CN116590625B - High-performance fine grain pressure vessel steel plate and manufacturing method thereof - Google Patents

High-performance fine grain pressure vessel steel plate and manufacturing method thereof Download PDF

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CN116590625B
CN116590625B CN202310439652.4A CN202310439652A CN116590625B CN 116590625 B CN116590625 B CN 116590625B CN 202310439652 A CN202310439652 A CN 202310439652A CN 116590625 B CN116590625 B CN 116590625B
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rolling
steel
steel sheet
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steel plate
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CN116590625A (en
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欧阳鑫
王储
胡昕明
邢梦楠
王爽
高强
徐海健
刘晨希
马骏
罗志华
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Angang Steel Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
    • B21B1/463—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting in a continuous process, i.e. the cast not being cut before rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
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    • C21D6/00—Heat treatment of ferrous alloys
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
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    • C21—METALLURGY OF IRON
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
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    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0231—Warm rolling
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/003—Cementite
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E30/00—Energy generation of nuclear origin
    • Y02E30/30—Nuclear fission reactors

Abstract

The invention discloses a high-performance fine grain pressure vessel steel plate and a manufacturing method thereof. The steel plate comprises the following components in percentage by weight: c:0.20 to 0.30 percent of Si:4.0 to 5.0 percent of Mn:0.90 to 1.50 percent, less than or equal to 0.015 percent of P, less than or equal to 0.005 percent of S, and Cr:1.0 to 2.0 percent of Ni:0.20 to 0.30 percent of Mo:1.0 to 2.0 percent, nb:0.01 to 0.02 percent of Ti: 0.02-0.03%, cu:0.80 to 0.90 percent, V:0.02 to 0.03 percent, B: 0.001-0.002%, als:2.0 to 3.0 percent, N: 0.06-0.08%, and the balance of Fe and unavoidable impurities. The invention realizes the refinement of microcomposite structure, so that the medium carbon steel not only has high room temperature strength, but also has good low temperature toughness and higher elongation after fracture.

Description

High-performance fine grain pressure vessel steel plate and manufacturing method thereof
Technical Field
The invention relates to a high-performance fine grain pressure vessel steel plate and a manufacturing method thereof, belonging to the technical field of steel.
Background
The conventional medium carbon steel is suitable for the production of tool steel and die steel with low requirements on toughness due to high hardness and high strength, but cannot be used for the production of structural materials such as pressure vessels due to high brittleness. Along with the continuous development of the industry, the development direction of equipment tends to be large-scale, high-performance and long-term service, so that higher requirements are put on raw materials for equipment manufacture, and the toughness of the traditional low-carbon alloy container steel plate cannot meet the manufacturing requirements of high-end pressure container equipment. As is known, the performance of the material depends on the tissue type, the tissue is uniformly refined, the comprehensive mechanical property of the material is greatly improved, and the high matching degree of the toughness is realized. At present, the tissue refinement of low carbon steel is successfully realized, but the tissue refinement of medium and high carbon steel is studied remarkably.
CN201911106651.8 discloses oneAccording to the method, one or more specified quantity of metamorphic elements are added into one or more nodes in smelting, refining and continuous casting processes according to the target equiaxed crystal proportion and size under corresponding working condition parameters in the steelmaking process, and molten steel containing the metamorphic elements is cast into billets to refine the solidification structure of the billets; CN201510900912.9 discloses a method for refining and purifying solidification structures of thick-wall steel castings, which combines the final deoxidation and the refining solidification structure process together in a ladle on the basis of adopting ferrosilicon, ferromanganese and silicon-calcium-barium alloy pre-deoxidation in a furnace, thereby realizing the refining and purifying of the solidification structures of the thick-wall steel castings; CN201510112841.6 discloses a method for refining steel structure and improving mechanical property by adding nano particles, after mixing nano particles and alloy nano powder uniformly, filling the mixture into slender steel tube, compacting and sealing, slowly extending the steel tube under the steel flow in the crystallizer at a certain speed under the fixed continuous casting drawing speed, and enabling the nano particles to be dispersed rapidly after entering the molten steel by means of continuous impact force of molten steel flowing down from a tundish and a flow field with intense disturbance in the crystallizer. However, the above-described structure refinement method is limited in the degree of grain refinement, and thus, there is also limited improvement in performance. CN201610841911.6 discloses a fine crystal modifier prepared by mixing ferrotitanium, ferrovanadium and ferroniobium powder obtained by atomization according to a set proportion and then mixing with rare earth ferrosilicon particles according to a set proportion, although the refining effect is improved, the byproduct AlCl is 3 HCl, chlorine, etc. can cause serious damage to the human body, the environment, and equipment.
Disclosure of Invention
The present invention aims to overcome the above problems and disadvantages and provide a high-performance fine grain pressure vessel steel sheet and a method for manufacturing the same. The invention adopts the silicon aluminum alloying, high-temperature short-time homogenizing treatment, two-stage rolling, short-time normalizing and two-stage small deformation rolling tissue refining technology to realize the refinement of microcomposite tissue, so that the medium carbon steel not only has high room temperature strength, but also has good low-temperature toughness and higher elongation after fracture.
In order to achieve the above purpose, the technical scheme of the invention is as follows:
the invention provides a fine grain pressure vessel steel plate, which comprises the following components in percentage by weight: c:0.20 to 0.30 percent of Si:4.0 to 5.0 percent of Mn:0.90 to 1.50 percent, less than or equal to 0.015 percent of P, less than or equal to 0.005 percent of S, and Cr:1.0 to 2.0 percent of Ni:0.20 to 0.30 percent of Mo:1.0 to 2.0 percent, nb:0.01 to 0.02 percent of Ti: 0.02-0.03%, cu:0.80 to 0.90 percent, V:0.02 to 0.03 percent, B: 0.001-0.002%, als:2.0 to 3.0 percent, N: 0.06-0.08%, and the balance of Fe and unavoidable impurities.
The action mechanism of each alloy component in the steel plate is as follows:
(1) C: c is a main constituent element of steel, the strength of the steel mainly depends on the content of C element in the steel, and the excessively high content of C element can lead to poor toughness, plasticity and welding performance of the steel; a low C element content results in lower strength of the steel and lower performance after simulated stress relief treatment. In order to ensure that the steel plate has good low-temperature impact toughness, strength and welding performance matching in the use process, the C content in the steel is required to be controlled within the range of 0.20-0.30 percent.
(2) Si: si is added to the medium carbon steel to affect the thermodynamics of the iron-carbon system and the kinetics of carbide formation and dissolution, and Si is used as a ferrite stabilization element to raise the Ac1 point of the steel. The addition of silicon causes the carbon content of the eutectoid composition to decrease, thereby increasing the amount of pre-eutectoid carbide, such that the volume fraction of carbide used to pin the grain boundaries in the gamma + theta two-phase region increases. Thus, not only the growth of ferrite and austenite grains is suppressed. Silicon is insoluble in carbide and when carbide precipitates, silicon is distributed around the carbide, locally forming a high concentration zone of silicon. Silicon is in turn an element that increases the activity of carbon. In the high concentration region of silicon, the activity of carbon is also increased, which reduces the diffusion flow rate of carbon to carbide, and thus can suppress coarsening of carbide, so that the Si content of the present invention is controlled to 4.0-5.0%.
(3) Mn: mn element can strengthen ferrite in steel grade through solid solution strengthening, C-Mn strengthening is also a main mode for improving strength of low-carbon steel, but Mn content is too high, so that production cost is increased, mn element is easy to combine with S element to generate MnS, and hydrogen-induced cracking resistance of the material is reduced, so that the Mn content in the steel is required to be controlled to be 0.90-1.50%.
(4) P: phosphorus is a harmful element in steel, increases cold brittleness of steel, worsens welding performance, reduces plasticity, worsens cold bending performance, and is particularly sensitive to irradiation embrittlement, so that the lower the P content in steel is required to be, the better the P content is, and the lower the P content in steel is required to be, the invention is required to be less than 0.015%.
(5) S: sulfur is a hazardous element in the usual case. S is generally liable to form brittle sulfides with alloy elements in steel, so that the steel is hot-brittle, ductility and toughness of the steel are reduced, and S also tends to accelerate irradiation embrittlement, so that the S content in the steel is required to be limited to below 0.005%.
(6) Als: the Ac1 point of the steel can be increased by aluminum alloying, the proeutectoid cementite is thinned and uniformly distributed, the formation of network carbide is suppressed, and after aluminum is added, both grain boundary carbide and widmannstatten structure carbide disappear, and a thinned complete pearlite structure is obtained, so that the Al content in the steel is required to be 2.0-3.0%.
(7) V: v belongs to microalloy elements, and V microalloy in steel can form tiny second phase particles, plays roles of pinning grain boundary and precipitation strengthening, can effectively refine grains, and greatly improves comprehensive mechanical properties such as strength, toughness, ductility, thermal fatigue resistance and the like of the steel, so that the range of V added in the steel is 0.02-0.03%.
(8) Ni: ni is a solid solution strengthening element in steel, can improve the strength of the steel, and reduces dislocation movement resistance of steel types to relax stress, so that the substructure of a matrix structure is changed, and the toughness of the steel, particularly the low-temperature toughness, is improved, and therefore, the Ni content is controlled to be 0.20-0.30%.
(9) Cr: chromium is an element that stabilizes carbides. Chromium addition reduces the dissolution rate of carbides. Therefore, when the thermal deformation structure refining process is adopted, eutectoid transformation can be avoided even if the heating temperature is increased or the heating time is prolonged, refined structure is obtained, and the chromium can inhibit graphitization of the silicon-containing and aluminum-containing ultrahigh-carbon steel, so that the Cr content in the steel is required to be controlled to be 1.0-2.0%.
(10) Cu: the outstanding effect of Cu in steel is to improve the corrosion resistance of common carbon low alloy steel, and also to improve the strength and yield ratio of steel without adverse effect on welding performance, when the content of Cu exceeds 0.75%, the Cu can produce aging strengthening effect after solution treatment and aging, and meanwhile, the Cu has the effect similar to nickel, and can play a role in saving nickel and reducing cost to a certain extent, but when the content is higher, copper embrittlement phenomenon is caused during thermal deformation processing, so the Cu content in the steel is required to be controlled to be 0.80-0.90%.
(11) Nb: nb is used as a strong carbide forming element to form NbC phase with large dispersion and good high-temperature stability in steel grade, plays a role of precipitation strengthening, can effectively refine grains through multistage rolling, improves the toughness reduction caused by precipitation strengthening, and thus enables the steel plate to obtain high-strength and high-toughness comprehensive performance.
(12) Mo: mo mainly relies on solid solution strengthening and grain boundary strengthening to improve the strength of steel; secondly, mo increases the stability of supercooled austenite, so that the austenite moves to the right of a ferrite transformation curve, and finer ferrite tissues are obtained after transformation; in addition, ti and Mo are combined, nano-sized Ti-Mo (CN) carbide is greatly precipitated in the steel, and the thinned carbide pins dislocation, so that the toughness of the steel is greatly improved, and the Mo content in the steel is required to be controlled to be 1.0-2.0%
(13) Ti: adding proper amount of Ti to form a large amount of dispersed fine TiN or Ti 2 O 3 Particle, they can be used as heterogeneous nucleation core of needle-shaped ferrite in tissue solidification to refine tissue, ti also has deoxidization function to ensure that B is not oxidized and nitrided, but B can reduce transformation temperature of austenite to ferrite phase to promote formation of needle-shaped ferrite in crystal grain to refine crystal grain, but when w (Ti) is more than or equal to 0.09%, the content of needle-shaped ferrite is reduced to deteriorate low-temperature toughness of steel plate, so that the Ti content in steel is required to be controlled to be 0.02-0.03%.
(14) B: b can reduce the transformation temperature of austenite to ferrite phase, promote the formation of acicular ferrite in the crystal grain and play a role of refining the crystal grain, so the invention requires that the B content in the steel is controlled to be 0.001-0.002%.
(15) N: n can be combined with Ti to form a large amount of tiny TiN which is dispersed and distributed, and the tiny TiN can be used as heterogeneous nucleation cores of the needle-shaped ferrite when the tissue is solidified, so that the tissue is refined, and therefore, the N content in the steel is required to be controlled to be 0.06-0.08%.
In the above-mentioned technical solution, further, the microstructure of the steel sheet is composed of cementite and ferrite, wherein the grain size of cementite is 0.1-0.5 μm, and the grain size of ferrite is 0.1-0.5 μm.
In the technical scheme, further, the tensile strength of the steel plate is 700-840 MPa, the yield strength is 460-600 MPa, the elongation after fracture is 50-60%, the impact power at minus 60 ℃ is 310-450J, the surface Brinell hardness is 390-460 HBW, and the high-temperature tensile yield strength at 450 ℃ is 365-505 MPa.
In the above technical scheme, further, the thickness of the steel plate is 15-95 mm.
In another aspect, the present invention provides a method for manufacturing the fine grain pressure vessel steel sheet, comprising the steps of:
(1) Smelting:
the thickness of the smelted continuous casting billet is 150-350 mm;
(2) Homogenizing:
after smelting of the continuous casting billet, homogenizing treatment is carried out in a direct hot charging heating furnace; the step is to perform homogenizing annealing in a single-phase austenite region, and fully dissolve carbon elements;
(3) Two-stage rolling:
after homogenization treatment, the continuous casting billet is hot-fed to a rolling mill for rolling, firstly, the continuous casting billet is rough rolled and cogged, a middle billet roller way is reciprocated and air-cooled after rough rolling, and continuous multipass finish rolling is carried out when the temperature is reduced to 600-650 ℃; the thermal deformation in the process is helpful for breaking the proeutectoid cementite separated out from austenite, so as to avoid forming net carbide;
(4) Normalizing:
after the rolling of the steel plate is completed, heat is sent to a heat treatment furnace, and the steel plate is discharged from the furnace for air cooling after being subjected to clean heat preservation for 10-25 min at the temperature of 910-930 ℃; the steel sheet undergoes austenitizing for a short period of time, which is known as off-eutectoid transformation, in which pearlite transformation does not occur, and carbides are spherically precipitated near undissolved carbides on austenite grain boundaries and inside austenite grains;
(5) Two-stage small deformation rolling:
in the air cooling and cooling process of the steel plate, two-stage small deformation rolling is carried out, the original austenite grains are further refined by deformation, so that ferrite grains are refined after phase transformation, the total rolling reduction rate of the two-stage small deformation rolling is 1-2%, and finally the steel plate is air cooled to room temperature.
In the above technical solution, further, in the step (2), the homogenizing temperature treatment is as follows: preserving heat for 1-2 h at 1140-1160 ℃.
In the above technical scheme, in the step (3), further, the rough rolling start temperature is 1080-1110 ℃, the finish rolling temperature is 810-840 ℃, the reduction rate of each pass is guaranteed to be 15-25%, the thickness of the intermediate billet is 2-3 times of the thickness of the finished steel plate, the reduction rate of each pass is guaranteed to be 5-15% by finish rolling, and the deformation rate of 1.0-2.0% is reserved to the thickness of the finished steel plate after finish rolling.
In the above technical solution, further, in the step (5), the two-stage small deformation rolling is: the first stage is to perform initial rolling with a rolling reduction of 0.5-1% at 800-850 ℃, and then roll table swing air cooling is performed until the temperature reaches 700-750 ℃ to perform final rolling with a rolling reduction of 0.5-1% at the second stage.
The beneficial effects of the invention are as follows:
1. according to the invention, silicon aluminum alloying is adopted, silicon is taken as a ferrite stabilization element, the Ac1 point of steel is improved, the growth of ferrite, austenite grains and carbide is effectively inhibited, the Ac1 point of steel can be improved by utilizing the aluminum alloying, the proeutectoid cementite is refined and uniformly distributed, the formation of reticular carbide is inhibited, and after aluminum is added, grain boundary carbide and Wittig tissue carbide are all disappeared, so that a refined metallographic structure is obtained, and the toughness matching and the elongation after fracture of the steel plate are greatly improved;
2. in the manufacturing method, high-temperature short-time homogenization treatment is carried out, homogenization annealing is carried out in a single-phase austenite region, and carbon elements are fully dissolved; two-stage rolling is performed, which is helpful for breaking the proeutectoid cementite separated out from austenite, and avoiding forming net carbide; pearlite transformation does not occur in the short-time normalizing process, and carbide is precipitated in a spherical shape on an austenite grain boundary near undissolved carbide and inside the austenite grain; finally, carrying out two-stage small deformation rolling in the air cooling and cooling process of the steel plate, and further refining original austenite grains by thermal deformation, so that ferrite grains after phase transformation are fully refined; the invention adopts the tissue refining technology to realize the refinement of microcomposite tissues, so that the medium carbon steel not only has high room temperature strength, but also has good low temperature toughness and higher elongation after fracture;
3. the finished steel plate has the tensile strength of 700-840 MPa, the yield strength of 460-600 MPa, the elongation after fracture of 50-60%, the impact energy of-60 ℃ of 310-450J, the surface Brinell hardness of 390-460 HBW and the high-temperature tensile yield strength of 450 ℃ of 365-505 MPa, and the good technological performance and mechanical property are expected to be widely applied in the field of pressure vessel equipment manufacturing.
Drawings
FIG. 1 is a photograph showing the metallographic structure of a steel sheet of example 1.
Detailed Description
The following examples are given to illustrate the present invention in detail, but are merely a general description of the present invention and are not intended to limit the present invention.
The compositions of the steel sheets in examples 1 to 6 of the present invention are shown in Table 1.
TABLE 1 Components (wt%) of Steel sheets of examples 1-6
The manufacturing method of the fine grain pressure vessel steel plate comprises the following steps:
(1) Smelting: smelting molten steel into a continuous casting blank;
(2) Homogenizing: after smelting the continuous casting billet, directly hot-charging the continuous casting billet into a heating furnace, homogenizing and annealing in a single-phase austenite area, and fully dissolving carbon elements; the main process parameters of smelting and homogenizing treatment in examples 1-6 are shown in Table 2;
TABLE 2 examples 1-6 major Process parameters for smelting and homogenizing
Examples Thickness/mm of continuous casting slab Thickness/mm of finished steel plate Heat preservation temperature/°c Holding time/h
1 150 15 1145 1.2
2 200 24 1157 1.5
3 230 32 1148 1.6
4 250 54 1156 1.9
5 300 77 1152 1.1
6 350 95 1146 1.5
(3) Two-stage rolling: after homogenization treatment, the continuous casting billet is hot-fed to a double-rack rolling mill for rolling, firstly, the continuous casting billet is rough rolled and cogged, a middle billet roller way after rough rolling swings reciprocally and is air-cooled, and after cooling, continuous multipass finish rolling is carried out, and the thermal deformation in the process is helpful for breaking the proeutectoid cementite separated out by austenite, so that the formation of netlike carbide is avoided; the main process parameters of the two-stage rolling treatment of examples 1-6 are shown in Table 3;
table 3 examples 1-6 major process parameters for two stage rolling treatment
(4) Normalizing: after the steel plate is rolled, heat is sent to a heat treatment furnace for normalizing treatment, the steel plate is austenitized for a short time, the process is called off-eutectoid transformation, pearlite transformation does not occur in the off-eutectoid transformation process, and carbide is precipitated near undissolved carbide on an austenite grain boundary and inside austenite grains in a spherical shape; the main process parameters of the normalizing treatment in examples 1-6 are shown in Table 4;
TABLE 4 examples 1-6 major Process parameters for normalizing Steel sheets
Examples Normalizing temperature (DEG C) Clean holding time h
1 929 19
2 902 10
3 920 25
4 917 21
5 907 24
6 930 17
(5) Two-stage small deformation rolling: in the air cooling and cooling process of the steel plate, two-stage small deformation rolling is carried out, and original austenite grains are further refined by deformation, so that ferrite grains are refined after phase transformation, and finally, the steel plate is air cooled to room temperature.
The main process parameters of the two-stage small deformation rolling treatment of examples 1-6 are shown in Table 5.
TABLE 5 major technological parameters for two-stage small deformation Rolling treatment of Steel sheets of examples 1-6
As shown in fig. 1, the microstructure of the steel sheet of example 1 was composed of cementite and ferrite, and the properties of the above-mentioned fine grain pressure vessel steel sheet were tested, and the grain size and the comprehensive mechanical properties of the steel sheet are shown in table 6.
TABLE 6 grain size and comprehensive mechanical Properties of the Steel sheets of examples 1 to 6
The present invention has been properly and fully described in the foregoing embodiments by way of example only, and not by way of limitation, and various changes and modifications may be made by one skilled in the art without departing from the spirit and scope of the invention, any modification, equivalent substitution, improvement, etc. should be included in the scope of the invention, and the scope of the invention is defined by the claims.

Claims (6)

1. The fine grain pressure vessel steel plate is characterized by comprising the following components in percentage by weight: c:0.20% -0.30%, si:4.0% -5.0%, mn:0.90% -1.50%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, cr:1.0% -2.0%, ni:0.20% -0.30%, mo:1.0% -2.0%, nb:0.01% -0.02%, ti:0.02% -0.03%, cu:0.80% -0.90%, V:0.02% -0.03%, B:0.001% -0.002%, als:2.0% -3.0%, N:0.06% -0.08%, and the balance being Fe and unavoidable impurities;
the preparation method of the steel plate comprises the following steps:
(1) Smelting:
the thickness of the smelted continuous casting billet is 150-350 mm;
(2) Homogenizing:
after smelting of the continuous casting billet, homogenizing treatment is carried out in a direct hot charging heating furnace;
(3) Two-stage rolling:
after homogenization treatment, carrying out hot rolling on the continuous casting billet to a rolling mill, firstly, rough rolling and cogging the continuous casting billet, and carrying out reciprocating swing air cooling on a middle billet roller way after rough rolling, and carrying out continuous multi-pass finish rolling when the temperature is reduced to 600-650 ℃;
(4) Normalizing:
after the rolling of the steel plate is completed, heat is sent to a heat treatment furnace, and the steel plate is discharged from the furnace for air cooling after being subjected to clean heat preservation for 10-25 min at the temperature of 910-930 ℃;
(5) Two-stage small deformation rolling:
performing two-stage small deformation rolling in the air cooling and cooling process of the steel plate, wherein the total rolling reduction rate of the two-stage small deformation rolling is 1-2%, and finally air cooling to room temperature;
in the step (5), the two-stage small deformation rolling is as follows: the first stage is to perform initial rolling with a rolling reduction of 0.5-1% at 800-850 ℃, and then perform final rolling with a rolling way swing air cooling to 700-750 ℃ and a rolling reduction of 0.5-1% at the second stage.
2. The fine grain pressure vessel steel sheet according to claim 1, wherein the microstructure of the steel sheet is composed of cementite and ferrite, wherein the grain size of cementite is 0.1 to 0.5 μm and the grain size of ferrite is 0.1 to 0.5 μm.
3. The fine grain pressure vessel steel sheet according to claim 1, wherein the steel sheet has a tensile strength of 700 to 840mpa, a yield strength of 460 to 600mpa, a elongation after break of 50 to 60%, an impact power of 310 to 450j at-60 ℃, a surface brinell hardness of 390 to 460hbw, and a high temperature tensile yield strength of 365 to 505mpa at 450 ℃.
4. The fine grain pressure vessel steel sheet according to claim 1, wherein the thickness of the steel sheet is 15 to 95mm.
5. The fine grain pressure vessel steel sheet according to claim 1, wherein in the step (2), the homogenization temperature treatment is: and preserving heat for 1-2 hours at 1140-1160 ℃.
6. The fine grain pressure vessel steel sheet according to claim 1, wherein in the step (3), the rough rolling start temperature is 1080-1110 ℃, the finish rolling temperature is 810-840 ℃, the rolling reduction of each pass is guaranteed to be 15-25%, the thickness of the intermediate blank is 2-3 times the thickness of the finished steel sheet, the rolling reduction of each pass is guaranteed to be 5-15% by finish rolling, and the deformation rate of 1.0-2.0% is reserved to the thickness of the finished steel sheet after finish rolling.
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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1106981A (en) * 1993-03-31 1995-08-16 日立金属株式会社 Wear- and seizure-resistant roll for hot rolling
CN107406953A (en) * 2015-04-08 2017-11-28 新日铁住金株式会社 steel plate for heat treatment
CN107429363A (en) * 2015-04-08 2017-12-01 新日铁住金株式会社 Heat- treated steel board member and its manufacture method
CN107532255A (en) * 2015-04-08 2018-01-02 新日铁住金株式会社 Heat- treated steel board member and its manufacture method
CN113166838A (en) * 2019-04-08 2021-07-23 日本制铁株式会社 Cold-rolled steel sheet and method for producing same

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1106981A (en) * 1993-03-31 1995-08-16 日立金属株式会社 Wear- and seizure-resistant roll for hot rolling
CN107406953A (en) * 2015-04-08 2017-11-28 新日铁住金株式会社 steel plate for heat treatment
CN107429363A (en) * 2015-04-08 2017-12-01 新日铁住金株式会社 Heat- treated steel board member and its manufacture method
CN107532255A (en) * 2015-04-08 2018-01-02 新日铁住金株式会社 Heat- treated steel board member and its manufacture method
CN113166838A (en) * 2019-04-08 2021-07-23 日本制铁株式会社 Cold-rolled steel sheet and method for producing same

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