CN114990305A - Method for producing Q890D ultrahigh-strength steel medium plate through online quenching - Google Patents

Method for producing Q890D ultrahigh-strength steel medium plate through online quenching Download PDF

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CN114990305A
CN114990305A CN202210571671.8A CN202210571671A CN114990305A CN 114990305 A CN114990305 A CN 114990305A CN 202210571671 A CN202210571671 A CN 202210571671A CN 114990305 A CN114990305 A CN 114990305A
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rolling
ultrahigh
strength steel
treatment
temperature
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CN114990305B (en
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武卫阳
路士平
王根矶
田鹏
王志勇
魏运飞
王凯凯
韩承良
于文飞
王东柱
马国金
狄国标
霍常浩
沈开照
张光磊
冯韦
王坤
杜群超
杨子江
慕文杰
冯博
齐岩
师大兴
于海波
孙博
郑文明
辛士伟
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Shougang Jingtang United Iron and Steel Co Ltd
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Shougang Jingtang United Iron and Steel Co Ltd
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    • 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
    • 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
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
    • 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
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/06—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
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

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  • Heat Treatment Of Steel (AREA)

Abstract

The application relates to the field of preparation of super-strong steel, in particular to a method for producing a Q890D super-strong steel medium plate by online quenching; the method comprises the following steps: obtaining a casting blank after continuous casting; heating and rough rolling a casting blank before rolling to obtain an intermediate blank; carrying out finish rolling, on-line quenching cooling and heat treatment on the intermediate billet to obtain medium-thickness Q890D ultrahigh-strength steel; wherein the heat treatment comprises tempering treatment and heat preservation treatment, the end point temperature of the tempering treatment is 600-620 ℃, the heat preservation treatment is carried out by the end point temperature of the tempering treatment, and the time of the heat preservation treatment is 60-70 min; the rolling reduction of the rough rolling in the last 3 passes is more than or equal to 36 mm; rolling by large-pass reduction in the rough rolling stage, performing online cooling, performing heat treatment, and performing heat preservation treatment, so that the microstructure of the steel plate can be effectively adjusted, carbides are precipitated, the microstructure of the steel plate is converted into a dual-phase structure containing lath martensite and granular bainite, and the effective preparation of the ultrahigh-strength steel with the medium thickness of 60-70 mm is ensured.

Description

Method for producing Q890D ultrahigh-strength steel medium plate through online quenching
Technical Field
The application relates to the field of preparation of super-strong steel, in particular to a method for producing a Q890D super-strong steel medium plate through online quenching.
Background
The ultrahigh-strength steel is a product with resource conservation, high technical content and high added value, along with the vigorous development of large-scale engineering, the ultrahigh-strength steel with the grade of Q890D or above is widely applied to the aspects of engineering machinery, mining, hoisting mine cars, ocean platforms and the like, and the ultrahigh-strength steel with the grade of Q890D has the characteristics that: the structure is simple, the dead weight is light, the safety is high, larger dynamic and static loads can be borne, and the service time is longer; at present, the production of medium-thickness steel plates of Q890D ultrahigh-strength steel mostly adopts a quenching and tempering state mode comprising (offline quenching and tempering), and the online quenching process is adopted for a very few Q890D ultrahigh-strength steels with the thickness below 50mm, but on Q890D ultrahigh-strength steel with the thickness above 50mm, the ultrahigh-strength steel obtained only by the online quenching mode cannot meet the requirements of the manufacturing industries of engineering machinery, mining machinery and the like.
Therefore, how to provide a preparation method of Qg90D ultrahigh-strength steel with the thickness specification of more than 50mm is a technical problem which needs to be solved at present.
Disclosure of Invention
The application provides a method for producing a Q890D ultrahigh-strength steel medium-thickness plate by online quenching, which aims to solve the technical problem that the medium-thickness Q890D ultrahigh-strength steel with the specification of more than 50mm in the prior art is difficult to effectively prepare.
In a first aspect, the present application provides a method for producing a Q890D ultra-high strength steel medium plate by on-line quenching, the method comprising:
obtaining a casting blank after continuous casting;
heating and rough rolling the casting blank before rolling to obtain an intermediate blank;
carrying out finish rolling, on-line quenching cooling and heat treatment on the intermediate billet to obtain medium-thickness Q890D ultrahigh-strength steel;
the heat treatment comprises tempering treatment and heat preservation treatment, wherein the end point temperature of the tempering treatment is 600-620 ℃, the heat preservation treatment is carried out by preserving the heat at the end point temperature of the tempering treatment, and the time of the heat preservation treatment is 60-70 min;
the rolling reduction of the rough rolling in the last 3 passes is more than or equal to 36 mm;
the thickness of the Q890D ultrahigh-strength steel is 60-70 mm.
Optionally, the chemical composition of the Q890D ultrahigh-strength steel comprises, by mass fraction: c: 0.14% -0.17%, Si: 0.20-0.50%, Mn: 1.00-1.50%, P is less than or equal to 0.015%, S is less than or equal to 0.003%, Cr: 0.30% -0.70%, Mo: 0.40-0.70%, Ni: 0.30-0.60%, Ti: 0.005-0.025%, Nb: 0.015% -0.040%, V: 0.03% -0.06%, B: 0.001% -0.0020%, Alt: 0.020-0.050% and the balance of Fe and inevitable impurities.
Optionally, CEV of the Q890D ultrahigh-strength steel is less than or equal to 0.65, and Pcm of the Q890D ultrahigh-strength steel is less than or equal to 0.35.
Optionally, the initial temperature of the online cooling is 810-830 ℃, and the temperature of the online cooling zone is less than or equal to 200 ℃.
Optionally, the speed of the on-line cooling is 15 ℃/s-30 ℃/s.
Optionally, the end point temperature of heating before rolling is 1150-1210 ℃, and the total time of heating before rolling is 260-450 min.
Optionally, the rough rolling includes a first rough rolling and a second rough rolling, the rolling temperature of the first rough rolling is 1050 ℃ to 1150 ℃, the rolling temperature of the second rough rolling is 880 ℃ to 900 ℃, and the finish rolling temperature of the second rough rolling is 840 ℃ to 870 ℃.
Optionally, the reduction rate of the last 2 passes of the first rough rolling is more than or equal to 18%.
Optionally, the thickness of the intermediate blank is more than or equal to 110 mm.
Optionally, the temperature rise rate of the tempering treatment is 1.6 min/mm-2.0 min/mm.
Compared with the prior art, the technical scheme provided by the embodiment of the application has the following advantages:
the method for producing the Q890D medium and thick plate of the ultrahigh-strength steel by online quenching, provided by the embodiment of the application, is characterized in that rolling is carried out by large-pass reduction in a rough rolling stage, austenite grains can be guaranteed to be flattened, so that the area of a grain boundary is increased, recrystallization nucleation points are increased, further forming fine and uniform austenite grains, realizing the phase transformation strengthening in the steel plate after the finish rolling through on-line cooling, finally leading the microstructure after the phase transformation to be further stably changed through heat treatment and utilizing the end point temperature of tempering treatment, combining heat preservation treatment, effectively adjusting the structure and separating out carbide, thereby the microstructure of the steel plate can be transformed into a dual-phase structure containing lath martensite and granular bainite, thereby ensuring the strength of the ultrahigh-strength steel with the thickness of 60-70 mm and further ensuring the effective preparation of the ultrahigh-strength steel with the thickness of 60-70 mm.
Drawings
The accompanying drawings, which are incorporated in and constitute a part of this specification, illustrate embodiments consistent with the invention and together with the description, serve to explain the principles of the invention.
In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings used in the description of the embodiments or the prior art will be briefly described below, and it is obvious for those skilled in the art that other drawings can be obtained according to the drawings without inventive exercise.
Fig. 1 is a schematic flow chart of a method provided in an embodiment of the present application;
FIG. 2 is a schematic diagram of a metallographic structure of a 70mm thick Q890D high-strength steel plate 1/4 after on-line quenching according to an embodiment of the present application;
FIG. 3 is a schematic diagram of a metallographic structure of a high-strength steel plate 1/4 of Q890D with a thickness of 70mm after tempering treatment according to an embodiment of the present application;
FIG. 4 is a schematic diagram of a metallographic structure of a 60mm thick Q890D high-strength steel plate 1/4 after on-line quenching according to an embodiment of the present application;
FIG. 5 is a schematic diagram of a metallographic structure of a 60mm thick Q890D high-strength steel plate 1/4 after tempering treatment.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present application clearer, the technical solutions in the embodiments of the present application will be clearly and completely described below with reference to the drawings in the embodiments of the present application, and it is obvious that the described embodiments are some embodiments of the present application, but not all embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present application.
In one embodiment of the present application, as shown in fig. 1, there is provided a method for producing a Q890D ultra-high strength steel medium plate by on-line quenching, the method comprising:
s1, obtaining a casting blank after continuous casting;
s2, heating and rough rolling the casting blank before rolling to obtain an intermediate blank;
s3, performing finish rolling, on-line quenching cooling and heat treatment on the intermediate billet to obtain medium-thickness Q890D ultrahigh-strength steel;
the heat treatment comprises tempering treatment and heat preservation treatment, wherein the end point temperature of the tempering treatment is 600-620 ℃, the heat preservation treatment is carried out at the end point temperature of the tempering treatment, and the heat preservation treatment lasts for 60-70 min;
the rolling reduction of the rough rolling in the last 3 passes is more than or equal to 36 mm;
the thickness of the Q890D ultrahigh-strength steel is 60-70 mm.
In the embodiment of the application, the positive effect that the end point temperature of the tempering treatment is 600-620 ℃ is that in the temperature range, the steel plate after finish rolling can be ensured to further carry out phase change, the structure form is adjusted, and carbides are precipitated, so that the microstructure is ensured to be converted into a dual-phase structure containing lath martensite and granular bainite, and the final ultrahigh-strength steel is enabled to meet the standard of Q890D ultrahigh-strength steel; when the value of the temperature is larger than the maximum value of the end point of the range, the temperature is too high, the stable change of the phase of the microstructure is influenced, so that part of the microstructure can not be converted into the two-phase structure, and when the value of the temperature is smaller than the minimum value of the end point of the range, the temperature is too low, and the phase change of the microstructure can not be carried out.
The time of the heat preservation treatment is 60-70 min, and the positive effects are that in the time range, the structure form can be adjusted, and simultaneously carbide is precipitated, so that the microstructure is converted into a dual-phase structure containing lath martensite and granular bainite, and the final super-strength steel meets the standard of Q890D super-strength steel; when the time value is larger than the maximum value of the end point of the range, the heat preservation time is too long, the stability of the formed two-phase structure is influenced, and when the time value is smaller than the minimum value of the end point of the range, the adverse effect is that the microscopic structure cannot be completely changed due to too short time, and the final strength of the super-strong steel is influenced.
The positive effect that the reduction of the rough rolling for the last 3 passes is more than or equal to 36mm is that in the range of the reduction, austenite grains can be effectively ensured to be flattened, so that the area of a grain boundary is increased, recrystallization nucleation points are increased, fine and uniform austenite grains are further formed, and the completeness of subsequent phase change is ensured; when the rolling reduction value is less than the end value of the range, austenite grains cannot be effectively flattened, so that the subsequent phase change cannot be completely carried out, and the strength of the final ultrahigh-strength steel is influenced.
In some optional embodiments, the Q890D ultrahigh-strength steel has a chemical composition including, in mass fraction: c: 0.14% -0.17%, Si: 0.20-0.50%, Mn: 1.00-1.50%, P is less than or equal to 0.015%, S is less than or equal to 0.003%, Cr: 0.30% -0.70%, Mo: 0.40-0.70%, Ni: 0.30-0.60%, Ti: 0.005-0.025%, Nb: 0.015% -0.040%, V: 0.03% -0.06%, B: 0.001% -0.0020%, Alt: 0.020-0.050% and the balance of Fe and inevitable impurities.
In the embodiment of the application, the positive effect that the mass fraction of C is 0.14-0.17% is to adjust the strength and the plastic toughness of the martensite structure, when the mass fraction is greater than the maximum value of the end point of the range, the whole carbon equivalent is improved, cracks are easy to generate during welding, when the mass fraction is less than the minimum value of the end point of the range, the tensile strength in a quenching state can not be ensured to be greater than 1000MPa, and then the strength is further adjusted through tempering, so that the toughness is improved.
The positive effect that the mass fraction of Si is 0.20-0.50% is that better deoxidation effect can be achieved; when the mass fraction is larger than the maximum value of the end point of the range, red iron sheet is easy to generate, and the toughness of the martensite high-strength steel is easy to deteriorate.
The positive effect that the mass fraction of Mn is 1.00-1.50% is that the hardenability of the steel can be improved; when the value of the mass fraction is larger than the maximum value of the end point of the range, inclusions such as segregation and MnS are easy to generate, and the toughness of the martensite high-strength steel is deteriorated.
P, S as impurity elements to influence the plasticity and toughness of steel, the smaller the value, the better, the invention controls the ranges of P less than or equal to 0.015% and S less than or equal to 0.003%.
The positive effect that the mass fraction of Cr is 0.30-0.70% is that the hardenability of the steel can be improved, and martensite and bainite structures can be formed during quenching; when the mass fraction is greater than the maximum value at the end of the range, larger sparks can occur during welding, and the welding quality is affected.
The positive effect that the mass fraction of Mo is 0.40-0.70% is to improve the hardenability of the steel and facilitate the formation of martensite and bainite structures during quenching; when the mass fraction is larger than the maximum value at the end of the range, the carbon equivalent increases to deteriorate the weldability, and Mo is a noble metal to increase the cost.
The positive effect that the mass fraction of Ni is 0.30-0.60% is that the martensite structure is refined, and the low-temperature impact toughness of the steel is improved; when the mass fraction is larger than the maximum value at the end of the range, the carbon equivalent increases to deteriorate the weldability, and at the same time, Ni is a noble metal to increase the cost.
Nb, Ti and V are microalloy elements, are added into steel in a proper amount, form a nano precipitate with elements such as C, N and the like, and inhibit the growth of austenite grains during heating; nb can increase the critical temperature of non-recrystallization and enlarge the production process window; fine precipitate particles of Ti can improve welding performance; v reacts with N and C in the tempering process to separate out nano-scale V (C, N) particles, so that the strength of the steel can be improved; the content range of niobium is 0.015-0.040%, the content range of titanium is 0.005-0.025%, and the content range of vanadium is 0.03-0.06%.
The positive effect that the mass fraction of B is 0.001-0.0020% is that the hardenability of the steel can be improved, and the strength of the steel is improved; when the mass fraction is larger than the maximum value at the end of the range, B is likely to segregate to form a carborundum compound, which seriously deteriorates the toughness of the steel.
The positive effect of Alt mass fraction of 0.020-0.050% is that the deoxidizer can be used for refining grains and improving impact toughness. When the mass fraction is larger than the maximum value at the end of the range, oxide inclusion defects of Al are likely to occur.
In some alternative embodiments, the CEV of the Q890D ultra-high strength steel is less than or equal to 0.65, and the Pcm of the Q890D ultra-high strength steel is less than or equal to 0.35.
In the embodiment of the application, the positive effect that the CEV of the Q890D ultrahigh-strength steel is less than or equal to 0.65 is that the strength, hardness and toughness of the ultrahigh-strength steel can be effectively ensured to meet the standard within the range of the carbon equivalent.
The positive effect that Pcm of the Q890D ultrahigh-strength steel is less than or equal to 0.35 is that the convenience of the ultrahigh-strength steel in the use process can be ensured within the range of welding cold crack sensitivity, so that the operation convenience of the ultrahigh-strength steel in the application process is ensured.
In some alternative embodiments, the initial temperature of the in-line cooling is 810 ℃ to 830 ℃, and the temperature of the in-line cooling zone is 200 ℃ or less.
In the embodiment of the application, the positive effect that the initial temperature of the on-line cooling is 810-830 ℃ is that the temperature can be ensured within the temperature range
In some alternative embodiments, the on-line cooling rate is from 15 ℃/s to 30 ℃/s.
In the embodiment of the application, the on-line cooling speed is 15-30 ℃/s, and the positive effect is that in the cooling speed range, the steel plate after finish rolling can be ensured to realize phase change, so that the subsequent microstructure is ensured to be converted into a dual-phase structure containing lath martensite and granular bainite; when the value of the cooling speed is larger than the maximum value of the end point of the range, the maximum cooling capacity which can be borne by equipment is exceeded, and when the value of the cooling speed is smaller than the minimum value of the end point of the range, the phase change is insufficient, even the phase change does not occur, a dual-phase structure containing lath martensite and granular bainite cannot be obtained, and the strength of the obtained steel plate is insufficient.
In some optional embodiments, the end temperature of the heating before rolling is 1150 ℃ to 1210 ℃, and the total time of the heating before rolling is 260min to 450 min.
In the embodiment of the application, the positive effect that the end point temperature of heating before rolling is 1150-1210 ℃ is that in the temperature range, the phase change of the metallographic structure of the steel plate in an austenite region can be ensured, so that the subsequent microstructure is ensured to be transformed into a dual-phase structure containing lath martensite and granular bainite, and the strength of the medium-thickness steel plate is ensured to meet the requirement of Q890D ultrahigh-strength steel; when the value of the temperature is larger than or smaller than the end value of the range, the metallographic structure of the steel plate cannot be effectively performed in the phase change stage, so that the subsequent microstructure can not be ensured to be converted into a dual-phase structure, and the strength of the medium-thickness steel plate can not be ensured to meet the requirement of Q890D ultrahigh-strength steel.
The positive effect that the total heating time before rolling is 260-450 min is that in the time range, the phase change of the metallographic structure of the steel plate in an austenite region can be ensured, so that the subsequent microstructure is changed into a dual-phase structure containing lath martensite and granular bainite, and the strength of the medium-thickness steel plate is ensured to meet the requirement of Q890D ultrahigh-strength steel; when the time value is larger than or smaller than the end value of the range, the metallographic structure of the steel plate cannot be effectively performed in the phase change stage, so that the subsequent microstructure can not be ensured to be converted into a dual-phase structure, and the strength of the medium-thickness steel plate can not be ensured to meet the requirement of Q890D ultrahigh-strength steel.
In some optional embodiments, the rough rolling comprises a first rough rolling and a second rough rolling, the rolling temperature of the first rough rolling is 1050 ℃ to 1150 ℃, the rolling temperature of the second rough rolling is 880 ℃ to 900 ℃, and the rolling temperature of the second rough rolling is 840 ℃ to 870 ℃.
In the embodiment of the application, the rolling temperature of the first rough rolling is 1050-1150 ℃, so that the initial forming of austenite grains in the rough rolling process can be ensured in the temperature range, and the preparation for fully extruding the austenite grains in the subsequent rolling stage is made; when the temperature is higher or lower than the end value of the range, the austenite grains are not suitable for extrusion in the rolling stage, and the steel plate cannot be ensured to be in a proper strength range.
The rolling temperature of the second rough rolling is 880-900 ℃, and the positive effect is that in the temperature range, complete forming of austenite crystal grains in the rough rolling process can be ensured, and preparation is made for fully extruding the austenite crystal grains in the subsequent rolling stage; when the temperature is greater than or less than the end value of the range, the size of austenite grains is not suitable for extruding the bulk austenite grains in the rolling stage, and the steel plate cannot be ensured to be in a proper strength range.
The finish rolling temperature of the second rough rolling is 840-870 ℃, and the positive effect is that in the temperature range, austenite grains in the metallographic structure of the steel plate after the rough rolling can be stably formed, so that sufficient temperature is provided for subsequent austenite grain transformation; when the temperature value is larger than or smaller than the end value of the range, austenite in a metallographic structure is unstable, and the strength of a subsequent steel plate is influenced.
In some alternative embodiments, the reduction rate of the last 2 passes of the first rough rolling is greater than or equal to 18%.
In the embodiment of the application, the positive effect that the reduction rate of the last 2 passes of the first rough rolling is more than or equal to 18 percent is that in the range of the reduction rate, austenite grains can be effectively ensured to be flattened, so that the area of a grain boundary is increased, recrystallization nucleation points are increased, fine and uniform austenite grains are further formed, and the completeness of subsequent phase change is ensured; when the rolling reduction value is less than the end value of the range, austenite grains cannot be effectively flattened, so that the subsequent phase change cannot be completely carried out, and the strength of the final ultrahigh-strength steel is influenced.
In some alternative embodiments, the thickness of the intermediate blank is greater than or equal to 110 mm.
In the embodiment of the application, the positive effect that the thickness of the intermediate billet is more than or equal to 110mm is that in the range, the thickness of the steel plate obtained subsequently can be ensured to be 60-70 mm, and the steel plate is ensured to meet the requirement of Q890D ultrahigh-strength steel; when the thickness of the intermediate billet is less than the end value of the range, the thickness of the steel plate is reduced, and meanwhile, the steel plate can not meet the requirement of Q890D ultrahigh-strength steel.
In some optional embodiments, the tempering treatment has a temperature rise rate of 1.6min/mm to 2.0 min/mm.
In the embodiment of the application, the positive effect that the temperature rise rate of the tempering treatment is 1.6 min/mm-2.0 min/mm is that in the rate range, the steel plate after finish rolling can be further subjected to phase change, the structure form is adjusted, and carbides are precipitated, so that the microstructure is changed into a dual-phase structure containing lath martensite and granular bainite, and the final ultrahigh-strength steel is in accordance with the standard of Q890D ultrahigh-strength steel; when the temperature rise rate is larger or smaller than the end point value of the range, the phase change is influenced, so that the microstructure can not be completely transformed, and the strength of the ultrahigh-strength steel is influenced.
Example 1
As shown in figure 1, the method for producing the Q890D ultra-high strength steel medium plate by on-line quenching comprises the following steps:
s1, obtaining a casting blank after continuous casting, wherein the size of the casting blank is 300mm multiplied by 2000mm multiplied by 3350 mm;
s2, heating and rough rolling a casting blank before rolling to obtain an intermediate blank;
s3, carrying out finish rolling, on-line quenching cooling and heat treatment on the intermediate billet to obtain medium-thickness Q890D ultrahigh-strength steel;
wherein the heat treatment comprises tempering treatment and heat preservation treatment, the end point temperature of the tempering treatment is 610 ℃, the heat preservation treatment is carried out by keeping the end point temperature of the tempering treatment, and the time of the heat preservation treatment is 70 min;
the rolling reduction of the rough rolling in the last 3 passes is respectively as follows: 39.3mm, 39.3mm and 38.8 mm;
the size of the Q890D ultrahigh-strength steel is 70mm multiplied by 2000mm multiplied by 14357 mm;
during the water cooling process, the cooling device swings back and forth at the speed of 0.5m/s to enhance the cooling intensity.
The Q890D ultrahigh-strength steel comprises the following chemical components in percentage by mass: c: 0.5%, Si: 0.24%, Mn: 1.22%, P: 0.008%, S: 0.0009%, Cr: 0.49%, Mo: 0.54%, Ni: 0.39%, Ti: 0.0014%, Nb: 0.022%, V: 0.048%, B: 0.0014%, Alt: 0.022 percent, and the balance of Fe and inevitable impurities.
CEV of Q890D ultrahigh strength steel was 0.59, and Pcm of Q890D ultrahigh strength steel was 0.29.
The initial temperature of the in-line cooling was 828 ℃ and the re-reddening temperature in the in-line cooling zone was 178 ℃.
The on-line cooling rate was 22 ℃/s.
The final temperature of heating before rolling was 1194 ℃, and the total time of heating before rolling was 278 min.
The rough rolling comprises first rough rolling and second rough rolling, wherein the rolling temperature of the first rough rolling is 1145 ℃, the rolling temperature of the second rough rolling is 898 ℃, and the final rolling temperature of the second rough rolling is 855 ℃.
The reduction ratios of the last 2 passes of the first rough rolling were 20.2% and 25.0%, respectively.
The thickness of the intermediate blank is 110 mm.
The temperature rise rate of the tempering treatment is 1.6 min/mm-2.0 min/mm.
Example 2
Comparing example 2 with example 1, example 2 differs from example 1 in that:
the heat treatment comprises tempering treatment and heat preservation treatment, wherein the end point temperature of the tempering treatment is 610 ℃, the heat preservation treatment is carried out by keeping the end point temperature of the tempering treatment, and the heat preservation treatment time is 60 min;
the rolling reduction of the rough rolling in the last 3 passes is respectively as follows: 39.5mm, 39.3mm and 38.9 mm;
the size of the Q890D ultrahigh-strength steel is 60mm multiplied by 2200mm multiplied by 15227 mm;
during the water cooling process, the cooling device swings back and forth at the speed of 0.5m/s to enhance the cooling intensity.
The Q890D ultrahigh-strength steel comprises the following chemical components in percentage by mass: c: 0.15%, Si: 0.23%, Mn: 1.21%, P: 0.008%, S: 0.0012%, Cr: 0.50%, Mo: 0.55%, Ni: 0.38%, Ti: 0.0014%, Nb: 0.022%, V: 0.049%, B: 0.0014%, Alt: 0.024 percent, and the balance of Fe and inevitable impurities.
CEV of Q890D ultrahigh strength steel was 0.59, and Pcm of Q890D ultrahigh strength steel was 0.29.
The initial temperature of the in-line cooling was 822 ℃ and the re-reddening temperature in the in-line cooling zone was 154 ℃.
The rate of in-line cooling was 22 ℃/s.
The end point temperature of heating before rolling is 1197 ℃, and the total time of heating before rolling is 265 min.
The rough rolling comprises first rough rolling and second rough rolling, wherein the rolling temperature of the first rough rolling is 1145 ℃, the rolling temperature of the second rough rolling is 899 ℃, and the finish rolling temperature of the second rough rolling is 854 ℃.
The reduction ratios of the last 2 passes of the first rough rolling were 20.4% and 25.2%, respectively.
The thickness of the intermediate blank is 110 mm.
Comparative example 1
Comparative example 1 is compared with example 1, and comparative example 1 differs from example 1 in that:
the terminal temperature of the tempering treatment is 580 ℃, the heat preservation treatment is carried out at the terminal temperature of the tempering treatment, and the heat preservation treatment time is 50 min;
the rolling reduction of the rough rolling of the last 3 passes is less than or equal to 36 mm;
the thickness of the Q890D ultrahigh-strength steel is 70 mm.
Comparative example 2
Comparative example 1 is compared to example 1, and comparative example 2 differs from example 1 in that:
the terminal temperature of the tempering treatment is 630 ℃, the heat preservation treatment is carried out at the terminal temperature of the tempering treatment, and the heat preservation treatment time is 75 min;
the thickness of the Q890D ultrahigh-strength steel is 60 mm.
Related experiments:
the super-strong steels obtained in examples 1 to 2 and comparative examples 1 to 2 were collected and subjected to performance tests, and the results are shown in table 1.
Test methods of the related experiments:
yield strength: the determination is carried out according to the standard GB/T228;
tensile strength: the determination is carried out according to the standard GB/T228;
elongation after fracture: the determination is carried out according to the standard GB/T228;
-20 ℃ work of impact: the determination is carried out according to the standard GB/T229;
TABLE 1
Figure BDA0003658313620000091
Specific analysis of table 1: elongation after fracture
The yield strength refers to the yield limit of the produced steel plate when the steel plate has yield phenomenon, namely the stress resisting micro plastic deformation, and the larger the yield strength is, the higher the yield limit of the steel plate is.
The tensile strength refers to the maximum stress value which can be borne by the prepared steel plate before the steel plate is broken, and the larger the tensile strength is, the larger the maximum stress value which can be borne by the steel plate before the steel plate is broken is.
The elongation after fracture refers to the percentage of the elongation of the gauge length of the steel plate after the steel plate is subjected to tensile fracture to the original gauge length, and the higher the elongation after fracture is, the better the toughness of the steel plate is.
The impact energy at the temperature of-20 ℃ refers to the impact force borne by the steel plate under the low-temperature condition, and the larger the impact energy is, the stronger the impact resistance of the steel plate is.
From the data of examples 1-2, it can be seen that:
by adopting the method, the performance of the steel plate with the thickness of 60-70 mm can be effectively ensured to meet the standard, and the steel plate has abundant mechanical properties, such as yield allowance of 107MPa, tensile allowance of 98MPa, elongation allowance of 4 percent and impact performance allowance of more than 50J in the steel plate in example 1; the steel plate in the embodiment 2 has yield allowance of 115MPa, tensile allowance of 108MPa, elongation allowance of 3.5% and impact performance allowance of more than 50J, and can meet the requirements of manufacturing industries such as engineering machinery and mining machinery.
From the data of comparative examples 1-2, it can be seen that:
the tempering temperature is lower than the set temperature of the invention, the heat preservation time is shorter, when the reduction of the rough rolling in the last 3 passes is smaller, the tensile property can exceed the standard range, and the impact energy is relatively influenced; the tempering temperature is higher than the set temperature of the invention, and the tensile property is less than the standard when the heat preservation time is longer.
One or more technical solutions in the embodiments of the present application at least have the following technical effects or advantages:
(1) according to the method provided by the embodiment of the application, rolling is performed through the large-pass reduction in the rough rolling stage, austenite grains can be guaranteed to be flattened, then on-line cooling is performed, phase transformation strengthening in a steel plate after finish rolling is achieved, finally, through heat treatment and heat preservation treatment, the microstructure of the steel plate can be effectively adjusted, carbides can be precipitated, the microstructure of the steel plate can be converted into a dual-phase structure containing lath martensite and granular bainite, and effective preparation of ultra-high-strength steel with the thickness of 60-70 mm is guaranteed.
(2) The method provided by the embodiment of the application can effectively prepare the blank with the thickness of 300mm into the steel plate with the thickness of 60 mm-70 mm.
(3) According to the method provided by the embodiment of the application, the high-strength and high-toughness lath martensite and the granular bainite steel are obtained by utilizing the processes of online quenching and tempering, the Q890D high-strength steel plate with the thickness of 60-70 mm in an online quenching and tempering state can be produced, the yield allowance is more than 30MPa, the tensile allowance is more than 40MPa, the elongation allowance is 2-4%, and the impact performance allowance is more than 50J.
(4) The method provided by the embodiment of the application adopts on-line quenching cooling, and the on-line quenching shortens the process flow and reduces the cost.
The drawings illustrate:
FIG. 2 is a schematic diagram of a metallographic structure of a 70mm thick Q890D high-strength steel plate 1/4 after on-line quenching according to an embodiment of the present application;
FIG. 3 is a schematic diagram of a metallographic structure of a high-strength steel plate 1/4 of Q890D with a thickness of 70mm after tempering treatment according to an embodiment of the present application;
FIG. 4 is a schematic diagram of a metallographic structure of a 60mm thick Q890D high-strength steel plate 1/4 after on-line quenching according to an embodiment of the present application;
FIG. 5 is a schematic diagram of a metallographic structure of a 60mm thick Q890D high-strength steel plate 1/4 after tempering treatment.
As can be seen from fig. 2 to 5, according to the method of the present invention, a steel sheet having a dual phase structure including lath martensite and granular bainite can be effectively obtained, and the thickness of the Q890D super steel is within 60mm to 70 mm.
It is noted that, in this document, relational terms such as "first" and "second," and the like, may be used solely to distinguish one entity or action from another entity or action without necessarily requiring or implying any actual such relationship or order between such entities or actions. Also, the terms "comprises," "comprising," or any other variation thereof, are intended to cover a non-exclusive inclusion, such that a process, method, article, or apparatus that comprises a list of elements does not include only those elements but may include other elements not expressly listed or inherent to such process, method, article, or apparatus. Without further limitation, an element defined by the phrase "comprising an … …" does not exclude the presence of other identical elements in a process, method, article, or apparatus that comprises the element.
The endpoints of the ranges and any values disclosed herein are not limited to the precise range or value, and these ranges or values should be understood to encompass values close to these ranges or values. For ranges of values, between the endpoints of each of the ranges and the individual points, and between the individual points may be combined with each other to give one or more new ranges of values, and these ranges of values should be considered as specifically disclosed herein.
The foregoing are merely exemplary embodiments of the present invention, which enable those skilled in the art to understand or practice the present invention. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the generic principles defined herein may be applied to other embodiments without departing from the spirit or scope of the invention. Thus, the present invention is not intended to be limited to the embodiments shown herein but is to be accorded the widest scope consistent with the principles and novel features disclosed herein.

Claims (10)

1. A method for producing Q890D ultrahigh strength steel medium plate by online quenching, which is characterized by comprising the following steps:
obtaining a casting blank after continuous casting;
heating and rough rolling the casting blank before rolling to obtain an intermediate blank;
carrying out finish rolling, on-line quenching cooling and heat treatment on the intermediate billet to obtain medium-thickness Q890D ultrahigh-strength steel;
the heat treatment comprises tempering treatment and heat preservation treatment, wherein the end point temperature of the tempering treatment is 600-620 ℃, the heat preservation treatment is carried out at the end point temperature of the tempering treatment, and the heat preservation treatment lasts for 60-70 min;
the reduction of the rough rolling in the last 3 passes is more than or equal to 36 mm;
the thickness of the Q890D ultrahigh-strength steel is 60-70 mm.
2. The method of claim 1, wherein the chemical composition of the Q890D ultrahigh-strength steel comprises, in mass fraction: c: 0.14% -0.17%, Si: 0.20-0.50%, Mn: 1.00-1.50%, P is less than or equal to 0.015%, S is less than or equal to 0.003%, Cr: 0.30% -0.70%, Mo: 0.40-0.70%, Ni: 0.30-0.60%, Ti: 0.005-0.025%, Nb: 0.015% -0.040%, V: 0.03% -0.06%, B: 0.001% -0.0020%, Alt: 0.020-0.050% and the balance of Fe and inevitable impurities.
3. The method of claim 2, wherein Pcm of the Q890D ultrahigh strength steel is less than or equal to 0.35 for the Q890D ultrahigh strength steel.
4. The method of claim 1, wherein the initial temperature of the in-line cooling is 810 ℃ to 830 ℃ and the re-reddening temperature of the in-line cooling zone is 200 ℃ or less.
5. The method according to claim 1 or 4, wherein the rate of in-line cooling is 15 ℃/s to 30 ℃/s.
6. The method according to claim 1, wherein the end temperature of the heating before rolling is 1150-1210 ℃ and the total time of the heating before rolling is 260-450 min.
7. The method according to claim 1, wherein the rough rolling comprises a first rough rolling and a second rough rolling, the first rough rolling having a rolling temperature of 1050 ℃ to 1150 ℃, the second rough rolling having a rolling temperature of 880 ℃ to 900 ℃, and the second rough rolling having a finishing temperature of 840 ℃ to 870 ℃.
8. The method according to claim 7, wherein the reduction of the first rough rolling in the last 2 passes is equal to or greater than 18%.
9. The method according to claim 1, wherein the thickness of the intermediate blank is greater than or equal to 110 mm.
10. The method according to claim 1, wherein the temperature increase rate of the tempering treatment is 1.6min/mm to 2.0 min/mm.
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