CN114807556A - Method for producing Q960E ultrahigh-strength steel by online quenching - Google Patents

Method for producing Q960E ultrahigh-strength steel by online quenching Download PDF

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CN114807556A
CN114807556A CN202210573874.0A CN202210573874A CN114807556A CN 114807556 A CN114807556 A CN 114807556A CN 202210573874 A CN202210573874 A CN 202210573874A CN 114807556 A CN114807556 A CN 114807556A
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rolling
rough rolling
strength steel
temperature
treatment
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CN114807556B (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
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    • C21D1/18—Hardening; Quenching with or without subsequent tempering
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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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
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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
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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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
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
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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
    • C21D2211/008—Martensite

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Abstract

The application relates to the field of super-strong steel preparation, in particular to a method for producing Q960E super-strong steel 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 Q960E ultrahigh-strength steel; wherein the heat treatment comprises tempering treatment and heat preservation treatment, the end point temperature of the 7 tempering treatment is 50-590 ℃, and the time of the heat preservation treatment is 40-80 min; the rough rolling comprises first rough rolling and second rough rolling; the reduction of the last 3 passes of the first rough rolling is more than or equal to 36mm, and the reduction of the last 2 passes of the second rough rolling is more than or equal to 18 percent; rolling by the large-pass reduction of two times of rough rolling, performing online cooling, performing heat treatment, combining heat preservation treatment, effectively adjusting the structure and precipitating carbide, converting the microstructure of the steel plate into a dual-phase structure containing lath martensite and granular bainite, and ensuring the effective preparation of the ultra-high strength steel of 40-70 mm.

Description

Method for producing Q960E ultrahigh-strength steel by online quenching
Technical Field
The application relates to the field of super-strong steel preparation, in particular to a method for producing Q960E super-strong steel 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 Q960E 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 Q960E has the characteristics that: the structure is simple, the dead weight is light, the safety is high, the large dynamic and static loads can be borne, and the service time is long; at present, the production of medium-thickness specification steel plates of Q960E ultrahigh-strength steel mostly adopts a quenching and tempering state mode comprising (offline quenching and tempering), and very few Q960E ultrahigh-strength steel with the thickness below 50mm adopts an online quenching process, but on Q960E ultrahigh-strength steel with the thickness specification above 50mm, the ultrahigh-strength steel obtained only by adopting the online quenching mode cannot meet the requirements of manufacturing industries of engineering machinery, mining machinery and the like.
Although the mode of combining online quenching and tempering exists at present, when the ultrahigh steel is produced by online quenching and tempering, the cooling, tempering and the like of the high-strength steel need to be controlled in real time within the thickness range of 40-70 mm of the final steel product, so that the strength of the finally obtained high-strength steel is too low, and the high-strength steel is difficult to conform to the application environment of Q960E type high-strength steel, and how to improve the strength of the high-strength steel under the condition of combining online quenching and tempering is a technical problem which needs to be solved urgently at present.
Disclosure of Invention
The application provides a method for producing Q960E ultrahigh-strength steel by on-line quenching, which aims to solve the technical problem that the strength of the high-strength steel is difficult to meet the requirement of Q960E type high-strength steel under the condition of on-line quenching and tempering in the prior art.
In a first aspect, the present application provides a method for producing Q960E ultra-high strength steel 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 Q960E ultrahigh-strength steel meeting the strength requirement;
the heat treatment comprises tempering treatment and heat preservation treatment, wherein the end point temperature of the tempering treatment is 570-590 ℃, the heat preservation treatment is carried out at the end point temperature of the tempering treatment, and the heat preservation treatment lasts 40-80 min;
the rough rolling comprises first rough rolling and second rough rolling;
the reduction of the last 3 passes of the first rough rolling is more than or equal to 36mm, and the reduction of the last 2 passes of the second rough rolling is more than or equal to 18%;
the thickness of the Q960E ultrahigh strength steel is 40-70 mm.
Optionally, the chemical composition of the Q960E ultrahigh-strength steel comprises, by mass fraction: 0.14 to 0.17 percent of C, 0.20 to 0.50 percent of Si, 1.00 to 1.50 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.003 percent of S, 0.30 to 0.70 percent of Cr, 0.40 to 0.70 percent of Mo, 0.30 to 0.60 percent of Ni, 0.005 to 0.025 percent of Ti, 0.015 to 0.040 percent of Nb, 0.03 to 0.06 percent of V, 0.001 to 0.0020 percent of B, 0.020 to 0.050 percent of Alt, and the balance of Fe and inevitable impurities.
Optionally, CEV of the Q960E ultrahigh-strength steel is less than or equal to 0.65, and Pcm of the Q960E ultrahigh-strength steel is less than or equal to 0.35.
Optionally, the in-line cooling comprises: cooling in a mode of swinging the cooling device back and forth in the cooling process so as to enhance the cooling strength;
the initial temperature of the on-line cooling is 810-830 ℃, and the temperature of the red returning of the on-line cooling area is less than or equal to 200 ℃.
Optionally, the speed of the online 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 rolling temperature of the first rough rolling is 1050-1150 ℃.
Optionally, the rolling temperature of the second rough rolling is 880-900 ℃, and the finish rolling temperature of the second rough rolling is 840-870 ℃.
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:
according to the method for producing the Q960E ultrahigh-strength steel through online quenching, firstly, two times of rough rolling are adopted in the rough rolling stage, and the two times of rough rolling are rolled with large pass rolling reduction, so that austenite crystal grains can be guaranteed to be flattened, the grain boundary area is increased, the recrystallization nucleation points are increased, fine and uniform austenite crystal grains are further formed, the phase transformation strengthening in the steel plate after finish rolling is realized through online cooling, finally, the microstructure after phase transformation is further stably changed through heat treatment by utilizing the terminal temperature of tempering treatment, the heat preservation treatment is combined, the structure can be effectively adjusted, carbides are precipitated, the microstructure of the steel plate can be further converted into a dual-phase structure containing martensite laths and granular bainite, the strength of the ultrahigh-strength steel with the thickness of 40 mm-70 mm meets the standard of the Q960E ultrahigh-strength steel, and the strength of the ultrahigh-strength steel prepared under the condition of online quenching and tempering is guaranteed to meet the standard of the Q960Q 960E ultrahigh-strength steel The method is accurate.
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 or technical solutions in the prior art of the present invention, 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 to obtain other drawings without inventive labor.
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 the metallographic structure of a 70mm thick Q960E high-strength steel plate 1/4 after on-line quenching according to an embodiment of the present disclosure;
FIG. 3 is a schematic diagram of a metallographic structure of a high-strength steel plate 1/4 which is tempered and has a thickness of 70mm and is Q960E according to an embodiment of the present disclosure;
FIG. 4 is a schematic diagram of the metallographic structure of a 40mm thick Q960E high-strength steel plate 1/4 after on-line quenching according to an embodiment of the present disclosure;
FIG. 5 is a schematic diagram of the metallographic structure of a 40mm thick Q960E high-strength steel plate 1/4 after tempering treatment according to the embodiment of the present application.
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 obtained by a person of ordinary skill in the art based on the embodiments in the present application without making creative efforts 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 Q960E ultra-high strength steel 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 Q960E ultrahigh-strength steel meeting the strength requirement;
the heat treatment comprises tempering treatment and heat preservation treatment, wherein the end point temperature of the tempering treatment is 570-590 ℃, the heat preservation treatment is carried out at the end point temperature of the tempering treatment, and the heat preservation treatment lasts 40-80 min;
the rough rolling comprises first rough rolling and second rough rolling;
the reduction of the last 3 passes of the first rough rolling is more than or equal to 36mm, and the reduction of the last 2 passes of the second rough rolling is more than or equal to 18%;
the thickness of the Q960E ultrahigh strength steel is 40-70 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 Q960E 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 within 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 Q960E 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 first rough rolling in the last 3 passes is more than or equal to 36mm is that in the reduction range, the austenite grains can be effectively ensured to be preliminarily flattened, so that the area of a grain boundary is preliminarily increased, the recrystallization nucleation points are preliminarily increased, and then the fine and uniform austenite grains can be conveniently formed in the follow-up process, so that the completeness of the follow-up 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.
The reduction rate of the second rough rolling for the last 2 passes is more than or equal to 18 percent, and the positive effect 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 optional embodiments, the chemical composition of the Q960E ultrahigh strength steel comprises, in mass fraction: 0.14 to 0.17 percent of C, 0.20 to 0.50 percent of Si, 1.00 to 1.50 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.003 percent of S, 0.30 to 0.70 percent of Cr, 0.40 to 0.70 percent of Mo, 0.30 to 0.60 percent of Ni, 0.005 to 0.025 percent of Ti, 0.015 to 0.040 percent of Nb, 0.03 to 0.06 percent of V, 0.001 to 0.0020 percent of B, 0.020 to 0.050 percent of Alt, 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 easily generated, and the toughness of the martensitic 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 steel can be improved, and martensite and bainite tissues 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 that the mass fraction of Alt is 0.020-0.050% is used as a deoxidizer, crystal grains can be refined, and impact toughness is improved; 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 Q960E ultra-high strength steel is less than or equal to 0.65, and the Pcm of the Q960E 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 Q960E ultra-high strength steel is less than or equal to 0.65 is that the strength, hardness and toughness of the ultra-high strength steel can be effectively ensured to meet the standard within the range of the carbon equivalent.
The positive effect that Pcm of the Q960E 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 less than or equal to 200 ℃.
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 positive effect that the online cooling speed is 15-30 ℃/s 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 Q960E ultrahigh-strength steel; when the temperature 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 Q960E 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 Q960E 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 Q960E ultrahigh-strength steel.
In some alternative embodiments, the opening temperature of the first rough rolling is 1050 ℃ to 1150 ℃.
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 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.
In some optional embodiments, the rolling temperature of the second rough rolling is 880 ℃ to 900 ℃, and the finishing temperature of the second rough rolling is 840 ℃ to 870 ℃.
In the embodiment of the application, the rolling temperature of the second rough rolling is 880-900 ℃, and the positive effect is that in the temperature range, the complete forming of austenite grains in the rough rolling process can be ensured, and the preparation is fully made for the extrusion of the austenite 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 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 Q960E 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 the steel plate can not meet the requirement of Q960E 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 meets the standard of Q960E ultrahigh-strength steel; when the temperature rise rate is larger or smaller than the end 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 fig. 1, a method for producing Q960E ultra-high strength steel by on-line quenching, comprising:
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 Q960E ultrahigh-strength steel meeting the strength requirement;
the heat treatment comprises tempering treatment and heat preservation treatment, wherein the end point temperature of the tempering treatment is 580 ℃, the heat preservation treatment is carried out at the end point temperature of the tempering treatment, and the heat preservation treatment lasts for 70 min;
the rough rolling comprises first rough rolling and second rough rolling;
the reduction of the first rough rolling in the last 3 passes is 39.6mm, 39.6mm and 39.3mm respectively, and the reduction of the second rough rolling in the last 2 passes is 20.9% and 26.3% respectively;
the size of the Q960E 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 strength.
The Q960E ultrahigh-strength steel comprises the following chemical components in percentage by mass: 0.15% of C, 0.23% of Si, 1.21% of Mn, 0.007% of P, 0.0008% of S, 0.48% of Cr, 0.55% of Mo, 0.37% of Ni, 0.0015% of Ti, 0.021% of Nb, 0.049% of V, 0.0013% of B, 0.023% of Alt and the balance of Fe and inevitable impurities.
CEV of Q960E ultrahigh strength steel was 0.59, and Pcm of Q960E 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 181 ℃.
The on-line cooling rate was 23 ℃/s.
The end temperature of heating before rolling was 1192 ℃, and the total time of heating before rolling was 266 min.
The open rolling temperature for the first rough rolling was 1145 ℃.
The opening rolling temperature of the second rough rolling is 892 ℃, and the finishing rolling temperature of the second rough rolling is 851 ℃.
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 580 ℃, 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 40 min;
the reduction of the first rough rolling in the last 3 passes is 39.2mm, 39.2mm and 39.0mm respectively, and the reduction of the second rough rolling in the last 2 passes is 20.4% and 26.1% respectively;
the size of the Q960E ultrahigh strength steel is 40mm multiplied by 2200mm multiplied by 22840 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 Q960E ultrahigh-strength steel comprises the following chemical components in percentage by mass: 0.15% of C, 0.23% of Si, 1.22% of Mn, 0.008% of P, 0.0010% of S, 0.49% of Cr, 0.54% of Mo, 0.38% of Ni, 0.0016% of Ti, 0.021% of Nb, 0.050% of V, 0.0014% of B, 0.024% of Alt, and the balance of Fe and inevitable impurities.
CEV of Q960E ultrahigh strength steel was 0.59, and Pcm of Q960E ultrahigh strength steel was 0.29.
The initial temperature of the in-line cooling was 820 ℃ and the re-reddening temperature of the in-line cooling zone was 101 ℃.
The on-line cooling rate was 25 ℃/s.
The final temperature of heating before rolling is 1190 ℃, and the total time of heating before rolling is 272 min.
The open rolling temperature for the first rough rolling was 1145 ℃.
The opening rolling temperature of the second rough rolling is 899 ℃, and the finishing rolling temperature of the second rough rolling is 855 ℃.
The thickness of the intermediate blank is 110 mm.
Comparative example 1
Comparative example 1 and example 1 were compared, and comparative example 1 and example 1 were distinguished in that:
the terminal temperature of the tempering treatment is 550 ℃, the heat preservation treatment is carried out at the terminal temperature of the tempering treatment, and the heat preservation treatment time is 30 min;
the rough rolling comprises first rough rolling and second rough rolling;
the reduction of the first rough rolling of the last 3 passes is less than 36mm, and the reduction of the second rough rolling of the last 2 passes is less than 18%;
the thickness of the Q960E ultrahigh-strength steel is 40 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 610 ℃, the heat preservation treatment is carried out at the terminal temperature of the tempering treatment, and the heat preservation treatment time is 90 min;
the thickness of the Q960E 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;
-40 ℃ work of impact: the determination is carried out according to the standard GB/T229;
TABLE 1
Figure BDA0003658326540000091
Specific analysis of table 1: elongation after fracture
The yield strength refers to the yield limit of the prepared steel plate when the steel plate is subjected to a yield phenomenon, namely, the stress resisting micro plastic deformation, and the higher 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 minus 40 ℃ 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 medium thickness of 40-70 mm can be effectively ensured to meet the standard, and the steel plate has abundant mechanical properties, such as yield surplus of 80MPa, tensile surplus of 108MPa, elongation surplus of 2.5 percent and impact performance surplus of more than 30J in the steel plate in example 1; the yield margin of the steel plate in the embodiment 2 is 98Mpa, the tensile margin is 160Mpa, the elongation margin is 3.5%, and the impact performance margin is more than 30J, so that the steel plate 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; and the tempering temperature is higher than the set temperature of the invention, and the yield and tensile property can be lower 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, firstly, the rough rolling stage adopts a twice rough rolling mode, rolling is carried out with large-pass rolling reduction, austenite grains can be guaranteed to be flattened, then, the phase transformation strengthening in the steel plate after finish rolling is realized through online cooling, finally, the microstructure of the steel plate can be effectively adjusted and carbide can be precipitated through heat treatment and heat preservation treatment, further, the microstructure of the steel plate can be converted into a dual-phase structure containing lath martensite and granular bainite, and further, the effective preparation of the ultrahigh-strength steel with the thickness of 40-70 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 40 mm-70 mm.
(3) According to the method provided by the embodiment of the application, the lath martensite and the granular bainite steel with high strength and high toughness are obtained by utilizing the processes of online quenching and tempering, the Q960E state high-strength steel plate with the thickness of 40-70 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 30J.
(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.
(5) According to the method provided by the embodiment of the application, due to the adoption of the low-content design with the Ni content of 0.30-0.60%, the addition of expensive metals can be reduced, and the cost is reduced.
The drawings illustrate:
FIG. 2 is a schematic diagram of the metallographic structure of a 70mm thick Q960E high-strength steel plate 1/4 after on-line quenching according to an embodiment of the present disclosure;
FIG. 3 is a schematic diagram of a metallographic structure of a high-strength steel plate 1/4 which is tempered and has a thickness of 70mm and is Q960E according to an embodiment of the present disclosure;
FIG. 4 is a schematic diagram of the metallographic structure of a 40mm thick Q960E high-strength steel plate 1/4 after on-line quenching according to an embodiment of the present disclosure;
FIG. 5 is a schematic diagram of the metallographic structure of a 40mm thick Q960E 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 Q960E super steel is within 40mm 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 such ranges or values should be understood to encompass values close to those 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 Q960E ultra-high strength steel 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 Q960E ultrahigh-strength steel meeting the strength requirement;
the heat treatment comprises tempering treatment and heat preservation treatment, wherein the end point temperature of the tempering treatment is 570-590 ℃, the heat preservation treatment is carried out at the end point temperature of the tempering treatment, and the heat preservation treatment lasts 40-80 min;
the rough rolling comprises first rough rolling and second rough rolling;
the reduction of the last 3 passes of the first rough rolling is more than or equal to 36mm, and the reduction of the last 2 passes of the second rough rolling is more than or equal to 18%;
the thickness of the Q960E ultrahigh strength steel is 40-70 mm.
2. The method of claim 1, wherein the chemical composition of the Q960E ultra-high 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 the CEV of the Q960E ultra-high strength steel is less than or equal to 0.65, and the Pcm of the Q960E ultra-high strength steel is less than or equal to 0.35.
4. The method of claim 1, wherein the in-line cooling comprises: cooling in a mode of swinging the cooling device back and forth in the cooling process so as to enhance the cooling strength;
the initial temperature of the on-line cooling is 810-830 ℃, and the temperature of the red returning of the on-line cooling area is less than or equal to 200 ℃.
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, characterized in that the opening temperature of the first rough rolling is 1050-1150 ℃.
8. The method according to claim 1 or 7, wherein 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 ℃.
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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