CN113025924A - Steel for ultrahigh-strength dual-phase corrosion-resistant stirring tank and production process thereof - Google Patents
Steel for ultrahigh-strength dual-phase corrosion-resistant stirring tank and production process thereof Download PDFInfo
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- CN113025924A CN113025924A CN202110177792.XA CN202110177792A CN113025924A CN 113025924 A CN113025924 A CN 113025924A CN 202110177792 A CN202110177792 A CN 202110177792A CN 113025924 A CN113025924 A CN 113025924A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
Abstract
The invention particularly relates to steel for an ultrahigh-strength dual-phase corrosion-resistant stirring tank and a production process thereof, belonging to the technical field of steel preparation, wherein the steel comprises the following chemical components in percentage by mass: c: 0.20% -0.24%, S: 1.50% -1.75%, Mn: 1.80% -2.10%, Alt: 0.030% -0.065%, P: less than or equal to 0.015 percent, S: less than or equal to 0.004%, B: 0.0005 to 0.0009%, Sb: 0.08-0.12%, Sn: 0.020-0.035%, and the balance of Fe and inevitable impurities; the steel plate has the advantages of easy forming, high strength, high wear resistance, good corrosion resistance, weldability and the like, and solves the problems of cold forming cracking of a high-strength steel plate, softening of a heat affected zone after welding, poor wear resistance and corrosion resistance, heavy tank body and the like; the steel plate has good stability, and avoids the defects of bulging or collapse in the pressurizing process.
Description
Technical Field
The invention belongs to the technical field of steel preparation, and particularly relates to steel for an ultrahigh-strength dual-phase corrosion-resistant stirring tank and a production process thereof.
Background
The concrete mixing and transporting truck is a special truck for transporting concrete for construction; due to its shape, it is also commonly referred to as a vivipara. These trucks are equipped with cylindrical mixing drums to carry the mixed concrete. The mixing drum can be always kept to rotate in the transportation process so as to ensure that the carried concrete can not be solidified. After the concrete is conveyed, water is usually used for flushing the interior of the mixing drum to prevent the hardened concrete from occupying space. At present, the steel for the stirring tank is generally made of Q355B material, the strength is low, the lightweight is not facilitated, part of enterprises begin to use steel with the tensile strength of 520MPa, and a few enterprises perform production trial production of the 900MPa ultrahigh-strength stirring tank. The prior patent technology discloses a production technology of steel for a stirring tank with the tensile strength grade of 520MPa-650MPa, and a steel product for the stirring tank with a higher strength grade is not reported.
In order to meet the requirements of high strength, long service life, easy forming and light weight of steel for the stirring tank, the stirring tank with different volumes manufactured by adopting higher-strength steel is the next development direction. The steel for a stirring tank is required to have not only high strength but also good plate shape, cold formability, weldability and the like, and currently, the steel for a stirring tank is generally used as Q355B.
The applicant finds in the course of the invention that: the Q355B material has low strength and is easy to soften after welding, and due to the adoption of the high-carbon equivalent design, the structure has obvious banded structures, the cold forming is easy to crack, the fatigue life is short and the like; in addition, because the strength is low, the tank is very easy to wear and scrap in the service process, and the service life of the tank body is influenced.
The traditional ultrahigh-strength steel mainly takes a tempered martensite structure as a matrix and is produced by adopting an online quenching or offline heat treatment process, and the steel plate has higher yield ratio and is not beneficial to tank-making forming and tailor-welding of the stirring tank.
Disclosure of Invention
In view of the above problems, the present invention has been made to provide a steel for an ultra high strength dual phase corrosion resistant agitator tank and a process for producing the same, which overcome the above problems or at least partially solve the above problems.
The embodiment of the invention provides steel for an ultrahigh-strength dual-phase corrosion-resistant stirring tank, which comprises the following chemical components in percentage by mass:
c: 0.20% -0.24%, S: 1.50% -1.75%, Mn: 1.80% -2.10%, Alt: 0.030% -0.065%, P: less than or equal to 0.015 percent, S: less than or equal to 0.004%, B: 0.0005 to 0.0009%, Sb: 0.08-0.12%, Sn: 0.020-0.035%, and the balance of Fe and inevitable impurities.
Optionally, the steel comprises the following chemical components in percentage by mass:
c: 0.21% -0.23%, S: 1.55-1.70%, Mn: 1.90% -2.00%, Alt: 0.040% -0.055%, P: less than or equal to 0.015 percent, S: less than or equal to 0.004%, B: 0.0006% -0.0008%, Sb: 0.09% -0.11%, Sn: 0.025 to 0.030 percent, and the balance of Fe and inevitable impurities.
Optionally, the metallographic structure of the steel is, in terms of volume fraction: 55% or more of bainite, 35% or more of polygonal ferrite, and 5% or less of M-A component.
Optionally, the grain size of the polygonal ferrite is 3.8 μm to 5.5 μm.
Based on the same inventive concept, the embodiment of the invention also provides a production process of the steel for the ultra-high-strength dual-phase corrosion-resistant stirring tank, which comprises the following steps:
obtaining a casting blank of the steel for the ultrahigh-strength dual-phase corrosion-resistant stirring tank;
and (3) reheating the casting blank, rough rolling, finish rolling and continuous rolling, cooling, coiling, slow cooling and leveling to obtain the steel for the ultrahigh-strength dual-phase corrosion-resistant stirring tank.
Optionally, in the reheating of the casting blank, a hot charging and heating delivery process is adopted, the charging temperature is more than or equal to 600 ℃, the reheating temperature of the casting blank is controlled at 1180-1220 ℃, and the heating time is less than 180 min.
Optionally, in the rough rolling, 6 passes of rolling are adopted, and the outlet temperature of the rough rolling is 980-1030 ℃.
Optionally, the method is characterized in that in the precision rolling and continuous rolling, 6 racks are adopted for continuous rolling, the thickness of a precision-rolled intermediate billet is controlled to be 40-54 mm, the inlet temperature of the precision rolling is 980-1030 ℃, and the outlet temperature of the precision rolling is 810-840 ℃.
Optionally, in the cooling, four-stage cooling is adopted, and the first-stage cooling: air cooling to 750 ℃, and second-stage cooling: water cooling to 680 ℃, and third stage cooling: air cooling to 550 ℃, and cooling in the fourth stage: water cooling to 350 ℃.
Optionally, the coiling temperature is 310-350 ℃.
One or more technical solutions in the embodiments of the present invention have at least the following technical effects or advantages:
the steel for the ultra-high-strength dual-phase corrosion-resistant stirring tank provided by the embodiment of the invention comprises the following chemical components in percentage by mass: c: 0.20% -0.24%, S: 1.50% -1.75%, Mn: 1.80% -2.10%, Alt: 0.030% -0.065%, P: less than or equal to 0.015 percent, S: less than or equal to 0.004%, B: 0.0005 to 0.0009%, Sb: 0.08-0.12%, Sn: 0.020-0.035%, and the balance of Fe and inevitable impurities; the design of C, Si and Mn with medium and high content is adopted, the cheap strengthening effect of C, Si and Mn is fully exerted to improve the strength, the ferrite proportion and the corrosion resistance are improved by adding high Si, a bainite structure is obtained by adding a small amount of B element, the microalloying thought of Sb-Sn composite addition is adopted, the alloy cost is effectively controlled and reduced, the steel plate has the advantages of easiness in forming, high strength, high wear resistance, good corrosion resistance, weldability and the like, and the problems of cold forming cracking of a high-strength steel plate, softening of a heat affected zone after welding, poor wear resistance and corrosion resistance, heavy tank body and the like are solved; the steel plate has good stability, and avoids the defects of bulging or collapse in the pressurizing process.
The foregoing description is only an overview of the technical solutions of the present invention, and the embodiments of the present invention are described below in order to make the technical means of the present invention more clearly understood and to make the above and other objects, features, and advantages of the present invention more clearly understandable.
Drawings
In order to more clearly illustrate the technical solutions in the embodiments of the present invention, the drawings needed to be used in the description of the embodiments are briefly introduced below, and it is obvious that the drawings in the following description are some embodiments of the present invention, and it is obvious for those skilled in the art to obtain other drawings based on the drawings without creative efforts.
FIG. 1 is a photograph showing the metallographic structure of steel for an ultra-high-strength dual-phase corrosion-resistant agitator tank according to an embodiment of the present invention.
Detailed Description
The present invention will be described in detail below with reference to specific embodiments and examples, and the advantages and various effects of the present invention will be more clearly apparent therefrom. It will be understood by those skilled in the art that these specific embodiments and examples are for the purpose of illustrating the invention and are not to be construed as limiting the invention.
Throughout the specification, unless otherwise specifically noted, terms used herein should be understood as having meanings as commonly used in the art. Accordingly, unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. If there is a conflict, the present specification will control.
Unless otherwise specifically stated, various raw materials, reagents, instruments, equipment and the like used in the present invention are commercially available or can be prepared by existing methods.
The stirring tank needs to meet the requirements of high strength, long service life, easy forming, light weight and the like, the steel prepared by the stirring tank not only needs high strength, but also needs materials with good plate shape, cold forming performance, welding performance and the like, the steel for the stirring tank generally adopts Q355B, and the applicant finds in the invention process that: the prior art has the following defects: (1) the steel strength level is low, the thickness of the tank body of the stirring tank is large, and the whole tank body and the stirring truck are difficult to realize light weight; (2) the wear resistance of steel is poor, the tank body is seriously worn in the service process, and the service life is short; (3) the steel basically has no corrosion resistance, low alloy steel Q355B commonly used in the prior art and steel for a 500MPa stirring tank are not added with corrosion resistant elements, and the service life of the stirring tank body is influenced due to the corrosion problem in the service process; the Q355B material has low strength and is easy to soften after welding, and due to the adoption of a high-carbon equivalent design, the structure has obvious banded structures, the cold forming is easy to crack, the fatigue life is short and the like; in addition, because the strength is low, abrasion and scrapping are easy to occur in the service process, and the service life of the tank body is influenced; the traditional 500 MPa-grade steel for the stirring tank mainly takes a tempered martensite structure as a matrix, and is produced by adopting an online quenching or offline heat treatment process, and a steel plate has a high yield ratio and is not beneficial to tank-making forming and tailor-welding of the stirring tank; (4) the high-strength steel is difficult to form, the resilience is not uniform, the tank body is difficult to splice, and a welding interface is easy to deform. The creative discovery of the applicant: the steel is designed by adopting the C, Si and Mn with medium and high content, the strength is improved by fully playing the cheap strengthening effect of the C, Si and Mn, the ferrite proportion and the corrosion resistance are improved by adding high Si, a bainite structure is obtained by adding a small amount of B element, the microalloying idea of Sb-Sn composite addition is adopted, the prepared steel has the characteristics of easy forming, high wear resistance and good corrosion resistance, and the alloy cost is effectively controlled and reduced.
According to an exemplary embodiment of the present invention, there is provided a steel for an ultra-high strength dual-phase corrosion-resistant agitator tank, the steel comprising the following chemical components in mass fraction: c: 0.20-0.24%, Si: 1.50% -1.75%, Mn: 1.80% -2.10%, Alt: 0.030% -0.065%, P: less than or equal to 0.015 percent, S: less than or equal to 0.004%, B: 0.0005 to 0.0009%, Sb: 0.08-0.12%, Sn: 0.020-0.035%, and the balance of Fe and inevitable impurities.
In the embodiment, the design of middle-high content C is adopted, and the main purpose is to improve the strength and the wear resistance of the material; obtaining a bainite structure with high hardness, wherein the upper limit of the addition needs to be controlled because C has great influence on the weldability and the toughness of steel; the carbon content adopted in the embodiment is 0.20-0.24%;
in the embodiment, a high-Si design is adopted, and the main purpose of adding Si is to promote the generation of polygonal ferrite, improve the ferrite proportion, improve the cold forming performance, reduce the subsequent tank making difficulty and improve the precision; the corrosion resistance of the material can be improved by adding high Si, but the toughness and weldability of the material are adversely affected by excessively high Si. Therefore, the content of the added silicon is 1.50 to 1.75 percent;
in the embodiment, manganese (Mn) has a solid solution strengthening effect and can improve the hardenability of the material, but segregation is easily generated when the manganese content is excessively high, the toughness of the material is reduced, and the weldability is reduced, wherein the manganese content is 1.8-2.1%;
in the embodiment, P is a harmful element, the performance of a welding joint is reduced, and the fatigue strength of the stirring tank is not ensured, so that the upper limit is controlled. Therefore, the phosphorus content added in this example is less than or equal to 0.015%
In the embodiment, S is a harmful element, and is not beneficial to ensuring the toughness and the fatigue life of the ultrahigh-strength steel. S can consume Ti element at the same time, reduce the effective titanium content in the steel and reduce various performance indexes of the material. Therefore, the upper limit of the addition should be controlled, therefore, the sulfur content added in this example is less than or equal to 0.004%;
in the embodiment, aluminum (Alt) is a deoxidizing element, so that the cleanliness and inclusion control level of steel are improved, and the aluminum content range is controlled to be 0.030-0.065%;
in this example, Sn is added to improve the corrosion resistance of the steel. Sn element can form a compact oxidation film on the surface of steel and change the potential of a matrix electrode to improve the corrosion resistance. Meanwhile, the Si-Cr-Sn added in the invention further increases the corrosion resistance of the surface of the steel. However, Sn is a low-melting point element, and addition of too much Sn adversely affects the soldering properties of the material. Therefore, 0.02-0.035% of tin is added in the embodiment;
in this example, Sb element was added to improve the corrosion resistance of the steel. Except that Sb element can form a compact oxide film on the surface and change the potential of a matrix electrode to improve the corrosion resistance, the invention accords with the condition that the added high Si can further improve the corrosion resistance of the surface of steel, and the Sn element is added in combination with Sb to improve the corrosion resistance of the material under the complex abrasion corrosion working condition environment of a stirring tank. Therefore, 0.08-0.12% of antimony is added in the embodiment;
the effect of adding B element in the embodiment is to control the type of the target structure and avoid the softening of the welding joint, replace part of Cr or Mo effect and reduce the alloy cost. By adding B and combining with a proper controlled cooling process, a medium-low temperature transformation structure with excellent corrosion resistance and a ratio of more than 55 is obtained. On the other hand, the addition of the element B can improve the hardenability of a welding heat affected zone and ensure the strength and the wear resistance of a welding joint. However, the upper limit should be controlled because too much boron is likely to adversely affect the toughness of the material. Therefore, the present invention adds 0.0005% to 0.0009% of the element B.
The chemical components and the mass fractions thereof are selected to solve the technical problems of cold forming cracking of the high-strength steel plate, softening of a heat affected zone after welding, poor wear resistance and corrosion resistance and heavy tank body, and the technical obstacles to be overcome are to accurately control the chemical components and production process parameters and reduce fluctuation.
As an alternative embodiment, the steel has the following chemical components in mass fraction: c: 0.21% -0.23%, S: 1.55-1.70%, Mn: 1.90% -2.00%, Alt: 0.040% -0.055%, P: less than or equal to 0.015 percent, S: less than or equal to 0.004%, B: 0.0006% -0.0008%, Sb: 0.09% -0.11%, Sn: 0.025 to 0.030 percent, and the balance of Fe and inevitable impurities.
As an alternative embodiment, the metallographic structure of the steel is, in volume fraction: the bainite steel is characterized in that the bainite steel comprises more than 55%, more than 35% of polygonal ferrite and less than 5% of M-A components, the strength of the steel can be effectively improved by adopting the above embodiment, and in order to achieve the above composition ratio, the production process needs to be accurately controlled, for example, the toughness and the corrosion resistance are prevented from being reduced due to coarse cementite laths by combining lower rolling temperature and accurate final cooling temperature control, so that the bainite steel can be more than 55%; the ferrite nucleation rate is improved through low-temperature rolling and rapid cooling, and a sufficient ferrite proportion, namely polygonal ferrite with a proportion of more than 35 percent, is ensured through air cooling in a ferrite phase transition region, and detailed operation is specifically described below, so to sum up, the control of the tissue type in the embodiment is realized through combination of phase transition control elements such as Mn and B and a precise controlled rolling and controlled cooling process; further improving the strength grade of the steel to more than 1000 MPa.
As an alternative embodiment, the grain size of the polygonal ferrite is 3.8 μm to 5.5 μm.
The ferrite grain size is controlled to be 3.8-5.5 microns, the cold forming performance of the steel plate is improved, the resilience is reduced, and the size precision of a welding joint is improved;
according to another exemplary embodiment of the present invention, there is provided a process for producing the above steel for an ultra high strength dual phase corrosion resistant agitator tank, the process comprising:
s1, obtaining a casting blank through smelting and continuous casting, wherein the casting blank comprises the following chemical components: carbon: 0.20 to 0.24 percent; silicon: 1.50% -1.75%; manganese: 1.80% -2.10%; aluminum: 0.030-0.065%; phosphorus: less than or equal to 0.015 percent; sulfur: less than or equal to 0.004 percent; boron: 0.0005% -0.0009%, antimony: 0.08-0.12%, tin: 0.020-0.035%, and the balance of iron and inevitable impurities;
s2, reheating a casting blank produced by smelting continuous casting, wherein the heating process of the casting blank adopts a hot charging and hot conveying process, the charging temperature is more than or equal to 600 ℃, the reheating temperature of the casting blank is 1180-1220 ℃, and the heat preservation time is less than 180 min.
And S3, after the casting blank is taken out of the heating furnace, rough rolling and 6-rack continuous finish rolling are carried out, wherein 6-pass reciprocating rolling is adopted for rough rolling, the inlet temperature of finish rolling is 980-1030 ℃, the thickness of an intermediate blank is 40-54 mm, 6-rack continuous rolling is adopted for finish rolling, and the finish rolling temperature is 810-840 ℃.
S4, cooling after rolling adopts a four-section cooling mode, the strip steel is subjected to finish rolling and air cooling to 750 ℃, the finishing temperature of the front section water cooling is 680 ℃, the starting temperature of the rear section water cooling is 550 ℃, the finishing temperature of the rear section cooling is 350 ℃, and the target coiling temperature is 310-350 ℃.
S5, straightening and transversely cutting the steel coil to form a finished product decoiling plate.
The content of P, S and the size and quantity of inclusions are strictly controlled in the smelting process, and a continuous casting slab is obtained. In order to improve the production efficiency, save energy and improve the quality of casting blanks, the continuously cast casting blanks enter a hot rolling heating furnace to be reheated at the temperature of higher than 600 ℃, the reheating temperature of the casting blanks is 1180-1220 ℃, and the heat preservation time is less than 180 min. The lower heating temperature is adopted because the steel grade has no indissolvable alloy elements, so that the energy consumption can be reduced as much as possible.
And 6-pass reciprocating rolling is adopted for rough rolling, the finish temperature of the rough rolling is 980-1030 ℃, and the target thickness of the intermediate blank after rolling is 40-54 mm. And in the rough rolling stage, the reciprocating large deformation of an austenite recrystallization region is adopted, so that austenite recrystallization is fully performed, and the structure state of the intermediate blank is controlled by controlling the finish temperature of rough rolling. The invention adopts the lower finish rolling inlet temperature of 980-1030 ℃ and aims to refine the austenite grain size of the intermediate billet, reduce the rolling amount of a partial recrystallization zone and avoid the occurrence of mixed crystal defects.
And (3) continuously finishing by adopting 6 frames, wherein the finishing temperature is 810-840 ℃. Different finishing rolling temperatures are selected according to different thicknesses, more austenite non-recrystallization region accumulated reduction refined austenite grains are obtained, and the subsequent nucleation number is increased, so that the grains are refined. If the finishing temperature is lower than 810 ℃, the rolling load is increased, and the control of the rolled plate shape is not facilitated; if the finishing temperature is higher than 840 ℃, the structure is coarse, and the strength, toughness and forming performance of the material are reduced.
The key point for obtaining the ideal biphase structure is that the cooling after rolling adopts a four-section cooling mode, namely the strip steel is discharged from the finish rolling and air-cooled to 750 ℃, the finishing temperature of the front section water cooling is 680 ℃, the starting temperature of the rear section water cooling is 550 ℃, the finishing temperature of the rear section water cooling is 350 ℃, and the target coiling temperature is 310-350 ℃. The strip steel is subjected to finish rolling and is firstly subjected to air cooling, the finishing temperature of the air cooling is 750 ℃, the main purpose is to improve the problems of strip shape and residual stress caused by high-temperature water cooling, and the material is still in an austenite state and does not undergo phase change at the stage; the temperature of 750-680 ℃ is a first section of water cooling temperature interval, a laminar cooling mode is adopted, and the main purposes are that a pearlite structure appears in a bar, the nucleation number of ferrite is increased, and ferrite grains are refined; 680-550 ℃ is a second section of air cooling temperature interval, partial ferrite phase change occurs in the strip steel in the air cooling process, and the proportion of ferrite is controlled by strictly controlling the starting temperature and the ending temperature of the air cooling; the temperature of 550-350 ℃ is a second section of water cooling temperature interval, and the purpose of water cooling in the temperature interval is to obtain bainite structures with sufficient proportion and improve the hardness and the wear resistance of the material; the target coiling temperature is 310-.
The steel for an ultra-high-strength dual-phase corrosion-resistant agitator tank and the production process thereof according to the present application will be described in detail with reference to examples, comparative examples, and experimental data.
Example 1
S1, obtaining a casting blank through smelting and continuous casting, wherein the casting blank comprises the following chemical components: carbon: 0.21 percent; silicon: 1.55 percent; manganese: 2.08 percent; aluminum: 0.035%; phosphorus: 0.009%; sulfur: 0.003%; boron: 0.0008%, antimony: 0.10%, tin: 0.035%, the balance of iron and inevitable impurities;
s2, reheating a casting blank produced by smelting continuous casting, wherein the heating process of the casting blank adopts a hot charging and hot conveying process, the charging temperature is more than or equal to 600 ℃, the reheating temperature of the casting blank is 1220 ℃, and the heat preservation time is less than 180 min.
And S3, after the casting blank is taken out of the heating furnace, rough rolling and 6-rack continuous finish rolling are carried out, wherein 6-pass reciprocating rolling is adopted for the rough rolling, the inlet temperature of the finish rolling is 1030 ℃, the thickness of the intermediate blank is 40mm, 6-rack continuous rolling is adopted for the finish rolling, and the finish rolling temperature is 840 ℃.
S4, cooling after rolling adopts a four-section cooling mode, the finish rolling air cooling of the strip steel is carried out until the temperature reaches 700 ℃, the finishing temperature of the front section water cooling is 660 ℃, the starting temperature of the rear section water cooling is 500 ℃, the finishing temperature of the rear section cooling is 300 ℃, and the target coiling temperature is 300 ℃.
S5, straightening and transversely cutting the steel coil to form a finished product, namely a decoiling plate, wherein the thickness of the finished product is 3.0 mm.
Example 2
S1, obtaining a casting blank through smelting and continuous casting, wherein the casting blank comprises the following chemical components: carbon: 0.22 percent; silicon: 1.75 percent; manganese: 1.83 percent; aluminum: 0.036%; phosphorus: 0.010%; sulfur: 0.003%; boron: 0.0009%, antimony: 0.11%, tin: 0.032%, and the balance of iron and inevitable impurities;
s2, reheating a casting blank produced by smelting continuous casting, wherein the heating process of the casting blank adopts a hot charging and hot conveying process, the charging temperature is more than or equal to 600 ℃, the reheating temperature of the casting blank is 1220 ℃, and the heat preservation time is less than 180 min.
And S3, after the casting blank is taken out of the heating furnace, rough rolling and 6-rack continuous finish rolling are carried out, wherein the rough rolling adopts 6-pass reciprocating rolling, the inlet temperature of the finish rolling is 1030 ℃, the thickness of the intermediate blank is 42mm, the finish rolling adopts 6-rack continuous rolling, and the finish rolling temperature is 840 ℃.
S4, cooling after rolling adopts a four-section cooling mode, the strip steel is subjected to finish rolling air cooling until the front section water cooling finishing temperature is 700 ℃, the rear section water cooling starting temperature is 600 ℃, the rear section cooling finishing temperature is 400 ℃, and the target coiling temperature is 340 ℃.
S5, straightening and transversely cutting the steel coil to form a finished product, namely a decoiling plate, wherein the thickness of the finished product is 4.0 mm.
Example 3
S1, obtaining a casting blank through smelting and continuous casting, wherein the casting blank comprises the following chemical components: carbon: 0.24 percent; silicon: 1.70 percent; manganese: 1.90 percent; aluminum: 0.046 percent; phosphorus: 0.008 percent; sulfur: 0.004%; boron: 0.0007%, antimony: 0.09%, tin: 0.027%, the balance being iron and unavoidable impurities;
s2, reheating a casting blank produced by smelting continuous casting, wherein the heating process of the casting blank adopts a hot charging and hot conveying process, the charging temperature is more than or equal to 600 ℃, the reheating temperature of the casting blank is 1220 ℃, and the heat preservation time is less than 180 min.
And S3, after the casting blank is taken out of the heating furnace, rough rolling and 6-rack continuous finish rolling are carried out, wherein the rough rolling adopts 6-pass reciprocating rolling, the inlet temperature of the finish rolling is 1030 ℃, the thickness of the intermediate blank is 44mm, the finish rolling adopts 6-rack continuous rolling, and the finish rolling temperature is 840 ℃.
S4, cooling after rolling adopts a four-section cooling mode, the steel strip is subjected to finish rolling and air cooling to 750 ℃, the finishing temperature of the front section water cooling is 680 ℃, the starting temperature of the rear section water cooling is 550 ℃, the finishing temperature of the rear section cooling is 350 ℃, and the target coiling temperature is 330 ℃.
S5, straightening and transversely cutting the steel coil to form a finished product, namely a flat plate, wherein the thickness of the finished product is 5.0 mm.
Example 4
S1, obtaining a casting blank through smelting and continuous casting, wherein the casting blank comprises the following chemical components: carbon: 0.20 percent; silicon: 1.72 percent; manganese: 1.96 percent; aluminum: 0.050%; phosphorus: 0.009%; sulfur: 0.003%; boron: 0.0006%, antimony: 0.08%, tin: 0.029%, and the balance of iron and inevitable impurities;
s2, reheating a casting blank produced by smelting continuous casting, wherein the heating process of the casting blank adopts a hot charging and hot conveying process, the charging temperature is more than or equal to 600 ℃, the reheating temperature of the casting blank is 1210 ℃, and the heat preservation time is less than 180 min.
And S3, after the casting blank is taken out of the heating furnace, rough rolling and 6-rack continuous finish rolling are carried out, wherein 6-pass reciprocating rolling is adopted for the rough rolling, the inlet temperature of the finish rolling is 1020 ℃, the thickness of the intermediate blank is 46mm, 6-rack continuous rolling is adopted for the finish rolling, and the finish rolling temperature is 830 ℃.
S4, cooling after rolling adopts a four-section cooling mode, the steel strip is subjected to finish rolling and air cooling to 750 ℃, the finishing temperature of the front section water cooling is 680 ℃, the starting temperature of the rear section water cooling is 550 ℃, the finishing temperature of the rear section cooling is 350 ℃, and the target coiling temperature is 330 ℃.
S5, straightening and transversely cutting the steel coil to form a finished product, namely a decoiling plate, wherein the thickness of the finished product is 6.0 mm.
Example 5
S1, obtaining a casting blank through smelting and continuous casting, wherein the casting blank comprises the following chemical components: carbon: 0.22 percent; silicon: 1.59 percent; manganese: 1.85 percent; aluminum: 0.043 percent; phosphorus: 0.008 percent; sulfur: 0.002%; boron: 0.0008%, antimony: 0.12%, tin: 0.020% of iron and inevitable impurities as the rest;
s2, reheating a casting blank produced by smelting continuous casting, wherein the heating process of the casting blank adopts a hot charging and hot conveying process, the charging temperature is more than or equal to 600 ℃, the reheating temperature of the casting blank is 1210 ℃, and the heat preservation time is less than 180 min.
And S3, after the casting blank is taken out of the heating furnace, rough rolling and 6-rack continuous finish rolling are carried out, wherein 6-pass reciprocating rolling is adopted for the rough rolling, the inlet temperature of the finish rolling is 1020 ℃, the thickness of the intermediate blank is 48mm, 6-rack continuous rolling is adopted for the finish rolling, and the finish rolling temperature is 830 ℃.
S4, cooling after rolling adopts a four-section cooling mode, the strip steel is subjected to finish rolling and air cooling to 750 ℃, the finishing temperature of the front section water cooling is 680 ℃, the starting temperature of the rear section water cooling is 550 ℃, the finishing temperature of the rear section cooling is 350 ℃, and the target coiling temperature is 320 ℃.
S5, straightening and transversely cutting the steel coil to form a finished product, namely a flat plate, wherein the thickness of the finished product is 7.0 mm.
Example 6
S1, obtaining a casting blank through smelting and continuous casting, wherein the casting blank comprises the following chemical components: carbon: 0.21 percent; silicon: 1.64 percent; manganese: 2.05 percent; aluminum: 0.030%; phosphorus: 0.007%; sulfur: 0.002%; boron: 0.0007%, antimony: 0.11%, tin: 0.030%, the balance being iron and inevitable impurities;
s2, reheating a casting blank produced by smelting continuous casting, wherein the heating process of the casting blank adopts a hot charging and hot conveying process, the charging temperature is more than or equal to 600 ℃, the reheating temperature of the casting blank is 1200 ℃, and the heat preservation time is less than 180 min.
And S3, after the casting blank is taken out of the heating furnace, rough rolling and 6-rack continuous finish rolling are carried out, wherein 6-pass reciprocating rolling is adopted for the rough rolling, the inlet temperature of the finish rolling is 1010 ℃, the thickness of the intermediate blank is 50mm, 6-rack continuous rolling is adopted for the finish rolling, and the finish rolling temperature is 820 ℃.
S4, cooling after rolling adopts a four-section cooling mode, the strip steel is subjected to finish rolling and air cooling to 750 ℃, the finishing temperature of the front section water cooling is 680 ℃, the starting temperature of the rear section water cooling is 550 ℃, the finishing temperature of the rear section cooling is 350 ℃, and the target coiling temperature is 320 ℃.
S5, straightening and transversely cutting the steel coil to form a finished product, namely a flat plate, wherein the thickness of the finished product is 8.0 mm.
Example 7
S1, obtaining a casting blank through smelting and continuous casting, wherein the casting blank comprises the following chemical components: carbon: 0.22 percent; silicon: 1.68 percent; manganese: 1.90 percent; aluminum: 0.039%; phosphorus: 0.009%; sulfur: 0.002%; boron: 0.0009%, antimony: 0.09%, tin: 0.028%, the balance being iron and inevitable impurities;
s2, reheating a casting blank produced by smelting continuous casting, wherein the heating process of the casting blank adopts a hot charging and hot conveying process, the charging temperature is more than or equal to 600 ℃, the reheating temperature of the casting blank is 1190 ℃, and the heat preservation time is less than 180 min.
And S3, after the casting blank is taken out of the heating furnace, rough rolling and 6-rack continuous finish rolling are carried out, wherein 6-pass reciprocating rolling is adopted for the rough rolling, the inlet temperature of the finish rolling is 1000 ℃, the thickness of the intermediate blank is 52mm, 6-rack continuous rolling is adopted for the finish rolling, and the finish rolling temperature is 820 ℃.
S4, cooling after rolling adopts a four-section cooling mode, the steel strip is subjected to finish rolling and air cooling to 750 ℃, the finishing temperature of the front section water cooling is 680 ℃, the starting temperature of the rear section water cooling is 550 ℃, the finishing temperature of the rear section cooling is 350 ℃, and the target coiling temperature is 310 ℃.
S5, straightening and transversely cutting the steel coil to form a finished product, namely a decoiling plate, wherein the thickness of the finished product is 9.0 mm.
Example 8
S1, obtaining a casting blank through smelting and continuous casting, wherein the casting blank comprises the following chemical components: carbon: 0.23 percent; silicon: 1.70 percent; manganese: 2.10 percent; aluminum: 0.037%; phosphorus: 0.010%; sulfur: 0.003%; boron: 0.0008%, antimony: 0.12%, tin: 0.026%, and the balance of iron and inevitable impurities;
s2, reheating a casting blank produced by smelting continuous casting, wherein the heating process of the casting blank adopts a hot charging and hot conveying process, the charging temperature is more than or equal to 600 ℃, the reheating temperature of the casting blank is 1180 ℃, and the heat preservation time is less than 180 min.
And S3, after the casting blank is taken out of the heating furnace, rough rolling and 6-rack continuous finish rolling are carried out, wherein 6-pass reciprocating rolling is adopted for rough rolling, the inlet temperature of finish rolling is 980 ℃, the thickness of an intermediate blank is 54mm, 6-rack continuous rolling is adopted for finish rolling, and the finish rolling temperature is 810 ℃.
S4, cooling after rolling adopts a four-section cooling mode, the steel strip is subjected to finish rolling and air cooling to 750 ℃, the finishing temperature of the front section water cooling is 680 ℃, the starting temperature of the rear section water cooling is 550 ℃, the finishing temperature of the rear section cooling is 350 ℃, and the target coiling temperature is 310 ℃.
S5, straightening and transversely cutting the steel coil to form a finished product open flat plate, wherein the thickness of the finished product is 10.0 mm.
Comparative example 1
S1, obtaining a casting blank through smelting and continuous casting, wherein the casting blank comprises the following chemical components: carbon: 0.21 percent; silicon: 1.64 percent; manganese: 2.05 percent; aluminum: 0.030%; phosphorus: 0.007%; sulfur: 0.002%; boron: 0.0007%, antimony: 0.11%, tin: 0.030%, the balance being iron and inevitable impurities;
s2, reheating a casting blank produced by smelting continuous casting, wherein the heating process of the casting blank adopts a hot charging and hot conveying process, the charging temperature is more than or equal to 600 ℃, the reheating temperature of the casting blank is 1200 ℃, and the heat preservation time is less than 180 min.
And S3, after the casting blank is taken out of the heating furnace, rough rolling and 6-rack continuous finish rolling are carried out, wherein 6-pass reciprocating rolling is adopted for the rough rolling, the inlet temperature of the finish rolling is 1010 ℃, the thickness of the intermediate blank is 50mm, 6-rack continuous rolling is adopted for the finish rolling, and the finish rolling temperature is 820 ℃.
S4, cooling after rolling by adopting a conventional cooling mode, namely a front section laminar cooling mode, wherein the final cooling temperature is 600 ℃ and the coiling temperature is 590 ℃.
S5, straightening and transversely cutting the steel coil to form a finished product, namely a flat plate, wherein the thickness of the finished product is 8.0 mm.
Comparative example 2
S1, obtaining a casting blank through smelting and continuous casting, wherein the casting blank comprises the following chemical components: carbon: 0.19 percent; silicon: 1.49 percent; manganese: 1.79 percent; aluminum: 0.029%; phosphorus: 0.016 percent; sulfur: 0.005 percent; boron: 0.0004%, antimony: 0.07%, tin: 0.019%, and the balance of iron and inevitable impurities;
s2, reheating a casting blank produced by smelting continuous casting, wherein the heating process of the casting blank adopts a hot charging and hot conveying process, the charging temperature is more than or equal to 600 ℃, the reheating temperature of the casting blank is 1200 ℃, and the heat preservation time is less than 180 min.
And S3, after the casting blank is taken out of the heating furnace, rough rolling and 6-rack continuous finish rolling are carried out, wherein 6-pass reciprocating rolling is adopted for the rough rolling, the inlet temperature of the finish rolling is 1010 ℃, the thickness of the intermediate blank is 50mm, 6-rack continuous rolling is adopted for the finish rolling, and the finish rolling temperature is 820 ℃.
S4, cooling after rolling adopts a four-section cooling mode, the strip steel is subjected to finish rolling and air cooling to 750 ℃, the finishing temperature of the front section water cooling is 680 ℃, the starting temperature of the rear section water cooling is 550 ℃, the finishing temperature of the rear section cooling is 350 ℃, and the target coiling temperature is 320 ℃.
S5, straightening and transversely cutting the steel coil to form a finished product, namely a flat plate, wherein the thickness of the finished product is 8.0 mm.
Comparative example 3
S1, obtaining a casting blank through smelting and continuous casting, wherein the casting blank comprises the following chemical components: carbon: 0.25 percent; silicon: 1.76 percent; manganese: 2.11 percent; aluminum: 0.066%; phosphorus: 0.016 percent; sulfur: 0.005 percent; boron: 0.0010%, antimony: 0.13%, tin: 0.036%, the balance being iron and inevitable impurities;
s2, reheating a casting blank produced by smelting continuous casting, wherein the heating process of the casting blank adopts a hot charging and hot conveying process, the charging temperature is more than or equal to 600 ℃, the reheating temperature of the casting blank is 1200 ℃, and the heat preservation time is less than 180 min.
And S3, after the casting blank is taken out of the heating furnace, rough rolling and 6-rack continuous finish rolling are carried out, wherein 6-pass reciprocating rolling is adopted for the rough rolling, the inlet temperature of the finish rolling is 1010 ℃, the thickness of the intermediate blank is 50mm, 6-rack continuous rolling is adopted for the finish rolling, and the finish rolling temperature is 820 ℃.
S4, cooling after rolling adopts a four-section cooling mode, the strip steel is subjected to finish rolling and air cooling to 750 ℃, the finishing temperature of the front section water cooling is 680 ℃, the starting temperature of the rear section water cooling is 550 ℃, the finishing temperature of the rear section cooling is 350 ℃, and the target coiling temperature is 320 ℃.
S5, straightening and transversely cutting the steel coil to form a finished product, namely a flat plate, wherein the thickness of the finished product is 8.0 mm.
Experimental example:
the steels obtained in examples 1 to 8 and comparative example 1 and a commercially available steel for a 520MPa stirred tank were mixed: and carrying out performance detection on sample steel 1 and sample steel 2.
The chemical composition detection results are shown in the following table:
| serial number | C | Si | Mn | P | S | Alt | Sn | Sb | B |
| Example 1 | 0.21 | 1.55 | 2.08 | 0.009 | 0.003 | 0.035 | 0.035 | 0.10 | 0.0008 |
| Example 2 | 0.22 | 1.75 | 1.83 | 0.010 | 0.003 | 0.036 | 0.032 | 0.11 | 0.0009 |
| Example 3 | 0.24 | 1.70 | 1.90 | 0.008 | 0.004 | 0.046 | 0.027 | 0.09 | 0.0007 |
| Example 4 | 0.20 | 1.72 | 1.96 | 0.009 | 0.003 | 0.050 | 0.029 | 0.08 | 0.0006 |
| Example 5 | 0.22 | 1.59 | 1.85 | 0.008 | 0.002 | 0.043 | 0.020 | 0.12 | 0.0008 |
| Example 6 | 0.21 | 1.64 | 2.05 | 0.007 | 0.002 | 0.030 | 0.030 | 0.11 | 0.0007 |
| Example 7 | 0.22 | 1.68 | 1.90 | 0.009 | 0.002 | 0.039 | 0.028 | 0.09 | 0.0009 |
| Example 8 | 0.23 | 1.70 | 2.10 | 0.010 | 0.003 | 0.037 | 0.026 | 0.12 | 0.0008 |
| Comparative example 1 | 0.21 | 1.64 | 2.05 | 0.007 | 0.002 | 0.030 | 0.030 | 0.11 | 0.0007 |
| Comparative example 2 | 0.19 | 1.49 | 1.79 | 0.016 | 0.005 | 0.029 | 0.019 | 0.07 | 0.0004 |
| Comparative example 3 | 0.25 | 1.76 | 2.11 | 0.016 | 0.005 | 0.066 | 0.036 | 0.13 | 0.0010 |
| Sample Steel 1 | 0.17 | 0.20 | 1.10 | 0.018 | 0.007 | 0.028 | - | ||
| Sample Steel 2 | 0.14 | 0.10 | 1.50 | 0.014 | 0.004 | 0.032 | 0.31 | - | - |
The steel structure type and mechanical property test results are shown in the following table:
in the table, the area ratio of each metallographic structure was measured by the following method: a transverse metallographic specimen (an observation surface is vertical to the rolling direction) is taken by using a wire cutting machine, is ground by using 150# to 2000# abrasive paper, and is then ground and polished by using a polishing machine. And corroding the polished observation surface of the metallographic specimen by using a 3% nitric acid ethanol solution, observing 5 visual fields by using a multiplying power of 500 times, and distinguishing the metallographic structure type by using picture analysis software. The average value of 5 visual fields is taken as the area ratio of the metallographic structure of the metal.
The method for testing the grain size of each metallographic structure comprises the following steps: each of the above-mentioned fields of view was subjected to measurement of 20 polygonal ferrite grain sizes, each polygonal ferrite measured two data of length and width perpendicular to each other, and all the data were averaged to obtain the polygonal ferrite grain size.
The corrosion test results for the steels are given in the following table:
| serial number | Test time (h) | Corrosion rate g/(m 2. h) | Relative corrosion Rate% |
| Standard sample Q355B | 72 | 3.732 | 100 |
| Example 1 | 72 | 1.675 | 44.88 |
| Example 2 | 72 | 1.723 | 46.17 |
| Example 3 | 72 | 1.654 | 44.32 |
| Example 4 | 72 | 1.879 | 50.35 |
| Example 5 | 72 | 1.796 | 48.12 |
| Example 6 | 72 | 1.824 | 48.87 |
| Example 7 | 72 | 1.695 | 45.42 |
| Example 8 | 72 | 1.703 | 45.63 |
| Comparative example 1 | 72 | 1.874 | 50.21 |
| Comparative example 2 | 72 | 1.967 | 52.71 |
| Comparative example 3 | 72 | 1.906 | 51.07 |
| Sample Steel 1 | 72 | 3.696 | 99.04 |
| Sample Steel 2 | 72 | 3.401 | 91.13 |
The corrosion test method comprises the following steps: 0.01mol/L sodium bisulfite solution, test time 72 hours, test standard TB/T2375-1993.
From the data in the table, one can see: the results of the example data and the comparative and sample steel data show that the corrosion resistance of the steel produced by the method provided by this example is improved by about 1 times compared to the comparative and sample steels.
The wear resistance test results are shown in the following table:
| serial number | 60min weight loss/g | 90min weight loss/g |
| Q355B | 0.896 | 1.117 |
| Example 1 | 0.396 | 0.541 |
| Example 2 | 0.401 | 0.515 |
| Example 3 | 0.398 | 0.507 |
| Example 4 | 0.412 | 0.534 |
| Example 5 | 0.415 | 0.528 |
| Example 6 | 0.399 | 0.517 |
| Example 7 | 0.387 | 0.542 |
| Example 8 | 0.405 | 0.533 |
| Comparative example 1 | 0.762 | 0.896 |
| Comparative example 2 | 0.314 | 0.425 |
| Comparative example 3 | 0.686 | 0.792 |
| Sample Steel 1 | 0.923 | 1.118 |
| Sample Steel 2 | 0.872 | 1.086 |
The method for testing the wear resistance comprises the following steps: use MLD-10 dynamic load grit abrasion tester, impact load 10Kg, impact hammer stroke is 40mm, and the abrasive material is quartz sand, and the abrasive particle size is 10 meshes, sand flow: 30kg/h, impact frequency: 100 times/min, impact time: for 90 minutes. And (3) washing the sample with alcohol before abrasion, drying and weighing, putting the sample into an acetone solution after abrasion, washing for 25min with ultrasonic waves, drying and weighing, and measuring the sample weight of 60min and 90min of impact time respectively to obtain the wear-resisting property of the weight loss characterization material.
From the data in the table, one can see: the data results of the example, the comparative example and the sample steel show that the wear resistance of the steel prepared by the method provided by the embodiment is improved by more than 1 time compared with the comparative example and the sample steel.
In conclusion, the steel for the ultra-high-strength stirring tank provided by the invention has the advantages that through reasonable design of the proportion of chemical components in the steel, high-cost-performance corrosion-resistant elements and element combinations are accurately added, and the controlled rolling and controlled cooling technology of an accurate process window is combined, the finally obtained steel plate finished product has ultrahigh strength, good cold forming performance, good low-temperature toughness and welding performance, and excellent corrosion resistance; meanwhile, the product has a low yield ratio, and is easy to form in the process of manufacturing the stirring tank. Compared with the common steel for Q355B and 520MPa stirring tanks, the tensile strength is improved by nearly 1 time, and the wear resistance is improved by more than 1 time. Meanwhile, due to the addition of Sn and Sb elements and the combined action of high Si, the corrosion resistance of the steel is improved by about 1 time. Meanwhile, due to the existence of polygonal ferrite, the yield ratio of the material is greatly reduced, and the tank manufacturing process of the ultrahigh-strength stirring tank is easy to smoothly carry out.
One or more technical solutions in the embodiments of the present invention at least have the following technical effects or advantages:
(1) the embodiment of the invention provides the steel for the ultrahigh-strength stirring tank, which is easy to form, high in strength and wear resistance, good in corrosion resistance and weldability, and solves the problems of cold forming cracking of a high-strength steel plate, softening of a heat affected zone after welding, poor wear resistance and corrosion resistance, heavy tank body and the like; the steel plate has good stability, and the defects of bulging or collapse in the pressurizing process are avoided;
(2) the material meets the requirements of safety and use, achieves the aims of reducing weight, reducing consumption and reducing emission, becomes a new generation of environment-friendly material, and can be used for improving the wear resistance and corrosion resistance of a stirring tank and realizing light weight.
(3) In the aspect of production process, a precise controlled rolling and controlled multi-section cooling process is adopted, the structure state is controlled to be a ferrite and bainite dual-phase structure, the content of an M-A component is controlled, the plate shape quality and the yield are improved, and the pipe manufacturing efficiency is improved;
(4) through the composition ratio and the synergistic cooperation with the preparation process, particularly through the composition design and the core four-section cooling process, a high-strength and high-toughness easily-formed structure mainly comprising ferrite and bainite is obtained, and finally the steel for the ultrahigh-strength stirring tank with good weldability is obtained, and can be used for lightening the stirring tank and prolonging the service life of the stirring tank.
Finally, it should also be noted that 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.
While preferred embodiments of the present invention have been described, additional variations and modifications in those embodiments may occur to those skilled in the art once they learn of the basic inventive concepts. Therefore, it is intended that the appended claims be interpreted as including preferred embodiments and all such alterations and modifications as fall within the scope of the invention.
It will be apparent to those skilled in the art that various changes and modifications may be made in the present invention without departing from the spirit and scope of the invention. Thus, if such modifications and variations of the present invention fall within the scope of the claims of the present invention and their equivalents, the present invention is also intended to include such modifications and variations.
Claims (10)
1. The steel for the ultrahigh-strength dual-phase corrosion-resistant stirring tank is characterized by comprising the following chemical components in percentage by mass:
c: 0.20% -0.24%, S: 1.50% -1.75%, Mn: 1.80% -2.10%, Alt: 0.030% -0.065%, P: less than or equal to 0.015 percent, S: less than or equal to 0.004%, B: 0.0005 to 0.0009%, Sb: 0.08-0.12%, Sn: 0.020-0.035%, and the balance of Fe and inevitable impurities.
2. The steel for an ultra-high strength dual phase corrosion-resistant agitator tank of claim 1, wherein the chemical composition of the steel is, in mass fraction:
c: 0.21% -0.23%, S: 1.55-1.70%, Mn: 1.90% -2.00%, Alt: 0.040% -0.055%, P: less than or equal to 0.015 percent, S: less than or equal to 0.004%, B: 0.0006% -0.0008%, Sb: 0.09% -0.11%, Sn: 0.025 to 0.030 percent, and the balance of Fe and inevitable impurities.
3. The steel for an ultra-high strength dual phase corrosion-resistant agitator tank of claim 1, wherein the metallographic structure of the steel is, in terms of volume fraction: 55% or more of bainite, 35% or more of polygonal ferrite, and 5% or less of M-A component.
4. The steel for an ultra high strength dual phase corrosion resistant agitator tank of claim 3, wherein the grain size of the polygonal ferrite is 3.8 to 5.5 μm.
5. A process for the production of steel for ultra high strength dual phase corrosion resistant agitator tank as defined in any one of claims 1 to 4, wherein the process comprises:
obtaining a casting blank of the steel for the ultrahigh-strength dual-phase corrosion-resistant stirring tank;
and (3) reheating the casting blank, rough rolling, finish rolling and continuous rolling, cooling, coiling, slow cooling and leveling to obtain the steel for the ultrahigh-strength dual-phase corrosion-resistant stirring tank.
6. The process for producing the steel for the ultra-high strength dual-phase corrosion-resistant agitator tank according to claim 5, wherein a hot charging and delivering process is adopted in reheating the casting blank, the charging temperature is more than or equal to 600 ℃, the reheating temperature of the casting blank is controlled at 1180-1220 ℃, and the heating time is less than 180 min.
7. The process for producing the steel for the ultra-high-strength dual-phase corrosion-resistant stirring tank as claimed in claim 5, wherein the rough rolling is performed in 6 passes, and the outlet temperature of the rough rolling is 980-1030 ℃.
8. The process for producing the steel for the ultra-high-strength dual-phase corrosion-resistant agitator tank according to claim 5, wherein the finish rolling is performed by continuous rolling using 6 stands, the thickness of the finish-rolled intermediate slab is controlled to be 40mm to 54mm, the inlet temperature of the finish rolling is controlled to be 980 ℃ to 1030 ℃, and the outlet temperature of the finish rolling is controlled to be 810 ℃ to 840 ℃.
9. The process for producing the steel for the ultra-high-strength dual-phase corrosion-resistant agitator tank according to claim 5, wherein four-stage cooling is adopted in the cooling, and the first-stage cooling: air cooling to 750 ℃, and second-stage cooling: water cooling to 680 ℃, and third stage cooling: air cooling to 550 ℃, and cooling in the fourth stage: water cooling to 350 ℃.
10. The process for producing the steel for the ultra-high-strength dual-phase corrosion-resistant agitator tank according to claim 5, wherein the coiling temperature is 310 ℃ to 350 ℃.
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