CN113699437A - Hot continuous rolling dual-phase wear-resistant steel for carriage plate and production method thereof - Google Patents
Hot continuous rolling dual-phase wear-resistant steel for carriage plate and production method thereof Download PDFInfo
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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
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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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
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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
- C21D2211/005—Ferrite
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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
- C21D2211/008—Martensite
Abstract
The invention discloses hot continuous rolling dual-phase wear-resistant steel for a carriage plate and a production method, and belongs to the technical field of metallurgy. The hot continuous rolling wear-resistant steel comprises the following chemical components in percentage by mass: c: 0.10 to 0.20%, Si: 0.08-0.40%, Mn: 0.5-2.0%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Als: 0.01-0.06%, Nb is less than or equal to 0.02%, Ti is less than or equal to 0.02%, B is less than or equal to 0.005%, and the balance of Fe and impurities; the process comprises the steps of adopting blast furnace molten iron, desulfurizing the molten iron, smelting in a converter, refining LF and RH, continuously casting, heating, rolling, cooling, coiling, flattening and transversely cutting a process route. The wear-resistant steel prepared by the method has stable and excellent performance, and more importantly, the production efficiency is high.
Description
Technical Field
The invention relates to hot continuous rolling wear-resistant steel, belongs to the technical field of metallurgy, and particularly relates to hot continuous rolling dual-phase wear-resistant steel for a carriage plate and a production method thereof.
Background
The main domestic iron and steel enterprises such as Bao steel, saddle steel, ripple steel, south steel, dance steel and the like mainly adopt an off-line quenching and tempering process to produce wear-resistant steel, the organization type is mainly tempered martensite, the quality is stable, the performance is excellent, and the downstream industry is approved.
The Chinese invention patent (CN105543676A) discloses a martensite-ferrite dual-phase wear-resistant steel plate and a preparation method thereof, wherein the volume fraction of a martensite structure is more than 90%, the hardness is 480-560 HB, and the martensite-ferrite dual-phase wear-resistant steel plate is prepared by adopting specific dosage of C, Si, Mn, P, S, Nb, V, Ti, Mo, Ni, Cr, Al, B, N, Fe and other elements. The prepared martensite-ferrite dual-phase wear-resistant steel plate has high hardness and good low-temperature toughness and wear resistance, and is beneficial to manufacturing of mechanical parts under severe environment, especially under extremely low temperature condition. The preparation method of the martensite-ferrite dual-phase wear-resistant steel plate has simple process, can obtain a martensite-ferrite dual-phase structure, comprehensively improves the hardness, low-temperature toughness and wear resistance of the obtained martensite-ferrite dual-phase wear-resistant steel plate, and is suitable for large-scale production.
The Chinese invention patent (CN106917051A) discloses a corrosion-resistant dual-phase wear-resistant steel plate and a production method thereof, wherein the steel plate comprises the following chemical components in percentage by weight: c is less than or equal to 0.13 percent, Si is less than or equal to 0.60 percent, Mn: 1.60 percent of the total Fe-based alloy, less than or equal to 0.015 percent of P, less than or equal to 0.003 percent of S, less than or equal to 0.060 percent of Al, less than or equal to 1.20 percent of Cr, less than or equal to 0.30 percent of Mo, and the balance of Fe and inevitable impurities. The production method comprises the working procedures of heating, rolling and heat treatment. The steel plate has good structure, mechanical property, corrosion resistance, wear resistance and welding property by adopting C, Mn, Cr and Mo solid solution strengthening in the design of chemical components, and can be widely applied to the corrosion-resistant and wear-resistant environment.
The Chinese invention patent (CN108396248A) discloses a corrosion-resistant double-phase wear-resistant steel plate with 690-grade yield strength and a production method thereof, wherein the steel plate comprises the following chemical components in percentage by weight: less than or equal to 0.15 percent of C, less than or equal to 0.60 percent of Si, less than or equal to 1.20 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.003 percent of S, less than or equal to 0.60 percent of Al, less than or equal to 1.20 percent of Cr, less than or equal to 0.40 percent of Mo, less than or equal to 0.0030 percent of B, less than or equal to 0.020 percent of Ti, and the balance of Fe and inevitable impurities. The steel plate is designed by adopting C, Mn, Cr and Mo for solid solution strengthening, and trace B elements are added to improve the hardenability of the steel, so that the steel plate has good organization, mechanical property, corrosion resistance, wear resistance and welding property, meanwhile, the strength level is lower, the yield ratio is lower, the steel plate is suitable for reel pipes, the wear resistance of the corrosion-resistant dual-phase wear-resistant steel is consistent with that of NM360E, but the strength and hardness are far lower than those of NM360E, the steel plate can better meet the requirements of the corrosion-resistant wear-resistant steel, has excellent impact toughness at-30 ℃, can be widely used in corrosion-resistant wear-resistant environments, and has wide application prospects.
However, the existing wear-resistant steel has the technical problems of high alloy content, low strength grade and the like.
Disclosure of Invention
In order to solve the technical problems, the invention provides hot continuous rolling dual-phase wear-resistant steel for a carriage plate and a production method thereof.
In order to achieve the aim, the invention discloses hot continuous rolling dual-phase wear-resistant steel for a carriage plate, which comprises the following chemical components in percentage by mass:
c: 0.10 to 0.20%, Si: 0.08-0.90%, Mn: 0.5-2.0%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Als: 0.01-0.06%, Nb is less than or equal to 0.02%, Ti is less than or equal to 0.02%, B is less than or equal to 0.005%, and the balance is Fe and impurities.
Further, the paint comprises the following chemical components in percentage by mass:
c: 0.10 to 0.16%, Si: 0.08 to 0.87%, Mn: 0.5-1.5%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Als: 0.01-0.06%, Nb is more than or equal to 0.005% and less than or equal to 0.012%, Ti is more than or equal to 0.001% and less than 0.012%, B is less than 0.004%, and the balance is Fe and impurities.
Further, the carbon element satisfies, C: 0.14-0.16%; the manganese element satisfies the following formula (Mn: 1.2 to 1.5 percent.
In order to better realize the technical purpose of the invention, the invention also discloses a production method of the hot continuous rolling double-phase wear-resistant steel for the carriage plate, which comprises the following process flows of:
adopting blast furnace molten iron, molten iron desulphurization, converter smelting, LF + RH refining, continuous casting, heating, rolling, cooling, coiling, splitting and transverse cutting processes;
the heating process comprises the following steps:
the second-stage heating temperature and the soaking end-stage temperature are 1200-1300 ℃, the total time of the second-stage heating and soaking is not less than 60min, and the total in-furnace time is not less than 140 min;
the rolling comprises rough rolling and finish rolling, the outlet temperature of the rough rolling is 1000-1100 ℃, the thickness of an intermediate billet is 30-50 mm, the start rolling temperature of the finish rolling is 950-1050 ℃, the rolling speed is 3-8 m/s, and the finish rolling temperature is 800-900 ℃;
the cooling and coiling process comprises the following steps:
and immediately cooling the FT7, cooling to 580-650 ℃ at a cooling speed of 10-100 ℃/s, air-cooling for 5-15 s, continuously controlling the cooling speed to be 5-100 ℃/s, cooling to 150-300 ℃, coiling, and realizing on-line quenching.
Further, the heating process comprises:
the second-stage heating temperature and the soaking end-stage temperature are 1210-1285 ℃, the total time of the second-stage heating and soaking is 65-95 min, and the total in-furnace time is 150-180 min.
Further, the outlet temperature of the rough rolling is 1010-1090 ℃.
Furthermore, the start rolling temperature of the finish rolling is 960-1040 ℃, the rolling speed is 3-8 m/s, and the finish rolling temperature is 800-870 ℃.
Furthermore, the cooling speed of the first section is 25-81 ℃/s.
Further, the second section cooling speed is 5-40 ℃/s, and the temperature is cooled to 160-300 ℃.
Further, the air cooling time is 6-14 s.
The beneficial effects of the invention are mainly embodied in the following aspects:
1. the preparation process designed by the application is relatively simple and high in production efficiency.
2. The hot continuous rolling wear-resistant steel designed by the application has the advantages of low yield ratio, relatively good wear resistance, stable and excellent plate shape performance and relatively good cold bending performance, and is suitable for various environments.
Drawings
FIG. 1 is a schematic microstructure diagram of a hot continuous rolling dual-phase wear-resistant steel for a carriage plate prepared by the invention.
Detailed Description
The invention discloses hot continuous rolling dual-phase wear-resistant steel for a carriage plate, which comprises the following chemical components in percentage by mass:
c: 0.10 to 0.20%, Si: 0.08-0.90%, Mn: 0.5-2.0%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Als: 0.01-0.06%, Nb is less than or equal to 0.02%, Ti is less than or equal to 0.02%, B is less than or equal to 0.005%, and the balance is Fe and impurities.
Further, the paint comprises the following chemical components in percentage by mass:
c: 0.10 to 0.16%, Si: 0.08-0.90%, Mn: 0.5-1.5%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Als: 0.01-0.06%, Nb is more than or equal to 0.005% and less than or equal to 0.012%, Ti is more than or equal to 0.001% and less than 0.012%, B is less than 0.004%, and the balance is Fe and impurities.
Further, the carbon element satisfies, C: 0.14-0.16%; the manganese element satisfies the following formula (Mn: 1.2 to 1.5 percent.
The principle of the invention for designing and adopting the alloy elements with the contents is as follows:
carbon (C): is the cheapest element for improving the strength of the material, and the hardness and the strength are improved along with the increase of the carbon content, but the ductility and the toughness and the welding performance are reduced. Comprehensively considering, the weight percentage of C is 0.10-0.20%; the content of 0.14-0.16% is further optimized.
Silicon (Si): the effect on hardenability is weaker and far less than that of Cr and Mn, Si can reduce the diffusion rate of carbon in ferrite, but if Si is too high, quenching cracks are easy to generate, and the surface quality is also deteriorated. Comprehensively considering, the weight percentage content of Si is preferably 0.08-0.90%;
manganese (Mn): the Ar1 temperature, the austenite decomposition speed and the martensite transformation temperature of steel are obviously reduced, the residual austenite content in a final structure is increased, the comprehensive performance is improved, the critical quenching speed of the steel can be obviously reduced by manganese, the hardness and the strength can be improved by infinite solid solution with Fe, the tempering brittleness of the steel can be increased if the content of Mn is too high, and serious center segregation is caused, the weight percentage content of Mn is preferably 0.5-2.0% in comprehensive consideration, and the optimal content is further preferably 1.2-1.5%.
Acid-soluble aluminum (Als): can deoxidize in steel and also can play a role in refining grains, and the comprehensive consideration is that Als is added into the steel in the proportion of Als: 0.01 to 0.06 percent.
Niobium (Nb): the Nb-containing ferrite has strong affinity with C, N in steel, forms a stable Nb (C, N) compound, is induced to be separated out in the controlled rolling process, is dispersed and distributed along austenite grain boundaries and serves as nucleation particles of phase change, can effectively prevent recrystallization, improves the ferrite nucleation rate, has obvious effect on grain refinement, and has the Nb weight percentage content of less than or equal to 0.02 percent in comprehensive consideration; the content of 0.005-0.012% is further optimized to be optimal.
Titanium (Ti): can combine with N to generate stable TiN in the solidification process of steel, and can strongly hinder the migration of austenite grain boundaries, thereby refining austenite grains. Ti and C are combined to generate TiC which can play a role in precipitation strengthening, and the toughness can be improved by adding a trace amount of Ti, wherein the weight percentage of Ti is less than or equal to 0.02 percent in comprehensive consideration; the content of 0.001-0.012% is further optimized to be optimal.
Boron (B): the hardenability of the steel can be greatly improved by adding a small amount of B, but when the B is excessive, the B is easy to enrich in a crystal boundary, the crystal boundary binding energy can be reduced, the steel plate is more prone to fracture along the crystal when subjected to impact load, and the low-temperature impact energy of the steel plate is reduced, so that the adding amount of B is less than or equal to 0.005%, and the optimal amount of B is further preferably less than 0.004%.
Phosphorus (P), sulfur (S): the steel is harmful impurity elements in the steel, P in the steel is easy to form segregation in the steel, the toughness and the welding performance of the steel are reduced, S is easy to form plastic sulfide, the steel plate is layered, and the performance of the steel plate is deteriorated, so the lower the P, S content is, the better the steel is, the comprehensive consideration is that the P, S content of the steel is equal to or less than 0.015 percent of P, and the S is equal to or less than 0.005 percent of S.
In addition, the invention also discloses a preparation method of the HB400 grade hot continuous rolling wear-resistant steel containing ferrite, which comprises the following process flows:
adopting blast furnace molten iron, molten iron desulphurization, converter smelting, LF + RH refining, continuous casting, heating, rolling, cooling, coiling, splitting and transverse cutting processes;
the heating process comprises the following steps:
the second section heating temperature and the soaking end section temperature are 1200-1300 ℃, the total heating time of the second section and the soaking section is not less than 60min, and the total in-furnace time is not less than 140 min; the temperature of the second-stage heating and the temperature of the last soaking stage are preferably 1210-1285 ℃, the total time of the second-stage heating and soaking stages is 65-95 min, and the total in-furnace time is 150-180 min; the purpose of the operation is to ensure that the alloy elements such as Mn, Nb, Ti, V and the like are completely dissolved in solid and fully austenitized, and the temperature of the plate blank is uniform on the premise of fully austenitizing, thereby laying the foundation for the subsequent rolling and cooling process.
The rolling comprises rough rolling and finish rolling, the outlet temperature of the rough rolling is 1000-1100 ℃, the thickness of an intermediate billet is 30-50 mm, the start rolling temperature of the finish rolling is 950-1050 ℃, the rolling speed is 3-8 m/s, and the finish rolling temperature is 800-900 ℃; according to the invention, the preferable rough rolling outlet temperature is 1010-1090 ℃, the finish rolling start temperature is 960-1040 ℃, and the finish rolling finishing temperature is 800-870 ℃. The method has the advantages that the higher finish rolling inlet temperature is selected, so that the rolling load of the F1-F4 rack is reduced, the rolling load distribution in the finish rolling stage is facilitated, the total reduction rate in the finish rolling stage is not too large, the limitation of the method is 20-50%, under the reduction rate, the finish rolling load can be reduced, the uniformity of plastic deformation in the finish rolling stage is facilitated, the internal stress of a rolled steel plate is more uniform, and the better rolled plate shape is obtained.
The cooling and coiling process comprises the following steps:
and immediately cooling the steel after FT7 is taken out, cooling the steel to 580-650 ℃ at a cooling speed of 10-100 ℃/s, air-cooling the steel for 5-15 s to obtain a certain amount of ferrite, wherein the cooling speed is limited to 20-40%, continuously controlling the cooling speed to 5-100 ℃/s, cooling the steel to 150-300 ℃ for coiling, and realizing on-line quenching. The first section cooling speed is preferably 25-81 ℃/s, the second section cooling speed is preferably 5-40 ℃/s, and the cooling is carried out to 160-300 ℃.
The invention selects and controls the cooling speed, aims to adopt proper cooling speed according to different thicknesses, prevents the excessively high cooling speed, has obvious effects of thermal expansion and cold contraction and deteriorates the quality of the plate shape and the distribution of internal stress, and simultaneously avoids the application problems that the strength, the hardness and the wear resistance cannot be ensured because the martensite is difficult to obtain due to too high coiling temperature, the temperature of the self-tempering process of the steel coil cannot be ensured due to too low coiling temperature, cracking and the like can occur in the using process of users by controlling the coiling temperature.
The thickness of the steel plate prepared by the process is 2-15 mm.
In order to better explain the invention, the following further illustrate the main content of the invention in connection with specific examples, but the content of the invention is not limited to the following examples.
The invention designs 10 examples and 5 comparative examples, wherein the wear-resistant steel of each example and each comparative example comprises the following chemical components in percentage by mass as shown in Table 1:
TABLE 1 chemical component contents (wt%) of examples and comparative examples
| C/％ | Si/％ | Mn/％ | P/％ | S/％ | Als/％ | Nb/％ | Ti/％ | B/％ | |
| Example 1 | 0.12 | 0.18 | 1 | 0.012 | 0.001 | 0.05 | 0.011 | 0.012 | 0.003 |
| Example 2 | 0.16 | 0.45 | 1.5 | 0.007 | 0.002 | 0.01 | 0.005 | 0.012 | 0.003 |
| Example 3 | 0.14 | 0.66 | 1.2 | 0.011 | 0.004 | 0.03 | 0.015 | 0.012 | 0.004 |
| Example 4 | 0.16 | 0.46 | 1.3 | 0.006 | 0.005 | 0.02 | 0.01 | 0.011 | 0.004 |
| Example 5 | 0.11 | 0.78 | 1.7 | 0.009 | 0.002 | 0.05 | 0.014 | 0.009 | 0.005 |
| Example 6 | 0.14 | 0.79 | 1.4 | 0.008 | 0.005 | 0.02 | 0 | 0.014 | 0.002 |
| Example 7 | 0.12 | 0.87 | 0.9 | 0.007 | 0.003 | 0.01 | 0.011 | 0.013 | 0.003 |
| Example 8 | 0.15 | 0.51 | 0.8 | 0.009 | 0.004 | 0.06 | 0.007 | 0.008 | 0.003 |
| Example 9 | 0.18 | 0.28 | 1.5 | 0.008 | 0.005 | 0.03 | 0.012 | 0 | 0.003 |
| Example 10 | 0.12 | 0.74 | 1.2 | 0.011 | 0.004 | 0.02 | 0.011 | 0.012 | 0.003 |
| Comparative example 1 | 0.15 | 0.35 | 1.52 | 0.01 | 0.003 | 0.04 | 0.03 | 0.03 | 0.005 |
| Comparative example 2 | 0.17 | 0.32 | 1.58 | 0.012 | 0.003 | 0.035 | 0.05 | 0.04 | 0.003 |
| Comparative example 3 | 0.008 | 0.25 | 0.4 | 0.009 | 0.002 | 0.05 | 0.004 | 0.03 | 0.005 |
| Comparative example 4 | 0.25 | 0.25 | 2.2 | 0.009 | 0.002 | 0.05 | 0.025 | 0.03 | 0.005 |
| Comparative example 5 | 0.22 | 0.18 | 1 | 0.012 | 0.001 | 0.05 | 0.011 | 0.02 | 0.003 |
Meanwhile, the above comparative example 5 further contains the element V, and its content is 0.004%.
The technological parameters of the wear-resistant steel prepared by smelting the alloy listed in the table 1 are respectively shown in tables 2 and 3;
TABLE 2 tabulations (A) of the process parameters for each of the examples and comparative examples
TABLE 3 tabulation of the process parameters for each example and comparative example (II)
The properties of HB400 grade hot continuous rolling wear resistant steels containing ferrite according to GB/T228 and GB/T231 national standards of test examples 1-10 and comparative examples 1-2 are shown in Table 4.
TABLE 4 List of the properties of the examples and comparative examples
Fig. 1 is a schematic view of the microstructure of the wear-resistant steel manufactured in example 1 of the present invention, and it can be known from fig. 1 that the microstructure of the wear-resistant steel is fine and uniform tempered martensite and about 25% to 30% ferrite under a specific process.
As can be seen by combining the table 1, the table 2, the table 3 and the table 4, the wear-resistant steel prepared by adopting the alloy elements and the preparation process designed by the invention has the advantages of low yield ratio, relatively good wear resistance, stable and excellent plate shape performance, HB400 hardness level, elongation of more than 12 percent and plate shape quality within 5mm/m after further transverse cutting.
In addition, the wear-resistant steel prepared by the invention has excellent cold bending performance, the transverse cold bending d is 4a, the bending at 90 degrees is qualified, the bending d is 5a, the bending at 180 degrees is qualified, and the wear-resistant steel can be applied to various application environments.
As known by the technical personnel in the field, the production of the hot continuous rolling wear-resistant steel needs a heat treatment process, and the steel needs to be leveled after on-line quenching, the process is relatively complex, the preparation process of the steel is relatively simple, heat treatment is not needed, leveling is not needed after on-line quenching, direct transverse cutting delivery is only needed, and the production efficiency is relatively high.
In addition, the performances of the wear-resistant steel for the carriage plate prepared by the method are compared with those of HB400 grade hot continuous rolling wear-resistant steel containing ferrite prepared by 5, and the yield ratio of the alloy steel designed by the method is improved, and meanwhile, the wear resistance is also reduced, which is possibly related to the differential control of alloy elements. Therefore, the alloy steel designed by the application is more suitable for the carriage plate.
The above examples are merely preferred examples and are not intended to limit the embodiments of the present invention. In addition to the above embodiments, the present invention has other embodiments. All technical solutions formed by adopting equivalent substitutions or equivalent transformations fall within the protection scope of the claims of the present invention.
Claims (10)
1. The hot continuous rolling dual-phase wear-resistant steel for the carriage plate is characterized by comprising the following chemical components in percentage by mass:
c: 0.10 to 0.20%, Si: 0.08-0.90%, Mn: 0.5-2.0%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Als: 0.01-0.06%, Nb is less than or equal to 0.02%, Ti is less than or equal to 0.02%, B is less than or equal to 0.005%, and the balance is Fe and impurities.
2. The hot continuous rolling dual-phase wear-resistant steel for the carriage plate according to claim 1, which comprises the following chemical components in percentage by mass:
c: 0.10 to 0.16%, Si: 0.08 to 0.87%, Mn: 0.5-1.5%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Als: 0.01-0.06%, Nb is more than or equal to 0.005% and less than or equal to 0.012%, Ti is more than or equal to 0.001% and less than 0.012%, B is less than 0.004%, and the balance is Fe and impurities.
3. The hot-rolled dual-phase wear-resistant steel for the carriage plate according to claim 2, wherein the carbon element satisfies the following formula (C: 0.14-0.16%; the manganese element satisfies the following formula (Mn: 1.2 to 1.5 percent.
4. A production method of hot continuous rolling dual-phase wear-resistant steel for a carriage plate is characterized by comprising the following process flows of:
adopting blast furnace molten iron, molten iron desulphurization, converter smelting, LF + RH refining, continuous casting, heating, rolling, cooling, coiling, splitting and transverse cutting processes;
the heating process comprises the following steps:
the second-stage heating temperature and the soaking end-stage temperature are 1200-1300 ℃, the total time of the second-stage heating and soaking is not less than 60min, and the total in-furnace time is not less than 140 min;
the rolling comprises rough rolling and finish rolling, the outlet temperature of the rough rolling is 1000-1100 ℃, the thickness of an intermediate billet is 30-50 mm, the start rolling temperature of the finish rolling is 950-1050 ℃, the rolling speed is 3-8 m/s, and the finish rolling temperature is 800-900 ℃;
the cooling and coiling process comprises the following steps:
and immediately cooling the FT7, cooling to 580-650 ℃ at a cooling speed of 10-100 ℃/s, air-cooling for 5-15 s, continuously controlling the cooling speed to be 5-100 ℃/s, cooling to 150-300 ℃, coiling, and realizing on-line quenching.
5. The production method of the hot continuous rolling dual-phase wear-resistant steel for the carriage plate as claimed in claim 4, wherein the heating process comprises the following steps:
the second-stage heating temperature and the soaking end-stage temperature are 1210-1285 ℃, the total time of the second-stage heating and soaking is 65-95 min, and the total in-furnace time is 150-180 min.
6. A production method of hot continuous rolling dual-phase wear-resistant steel for carriage plates according to claim 4, wherein the rough rolling outlet temperature is 1010-1090 ℃.
7. The production method of the hot continuous rolling dual-phase wear-resistant steel for the carriage plate as claimed in claim 4, wherein the finish rolling start temperature is 960-1040 ℃, the rolling speed is 3-8 m/s, and the finish rolling temperature is 800-870 ℃.
8. The production method of the hot continuous rolling dual-phase wear-resistant steel for the carriage plate as claimed in claim 4, wherein the cooling speed of the first section is 25-81 ℃/s.
9. The production method of the hot continuous rolling dual-phase wear-resistant steel for the carriage plate as claimed in claim 4, wherein the cooling rate of the second section is 5-40 ℃/s, and the cooling is performed to 160-300 ℃.
10. The production method of the hot continuous rolling dual-phase wear-resistant steel for the carriage plate as claimed in claim 4, wherein the air cooling time is 6-14 s.
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