CN108929986B - High-strength wear-resistant hot rolled steel plate for automobile braking and production process thereof - Google Patents
High-strength wear-resistant hot rolled steel plate for automobile braking and production process thereof Download PDFInfo
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C21—METALLURGY OF IRON
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- C21C5/00—Manufacture of carbon-steel, e.g. plain mild steel, medium carbon steel or cast steel or stainless steel
- C21C5/28—Manufacture of steel in the converter
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- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
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- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
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- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/10—Handling in a vacuum
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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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- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- 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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- 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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- 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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- 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
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
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- 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
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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- 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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- 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
- C21D2211/001—Austenite
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
A high-strength wear-resistant hot-rolled steel plate for automobile braking is prepared through smelting, refining, continuous casting, rough rolling, finish rolling and heat treatment, wherein the grain size of the microstructure of the steel plate for automobile braking is 20-25 microns after the heat treatment, the average grain size of carbides is 30-50nm, a Cu-rich phase is precipitated, the structure comprises 40-50% of tempered sorbite, 30-35% of martensite and the balance of austenite and bainite in percentage by volume; the yield strength is 1000-1100MPa, the tensile strength is 1200-1350MPa, the elongation is 18-25%, and the hardness is 35-40 HRC.
Description
Technical Field
The invention belongs to the technical field of steel materials, and particularly relates to a high-strength wear-resistant hot-rolled steel plate for automobile braking and a production process thereof.
Background
The existing metal materials for producing automobile brakes are usually cast iron, martensitic stainless steel, microalloyed steel and the like, and the preparation method comprises powder metallurgy, continuous casting, smelting forging and the like.
The metal material for automobile braking is an important part of an automobile braking system and also an easily-worn part of an automobile, and is directly related to driving safety. The working environment and the processing technology of the metal material for automobile braking require that the steel base has good hardenability, wear resistance, higher strength and the like, and particularly require that the steel base still has the hardness of 14-18 HRC after being sintered at the temperature of 600-800 ℃. In addition, the metal material for automobile braking has high requirements on the thickness precision and the surface of the steel strip, the thickness precision requirement reaches +/-0.03 mm, and the surface roughness requirement is less than 0.3 um. To meet this requirement, steel base materials for metal materials for automobile brakes at present generally employ cold rolled 40Mn, 50Mn or 65Mn steel strips. Although the cold-rolled steel strip can meet the requirements of the friction plate on thickness precision and surface, the cost of the cold-rolled steel strip is higher. Based on the above, there is a need for a material that meets the requirements of the existing processing technology and has a low cost. At present, hot-rolled 65Mn materials are also used for replacing cold-rolled materials, but the strength and the hardness cannot meet the requirements of consumers and the requirements of the existing process. The invention is studied in order to meet the requirements of long service life, high strength and good wear resistance.
Disclosure of Invention
The invention aims to provide a hot rolled steel plate for automobile braking, which has long service life, high strength and good wear resistance, and a production process thereof. In order to achieve the above objects, the present invention requires controlling the composition of the steel sheet on the one hand and controlling the production process of the steel sheet on the other hand.
The technical scheme is as follows:
a high-strength wear-resistant hot rolled steel plate for automobile braking comprises the following components in percentage by weight: c: 0.35-0.4%, Si: 0.5-0.6%, Mn: 1.50-1.80%, Cr: 1-6%, Ni: 1.0-1.2%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003% of Fe and the balance of inevitable impurities.
A high-strength wear-resistant hot rolled steel plate for automobile braking comprises the following components in percentage by weight: c: 0.35-0.4%, Si: 0.5-0.6%, Mn: 1.50-1.80%, Cr: 5-6%, Ni: 1.0-1.2%, Al: 0.5-1.0%, Cu: 0.5-0.6%, Mo: 0.3-0.4%, Co: 0.15-0.25%, W: 0.15-0.25%, Nb: 0.03 to 0.04%, Ti: 0.02 to 0.03%, Ta: 0.05-0.1%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003% of Fe and inevitable impurities in balance, smelting, refining, continuous casting, rough rolling, finish rolling and heat treatment, wherein the microstructure grain size of the steel plate for automobile braking after heat treatment is 20-25 μm, the average grain size of carbides is 30-50nm, a Cu-rich phase is precipitated, the structure comprises 40-50% of tempering sorbite, 30-35% of martensite and the balance of austenite and bainite by volume percentage; the yield strength is 1000-1100MPa, the tensile strength is 1200-1350MPa, the elongation is 18-25%, and the hardness is 35-40 HRC.
Further: a high-strength wear-resistant hot rolled steel plate for automobile braking comprises the following components in percentage by weight: c: 0.35%, Si: 0.5%, Mn: 1.50%, Cr: 5%, Ni: 1.0%, Al: 0.5%, Cu: 0.5%, Mo: 0.3%, Co: 0.15%, W: 0.15%, Nb: 0.03%, Ti: 0.02%, Ta: 0.05%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002%, B: 0.001%, and the balance of Fe and inevitable impurities.
Further: a high-strength wear-resistant hot rolled steel plate for automobile braking comprises the following components in percentage by weight: c: 0.4%, Si0.6%, Mn: 1.80%, Cr: 6%, Ni: 1.2%, Al: 1.0%, Cu: 0.6%, Mo: 0.4%, Co: 0.25%, W: 0.25%, Nb: 0.04%, Ti: 0.03%, Ta: 0.1%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.0035%, B: 0.003% and the balance of Fe and inevitable impurities.
The production process of the high-strength wear-resistant hot rolled steel plate for automobile braking is characterized by comprising the following steps of: the process route comprises the following steps: smelting, refining, continuous casting, rough rolling, finish rolling and heat treatment; the method comprises the following specific steps: (1) smelting: KR molten iron is pretreated to remove S, the S in the molten iron is controlled to be less than or equal to 0.005 percent, then smelting is carried out in a top-bottom combined blown converter, the mass ratio of the molten iron to the scrap steel is 6-8: 1, the scrap steel is added firstly, then the molten iron is added, and the end point alkalinity of the converter is 3.5-3.8; the tapping temperature is 1580-1600 ℃; carrying out double slag-blocking tapping by adopting a slag-blocking plug and a slag-blocking rod;
(2) refining: firstly, adding aluminum wires, fluorite and lime, and controlling the flow of bottom blowing argon to stop electrifying after the slag is completely white; stirring vigorously for desulfurization, controlling the flow of bottom blowing argon at 600-700L/min, stirring for 10-15min under the condition, then controlling the flow of bottom blowing argon at 80-100L/min, stirring for 8-10min under the condition, electrifying again to adjust the temperature of the molten pool so as to facilitate steel tapping, stopping argon blowing by soft blowing, and finishing LF refining; then RH refining is carried out: vacuumizing under the condition of not blowing oxygen for natural decarburization, increasing the Ar flow rate to 800 plus 850NL/min, performing molten steel dehydrogenation, ensuring that the deep vacuum treatment time is more than or equal to 12min, adding 0.01-0.03kg/t of aluminum-manganese composite deoxidizer to remove redundant oxygen in the molten steel, alloying the molten steel, performing soft blowing on the molten steel before ladle lifting, controlling the flow rate of the soft argon blowing to be 50-60L/min, not blowing off the slag surface, and ensuring the soft blowing time of the molten steel to be 12-13 min; standing for 5-6min after soft blowing;
(3) the continuous casting process comprises the following steps: argon blowing protection is carried out in the whole process, molten steel oxidation is avoided, and nitrogen increase in the continuous casting process is controlled; the tundish covering agent is adopted to avoid the exposure of the molten steel, and the secondary cooling water selects the low-carbon alloy covering slag according to the low-carbon alloy steel water distribution mode; the continuous casting secondary cooling area adopts the functions of electromagnetic stirring and heavy reduction, the electromagnetic stirring current is 300-320A, the frequency is 8-15Hz, and the heavy reduction amount is 30-35 mm; the superheat degree of the tundish is 15-25 ℃, and the thickness of the casting blank discharged out of the crystallizer is 100-200 mm;
(4) heating and rolling; the billet is put into a heating furnace, the heating temperature is 1180-; the rolling start temperature of finish rolling is 920-930 ℃, the finishing temperature is 830-850 ℃, the accumulated reduction rate is 70-80%, and the finish rolling is carried out for 6-7 passes to form high-density dislocation in the rolling process;
(5) heat treatment; firstly heating the rolled steel plate to 1050 ℃ plus material temperature, preserving heat for 40-80min, then cooling to 500 ℃ plus material temperature of 400 ℃ at the speed of 2-5 ℃/s, then heating to 950 ℃ plus material temperature of 940 ℃, preserving heat for 40-80min, then cooling to 300 ℃ plus material temperature of 200 ℃ plus material temperature at the speed of 60-80 ℃/s for quenching, then heating to 610 ℃ plus material temperature again, preserving heat for 40-80min, then air cooling to room temperature, and then flattening and packaging.
Further: step (4), heating and rolling; feeding the steel billet into a heating furnace, heating at 1180 ℃ for 105min, removing scale from the steel billet by high-pressure water after the steel billet is taken out of the heating furnace, wherein the pressure is 20MPa, the initial rolling temperature of rough rolling is 1060 ℃, the single-pass reduction rate is 20%, the final-pass reduction rate is 30%, and the rough rolling is carried out for 5 passes, and then recrystallization and austenite grain refinement are carried out; the initial rolling temperature of finish rolling is 920 ℃, the final rolling temperature is 840 ℃, the accumulated reduction rate is 75%, the finish rolling is carried out for 6 passes, and high-density dislocation is formed in the rolling process.
Further: step (4), heating and rolling; the method comprises the following steps of putting a billet into a heating furnace, heating at 1180 ℃ for 105min, removing scale from the billet after the billet is taken out of the heating furnace by high-pressure water, controlling the pressure to be 20MPa, the initial rolling temperature of rough rolling to be 1060 ℃, the single-pass reduction rate to be 20% and the final-pass reduction rate to be 30%, carrying out rough rolling for 5 passes, and carrying out recrystallization and austenite grain refinement on the billet, wherein the rolling speed distribution of each pass is 2.2m/s, 2.0m/s, 1.8m/s, 1.6m/s and 1.6 m/s; the initial rolling temperature of the finish rolling is 920 ℃, the final rolling temperature is 840 ℃, the cumulative reduction rate is 75%, the finish rolling is carried out for 6 passes, the rolling speed distribution of each pass is 1.8m/s, 1.7m/s, 1.6m/s and 1.6m/s, and high-density dislocation is formed in the rolling process. The rolling speed in the high-reduction rolling process has an important influence on the structure and the performance of the core of the steel plate, and the lower the rolling speed in the rough rolling process, the more complete the recovery and recrystallization, and the finer the grains of the core of the steel plate. The structural uniformity of a test steel plate with high rolling speed (2.0m/s) in the thickness direction is poor, while the structural uniformity of a steel plate with low rolling speed (1.7m/s) is good because the rolling force permeates into the center part in the deformation process, and if the speed is too low, the continuous rolling production process cannot be ensured, and at the moment, the corresponding technical effect is also saturated. Therefore, the invention adopts the process that the rolling speed is gradually reduced.
Further: step (5) heat treatment; firstly, heating the rolled steel plate to 1030 ℃, preserving heat for 60min, then cooling to 450 ℃ at the speed of 5 ℃/s, then heating to 940 ℃ again, preserving heat for 60min, then cooling to 240 ℃ at the speed of 80 ℃/s for quenching, then heating to 600 ℃, preserving heat for 60min, then air-cooling to room temperature, and then flattening and packaging.
The casting process of the invention recommends a continuous casting process, and the continuous casting process focuses on controlling the casting temperature so as to refine the original cast structure. In order to control the Mn segregation at the center of the continuous casting billet, an electromagnetic stirring process is adopted, specifically, the continuous casting secondary cooling zone adopts the functions of electromagnetic stirring and heavy reduction, the electromagnetic stirring current is 300-320A, the frequency is 8-15Hz, and the heavy reduction is 30-35 mm; the superheat degree of the tundish is 15-25 ℃, and the thickness of the casting blank discharged out of the crystallizer is 100-200 mm.
Next, the reason for limiting the chemical components of the present invention will be described. Here, the% of the component means mass%.
The element C is necessary for obtaining high strength and hardness. The high C content is advantageous for the strength, hardness, etc. of the steel, but is extremely disadvantageous for the plasticity and toughness of the steel, and decreases the yield ratio, increases the decarburization sensitivity, and deteriorates the fatigue resistance, workability, and high-temperature plasticity of the steel. Therefore, the C content in the steel is properly reduced and controlled to be less than 0.4%. However, in order to obtain a desired high strength after quenching and high-temperature tempering, the C content should be 0.35% or more, and thus the C content is preferably controlled to 0.35 to 0.4%.
Si is a main deoxidizing element in steel and has strong solid solution strengthening effect, but the plasticity and toughness of the steel are reduced due to the excessively high content of Si, the activity of C is increased, the decarburization and graphitization tendency of the steel in the rolling and heat treatment processes is promoted, smelting is difficult, inclusions are easy to form, and the fatigue resistance of the steel is deteriorated. Therefore, the Si content is controlled to be 0.5-0.6%.
Mn is an effective element for deoxidation and desulfurization, and can also improve the hardenability and strength of the steel. However, when the quenched steel is tempered, Mn and P have strong tendency of grain boundary co-segregation, the tempering brittleness is promoted, the toughness of the steel is deteriorated, and excessively high Mn content easily causes austenite-martensite transformation in the repeated heating and cooling process, causes the thermal expansion coefficient and the thermal conductivity coefficient to be changed rapidly, and reduces the cold and hot fatigue performance of a brake disc, so that the Mn content is controlled to be 1.50-1.80%.
Cr can effectively improve the hardenability and the tempering resistance of the steel so as to obtain the required high strength; meanwhile, Cr can also reduce the activity of C, can reduce the decarburization tendency of the surface of steel in the heating, rolling and heat treatment processes, and is beneficial to obtaining high fatigue resistance and good high-temperature performance and obtaining a specific amount of martensite. However, too high content deteriorates the toughness of the steel, so that the Cr content is controlled to 5-6%.
Ni can improve the hardenability and corrosion resistance of the steel and ensure the toughness of the steel at low temperature. While Ni delays precipitation of Cr carbonitride at high temperature and maintains hardness of a martensite structure supersaturated with solid-solution C, too high Ni content tends to cause austenite-martensite transformation during repeated heating and cooling, thereby causing rapid change in thermal expansion coefficient and lowering cold and hot fatigue properties of the brake disc, so Ni content is 1.0 to 1.2%.
Al is an element added to steel for deoxidation. After the deoxidation is completed, Al reduces the O content in the steel sheet to improve the aging properties of the steel sheet. In addition, the addition of a proper amount of Al is beneficial to refining grains, so that the toughness of the steel is improved. The Al content is adjusted to be far higher than the Al content (generally less than or equal to 0.1%) of a common hot rolled steel plate for automobile braking, and the Al is used for increasing the high-temperature strength of the steel and improving the high-temperature fatigue property by solid solution strengthening mainly considering the specific application of the hot rolled steel plate for automobile braking. Therefore, Al: 0.5 to 1.0 percent.
Cu realizes precipitation strengthening through precipitation of a Cu-rich phase, the strength of steel is improved, in addition, a proper amount of Cu element is added, the atmospheric corrosion resistance of the steel can be improved, but Cu is an element for enlarging a gamma phase region, the austenite-martensite transformation is easily generated in the repeated heating and cooling process of a braking material due to higher content, the thermal expansion coefficient is changed rapidly, and the cold and hot fatigue performance of a brake disc is reduced, so the Cu content is controlled to be 0.5-0.6%.
The function of Mo in steel is mainly to improve hardenability, improve tempering resistance and prevent tempering brittleness. In addition, the reasonable matching of the Mo element and the Cr element can obviously improve the hardenability and the tempering resistance, the effect is limited when the Mo content is too low, the effect is saturated when the Mo content is too high, and the cost of the steel is increased. Therefore, the Mo content is controlled to be 0.3 to 0.4%.
Co and W are replaced by elements in crystal lattices, so that the temperature of a friction surface is continuously increased when an automobile is in a continuous long braking stroke, and the oxidation of the friction surface needs to be inhibited; w is a strong carbide forming element, improves the high-temperature strength and the heat resistance of steel, and comprehensively considers the cost factor, namely, Co: 0.15-0.25%, W: 0.15-0.25%.
Trace Nb element is added into steel for the purpose of carrying out non-recrystallization controlled rolling, and when the addition amount of Nb is less than 0.03 percent, the effective controlled rolling effect cannot be exerted; when the addition amount of Nb exceeds 0.04%, toughness is seriously deteriorated, and Nb is an expensive metal element, and the addition of a large amount of Nb increases the production cost. Therefore, the Nb content is controlled between 0.03 and 0.04 percent, the best rolling control effect is obtained, and simultaneously the toughness is not damaged.
The purpose of adding a trace amount of Ti in the steel is to combine with N in the steel to generate TiN particles with high stability, inhibit the growth of crystal grains and improve the toughness of the steel. The content of Ti added in the steel is matched with the content of N in the steel, and the matching principle is that TiN cannot be precipitated in liquid molten steel and must be precipitated in a solid phase; therefore, the precipitation temperature of TiN must be ensured to be lower than 1400 ℃, and when the content of added Ti is too low, the quantity of formed TiN particles is insufficient, and the growth of crystal grains is not inhibited and the toughness is not improved; when the content of Ti is excessive, the precipitation temperature of TiN exceeds 1400 ℃, large-size TiN particles can be precipitated in the solidification stage of molten steel in a crystallizer, and the large-size TiN particles can not inhibit the growth of crystal grains and instead become the starting point of crack initiation; therefore, the optimal control range of the Ti content is 0.02 to 0.03 percent
Ta is an element for improving the heat resistance of the steel sheet. To obtain this effect, 0.05% or more should be contained, but if these elements forming carbonitrides or the like are contained excessively, the carbonitrides or the like are significantly hardened or softened, which causes the hardness of the steel sheet after quenching and tempering to deviate from the appropriate range. Thus, Ta: 0.05-0.1 percent.
P is used as harmful impurities in steel and has mechanical performance on steel, and the content of P is controlled to be less than or equal to 0.010%.
S has great damage effect on the performance of steel as harmful impurities in the steel, and the content of S needs to be controlled to be less than or equal to 0.002 percent.
The control range of N corresponds to that of Ti, the content of N is too low, the quantity of generated TiN particles is small, the size is large, and the grain refinement of steel cannot be improved; however, if the N content is too high, the free [ N ] in the steel increases, and the toughness is impaired. Thus N: 0.002-0.0035%.
B strongly suppresses the formation of pro-eutectoid ferrite and promotes the formation of low-temperature transformation structures such as bainite, so solid solution B is important for obtaining low-temperature transformation structures such as bainite to improve the strength of the steel sheet. B can also improve toughness, so B: 0.001-0.003%.
Compared with the prior art, the invention has the technical effects that:
1. the invention ensures the uniformity of the mechanical property of the tissue plate blank by accurately controlling the components and the production process of the product, and lists the rolling pass reduction system and the rolling speed. The high-strength wear-resistant steel has high strength, high toughness, wear resistance, high hardness, good oxidation resistance and long service life.
2. According to the invention, by accurately controlling the alloy elements, the improvement of replacing the alloy with increased amount is avoided, the process cost is saved, and the production efficiency is improved.
3. The steel plate for automobile braking has the advantages that through reasonable chemical component design, a controlled rolling and controlled cooling process and a heat treatment process are adopted, the sizes of microstructure grains of the steel plate for automobile braking after heat treatment are all 20-25 mu m, the average grain size of carbides is 30-50nm, a Cu-rich phase is separated out, tempered sorbite accounts for 40-50% in the structure, martensite accounts for 30-35% in the structure, and the balance is austenite and bainite; the yield strength is 1000-1100MPa, the tensile strength is 1200-1350MPa, the elongation is 18-25%, and the hardness is 35-40 HRC.
Detailed Description
The technical solution of the present invention will be described in detail with reference to exemplary embodiments. Example embodiments may, however, be embodied in many different forms and should not be construed as limited to the embodiments set forth herein; rather, these embodiments are provided so that this disclosure will be thorough and complete, and will fully convey the concept of example embodiments to those skilled in the art.
Example 1
A high-strength wear-resistant hot rolled steel plate for automobile braking comprises the following components in percentage by weight: c: 0.35-0.4%, Si: 0.5-0.6%, Mn: 1.50-1.80%, Cr: 5-6%, Ni: 1.0-1.2%, Al: 0.5-1.0%, Cu: 0.5-0.6%, Mo: 0.3-0.4%, Co: 0.15-0.25%, W: 0.15-0.25%, Nb: 0.03 to 0.04%, Ti: 0.02 to 0.03%, Ta: 0.05-0.1%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003% of Fe and the balance of inevitable impurities, and comprises the following steps: (1) smelting: KR molten iron is pretreated to remove S, the S in the molten iron is controlled to be less than or equal to 0.005 percent, then smelting is carried out in a top-bottom combined blown converter, the mass ratio of the molten iron to the scrap steel is 6-8: 1, the scrap steel is added firstly, then the molten iron is added, and the end point alkalinity of the converter is 3.5-3.8; the tapping temperature is 1580-1600 ℃; carrying out double slag-blocking tapping by adopting a slag-blocking plug and a slag-blocking rod;
(2) refining: firstly, adding aluminum wires, fluorite and lime, and controlling the flow of bottom blowing argon to stop electrifying after the slag is completely white; stirring vigorously for desulfurization, controlling the flow of bottom blowing argon at 600-700L/min, stirring for 10-15min under the condition, then controlling the flow of bottom blowing argon at 80-100L/min, stirring for 8-10min under the condition, electrifying again to adjust the temperature of the molten pool so as to facilitate steel tapping, stopping argon blowing by soft blowing, and finishing LF refining; then RH refining is carried out: vacuumizing under the condition of not blowing oxygen for natural decarburization, increasing the Ar flow rate to 800 plus 850NL/min, performing molten steel dehydrogenation, ensuring that the deep vacuum treatment time is more than or equal to 12min, adding 0.01-0.03kg/t of aluminum-manganese composite deoxidizer to remove redundant oxygen in the molten steel, alloying the molten steel, performing soft blowing on the molten steel before ladle lifting, controlling the flow rate of the soft argon blowing to be 50-60L/min, not blowing off the slag surface, and ensuring the soft blowing time of the molten steel to be 12-13 min; standing for 5-6min after soft blowing;
(3) the continuous casting process comprises the following steps: argon blowing protection is carried out in the whole process, molten steel oxidation is avoided, and nitrogen increase in the continuous casting process is controlled; the tundish covering agent is adopted to avoid the exposure of the molten steel, and the secondary cooling water selects the low-carbon alloy covering slag according to the low-carbon alloy steel water distribution mode; the continuous casting secondary cooling area adopts the functions of electromagnetic stirring and heavy reduction, the electromagnetic stirring current is 300-320A, the frequency is 8-15Hz, and the heavy reduction amount is 30-35 mm; the superheat degree of the tundish is 15-25 ℃, and the thickness of the casting blank discharged out of the crystallizer is 100-200 mm;
(4) heating and rolling; the billet is put into a heating furnace, the heating temperature is 1180-; the rolling start temperature of finish rolling is 920-930 ℃, the finishing temperature is 830-850 ℃, the accumulated reduction rate is 70-80%, and the finish rolling is carried out for 6-7 passes to form high-density dislocation in the rolling process;
(5) heat treatment; firstly heating the rolled steel plate to 1050 ℃ plus material temperature, preserving heat for 40-80min, then cooling to 500 ℃ plus material temperature of 400 ℃ at the speed of 2-5 ℃/s, then heating to 950 ℃ plus material temperature of 940 ℃, preserving heat for 40-80min, then cooling to 300 ℃ plus material temperature of 200 ℃ plus material temperature at the speed of 60-80 ℃/s for quenching, then heating to 610 ℃ plus material temperature again, preserving heat for 40-80min, then air cooling to room temperature, and then flattening and packaging.
After smelting, refining, continuous casting, rough rolling, finish rolling and heat treatment, the grain size of the microstructure of the steel plate for automobile braking is 20-25 mu m after heat treatment, the average grain size of carbide is 30-50nm, a Cu-rich phase is precipitated, the volume percentage of tempered sorbite in the microstructure is 40-50%, the volume percentage of martensite is 30-35%, and the balance of austenite and bainite; the yield strength is 1000-1100MPa, the tensile strength is 1200-1350MPa, the elongation is 18-25%, and the hardness is 35-40 HRC.
Comparative example 1
A high-strength wear-resistant hot rolled steel plate for automobile braking comprises the following components in percentage by weight: c: 0.3%, Si: 0.4%, Mn: 1.1%, Cr: 5-6%, Ni: 1.0-1.2%, Al: 0.5-1.0%, Cu: 0.5-0.6%, Mo: 0.3-0.4%, Co: 0.15-0.25%, W: 0.15-0.25%, Nb: 0.03 to 0.04%, Ti: 0.02 to 0.03%, Ta: 0.05-0.1%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003%, and the balance of Fe and inevitable impurities,
the preparation method is consistent with example 1; the final product has yield strength of 800-900MPa, tensile strength of 900-1000MPa, elongation of 12-15% and hardness of 20-30 HRC.
Comparative example 2
A high-strength wear-resistant hot rolled steel plate for automobile braking comprises the following components in percentage by weight: c: 0.35-0.4%, Si: 0.5-0.6%, Mn: 1.50-1.80%, Cr: 0.1-1%, Ni: 0.5-0.8%, Al: 0.05-0.2%, Cu: 0.5-0.6%, Mo: 0.3-0.4%, Co: 0.15-0.25%, W: 0.15-0.25%, Nb: 0.03 to 0.04%, Ti: 0.02 to 0.03%, Ta: 0.05-0.1%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003%, and the balance of Fe and inevitable impurities,
the preparation process was identical to example 1.
The preparation method is consistent with example 1; the final product has yield strength of 850-950MPa, tensile strength of 950-1030MPa, elongation of 13-18% and hardness of 20-30 HRC.
Comparative example 3
A high-strength wear-resistant hot rolled steel plate for automobile braking comprises the following components in percentage by weight: c: 0.35-0.4%, Si: 0.5-0.6%, Mn: 1.50-1.80%, Cr: 5-6%, Ni: 1.0-1.2%, Al: 0.5-1.0%, Cu: 0.5-0.6%, Mo: 0.1-0.2%, Nb: 0.03 to 0.04%, Ti: 0.02 to 0.03%, Ta: 0.05-0.1%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003%, and the balance of Fe and inevitable impurities,
the preparation method is consistent with example 1; the final product has yield strength of 870-970MPa, tensile strength of 950-105MPa, elongation of 13-20% and hardness of 20-30 HRC.
Comparative example 4
A high-strength wear-resistant hot rolled steel plate for automobile braking comprises the following components in percentage by weight: c: 0.35-0.4%, Si: 0.5-0.6%, Mn: 1.50-1.80%, Cr: 5-6%, Ni: 1.0-1.2%, Al: 0.5-1.0%, Cu: 0.5-0.6%, Mo: 0.3-0.4%, Co: 0.15-0.25%, W: 0.15-0.25%, Nb: 0.03 to 0.04%, Ti: 0.02 to 0.03%, Ta: 0.05-0.1%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003%, and the balance of Fe and inevitable impurities,
preparation steps (1) - (3) are consistent with example 1;
(4) heating and rolling; the method comprises the following steps of putting a steel billet into a heating furnace, heating at 1180-1185 ℃ for 100-110min, removing scale from the heating furnace by high-pressure water, wherein the pressure is 20-25MPa, the initial rolling temperature of rough rolling is 1050-1060 ℃, the reduction rate of a single pass is 12%, the reduction rate of a last pass is 20%, and the rough rolling is carried out for 4-5 passes, and then recrystallization is carried out to refine austenite grains; the initial rolling temperature of finish rolling is 900 ℃, the final rolling temperature is 800 ℃, the accumulated reduction rate is 70-80%, the finish rolling is carried out for 6 passes, and high-density dislocation is formed in the rolling process;
(5) heat treatment; firstly heating the rolled steel plate to 940-.
The final product has yield strength of 880-1000MPa, tensile strength of 1000-1100MPa, elongation of 15-20% and hardness of 205-30 HRC.
The terminology used herein is for the purpose of description and illustration, rather than of limitation. As the present invention may be embodied in several forms without departing from the spirit or essential characteristics thereof, it should also be understood that the above-described embodiments are not limited by any of the details of the foregoing description, but rather should be construed broadly within its spirit and scope as defined in the appended claims, and therefore all changes and modifications that fall within the meets and bounds of the claims, or equivalences of such meets and bounds are therefore intended to be embraced by the appended claims.
Claims (5)
1. A high-strength wear-resistant hot rolled steel plate for automobile braking comprises the following components in percentage by weight: c: 0.35-0.4%, Si: 0.5-0.6%, Mn: 1.50-1.80%, Cr: 5-6%, Ni: 1.0-1.2%, Al: 0.5-1.0%, Cu: 0.5-0.6%, Mo: 0.3-0.4%, Co: 0.15-0.25%, W: 0.15-0.25%, Nb: 0.03 to 0.04%, Ti: 0.02 to 0.03%, Ta: 0.05-0.1%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003% of Fe and inevitable impurities in balance, smelting, refining, continuous casting, rough rolling, finish rolling and heat treatment, wherein the microstructure grain size of the steel plate for automobile braking after heat treatment is 20-25 μm, the average grain size of carbides is 30-50nm, a Cu-rich phase is precipitated, the structure comprises 40-50% of tempering sorbite, 30-35% of martensite and the balance of austenite and bainite by volume percentage; the yield strength is 1000-1100MPa, the tensile strength is 1200-1350MPa, the elongation is 18-25%, and the hardness is 35-40 HRC;
the production process of the high-strength wear-resistant hot rolled steel plate for automobile braking comprises the following specific steps: (1) smelting: KR molten iron is pretreated to remove S, the S in the molten iron is controlled to be less than or equal to 0.005 percent, then smelting is carried out in a top-bottom combined blown converter, the mass ratio of the molten iron to the scrap steel is 6-8: 1, the scrap steel is added firstly, then the molten iron is added, and the end point alkalinity of the converter is 3.5-3.8; the tapping temperature is 1580-1600 ℃; carrying out double slag-blocking tapping by adopting a slag-blocking plug and a slag-blocking rod;
(2) refining: firstly, adding aluminum wires, fluorite and lime, and controlling the flow of bottom blowing argon to stop electrifying after the slag is completely white; stirring vigorously for desulfurization, controlling the flow of bottom blowing argon at 600-700L/min, stirring for 10-15min under the condition, then controlling the flow of bottom blowing argon at 80-100L/min, stirring for 8-10min under the condition, electrifying again to adjust the temperature of the molten pool so as to facilitate steel tapping, stopping argon blowing by soft blowing, and finishing LF refining; then RH refining is carried out: vacuumizing under the condition of not blowing oxygen for natural decarburization, increasing the Ar flow rate to 800 plus 850NL/min, performing molten steel dehydrogenation, ensuring that the deep vacuum treatment time is more than or equal to 12min, adding 0.01-0.03kg/t of aluminum-manganese composite deoxidizer to remove redundant oxygen in the molten steel, alloying the molten steel, performing soft blowing on the molten steel before ladle lifting, controlling the flow rate of the soft argon blowing to be 50-60L/min, not blowing off the slag surface, and ensuring the soft blowing time of the molten steel to be 12-13 min; standing for 5-6min after soft blowing;
(3) the continuous casting process comprises the following steps: argon blowing protection is carried out in the whole process, molten steel oxidation is avoided, and nitrogen increase in the continuous casting process is controlled; the tundish covering agent is adopted to avoid the exposure of the molten steel, and the secondary cooling water selects the low-carbon alloy covering slag according to the low-carbon alloy steel water distribution mode; the continuous casting secondary cooling area adopts the functions of electromagnetic stirring and heavy reduction, the electromagnetic stirring current is 300-320A, the frequency is 8-15Hz, and the heavy reduction amount is 30-35 mm; the superheat degree of the tundish is 15-25 ℃, and the thickness of the casting blank discharged out of the crystallizer is 100-200 mm;
(4) heating and rolling; the billet is put into a heating furnace, the heating temperature is 1180-; the rolling start temperature of finish rolling is 920-930 ℃, the finishing temperature is 830-850 ℃, the accumulated reduction rate is 70-80%, and the finish rolling is carried out for 6-7 passes to form high-density dislocation in the rolling process;
(5) heat treatment; firstly heating the rolled steel plate to 1050 ℃ of-.
2. A production process of the high-strength wear-resistant hot rolled steel plate for automobile braking as claimed in claim 1, comprises the following specific steps: (1) smelting: KR molten iron is pretreated to remove S, the S in the molten iron is controlled to be less than or equal to 0.005 percent, then smelting is carried out in a top-bottom combined blown converter, the mass ratio of the molten iron to the scrap steel is 6-8: 1, the scrap steel is added firstly, then the molten iron is added, and the end point alkalinity of the converter is 3.5-3.8; the tapping temperature is 1580-1600 ℃; carrying out double slag-blocking tapping by adopting a slag-blocking plug and a slag-blocking rod;
(2) refining: firstly, adding aluminum wires, fluorite and lime, and controlling the flow of bottom blowing argon to stop electrifying after the slag is completely white; stirring vigorously for desulfurization, controlling the flow of bottom blowing argon at 600-700L/min, stirring for 10-15min under the condition, then controlling the flow of bottom blowing argon at 80-100L/min, stirring for 8-10min under the condition, electrifying again to adjust the temperature of the molten pool so as to facilitate steel tapping, stopping argon blowing by soft blowing, and finishing LF refining; then RH refining is carried out: vacuumizing under the condition of not blowing oxygen for natural decarburization, increasing the Ar flow rate to 800 plus 850NL/min, performing molten steel dehydrogenation, ensuring that the deep vacuum treatment time is more than or equal to 12min, adding 0.01-0.03kg/t of aluminum-manganese composite deoxidizer to remove redundant oxygen in the molten steel, alloying the molten steel, performing soft blowing on the molten steel before ladle lifting, controlling the flow rate of the soft argon blowing to be 50-60L/min, not blowing off the slag surface, and ensuring the soft blowing time of the molten steel to be 12-13 min; standing for 5-6min after soft blowing;
(3) the continuous casting process comprises the following steps: argon blowing protection is carried out in the whole process, molten steel oxidation is avoided, and nitrogen increase in the continuous casting process is controlled; the tundish covering agent is adopted to avoid the exposure of the molten steel, and the secondary cooling water selects the low-carbon alloy covering slag according to the low-carbon alloy steel water distribution mode; the continuous casting secondary cooling area adopts the functions of electromagnetic stirring and heavy reduction, the electromagnetic stirring current is 300-320A, the frequency is 8-15Hz, and the heavy reduction amount is 30-35 mm; the superheat degree of the tundish is 15-25 ℃, and the thickness of the casting blank discharged out of the crystallizer is 100-200 mm;
(4) heating and rolling; the billet is put into a heating furnace, the heating temperature is 1180-; the rolling start temperature of finish rolling is 920-930 ℃, the finishing temperature is 830-850 ℃, the accumulated reduction rate is 70-80%, and the finish rolling is carried out for 6-7 passes to form high-density dislocation in the rolling process;
(5) heat treatment; firstly heating the rolled steel plate to 1050 ℃ of-.
3. The process for producing a high-strength, wear-resistant, hot-rolled steel sheet for automobile braking as claimed in claim 2, wherein: step (4), heating and rolling; feeding the steel billet into a heating furnace, heating at 1180 ℃ for 105min, removing scale from the steel billet by high-pressure water after the steel billet is taken out of the heating furnace, wherein the pressure is 20MPa, the initial rolling temperature of rough rolling is 1060 ℃, the single-pass reduction rate is 20%, the final-pass reduction rate is 30%, and the rough rolling is carried out for 5 passes, and then recrystallization and austenite grain refinement are carried out; the initial rolling temperature of finish rolling is 920 ℃, the final rolling temperature is 840 ℃, the accumulated reduction rate is 75%, the finish rolling is carried out for 6 passes, and high-density dislocation is formed in the rolling process.
4. The process for producing a high-strength, wear-resistant, hot-rolled steel sheet for automobile braking as claimed in claim 2, wherein: step (4), heating and rolling; the method comprises the following steps of putting a billet into a heating furnace, heating at 1180 ℃ for 105min, removing scale from the billet after the billet is taken out of the heating furnace by high-pressure water, controlling the pressure to be 20MPa, the initial rolling temperature of rough rolling to be 1060 ℃, the single-pass reduction rate to be 20% and the final-pass reduction rate to be 30%, carrying out rough rolling for 5 passes, and carrying out recrystallization and austenite grain refinement on the billet, wherein the rolling speed distribution of each pass is 2.2m/s, 2.0m/s, 1.8m/s, 1.6m/s and 1.6 m/s; the initial rolling temperature of the finish rolling is 920 ℃, the final rolling temperature is 840 ℃, the cumulative reduction rate is 75%, the finish rolling is carried out for 6 passes, the rolling speed distribution of each pass is 1.8m/s, 1.7m/s, 1.6m/s and 1.6m/s, and high-density dislocation is formed in the rolling process.
5. The process for producing a high-strength, wear-resistant, hot-rolled steel sheet for automobile braking as claimed in claim 2, wherein: step (5) heat treatment; firstly, heating the rolled steel plate to 1030 ℃, preserving heat for 60min, then cooling to 450 ℃ at the speed of 5 ℃/s, then heating to 940 ℃ again, preserving heat for 60min, then cooling to 240 ℃ at the speed of 80 ℃/s for quenching, then heating to 600 ℃, preserving heat for 60min, then air-cooling to room temperature, and then flattening and packaging.
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