temperature and sometimes used under severe environments, there may be cases where the wear-resistant steel plates are required to have a small decrease in hardness (excellent high-temperature hardness) even in a temperature range higher than a room temperature (for example, a temperature range of about 150° C. to 300° C.).
  • Steel plates in which the Si content is increased to secure hardness in a temperature range higher than a room temperature hereinafter, sometimes referred to as “high-temperature hardness”.
  • Patent Document 1 Japanese Unexamined Patent Application, First Publication No. H8-41535
  • Patent Document 2 Japanese Unexamined Patent Application, First Publication. No. 2001-49387
  • Patent Document 3 Japanese Unexamined Patent Application, First Publication No. 2002-235144
  • Patent Document 1 proposes a steel plate having a Si content of 0.40 to 1.50 mass % (hereinafter, “mass %” is simply referred to as “%”) and containing Nb.
  • mass % is simply referred to as “%”
  • the steel thickness of the steel plate is 40 mm or less, the hardness at the thickness center portion thereof is not described, and there is no examination from the viewpoint of securing a wear margin due to an increase in the thickness of the steel plate.
  • Patent Document 2 a severe wear environment locally exposed to a temperature higher than a room temperature is postulated, and a steel which contains Si in an amount of more than 0.5% to 1.2% in order to secure the high-temperature hardness of the steel and uses precipitation strengthening caused by V carbide is proposed.
  • the steel containing a large amount of V is liable to cause cracking of cast pieces, and there is concern of a decrease in manufacturability.
  • Patent Document 3 proposes a steel plate containing 1.00%) to 1.50% of Si in order to secure the high-temperature hardness of the steel plate. In Patent Document 3, it is considered to secure the hardness at the thickness center portion of the steel plate. However, the difference between the hardness at the surface layer portion and the hardness at the thickness center portion (hereinafter, sometimes referred to as “hardness difference between the surface layer portion and the thickness center portion”, or simply “hardness difference”) is not described, and there is no examination from the viewpoint of securing a wear margin due to an increase in the thickness of the steel plate.
  • the inventors found that in a steel plate containing Si in an amount of more than 1.00%, there is a tendency toward a significant increase in the difference between the hardness at the surface layer portion and the hardness at the thickness center portion, which is not preferable regarding the wear resistance of the steel plate.
  • the present invention has been made taking the foregoing circumstances into consideration, and an object thereof is to provide a steel plate having excellent wear resistance, in which high hardness can be maintained even in a high-temperature environment as well as at a room temperature, the carbon equivalent of a steel plate particularly having a steel thickness of 40 mm or more is set to be less, than 0.800%, and the difference between a hardness at a surface layer portion and a hardness at a thickness center portion at a room temperature is set to 15.0% or less of the hardness at the surface layer portion.
  • Steels containing Si in an amount of more than 1.00% to 2.00% are advantageous in terms of wear resistance because hardness can be secured at a room temperature and high temperatures.
  • the influence of an increase in the Si content is not necessarily clear.
  • the inventors derives an index Q for reducing the difference between a hardness at a surface layer portion and a hardness at a thickness center portion at a room temperature in a steel plate having a steel thickness of 40 mm or more and containing Si in an amount of more than 1.00%.
  • the index Q is obtained by Equation (1) in which the hardenability of alloying elements and the steel thickness are considered.
  • Equation (1) since attention is paid to the alloying elements (C, Mn, Ni, Cr, and Mo) other than Si, which are necessary to reduce the difference between the hardness, at the surface layer portion and the hardness at the thickness center portion of the steel plate containing Si in an amount of more than 1.00%, the amount of Si is not considered.
  • the hardness at a room temperature is sometimes referred to as “a room-temperature hardness”.
  • a room-temperature hardness simply “hardness” represents hardness at a room temperature, and a room temperature represents 22 ⁇ 5° C. (17° C. to 27° C.).
  • the steel plate according to the present invention has a steel thickness of 40 mm or more and when the steel plate is affected by residual stress due to welding or the like, there is concern of delayed cracking due to hydrogen. Therefore, the carbon equivalent Ceq (%) obtained by Equation (2) is less than 0.800%.
  • the index Q obtained by Equation (1) By causing the index Q obtained by Equation (1) to be 0.00 or more, the hardness difference between the surface layer portion and the thickness center portion at a room temperature becomes 15.0% or less of the hardness at the surface layer portion, so that a steel plate having a small hardness difference, a low carbon equivalent, a steel thickness of 40 mm or more, and excellent, wear resistance can be obtained.
  • the unit of the index Q obtained by substituting dimensionless numerical values for the steel thickness T and the amount [X] of each element X in Equation (1) is dimensionless.
  • the unit of the carbon equivalent Ceq obtained by Equation (2) is “%”.
  • the index Q of Equation (1) is calculated by substituting the numerical value of the steel thickness T (mm), the numerical value of the amount [X] of each element X in terms of mass % and 0 in a case where the element X is not contained.
  • the carbon equivalent Ceq (%) of Equation (2) is calculated by substituting the numerical value of the amount [X] of each element X in terms of mass % and 0 in a case where the element X is not contained.
  • the present invention has been made based on the above findings, and the gist thereof is as follows.
  • a steel plate according to an aspect of the present invention includes, as a chemical composition, by mass %:
  • Si more than 1.00% to 2.00%
  • Mn 0.60% to 2.00%
  • Nb 0% to 0.05%
  • V 0 to 0.120%
  • Mg 0% to 0.050%
  • Equation (2) a carbon equivalent Ceq (%) obtained by Equation (2) is less than 0.800%;
  • a ratio of a difference between a hardness at a surface layer portion and a hardness at a thickness center portion to the hardness at the surface layer portion at a room temperature is 15.0% or less and the hardness at the surface layer portion at a room temperature is 400 or more in terms of Vickers hardness;
  • a steel thickness T is 40 mm or more.
  • the index Q of Equation (1) is calculated by substituting; a numerical value of the steel thickness (mm), a numerical value of an amount [X] of each element X in terms of mass % and 0 in a case where the element X is not contained
  • the carbon equivalent Ceq (%) of Equation (2) is calculated by substituting a numerical value of an amount [X] of each element X in terms of mass % and 0 in a case where the element X is not contained.
  • the index Q may be 0.04 or more, and the ratio may be 13.0% or less.
  • Ni is 0.05% to 1.00%.
  • Mn is 0.63% to 2.00%.
  • the aspect of the present invention it is possible to provide a steel plate having excellent wear resistance, in which high hardness can be maintained even in a high-temperature environment as well as at a room temperature, the carbon equivalent Ceq (%) of a steel plate particularly having a steel thickness of 40 mm or more is less than 0.800%, and the difference between the hardness at the surface layer portion and the hardness at the thickness center portion at a room temperature is set to 15.0% or less of the hardness at the surface layer portion.
  • the steel plate according to the present invention can be used over a long period of time even in a severe environment at a temperature of about 150° C. to 300° C. and thus the contribution thereof to the industry is extremely remarkable.
  • FIG. 1 is a view illustrating a change in the difference between a surface hardness of a steel plate and a reference hardness with temperature.
  • FIG. 2 is a view illustrating hardness distributions of steel plates in a through-thickness direction.
  • FIG. 3 is a view illustrating the relationship between a hardness difference ratio ⁇ Hv/Hvs of the steel plate and an index Q.
  • FIG. 1 is a view illustrating a change in the difference between a surface hardness of the steel plate and a reference hardness with temperature.
  • a result of performing hardening on steel plates having a constant C content, a varying Si content, and a steel thickness of 40 mm and measuring the Vickers hardness (surface hardness) HV5 at the surface of the steel plate from a room temperature to 400° C. is shown in FIG. 1 .
  • the Vickers hardness HV5 was measured by cutting out a sample from a position of 5 mm deep from the surface of the steel plate and conducting a high-temperature Vickers hardness test based on JIS Z 2252-1991 with a test force of 49.03 N (5 kgf).
  • the reference hardness was measured under the same conditions as those of the high-temperature Vickers hardness test described above except for temperature control.
  • FIG. 2 shows hardness distributions (Vickers hardness) of steel plates (steel thickness 40 mm) containing Si in an amount of more than 1.00% in the through-thickness direction after hardening.
  • the Vickers hardness HV5 was measured based on JIS Z 2244: 2009 at a room temperature with a test force of 49.03 N (5 kgf).
  • a hardness at a thickness center portion is lower than a hardness at a surface layer portion.
  • the hardness at the surface layer portion Hvs (the average value of Vickers hardnesses measured in a range of 1 mm to 5 mm from the surface of the steel plate in the through-thickness direction) and the hardness at the thickness center portion Live (the average value of Vickers hardnesses measured in a range of ⁇ 5 mm (10 mm in total thickness) from the center portion of the steel plate in the through-thickness direction) were obtained, and the difference (hardness difference) ⁇ Hv between the hardness at the thickness center portion and the hardness at the surface layer portion at a room temperature was calculated. That is, ⁇ Hv is expressed by Equation (a).
  • the inventors conducted examinations on a method of reducing the hardness difference between the surface layer portion and the thickness center portion at a room temperature in a steel plate containing Si in an amount of more than 1.00% and having a steel thickness of 40 mm or more.
  • the inventors repeatedly conducted examinations to reduce the hardness difference of the steel plate in consideration of the hardenability of alloying elements and the steel thickness.
  • the steel plate In order to secure the hardness of the steel plate, in hot rolling, the steel plate is typically reheated to a temperature of the Ac 3 point or higher at which transformation to austenite ends when the temperature rises, and thereafter subjected to water cooling or the like (hardening). At this time, the cooling rate at the surface layer portion of the steel plate is fast and thus sufficient hardness can be secured. On the other hand, the cooling rate at the thickness center portion of the steel plate is lower than that of the hardness at the surface layer portion, so that the formation of martensite becomes insufficient, resulting in a decrease in hardness.
  • the cooling rate decreases at the thickness center portion of the steel plate. Therefore, in order to secure a sufficient hardness at the thickness center portion of the steel plate, it is necessary to increase the amounts of the alloying elements to increase hardenability.
  • the amounts of the alloying elements are constant, there are problems that the hardenability becomes insufficient depending on the steel thickness, and the costs are increased, or weldability is impaired by including unnecessary amounts of the alloying elements. Therefore, in order to control the amounts of the alloying elements within appropriate ranges, it is necessary to consider the influence of the steel thickness on the cooling rate at the thickness center portion.
  • the inventors establishes the relationship between the amounts of the alloying elements having hardenability and the steel thickness, which influences the hardness difference ratio ⁇ Hv/Hvs of various steels containing Si in an amount of more than 1.00% and having a steel thickness of 40 mm or more, and derives an index Q shown in Equation (1).
  • the hardness difference ratio ⁇ Hv/Hvs (%) represents the ratio obtained by dividing the difference between the hardness at the surface layer portion and the hardness at the thickness center portion at a room temperature by the hardness at the surface portion as a percentage.
  • the hardness difference ratio ⁇ Hv/Hvs (%) is expressed by Equation (b).
  • Hvs is the hardness at the surface layer portion (the average value of Vickers hardnesses measured in a range of 1 mm to 5 mm from the surface of the steel plate in the through-thickness direction)
  • the live is the hardness at the thickness center portion (the average value of Vickers hardnesses measured in a range of ⁇ 5 mm (10 mm in total thickness) from the center portion of the steel plate in the through-thickness direction).
  • Equation (1) is based on the finding of the inventors that it is necessary to secure hardenability by including the alloying elements (C, Mn, Ni, Cr, and Mo) in addition to Si in order to increase the hardness at the thickness center portion, and the index Q does not include a Si content term.
  • the index Q of Equation (1) is calculated by substituting the numerical value of the steel thickness T (mm), the numerical value of the amount [X] of each element X in terms of mass % and 0 in a case where the element X is not contained.
  • the index Q is calculated by substituting dimensionless numerical values for the steel thickness T and the amount [X] of each element in Equation (1).
  • log in Equation (1) is the logarithm to base 10, that is, the common logarithm.
  • FIG. 3 shows the relationship between the hardness difference ratio ⁇ Hv/Hvs (%) and the index Q. From FIG. 3 , it is found that in a case where the hardness difference ratio ⁇ Hv/Hvs (%) is set to 15.0% or less of the hardness at the surface layer portion Hvs as a criterion for causing a thick steel plate to have a long service life, it is necessary to satisfy Q ⁇ 0.00. In addition, it is found that in a case of setting the hardness difference ratio ⁇ Hv/Hvs (%) to 13.0% or less of the hardness at the surface layer portion Hvs, it is necessary to satisfy Q ⁇ 0.04.
  • Equation (2) since the steel plate according to this embodiment has a steel thickness of 40 mm or more, there is concern of hydrogen embrittlement cracking under the influence of residual stress due to welding. Therefore, the carbon equivalent Ceq (%) expressed by Equation (2) is less than 0.800%. Equation (2) includes a Si content term because, the weldability of the steel plate needs to be taken into consideration.
  • the carbon equivalent Ceq (%) of Equation (2) is calculated by substituting the numerical value of the amount [X] of each element X in terms of mass %, and 0 is substituted in a case where the element X is not contained.
  • the unit of the carbon equivalent Ceq obtained by Equation (2) is “%”.
  • the index Q in Equation (1) By causing the index Q in Equation (1) to be 0.00 or more, the hardness difference ⁇ Hv between the surface layer portion and the thickness center portion of the steel plate at a room temperature becomes 15.0% or less of the hardness at the surface layer portion Hvs, so that a steel plate having a small hardness difference, a carbon equivalent of less than 0.800%, a steel thickness of 40 mm or more, and excellent wear resistance can be obtained.
  • the C is an element effective for improving the hardness, and the C content is set to 0.20% or more in order to secure the hardness of the steel plate.
  • the C content is preferably 0.22% or more, and more preferably 0.24% or more.
  • the C content is set to 0.35% or less.
  • the C content is set to preferably 0.32% or less, and more preferably 0.30% or less.
  • Si is a deoxidizing agent and is an element effective for improving the hardness of the steel plate.
  • Si is an extremely important element for maintaining the hardness of the steel plate in a high-temperature environment.
  • the Si content is set to be more than 1.00%, The Si content is preferably 1.10% or more, and more preferably 1.20% or more, or 1.30% or more.
  • the Si content exceeds 2.00%, the toughness of the steel plate may be impaired, so that the Si content is set to 2.00% or less.
  • the Si content is set to preferably 1.90% or less, and more preferably 1.80% or less.
  • Mn is an element which increases the hardenability and improves the hardness, and needs to be contained, in an amount of 0.60% or more in order to secure the hardness of the steel plate.
  • the Mn content is preferably 0.70% or more, and more preferably 0.80% or more.
  • the Mn content is set to 2.00% or less.
  • the Mn content is set to preferably 1.50% or less or 1.35% or less, and more preferably 1.20% or less or 1.00% or less.
  • the Cr content is an element which increases the hardenability and improves the toughness and hardness of the steel plate.
  • the Cr content is set to 0.10% or more.
  • the Cr content is preferably 0.50% or more, and more preferably 0.80% or more.
  • the toughness of the steel plate decreases, so that the Cr content is set to 2.00% or less.
  • the Cr content is set to preferably 1.70% or less, and more preferably 1.50% or less.
  • Mo is also an element which increases the hardenability and improves the hardness of the steel plate.
  • Mo is an element effective for maintaining the hardness of the steel plate even in a high-temperature environment. Therefore, the Mo content is set to 0.05% or more.
  • the Mo content is set to preferably 0.10% or more, and more preferably 0.20% or more.
  • the Mo content exceeds 1.00%, the toughness of the steel plate decreases, so that the Mo content is set to 1.00% or less.
  • the Mo content is set to preferably 0.60% or less, and more preferably 0.40% or less.
  • A1 is an element effective as a deoxidizing agent.
  • A1 is bonded to N to form in AlN, and refines crystal grains, thereby improving the toughness of the steel plate. Therefore, the Al content is set to 0.010% or more.
  • the Al content is set to preferably 0.020% or more, and more preferably 0.030% or more.
  • the toughness of the steel plate decreases, so that the Al content is set to 0.100% or less.
  • the Al content is set to preferably 0.080% or less, and more preferably 0.070% or less.
  • N is an element that is bonded to Al and Ti to form nitrides, and refines crystal grains, thereby improving the toughness of the steel plate. Therefore, the N content is set to 0.0020% or more.
  • the N content is set to preferably 0.0030% or more, and more preferably 0.0040% or more.
  • the N content is set to 0.0100% or less.
  • the N content is set to preferably 0.0080% or less, and more preferably 0.0060% or less.
  • the B is, an element that significantly increases the hardenability of steel and is particularly effective for improving the hardness at the thickness center portion of the steel plate. Therefore, the B content is set to 0.0003% or more.
  • the B content is set to preferably 0.0005% or more, more preferably 0.0007% or more, and even more preferably 0.0010% or more.
  • the B content is set to 0.0020% or less.
  • the B content is preferably 0.0018% or less, and more preferably 0.0016% or less.
  • the P content is an impurity, and reduces, the toughness and workability of the steel plate. Therefore, the P content is limited to 0.0200% or less.
  • the P content is set to preferably 0.0150% or less, and more preferably 0.0100% or less.
  • the lower limit of the P content is preferably 0%, but from the viewpoint of manufacturing costs, the P content may be 0.0001% or more
  • the S content is limited to less than 0.0100%.
  • the S content is set to preferably 0.0070% or less, more preferably 0.0050% or less, and even more preferably 0.0030% or less.
  • the lower limit of the S content is preferably 0%, but from the viewpoint of manufacturing costs, the S content may be 0.0001% or more.
  • one or more of Cu, Ni, Nb, V, and Ti can be selectively contained for, the purpose of improving the mechanical properties such as the hardness and toughness of the steel plate.
  • the lower limit of the amounts of these elements is 0%.
  • Cu is an element that forms fine precipitates and contributes to the improvement of the strength (4 the steel plate, and may be contained in an amount of 0.001% or more.
  • the Cu content is set to more preferably 0.050% or more, and even more preferably 0.100% or more.
  • the upper limit of the Cu content is set to 0.500% or less.
  • the Cu content is set to more preferably 0.450% or less, and even more preferably 0.400 or less.
  • Ni is an element that increases the hardenability of the steel and contributes to the in of the hardness of the steel plate, and may be contained in an amount of 0.05% or more.
  • the Ni content is set to more preferably or more, and even more preferably 0.20% or more.
  • the Ni content is set to 1.00% or less.
  • the Ni content is set to more preferably 0.70% or less, and even more preferably 0.50% or less.
  • Nb is an element contributing to grain refinement by the formation of nitride and suppressing recrystallization, and may be contained in an amount of 0.005% or more in order to improve the toughness of the steel plate.
  • the Nb content is set to more preferably 0.007% or more, and even more preferably 0.010% or more.
  • the toughness of the steel plate may decrease. Therefore, the Nb content is set to 0.050% or less.
  • the Nb content is set to more preferably 0.030% or less, and even more preferably 0.020% or less.
  • V is an element that contributes to the improvement of the hardness of the steel plate, and may be contained in an amount of 0.010% or more.
  • the V content is set to more preferably 0.020% or more, and even more preferably 0.040% or more.
  • the V content is set to 0.120% or less.
  • the V content is set to more preferably 0.100% or less, and even more preferably 0.070% or less.
  • Ti is an element that forms TiN, refines crystal grains, and thus improves the toughness of the steel plate, and may be contained in an amount of 0.005% or more.
  • the Ti content is set to more preferably 0.007% or more, and even more preferably 0.010% or more.
  • excessive inclusion of Ti may reduce the toughness of the steel plate, so that the Ti content is set to 0.025% or less.
  • the Ti content is set to more preferably 0.020% or less, and even more preferably to 0.015% or less.
  • one or more of Ca, Mg, and REM can be selectively contained.
  • the lower limit of the amounts of these elements is 0%.
  • any of Ca, Mg, and REM is an element that is bonded to S to form sulfides and forms inclusions that are less likely to be stretched by hot rolling, and mainly contributes to the improvement of the toughness of the steel plate.
  • Ca, Mg, and REM when Ca, Mg, and REM are excessively contained, these elements form coarse oxides with O, and there may be cases where the toughness of the steel plate may decrease. Therefore, each of the Ca content and the Mg content is set to 0.050% or less, and the REM content is set to 0.100% or less.
  • Each of the Ca content, the Mg content, and the REM content is each set to more preferably 0.020% or less, and even more preferably 0.010% or less, or 0.005% or less.
  • each of the Ca content and the Mg content is set to 0.0005% or more, and the REM content is set to 0.001% or more. More preferably, each of the Ca content and the Mg content is set to 0.0007% or more, and the REM content is set to 0.002% or more.
  • REM rare-earth metal elements
  • the REM content means the total amount of these 17 elements.
  • the remainder of the chemical composition of the steel plate according to this embodiment consists of Fe and impurities.
  • the impurities mean elements that are incorporated when a steel plate is industrially manufactured, due to various factors in a manufacturing process including raw materials such as ore and scrap, and are acceptable within a range in which the characteristics of the steel plate according to this embodiment are not adversely affected.
  • the upper limits of P and S among the impurities need to be specified as described above.
  • O may be incorporated as an impurity in the steel, in some cases.
  • the O content is preferably small.
  • the O content is set to 0.006% or less.
  • the O content is set to preferably 0.005% or less, and more preferably to 0.004% or less.
  • Sb is an element incorporated from scrap as a steel raw material.
  • the wear resistance of the steel plate deteriorates, so that the Sb content is set to 0.01% or less.
  • the Sb content is set to preferably 0.007% or less, or 0.005% or less.
  • Sn is an element incorporated from scrap as a steel raw material.
  • the wear resistance of the steel plate deteriorates, so that the Sn content is set to 0.01% or less.
  • the Sn content is set to preferably 0.007% or less, or 0.005% or less.
  • As is an element incorporated from scrap as a steel raw material.
  • the wear resistance of the steel plate deteriorates, so that the As content is set to 0.01% or less.
  • the As content is set to preferably 0.007% or less, or 0.005% or less.
  • the index Q obtained by Equation (1) is set to 0.00 or more so that the hardness difference between the surface layer portion and the thickness center portion of the steel plate at a room temperature is small and the ratio of the hardness difference to the hardness at the surface layer portion is 15.0% or less.
  • the index Q is calculated by substituting dimensionless numerical values for the numerical value of the steel thickness T (mm) and the numerical value of the amount [X] of each element X in terms of mass %, and [X] is set to 0 in a case where the element X is not contained.
  • the index Q is set to preferably 0.01 or more, more preferably 0.04 or more, even more preferably 0.05 or more, and still more preferably 0.10 or more.
  • the upper limit of the index Q is not particularly specified. However, since the carbon equivalent Ceq (%) also increases as the index Q increases, the index Q is limited by itself. In order to secure the weldability by causing the carbon equivalent Ceq (%) to be less than 0.800%, the index Q is preferably 1.10 or less.
  • the index Q is set to more preferably 0.80 or less or 0.50 or less, and more preferably 0.30 or less or 0.20 or less.
  • the carbon equivalent Ceq (%) is set to be less than 0.800%.
  • the carbon equivalent Ceq (%) is calculated by substituting the numerical value of the amount [X] of each element in terms of mass %, and [X] is set to 0 in a case where the element X is not contained.
  • the lower limit of the carbon equivalent is not particularly specified.
  • the carbon equivalent Ceq (%) is limited by itself. In order to reduce the hardness difference by setting the index Q to 0.00 or more, the carbon equivalent Ceq (%) is preferably 0.507% or more.
  • the carbon equivalent Ceq (%) is set to more preferably 0.600% or more, and more preferably 0.650% or more.
  • the carbon equivalent Ceq (%) is set to even more preferably 0.700% or more.
  • the carbon, equivalent Ceq (%) may be 0.785% or less, 0.770% or less, or 0.760% or less.
  • the difference (hardness difference) between the hardness at the surface layer portion and the hardness at the thickness center portion at a room temperature is small and the ratio of the difference between the hardness at the surface layer portion and the hardness at the thickness center portion to the hardness at the surface layer portion is 15.0% or less, excellent wear resistance can be exhibited over a long period of time.
  • the hardness difference ratio ⁇ Hv/Hvs) is as small as possible.
  • the hardness difference ratio ⁇ Hv/Hvs (%) may be 3.0% or more.
  • the hardness at the surface layer portion and the hardness at the thickness center portion are Vickers hardnesses HV5 at a room temperature and are measured based on JIS Z 2244:2009.
  • the hardness at the surface layer portion is measured using a section parallel to the rolling direction and the through-thickness direction of the steel plate as a measurement surface, and is the average value of Vickers hardnesses HV5 measured in a range of 1 mm to 5 mm from the surface of the steel plate in the through-thickness direction.
  • Vickers hardnesses at a total of 25 points 5 points at least every 1 mm in the range are measured.
  • the hardness at the thickness center portion is the average value of Vickers hardnesses HV5 measured in a range of ⁇ 5 mm (10 mm in total thickness) from the thickness center portion of the steel plate in the through-thickness direction on the measurement surface.
  • Vickers hardnesses at a total of 55 points 5 points at least every 1 mm in the range are measured.
  • the hardness at the surface layer portion Hvs at room temperature is 400 or more in terms of Vickers hardness (HV5).
  • HV5 Vickers hardness
  • the hardness at the surface layer portion Hvs is less than 400 in terms of Vickers hardness (HV5), the strength of the hardness at the surface layer portion of the steel plate is insufficient, and cannot be used for applications such as construction machines and industrial machines.
  • the hardness at the surface layer portion Hvs at room temperature may be 440 or more, 460 or more, 480 or more, or 500 or more in terms of Vickers hardness (Hv5).
  • the steel plate according to this embodiment exhibit very high hardness from the hardness at the surface layer portion to the hardness at the thickness center portion and very high tensile strength.
  • the tensile strength (TS) thereof at room temperature may be set to 1000 MPa or more, 1200 MPa or more, 1350 MPa or more, or 1500 MPa or more.
  • the upper limit of the tensile strength does not need to be particularly determined, but may be 2300 MPa or less.
  • the tensile strength is measured based on JIS Z 2241;2011 by extracting an overall thickness test piece (that is, a plate-shaped test piece) or a round bar test piece from a position (T/4) away from the surface of the steel plate by 1 ⁇ 4 of the steel thickness T.
  • the steel plate according to this embodiment is a steel plate manufactured by hot rolling and is a steel plate having a steel thickness of 40 mm or more, preferably 42 mm or more or 50 mm or more, and more preferably 60 mm or more or 80 mm or more.
  • the upper limit of the steel thickness is not particularly specified, and may be 150 mm depending on the application. In consideration homogenization of the properties of the steel plate in the through-thickness direction, the steel thickness may be set to 100 mm or less.
  • the steel piece having the above-described chemical composition can be manufactured by a known method such as a continuous casting method of an ingot-making and blooming method after melting in a typical refining process using a converter, an electric furnace, or the like, and there is no particular limitation.
  • the steel piece obtained by casting is hot-rolled, water-cooled as it is or air-cooled, and thereafter reheated and hardened, thereby manufacturing the steel plate.
  • the steel plate is hardened but is not subjected to a heat treatment such as tempering.
  • a steel may be subjected to melting, casting, and thereafter hot rolling as it is.
  • a steel piece may be once cooled to room temperature, reheated to a temperature of the Ac 3 point or higher, and then hot rolled.
  • the Ac 3 point is a temperature at which the structure of the steel becomes austenite (austenitic transformation is completed) due to a temperature rise.
  • the heating temperature of the hot rolling is set to preferably 900° C. or higher, and more preferably 1000° C. or higher in order to reduce the deformation resistance.
  • the heating temperature is preferably 1250° C. or lower.
  • the heating temperature is more preferably 1200° C. or lower, and even more preferably 1150° C. or lower.
  • the hot rolling is ended at the Ar 3 point or higher, which is the temperature at which ferritic transformation starts by a temperature decrease.
  • the Ac 3 point and the Ar 3 point can be obtained by extracting a test piece from a steel piece and obtaining a thermal expansion behavior at the time of heating and cooling.
  • the steel plate is hardened to a temperature of 250° C. or lower immediately after the hot rolling, or is air-cooled after the hot rolling, reheated to a temperature of the Ac 3 point or higher, hardened to a temperature of 250° C. or lower.
  • the present invention will be described in more detail by employing examples of the steel plate according to the present invention.
  • the present invention is not limited to the following examples as a matter of course, and can be embodied by appropriately adding changes within a range that is appropriate for the gist of the present invention, and all such changes are included in the technical scope of the present invention.
  • a steel having a chemical composition shown in Table 2 was melted, cast, thereafter hot-rolled into a steel plate having a steel thickness shown in Table 3, and air-cooled to room temperature. Thereafter, a steel plate having a steel thickness of 40 mm or more was manufactured by increasing the temperature to a hardening temperature shown in Table 3 and performing hardening thereon.
  • a test piece was extracted from the obtained steel plate, and using a section of the steel plate parallel to the rolling direction and the through-thickness direction as a test surface, the Vickers hardnesses at the surface layer portion and the thickness center portion were measured based on JIS Z 2244:2009 at room temperature with a test force of 49.03 N (5 kgf).
  • the Vickers hardness (a hardness at the surface layer portion) Hvs of at the surface layer portion was obtained by measuring Vickers hardnesses at a total of 25 points, 5 points every 1 mm, in a range (surface layer portion) of 1 mm to 5 mm from the surface of the steel plate in the through-thickness direction, and obtaining the average value (arithmetic mean) thereof.
  • the Vickers hardness (hardness at a thickness center portion) Hvc of the thickness center portion was obtained by measuring Vickers hardnesses at a total of 55 points, 5 points every 1 mm, in a range of ⁇ 5 mm (10 mm in total thickness) from the thickness center portion of the steel plate in the through-thickness direction, and obtaining the average value (arithmetic mean) thereof.
  • the hardness difference ratio ⁇ Hv/Hvs (%) representing the hardness difference between the surface layer portion and the thickness center portion of the steel plate at a room temperature was obtained.
  • the hardness difference ratio ⁇ Hv/Hvs (%) is expressed by Equation (b).
  • the criteria of evaluation items are as follows. Regarding both the hardness at the surface layer portion Hvs (HV5) and the hardness at the thickness center portion Hvc (HV5), a hardness of 400 or more was determined to be good from the viewpoint of wear resistance, and a hardness of 600 or less was determined to be good from the viewpoint of cutting workability. Regarding the high-temperature hardness (HV5) at the surface layer portion, a hardness of 300 or more was determined to be good from the viewpoint of wear resistance at high temperatures. A Charpy absorbed energy at 0° C. of 15 J or more was determined to be good.
  • the parameters of the chemical composition including the index Q and the carbon equivalent Ceq (%) and the steel thickness T are within the ranges of the present invention, and the hardness difference ratio ⁇ Hv/Hvs between the surface layer portion and the center portion is 15.0% or less. Any of these steels is a steel plate excellent in the hardness at the surface layer portion Hvs, the hardness at the thickness center portion live, the high-temperature hardness at the surface layer portion, and the Charpy absorbed energy at 0° C.
  • Nos. 101 to 115 in Table 3 are comparative examples, and the chemical compositions including the Q value are out of the ranges of the present in Nos. 101 to 103 are examples in which the Q value was low in relation to the steel thickness and the hardness difference ratio ⁇ Hv/Hvs (%) exceeded 15.0%.
  • No. 107 is an example in which the Si content was insufficient and the high-temperature hardness at the surface layer portion had decreased.
  • No. 107 is an example in which the Si content was large and the toughness had decreased.
  • Nos. 104, 108 and 114 are examples in which the C content, the Mn content, and the B content were insufficient, respectively, and the hardness at the surface layer portion Hvs, the hardness at the thickness center portion Hvc, and the high-temperature hardness at the surface layer portion had decreased.
  • No. 110 in which the Cr content was insufficient is an example in which the toughness had decreased in addition to the hardness at the surface layer portion Hvs, the hardness at the thickness center portion Hvc, and the high-temperature hardness at the surface layer portion.
  • No. 112 in which the Mo content was insufficient is an example in which the hardness at the thickness center portion Hvc, the high-temperature hardness at the surface layer portion, and the toughness had decreased.
  • No. 105 is an example in which the C content was large and the hardness at the surface layer portion Hvs was excessively high.
  • No. 109 with a high Mn content, No. 111 with a high Cr content, and No. 113 with a high Mo content are examples in which the toughness had decreased.
  • No. 115 with an excessive B content is an example in which the hardness at the surface layer portion Hvs, the hardness at the thickness center portion Hvc, and the high-temperature hardness at the surface layer portion had decreased.
  • the O content was 0.006% or less, and all the Sb content, the Sn content, and the As content were 0.01% or less.

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Family Cites Families (11)

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JPH0841535A (ja) * 1994-07-29 1996-02-13 Nippon Steel Corp 低温靱性に優れた高硬度耐摩耗鋼の製造方法
JPH10251800A (ja) * 1997-03-12 1998-09-22 Kawasaki Steel Corp 高炭素薄物熱延鋼板及びその製造方法
JP2001049387A (ja) * 1999-08-03 2001-02-20 Nippon Steel Corp 高靭性厚手高温耐摩耗鋼
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JP5029748B2 (ja) * 2010-09-17 2012-09-19 Ｊｆｅスチール株式会社 靭性に優れた高強度熱延鋼板およびその製造方法
CN102691017A (zh) * 2012-03-27 2012-09-26 北京科技大学 一种具有nm550硬度的低成本耐磨钢板及制造方法
JP5966730B2 (ja) * 2012-07-30 2016-08-10 Ｊｆｅスチール株式会社 耐衝撃摩耗特性に優れた耐摩耗鋼板およびその製造方法
KR101542709B1 (ko) * 2013-08-13 2015-08-12 신닛테츠스미킨 카부시키카이샤 강판
JP5924332B2 (ja) * 2013-12-12 2016-05-25 Ｊｆｅスチール株式会社 加工性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法

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EP3502296A1 (en) 2019-06-26
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BR112019006254B1 (pt) 2022-08-09
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