CN111876674A - Preparation method of high-strength medium-carbon low-alloy steel plate - Google Patents
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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
- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0231—Warm 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
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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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
- C21D2211/003—Cementite
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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
A preparation method of a high-strength medium-carbon low-alloy steel plate comprises the following steps: (1) smelting molten steel according to the D6A steel component, smelting under the protective atmosphere condition, and casting to prepare an ingot with original coarse grains; (2) heating the cast ingot to 1200 +/-50 ℃ for solution treatment, then carrying out 6-pass hot rolling, and air-cooling to room temperature to prepare a hot rolled plate; (3) heating to 760 +/-20 ℃, preserving the temperature for 5-10 min, and carrying out single-pass warm rolling to obtain 20 +/-0.5% of total deformation; air cooling to room temperature, keeping the temperature at 650 +/-20 ℃ for 10-15 min, and air cooling to room temperature. The product of the invention has higher room temperature tensile strength and good plasticity, and is superior to the comprehensive mechanical property of steel materials prepared by the traditional quenching and tempering method; the preparation method is simple, and can be obtained by only improving process conditions and controlling proper heat treatment parameters.
Description
Technical Field
The invention belongs to the technical field of materials, and particularly relates to a preparation method of a high-strength medium-carbon low-alloy steel plate.
Background
The low-alloy ultrahigh-strength steel is developed on the basis of adding a small amount of alloy elements into structural steel, wherein the alloy elements enable the steel to generate solid solution strengthening and improve the hardenability of the steel and the tempering stability of martensite through the alloy elements; the main alloy elements comprise Mn, Cr, Si, Ni, Mo, V and the like, but the total content of the Mn, Cr, Si, Ni, Mo, V and the like is generally within 5 percent; compared with structural steel, the structural steel has slightly higher Mo content and slightly different contents and types of other alloy elements, can be roughly divided into steel systems such as CrNiMo steel, CrMo steel, CrMnNiSi steel, CrMnSi steel, SiMnAlV steel and the like, the carbon content is generally 0.27-0.50%, the structure of most low-alloy high-strength commercial steel is tempered martensite or lower bainite, and the tensile strength of the steel is mainly determined by the carbon content in the steel or the carbon equivalent in the martensite.
The high strength is one of the trends of the development of steel materials, and is an important way for realizing energy conservation and emission reduction. Although various new materials are continuously appeared, the ultrahigh strength steel still has great advantages in the aspects of elastic modulus, impact toughness, strength and the like. Generally, the steel with the tensile strength of more than 1350MPa is considered to be ultrahigh-strength steel, and is widely applied to the field of aerospace. The development and preparation of the new generation of low-alloy high-strength steel mainly aims at obtaining a superfine crystal structure (less than 1 mu m) with uniform structure and no defect; the grain refinement can improve the strength and the toughness of the material, is always an effective method for improving the comprehensive mechanical property of the material, and is a development direction of low-alloy high-strength steel in the new century; the current superfine crystal steel material storage technology mainly comprises the following steps: a large plastic deformation preparation technology, a heat treatment preparation technology, a deformation induced ferrite phase change preparation technology, a micro-alloying preparation technology, a field treatment preparation technology and the like; however, the ultra-fine grain preparation technology in the field of steel materials is limited by the application range of the preparation technology and develops slowly.
D6A is a medium-carbon low-alloy ultrahigh-strength steel with good hardenability, has the advantages of high strength, good stress corrosion resistance, low cost, reliable application and the like, and is widely applied to manufacturing high-strength structural parts such as airplane engine crankshafts, crossbeams, landing gears, medium and small rocket cases and the like at present; however, although the conventional process for preparing the D6A steel by quenching and tempering firstly can obtain high strength, the comprehensive performance is influenced by poor plasticity. Multiple researches show that the obtained high-strength and high-toughness ultrafine grain steel not only adopts forced deformation and dynamic recrystallization rolling factors, but also can adopt a deformation induced ferrite phase transition (DIFT) technology to deform the steel near the Ac1 temperature, so that the energy in austenite is increased, the stability is reduced, and the ultrafine grain is obtained.
In actual industrial production, the strength and toughness of the material are improved by adopting a grain refining method, and the method can be described by using a famous Hall-Petch relation, namely, a large amount of grain boundary nail rolling dislocation is utilized to block the movement of the dislocation. Therefore, how to control the grain size by proper components and processing technology design and further improve the yield strength by the pinning effect of the grain boundary or substructure on dislocation has a certain plastic deformation capability, and becomes one of the hot spots of material research. In general, grain refinement of metallic materials is mainly achieved by conventional plastic deformation processing and subsequent annealing processes, i.e., recrystallization and grain growth, in which a common coarse-crystal steel (grain size of about 100 μm) is stretched at room temperature with a yield strength (σ y) of about 90MPa, an ultra-fine-crystal microalloy steel ((Fe-0.8C, grain size of about 6 μm) is stretched at room temperature with a yield strength σ y of 310MPa (Bramfitt B.L, MarderA.R, Metallurgical and Petroleum Engineers, 191-198(1973)), and a low-alloy ultra-high-strength steel for aerospace (D6AC) is subjected to vacuum induction melting and electroslag remelting, followed by 900 ℃ x 20min air cooling and 880 ℃ x 20min oil cooling
Air cooling at 550 deg.C for 2 hr to yield strength of 1400MPa (Chengkui, performance study of D6AC ultrahigh strength steel, Sichuan metallurgy, 1992, 43 (2): 30); when the austenite graded quenching process is 900 ℃/30min-530 ℃/30min oil cooling and then 530 ℃ tempering for 2h, the elongation after fracture is increased from 10% to 14% on the premise of ensuring the high strength of the material (the research of the graded quenching optimization process of D6AC steel austenite bay, aerospace material process, 1994, 5 (4): 33-36); the D6A steel is subjected to two-phase region rolling and annealing treatment to obtain ferrite and nano-scale spherical cementite structures with the grain sizes of 410-780 nm (Wangpojie, microstructure and mechanical properties of rolling-isothermal preparation of ultrafine grain D6A steel, Shenyang: northeast university, 2016).
Singon KANG et al treated D6A steel by Q-P process to obtain retained austenite which is transformed into martensite during the drawing deformation process, with an ultimate tensile strength of about 1500MPa and a total elongation of about 10%, with improved drawing properties compared to conventional quenching and tempering heat treatments (Kang S., Kim K., Son Y I., et al. application of working and finishing to D6AC steel,2016,56(11): 2057-. Khodamorad Abbaszadeh et al found that the yield strength and tensile strength of the mixed structure of martensite and 28% by volume of lower bainite were higher than those of the fully martensitic structure, and could reach 1850MPa (Abbaszadeh K., Saghafian H., Kheiraninss, et al. Effect of basic morphology on mechanical properties of the mixed ideal-martensite microstructure D6AC steel, Journal of materials Science and Technology,2012,28(4): 336-. Chun-Ming Lin et al found that an increase in annealing temperature increased the plasticity of the test steel, but resulted in a decrease in hardness and tensile strength of the test steel (LinC.M., Lu C.H., Effects of measuring temperature on microstructural evaluation and mechanical properties of high-strength h low-alloy D6AC planar arcs, Materials Science and Engineering A,2016,676(5): 28-37). The tempering Lian is used for tempering D6AC steel, the yield strength is increased from 400MPa to 1300MPa, the elongation is increased from 0.4% to 9% (Lian. microscopic properties of the treated D6ac steel [ J ]. Applied surface science,2013,264(JAN.1):100-104), although the yield strength and the tensile strength are high, the plasticity is still low, the best matching of the strength and the plasticity is not achieved, and the requirements of the field with high requirements on the strength and the plasticity cannot be met.
Disclosure of Invention
Aiming at the defects of the existing preparation process on the comprehensive mechanical property, the invention provides a preparation method of a high-strength medium-carbon low-alloy steel plate, which controls the grain refinement of ferrite and the precipitation of cementite by controlling a rolling-annealing process, so that the material generates a strengthening effect similar to the Hall-Petch effect, the high-strength steel with micron-grade fine grain strengthening is prepared, and the comprehensive property of the material is improved.
The method of the invention is carried out according to the following steps:
1. smelting molten steel according to the component D6A steel, wherein the component comprises, by mass, 0.42-0.45% of C, 0.16-0.18% of Si, 0.71-0.74% of Mn, less than or equal to 0.014% of P, 1-1.03% of Mo, 1.02-1.06% of Cr, 0.006-0.008% of Ni, 0.08-0.1% of V, 0.002-0.006% of N, 0.02-0.04% of Al, less than or equal to 0.005% of S, and the balance of Fe and unavoidable impurities; smelting under the condition of protective atmosphere, and casting to prepare an ingot with original coarse crystals;
2. heating the cast ingot to 1200 +/-50 ℃, preserving heat for 120-150 min, carrying out solid solution treatment, then carrying out 6-pass hot rolling, carrying out initial rolling at the temperature of 1150 +/-50 ℃, carrying out final rolling at the temperature of 950 +/-50 ℃ and carrying out total deformation at the temperature of 84 +/-0.5%, and carrying out air cooling to room temperature to obtain a hot rolled plate;
3. heating the hot rolled plate to 760 +/-20 ℃, preserving heat for 5-10 min, and then carrying out single-pass warm rolling, wherein the initial rolling temperature of the single-pass warm rolling is 760 +/-20 ℃, and the total deformation is 20 +/-0.5%; and air-cooling to room temperature after single-pass warm rolling, heating to 650 +/-20 ℃, preserving the temperature for 10-15 min, and finally air-cooling to room temperature to prepare the high-strength medium-carbon low-alloy steel plate.
The microstructure of the cast ingot is ferrite and pearlite, the grain size is 15-25 mu m, the yield strength is 390 +/-5 MPa, the tensile strength is 750 +/-5 MPa, and the elongation is 22 +/-0.5%.
The microstructure of the high-strength medium-carbon low-alloy steel plate is ferrite, cementite and a small amount of martensite, the grain size is 2-5 mu m, the yield strength is 1000 +/-5 MPa, the tensile strength is 1170 +/-5 MPa, and the elongation is 19 +/-0.5%.
According to the invention, the rolling-annealing combined treatment is carried out on the coarse-grain D6A steel (cast ingot), so that the fine-grain D6A steel with higher strength can be obtained; the grains are continuously refined, the density of the grain boundary is improved, and the movement of dislocation is hindered by the grain boundary, so that the finer the grains are, the higher the density of the grain boundary is, the more difficult the movement of dislocation is, and the strength is improved; the fine-grained D6A steel structure contains a large amount of nano-sized cementite (second phase) which can hinder the movement of dislocations to increase the strength, and the larger the volume content of the second phase, the finer the size, the more the strength increase is brought about, so the fine-grained strengthening and the second phase (granular cementite) strengthening result in a large increase in strength.
The material with fine grain size and high strength is prepared by reasonable heat treatment process and process parameters, has higher room-temperature tensile strength and good plasticity, and is superior to the comprehensive mechanical property of the steel material prepared by the traditional quenching and tempering method; the product has strong applicability, the grain boundary area is increased along with the continuous refinement of crystal grains in the rolling process, a large amount of dislocation is generated, and simultaneously, the movement of the dislocation is blocked due to the existence of the nano-scale granular cementite, so the structures of ferrite and the granular cementite have the effects of high strength and high toughness; the method has important significance for the development of industries such as aerospace, automobile, electric power and the like; the preparation method is simple, and can be obtained by only improving process conditions and controlling proper heat treatment parameters.
Drawings
FIG. 1 is a microstructure morphology and an IPF chart of a high-strength medium-carbon low-alloy steel sheet in example 1 of the present invention; wherein, the a picture is a microstructure topography picture, and the b picture is an IPF picture;
FIG. 2 is a stress-strain curve of the cast ingot and the high-strength medium-carbon low-alloy steel sheet in the embodiment 1 of the present invention, which are uniaxially stretched at room temperature; wherein ● is cast ingot, and t is high-strength medium-carbon low-alloy steel plate.
Detailed Description
The hot rolling equipment adopted in the embodiment of the invention is a phi 450 double-roller one-way asynchronous rolling mill.
The warm rolling equipment adopted in the embodiment of the invention is a double-roller mill.
In the embodiment of the invention, a box type resistance furnace is adopted for heating and heat preservation.
In the embodiment of the invention, the adopted heat preservation equipment after warm rolling is an SX-8-13 high-temperature box type resistance furnace.
In the embodiment of the invention, the number of passes of the multi-pass hot rolling is 6.
In the embodiment of the invention, the model of the equipment for observing the microstructure is a JSM-6510A scanning electron microscope.
The model of equipment adopted for IPF observation in the embodiment of the invention is ULTRA55 scanning electron microscope.
The molten steel in the embodiment of the invention comprises, by mass, 0.42-0.45% of C, 0.16-0.18% of Si, 0.71-0.74% of Mn, less than or equal to 0.014% of P, 1-1.03% of Mo, 1.02-1.06% of Cr, 0.006-0.008% of Ni, 0.08-0.1% of V, 0.002-0.006% of N, 0.02-0.04% of Al, less than or equal to 0.005% of S, and the balance Fe.
The protective atmosphere in the embodiment of the invention is argon atmosphere.
The microstructure of the high-strength medium-carbon low-alloy steel plate in the embodiment of the invention is ferrite, cementite and a small amount of martensite, the grain size is 2-5 mu m, the yield strength is 1000 +/-5 MPa, the tensile strength is 1170 +/-5 MPa, and the elongation is 19 +/-0.5%.
The thickness of the high-strength medium-carbon low-alloy steel plate in the embodiment of the invention is 6-10 mm.
Example 1
Smelting molten steel according to the D6A steel component, smelting under the protective atmosphere condition, and casting to prepare an ingot with original coarse grains; the microstructure of the ingot is ferrite and pearlite, the grain size is 15-25 mu m, the yield strength is 390 plus or minus 5MPa, the tensile strength is 750 plus or minus 5MPa, and the elongation is 22 plus or minus 0.5%;
heating the cast ingot to 1200 +/-50 ℃, preserving heat for 120min, carrying out solid solution treatment, then carrying out 6-pass hot rolling, carrying out air cooling to room temperature, and preparing a hot rolled plate, wherein the initial rolling temperature of the hot rolling is 1150 +/-50 ℃, the final rolling temperature is 950 +/-50 ℃, and the total deformation is 84 +/-0.5%;
heating the hot rolled plate to 760 +/-20 ℃, preserving heat for 10min, and then carrying out single-pass warm rolling at the initial rolling temperature of 760 +/-20 ℃ and the total deformation of 20 +/-0.5%; carrying out air cooling to room temperature after single-pass warm rolling to obtain a warm rolled plate, heating the warm rolled plate to 650 +/-20 ℃, then carrying out heat preservation for 10min, and finally carrying out air cooling to room temperature to obtain the high-strength medium-carbon low-alloy steel plate, wherein the microstructure comprises ferrite, cementite and a small amount of martensite, the grain size is 2-5 mu m, the yield strength is 1000 +/-5 MPa, the tensile strength is 1170 +/-5 MPa, and the elongation is 19 +/-0.5%; the microstructure morphology is shown in FIG. 1a, the IPF diagram is shown in FIG. 1b, and the engineering stress-strain curve is shown in FIG. 2; compared with the traditional method, all the properties are in excellent level, the comprehensive properties are quite excellent, the yield strength and the tensile strength are greatly improved under the condition of ensuring that the elongation rate reaches a certain level, and the product of strength and elongation is greatly improved.
Example 2
The method is the same as example 1, except that:
(1) the solution treatment time is 150 min;
(2) keeping the temperature for 5min after 760 +/-20 ℃;
(2) keeping the temperature at 650 +/-20 ℃ for 15 min.
Example 3
The method is the same as example 1, except that:
(1) the solution treatment time is 130 min;
(2) keeping the temperature for 8min after 760 +/-20 ℃;
(2) keeping the temperature at 650 plus or minus 20 ℃ for 12 min.
Claims (3)
1. The preparation method of the high-strength medium-carbon low-alloy steel plate is characterized by comprising the following steps of:
(1) smelting molten steel according to the component D6A steel, wherein the component comprises, by mass, 0.42-0.45% of C, 0.16-0.18% of Si, 0.71-0.74% of Mn, less than or equal to 0.014% of P, 1-1.03% of Mo, 1.02-1.06% of Cr, 0.006-0.008% of Ni, 0.08-0.1% of V, 0.002-0.006% of N, 0.02-0.04% of Al, less than or equal to 0.005% of S, and the balance of Fe and unavoidable impurities; smelting under the condition of protective atmosphere, and casting to prepare an ingot with original coarse crystals;
(2) heating the cast ingot to 1200 +/-50 ℃, preserving heat for 120-150 min, carrying out solid solution treatment, then carrying out 6-pass hot rolling, carrying out initial rolling at the temperature of 1150 +/-50 ℃, carrying out final rolling at the temperature of 950 +/-50 ℃ and carrying out total deformation at the temperature of 84 +/-0.5%, and carrying out air cooling to room temperature to obtain a hot rolled plate;
(3) heating the hot rolled plate to 760 +/-20 ℃, preserving heat for 5-10 min, and then carrying out single-pass warm rolling, wherein the initial rolling temperature of the single-pass warm rolling is 760 +/-20 ℃, and the total deformation is 20 +/-0.5%; and air-cooling to room temperature after single-pass warm rolling, heating to 650 +/-20 ℃, preserving the temperature for 10-15 min, and finally air-cooling to room temperature to prepare the high-strength medium-carbon low-alloy steel plate.
2. The method for preparing a high-strength medium-carbon low-alloy steel plate according to claim 1, wherein the microstructure of the ingot is ferrite and pearlite, the grain size is 15-25 μm, the yield strength is 390 plus or minus 5MPa, the tensile strength is 750 plus or minus 5MPa, and the elongation is 22 plus or minus 0.5%.
3. The method according to claim 1, wherein the microstructure of the high-strength medium-carbon low-alloy steel sheet is ferrite, cementite and a small amount of martensite, the grain size is 2 to 5 μm, the yield strength is 1000 ± 5MPa, the tensile strength is 1170 ± 5MPa, and the elongation is 19 ± 0.5%.
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| CN115323275A (en) * | 2022-09-05 | 2022-11-11 | 东北大学 | High-strength high-toughness rare earth warm-rolled low-carbon low-manganese TRIP steel and preparation method thereof |
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| CN112646958A (en) * | 2020-11-30 | 2021-04-13 | 中国科学院金属研究所 | Heat treatment process of low-alloy high-strength high-weather-resistance structural steel for highway guardrail |
| CN114686664A (en) * | 2022-02-28 | 2022-07-01 | 东北大学 | Composite preparation method of high-strength D6A fine-grained steel |
| CN114686664B (en) * | 2022-02-28 | 2023-03-07 | 东北大学 | Composite preparation method of high-strength D6A fine-grained steel |
| CN115323275A (en) * | 2022-09-05 | 2022-11-11 | 东北大学 | High-strength high-toughness rare earth warm-rolled low-carbon low-manganese TRIP steel and preparation method thereof |
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