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    abstract patent of invention: "steel plate resistant to abrasion that has rigidity at low temperature and method of manufacturing it". a plate has a brinell hardness (hbw10 / 3000) of 361 or more, and a thickness of 6 to 125 mm, contains 50/100 µm2 or more of fine precipitates with a diameter of 50nm or less in clap martensite steel with crystal grains , which are surrounded by high angle grain outlines of a wrong orientation of 15 ° or more, and have an average particle size of 20 µm or less. steel contains, by weight%, c: 0.10 to less than 0.20%, si: 0.05 to 0.5%, mn: 0.5 to 1.5%, cr: 0.05 to 1.20%, nb: 0.01 to 0.08%, b: 0.0005 to 0.003%, al: 0.01 to 0.08%, n: 0.0005 to 0.008%, p: 0.05 % or less, s: 0.005% or less, o: 0.008% or less, in addition, contains, one or more rare earth elements among mo, v, ti, nd, cu, ni, w, ca and mg, and satisfies 0.03 = nb + ti + al + v = 0.14, with the remainder constituting fe and the inevitable impurities. the steel is melted, and after rolling, reheated to the transformation point ac3 or higher, and successively cooled sharply from the transformation point ar3 or higher to a temperature of 250 ° c or less by cooling with water. as required, the steel is reheated to 1100 ° c or more, the reduction in rolling in a non-recrystallized region is 30% or more, and the steel is cooled by cooling with water to a temperature of 250 ° c or less , and reheated at a rate of 1 ° c / s or more to transformation point ac3 or greater.
    公开号:BR112015020046B1
    申请号:R112015020046
    申请日:2014-03-19
    公开日:2020-05-05
    发明作者:Nagao Akihide；Ishikawa Nobuyuki；Miura Shinichi
    申请人:Jfe Steel Corp；
    IPC主号:
    专利说明:

    Descriptive Report of the Invention Patent for ABRASION-RESISTANT THICK STEEL PLATE WITH EXCELLENT RIGIDITY AT LOW TEMPERATURE AND THE MANUFACTURING METHOD OF THE SAME.
    FIELD OF TECHNIQUE [0001] The present invention relates to abrasion-resistant steel plates that have excellent low temperature stiffness and to the methods of manufacturing such steel plates. In particular, the invention relates to techniques suitable for abrasion-resistant steel plates with excellent low temperature stiffness having a Brinell hardness of 361 or more.
    BACKGROUND TECHNIQUE [0002] In recent years, there has been a trend to increase the hardness of steel plates that are used in the field of industrial machinery in abrasive environments such as mines, civil engineering, agricultural machinery and construction with the aim of, for example , extend the life of the crushing capacity to crush powder ores.
    [0003] However, the increase in steel hardness is generally accompanied by a decrease in stiffness at low temperature and, consequently, poses a risk that the steel may be cracked during use. Thus, there is a strong demand for the improvement in the low temperature stiffness of high hardness abrasion resistant steel plates, in particular, the abrasion resistant steel plates that have a Brinell hardness of 361 or more.
    [0004] Approaches for making abrasion-resistant steel plates with excellent low temperature stiffness and methods of manufacturing such steel plates have been proposed in the art as in Patent Literature 1, 2 and 3 in which stiffness low temperature is improved by optimizing the carbon equivalent and the
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    2/23 hardenability index.
    CITATION LIST PATENT LITERATURE [0005] PTL 1: Unexamined Patent Application Publication
    Japanese No. 2002-256382 [0006] PTL 2: Japanese Patent No. 3698082 [0007] PTL 3: Japanese Patent No. 4238832 [0008] DISCLOSURE OF THE INVENTION TECHNICAL PROBLEM [0009] However, the Charpy absorbed energy at -40 ° C, which is obtained with stability by conventional methods, such as those described in Patent Literature 1, 2 and 3 reaches a limit of about 50 to 100 J. Thus, there has been a demand for abrasion resistant steel plates that have greater stiffness at low temperature and for methods capable of making such steel plates.
    [0010] The present invention has been made in the light of the circumstances in the technique discussed above. It is, therefore, an object of the invention to provide abrasion-resistant steel plates that have a Brinell hardness of 361 or more and that still exhibit higher than low temperature stiffness in conventional abrasion-resistant steel plates, and to provide methods of making such plates of steel.
    SUMMARY OF THE INVENTION SOLUTION TO THE PROBLEM [0011] The three basic quality design guidelines for improving low temperature stiffness of martensellitic steel on clapboard as tempered are to reduce the size of the high-angle grain contours that generally determine the fracture facet sizes, decrease the amount of impurities, such as phosphorus and sulfur that reduce the bond strength in the grain contours, and reduce the size and amount of inclusions that induce low fragility
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    3/23 temperature.
    [0012] The present inventors have carried out extensive studies aimed at improving the low temperature stiffness of abrasion resistant steel plates based on the above point of view. As a result, the present inventors have found that the thickening of reheated austenite grains is suppressed by dispersing a large amount of fine precipitates, such as Nb carbonitride, which has a diameter of no more than 50 nm and, consequently, the size of packages, which determine fracture facet sizes, is significantly reduced to make it possible to obtain abrasion-resistant steel plates that have greater stiffness at low temperature than conventional materials.
    [0013] The present invention has been completed by further studies based on the above finding, and provides the following abrasion resistant steel plates that have excellent low temperature stiffness, as well as the methods of making such steel plates.
    (1) An abrasion-resistant thick steel plate with excellent low temperature stiffness that includes, by weight% of C: 0.10% to less than 0.20%, of Si: 0.05 to 0.5% , from Mn: 0.5 to 1.5%, from Cr: 0.05 to 1.20%, from Nb: 0.01 to 0.08%, from B: 0.0005 to 0.003%, from Al: 0.01 to 0.08%, N: 0.0005 to 0.008%, P: no more than 0.05%, S: no more than 0.005% and O: no more than 0.008% , the rest being Fe and unavoidable impurities, the thick steel plate includes fine precipitates of 50 nm or less in diameter with a density of 50 or more particles per 100 pm 2 , the thick steel plate that has a martensitic structure in clapboard from the surface of the thick steel plate by at least a depth of 1/4 of the thickness of the plate, the clapboard martensitic structure that has an average grain size of no more than 20 pm, in which the average grain size is the average grain size of cris beans
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    4/23 such surrounded by high-angle grain contours that have an orientation difference of 15 ° or more, the thick steel plate that has a Brinell hardness (HBW10 / 3000) of 361 or more.
    (2) The abrasion-resistant thick steel plate with excellent low temperature stiffness described in (1), where the steel additionally includes, by weight%, one, or two or more Mo: no more than 0 , 8%, of V: not more than 0.2% and of Ti: not more than 0.05%.
    (3) The abrasion resistant thick steel plate with excellent low temperature stiffness described in (1) or (2), in which the chemical composition of the steel additionally includes, by weight%, one, or two or more of Nd: no more than 1% Cu: no more than 1% Ni: no more than 1% W: no more than 1% Ca: no more than 0.005% Mg: no more than than 0.005% and REM: no more than 0.02% (note: REM is an abbreviation for rare earth metal).
    (4) The abrasion-resistant thick steel plate with excellent low temperature stiffness described in any one of (1) to (3), in which the contents of Nb, Ti, Al and V satisfy 0.03 <Nb + Ti + Al + V <0.14 where Nb, Ti, Al and V indicate the respective levels (in% by mass) and are 0 when Nb, Ti, Al and V are not added.
    (5) The abrasion-resistant thick steel plate with excellent low temperature stiffness described in any of (1) to (4), where the thickness of the plate is from 6 to 125 mm.
    (6) The abrasion-resistant thick steel plate described in any of (1) to (5), where the energy absorbed by Charpy at 40 ° C is not less than 27 J.
    (7) A method for manufacturing an abrasion-resistant thick steel plate with excellent low temperature stiffness, which includes ingot steel that has the chemical composition described in
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    5/23 any one of (1) to (4), hot laminate the sheet to form a thick steel sheet having a prescribed plate thickness, reheat the thick steel sheet to the transformation point Ac3 or above and subsequently tempering the thick steel plate by cooling with water from a temperature of not less than the transformation point Ar3 to a temperature of not more than 250 ° C.
    (8) The method for manufacturing an abrasion-resistant thick steel plate with excellent low temperature stiffness described in (7), which additionally includes reheating the plate to be cast to 1,100 ° C or above.
    (9) The method for manufacturing an abrasion-resistant thick steel plate with excellent low temperature stiffness described in (7) or (8), in which the reduction of lamination during hot rolling in a non-recrystallized region is not less than 30%.
    (10) The method for manufacturing an abrasion-resistant thick steel plate with excellent low temperature stiffness described in any of (7) to (9), which additionally includes hot-rolled thick plate for hot-rolled thick plate by cooling with water to a temperature of no more than 250 ° C.
    (11) The method for manufacturing an abrasion-resistant thick steel plate with excellent low temperature stiffness described in any one of (7) to (10), where the reheating of the hot-rolled or cooled thick steel plate water up to the transformation point Ac3 or above is carried out at a rate of not less than 1 ° C / s.
    ADVANTAGE EFFECTS OF THE INVENTION [0014] The abrasion-resistant steel plates of the present invention
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    6/23 tion have a Brinell hardness of 361 or more and still exhibit higher stiffness at low temperature, and inventive methods can produce such steel plates. These advantages are very useful in the industry.
    DESCRIPTION OF THE MODALITIES [0015] The reasons why the microstructure in the invention is limited will be described.
    [0016] An abrasion-resistant thick steel plate of the present invention includes a clapboard martensitic steel that has a microstructure in which the region from the surface of the thick steel plate to at least a depth of 1/4 of the plate thickness it is a martensitic structure in clapboard and the average grain size of the crystal grains surrounded by the high angle grain contours that has an orientation difference of 15 ° or more is not greater than 20 pm, preferably not greater than 10 pm , and most preferably not greater than 5 mm.
    [0017] High angle grains serve as locations where landslides are accumulated. The reduction in the size of high-angle grains solves the problem of stress concentration due to the accumulation of slips to the grain contours, and therefore reduces the occurrence of breaks due to brittle rupture, thus improving low temperature stiffness . The effect of improving low temperature stiffness is increased by decreasing grain sizes. The indicated effect can be obtained by controlling the average grain size of crystal grains surrounded by high angle grain contours that have an orientation difference of 15 ° or more up to no more than 20 μm. The average grain size is preferably not more than 10 μm and, more preferably, not more than 5 μm.
    [0018] For example, crystal orientations can be measured by analyzing crystal orientations in a 100 μm region
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    7/23 squared by an Electron Diffraction method (posterior electron scattering pattern). Assuming that the high angle refers to a difference of 15 ° or more in the grain contour orientations, the diameters of the grains surrounded by such grain contours are measured and the simple average of the results is determined.
    [0019] In the invention, steel includes fine precipitates that have a diameter of not more than 50 nm, preferably not more than 20 nm, and more preferably, not more than 10 nm, with a density of 50 or more particles per 100 pm 2 .
    [0020] The main fine precipitates whose effects have been confirmed are Nb carbonitrides, Ti carbonitrides, Al nitrides and V carbides. However, the precipitates are not limited to these, as long as the sizes match, and may include other shapes, such as oxides. Fine precipitates that have a smaller diameter and greater density provide greater effects in suppressing crystal thickening due to their immobilization effect. The size of the crystal grains is reduced and the low temperature stiffness is enhanced by the presence of at least 50 or more fine precipitate particles that have a diameter of no more than 50 nm, preferably no more than 20 nm and, more preferably, not more than 10 nm per 100 pm 2 .
    [0021] To determine the average particle diameter of the fine precipitates, for example, a sample prepared by a replica carbon extraction method is observed and photographed by TEM, and the image is analyzed to measure the average particle diameter of 50 or more particles of fine precipitates as the simple average.
    [0022] Brinell hardness is 361 or more, with the objective of obtaining high abrasion resistance performance. The thickness of the plate is 6 to 125 mm, which is the general rate of thickness of abrasion-resistant steel plates. However, the thickness of the plate is not limited to
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    8/23 this rate and the technique of the present invention is applicable to steel plates having other thicknesses. It is not always necessary for the thick steel plate to be entirely composed of the martensitic structure in clapboard. Depending on the use, for example, the martensitic structure in clapboard can extend from the surface of the thick steel plate to a depth of 1/4 of the thickness of the plate, and the other region extending from 1/4 to 3/4 of the thickness of the plate can be, for example, a lower bainitic structure or an upper bainitic structure.
    [0023] A preferred chemical composition and conditions for the manufacture of abrasion-resistant steel plates that have the aforementioned microstructure are limited for the reasons described below.
    [CHEMICAL COMPOSITION] THE UNIT% IN THE CHEMICAL COMPOSITION IS MASS%.
    C: 0.10% to less than 0.20% [0024] Carbon is added to guarantee martensitic hardness and hardenability. These effects are not sufficiently achieved if the amount added is less than 0.10%. On the other hand, the addition of 0.20% or more of carbon results in a decrease in the stiffness of the base steel and welds the affected areas by heat, and also causes a marked decrease in weldability. Thus, the C content is limited from 0.10% to less than 0.20%.
    Si: 0.05 to 0.5% [0025] Silicon is added as a deoxidizer in steelmaking and also as an element to guarantee hardenability. These effects are not sufficiently achieved if the amount added is less than 0.05%. If, on the other hand, more than 0.5% of silicon is added, the grain contours are weakened and the low temperature is reduced. Thus, the Si content is limited from 0.05 to 0.5%.
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    9/23
    Mn: 0.5 to 1.5% [0026] Manganese is added as an element to guarantee hardenability. This effect is not sufficiently achieved if the amount added is less than 0.5%. If, on the other hand, more than 1.5% of manganese is added, the strength in the grain contours is reduced and the stiffness at low temperature is reduced. Thus, the Mn content is limited from 0.5 to 1.5%.
    Cr: 0.05 to 1.20% [0027] Chromium is added as an element to guarantee hardenability. This effect is not sufficiently achieved if the amount added is less than 0.05%. On the other hand, the addition of more than 1.20% chromium results in a decrease in weldability. Thus, the Cr content is limited from 0.05 to 1.20%.
    Nb: 0.01 to 0.08% [0028] Niobium forms the Nb carbonitrides in the form of fine precipitates that serve to immobilize the heated austenite grains and, thus, suppress grain thickening. This effect is not sufficiently achieved if the Nb content is less than 0.01%. On the other hand, the addition of more than 0.08% niobium causes a decrease in the stiffness of areas affected by welding heat. Thus, the Nb content is limited from 0.01 to 0.08%.
    B: 0.0005 to 0.003% [0029] Boron is added as an element to guarantee hardenability. This effect is not sufficiently achieved if the amount added is less than 0.0005%. The addition of more than 0.003% of boron causes a decrease in stiffness. Thus, the B content is limited from 0.0005 to 0.003%.
    Al: 0.01 to 0.08% [0030] Aluminum is added as a deoxidizer and also forms Al nitrides in the form of fine precipitates, which serve
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    10/23 to immobilize the heated austenite grains and thus suppress grain thickening. Additionally, aluminum fixes free nitrogen like Al nitrides and thus suppresses the formation of B nitrides to allow free boron to be used effectively to improve hardenability. Thus, in the invention, it is more important to control the Al content. Aluminum needs to be added by 0.01% or more, because the above effects are not sufficiently achieved if the Al content is less than 0.01% . Preferably, it is recommended to add 0.02% or more of aluminum and, more preferably, 0.03% or more of aluminum. On the other hand, the addition of more than 0.08% aluminum increases the likelihood of surface defects on steel plates. Thus, the Al content is limited from 0.01 to 0.08%.
    N: 0.0005 to 0.008% [0031] Nitrogen forms nitrides with elements such as niobium, titanium and aluminum in the form of fine precipitates, which serve to immobilize the heated austenite grains and, thus, suppress grain thickening . Thus, nitrogen is added to obtain a stiffness-enhancing effect at low temperature. The effect of reducing the size of the microstructure is not sufficiently achieved if the amount added is less than 0.0005%. If, on the other hand, more than 0.008% nitrogen is added, the amount of solute nitrogen is then increased, so that the stiffness of the base steel and the welding of heat-affected zones is decreased. Thus, the N content is limited from 0.0005 to 0.008%.
    P: no more than 0.05% [0032] Phosphorus is an impurity element and is readily segregated in the crystal grain outlines. If the P content exceeds 0.05%, the bond strength between the adjacent crystal grains is reduced and the low temperature stiffness is decreased. Thus, the P content is
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    11/23 limited to no more than 0.05%.
    S: no more than 0.005% [0033] Sulfur is an impurity element and is readily segregated in the crystal grain outlines. Sulfur also tends to form MnS, which is a non-metal inclusion. The addition of more than 0.005% sulfur decreases the bond strength between adjacent crystal grains and also increases the amount of inclusions, which results in a decrease in stiffness at low temperature. Thus, the S content is limited to no more than 0.005%.
    O: no more than 0.008% [0034] Oxygen affects the workability of steel by forming oxides with elements such as aluminum. If more than 0.008% oxygen is added, the working capacity is impaired due to the increase in the amount of inclusions. Thus, the O content is limited to no more than 0.008%.
    [0035] The abrasion-resistant thick steel plate of the invention is composed of the basic components described above and the remainder which is Fe and the inevitable impurities.
    [0036] In the invention, the following components can be added, additionally, according to the desired characteristics.
    Mo: no more than 0.8% [0037] Molybdenum has a temperability-enhancing effect. However, this effect is not sufficiently achieved if the amount added is less than 0.05%. It is therefore preferable to add 0.05% or more of molybdenum. Economic efficiency is impaired if more than 0.8% molybdenum is added. Thus, the molybdenum content, when added, is limited to no more than 0.8%.
    V: no more than 0.2% [0038] Vanadium has a temperability-enhancing effect and also forms V carbides in the form of fine precipitates
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    12/23 nos, which serve to immobilize the heated austenite grains and thereby suppress grain thickening. These effects are not sufficiently achieved if the amount added is less than 0.005%. It is therefore preferable to add 0.005% or more of vanadium. However, the addition of more than 0.2% vanadium results in a decrease in the stiffness of areas affected by welding heat. Thus, the vanadium content, when added, is limited to no more than 0.2%.
    Ti: no more than 0.05% [0039] Titanium forms Ti carbonitrides in the form of fine precipitates, which serve to immobilize heated austenite grains and thus suppress grain growth. In addition, titanium fixes free nitrogen like Ti nitrides and thus suppresses the formation of B nitrides to allow free boron to be used effectively to improve hardenability. However, these effects are not sufficiently achieved if the amount added is less than 0.005%. It is therefore preferable to add 0.005% or more of titanium. However, the addition of more than 0.05% titanium results in a decrease in the stiffness of areas affected by welding heat. Thus, the titanium content, when added, is limited to no more than 0.05%.
    Nd: no more than 1% [0040] Neodymium decreases the amount of sulfur secreted in the grain boundaries by incorporating sulfur as inclusions, and thus improves stiffness at low temperature. However, these effects are not sufficiently achieved if the amount added is less than 0.005%. It is therefore preferable to add 0.005% or more of neodymium. However, the addition of more than 1% neodymium results in a decrease in the stiffness of areas affected by welding heat. Thus, the neodymium content, when added, is limited to not
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    13/23 more than 1%.
    Cu: no more than 1% [0041] Copper has a temperability-enhancing effect. However, this effect is not sufficiently achieved if the amount added is less than 0.05%. It is therefore preferable to add 0.05% or more of copper. If, however, the Cu content exceeds 1%, the tendency is for hot break to occur during heating and welding of the plate. Thus, the copper content, when added, is limited to no more than 1%.
    Ni: no more than 1% [0042] Nickel has an effect of improving rigidity and hardenability. However, this effect is not sufficiently achieved if the amount added is less than 0.05%. It is therefore preferable to add 0.05% or more of nickel. If, however, the Ni content exceeds 1%, economic efficiency decreases. Thus, the nickel content, when added, is limited to no more than 1%.
    W: no more than 1% [0043] Tungsten has a hardening effect. This effect is not sufficiently achieved if the amount added is less than 0.05%. It is therefore preferable to add 0.05% or more of tungsten. However, the addition of more than 1% tungsten causes a decrease in weldability. Thus, the tungsten content, when added, is limited to no more than 1%.
    Ca: no more than 0.005% [0044] Calcium has a form control effect of the inclusion of sulfide for CaS which is a spherical inclusion that hardly extends by lamination, instead of MnS, which is a form of inclusion that readily extends by lamination. However, this effect is not sufficiently achieved if the amount added is less than 0.0005%. It is therefore preferable to add 0.0005% or more of
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    14/23 calcium. However, the addition of more than 0.005% of calcium decreases the purity and results in a deterioration in quality, such as stiffness. Thus, the calcium content, when added, is limited to no more than 0.005%.
    Mg: no more than 0.005% [0045] Magnesium is added as a desulfurizer for hot metal. However, this effect is not sufficiently achieved if the amount added is less than 0.0005%. It is therefore preferable to add 0.0005% or more of magnesium. However, the addition of more than 0.005% of magnesium causes a decrease in purity. Thus, the amount of magnesium, when added, is limited to no more than 0.005%.
    REM: no more than 0.02% [0046] Rare earth metals form REM (O, S) oxysulfides in steel and thus decrease the amount of solute sulfur in crystal grain boundaries to provide characteristics of improved SR crack resistance. However, this effect is not sufficiently achieved if the amount added is less than 0.0005%. It is therefore preferable to add 0.0005% or more of rare earth metals. However, the addition of more than 0.02% of rare earth metals results in an excessive accumulation of REM sulfides in sedimentation zones and causes a decrease in quality. Thus, the amount of rare earth metals, when added, is limited to no more than 0.02%.
    0.03 <Nb + Ti + Al + V <0.14 [0047] Niobium, titanium, aluminum and vanadium form Nb carbonitrides, Ti carbonitrides, Al nitrides and V carbides in shape of fine precipitates, which serve to immobilize the heated austenite grains and thus suppress grain thickening. Detailed studies of the relationship between the contents of these ele
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    15/23 ments and grain size showed that a marked reduction in crystal grain size is achieved and an improvement in stiffness at low temperature is achieved when the contents satisfy 0.03 <Nb + Ti + Al + V <0, 14. Thus, the levels are limited to 0.03 <Nb + Ti + Al + V <0.14. In it, Nb, Ti, Al and V indicate the respective levels (in% by mass) and are 0 when these elements are absent.
    MANUFACTURING CONDITIONS [0048] The shapes of the abrasion-resistant steel plates of the invention are not limited to steel plates and can be any of several other shapes such as tubes, molded steels and rod steels. The temperature and heating rate specified in the manufacturing conditions are parameters that describe the central area of the steel, that is, the center through the thickness of the plate of a thick steel plate, the center through the thickness of the plate of a portion of a molded steel to which the characteristics of the invention apply, or the center of the radial directions of a shank steel. However, the regions in the vicinity of the central area go through substantially the same temperature history and, thus, the above parameters do not strictly describe the temperature conditions for the exact center.
    CASTING CONDITIONS [0049] The present invention is effective for steels manufactured under any casting conditions. It is therefore not necessary to place particular limitations on the casting conditions. That is, the casting of cast steel and rolling of cast steel into sheets can be carried out by any method, without limitation. The use can be made of molten steel by a process such as a converting steelmaking process or an electric steelmaking process, and the sheets produced by such a process
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    16/23 as continuous casting or ingot casting.
    HARDENING BY REHEATING AND TEMPERING [0050] The thick steel plate that has been hot rolled to a prescribed plate thickness is reheated to the transformation point Ac3 or above, and is subsequently tempered by cooling with water from a temperature not lower than the transformation point Ar3 for a temperature of not more than 250 ° C, which forms a martensitic structure in the lath. [0051] If the reheat temperature is below the transformation point Ac3, the part of the ferrite remains unchanged and, as a consequence, the subsequent water cooling stops reaching the target hardness. If the temperature falls below the Ar3 transformation point before cooling with water, part of the austenite is transformed before cooling with water and, consequently, the subsequent cooling with water ceases to reach the target hardness. If the water cooling is finished at a temperature greater than 250 ° C, the crystal can be partially transformed into other structures besides clapboard martensite. Thus, the reheat temperature is limited to no less than the Ac3 transformation point, the water cooling start temperature is limited to no less than the Ar3 transformation point, and the water cooling end temperature is limited to no more than 250 ° C. [0052] In the invention, the transformation point Ac3 (° C) and the transformation point Ar3 (° C) can be obtained using any equations, without limitation. For example, Ac3 = 854 - 180C + 44Si 14Mn - 17.8Ni - 1.7Cr and Ar3 = 910 - 310C - 80Mn - 20Cu - 15Cr - 55Ni - 80Mo. In the equations, the element symbols indicate the levels (in% by mass) in the steel.
    [0053] In the invention, the following limitations on manufacturing conditions can be further adapted in accordance with
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    17/23 the desired characteristics.
    HOT LAMINATION CONDITIONS [0054] When appropriate, the plate is reheated to a temperature that is preferably controlled to not less than 1,100 ° C, more preferably not less than 1,150 ° C, and even more preferably, not less than 1,200 ° C. The purpose of this control is to allow a greater amount of crystals, such as Nb crystals formed on the plate, to be dissolved in the plate and, thus, effectively guarantee a sufficient amount of fine precipitates that will be formed.
    [0055] When hot rolling is controlled, it is preferable that the rolling reduction in a non-recrystallized region is not less than 30%, more preferably not less than 40% and, even more preferably, not less than 50 %. The purpose of lamination in a non-recrystallized region with 30% or more reduction is to form fine precipitates by precipitation induced by deformation of the precipitates such as Nb carbonitrides.
    COOLING [0056] When water cooling is carried out after the hot rolling is completed, it is preferable that the thick steel plate is forced to be cooled to a temperature of no more than 250 ° C. The purpose of this cooling is to restrict the growth of fine precipitates that have been formed by deformation-induced precipitation during lamination.
    TEMPERATURE INCREASE RATE DURING REHEATING [0057] When the reheat temperature during reheating for temper hardening is controlled, it is preferable that the thick steel plate is reheated to the transformation point Ac3 or above, at a rate of no less than 1 ° C / s. The purpose of
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    18/23 if control is to restrict the growth of fine precipitates formed before reheating and the growth of fine precipitates formed during reheating. The heating method can be any one, for example, induction heating, electric heating, infrared radiation heating and atmospheric heating, as long as the desired temperature rise rate is achieved.
    [0058] Under the conditions mentioned above, abrasion-resistant steel plates can be obtained which have fine crystal grains and which present excellent stiffness at low temperature.
    EXAMPLES [0059] A to K steels that have a chemical composition described in Table 1 are melted and cast on the sheets, which are worked under the conditions described in Table 2 to form steel plates. The temperature of the plates was measured with a thermocouple inserted in the central area through the thickness of the plate.
    [0060] Table 2 describes the structures of the steel plates, the average grain sizes of crystal grains surrounded by high angle grain contours that have an orientation difference of 15 ° or more, the densities of the fine precipitates with a diameter of no more than 50 nm, and Brinell hardnesses and Charpy energies absorbed at -40 ° C from the steel plates obtained.
    [0061] To determine the structures in the thick steel plate, a sample was collected from a cross section perpendicular to the rolling direction, the cross section received a specular polish and was etched with a solution of nitric acid methanol, and the structures were identified by observation with an optical microscope at x400 magnification with respect to an area that was 0.5 mm below the surface of the thick steel plate and an area that corresponded to 1/4 of the thickness of the plate.
    Petition 870190099024, of 10/03/2019, p. 33/39
    19/23 [0062] To measure the crystal orientations, a region of 100 pm square that included an area corresponding to 1/4 of the thickness of the plate was analyzed by an Electron Diffraction method (electron later scattering pattern). Although it defines a high angle as having 15 ° or more of difference in the grain contour orientations, the grain diameters surrounded by such grain contours were measured and the simple average of the results was obtained.
    [0063] To determine the numerical density of fine precipitates per unit area, a sample prepared from an area that corresponds to 1/4 of the thickness of the plate by a carbon extraction replica method was observed and photographed by TEM. The number of fine precipitates having a diameter of no more than 50 nm was counted, and the numerical density per 100 pm 2 was obtained.
    [0064] To determine Brinell hardness, an area that was 0.5 mm below the surface of the steel plate was tested in accordance with JIS Z2243 (2008) with a test force of 3000 kgf using a sphere cemented carbide that has a spherical diameter of 10 mm (HBW10 / 3000). The Charpy energy absorbed at -40 ° C was measured in accordance with JIS Z2242 (2005) with respect to the full-size Charpy V-notch samples that were collected from an area of 1/4 of the plate thickness over a direction perpendicular to the lamination direction. The data were obtained from three samples representing the respective conditions and the results were averaged.
    [0065] The target values (the inventive rate) of Brinell hardness were
    361 and above, and these target values of the Charpy energy absorbed at -40 ° C were 27 J and above.
    Petition 870190099024, of 10/03/2019, p. 34/39
    TABLE 1 (in percentage by mass)
    Steels Ç Si Mn Cr Nb B Al T.N P s O Mo V You Nd Ass Ni W Here Mg REM Nb + Ti + Al + V Ac3 (° C) Ar3 (° C) THE 0.14 0.32 0.97 0.38 0.019 0.0010 0.020 0.0035 0.012 0.0016 0.0032 0.014 0.05 829 783 B 0.14 0.38 1.19 0.11 0.022 0.0012 0.027 0.0033 0.011 0.0017 0.0033 0.130.012 0.06 829 759 Ç 0.15 0.37 1.03 0.12 0.021 0.0009 0.033 0.0037 0.010 0.0015 0.0035 0.260.015 0.07 829 759 D 0.15 0.32 0.97 0.75 0.019 0.0013 0.026 0.0028 0.013 0.0021 0.0041 0.36 0.042 0.012 0.10 826 746 AND 0.15 0.31 0.99 0.77 0.021 0.0015 0.051 0.0031 0.011 0.0016 0.0032 0.32 0.041 0.001 0.11 825 747 F 0.16 0.31 0.95 0.91 0.025 0.0009 0.033 0.0033 0.017 0.0019 0.0032 0.51 0.041 0.0120.29 0.28 0.11 819 709 G 0.16 0.30 0.96 1.18 0.032 0.0011 0.032 0.0032 0.013 0.0009 0.0035 0.78 0.043 0.011 0.023 0.23 0.0023 0.0024 0.0025 0.12 823 704 H 0.15 0.36 0.99 0.11 0.001 0.0012 0.020 0.0042 0.009 0.0016 0.0032 0.260.02 829 762 1 0.16 0.33 1.01 0.77 0.004 0.0014 0.023 0.0034 0.015 0.0018 0.0028 0.32 0.039 0.014 0.08 824 742 J 0.15 0.29 0.98 0.77 0.017 0.0012 0.009 0.0035 0.006 0.0017 0.0033 0.37 0.041 0.013 0.08 825 744 K 0.15 0.32 1.02 0.79 0.019 0.0014 0.006 0.0032 0.015 0.0011 0.0035 0.31 0.039 0.002 0.07 825 745
    Note 1: Acs (° C) = 854-180C + 44Si-14Mn-17.8Ni-1.7Cr in which the element symbols indicate the levels (in% by mass).
    Note 2: Ara (° C) = 910-310C-80Mn-20Cu-15Cr-55Ni-80Mo in which the element symbols indicate the levels (in% by mass).
    Note 3: The blanks indicate that the elements were not added and the levels were below the detection limits.
    Note 4: The underlined values are outside the ranges of the invention.
    20/23
    Petition 870190099024, of 10/03/2019, p. 35/39
    TABLE 2
    hi z ω o o < Plate thickness (mm) Temp. heating (° C) Lamination reduction in the non-recrystallized region (%) Temp. water cooling termination (° C) Reheat rate (° C / s) Temp. reheating(° C) Temp. start of water cooling (° C) Temp. cooling termination withwater (° C) Structures in thick steel plate (0.5 mm below the surface and ¼ thick) Average grain size (Pm) Density of fine precipitates (particles / 100 pm 2 ) Brinell hardness (HBW10 / 3000) vE-40° C (J) S $ 5 1 THE 12 1050 40 - 0.3 900 800 200 LM 15 62 402 167 Ex. Inv. 2 B 25 1100 0 - 0.3 900 820 200 LM 16 75 405 123 Ex. Inv. 3 Ç 32 1150 40 - 0.3 900 840 200 LM 14 91 421 98 Ex. Inv. 4 D 60 1150 60 - 0.3 900 850 200 LM 12 123 397 75 Ex. Inv. 5 AND 60 1150 60 - 0.3 900 850 200 LM 11 135 407 77 Ex. Inv. 6 F 100 1200 30 - 0.3 870 840 200 LM 16 132 412 56 Ex. Inv. 7 G 125 1200 30 - 0.3 860 840 200 LM 15 156 423 42 Ex. Inv. 8 H 32 1150 30 - 0.3 900 840 200 LM 65 19 421 12 Ex. Comp. 9 I 32 1150 30 - 0.3 900 840 200 LM 42 27 401 17 Ex. Comp. 10 THE 12 1150 40 - 0.3 900 800 200 LM 9 93 397 192 Ex. Inv. 11 B 25 1100 30 - 0.3 900 820 200 LM 11 102 395 153 Ex. Inv. 12 Ç 32 1150 40 - 0.3 820 760 200 LM + F 9 74 323 125 Ex. Comp. 13 D 60 1150 60 - 0.3 900 720 200 LM + F 10 119 301 102 Ex. Comp. 14 AND 60 1200 60 - 0.3 900 850 200 LM 6 179 402 112 Ex. Inv. 15 F 100 1200 30 200 0.3 870 840 200 LM 14 151 401 73 Ex. Inv. 16 G 125 1200 30 - 2.0 860 840 200 LM 12 161 415 61 Ex. Inv. 17 J 60 1150 60 - 0.3 900 850 200 LM 32 42 411 19 Ex. Comp. 18 K 60 1150 60 - 0.3 900 850 200 LM 45 35 421 17 Ex. Comp.
    Note 1: Underlined values or results are beyond inventive rates.
    Note 2: LM steel plate structures: martensitic clapboard, F: ferrite
    21/23
    Petition 870190099024, of 10/03/2019, p. 36/39
    22/23 [0066] Steel plates No. 1 to 7, 10, 11 and 14 to 16 described in Table 2 satisfy the chemical composition and manufacturing conditions required in the invention. These steel plates are also satisfactory in terms of the average grain size and the density of the fine precipitates required in the invention and reach the target values of Brinell hardness and vE-40 ° C in the invention.
    [0067] heating temperatures used for steel plates paragraph 10 and 14 were increased in the range of the invention when compared to those used for steel plates No. 1 and 5, respectively, resulting in a finer grain size and a higher density of fine precipitates. Consequently, a higher vE-40 ° C was obtained.
    [0068] The steel plate No. 11 satisfied what was required in the invention and involved a higher rolling reduction at a non - recrystallized region than in the steel plate No. 2. Accordingly, the grain size was reduced, the density of fine precipitates has been increased and vE-40 ° C has been improved.
    [0069] The steel plate No. 15 satisfied what was required in the invention and wrapped with cooling water after rolling as compared with the steel plate of No. 6. Therefore, the grain size was reduced, the density of fine precipitates was increased, and the vE-40 ° C was improved.
    [0070] The steel plate No. 16 satisfied the requirements involved in the invention and a greater temperature rise rate during reheating compared with the steel plate No. 7. Therefore, the grain size was reduced, density of fine precipitates has been increased and vE-40 ° C has been improved.
    [0071] On the other hand, the Nb content and the content of (Nb + Ti + Al + V) in the steel plate No. 8, and the Nb content in the steel plate No. 9 were below the lower limits of the bands of the invention. Conse
    Petition 870190099024, of 10/03/2019, p. 37/39
    23/23 therefore, their average grain sizes, the density of fine precipitates and vE-40 ° C did not reach the target values.
    [0072] In the steel plate of No. 12, the region from the surface to a depth of 1/4 of the plate thickness includes a two-phase structure, i.e. ferrite and martensite due to reheating temperature is lower than Ac3. Failure to sufficiently form the martensitic structure in batten resulted in a Brinell hardness below the level required in the invention.
    [0073] In the steel plate of No. 13, the region from the surface to a depth of 1/4 of the plate thickness includes a two-phase structure, i.e. ferrite and martensite due to the cooling start temperature to water that is less than Ar3. Failure to sufficiently form the martensitic structure in batten resulted in a Brinell hardness below the level required in the invention.
    [0074] On the other hand, the steel plates 17 and C 18 has a content of
    Al below the lower limit of the range of the invention. Consequently, their average grain sizes, densities of fine precipitates and vE-40 ° C did not reach the target values.
    权利要求:
    Claims (7)
    [1]
    1. Abrasion resistant thick steel plate with excellent stiffness at low temperature, characterized by the fact that it consists of, in mass%, from C: 0.10 to less than 0.20%, from Si: 0.05 to 0.5%, Mn: 0.5 to 1.5%, Cr: 0.05 to 1.20%, Nb: 0.01 to 0.08%, B: 0.0005 to 0.003% , from Al: 0.01 to 0.08%, from N: 0.0005 to 0.008%, from P: no more than 0.05%, from S: no more than 0.005%, from O: no more than 0.008%, optionally one, or two or more of Mo: not more than 0.8%, of V: not more than 0.2% and Ti: not more than 0.05%, optionally one , or two or more of Nd: no more than 1%, Cu: no more than 1%, Ni: no more than 1%, W: no more than 1%, Ca: no more than 0.005%, Mg: not more than 0.005% and REM: not more than 0.02% (note: REM is an abbreviation for rare earth metal), the balance being Fe and unavoidable impurities, the plate thick steel that includes fine precipitates of 50 nm or less in diameter with a density of 50 or more particles per 100 pm 2 , the thick steel plate that has a martensitic slat structure from the surface of the thick steel plate to at least a depth of 1/4 of the thickness of the plate, the slat martensitic structure that has a size average grain of no more than 20 pm where the average grain size is the average grain size of crystal grains surrounded by high angle grain outlines that have an orientation difference of 15 ° or more, the plate steel that has a Brinell hardness (HBW10 / 3000) of 361 or more, where the contents of Nb, Ti, Al and V satisfy 0.03 <Nb + Ti + Al + V <0.14 where Nb, Ti , Al and V indicate the contents (% by mass) of the respective elements and are 0 when Nb, Ti, Al and V are not added, and in which the energy absorbed by Charpy at - 40 ° C is not less than 27 J .
    [2]
    2. Abrasion resistant thick steel plate with excellent
    Petition 870190099024, of 10/03/2019, p. 9/39
    2/3 low temperature stiffness according to claim 1, characterized by the fact that the thickness of the plate is 6 to 125 mm.
    [3]
    3. Method for the manufacture of an abrasion-resistant thick steel plate with excellent low temperature stiffness, characterized by comprising ingot a steel that has the chemical composition as defined in claim 1, hot-rolling the plate to form a thick plate steel, reheat the thick steel plate to the transformation point Ac3 or above, and subsequently temper the thick steel plate by cooling with water from a temperature of not less than the transformation point Ar3 for a temperature of not more than 250 ° C.
    [4]
    4. Method for manufacturing an abrasion-resistant thick steel plate with excellent low temperature stiffness according to claim 3, characterized by the fact that it additionally comprises reheating the ingot plate at 1100 ° C or above.
    [5]
    5. Method for manufacturing an abrasion-resistant thick steel plate with excellent low temperature stiffness according to claim 3 or 4, characterized by the fact that the reduction of lamination during hot rolling in a non-recrystallized region is not less than 30%.
    [6]
    6. Method for manufacturing an abrasion-resistant thick steel plate with excellent low temperature stiffness according to any of claims 3 to 5, characterized in that it additionally comprises hot-rolled thick plate of the hot-rolled thick plate by cooling with water to a temperature of no more than 250 ° C.
    [7]
    7. Method for manufacturing an abrasion-resistant thick steel plate with excellent low temperature stiffness according to any of claims 3 to 5, characterized by the fact that the reheating of the hot-rolled thick steel plate
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    EP2980250A4|2016-04-27|
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    EP2980250A1|2016-02-03|
    KR20150119117A|2015-10-23|
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    AU2014245635A1|2015-08-20|
    CN105102656A|2015-11-25|
    RU2627830C2|2017-08-11|
    EP2980250B1|2019-09-25|
    JP2014194042A|2014-10-09|
    MX2015013642A|2016-02-18|
    RU2015146264A|2017-05-03|
    JP6007847B2|2016-10-12|
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    法律状态:
    2018-11-13| B06F| Objections, documents and/or translations needed after an examination request according art. 34 industrial property law|
    2019-07-09| B07A| Technical examination (opinion): publication of technical examination (opinion)|
    2020-03-03| B09A| Decision: intention to grant|
    2020-05-05| B16A| Patent or certificate of addition of invention granted|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 19/03/2014, OBSERVADAS AS CONDICOES LEGAIS. |
    优先权:
    申请号 | 申请日 | 专利标题
    JP2013069931A|JP6007847B2|2013-03-28|2013-03-28|Wear-resistant thick steel plate having low temperature toughness and method for producing the same|
    PCT/JP2014/001596|WO2014156079A1|2013-03-28|2014-03-19|Abrasion resistant steel plate having low-temperature toughness, and manufacturing method therefor|
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