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CN116288043B - Complex phase steel for wheel spokes and preparation method thereof - Google Patents

Complex phase steel for wheel spokes and preparation method thereof Download PDF

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Publication number
CN116288043B
CN116288043B CN202211094465.9A CN202211094465A CN116288043B CN 116288043 B CN116288043 B CN 116288043B CN 202211094465 A CN202211094465 A CN 202211094465A CN 116288043 B CN116288043 B CN 116288043B
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China
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steel
cooling
temperature
rolling
complex phase
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CN202211094465.9A
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CN116288043A (en
Inventor
董现春
张大伟
刘新垚
李学涛
张侠洲
肖宝亮
蔡宁
牟淑坤
赵英建
王凤会
张飞虎
刘宏
齐建
郭占山
魏绍东
田志红
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Shougang Group Co Ltd
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Shougang Group Co Ltd
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Priority to CN202211094465.9A priority Critical patent/CN116288043B/en
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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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23P—METAL-WORKING NOT OTHERWISE PROVIDED FOR; COMBINED OPERATIONS; UNIVERSAL MACHINE TOOLS
    • B23P15/00—Making specific metal objects by operations not covered by a single other subclass or a group in this subclass
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • 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
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • 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
    • C21D2261/00—Machining or cutting being involved
    • 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
    • Y02T—CLIMATE CHANGE MITIGATION TECHNOLOGIES RELATED TO TRANSPORTATION
    • Y02T10/00—Road transport of goods or passengers
    • Y02T10/80—Technologies aiming to reduce greenhouse gasses emissions common to all road transportation technologies
    • Y02T10/86—Optimisation of rolling resistance, e.g. weight reduction 

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

本申请涉及汽车零部件用钢材领域，尤其涉及一种车轮轮辐用复相钢及其制备方法；所述复相钢的化学成分包括：C:0.09％～0.22％，Si:0.05％～0.20％，Mn:1.20％～1.80％，P≤0.015％，S≤0.005％，Alt:0.02％～0.50％，Cr:0.25％～0.60％，Nb:0.010％～0.060％，Ti:0.015％～0.03％，B:0.0018％～0.0030％，其余为Fe及不可避免的杂质；所述方法包括：对含如权利要求1化学成分所述的板坯进行加热、粗轧、精轧、冷却和卷取，得到高强度的车轮轮辐用复相钢基体；对所述高强度的车轮轮辐用复相钢进行变形、制孔和热处理，得到螺栓孔带凸台的车轮轮辐用复相钢；通过对化学成分和制备方法的控制，能得到含有包括铁素体、贝氏体和马氏体的金相组织的钢材，并有效提高钢材的强度。

The present application relates to the field of steel for automobile parts, and in particular to a complex phase steel for wheel spokes and a preparation method thereof; the chemical composition of the complex phase steel comprises: C: 0.09% to 0.22%, Si: 0.05% to 0.20%, Mn: 1.20% to 1.80%, P≤0.015%, S≤0.005%, Alt: 0.02% to 0.50%, Cr: 0.25% to 0.60%, Nb: 0.010% to 0.060%, Ti: 0.015% to 0.03%, B: 0.00 18% to 0.0030%, and the rest is Fe and inevitable impurities; the method comprises: heating, rough rolling, finish rolling, cooling and coiling a slab containing the chemical composition as claimed in claim 1 to obtain a high-strength complex phase steel matrix for wheel spokes; deforming, drilling and heat treating the high-strength complex phase steel for wheel spokes to obtain a complex phase steel for wheel spokes with bosses in bolt holes; by controlling the chemical composition and the preparation method, a steel containing a metallographic structure including ferrite, bainite and martensite can be obtained, and the strength of the steel can be effectively improved.

Description

Complex-phase steel for wheel spokes and preparation method thereof
Technical Field
The application relates to the field of steel for automobile parts, in particular to complex phase steel for wheel spokes and a preparation method thereof.
Background
The wheels are important safety parts of the automobile, bear the torque output by rotation and movement of the gearbox, convert the power output into the pulling force and the pushing force of linear movement, and transmit the pulling force and the pushing force to the road surface through the tires, thus being important parts for realizing the functions of advancing, retreating, braking, steering and the like of the automobile.
At present, the spoke of an automobile is mostly manufactured by adopting a low-strength steel plate, because complex deformation treatment is needed in the spoke manufacturing process, if a high-strength material is adopted, the deformation treatment is difficult, but because the spoke has low strength, the bearing capacity is low, the spoke is not enough to bear the action of repeatedly changing driving force, braking force, steering force and ground impact force, and under the condition of complex road conditions, particularly the bolt hole part connected with a hub on the spoke is locally born with severe loads such as bending, abrasion and the like, accidents such as deformation, instability, fatigue fracture and the like are frequently caused, and great potential hazards of traffic safety are brought.
Therefore, how to improve the strength of steel for spoke is a technical problem to be solved at present.
Disclosure of Invention
The application provides complex phase steel for a wheel spoke and a preparation method thereof, which aim to solve the technical problem of low strength of steel for the wheel spoke in the prior art.
In a first aspect, the application provides a complex phase steel for wheel spokes, which comprises the following chemical components in percentage by mass:
C:0.09％～0.22％,Si:0.05％～0.20％,Mn:1.20％～1.80％,P≤0.015％,S≤0.005％,Alt:0.02％～0.50％,Cr:0.25％～0.60％,Nb:0.010％～0.060％,Ti:0.015％～0.03％,B:0.0018％～0.0030％, The balance of Fe and unavoidable impurities.
Optionally, the metallographic structure of the complex phase steel comprises, by mass, 50% -70% of ferrite, 20% -40% of bainite and 5% -15% of martensite.
Optionally, the thickness of the complex phase steel is 4 mm-22 mm.
In a second aspect, the present application provides a method of preparing the complex phase steel of the first aspect, the method comprising:
heating, rough rolling, finish rolling, cooling and coiling the slab containing the chemical components of the first aspect to obtain a complex phase steel matrix for the wheel spoke with high strength;
and (3) deforming, hole making and heat treatment are carried out on the high-strength complex phase steel for the wheel spoke, so as to obtain the complex phase steel with the lug boss on the bolt hole for the wheel spoke.
Optionally, the initial temperature of the finish rolling is 1000-1140 ℃, the final rolling temperature of the finish rolling is 840-920 ℃, and the rolling passes of the finish rolling are 6-7 times.
Optionally, the initial temperature of the rough rolling is 1150-1250 ℃, the final rolling temperature of the rough rolling is 1020-1180 ℃, and the rolling pass of the rough rolling is 5-7 times.
Optionally, the heating terminal temperature is 1200-1280 ℃, and the heating time is 120-240 min.
Optionally, the initial temperature of cooling is 840-920 ℃, and the final temperature of cooling is 300-550 ℃.
Optionally, the heat treatment comprises heat processing and cooling processing, wherein the peak temperature of the heat processing is 1000-1200 ℃, the end temperature of the cooling processing is 20-50 ℃, and the cooling speed of the cooling processing is 50-300 ℃ per second.
Optionally, the heat treatment further comprises tempering treatment, wherein the tempering treatment comprises tempering heating and tempering cooling, the end temperature of the tempering heating is 220-350 ℃, the end temperature of the tempering cooling is 20-50 ℃, and the cooling rate of the tempering cooling is 5-10 ℃ per second.
Compared with the prior art, the technical scheme provided by the embodiment of the application has the following advantages:
According to the complex phase steel for the wheel spoke, the tensile strength of steel is improved by limiting the added C and Si, the Ti element is added for second phase particle precipitation strengthening, the Al element is added for solid solution strengthening, the Nb element is added for fine crystal strengthening precipitation strengthening and the toughness of the steel is improved, and the B element and the Cr element are added for improving the hardenability of the steel, so that the metallographic structure of the steel comprises ferrite, bainite and a martensitic structure, the ferrite structure promotes the steel for the wheel spoke to have good toughness and is beneficial to improving the plastic deformation performance of the steel, and the bainite is a strengthening phase and has strong grain boundary bonding strength with the ferrite, so that the strength of the steel is improved, and the martensitic structure is harder, so that the wheel spoke is guaranteed to have good strength, and the metallographic structure of the steel for the wheel spoke is controlled, so that the effective improvement of the strength of the steel for the wheel spoke is guaranteed.
Drawings
The accompanying drawings, which are incorporated in and constitute a part of this specification, illustrate embodiments consistent with the invention and together with the description, serve to explain the principles of the invention.
In order to more clearly illustrate the embodiments of the invention or the technical solutions of the prior art, the drawings which are used in the description of the embodiments or the prior art will be briefly described, and it will be obvious to a person skilled in the art that other drawings can be obtained from these drawings without inventive effort.
FIG. 1 is a schematic flow chart of a method according to an embodiment of the present application;
Fig. 2 is a schematic structural view of complex phase steel for wheel spokes with bolt holes provided with external bosses according to an embodiment of the present application;
fig. 3 is a schematic structural view of complex phase steel for wheel spokes with built-in bosses in bolt holes according to an embodiment of the present application.
Detailed Description
For the purpose of making the objects, technical solutions and advantages of the embodiments of the present application more apparent, the technical solutions of the embodiments of the present application will be clearly and completely described below with reference to the accompanying drawings in the embodiments of the present application, and it is apparent that the described embodiments are some embodiments of the present application, but not all embodiments of the present application. All other embodiments, which can be made by those skilled in the art based on the embodiments of the application without making any inventive effort, are intended to be within the scope of the application.
In one embodiment of the application, a complex phase steel for wheel spokes is provided, and the complex phase steel comprises the following chemical components in percentage by mass:
C:0.09％～0.22％,Si:0.05％～0.20％,Mn:1.20％～1.80％,P≤0.015％,S≤0.005％,Alt:0.02％～0.50％,Cr:0.25％～0.60％,Nb:0.010％～0.060％,Ti:0.015％～0.03％,B:0.0018％～0.0030％, The balance of Fe and unavoidable impurities.
In the embodiment of the application, the mass fraction of C is 0.09% -0.22%, and the C content is a basic strengthening element of steel, so that the tensile strength grade of the steel plate is greatly determined, the C content is an important index for influencing the carbon equivalent, when the mass fraction is larger than the maximum value of the end point of the range, the hardenability is large to a certain extent, excessive high-hardness martensite brittle structure is generated in the processes of hole making and subsequent welding with a rim, cold cracks are easy to generate, the cracks rapidly expand along the direction of a martensite lath in the wheel service process, the wheel cracking failure influences the service safety, and when the mass fraction is smaller than the minimum value of the end point of the range, the hardenability is reduced to a certain extent, the strength of the steel is insufficient, and the target bainite and martensite structure proportion in the complex phase steel cannot be obtained in the processes of steel production and hole making.
The Si with the mass fraction of 0.05-0.20% has the positive effects that because Si is a solid solution strengthening element of the steel, the hardenability of the steel can be improved, so that the strength of the steel is improved, when the mass fraction is larger than the maximum value of the end point of the range, the Si content is too high to a certain extent, the steel plate is easy to become brittle, and when the mass fraction is smaller than the minimum value of the end point of the range, the Si+Mn joint deoxidization cannot be carried out in the subsequent spoke and rim welding to a certain extent, and the oxygen content in the welding seam is also improved, so that the fatigue performance of the welding seam is reduced.
The positive effect of Mn with mass fraction of 1.20% -1.80% is that Mn can improve the hardenability of the strip steel, so that the microstructure substructure of the strip steel is thinned, when the value of the mass fraction is larger than the maximum value of the end point of the range, the segregation tendency of Mn in the steel plate is increased to a certain extent, a layering defect is formed in the spoke spinning process, and when the value of the mass fraction is smaller than the minimum value of the end point of the range, the hardenability of the steel plate is reduced to a certain extent, and particularly, the microstructure proportion of target bainite and martensite cannot be obtained in the center part of the plate thickness.
The positive effect of P being less than or equal to 0.015% is that in the mass fraction range, the formability of the steel is easily affected by P, and the more the content is, the more adverse effect is on fatigue performance.
The positive effect of S content of 0.005% or less is that in the range of the mass fraction, the more S content is liable to affect formability of the steel, the more adverse effect on fatigue performance is caused.
The Alt has the positive effects that the hardness of the steel product can be improved because Al plays a solid solution strengthening role in the mass fraction range, when the value of the mass fraction is larger than the maximum value of the end point of the range, the solid solubility can be exceeded to a certain extent, the precipitation of Al is formed, the toughness of the steel is reduced, and when the value of the mass fraction is smaller than the minimum value of the end point of the range, the steel cannot be deeply deoxidized to a certain extent, the oxygen content in the steel is increased, and the plasticity of the steel is reduced.
The Cr has the positive effects that in the mass fraction range, the Cr can improve the hardenability of the steel, is beneficial to the transformation of martensite after hot working and has a certain solid solution strengthening effect, when the value of the mass fraction is larger than the maximum value of the end point of the range, cr can be segregated into a strip-shaped distribution structure to a certain extent, a high-hardness layered martensitic structure is generated, the uniformity of the structure performance is reduced, the spinning plastic forming of the spoke is not facilitated, and when the value of the mass fraction is smaller than the minimum value of the end point of the range, the structure proportion of target bainite and martensite can not be obtained to a certain extent, so that the strength of a final steel product is insufficient.
The Nb has the positive effects that in the mass fraction range, the Nb can refine the grain size, plays a role in fine grain strengthening and precipitation strengthening, and can improve the toughness of steel, when the value of the mass fraction is larger than the maximum value of the end point of the range, excessive niobium carbide can be precipitated to a certain extent, and as a great amount of C is adsorbed in the forming process of the niobium carbide, the austenite stability is reduced, the target bainite and martensite structure ratio cannot be obtained, and when the value of the mass fraction is smaller than the minimum value of the end point of the range, the grain coarsening and the strength reduction can be caused to a certain extent.
The positive effects of the Ti with the mass fraction of 0.015% -0.03% are that in the mass fraction range, the Ti can fix nitrogen and generate a strong precipitation strengthening effect, so that the plastic deformation capability of the steel can be improved, when the value of the mass fraction is larger than the maximum value of the end point of the range, large TiN inclusions can be formed to a certain extent, the formed inclusions are separated from a matrix to form a crack source when being formed by spinning, thereby causing cracking of the steel, and when the value of the mass fraction is smaller than the minimum value of the end point of the range, crystal grain coarsening can be caused to a certain extent, so that the strength of the steel is reduced.
The mass fraction of B is 0.0018% -0.0030%, and the positive effects are that in the mass fraction range, as B can improve the hardenability of the steel, in the process of local heating and rapid cooling of complex phase steel for wheel spokes with bosses in bolt holes, target bainite and martensite structures can be obtained, so that the steel has high local hardness, when the value of the mass fraction is larger than the maximum value of the end point of the range, the hardenability is excessively strong to cause rapid rise of phase change stress, the cracking of the steel is caused, and when the value of the mass fraction is smaller than the minimum value of the end point of the range, the hardenability of the steel is insufficient to a certain extent, so that the internal hardness of the steel is lower, and the bearing performance is affected.
In some optional modes, the metallographic structure of the complex phase steel comprises, by mass, 50% -70% of ferrite, 20% -40% of bainite and 5% -15% of martensite.
In the embodiment of the application, the volume fraction of ferrite is 50% -70%, and the positive effects are that the steel for the wheel spoke has good toughness due to ferrite structure, so that the plastic deformation performance of the steel is good, the stamping and spinning forming of the spoke are facilitated, when the volume fraction is larger than the maximum value of the end point of the range, the strength is reduced to a certain extent, the bearing performance is influenced to be reduced, and when the volume fraction is smaller than the minimum value of the end point of the range, the plasticity is reduced to a certain extent, thereby bringing about the problem of forming cracking, and meanwhile, the steel is difficult to process into the wheel with the specified shape and size.
The volume fraction of the bainite is 20% -40%, the bainite is a strengthening phase, strong grain boundary bonding strength is formed between the bainite and ferrite, the strength of the steel can be improved, when the volume fraction is larger than the maximum value of the end point of the range, the grain boundary aggregation strength is excessively high to a certain extent, so that the metal fluidity is weakened, the steel is formed to crack, and when the volume fraction is smaller than the minimum value of the end point of the range, the grain boundary bonding strength is reduced to a certain extent, so that the bearing performance is influenced.
The volume fraction of the martensite is 5% -15%, the positive effects are that the martensite structure is harder, so that the wheel spoke prepared from the steel can be guaranteed to have good strength, and the wheel spoke has strong bearing capacity, so that repeated driving force, braking force, steering tension and uneven ground impact force can be borne, safety is guaranteed, when the volume fraction is larger than the maximum value of the end point of the range, more brittleness can be caused to a certain extent, the fatigue crack expansion rate of the steel is accelerated, the fatigue life is reduced, and when the volume fraction is smaller than the minimum value of the end point of the range, the strength of the steel can be reduced to a certain extent, and the bearing performance of the wheel spoke prepared from the steel is influenced.
In some optional modes, the thickness of the complex phase steel is 4 mm-22 mm.
In the embodiment of the application, the thickness of the complex phase steel is 4 mm-22 mm, the steel is suitable for spokes of passenger vehicles and commercial vehicles in the thickness range, meanwhile, the thickness specification can be matched with chemical components and corresponds to the rolling and heat treatment process, so that the target tissue proportion and mechanical property can be obtained, when the thickness value is larger than the maximum value of the end point of the range, the consistency of the tissue property in the thickness direction can not be ensured to a certain extent, and when the thickness value is smaller than the minimum value of the end point of the range, the shape and the size of the boss on the spokes can not be obtained to a certain extent.
In one embodiment of the present application, as shown in fig. 1, there is provided a method for preparing complex phase steel for wheel spokes, the method comprising:
s1, heating, rough rolling, finish rolling, cooling and coiling a plate blank containing the chemical components to obtain a high-strength complex phase steel matrix for the wheel spoke;
s2, deforming, hole making and heat treatment are carried out on the high-strength complex-phase steel for the wheel spoke, so that the complex-phase steel for the wheel spoke with the lug boss in the bolt hole is obtained.
In some alternative modes, the initial temperature of the finish rolling is 1000-1140 ℃, the finish rolling temperature of the finish rolling is 840-920 ℃, and the rolling pass of the finish rolling is 6-7 times.
In the embodiment of the application, the initial temperature of finish rolling is 1000-1140 ℃, and the method has the advantages that in the temperature range, proper rolling deformation resistance can be obtained, the plate width hit rate is improved, when the temperature value is larger than the maximum value of the end point of the range, decarburization and thickening of oxide skin on the surface of steel products can be caused to a certain extent, the strength of the surface and the flatness of the surface can not be ensured, and when the temperature value is smaller than the minimum value of the end point of the range, the rolling deformation resistance of the steel products can be improved to a certain extent, the load of a rolling mill is increased sharply, and equipment is damaged.
The finish rolling temperature of 840-920 ℃ has the advantages that in the temperature range, a wider ferrite temperature transformation interval can be obtained, equiaxed ferrite grains are obtained, the plastic forming of the spoke is facilitated, when the temperature value is larger than the maximum value of the end point of the range, the ferrite grains are coarse to a certain extent, the fine grain strengthening effect is reduced, and when the temperature value is smaller than the minimum value of the end point of the range, the structure is flattened to a certain extent, the grains in the thickness direction are inconsistent, and the steel performance is fluctuated.
The finish rolling has the advantages that the structure grain size in the thickness direction of the steel plate is uniform and consistent through finish rolling with multiple passes and small deformation, the performance is stable, when the value of the rolling pass is larger than the maximum value of the end point of the range, the rolling temperature is reduced to a certain extent, the surface of the steel is fine, the load of a subsequent pass rolling mill is increased, when the value of the rolling pass is smaller than the minimum value of the end point of the range, the single pass deformation of the finish rolling is large to a certain extent, and the edge quality of the steel cannot be guaranteed.
In some alternative modes, the initial temperature of the rough rolling is 1150-1250 ℃, the final rolling temperature of the rough rolling is 1020-1180 ℃, and the rolling passes of the rough rolling are 5-7 times.
In the embodiment of the application, the initial temperature of rough rolling is 1150-1250 ℃, and the method has the advantages that in the temperature range, a good austenite matrix structure can be obtained, the controlled rolling and cooling in the steel rolling process are facilitated, and the ferrite, bainite and martensite structures can be sequentially obtained, when the temperature value is larger than the maximum value of the end point of the range, the coarse structure can be caused to a certain extent, the surface decarburization and oxide skin thickening of the steel can be caused, and when the temperature value is smaller than the minimum value of the end point of the range, the temperature between rough rolling and finish rolling can be reduced too quickly to a certain extent, and the fine control of grains is not facilitated.
The finish rolling temperature of rough rolling is 1020-1180 ℃, the method has the advantages that in the temperature range, the change of crystal grains can be controlled, meanwhile, surface oxide scales are removed, so that a reasonable finish rolling process temperature window is obtained, when the temperature value is larger than the maximum value of the end point of the range, the finish rolling temperature is excessively high to a certain extent, the crystal grains of steel are coarse, oxide scales are thick, when the temperature value is smaller than the minimum value of the end point of the range, the load of a rolling mill is increased to a certain extent, and the temperature window with uniform temperature is shortened.
The method has the advantages that the core of the casting blank can be loosened and shrinkage cavity in the range of the rolling pass, so that a good core structure is obtained, when the value of the rolling pass is larger than the maximum value of the end point of the range, the rolling temperature can be reduced more to a certain extent, the initial temperature control of finish rolling is not facilitated, when the value of the rolling pass is smaller than the minimum value of the end point of the range, the deformation rate of the plate blank is overlarge to a certain extent, the phenomena of bulging and warping can be bad in the flattening process of the steel, and the finish rolling control is not facilitated.
In some optional manners, the heating end point temperature is 1200-1280 ℃, and the heating time is 120-240 min.
In the embodiment of the application, the end temperature of heating is 1200-1280 ℃, and the positive effects of the application are that in the temperature range, the heating of the plate blank can be ensured to be sufficient, thereby facilitating the phase change of the structure, when the temperature value is larger than the end maximum value of the range, the excessive coarse grains can be caused, the strength of the steel is influenced, and when the temperature value is smaller than the end minimum value of the range, the excessive rolling force in the rolling process can be caused, and the working of the rolling mill is influenced.
In some alternatives, the initial temperature of the cooling is 840 ℃ to 920 ℃ and the final temperature of the cooling is 300 ℃ to 550 ℃.
In the embodiment of the application, the initial cooling temperature is 840-920 ℃, and the positive effects are that in the temperature range, the initial transformation of ferrite can be completed, so that matrix tissues and nano precipitated particles with proper proportion are obtained, when the temperature value is larger than the maximum value of the end point of the range, coarse grains can be caused to a certain extent, the plasticity and strength of steel are reduced, and when the temperature value is smaller than the minimum value of the end point of the range, the structure is flattened to a certain extent, and the difference of transverse and longitudinal properties of the steel is large.
The cooling end temperature is 300-550 ℃, and the method has the advantages that the target bainite to martensite ratio can be obtained in the temperature range, when the temperature value is larger than the end maximum value of the range, the martensite to bainite ratio can be reduced to a certain extent, the strength of the steel is reduced, and when the temperature value is smaller than the end minimum value of the range, the bainite ratio of the martensite can be improved to a certain extent, and the plasticity of the steel can be reduced.
In some alternatives, the heat treatment includes a heat treatment and a cooling treatment, the heat treatment having a peak temperature of 1000 ℃ to 1200 ℃, the cooling treatment having an end temperature of 20 ℃ to 50 ℃, and the cooling treatment having a cooling rate of 50 ℃ to 300 ℃ per second.
In the embodiment of the application, the peak temperature of the hot working is 1000-1200 ℃, and the positive effects are that in the temperature range, the metallographic structure of the steel can be completely austenitized, and in the subsequent cooling process, the metallographic structure can obtain sufficient phase change, so that the proportion of unstable structures is reduced, when the temperature value is larger than the maximum value of the end point of the range, the structures are overheated to a certain extent, meanwhile, the inter-crystal oxidation is caused, the toughness of the steel is reduced, and when the temperature value is smaller than the minimum value of the end point of the range, the incomplete structure transformation is caused to a certain extent, the final metallographic structure is uneven, and the performance stability of the wheel product is influenced.
The cooling processing end temperature is 20-50 ℃, the martensite and the bainite can be completely converted within the temperature range, so that a high-hardness local reinforced structure is obtained, when the temperature value is larger than the end maximum value of the range, the local strength of the steel is insufficient to a certain extent, when the temperature value is smaller than the end minimum value of the range, the larger phase change stress is generated in the production process to a certain extent, the dimensional deviation of the steel is caused, and meanwhile, the residual stress also reduces the fatigue service performance of the steel.
The cooling speed of the cooling processing is 50-300 ℃ per second, the cooling processing time period can be controlled within the cooling speed range, and therefore the controllable bainite and martensite structure proportion is obtained, when the cooling speed is larger than the maximum value of the end point of the range, the transformation stress is excessively large to a certain extent, the steel is cracked, and when the cooling speed is smaller than the minimum value of the end point of the range, the target bainite and martensite structure proportion cannot be obtained to a certain extent.
In some alternatives, the heat treatment further comprises a tempering treatment, the tempering treatment comprises tempering heating and tempering cooling, the end temperature of the tempering heating is 220 ℃ to 350 ℃, the end temperature of the tempering cooling is 20 ℃ to 50 ℃, and the cooling rate of the tempering cooling is 5 ℃ to 10 ℃ per second.
In the embodiment of the application, the end temperature of tempering heating is 220-350 ℃, and the positive effects are that in the temperature range, the martensite structure can be stabilized, thereby obtaining a tempered martensite entity, guaranteeing the toughness of steel, when the temperature value is larger than the end maximum value of the range, the structure proportion of martensite can be reduced to a certain extent, thereby reducing the strength of the steel, and when the temperature value is smaller than the end minimum value of the range, the final structure of martensite can be chilled and brittle to a certain extent, so that the steel is easy to fatigue crack.
The tempering cooling end temperature is 20-50 ℃, the positive effects are that in the temperature range, the balanced phase structure proportion can be obtained, when the temperature value is larger than the end maximum value of the range, the continuous decomposition of martensite can be caused to a certain extent, the strength of steel is reduced, and when the temperature value is smaller than the end minimum value of the range, the instability of martensite can be caused to a certain extent.
The tempering cooling has the advantages that the phase change stress can be released within the cooling rate range within 5-10 ℃ so as to reduce the residual stress level, when the cooling speed is larger than the end maximum value of the range, the residual stress is excessively high to a certain extent, the bearing performance of a steel product is reduced, and when the cooling speed is smaller than the end minimum value of the range, the excessive decomposition of martensite is caused to a certain extent, so that the product strength of the steel is reduced.
In some alternative modes, the hardness of the complex phase steel for the wheel spoke with the bolt hole and the boss is more than or equal to 280HV.
Example 1
The complex phase steel for the wheel spoke comprises the following chemical components in percentage by mass:
0.09% of C, 0.20% of Si, 1.80% of Mn, less than or equal to 0.015% of P, less than or equal to 0.005% of S, 0.03% of Alt, 0.60% of Cr, 0.02% of Nb, 0.02% of Ti, 0.0030% of B, and the balance of Fe and unavoidable impurities.
The thickness of the complex phase steel is 14mm.
A preparation method of complex phase steel for wheel spokes comprises the following steps:
S1, heating, rough rolling, finish rolling, cooling and coiling a slab to obtain a high-strength complex phase steel matrix for the wheel spoke;
S2, deforming, hole making and heat treatment are carried out on the high-strength complex-phase steel for the wheel spoke, wherein the complex-phase steel for the wheel spoke is provided with the bolt hole with the external boss and the complex-phase steel for the wheel spoke is provided with the bolt hole with the internal boss and is shown in FIG. 3, and the complex-phase steel for the wheel spoke is obtained.
The initial temperature of the finish rolling was 1140 ℃, the finish rolling temperature of the finish rolling was 920 ℃, and the rolling pass of the finish rolling was 7 times.
The initial temperature of the rough rolling is 1250 ℃, the final rolling temperature of the rough rolling is 1180 ℃, and the rolling pass of the rough rolling is 6 times.
The end point temperature of heating was 1280 ℃ and the time of heating was 240min.
The initial temperature of cooling was 920 ℃, and the end temperature of cooling was 550 ℃.
The heat treatment includes a heat process and a cooling process, the peak temperature of the heat process is 1000 ℃, the end temperature of the cooling process is 50 ℃, and the cooling rate of the cooling process is 300 ℃ per second.
The heat treatment also comprises tempering treatment, wherein the tempering treatment comprises tempering heating and tempering cooling, the end temperature of the tempering heating is 220 ℃, the end temperature of the tempering cooling is 20 ℃, and the cooling rate of the tempering cooling is 10 ℃ per second.
Example 2
Example 2 and example 1 were compared, and the difference between example 2 and example 1 is that:
The complex phase steel comprises the following chemical components in percentage by mass:
0.14% of C, 0.15% of Si, 1.60% of Mn, less than or equal to 0.015% of P, less than or equal to 0.005% of S, 0.10% of Alt, 0.50% of Cr, 0.010% of Nb, 0.015% of Ti, 0.0028% of B, and the balance of Fe and unavoidable impurities.
Example 3
Example 3 was compared with example 1, and the difference between example 3 and example 1 was:
The complex phase steel comprises the following chemical components in percentage by mass:
0.18% of C, 0.10% of Si, 1.60% of Mn, less than or equal to 0.015% of P, less than or equal to 0.005% of S, 0.25% of Alt, 0.40% of Cr, 0.030% of Nb, 0.015% of Ti, 0.0025% of B, and the balance of Fe and unavoidable impurities.
Example 4
Example 4 and example 1 were compared, and example 4 and example 1 differ in that:
The complex phase steel comprises the following chemical components in percentage by mass:
0.20 percent of C, 0.08 percent of Si, 1.40 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.005 percent of S, 0.30 percent of Alt, 0.25 percent of Cr, 0.040 percent of Nb, 0.030 percent of Ti, 0.0020 percent of B and the balance of Fe and unavoidable impurities.
Example 5
Example 5 was compared with example 1, and the difference between example 5 and example 1 was:
The complex phase steel comprises the following chemical components in percentage by mass:
0.22% of C, 0.05% of Si, 1.20% of Mn, less than or equal to 0.015% of P, less than or equal to 0.005% of S, 0.50% of Alt, 0.22% of Cr, 0.060% of Nb, 0.025% of Ti, 0.0018% of B, and the balance of Fe and unavoidable impurities.
Example 6
Comparing example 6 with example 1, example 6 differs from example 1 in that:
the thickness of the complex phase steel is 4mm.
The initial temperature of the finish rolling is 1000 ℃, the finish rolling temperature of the finish rolling is 840 ℃, and the rolling pass of the finish rolling is 6 times.
The initial temperature of rough rolling is 1150 ℃, the final rolling temperature of rough rolling is 1020 ℃, and the rolling passes of rough rolling are 5 times.
The end temperature of the heating was 1200 ℃ and the heating time was 120min.
The initial temperature of cooling was 840 ℃, and the end temperature of cooling was 300 ℃.
The heat treatment includes a heat process and a cooling process, the peak temperature of the heat process is 1000 ℃, the end temperature of the cooling process is 20 ℃, and the cooling rate of the cooling process is 50 ℃ per second.
The heat treatment also comprises tempering treatment, wherein the tempering treatment comprises tempering heating and tempering cooling, the end temperature of the tempering heating is 350 ℃, the end temperature of the tempering cooling is 50 ℃, and the cooling rate of the tempering cooling is 10 ℃ per second.
Example 7
Example 7 was compared with example 1, and the difference between example 7 and example 1 was:
the thickness of the complex phase steel is 22mm.
The initial temperature of the finish rolling was 1140 ℃, the finish rolling temperature of the finish rolling was 920 ℃, and the rolling pass of the finish rolling was 7 times.
The initial temperature of rough rolling was 1250 ℃, the final temperature of rough rolling was 1180 ℃, and the rolling passes of rough rolling were 7 times.
The end point temperature of heating was 1280 ℃ and the time of heating was 240min.
The initial temperature of cooling was 920 ℃, and the end temperature of cooling was 550 ℃.
The heat treatment includes a heat process and a cooling process, the peak temperature of the heat process is 1200 ℃, the end temperature of the cooling process is 50 ℃, and the cooling speed of the cooling process is 300 ℃ per second.
The heat treatment also comprises tempering treatment, wherein the tempering treatment comprises tempering heating and tempering cooling, the end temperature of the tempering heating is 350 ℃, the end temperature of the tempering cooling is 50 ℃, and the cooling rate of the tempering cooling is 10 ℃ per second.
Comparative example 1
Comparative example 1 was compared with example 1, and the difference between comparative example 1 and example 1 was that:
the steel comprises the following chemical components in percentage by mass:
0.08% of C, 0.02% of Si, 1.00% of Mn, less than or equal to 0.015% of P, less than or equal to 0.005% of S, 0.01% of Alt, 0.20% of Cr, 0.005% of Nb, 0.010% of Ti, 0.0010% of B, and the balance of Fe and unavoidable impurities.
Comparative example 2
Comparative example 2 was compared with example 1, and the difference between comparative example 2 and example 1 was:
the steel comprises the following chemical components in percentage by mass:
0.25% of C, 0.25% of Si, 1.00% of Mn, less than or equal to 0.015% of P, less than or equal to 0.005% of S, 0.55% of Alt, 0.70% of Cr, 0.080% of Nb, 0.05% of Ti, 0.0040% of B, and the balance of Fe and unavoidable impurities.
Related experiments:
The properties of the steel substrates for wheel spokes obtained in examples 1 to 7 and comparative examples 1 to 2 and the complex phase steel for wheel spokes with bosses in the bolt holes after molding were counted, and the results are shown in Table 1.
Test method of related experiment:
metallographic structure detection, namely detecting the metallographic structure on a OLYMPS laser confocal microscope.
Hardness Vickers hardness of each zone was measured using an HVS-10Z type Vickers durometer.
Tensile Strength the tensile property of the test sample was tested using a WE-100 tensile tester.
TABLE 1
Specific analysis of table 1:
The tensile strength refers to the maximum stress value which can be born by the prepared steel matrix before the steel matrix is broken, and the larger the tensile strength is, the larger the maximum stress value which can be born by the steel plate before the steel matrix is broken is.
From the data of examples 1-7, it can be seen that:
If the chemical components of the complex phase steel for the wheel spoke and the corresponding preparation method are adopted, the tensile strength of the steel is improved through adding C and Si, adding Ti element for second phase particle precipitation strengthening, adding Al for solid solution strengthening, adding Nb element for fine crystal strengthening precipitation strengthening and improving the toughness of the steel, and adding B and Cr elements to improve the hardenability of the steel, so that the strength of the steel is comprehensively improved.
From the data of comparative examples 1-2, it can be seen that:
If the chemical components of the complex phase steel for the wheel spoke defined by the application are not adopted and the corresponding technological parameters in the preparation method are matched, the hardness and the tensile strength of the prepared steel are lower or higher than those of the embodiment.
One or more technical solutions in the embodiments of the present application at least have the following technical effects or advantages:
(1) According to the complex phase steel for the wheel spoke, the tensile strength of the steel is improved through the addition of C and Si, the addition of Ti element is carried out for second phase particle precipitation strengthening, the addition of Al is carried out for solid solution strengthening, the addition of Nb element is carried out for fine crystal precipitation strengthening and the toughness of the steel is improved, the addition of B and Cr elements is carried out for improving the hardenability of the steel, and therefore the steel containing ferrite, bainite and martensite can be obtained, and the strength of the steel is effectively improved.
(2) The metallographic structure of the complex-phase steel for the wheel spoke provided by the embodiment of the application comprises 50% -70% of ferrite, 20% -40% of bainite and 5% -15% of martensite, and meanwhile, the yield strength of the complex-phase steel is 600-800 MPa, and the tensile strength of the complex-phase steel is 800-1000 MPa.
(3) The complex phase steel for the wheel spoke provided by the embodiment of the application not only can meet the requirement of complex deformation for preparing the wheel spoke, but also ensures that the wheel spoke has good strength, and meanwhile, the complex phase steel for the wheel spoke with the bolt hole provided with the boss has high hardness, rigidity and other performances, and the running safety performance of an automobile is improved.
(4) According to the method provided by the embodiment of the application, through controlling the process flow, the metallographic structure comprising 50% -70% of ferrite, 20% -40% of bainite and 5% -15% of martensite can be effectively ensured, and the prepared complex phase steel with the bolt holes and bosses for the wheel spokes has the characteristics of high local strength and rigidity, bending fatigue resistance and fretting fatigue resistance, and long service life.
It should be noted that in this document, relational terms such as "first" and "second" and the like are used solely to distinguish one entity or action from another entity or action without necessarily requiring or implying any actual such relationship or order between such entities or actions. Moreover, the terms "comprises," "comprising," or any other variation thereof, are intended to cover a non-exclusive inclusion, such that a process, method, article, or apparatus that comprises a list of elements does not include only those elements but may include other elements not expressly listed or inherent to such process, method, article, or apparatus. Without further limitation, an element defined by the phrase "comprising one does not exclude the presence of other like elements in a process, method, article, or apparatus that comprises an element.
The endpoints and any values of the ranges disclosed herein are not limited to the precise range or value, and are understood to encompass values approaching those ranges or values. For numerical ranges, one or more new numerical ranges may be found between the endpoints of each range, between the endpoint of each range and the individual point value, and between the individual point value, in combination with each other, and are to be considered as specifically disclosed herein.
The foregoing is only a specific embodiment of the invention to enable those skilled in the art to understand or practice the invention. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the generic principles defined herein may be applied to other embodiments without departing from the spirit or scope of the invention. Thus, the present invention is not intended to be limited to the embodiments shown herein but is to be accorded the widest scope consistent with the principles and novel features disclosed herein.

Claims (3)

1. A method of producing a complex phase steel, the method comprising:
Heating, rough rolling, finish rolling, cooling and coiling a plate blank to obtain a high-strength complex phase steel matrix for the wheel spoke, wherein the plate blank comprises the following chemical components:
C:0.09%～0.22%,Si:0.05%～0.20%,Mn:1.20%～1.80%,P≤0.015%,S≤0.005%,Alt:0.02%～0.50%,Cr:0.25%～0.60%,Nb:0.010%～0.060%,Ti:0.015%～0.03%,B:0.0018%～0.0030%, The balance of Fe and unavoidable impurities;
the high-strength complex phase steel for the wheel spoke is deformed, perforated and heat treated to obtain complex phase steel for the wheel spoke with a boss in a bolt hole;
Wherein the end temperature of the heating is 1200-1280 ℃, the time of the heating is 120-240 min, the initial temperature of the cooling is 840-920 ℃, the end temperature of the cooling is 300-550 ℃, the heat treatment comprises heat processing and cooling processing, the peak temperature of the heat processing is 1000-1200 ℃, the end temperature of the cooling processing is 20-50 ℃, the cooling speed of the cooling processing is 50-300 ℃ per second, the heat treatment further comprises tempering treatment, the tempering treatment comprises tempering heating and tempering cooling, the end temperature of the tempering heating is 220-350 ℃, the end temperature of the tempering cooling is 20-50 ℃, and the cooling speed of the tempering cooling is 5-10 ℃ per second;
The metallographic structure of the complex phase steel comprises, by mass, 50% -70% of ferrite, 20% -40% of bainite and 5% -15% of martensite, and the thickness of the complex phase steel is 4-22 mm.
2. The method according to claim 1, wherein the initial temperature of the finish rolling is 1000 ℃ to 1140 ℃, the finish rolling temperature of the finish rolling is 840 ℃ to 920 ℃, and the rolling passes of the finish rolling are 6 times to 7 times.
3. The method according to claim 1, wherein the initial temperature of the rough rolling is 1150 ℃ to 1250 ℃, the final rolling temperature of the rough rolling is 1020 ℃ to 1180 ℃, and the rolling passes of the rough rolling are 5 times to 7 times.
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