CN111057964A - Steel for high-strength steering knuckle of new energy automobile and preparation method and application of steel - Google Patents
Steel for high-strength steering knuckle of new energy automobile and preparation method and application of steel Download PDFInfo
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- CN111057964A CN111057964A CN201911386181.5A CN201911386181A CN111057964A CN 111057964 A CN111057964 A CN 111057964A CN 201911386181 A CN201911386181 A CN 201911386181A CN 111057964 A CN111057964 A CN 111057964A
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Images
Classifications
-
- 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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B62—LAND VEHICLES FOR TRAVELLING OTHERWISE THAN ON RAILS
- B62D—MOTOR VEHICLES; TRAILERS
- B62D7/00—Steering linkage; Stub axles or their mountings
- B62D7/18—Steering knuckles; King pins
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C5/00—Manufacture of carbon-steel, e.g. plain mild steel, medium carbon steel or cast steel or stainless steel
- C21C5/52—Manufacture of steel in electric furnaces
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/10—Handling in a vacuum
-
- 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
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- 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
-
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
-
- 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
-
- 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
-
- 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
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- 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
-
- 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
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
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Abstract
The invention relates to a steel for a high-strength steering knuckle of a new energy automobile, and a preparation method and application thereof, wherein the steel comprises the following components in parts by weight: 0.40-0.44%, Si: 0.31-0.37%, Mn: 0.50-0.59%, P: less than or equal to 0.015%, S: 0.031-0.037%, Cr: 0.90-0.99%, Ni: less than or equal to 0.25%, Cu: less than or equal to 0.15 percent, Mo: less than or equal to 0.10 percent, Al: 0.017-0.033%, Ti: 0.003-0.02%, N: 0.008-0.014%, wherein Al% is more than or equal to 27N%/14-9 Ti%/16; the preparation method comprises the steps of carrying out primary smelting on furnace burden by an electric arc furnace, refining by a steel ladle, vacuum degassing, continuous casting and pouring, and carrying out hot processing and rolling in sequence to obtain the finished product steel. Compared with the prior art, the invention has the advantages of wide sources of steel components, low cost, stable and reliable process control and the like.
Description
Technical Field
The invention belongs to the technical field of alloy steel, and relates to a steel for a high-strength steering knuckle of a new energy automobile, and a preparation method and application thereof.
Background
The knuckle is one of important parts in an automobile and a steering system, and is required to bear bending force of up-and-down swinging of the automobile during running, reaction force of the ground, torsion force during steering and impact force during braking (particularly emergency braking) of the automobile, so that the knuckle has certain tensile strength and yield strength and higher plasticity and toughness. In the prior art, cast iron, aluminum alloy or steel materials are generally adopted, the strength of an iron casting is low, the application range is limited, the light weight effect of an aluminum alloy steering knuckle is obvious, but the cost is high, the strength is low, the steel materials are two types at present, one type is CrMo series quenched and tempered steel, the other type is microalloyed non quenched and tempered steel, both types need to be added with certain alloy elements to improve the obdurability of the steering knuckle, and the alloy cost is increased.
Chinese patent CN102886642A discloses a method for manufacturing a knuckle for an automobile, the prepared steel ingot comprises C: 0.37-0.44%, Si: 0.15-0.35%, Mn: 0.70-0.90%, P: 0.15-0.25%, S: 0.015 to 0.025%, Cr: 0.70-0.95%, Mo: 0.30-0.40%, Ni: 1.6-2%, Cu: 0.10-0.20%, the tensile strength Rm of a finished product is more than or equal to 830MPa, the yield strength Rp0.2 is more than or equal to 690MPa, the elongation A is more than or equal to 14%, and the section shrinkage Z is more than or equal to 30%.
Chinese patent CN110129656A discloses a method for producing steel for an automobile steering knuckle, the prepared steel comprises C: 0.37-0.39%, Si: 0.20-0.30%, Mn: 0.75-0.80%, P: less than or equal to 0.020%, S: less than or equal to 0.015 percent, Cr: 1.05-1.10%, Ni: less than or equal to 0.3 percent, Al: 0.0015-0.0040%, Cu + Ni + V + Sn: less than or equal to 0.80 percent, H: less than or equal to 0.0002 percent, O: less than or equal to 0.0020 percent, and the balance of Fe and inevitable impurities. The quenching and tempering hardness of the finished part is 30-36HRC, the grain size is 5-8 grades, the fatigue life is 50 ten thousand times without damage, the steel prepared by the patent is essentially coarse grain steel, the grain uniformity is poor, and the performance is unstable.
Chinese patent CN104087819B discloses an as-cast low-temperature tough ferrite ductile iron material for a car steering knuckle and a preparation method thereof, wherein the prepared ferrite ductile iron material comprises C: 3.1-3.4%, Si: 3.1-3.3%, Mn: 0.2-0.30%, P: < 0.040%, S: < 0.015%, Cu: < 0.1%, Sn: < 0.01%, Cr: < 0.1%, Mo: < 0.1%, Ni: < 0.1%, Mg: 0.03-0.05 percent, the balance of Fe and inevitable impurities, the tensile strength Rm is more than or equal to 480MPa, the yield strength Rp0.2 is more than or equal to 360MPa, the elongation A is more than or equal to 18 percent, the hardness is HBW165-200, the ferrite ductile iron material prepared by the patent has lower strength and is not suitable for a new energy automobile front steering knuckle with large bearing capacity, and the added low-melting-point element increases the difficulty of material preparation.
Chinese patent CN109097644a discloses a high strength aluminum alloy for automobile steering knuckle and a method for preparing the same, the prepared aluminum alloy includes Si: 0.45-0.75%, Cu: 0.15-0.35%, Mn: less than or equal to 0.05 percent, Mg: 0.90-1.10%, Zn: less than or equal to 0.20 percent, Ti: less than or equal to 0.10 percent, Cr: 0.04-0.35% and the balance of Al. The tensile strength Rm is more than or equal to 400MPa, the yield strength Rp0.2 is more than or equal to 358MPa, the elongation A is more than or equal to 13 percent, the hardness HBW is more than or equal to 115, and the strength is lower.
In conclusion, in the prior art, the steel material has high content of alloy elements, large and thick crystal grains, and unstable performance while increasing the cost; the ductile iron and the aluminum alloy have low mechanical properties, are not ideal in smelting difficulty or cost control, and cannot meet the performance requirements of new energy automobiles on the front steering knuckle.
Disclosure of Invention
The invention aims to overcome the defects in the prior art, provides a new energy automobile high-strength steel material for a steering knuckle, and a preparation method and application thereof, and is used for solving the problems of high difficulty, high cost and unstable performance of a finished product of the steel material for the steering knuckle.
The purpose of the invention can be realized by the following technical scheme:
the steel for the high-strength steering knuckle of the new energy automobile comprises the following components in percentage by weight:
c: 0.40-0.44%, Si: 0.31-0.37%, Mn: 0.50-0.59%, P: less than or equal to 0.015%, S: 0.031-0.037%, Cr: 0.90-0.99%, Ni: less than or equal to 0.25%, Cu: less than or equal to 0.15 percent, Mo: less than or equal to 0.10 percent, Al: 0.017-0.033%, Ti: 0.003-0.020%, N: 0.0080-0.0140%, the balance being Fe and inevitable impurities.
C is an element necessary for ensuring the use strength of the steering knuckle and is one of main elements influencing hardenability, the steering knuckle has poor strength and cannot ensure good hardenability, in addition, the steering knuckle needs high strength and also needs sufficient impact toughness, and the impact toughness of the steering knuckle is reduced easily to cause the steering knuckle not to meet the performance requirement if the C content is too high, so the C content is controlled to be 0.40-0.44 percent in the invention.
Si can well eliminate the adverse effect of iron oxide on steel, can be dissolved in ferrite, strengthens the ferrite and improves the strength, hardness, elasticity, elastic limit and wear resistance of the steering knuckle; in addition, the Ac3 temperature of the steel can be increased by Si, so that the tempering stability and the oxidation resistance of the steering knuckle are greatly influenced, but the thermal conductivity of Si is poor, the steel is easy to crack, and the decarburization tendency is serious. Therefore, the Si content is controlled to be 0.31-0.37% in the invention.
Mn is an effective element for deoxidation and desulfurization, is also one of main elements influencing hardenability, can play roles in deoxidation and desulfurization when being added in smelting, and can also be dissolved in ferrite to play a role in solid solution strengthening; when the Mn content is less than 0.50%, the deoxidation and desulfurization effects are small, after the Mn content is more than 0.59%, the hardenability and segregation of the steering knuckle are not well controlled, and meanwhile, the thermoplasticity is poor, so that the production is influenced, therefore, the Mn content is controlled to be 0.50-0.59% in the invention.
P is a harmful element, and excessive P increases the cold brittleness of the steel, so that the P content is not more than 0.015% in the invention.
S is taken as an impurity element in steel, so that the plasticity and the toughness of the steel can be obviously reduced, but the cutting performance of the steel can be effectively improved by proper amount of sulfur, so that the content of S is controlled to be 0.031-0.037 percent.
Cr can remarkably improve the hardenability, strength, wear resistance and other properties of steel, and is beneficial to reducing the activity of C, and can prevent the decarburization phenomenon in the heating, rolling and heat treatment processes of the knuckle forging, but the toughness of the knuckle after quenching and tempering can be remarkably reduced due to the excessively high Cr content, so that the Cr content is controlled to be 0.90-0.99 percent in the invention.
Ni and Mo have the effect of improving the fatigue strength of the material, but too high content can reduce the machinability after hot working and simultaneously increase the alloy cost; cu can improve the strength and the toughness of the material, but too high content of Cu can enhance the hot brittleness of the material at high temperature so as to reduce the fatigue performance of the steering knuckle, so that the content of Ni is not more than 0.25 percent, the content of Mo is not more than 0.10 percent, and the content of Cu is not more than 0.15 percent.
Further, the steel comprises Al, N and Ti in percentage by weight, and the steel satisfies the following relation: al% is more than or equal to 27N%/14-9 Ti%/16.
In the technical scheme of the invention, by controlling the mass percentages of Al, Ti and N in the steel and the mass relation of Al, Ti and N, precipitated phase particles of one or more of carbide, nitride and carbonitride of (Al and Ti) are formed, thereby achieving the positive effects of pinning grain boundaries and refining grains. Therefore, the proper Al, Ti and N contents in the steel must be ensured, and the Al/N and Ti/N contents in the steel must be ensured at the same time, so that the influence of excessive or too little content of certain elements on the performance of the steel is avoided. In the initial stage of smelting, Al is mainly added as a deoxidizer and forms Al2O3Floating impurities, entering slag, feeding Al wires after VD vacuum treatment, adding the Al wiresUnder low oxygen conditions, Al in the alloy plays a role of micro-alloying mainly as an alloy element. Al bonds with N in steel to form an AlN phase, and serves to pin grain boundaries at austenite grain boundaries to inhibit austenite grain growth, but Al is easily formed in steel materials due to excessive Al or an inappropriate Al/N atomic ratio2O3Inclusions are difficult to remove, while Al2O3And CaS is easily adsorbed on a tundish nozzle to form nodules, so that the castability of molten steel is poor. The other element N of AlN is added in the form of alloy, but excessive N causes high gas content and easily forms subcutaneous bubbles, thereby influencing the quality of steel. In addition, AlN particles are unstable at high temperature, easily grow up or dissolve, and the pinning effect on grain boundaries is weakened, so that the present invention inhibits austenite grain growth at high temperature by adding a trace amount of Ti in combination with N element to preferentially form a TiN precipitate phase which is more stable at high temperature, but if the Ti content is too high, coarse TiN inclusions are easily formed in the steel, affecting the properties such as fatigue strength of the knuckle.
In summary, in consideration of the grain refining effect and the formation rule of precipitated phase, in the invention, the weight percentage content of Al is controlled to be 0.017-0.033%, the weight percentage content of Ti is controlled to be 0.003-0.020%, the weight percentage content of N is controlled to be 0.008-0.014%, and Al% is more than or equal to 27N%/14-9 Ti%/16.
Furthermore, in the steel, the level of the sulfide non-metallic inclusion is less than or equal to 2.5.
The preparation method of the steel for the high-strength steering knuckle of the new energy automobile comprises the following steps:
1) preparing furnace burden according to the components and the weight percentage content of the steel, and sequentially carrying out primary smelting, ladle refining, vacuum degassing and continuous casting pouring on the furnace burden through an electric arc furnace to obtain a continuous casting blank;
2) and (3) heating and rolling the continuous casting billet in the step 1) in sequence by adopting a hot processing rolling method of a rolling mill to obtain a finished product steel.
Further, in the step 1), in the initial smelting process of the electric arc furnace, the P is removed from the slag in the oxidation period, and the slag discharging condition comprises that: the slag discharging temperature is 1630-; the tapping conditions comprise: the tapping temperature is 1630-1650 ℃, the weight percentage of P is not more than 0.010 percent, and the weight percentage of C is not less than 0.03 percent;
adding aluminum in the ladle refining process to enable the weight percentage content of the Al in the molten steel to reach 0.038-0.042%, adding other metal alloys, stirring for 5-10min, and adjusting the chemical composition for internal control;
when the temperature of the molten steel in the ladle refining process reaches 1650-;
in the vacuum degassing process, the vacuum degree is 60-70Pa (preferably 66.7Pa), and the vacuum degassing time is not less than 15 min;
after the vacuum degassing process, adding titanium alloy into the molten steel until the weight percentage content of Ti reaches 0.003-0.020% so as to ensure the yield, and then enabling the molten steel to enter the continuous casting process through a ladle when the temperature of the molten steel reaches 1550-.
Wherein the furnace burden comprises low P, S scrap steel, crop, high-quality pig iron, metal alloy and reducing agent, the metal alloy comprises ferrochrome, low-phosphorus ferromanganese, and other metal-containing materials ferrosilicon and titanium alloy which are commonly used in steel-making process and can meet the category of the metal elements of the steel in the invention; the reducing agent comprises calcium carbide, carbon powder and aluminum powder, and the electric arc furnace is preferably a 30-150 ton electric arc furnace;
further, the ladle refining process is performed in a ladle refining furnace adapted to the capacity of the electric arc furnace, and includes: the method comprises the steps of molten steel refining, steel ladle seating, temperature measurement and analysis, argon pressure is adjusted according to conditions, and harmful gas and inclusions in molten steel are removed in the steel ladle refining process.
Further, in the step 1), in the continuous casting process, high-temperature molten steel passes through the protective sleeve and is poured into a tundish, and then a continuous casting billet is poured through a continuous casting crystallizer by matching with an electromagnetic stirring and soft reduction technology;
wherein, the inner surface of the tundish is a refractory coating, the tundish is completely cleaned before use and is checked to have no crack, and the superheat degree of the tundish is 20-40 ℃;
the casting speed of the continuous casting billet is 0.6-2.1m/min, the preferable section size of the continuous casting billet is 140mm multiplied by 140mm-320mm multiplied by 425mm, and the casting speed of the continuous casting billet is adjusted according to the section size;
and (3) placing the obtained continuous casting slab in a slow cooling pit, and performing the step 2) after the slow cooling process, wherein the slow cooling time of the slow cooling process is not less than 24 h.
Further, in step 2), the heating process is performed in a continuous furnace, and sequentially comprises: the device comprises a preheating section, a first heating section, a second heating section and a soaking section;
the temperature of the preheating section is not higher than 700 ℃;
the heating temperature of the first heating section is 700-980 ℃;
the heating temperature of the second heating section is 950-1200 ℃;
the heating temperature of the soaking section is 1100-1200 ℃;
the total heating time of the continuous casting billet in the continuous furnace is not less than 195 min.
Compared with the prior art, the soaking temperature of the technical scheme is increased by 20 ℃ to implement the diffusion process of heating the steel billet, thereby being beneficial to improving the component and structure uniformity of the continuous casting billet. At the same time, the precipitated phase particles have the fastest solid solution speed, so that the compounds of Al, N and Ti which are not dissolved originally in the steel are dissolved more by the high heating temperature, the concentrations of Al, N and Ti in the matrix are increased, more and more dispersed particles are precipitated during the later cooling, and in addition, the finishing rolling temperature can be increased only by increasing the temperature of the heating furnace upwards, so that the austenite after rolling is recovered and recrystallized more fully, and the precipitated phase particles are distributed more uniformly.
As a preferred technical scheme, the steel blank can be discharged from the furnace and enters the rolling process when the temperature difference between the cathode surface and the anode surface of the steel blank obtained after the soaking section does not exceed 30 ℃.
As a preferred technical scheme, before the heating process of the continuous casting billet, surface cleaning is firstly carried out; and after dephosphorization and descaling are carried out on the steel blank obtained after the heating process through high-pressure water, the steel blank enters the rolling process.
Further, in the rolling process, the initial rolling temperature is 1100-1200 ℃, and the final rolling temperature is not lower than 900 ℃.
Under the process, the N is beneficial to desolventizing from the gamma solid solution and combining with Ti and Al in the steel to form one or more precipitated phase particles of (Ti, Al) carbide, nitride and carbonitride. If the finish rolling temperature is low, the final rolling temperature is not lower than 900 ℃ because the peak value of precipitated phase particles precipitates, resulting in uneven distribution of precipitated phase particles and insufficient recovery recrystallization to cause anisotropy in the structure. In addition, the finishing rolling temperature is increased, so that finer grains can be obtained, the difference between the average grain diameter d of ferrite after transformation of the super-cooled austenite and the distance s between the manganese-rich zones is increased due to the fine grains, and the tendency of forming pearlite by the Mn-rich zones is reduced, so that the tissue segregation is reduced.
The steel can be used for preparing new energy automobile steering knuckles.
Furthermore, the tensile strength Rm of the steering knuckle is more than or equal to 870MPa, the yield strength Rp0.2 is more than or equal to 730MPa, and the elongation A is more than or equal to 14 percent;
the metallographic structure of the steering knuckle is tempered sorbite, and the austenite grain size is 7.5-8.0 grade.
Compared with the prior art, the invention has the following characteristics:
1) the steel and the steering knuckle prepared based on the steel have the advantages of low cost and good comprehensive mechanical property, can meet the technical requirements of the steering knuckle on durability of braking force, durability of lateral force, steering force impact, durability and the like, and also have the advantages of wide component element sources, stable and reliable process control and the like;
2) according to the invention, one or more precipitated phase particles of carbide, nitride and carbonitride of Al and Ti are formed by adjusting the absolute weight percentage and the relative weight percentage of Al, Ti and N in the steel, so that the positive effects of pinning grain boundaries and refining grains are achieved, and the tensile strength, yield strength and extensibility of the finished product steel are obviously improved;
3) the invention adopts a hot working rolling method to prepare finished steel products, promotes the component distribution and the tissue uniformity of the steel products by improving the temperature of a soaking section in a heating process, and improves the finish rolling temperature in the rolling process, so that austenite after rolling returns to recrystallize more fully, and precipitated phase particles are distributed more uniformly;
4) the method prolongs the sedation time and promotes the floating of the inclusion by reducing the temperature of the ladle (lower than the temperature of 20 ℃ of the conventional ladle), so as to improve the removal rate of the impurity in the steel and further improve the strength and the toughness of the finished product steel.
Drawings
Fig. 1, fig. 2, fig. 3 and fig. 4 are schematic diagrams of metallographic structures at different magnifications in example 3.
Detailed Description
The invention is described in detail below with reference to the figures and specific embodiments. The present embodiment is implemented on the premise of the technical solution of the present invention, and a detailed implementation manner and a specific operation process are given, but the scope of the present invention is not limited to the following embodiments.
A preparation method of steel comprises the following steps:
1) preparing furnace burden according to the components and weight percentage content of designed steel, and sequentially carrying out primary smelting, ladle refining, vacuum degassing and continuous casting pouring on the furnace burden in a 150t electric arc furnace to obtain a continuous casting blank;
2) and (2) carrying out surface cleaning, heating, high-pressure water dephosphorization and descaled layer removal and rolling on the continuous casting billet obtained in the step 1) in sequence by adopting a hot processing rolling method of a rolling mill to obtain a finished product steel.
Wherein, in step 1), the electric arc furnace is makeed the in-process, goes P at oxidation period office stream sediment, and the condition of slagging tap includes: the slag discharging temperature is 1630-; the tapping conditions comprise: the tapping temperature is 1630-1650 ℃, the weight percentage of P is not more than 0.010 percent, and the weight percentage of C is not less than 0.03 percent;
in the ladle refining process, adding aluminum alloy to ensure that the weight percentage content of Al in the molten steel reaches 0.038-0.042%, adding other metal alloy, stirring for 5-10min, and adjusting chemical components to perform internal control;
when the temperature of the molten steel in the ladle refining process reaches 1650-;
in the vacuum degassing process, the vacuum degree is 66.7Pa, and the vacuum degassing time is not less than 15 min;
after the vacuum degassing process, adding titanium alloy into the molten steel until the weight percentage content of Ti reaches 0.003-0.020% so as to ensure the yield, and then enabling the molten steel to enter a continuous casting process through a ladle when the temperature of the molten steel reaches 1550-;
in the continuous casting process, high-temperature molten steel passes through the protective sleeve and is poured into a tundish, then passes through a continuous casting crystallizer, and is matched with the electromagnetic stirring and soft reduction technology to cast a continuous casting blank,
the inner surface of the tundish is a refractory coating, the tundish is completely clean before use and is checked to have no crack, and the superheat degree of the tundish is 20-40 ℃;
the casting speed of the continuous casting billet is 0.6-2.1m/min, the preferable section size of the continuous casting billet is 140mm multiplied by 140mm-320mm multiplied by 425mm, and the casting speed of the continuous casting billet is adjusted according to the section size;
and (3) placing the obtained continuous casting slab in a slow cooling pit, and performing the step 2) after the slow cooling process, wherein the slow cooling time of the slow cooling process is not less than 24 h.
Wherein the furnace burden comprises low P, S scrap steel, crop, high-quality pig iron, metal alloy and reducing agent, the metal alloy comprises ferrochrome, low-phosphorus ferromanganese, and other metal-containing materials ferrosilicon and titanium alloy which are commonly used in the steelmaking process and can meet the types of steel metal elements; the reducing agent comprises calcium carbide, carbon powder and aluminum powder, and the electric arc furnace is preferably a 30-150 ton electric arc furnace;
further, the ladle refining process is performed in a ladle refining furnace adapted to the capacity of the electric arc furnace, and includes: the method comprises the steps of molten steel refining, steel ladle seating, temperature measurement and analysis, argon pressure is adjusted according to conditions, and harmful gas and inclusions in molten steel are removed in the steel ladle refining process.
In step 2), the heating process is carried out in a continuous furnace, and sequentially comprises the following steps: the device comprises a preheating section, a first heating section, a second heating section and a soaking section;
wherein the temperature of the preheating section is not higher than 700 ℃;
the heating temperature of the first heating section is 700-980 ℃;
the heating temperature of the second heating section is 950-1200 ℃;
the heating temperature of the soaking section is 1100-1200 ℃;
the total heating time of the continuous casting billet in the continuous furnace is not less than 195min, and when the temperature difference of the negative and positive surfaces of the steel billet obtained after the soaking section is not more than 30 ℃, the steel billet is taken out of the furnace and enters the rolling process;
in the rolling process, the initial rolling temperature is 1100-1200 ℃, and the final rolling temperature is not lower than 900 ℃.
Example 1:
in this example, 5 kinds of round rods with a diameter of 80mm were prepared by the above steps and combining the corresponding technical parameters, wherein the technical parameters for preparing 5 kinds of round rods are shown in table 1.
TABLE 1 technical parameters for the preparation of 5 round bars
Example 2:
in this example, 5 kinds of round rods of example 1 were sequentially subjected to heating, pre-forging, final forging, edge cutting, quenching and tempering to prepare knuckle parts, and after sampling of the tie rods, the chemical compositions and mechanical properties thereof were measured and compared with those of the knuckle parts of the prior art (1: CN 104087819B; 2: CN109097644A), and the results are shown in tables 2 and 3, respectively.
TABLE 2 chemical composition comparison (wt%) of the knuckle parts in this example with those of the prior art
TABLE 3 comparison of mechanical Properties of the knuckle parts of this example with those of the prior art
Example 3:
in this example, the results of the metallographic test of the knuckle part prepared in example 2 are shown in fig. 1, 2, 3 and 4, and it can be seen from the figure that the metallographic structure after the heat treatment is a tempered sorbite (shown in fig. 1); a large amount of precipitated phase particles such as AlN and TiN are uniformly distributed in the matrix (as shown in figure 2), austenite grain boundaries are effectively pinned, so that the grains of the steering knuckle are fine and uniform, the grain size is 7.5-8 grades (as shown in figure 3), the performance is stable, and the coarse grade and the fine grade of sulfide are not higher than 2.5 grades (as shown in figure 4) in reference to GB/T10561-2005.
The embodiments described above are described to facilitate an understanding and use of the invention by those skilled in the art. It will be readily apparent to those skilled in the art that various modifications to these embodiments may be made, and the generic principles described herein may be applied to other embodiments without the use of the inventive faculty. Therefore, the present invention is not limited to the above embodiments, and those skilled in the art should make improvements and modifications within the scope of the present invention based on the disclosure of the present invention.
Claims (10)
1. The steel for the high-strength steering knuckle of the new energy automobile is characterized by comprising the following components in percentage by weight:
c: 0.40-0.44%, Si: 0.31-0.37%, Mn: 0.50-0.59%, P: less than or equal to 0.015%, S: 0.031-0.037%, Cr: 0.90-0.99%, Ni: less than or equal to 0.25%, Cu: less than or equal to 0.15 percent, Mo: less than or equal to 0.10 percent, Al: 0.017-0.033%, Ti: 0.003-0.020%, N: 0.008-0.014%, the balance Fe and inevitable impurities.
2. The steel material for the high-strength steering knuckle of the new energy automobile as claimed in claim 1, wherein the weight percentage of Al, the weight percentage of N and the weight percentage of Ti in the steel material are respectively Al%, N% and Ti%, and satisfy the following relation: al% is more than or equal to 27N%/14-9 Ti%/16.
3. The steel material for the high-strength steering knuckle of a new energy automobile as claimed in claim 1, wherein the steel material has a sulfide-based non-metallic inclusion grade of 2.5 or less.
4. The method for producing a steel material for a high-strength steering knuckle of a new energy automobile according to any one of claims 1 to 3, characterized by comprising the steps of:
1) preparing furnace burden according to the components and the weight percentage content of the steel, and sequentially carrying out primary smelting, ladle refining, vacuum degassing and continuous casting pouring on the furnace burden through an electric arc furnace to obtain a continuous casting blank;
2) and (3) heating and rolling the continuous casting billet in the step 1) in sequence to obtain a finished product steel.
5. The preparation method of the steel for the high-strength steering knuckle of the new energy automobile according to claim 4, wherein in the step 1), in the primary smelting process of the electric arc furnace, the slag tapping condition comprises: the slag discharging temperature is 1630-; the tapping conditions comprise: the tapping temperature is 1630-1650 ℃, the weight percentage of P is not more than 0.010 percent, and the weight percentage of C is not less than 0.03 percent;
adding aluminum in the ladle refining process to ensure that the weight percentage content of the Al in the molten steel reaches 0.038-0.042%, and entering a vacuum degassing process when the temperature of the molten steel in the ladle refining process reaches 1650-;
in the vacuum degassing process, the vacuum degassing time is not less than 15 min;
after the vacuum degassing process, adding titanium alloy into the molten steel until the weight percentage of Ti in the molten steel reaches 0.003-0.020%, and when the temperature of the molten steel reaches 1550-.
6. The preparation method of the steel for the new energy automobile high-strength steering knuckle according to claim 4, characterized in that in the step 1), the superheat degree of a tundish used in the continuous casting process is 20-40 ℃, and the casting speed is 0.6-2.1 m/min;
and (3) after the obtained continuous casting slab is subjected to the slow cooling process, performing the step 2), wherein the slow cooling time of the slow cooling process is not less than 24 h.
7. The method for preparing the steel for the high-strength steering knuckle of the new energy automobile according to claim 4, wherein in the step 2), the heating process is performed in a continuous furnace, and sequentially comprises the following steps: the device comprises a preheating section, a first heating section, a second heating section and a soaking section;
the temperature of the preheating section is not higher than 700 ℃;
the heating temperature of the first heating section is 700-980 ℃;
the heating temperature of the second heating section is 950-1200 ℃;
the heating temperature of the soaking section is 1100-1200 ℃;
the total heating time of the continuous casting billet in the continuous furnace is not less than 195 min.
8. The preparation method of the steel for the high-strength steering knuckle of the new energy automobile as claimed in claim 4, wherein the rolling temperature is 1100-1200 ℃ and the finish rolling temperature is not lower than 900 ℃ in the rolling process.
9. Use of the steel material for a high-strength steering knuckle of a new energy automobile according to any one of claims 1 to 3, wherein the steel material is used for preparing a new energy automobile steering knuckle.
10. The application of the steel for the new energy automobile high-strength steering knuckle according to claim 9 is characterized in that the tensile strength Rm of the steering knuckle is more than or equal to 870MPa, the yield strength Rp0.2 is more than or equal to 730MPa, and the elongation A is more than or equal to 14%;
the metallographic structure of the steering knuckle is tempered sorbite, and the austenite grain size is 7.5-8.0 grade.
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