CN112458377A - Ferrite-based wear-resistant steel and preparation method thereof - Google Patents
Ferrite-based wear-resistant steel and preparation method thereof Download PDFInfo
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- CN112458377A CN112458377A CN202011380495.7A CN202011380495A CN112458377A CN 112458377 A CN112458377 A CN 112458377A CN 202011380495 A CN202011380495 A CN 202011380495A CN 112458377 A CN112458377 A CN 112458377A
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- resistant steel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with 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
- 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
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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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
-
- 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
- C21D2211/009—Pearlite
Abstract
The invention discloses ferrite-based wear-resistant steel and a preparation method thereof, belonging to the technical field of hot continuous rolling strip production. The invention provides ferrite-based hot-rolled wear-resistant steel with low cost, high strength, excellent formability, weldability and wear resistance, which comprises the following components: c: 0.15 to 0.25 percent, Ti: 0.35 to 0.50%, Nb: 0-0.05%, Cr: 0-0.5%, Mo: 0.1-0.3%, and the balance of Fe and unavoidable impurities. According to the invention, 0.35-0.50% of Ti is added, other components are controlled, and the process is optimized, and the precipitation of micron-nanometer dual-scale Ti (C, N) is used as a hard phase, so that the matrix structure is ferrite and a small amount of pearlite, the wear-resisting life is prolonged, the wear resistance of the abrasive particles is equivalent to NM400, the material is ensured to have excellent forming and welding properties, and the tensile strength reaches 800 MPa.
Description
Technical Field
The invention belongs to the technical field of hot continuous rolling strip production, and particularly relates to ferrite-based wear-resistant steel and a preparation method thereof, wherein the microstructure of the wear-resistant steel is ferrite and a small amount of pearlite, and the wear resistance of the wear-resistant steel is equivalent to NM 400.
Background
According to the relevant foreign experimental data, the vehicle weight is reduced by 10%, namely the oil consumption is reduced by 5-8%. For the truck, the weight of the truck is reduced, and the effective load weight can be improved, namely, the mass utilization coefficient is increased, so that the transportation efficiency is improved, the transportation cost is reduced, and meanwhile, the fuel cost is also reduced. At present, a lot of lightweight materials applied to domestic and foreign trucks comprise high-strength steel, aluminum alloy, magnesium alloy and the like. However, for vehicles transporting ores, coal and sand, the use requirements cannot be met by improving the strength of the carriage to reduce the self-weight alone, and impact of large-size ores and abrasive particles of small-size hard objects such as coal, sand and soil are abraded in the transportation process, so that steel materials with excellent forming performance and welding performance and excellent wear resistance are required.
The wear-resistant steel materials most widely used in industry mainly fall into three main categories: high manganese steel, wear-resistant cast iron (steel) and low-alloy wear-resistant steel.
High manganese steel is a traditional wear-resistant material and has high toughness, but the wear resistance of the high manganese steel depends on working conditions to a great extent. Under the conditions of serious impact and large stress, the high manganese steel is not lost as a superior wear-resistant material; however, under the conditions of small impact load and small stress, the advantages of the high manganese steel cannot be fully exerted, and the wear resistance of the high manganese steel is not high.
High-chromium cast iron (steel), namely a second-generation wear-resistant material, is formed by embedding M7C3 carbide with the Vickers hardness as high as 1300-1800 HV on a martensite (austenite) matrix, and the material shows little wear loss and long service life under a plurality of working conditions, but has limited application range due to the fact that the material contains a large amount of rare elements such as chromium, nickel and the like, and has strict and complex production process requirements and the inherent brittleness characteristic of the material.
The low-alloy high-strength wear-resistant steel has good wear resistance, the service life of the low-alloy high-strength wear-resistant steel is several times that of a traditional structural steel plate, the production process is simple, and the quenching and tempering process after rolling is generally adopted. Some steel companies in Japan, Germany and Sweden all produce low-alloy high-strength wear-resistant steel, and the German-derson Krupp XAR series wear-resistant steel has the hardness range of HB300-600 and is mainly alloyed by Cr and Mo. The series of wear-resistant steel plates such as German Dillidur400, DIllidur500 and the like have Brinell hardness of HB400 and HB500 respectively, the thickness range can cover 6-150mm, and the quenching and low-temperature tempering process is adopted after rolling. The low-alloy wear-resistant steel in China obtains the following structural states through alloy control and heat treatment: the lath martensite + lath retained austenite structure can be obtained by quenching and low-temperature tempering (for example, NM450(930 ℃ + heat preservation for 20min for quenching, 200 ℃ + heat preservation for 25min for tempering treatment), NM500(880 ℃ + heat preservation for 15min for quenching, 180 ℃ + heat preservation for 30min for tempering treatment)), bainite or a composite structure of bainite + martensite, and can be obtained by isothermal treatment or continuous cooling.
Aiming at the limitations of high manganese steel application occasions and the defects of high cost of wear-resistant cast iron (steel), a production method of high-hardness wear-resistant steel, such as martensite wear-resistant steel, bainite wear-resistant steel, austenite wear-resistant steel and the like, is obtained by adopting a mode of combining rolling and heat treatment in recent years. The wear-resistant steel has relatively low production cost and good wear resistance. However, the steel has poor plasticity because of high wear resistance obtained by rolling control, and is difficult to popularize and use for parts requiring forming.
Disclosure of Invention
The technical problem to be solved by the invention is as follows: a hot rolled steel sheet having low cost, high strength, excellent formability, weldability and abrasion resistance is provided.
In order to solve the technical problems, the invention provides ferrite-based wear-resistant steel which comprises the following chemical components in percentage by mass: c: 0.15 to 0.25 percent, Ti: 0.35 to 0.50%, Nb: 0-0.05%, Cr: 0-0.5%, Mo: 0.1-0.3%, and the balance of Fe and inevitable impurity elements.
Wherein, in the ferrite-based wear-resistant steel, the mass percent of Nb is 0.01-0.05%.
Wherein, in the ferrite-based wear-resistant steel, the mass percent of Cr is 0.2-0.5%.
Wherein, in the ferrite-based wear-resistant steel, the mechanical properties of the ferrite-based wear-resistant steel are as follows: ReL is more than or equal to 750MPa, Rm: 800-930 MPa, and A is more than or equal to 16.0%.
In the ferrite-based wear-resistant carriage steel, the wear resistance of the ferrite-based wear-resistant steel is equivalent to that of NM400 martensite wear-resistant steel, and the wear resistance index is 0.30-0.90 through the test of the method.
The invention also provides a preparation method of the ferrite-based wear-resistant steel, which comprises the following steps: performing molten iron desulphurization, converter smelting and LF furnace Ca treatment, controlling the components of molten steel according to the above steps, continuously casting to obtain a plate blank, and soaking the plate blank at 1210-1270 ℃; rough rolling, wherein the total deformation of the rough rolling is controlled to be more than or equal to 75 percent; performing finish rolling, wherein the inlet temperature of the finish rolling is controlled to be 950-1080 ℃, and the finishing temperature is controlled to be 830-920 ℃; and after finishing the finish rolling, cooling, and coiling at 590-640 ℃ to obtain a finished product.
Wherein, in the preparation method of the ferrite-based wear-resistant steel, the thickness of the obtained continuous casting billet is 200 mm-230 mm.
In the preparation method of the ferrite-based wear-resistant steel, the soaking time is 180-320 min.
In the preparation method of the ferrite-based wear-resistant steel, the rough rolling is carried out for 3-7 times; the deformation of the first pass of rough rolling is more than or equal to 20 percent.
In the preparation method of the ferrite-based wear-resistant steel, the thickness of the intermediate blank obtained by rough rolling is 30-60 mm.
In the preparation method of the ferrite-based wear-resistant steel, the cooling speed is 20-70 ℃/s.
The invention has the beneficial effects that:
according to the invention, 0.35-0.50% of Ti is added, other components are controlled, the process is optimized, precipitation of micron-nanometer dual-scale Ti (C, N) is used as a hard phase, a matrix structure is ferrite and a small amount of pearlite, the wear-resisting life is prolonged, the wear-resisting life of abrasive particles is equivalent to that of NM400, the material is ensured to have excellent forming and welding performance, the tensile strength reaches 800MPa level, and the material can be used as compartment steel; the invention can finish the production by using a common hot continuous rolling production line without heat treatment, thereby reducing the production cost and simplifying the operation.
Drawings
Fig. 1 is a ferrite + pearlite structure diagram of a steel coil obtained in example 1.
Fig. 2 is a Ti (C, N) hard phase diagram of the steel coil obtained in example 1, wherein the gray points are precipitated phases of the micron-nanometer dual-scale Ti (C, N).
Fig. 3 is a schematic view of the abrasive wear test equipment adopted by the invention.
Detailed Description
Specifically, the ferrite-based wear-resistant steel comprises the following chemical components in percentage by mass: c: 0.15 to 0.25 percent, Ti: 0.35 to 0.50%, Nb: 0-0.05%, Cr: 0-0.5%, Mo: 0.1-0.3%, and the balance of Fe and unavoidable impurities.
In the prior art, structure regulation is generally adopted, for example, microstructure of lath martensite + residual austenite between laths, bainite or bainite + martensite is formed to improve the wear resistance of steel, and by adding Ti, a precipitated phase of micron-nanometer dual-scale Ti (C, N) is used as a hard phase, and by controlling a matrix structure to be ferrite + a small amount of pearlite, the material is ensured to have excellent forming and welding properties and wear resistance; meanwhile, the content of Ti is controlled to be 0.35-0.50%, so that enough precipitation of micron-nanometer dual-scale Ti (C, N) is ensured to be used as a hard phase, and thus, in the abrasion process, the function of protecting a steel plate matrix can be realized under the hardness, and the service life of abrasion of the steel plate abrasive particles can be equivalent to that of NM 400.
In order to further ensure the performance of the steel, the content of Nb and Cr is not 0 at the same time, so that the mass percent of Nb is preferably controlled to be 0.01-0.05% and/or the mass percent of Cr is preferably controlled to be 0.2-0.5%.
The invention also provides a preparation method of the ferrite-based wear-resistant steel, which comprises the following steps: molten iron desulfurization, converter smelting and LF furnace Ca treatment are carried out to obtain molten steel with the components; continuously casting molten steel to obtain a plate blank, and soaking the plate blank for 180-320 min at 1210-1270 ℃; rough rolling, wherein the deformation of the first pass of the rough rolling is controlled to be more than or equal to 20 percent, and the total deformation is controlled to be more than or equal to 75 percent; performing finish rolling, wherein the inlet temperature of the finish rolling is controlled to be 950-1080 ℃, and the finishing temperature is controlled to be 830-920 ℃; and after finishing the finish rolling, cooling to 590-640 ℃ and coiling to obtain a finished product.
The invention takes the precipitation of micron-nanometer dual-scale Ti (C, N) as a hard phase, wherein one part of the precipitated phase comes from a precipitated phase with large size microns in the continuous casting process, and is crushed and homogenized in the hot continuous rolling process, which is micron-sized, and the other part of the precipitated phase is a deformation-induced precipitated phase in the hot continuous rolling process and a supersaturated precipitated phase in ferrite, which is nano-sized, so that the precipitated phase of micron-nanometer dual-scale Ti (C, N) is obtained.
In the method, the thickness of the obtained continuous casting billet is controlled to be 200-230 mm, and the thickness of the intermediate billet obtained by rough rolling is controlled to be 30-60 mm.
According to the invention, the process is optimized, so that the final structure enables the matrix structure to have better toughness and plasticity, the temperature of a finish rolling inlet is controlled to be 950-1080 ℃ and the temperature of a finish rolling is controlled to be 830-920 ℃ in the deformation process, and then the matrix structure is rapidly cooled to 590-640 ℃ at a cooling speed of 20-70 ℃/s for coiling, so that the large-size micron precipitated phase in the continuous casting process is reduced and uniform, and the matrix structure is controlled to be ferrite and a small amount of pearlite.
According to the invention, the matrix structure is controlled to be ferrite and a small amount of pearlite, so that the obtained steel has good toughness and is easy to form, expand and turn over, the wear-resisting index reaches 0.30-0.90, the service life of abrasive wear is equivalent to NM400, and the mechanical properties meet the requirements that ReL is more than or equal to 750MPa, Rm: 800-930 MPa, A is more than or equal to 16.0 percent, and the steel can be used as carriage steel.
The present invention is further illustrated by the following examples, which are not intended to limit the scope of the invention.
The NM mark is martensite wear-resistant steel, the wear resistance measurement method is to measure the hardness of the martensite wear-resistant steel, and the martensite is hard, so the characterization index of the martensite wear-resistant steel is higher.
Therefore, in the examples and comparative examples of the present invention, the wear resistance index was measured by the following method: wear resistance index is weight loss/load/sliding distance, wherein weight loss is weight after wear-weight before wear, load is 170N, and sliding distance is total sliding length of the pulley; the specific operation is as follows: a sample with the size of 57 × 25.5 × 6.0mm is placed on a sample table and fixed, 1.5kg of sand and 1kg of water are added into a container, a load of 170N is applied, and then a pulley and the sample are in contact rotation, so that the water sand can be sufficiently rubbed on the sample.
Example 1
The molten steel is subjected to the steelmaking step and then comprises the following components: 0.17% by weight of C, 0.36% by weight of Ti, 0.27% by weight of Cr, 0.21% by weight of Mo, and the balance being Fe and inevitable impurities, the thickness of a continuously cast slab being 230mm, soaking the slab in a heating furnace at 1250 ℃ to obtain an intermediate slab having a thickness of 43mm after rough rolling, a finishing rolling start temperature of 1060 ℃, and a finishing rolling temperature of 910 ℃. The thickness of the steel plate after finish rolling is 3.0mm, and then the steel plate is cooled to 620 ℃ at the cooling speed of 67 ℃/s through front-section laminar cooling and coiled; the yield strength (ReL), the tensile strength (Rm), the elongation (A) and the wear resistance index of the steel coil are shown in Table 1.
Example 2
The molten steel is subjected to the steelmaking step and then comprises the following components: 0.21% by weight of C, 0.50% by weight of Ti, 0.022% by weight of Nb, 0.27% by weight of Mo, and the balance being Fe and inevitable impurities, the thickness of a continuously cast slab being 200mm, then soaking in a heating furnace at 1230 ℃ to obtain a roughly rolled intermediate slab having a thickness of 45mm, a finishing rolling start temperature of 950 ℃ and a finishing rolling temperature of 830 ℃. The thickness of the steel plate after finish rolling is 3.0mm, and then the steel plate is cooled to 590 ℃ at a cooling speed of 68 ℃/s through front-section laminar cooling and is coiled; the yield strength (ReL), the tensile strength (Rm), the elongation (A) and the wear resistance index of the steel coil are shown in Table 1.
Example 3
The molten steel is subjected to the steelmaking step and then comprises the following components: 0.22% by weight of C, 0.47% by weight of Ti, 0.011% by weight of Nb, 0.29% by weight of Cr, 0.18% by weight of Mo, and the balance Fe and inevitable impurities, the thickness of a continuously cast slab being 220mm, then soaking in a furnace at 1240 ℃ and the thickness of a roughly rolled intermediate slab being 36mm, the finishing rolling temperature being 1000 ℃ and the finishing rolling temperature being 870 ℃. The thickness of the steel plate after finish rolling is 6.0mm, and then the steel plate is cooled to 610 ℃ at a cooling speed of 52 ℃/s through front-section laminar cooling and coiled; the yield strength (ReL), the tensile strength (Rm), the elongation (A) and the wear resistance index of the steel coil are shown in Table 1.
Comparative example 1
The molten steel is subjected to the steelmaking step and then comprises the following components: 0.23% by weight of C, 0.12% by weight of Ti, 0.046% by weight of Nb, 0.24% by weight of Cr, 0.19% by weight of Mo, the balance being Fe and unavoidable impurities, the thickness of the continuously cast slab being 230mm, then soaking in a 1230 ℃ heating furnace, the thickness of the roughly rolled intermediate slab being 59mm, the finishing rolling temperature being 950 ℃ and the finishing rolling temperature being 840 ℃. The thickness of the steel plate after finish rolling is 16.0mm, and then the steel plate is cooled to 630 ℃ at a cooling speed of 24 ℃/s through front-section laminar cooling and coiled; the yield strength (ReL), the tensile strength (Rm), the elongation (A) and the wear resistance index of the steel coil are shown in Table 1.
Comparative example 2
The molten steel is subjected to the steelmaking step and then comprises the following components: 0.21 wt% of C, 0.50 wt% of Ti, 0.022 wt% of Nb, 0.27 wt% of Mo, and the balance of Fe and inevitable impurities, the thickness of a continuously cast slab being 200mm, soaking in a heating furnace at 1160 ℃ to obtain an intermediate slab after rough rolling having a thickness of 41mm, a finishing rolling start temperature of 930 ℃ and a finishing rolling temperature of 780 ℃. The thickness of the steel plate after finish rolling is 5.0mm, and then the steel plate is cooled to 580 ℃ at the cooling speed of 9 ℃/s through front-section laminar cooling to be coiled; the yield strength (ReL), the tensile strength (Rm), the elongation (A) and the wear resistance index of the steel coil are shown in Table 1.
TABLE 1 mechanical Properties and wear indices of steels
| ReL(MPa) | Rm(MPa) | A(％) | Wear resistance index | |
| Example 1 | 766 | 857 | 19.5 | 0.88 |
| Example 2 | 792 | 889 | 20.0 | 0.34 |
| Example 3 | 827 | 908 | 18.5 | 0.53 |
| Comparative example 1 | 778 | 874 | 20.5 | 2.98 |
| Comparative example 2 | 633 | 712 | 17.5 | 1.62 |
The wear-resisting index of NM400 steel is detected by the same method, the wear-resisting index is 0.86, and the smaller the wear-resisting index is, the better the wear-resisting property is, therefore, the data in Table 1 show that the precipitated phase of micron-nanometer dual-scale Ti (C, N) is taken as the hard phase, the wear-resisting service life of the steel is obviously prolonged, and meanwhile, the steel has excellent mechanical properties.
Claims (10)
1. Ferrite-based wear-resistant steel, characterized in that: the paint comprises the following chemical components in percentage by mass: c: 0.15 to 0.25 percent, Ti: 0.35 to 0.50%, Nb: 0-0.05%, Cr: 0-0.5%, Mo: 0.1-0.3%, and the balance of Fe and unavoidable impurities.
2. The ferritic based wear resistant steel according to claim 1 characterized in that: the mass percent of Nb is 0.01-0.05%.
3. The ferritic based wear resistant steel according to claim 1 characterized in that: the mass percent of the Cr is 0.2-0.5%.
4. The ferritic based abrasion resistant steel according to any one of claims 1 to 3, characterized in that: the mechanical properties of the ferrite-based wear-resistant steel are as follows: ReL is more than or equal to 750MPa, Rm: 800-930 MPa, and A is more than or equal to 16.0%.
5. The method of producing a ferritic-based wear-resistant steel as set forth in any one of claims 1 to 4, characterized by: the method comprises the following steps: performing molten iron desulphurization, converter smelting and LF furnace Ca treatment, controlling the components of molten steel according to any one of claims 1-4, continuously casting to obtain a plate blank, and soaking the plate blank at 1210-1270 ℃; rough rolling, wherein the total deformation of the rough rolling is controlled to be more than or equal to 75 percent; performing finish rolling, wherein the inlet temperature of the finish rolling is controlled to be 950-1080 ℃, and the finishing temperature is controlled to be 830-920 ℃; and after finishing the finish rolling, cooling, and coiling at 590-640 ℃ to obtain a finished product.
6. The method of producing a ferritic based wear resistant steel according to claim 5, characterized in that: the thickness of the obtained continuous casting billet is 200 mm-230 mm.
7. The method of producing a ferritic based wear resistant steel according to claim 5, characterized in that: the soaking time is 180-320 min.
8. The method of producing a ferritic based wear resistant steel according to claim 5, characterized in that: the rough rolling is carried out for 3-7 times; the deformation of the first pass of rough rolling is more than or equal to 20 percent.
9. The method of producing a ferritic based wear resistant steel according to claim 5, characterized in that: the thickness of the intermediate blank obtained by rough rolling is 30-60 mm.
10. The method of producing a ferritic-based wear resistant steel according to any one of claims 5 to 9, characterized in that: the cooling speed of the cooling is 20-70 ℃/s.
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| CN113957357A (en) * | 2021-10-29 | 2022-01-21 | 攀钢集团攀枝花钢铁研究院有限公司 | Hot-rolled wear-resistant steel and production method thereof |
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| CN108118257A (en) * | 2017-12-19 | 2018-06-05 | 钢铁研究总院 | TiC particle strengthenings ferrite/bainite base wear-resisting steel plate and manufacturing method |
| CN108998615A (en) * | 2018-09-13 | 2018-12-14 | 武汉钢铁有限公司 | A kind of 600MPa grades of offshore engineering structure steel and production method with excellent wear |
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| CN108118257A (en) * | 2017-12-19 | 2018-06-05 | 钢铁研究总院 | TiC particle strengthenings ferrite/bainite base wear-resisting steel plate and manufacturing method |
| CN108998615A (en) * | 2018-09-13 | 2018-12-14 | 武汉钢铁有限公司 | A kind of 600MPa grades of offshore engineering structure steel and production method with excellent wear |
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| CN113957357A (en) * | 2021-10-29 | 2022-01-21 | 攀钢集团攀枝花钢铁研究院有限公司 | Hot-rolled wear-resistant steel and production method thereof |
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Application publication date: 20210309 |