CN109182919B - Production method of multiphase structure high-toughness ship plate steel EH47 - Google Patents

Production method of multiphase structure high-toughness ship plate steel EH47 Download PDF

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CN109182919B
CN109182919B CN201811401096.7A CN201811401096A CN109182919B CN 109182919 B CN109182919 B CN 109182919B CN 201811401096 A CN201811401096 A CN 201811401096A CN 109182919 B CN109182919 B CN 109182919B
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steel
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CN109182919A (en
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罗登
于青
肖大恒
刘丹
王振
冯赞
欧阳藩
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Hunan Valin Xiangtan Iron and Steel Co Ltd
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    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/02Ferrous alloys, e.g. steel alloys containing silicon
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226Hot rolling
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/002Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/06Ferrous alloys, e.g. steel alloys containing aluminium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00Microstructure comprising significant phases
    • C21D2211/001Austenite
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00Microstructure comprising significant phases
    • C21D2211/002Bainite
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00Microstructure comprising significant phases
    • C21D2211/005Ferrite

Abstract

The multiphase structure high-toughness ship plate steel EH47 comprises the following chemical components, by weight, 0.04-0.08% of carbon, 0.15-0.35% of silicon, 1.60-1.80% of manganese, 0.015% or less of phosphorus, 0.005% or less of sulfur, 0.03-0.04% of niobium, 0.008-0.02% of titanium, 0.015-0.05% of aluminum, 0.30-0.40% of nickel, 0.25-0.35% of copper, 0.15-0.25% of chromium, and the balance of Fe and inevitable impurities. The process steps comprise smelting, continuous casting, rolling, relaxation and cooling. The method breaks through the compression ratio limitation of the continuous casting billet rolled by the traditional TMCP process, and does not need to add a heat treatment process; the high-toughness steel plate with the low-temperature impact requirement below-40 ℃ is produced, the maximum thickness can reach 100mm, and the product can be widely applied to the manufacturing of thick plates in various fields such as shipbuilding, maritime work, wind power, bridges, buildings, engineering machinery and the like; the method can be realized by utilizing the existing equipment and process conditions of a steel mill, not only does not need to increase investment and equipment modification, but also improves the production efficiency, saves energy and reduces consumption.

Description

Production method of multiphase structure high-toughness ship plate steel EH47
Technical Field
The invention belongs to the technical field of metallurgy, and relates to a production method of multiphase structure high-toughness ship plate steel EH 47.
Background
When a continuous casting billet is adopted to produce a medium plate product with a high toughness requirement, only when an austenite structure entering phase transformation is uniformly refined in a traditional rolling mode, a ferrite pearlite structure or a bainite structure after the transformation of the product has good strength and toughness, so that the traditional TMCP process can only be used for rolling a thin plate with the thickness of below 50 mm. For the thick plate with the thickness of more than 50mm, because of the limitation of a compression ratio, the original austenite grains can not be fully recrystallized and refined in the rolling process, the structure is generally thicker and the toughness is poor, and the toughness matching of the thick plate can be ensured only by adding a heat treatment process, so that the production cost is increased, and the production period is also prolonged. In addition, the prior art of the international TMCP process for producing medium plate products is generally a single-phase matrix structure of pure ferrite or pure bainite, although a mixed structure or a multi-phase structure of ferrite and bainite can be obtained sometimes by controlling steel rolling parameters, the medium plate products are generally a grain-shell structure with relatively coarse grains, and the strength is improved, but the plasticity and the toughness are poor.
Chinese patent 200680039706.2 discloses a method for producing TRIP steel (transformation induced plasticity steel) by hot continuous rolling process, which adds higher carbon in the composition design and has no requirement for Ni content, the composition system is only suitable for producing hot continuous rolled or cold rolled strip steel or coiled plate with thickness less than or equal to 16mm, and is not suitable for single rolled medium plate. Chinese patent 201180011390.7 discloses a "multiphase structure stainless steel sheet and steel strip and their manufacturing method", which is formed by off-line multiphase annealing of a cold rolled stainless steel sheet or steel strip to form a multiphase structure of ferrite and martensite, which is significantly different from the on-line rolling of the present invention. Chinese patent 201410791739.9 discloses that "X90 grade multiphase structure pipeline steel plate for straight welded pipe and method for manufacturing the same" the chemical composition of the contents of the invention is different from the present invention, Mo element is added, the cost is high, and the addition of Mo element can remarkably improve the strength of the steel plate, but the addition of Mo element can inhibit the aggregation and diffusion of carbide, thereby inhibiting the generation of ferrite, promoting the generation of granular bainite, and is unfavorable for the core toughness of thick gauge steel plate with large rolling original austenite grains, therefore, the invention is only suitable for pipeline steel products with thickness below 30mm, but not suitable for thick gauge steel plate with thickness above 50 mm. Meanwhile, the cooling speed after rolling in the production process reaches 25-35 ℃/s, the capacity of the cooling equipment after rolling in the wide and thick plate production enterprises at present is not enough, and particularly, the cooling speed is difficult to realize for steel plates with the thickness of more than 50 mm.
Disclosure of Invention
The invention aims to provide a production method of multiphase-structure high-toughness ship plate steel EH47, particularly a thick plate with the thickness of 50-100 mm, overcomes the defects of the existing TMCP process technology, meets the development requirements of the industry, and realizes the green iron and steel concepts of energy conservation, consumption reduction, low carbon and environmental protection.
The technical scheme of the invention is as follows:
the multiphase structure high-toughness ship plate steel EH47 and the production method thereof, the chemical composition weight percentage of the steel is carbon = 0.04-0.08, silicon = 0.15-0.35, manganese = 1.60-1.80, phosphorus is less than or equal to 0.015, sulfur is less than or equal to 0.005, niobium = 0.03-0.04, titanium = 0.008-0.02, aluminum = 0.015-0.05, nickel = 0.30-0.40, copper = 0.25-0.35, chromium = 0.15-0.25%, and the rest is Fe and inevitable impurities; the process comprises the following steps:
smelting: the converter tapping [ C ] is less than or equal to 0.005; adopting an LF and RH refining process, blowing argon in the whole refining process of an LF furnace, keeping the white slag for more than or equal to 20min, carrying out RH vacuum degassing treatment, wherein [ N ] of the outbound molten steel is less than or equal to 40ppm, and [ H ] is less than or equal to 1.5 ppm;
continuous casting: the whole-process protective casting is adopted, the thickness of the casting blank is more than or equal to 300mm, and the core segregation C class of the casting blank is controlled to be less than or equal to 0.5 level;
rolling: two-stage rolling is adopted, wherein the rough rolling finishing temperature is more than or equal to 980 ℃, the intermediate billet is more than or equal to 2 times of the thickness of the plate, the finish rolling starting temperature is 730-760 ℃, and the finishing temperature is 720-750 ℃;
relaxation: after rolling, relaxing to 10-20 ℃ below Ar3, and cooling by water when the relaxation time is controlled to be ferrite phase transition 1/3;
and (3) cooling: the DQ ultra-fast cooling process of Mulpic is adopted, the cooling rate requires 5-10 ℃/S of the core of the steel plate, and the final cooling temperature is less than or equal to 200 ℃.
The high-toughness ship plate steel EH47 produced by the method has a structure of a multi-phase structure of proeutectoid ferrite, low-carbon bainite and a small amount of residual austenite, wherein the volume fraction of the ferrite is 25-40%, the volume fraction of the bainite is 50-70%, and the volume fraction of the MA component is 5-15%. The thickness of the steel plate is 50-100 mm, the yield strength is 460-530 MPa, the tensile strength is 570-660 MPa, the core impact toughness at the low temperature of minus 40 ℃ reaches more than 200J, and the carbon equivalent Ceq is less than or equal to 0.45.
The innovative principle of the invention is as follows: the conventional process generally refines grains by recrystallization of austenite in a rough rolling stage and flattening and elongation of grains in a finish rolling stage. The invention precisely controls the rolled phase change structure through the processes of component design, low-temperature rolling, relaxation and forced cooling to form a fine multi-phase structure to refine original austenite grains and achieve the purpose of improving the toughness of the steel plate.
Solid-state phase transition principle: in the rolling process, finishing rolling at the finishing rolling stage above the Ar3 point; and entering a relaxation temperature waiting stage, and the pre-eutectoid ferrite is preferentially transformed near the austenite crystal boundary. When the volume fraction of transformed ferrite reaches 1/3, the transformed ferrite enters Mulpic for rapid cooling, unconverted undercooled austenite can rapidly enter a bainite transformation interval, the undercooled austenite is gradually transformed into low-carbon bainite structures such as needle iron, grain bainite and plate bainite by controlling the cooling speed to be 5-10 ℃/S, and simultaneously, coarse original austenite grains are cut together with proeutectoid ferrite to form fine grains, so that the toughness of a steel plate is improved. The remained untransformed super-cooled austenite enters a martensite transformation region along with further temperature reduction to become an MA island component, and finally a mixed multi-phase structure of proeutectoid ferrite, low-carbon bainite and a small amount of residual austenite is formed.
The chemical composition design adopts the design concept of low carbon. The increase in the C content can improve the strength and reduce the Ar3 temperature, but deteriorates the low-temperature toughness and weldability of the steel, and the low C content can suppress the formation of pearlite at the time of high-temperature ferrite transformation and promote transformation of bainite, so the C content is controlled to 0.04 to 0.08%. Manganese is a weak carbide forming element, can reduce austenite transformation temperature, refines ferrite grains and is beneficial to improving the strength and the toughness of the steel plate. In order to improve the strength without influencing the impact toughness, alloy elements such as Nb, Ti, Ni, Cr, Cu and the like are added in a compounding way on the basis of the solid solution strengthening of C-Mn steel, and the effects of grain refinement, precipitation strengthening, phase change strengthening and the like are fully exerted to achieve the purposes of high strength, high toughness and excellent welding performance. Ni is particularly key to improving the toughness of the steel plate, can effectively disperse the aggregation of carbides, stabilize super-cooled austenite and inhibit the growth of ferrite and bainite grains. When the content is more than 0.3%, a DQ ultra-fast cooling process of Mulpic is combined, the cooling rate after rolling is controlled to be 5-10 ℃/S, a composite multiphase structure mainly comprising pro-eutectoid ferrite and low-carbon bainite is finally formed, cutting of original austenite grains is completed, and low-temperature toughness is improved. However, since Ni is expensive and the addition of too much Ni increases the production cost, the upper limit is set to 0.4%.
The outstanding characteristics and the obvious effects of the invention are mainly reflected in that:
(1) the invention breaks through the compression ratio limitation of the rolling continuous casting billet of the traditional TMCP process, does not need to add a heat treatment process, produces the high-toughness steel plate with the low-temperature impact requirement below-40 ℃, has the maximum thickness of 100mm, reduces the alloy content and the production cost while ensuring the product quality, and shortens the delivery period.
(2) The present invention utilizes the existing equipment and technological conditions of the common steel mills, i.e. investment and equipment modification are not needed to be added, the production efficiency is improved, and energy and consumption are saved.
(3) The product of the invention is a new variety of economical, low-carbon and environment-friendly steel, and can be widely applied to the manufacture of thick plates in a plurality of fields such as shipbuilding, maritime work, wind power, bridges, buildings, engineering machinery and the like.
Drawings
Fig. 1 shows a typical metallographic structure (500X) of a ship plate EH47 produced according to the present invention.
Detailed Description
The following will further explain the main contents of the present invention, such as the control range and the best mode, by referring to the following examples:
example 1:
the production method of the multiphase structure high-toughness ship plate steel EH47 comprises the following chemical components of, by weight, carbon =0.05, silicon =0.21, manganese =1.68, phosphorus =0.009, sulfur =0.0017, niobium =0.039, titanium =0.015, aluminum =0.045, nickel =0.38, copper =0.28, chromium =0.18, and the balance of Fe and inevitable impurities. The process comprises the following steps: smelting, tapping [ C = ] =0.0024 through a converter, adopting an LF + RH refining process, blowing argon in the whole refining process of the LF furnace, keeping the white slag for 21min, carrying out RH vacuum degassing treatment, discharging molten steel [ N ] =38 ppm, and [ H ] =1.1 ppm; the continuous casting adopts the whole-process protective casting, the thickness of a casting blank is 300mm, and the low-power center segregation C class of the casting blank is 0.5 grade.
In the embodiment, a casting blank is used for rolling a finished product EH47 ship board with the thickness of 50mm, the heating temperature is 1154 ℃, two-stage rolling is adopted, the temperature of the first-stage rough rolling and final rolling is 1023 ℃, the temperature of the intermediate blank is 120mm, the temperature of the second-stage finish rolling and initial rolling is 758 ℃, and the temperature of the final rolling is 732 ℃; and (3) relaxing the rolled steel plate by 89S, cooling the rolled steel plate in water at the temperature of 702 ℃, and cooling by adopting a DQ process of Mulpic at the average cooling rate of 9.8 ℃/S and the final cooling temperature of 152 ℃. The mechanical properties of the steel sheet are shown in Table 1.
Example 2:
the production method of the multiphase structure high-toughness ship plate steel EH47 comprises the following chemical components of, by weight, carbon =0.07, silicon =0.23, manganese =1.65, phosphorus =0.008, sulfur =0.0023, niobium =0.036, titanium =0.012, aluminum =0.042, nickel =0.36, copper =0.28, chromium =0.20, and the balance of Fe and inevitable impurities. The process comprises the following steps: smelting, tapping [ C ] by a converter by 0.0038%, adopting an LF + RH refining process, blowing argon in the whole refining process of the LF furnace, keeping white slag for 23min, carrying out RH vacuum degassing treatment, and discharging molten steel [ N ] =37 ppm and [ H ] =1.2 ppm; the continuous casting adopts the whole-process protective casting, the thickness of a tundish casting blank is 300mm, and the low-power core segregation C class of the casting blank is 0.5 grade.
In the embodiment, a casting blank is used for rolling a finished product EH47 ship board with the thickness of 80mm, the heating temperature is 1182 ℃, two-stage rolling is adopted, the first-stage rough rolling and final rolling temperature is 1062 ℃, the intermediate blank is 185mm, the second-stage finish rolling and initial rolling temperature is 739 ℃, and the final rolling temperature is 728 ℃; and (3) relaxing a rolled steel plate by 246S, cooling the rolled steel plate in water at the temperature of 696 ℃, and cooling by adopting a DQ (data of interference) process of Mulpic at the average cooling rate of 6.4 ℃/S and at the final cooling temperature of 85 ℃. The mechanical properties of the steel sheet are shown in Table 1.
Example 3:
the production process of multiphase structure high toughness ship plate steel EH47 includes the chemical components of C =0.06, Si =0.23, Mn =1.66, P =0.010, S =0.0015, Nb =0.038, Ti =0.016, Al =0.049, Ni =0.38, Cu =0.30%, Cr =0.21 and Fe and inevitable impurity for the rest. The process comprises the following steps: smelting, tapping [ C ] =0.0032 by a converter, adopting an LF + RH refining process, blowing argon in the whole refining process of the LF furnace, keeping the white slag for 22min, carrying out RH vacuum degassing treatment, discharging molten steel [ N ] =38 ppm, and [ H ] =1.0 ppm; the continuous casting adopts the whole-process protective casting, the thickness of a tundish casting blank is 300mm, and the low-power core segregation C class of the casting blank is 0.5 grade.
In the embodiment, a casting blank is used for rolling a finished product EH47 ship plate with the thickness of 100mm, the heating temperature is 1208 ℃, two-stage rolling is adopted, the first-stage rough rolling and final rolling temperature is 1026 ℃, the intermediate billet is 205mm, the second-stage finish rolling start temperature is 731 ℃, and the final rolling temperature is 725 ℃; and (3) relaxing the rolled steel plate by 308S, cooling in water at the temperature of 688 ℃ in the steel plate with the average cooling rate of 5.2 ℃/S and the final cooling temperature of 35 ℃ by adopting a DQ (data rate) process of Mulpic. The mechanical properties of the steel sheet are shown in Table 1.
Mechanical properties of EH47 steel in the examples of Table 1
The test results in the table 1 show that the EH47 steel plate produced by the method has the thickness specification of 50-100 mm, the yield strength of 460-530 MPa, the tensile strength of 570-660 MPa, the core impact toughness of 200J or more at the low temperature of minus 40 ℃ and the carbon equivalent (Ceq) of 0.45 or less by regulating the multi-phase structure with the ferrite content of about 30%, and the EH47 steel plate integrates high strength, high toughness and high welding performance, thereby being capable of well meeting the use requirements of the steel for ultra-large ships.

Claims (1)

1. The multiphase structure high-toughness ship plate steel EH47 and the production method thereof, the chemical composition weight percentage of the steel is carbon = 0.04-0.08, silicon = 0.15-0.35, manganese = 1.60-1.80, phosphorus is less than or equal to 0.015, sulfur is less than or equal to 0.005, niobium = 0.03-0.04, titanium = 0.008-0.02, aluminum = 0.015-0.05, nickel = 0.30-0.40, copper = 0.25-0.35, chromium = 0.15-0.25%, and the rest is Fe and inevitable impurities; the process comprises the following steps:
smelting: the converter tapping [ C ] is less than or equal to 0.005; adopting an LF and RH refining process, blowing argon in the whole refining process of an LF furnace, keeping the white slag for more than or equal to 20min, carrying out RH vacuum degassing treatment, wherein [ N ] of the outbound molten steel is less than or equal to 40ppm, and [ H ] is less than or equal to 1.5 ppm;
continuous casting: the whole-process protective casting is adopted, the thickness of the casting blank is more than or equal to 300mm, and the core segregation C class of the casting blank is controlled to be less than or equal to 0.5 level;
rolling: two-stage rolling is adopted, wherein the rough rolling finishing temperature is more than or equal to 980 ℃, the intermediate billet is more than or equal to 2 times of the thickness of the plate, the finish rolling starting temperature is 730-760 ℃, and the finishing temperature is 720-750 ℃;
relaxation: after rolling, relaxing to 10-20 ℃ below Ar3, and cooling by water when the relaxation time is controlled to be ferrite phase transition 1/3;
and (3) cooling: the DQ ultra-fast cooling process of Mulpic is adopted, the cooling rate requires 5-10 ℃/S of the core of the steel plate, and the final cooling temperature is less than or equal to 200 ℃.
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