• 专利附录
  • 专利说明
  • 权利要求
  • 类似技术
  • 同族专利
  • 引用文献
  • 法律状态
  • 优先权
    • 专利摘要:
    A high strength steel plate, having excellent toughness not only in an inside portion of the steel plate but also in a surface layer of the steel plate, can be stably produced. The steel plate has a chemical composition containing, in mass%, C: 0.080 % or more and 0.200 % or less, Si: 0.40 % or less, Mn: 0.50 % or more and 5.00 % or less, P: 0.015 % or less, S: 0.0050 % or less, Cr: 3.00 % or less, Ni: 5.00 % or less, Al: 0.080 % or less, N: 0.0070 % or less, and B: 0.0030 % or less, the balance being Fe and inevitable impurities, wherein an equivalent carbon content CeqIIW is 0.57 % or more, an area fraction of bainite in the surface layer is 10 % or more, and a yield stress is 620 MPa or more.
    公开号:EP3680358A1
    申请号:EP18853601.5
    申请日:2018-09-07
    公开日:2020-07-15
    发明作者:Shigeki Kitsuya；Katsuyuki Ichimiya
    申请人:JFE Steel Corp；
    IPC主号:C21D1-00
    专利说明:
    [0001] The present disclosure relates to a thick steel plate having a thickness of 100 mm or more among steel plates used for steel structures such as buildings, bridges, shipbuilding, marine structures, construction machinery, tanks, and penstocks, and a method of producing the same. BACKGROUND
    [0002] When steel materials are used for structures such as buildings, bridges, shipbuilding, marine structures, construction machinery, tanks, and penstocks, the steel materials are joined by welding according to the shape of the structure to obtain a desired shape. In recent years, the size of such steel structures has been greatly increased, and the strength and thickness of steel materials used have also been increased. For example, Kouzaburou Ootani and four others, "Development of extremely thick (210 mm) 800N/mm2 grade steel plates for racks of jack-up rigs", Nippon Steel Technical Report, 1993, No. 348, pages 10 to 16 (NPL 1) reports an extremely thick steel plate having a thickness of 210 mm that is developed for racks of jack-up rigs. NPL 1 describes a chemical composition and production conditions for guaranteeing the toughness of the mid-thickness part of the thick steel plate. CITATION LISTNon-patent Literature
    [0003] NPL 1: Kouzaburou Ootani and four others, "Development of extremely thick (210 mm) 800N/mm2 grade steel plates for racks of jack-up rigs", Nippon Steel Technical Report, 1993, No. 348, pages 10 to 16 SUMMARY(Technical Problem)
    [0004] A high strength steel plate having a thickness of 100 mm or more is usually produced by performing quenching and tempering after hot rolling to obtain high toughness in addition to high strength. When producing a thick steel plate in this way, the cooling rate in the quenching process after hot rolling is lower in an inside portion of the steel plate, which is inside a surface layer of the steel plate, than in the surface layer. Therefore, a microstructure with relatively low strength such as ferrite tends to be formed in the inside portion of the steel plate. In order to suppress the generation of such a low-strength microstructure in the inside portion of the steel plate, it is necessary to add a large amount of alloying element.
    [0005] The surface layer of the steel plate here refers to a region on the front surface side and a region on the back surface side, which extend respectively from the front surface and the back surface of the steel plate to a position of at one quarter in height of the plate thickness (1/4 t, where "t" represents the plate thickness) in the thickness direction, and the portion inside the surface layer (including 1/4 t) is the inside portion of the steel plate.
    [0006] In particular, in order to achieve the strength and toughness in the inside portion of the thick steel plate, it is important to form bainite or a mixed microstructure of bainite and martensite in the inside portion of the steel plate during quenching, and it is necessary to add a large amount of alloying elements such as Mn, Ni, Cr, and Mo.
    [0007] On the other hand, when a large amount of the above-mentioned alloying elements is added, the surface layer of the steel plate, which has a higher cooling rate than the inside portion of the steel plate during quenching, is formed with a martensite microstructure inferior in toughness. Therefore, the toughness of the surface layer of the steel plate is lower than that of the inside portion of the steel plate even after tempering.
    [0008] However, as NPL 1 does not mention the toughness deterioration in the surface layer of the steel plate that is rapidly cooled, and no attention has been paid on this problem so far.
    [0009] It could thus be helpful to provide a method of stably producing a high strength steel plate having excellent toughness not only in the inside portion of the steel plate but also in the surface layer of the steel plate. (Solution to Problem)
    [0010] In order to solve the above problem, we have intensively studied thick steel plates having a yield stress of 620 MPa or more and a thickness of 100 mm or more with respect to microstructure control factors for suppressing a reduce in toughness in the surface layer of the steel plate and a reduce in strength in the inside portion of the steel plate, and found the following discoveries I to III.
    [0011] I. In order to obtain high strength while maintaining good toughness in the inside portion of a steel plate where the cooling rate is significantly lower than the surface layer of the steel plate during quenching, it is important that the microstructure be a martensite microstructure and/or a bainite microstructure even if the quenching is performed at a low cooling rate. For this purpose, it is necessary to select an appropriate chemical composition and to make the equivalent carbon content 0.57 % or more.
    [0012] II. When subjecting a steel plate having the selected chemical composition to quenching, a martensite microstructure that is disadvantageous for guaranteeing toughness is formed in the surface layer of the steel plate where the cooling rate is high during the quenching, and the microstructure unit of the martensite microstructure called block or packet once formed does not change even after tempering, which renders it difficult to guarantee stable toughness.
    [0013] III. In order to suppress the formation of a tempered martensite single-phase microstructure that is disadvantageous to toughness, it is important to control the average cooling rate at a range of 0.2 °C/s to 10 °C/s when the surface layer of the steel plate and the inside portion of the steel plate are in a temperature range from (Ar3 transformation point + 50) °C or higher to (Ar3 transformation point - 20) °C or lower so that bainite is formed at a predetermined ratio or more in the surface layer of the steel plate.
    [0014] The present disclosure is based on the above discoveries. The primary features of the present disclosure are as follows.1. A steel plate comprising a chemical composition containing (consisting of), in mass%,C: 0.080 % or more and 0.200 % or less,Si: 0.40 % or less,Mn: 0.50 % or more and 5.00 % or less,P: 0.015 % or less,S: 0.0050 % or less,Cr: 3.00 % or less,Ni: 5.00 % or less,Al: 0.080 % or less,N: 0.0070 % or less, andB: 0.0030 % or less in a range satisfying the following formula (1),C + Mn / 6 + Ni / 15 + Cr / 15 ≥ 0.57
    [0015] According to the present disclosure, it is possible to stably produce a high strength steel plate having excellent toughness not only in the inside portion of the steel plate but also in the surface layer of the steel plate. DETAILED DESCRIPTION[Chemical composition]
    [0016] The following describes the production conditions of a steel plate of an embodiment of the present disclosure. The reasons for limiting the chemical composition of steel are described first. In the present specification, when components are expressed in "%", it refers to "mass%" unless otherwise specified. C: 0.080 % or more and 0.200 % or less
    [0017] C is an element that is useful for obtaining the strength required for structural-use steel at low cost. To achieve this effect, the C content needs to be 0.080 % or more. On the other hand, when the C content exceeds 0.200 %, the toughness of base metal and weld is significantly deteriorated. Therefore, the upper limit is set to 0.200 %. The C content is preferably 0.080 % or more and 0.140 % or less. Si: 0.40 % or less
    [0018] Si is preferably added in an amount of 0.05 % or more for deoxidation. However, when the Si content exceeds 0.40 %, the toughness of base metal and heat-affected zone is significantly deteriorated. Therefore, the Si content is set to 0.40 % or less. The Si content is preferably 0.05 % or more and 0.30 % or less. The Si content is more preferably 0.05 % or more and 0.25 % or less. Mn: 0.50 % or more and 5.00 % or less
    [0019] Mn is added from the viewpoint of guaranteeing the strength of base metal. However, when the Mn content is less than 0.50 %, the effect is insufficient. On the other hand, when the Mn content exceeds 5.00 %, the toughness of base metal is deteriorated, and central segregation is promoted. Therefore, the upper limit is set to 5.00 %. The Mn content is preferably 0.60 % or more and 2.00 % or less. The Mn content is more preferably 0.60 % or more and 1.60 % or less. P: 0.015 % or less
    [0020] When the P content exceeds 0.015 %, the toughness of base metal and heat-affected zone is significantly deteriorated. Therefore, the P content is set to 0.015 % or less. The P content is preferably 0.010 % or less. It is difficult to reduce the content to less than 0.001 % in industrial-scale production, so that a content of 0.001 % or more is acceptable. S: 0.0050 % or less
    [0021] When the S content exceeds 0.0050 %, the toughness of base metal and heat-affected zone is significantly deteriorated. Therefore, the S content is set to 0.0050 % or less. The S content is preferably 0.0010 % or less. It is difficult to reduce the content to less than 0.0001 % in industrial-scale production, so that a content of 0.0001 % or more is acceptable. Cr: 3.00 % or less
    [0022] Cr is an element that is effective for increasing the strength of base metal, and Cr is preferably added in an amount of 0.10 % or more. However, a large amount of Cr deteriorates the weldability. Therefore, the Cr content is set to 3.00 % or less. The Cr content is preferably 0.10 % or more and 2.00 % or less. Ni: 5.00 % or less
    [0023] Ni is a beneficial element that improves the strength of steel and the toughness of heat-affected zone, and Ni is preferably added in an amount of 0.50 % or more. However, when Ni is added more than 5.00 %, the economic efficiency is significantly decreased. Therefore, the Ni content is set to 5.00 % or less. The Ni content is preferably 0.50 % or more and 4.00 % or less. Al: 0.080 % or less
    [0024] Al is added to sufficiently deoxidize the molten steel. However, when Al is added more than 0.080 %, a large amount of Al dissolves in the base metal and the toughness of base metal deteriorates. Therefore, the Al content is set to 0.080 % or less. The Al content is preferably 0.030 % or more and 0.080 % or less. The Al content is more preferably 0.030 % or more and 0.060 % or less. N: 0.0070 % or less
    [0025] N has an effect of refining the microstructure and improving the toughness of base metal and heat-affected zone by forming nitrides with Al or other elements. Therefore, N is preferably added in an amount of 0.0020 % or more. However, when N is added more than 0.0070 %, the amount of nitride precipitated in the base metal is increased, the toughness of base metal is significantly deteriorated, and coarse carbonitrides are formed in the heat-affected zone to deteriorate the toughness. Therefore, the N content is set to 0.0070 % or less. The N content is preferably 0.0050 % or less, and more preferably 0.0040 % or less. Note that the N content may be 0 %. B: 0.0030 % or less
    [0026] B has an effect of suppressing the ferrite transformation from grain boundaries and improving the quench hardenability by segregating at austenite grain boundaries. Therefore, B is preferably added in an amount of 0.0003 % or more. On the other hand, when B is added more than 0.0030 %, it precipitates as carbonitrides, deteriorates the quench hardenability, and causes a decrease in toughness. Therefore, the B content is set to 0.0030 % or less. The B content is preferably 0.0003 % or more and 0.0030 % or less. The B content is more preferably 0.0005 % or more and 0.0020 % or less. Equivalent Carbon Content CeqIIW
    [0027] In the present disclosure, in order to guarantee a yield stress of 620 MPa or more and good toughness in the inside portion of a steel plate, particularly in the inside portion of a steel plate having a thickness of 100 mm or more, it is necessary to design an appropriate chemical composition and to adjust the chemical composition to the range satisfying the following formula (1) regarding equivalent carbon content CeqIIW. This is because, in the case where the equivalent carbon content does not satisfy the following formula (1), ferrite, which is inferior in strength, or the like tends to be formed, rendering it difficult to stably guarantee a desired strength.C + Mn / 6 + Ni / 15 + Cr / 15 ≥ 0.57
    [0028] The basic components of the present disclosure have been described above. The balance other than the above-mentioned components is Fe and inevitable impurities. In the present disclosure, other elements may be optionally added as appropriate.
    [0029] Specifically, in order to further increase the strength and toughness, it is possible to contain at least one selected from the group consisting of Cu: 0.50 % or less, Mo: 1.50 % or less, Nb: 0.100 % or less, V: 0.200 % or less, and Ti: 0.005 % or more and 0.020 % or less.
    [0030] In this case, the chemical composition is adjusted so that the equivalent carbon content CeqIIW is in the range satisfying the following formula (2) rather than the above formula (1).C + Mn / 6 + Cu + Ni / 15 + Cr + Mo + V / 15 ≥ 0.57
    [0031] Cu can improve the strength of steel without deteriorating the toughness. However, when Cu is added more than 0.50 %, cracking occurs in the surface layer of the steel plate during hot working. Therefore, when Cu is contained, the content is set to 0.50 % or less. The Cu content is preferably 0.03 % or more and 0.40 % or less. Mo: 1.50 % or less
    [0032] Mo is an element that effectively strengthens the base metal. However, when Mo is added more than 1.50 %, the hardness is increased, and the toughness is decreased due to precipitation of alloy carbides. Therefore, when Mo is contained, the content is set to 1.50 % or less. The Mo content is preferably 0.02 % or more and 0.80 % or less. Nb: 0.100 % or less
    [0033] Nb is useful because it has an effect of increasing the strength of base metal. However, when Nb is added more than 0.100 %, the toughness of base metal is significantly deteriorated. Therefore, when Nb is contained, the upper limit is set to 0.100 %. The Nb content is preferably 0.025 % or less. In addition, when the content is less than 0.003 %, the effect of improving the properties cannot be obtained. Therefore, when Nb is contained, the content is set to 0.003 % or more. V: 0.200 % or less
    [0034] V is effective in improving the strength and toughness of base metal and reducing solute N by precipitating as VN. However, when V is added more than 0.200 %, the toughness is deteriorated due to precipitation of hard VC. Therefore, when V is contained, the content is set to 0.200 % or less. The V content is preferably 0.010 % or more and 0.100 % or less. Ti: 0.005 % or more and 0.020 % or less
    [0035] Ti forms TiN during heating, effectively suppresses the coarsening of austenite, and improves the toughness of base metal and heat-affected zone. However, when Ti is added more than 0.020 %, the Ti nitride coarsens and the toughness of base metal decreases. Therefore, when Ti is contained, the content is set to 0.005 % or more and 0.020 % or less. The Ti content is preferably 0.008 % or more and 0.015 % or less.
    [0036] In order to further improve the material properties, it is possible to contain at least one selected from the group consisting of Mg: 0.0005 % or more and 0.0100 % or less, Ta: 0.010 % or more and 0.200 % or less, Zr: 0.0050 % or more and 0.1000 % or less, Y: 0.001 % or more and 0.010 % or less, Ca: 0.0005 % or more and 0.0050 % or less, and REM: 0.0005 % or more and 0.0200 % or less. Mg: 0.0005 % or more and 0.0100 % or less
    [0037] Mg forms stable oxides at high temperatures, effectively suppresses the coarsening of prior γ grains in the heat-affected zone, and effectively improves the toughness of weld. However, when the content is less than 0.0005 %, a clear effect cannot be obtained, and when the content exceeds 0.0100 %, the amount of inclusions increases and the toughness decreases. Therefore, when Mg is contained, the content is set to 0.0005 % or more and 0.0100 % or less. The Mg content is preferably 0.0005 % or more and 0.0050 % or less. Ta: 0.010 % or more and 0.200 % or less
    [0038] Ta is effective in improving the strength. However, when the content is less than 0.010 %, a clear effect cannot be obtained, and when the content exceeds 0.200 %, the toughness decreases due to formation of precipitates. Therefore, when Ta is contained, the content is set to 0.010 % or more and 0.200 % or less. Zr: 0.0050 % or more and 0.1000 % or less
    [0039] Zr is an element effective in improving the strength. However, when the content is less than 0.0050 %, a clear effect cannot be obtained, and when the content exceeds 0.1000 %, coarse precipitates are formed to deteriorate the toughness. Therefore, when Zr is contained, the content is set to 0.0050 % or more and 0.1000 % or less. Y: 0.001 % or more and 0.010 % or less
    [0040] Y forms stable oxides at high temperatures, effectively suppresses the coarsening of prior γ grains in the heat-affected zone, and effectively improves the toughness of weld. However, when the content is less than 0.001 %, the effect cannot be obtained, and when the content exceeds 0.010 %, the amount of inclusions increases and the toughness decreases. Therefore, when Y is contained, the content is set to 0.001 % or more and 0.010 % or less. Ca: 0.0005 % or more and 0.0050 % or less
    [0041] Ca is an element useful for controlling the morphology of sulfide inclusions. To achieve this effect, the Ca content needs to be 0.0005 % or more. However, when Ca is added more than 0.0050 %, the cleanliness is lowered, and the toughness is deteriorated. Therefore, when Ca is contained, the content is set to 0.0005 % or more and 0.0050 % or less. The Ca content is preferably 0.0005 % or more and 0.0025 % or less. REM: 0.0005 % or more and 0.0200 % or less
    [0042] REM (rare earth metal), like Ca, has an effect of improving the material properties by forming oxides and sulfides in the steel. To achieve this effect, the REM content needs to be 0.0005 % or more. However, when REM is added more than 0.0200 %, the effect is saturated. Therefore, when REM is contained, the content is set to 0.0005 % or more and 0.0200 % or less. The REM content is preferably 0.0005 % or more and 0.0050 % or less. [Microstructure]
    [0043] In the present disclosure, it is important that the area fraction of bainite in the surface layer of the steel plate be 10 % or more. When the surface layer of the steel plate has such a microstructure, the surface layer of the steel plate can also obtain excellent toughness. The area fraction of bainite in the surface layer of the steel plate is preferably 20 % or more. The balance is tempered martensite, ferrite, or the like.
    [0044] It is preferable that, in addition to the surface layer of the steel plate, the inside portion of the steel plate also have an area fraction of bainite of 10 % or more. When the inside portion of the steel plate also has such a microstructure, it is possible to obtain a steel plate where the difference in properties between the surface layer of the steel plate and the inside portion of the steel plate is small. The area fraction of bainite in the inside portion of the steel plate is more preferably 20 % or more.
    [0045] The evaluation of the area fraction in the microstructure of the surface layer of the steel plate and the area fraction in the microstructure of the inside portion of the steel plate can be performed by collecting a sample of the cross section in the rolling direction of a quenched steel material, revealing the microstructure with a nital etching solution, observing five or more locations at 200 times magnification under an optical microscope, and determining the area fraction in each of the microstructures such as bainite by image analysis. For the surface layer of the steel plate, a sample of the cross section in the rolling direction having a thickness of 15 mm is collected centering on the position of 1/8 thickness (1/8 t). For the inside portion of the steel plate, a sample of the cross section in the rolling direction having a thickness of 15 mm is collected centering on the position of 3/8 thickness (3/8 t).
    [0046] In order to obtain a microstructure where at least the area fraction of bainite in the surface layer of the steel plate is 10 % or more, it is necessary to subjecting a steel material whose chemical composition has been adjusted to the above range to hot rolling to obtain a hot-rolled steel plate, cooling the hot-rolled steel plate, then heating the steel plate to a temperature range of AC3 transformation point or higher and 1050 °C or lower, and then subjecting the steel plate to cooling treatment where the average cooling rate in a temperature range from (Ar3 transformation point + 50) °C or higher to (Ar3 transformation point - 20) °C or lower is 0.2 °C/s to 10 °C/s to cool the steel plate to 350 °C or lower. It is important that both the surface layer of the hot-rolled steel plate and the inside portion of the steel plate satisfy the specified temperature conditions. Details will be described later. [Toughness]
    [0047] Researchers have not paid too much attention to the toughness of the surface layer of a steel plate so far. However, the surface layer is being required to have the same toughness as that of the inside portion of a steel plate in response to growing demands for improving the safety of structures. For the steel plate of the present disclosure, when the toughness difference between the surface layer of the steel plate and the inside portion of the steel plate is evaluated by ductile-brittle fracture appearance transition temperature (vTrs), the difference in vTrs is preferably within 20 °C. This is because in this case, the toughness of the surface layer of the steel plate and the toughness of the inside portion of the steel plate can be evaluated as substantially the same. The vTrs here is evaluated with the method described in JIS Z2242. The reason why the difference in vTrs is set within 20 °C is that, in the case of evaluating the toughness by vTrs, the value of the difference may be up to about 20 °C due to errors in the measurement of brittle fracture appearance ratio, even if the toughness is at the same level. Therefore, it is set 20 °C within which the toughness can be considered substantially equivalent. [Yield stress]
    [0048] In the present disclosure, the yield stress of the inside portion of the steel plate is 620 MPa or more. The reason is that, in order to contribute to increasing the size of a structure, it is required to have a yield stress of 620 MPa or more.
    [0049] Next, a method of producing the steel plate of the present disclosure will be described. Unless otherwise specified, the temperature in the following description refers to the temperature of the mid-thickness part (1/2 t). [Steel material]
    [0050] Molten steel having the above-described chemical composition is obtained by steelmaking with a normal method such as using a converter, an electric heating furnace or a vacuum melting furnace, and is made into a steel material such as a slab or billet with a normal casting method such as a continuous casting method or an ingot casting method. If there are restrictions on, for example, rolling mill load, the steel material may be further forged or subjected to blooming to reduce the thickness of the steel material. [Hot rolling]
    [0051] The steel material is subjected to hot rolling. In order to achieve both the toughness of the surface layer of the steel plate and the strength and toughness of the inside portion of the steel plate, it is effective to promote the recrystallization in the γ region to refine the prior γ grains during the hot rolling. Therefore, the rolling finish temperature in the hot rolling is preferably Ar3 point or higher.
    [0052] The Ar3 transformation point may be the value calculated from the formula (4) described later. [Cooling after hot rolling]
    [0053] The hot-rolled steel plate is subjected to air cooling or accelerated cooling. Accelerated cooling is particularly effective in improving the toughness. This is because accelerated cooling shortens the residence time at high temperature ranges as compared with the case of air cooling, refines crystal grains and suppresses coarsening of precipitates. Therefore, in the case of accelerated cooling, it is performed until the temperature is lower than Ar3 point. The cooling during the accelerated cooling is performed with water or air blast, and in either case, the cooling rate in the steel plate surface is preferably 0.1 °C/s or more. [Heating temperature after hot rolling: AC3 transformation point or higher and 1050 °C or lower]
    [0054] The cooled hot-rolled steel plate is heated to AC3 transformation point or higher and 1050 °C or lower. The steel plate is heated to AC3 transformation point or higher, because this makes the steel uniform into an austenite single phase. The reheating temperature is set to 1050 °C or lower, because a high reheating temperature exceeding 1050 °C causes coarsening of austenite grains, which significantly deteriorates the toughness of base metal. It is preferably AC3 transformation point or higher and 1000 °C or lower. It is more preferably AC3 transformation point or higher and 950 °C or lower.
    [0055] The value calculated from the following formula (3) is used as the AC3 transformation point.Ac 3 = 937.2 − 476.5 C + 56 Si − 19.7 Mn − 16.3 Cu − 26.6 Ni − 4.9 Cr + 38.1 Mo + 124.8 V + 136.3 Ti + 198.4 Al + 3315 B
    [0056] Cooling treatment is performed after the heating. During the cooling treatment, when the surface layer of the steel plate and the inside portion of the steel plate are being cooled to 350 °C or lower, it is important to perform the cooling treatment so that the average cooling rate of each of the surface layer of the steel plate and the inside portion of the steel plate in the temperature range from (Ar3 transformation point + 50) °C or higher to (Ar3 transformation point - 20) °C or lower is 0.2 °C/s to 10 °C/s. Performing such cooling treatment can form a microstructure where the area fraction of bainite is 10 % or more in the surface layer of the steel plate and significantly improve the toughness of the surface layer of the steel plate. In the same way, a microstructure with 10 % or more of bainite can also be formed in the inside portion of the steel plate.
    [0057] The cooling rate can be controlled by, for example, adjusting the flow rate of water, performing the cooling intermittently, or performing air blast cooling.
    [0058] Specifically, the average cooling rate in the surface layer of the steel plate and in the inside portion of the steel plate is controlled by deriving the cooling method, water adjustment and intermittent conditions by, for example, simulation to achieve the desired cooling rate.
    [0059] The temperature in the surface layer of the steel plate and in the inside portion of the steel plate can be determined by, for example, simulation calculation based on the thickness, surface temperature, cooling conditions, and the like. For example, the temperature from the surface layer of the steel plate to the inside portion of the steel plate can be determined by calculating the temperature distribution in the thickness direction using the finite difference method.
    [0060] The value calculated from the following formula (4) is used as the Ar3 transformation point.Ar 3 = 910 − 310 C − 80 Mn − 20 Cu − 15 Cr − 55 Ni − 80 Mo
    [0061] The stop temperature of the cooling is set to 350 °C or lower. This is because when the temperature is lowered to 350 °C or lower, the transformation of the whole steel plate is completed, and a uniform microstructure is obtained.
    [0062] The cooling method is generally water cooling in industrial terms. However, the cooling method may be other than water cooling, such as gas cooling. [Tempering]
    [0063] After the above-described rapid cooling, tempering may be performed in a temperature range of 450 °C or higher and 700 °C or lower as necessary. When the temperature is lower than 450 °C, the effect of removing residual stress is small. On the other hand, when the temperature is higher than 700 °C, various carbides are precipitated, the microstructure of the base metal is coarsened, and the strength and the toughness are significantly deteriorated.
    [0064] Steel may be repeatedly quenched in industrial terms for the purpose of improving the toughness of the steel. In the present disclosure, it is also acceptable to perform quenching repeatedly. Note that during the final quenching, it is preferable to perform cooling so that the average cooling rate of the surface layer of the steel plate and the inside portion of the steel plate is 0.2 °C/s or more and 10 °C/s or less in a temperature range from (Ar3 transformation point + 50) °C or higher to (Ar3 transformation point - 20) °C or lower, and then cool the steel plate to 350 °C or lower and temper the steel plate at 450 °C or higher and 700 °C or lower. EXAMPLES
    [0065] Steel Nos. 1 to 31 as listed in Table 1 were obtained by steelmaking and were made into slabs. Subsequently, the slabs were made into steel plates having a thickness of 100 mm or more and 240 mm or less under the production conditions listed in Table 2. Subsequently, the steel plates were subjected to cooling treatment and tempering treatment to obtain thick steel plates of Sample Nos. 1 to 37, and the thick steel plates were subjected to the following tests.
    [0066] Round bar tensile test pieces with a diameter of 12.5 mm were taken at a length of 50 mm in the direction perpendicular to the rolling direction from the 1/8 thickness (1/8 t) part and the 1/4 thickness (1/4 t) part of each steel plate, and their yield stress (YS) and tensile strength (TS) were measured. The yield stress (YS) and the tensile strength (TS) were measured according to JIS Z2241. [Charpy impact test]
    [0067] Fifteen 2-mm V-notch Charpy test pieces whose longitudinal direction was the rolling direction were taken from each steel plate at the position 2 mm below the surface layer of the steel plate and at the 1/4 thickness (1/4 t) part respectively. The vTrs (ductile-brittle fracture appearance transition temperature) of each test piece was evaluated according to JIS Z 2242.
    [0068] The test results are listed in Table 2. From these results, it is understood that, for each of the steel plates of Examples (Sample Nos. 1 to 22) in which the chemical composition of the steel and the microstructure conform to the present disclosure, the YS of the 1/4 t part is 620 MPa or more, the TS of the 1/4 t part is 720 MPa or more, the toughness (vTrs) of the surface layer of the steel plate and the 1/4 t part are lower than -30 °C, and the difference in vTrs is within 20 °C. These results explain that the strength of the base metal is favorable and the difference in toughness between the surface layer of the steel plate and the inside portion of the steel plate is small, indicating the excellent toughness in the thickness direction throughout from the surface layer of the steel plate to the inside portion of the steel plate.
    [0069] On the other hand, the steel plates of Comparative Examples (Sample Nos. 23 to 32) deviating from the chemical composition or the microstructure of the present disclosure are inferior in any of the following properties: the YS of the inside portion of the steel plate is less than 620 MPa, the TS is less than 720 MPa, or the toughness (vTrs) of the surface layer of the steel plate and the 1/4 t part is -30 °C or higher, or the vTrs difference exceeds 20 °C.
    [0070] In addition, it is understood from Sample Nos. 33 to 37 that, for the steel plates where the chemical composition of the steel conforms to the present disclosure yet the production conditions do not conform to the present disclosure, they are inferior in one or more of the properties of YS, TS, toughness, and toughness difference. INDUSTRIAL APPLICABILITY
    [0071] According to the present disclosure, it is possible to obtain a thick steel plate having a thickness of 100 mm or more, a yield stress of 620 MPa or more in the base metal, excellent toughness in the surface layer of the steel plate, excellent strength and toughness in the inside portion of the steel plate, and excellent production stability, and to greatly contributes to increasing the size of steel structures and improving the safety of steel structures.
    权利要求:
    Claims (6)
    [0001] A steel plate comprising a chemical composition containing, in mass%,C: 0.080 % or more and 0.200 % or less,Si: 0.40 % or less,Mn: 0.50 % or more and 5.00 % or less,P: 0.015 % or less,S: 0.0050 % or less,Cr: 3.00 % or less,Ni: 5.00 % or less,Al: 0.080 % or less,N: 0.0070 % or less, andB: 0.0030 % or less in a range satisfying the following formula (1),C + Mn / 6 + Ni / 15 + Cr / 15 ≥ 0.57
    [0002] The steel plate according to claim 1, whereinthe chemical composition further contains, in mass%, at least one selected from the group consisting ofCu: 0.50 % or less,Mo: 1.50 % or less,Nb: 0.100 % or less,V: 0.200 % or less, andTi: 0.005 % or more and 0.020 % or less in a range satisfyingthe following formula (2) rather than the formula (1),C + Mn / 6 + Cu + Ni / 15 + Cr + Mo + V / 15 ≥ 0.57
    [0003] The steel plate according to claim 1 or 2, whereinthe chemical composition further contains, in mass%, at least one selected from the group consisting ofMg: 0.0005 % or more and 0.0100 % or less,Ta: 0.010 % or more and 0.200 % or less,Zr: 0.0050 % or more and 0.1000 % or less,Y: 0.001 % or more and 0.010 % or less,Ca: 0.0005 % or more and 0.0050 % or less, and REM: 0.0005 % or more and 0.0200 % or less.
    [0004] A method of producing a steel plate, comprisingpreparing a steel material having a chemical composition containing, in mass%,C: 0.080 % or more and 0.200 % or less,Si: 0.40 % or less,Mn: 0.50 % or more and 5.00 % or less,P: 0.015 % or less,S: 0.0050 % or less,Cr: 3.00 % or less,Ni: 5.00 % or less,Al: 0.080 % or less,N: 0.0070 % or less, andB: 0.0030 % or less in a range satisfying the following formula (1),C + Mn / 6 + Ni / 15 + Cr / 15 ≥ 0.57
    [0005] The method of producing a steel plate according to claim 4, whereinthe chemical composition further contains, in mass%, at least one selected from the group consisting ofCu: 0.50 % or less,Mo: 1.50 % or less,Nb: 0.100 % or less,V: 0.200 % or less, andTi: 0.005 % or more and 0.020 % or less in a range satisfying the following formula (2) rather than the formula (1),C + Mn / 6 + Cu + Ni / 15 + Cr + Mo + V / 15 ≥ 0.57
    [0006] The method of producing a steel plate according to claim 4 or 5, whereinthe chemical composition further contains, in mass%, at least one selected from the group consisting ofMg: 0.0005 % or more and 0.0100 % or less,Ta: 0.010 % or more and 0.200 % or less,Zr: 0.0050 % or more and 0.1000 % or less,Y: 0.001 % or more and 0.010 % or less,Ca: 0.0005 % or more and 0.0050 % or less, andREM: 0.0005 % or more and 0.0200 % or less.
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    同族专利:
    公开号 | 公开日
    SG11202001759QA|2020-03-30|
    KR20200034770A|2020-03-31|
    EP3680358A4|2020-07-15|
    WO2019050010A1|2019-03-14|
    JPWO2019050010A1|2019-11-07|
    CN111051555A|2020-04-21|
    JP6795083B2|2020-12-02|
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