CN113981310A - High-fatigue-resistance and high-corrosion-resistance steel for train bogie and preparation method thereof - Google Patents

High-fatigue-resistance and high-corrosion-resistance steel for train bogie and preparation method thereof Download PDF

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CN113981310A
CN113981310A CN202111132825.5A CN202111132825A CN113981310A CN 113981310 A CN113981310 A CN 113981310A CN 202111132825 A CN202111132825 A CN 202111132825A CN 113981310 A CN113981310 A CN 113981310A
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steel
resistance
rolling
fatigue
corrosion
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CN113981310B (en
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冯佳
陈吉清
宋育来
刘志勇
徐进桥
张鹏武
石磊
张扬
骆海贺
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Wuhan Iron and Steel Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite
    • 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
    • Y02T30/00—Transportation of goods or passengers via railways, e.g. energy recovery or reducing air resistance

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

Abstract

The application relates to the technical field of low-alloy high-strength steel, in particular to high-fatigue-resistance and high-corrosion-resistance steel for a train bogie and a preparation method thereof, wherein the high-fatigue-resistance and high-corrosion-resistance steel comprises the following chemical components in percentage by mass: c, Si, Mn, P, S, Cu, Ni, Nb, Mo, Sb, Ca, and the balance of Fe and inevitable impurities; the method comprises the following steps: obtaining molten iron containing the chemical components; sequentially carrying out desulfurization, converter smelting, external refining, continuous casting and hot rolling on the molten iron to obtain high-fatigue-resistance and high-corrosion-resistance steel; the composite effect of Cu, Ni, Sb and Ca added in chemical components is utilized, the low-temperature toughness of Cu and the low-temperature toughness of Ni are utilized to increase the fatigue cracking resistance and corrosion resistance of steel, Sb is utilized to form a compact protective film on the surface of steel, the corrosion resistance of steel is improved, and Ca is utilized to improve the corrosion resistance of steel, so that the steel with high fatigue resistance and high corrosion resistance is obtained.

Description

High-fatigue-resistance and high-corrosion-resistance steel for train bogie and preparation method thereof
Technical Field
The application relates to the technical field of low-alloy high-strength steel, in particular to high-fatigue-resistance high-corrosion-resistance steel for a train bogie and a preparation method thereof.
Background
The bogie is a key component of a high-speed train and directly determines the safety, stability and comfort of the train. The bogie steel is used as a key material, and is required to have excellent comprehensive properties of high strength, high toughness, high weather resistance, easy welding and fatigue resistance, and the failure possibly caused by corrosion and fatigue in the actual service process seriously threatens the safety of trains.
At present, the materials of the high-speed train bogie in China mainly adopt two kinds of weathering resistant steel, namely Japanese-grade SMA490 and European-grade S355J 2W. Although the two steels with the yield strength of 355MPa have better atmospheric corrosion resistance, the corrosion resistance in an acid medium is poorer, and meanwhile, the requirements on fatigue performance are not met. Therefore, how to obtain a train bogie with excellent corrosion resistance and excellent fatigue resistance in an acid medium environment is a technical problem to be solved urgently.
Disclosure of Invention
The application provides high-fatigue-resistance and high-corrosion-resistance steel for a train bogie and a preparation method thereof, which aim to solve the technical problems of low corrosion resistance and low fatigue resistance of the steel for the train bogie in an acid medium environment in the prior art.
In a first aspect, the present application provides a high fatigue resistance and high corrosion resistance steel for a train bogie, wherein the chemical composition of the high fatigue resistance and high corrosion resistance steel comprises the following components by mass fraction: c: 0.03% -0.05%, Si: 0.30-0.50%, Mn: 0.70-1.20%, P is less than or equal to 0.012%, S is less than or equal to 0.003%, Cu: 0.25% -0.55%, Ni: 0.15% -0.40%, Nb: 0.020% -0.050%, Mo: 0.10% -0.20%, Sb: 0.05-0.15%, Ca: 0.0012 to 0.0060 percent of Fe and the balance of inevitable impurities.
Optionally, the metallographic structure of the high fatigue resistance and high corrosion resistance steel comprises 96.23-98.95% of ferrite and 1.05-3.77% of pearlite in volume fraction.
Optionally, the grain size of the ferrite is 11-13 grade.
Optionally, the yield strength of the high-fatigue-resistance and high-corrosion-resistance steel is more than or equal to 450MPa, the tensile strength is more than or equal to 550MPa, the elongation is more than or equal to 22%, the fatigue limit is more than or equal to 330MPa, and the impact energy A isKVNot less than 100J, corrosion rate not more than 0.8g/m2·h。
Optionally, the carbon equivalent of the high fatigue resistance and high corrosion resistance steel satisfies:
CEV＝[C]+[Mn]/6+([Cr]+[Mo]+[V])/5+([Ni]+[Cu])/15≤0.35％，
wherein [ C ] represents the mass fraction of C, [ Mn ] represents the mass fraction of Mn, [ Cr ] represents the mass fraction of Cr, [ Mo ] represents the mass fraction of Mo, [ V ] represents the mass fraction of V, [ Ni ] represents the mass fraction of Ni, [ Cu ] represents the mass fraction of Cu.
In a second aspect, the present application provides a method for preparing a high fatigue resistance and high corrosion resistance steel for a train bogie, the method comprising:
obtaining molten iron containing the chemical components;
sequentially carrying out desulfurization, converter smelting, external refining, continuous casting and hot rolling on the molten iron to obtain high-fatigue-resistance and high-corrosion-resistance steel;
the hot rolling comprises heating before rolling, cooling after rolling and coiling;
the post-rolling cooling comprises: and carrying out laminar cooling after rolling.
Optionally, the molten steel continuous casting includes: carrying out continuous casting of molten steel under the condition of electromagnetic stirring, and then cooling with cooling water;
the superheat degree of the molten steel of the tundish for continuous casting of the molten steel is 10-25 ℃, the drawing speed is 0.9-1.3 m/min, and the soft reduction rate is 2-5%.
Optionally, the consumption of the cooling water and the drawing speed of the molten steel continuous casting satisfy:
Φ＝3.64×103×Vpulling device，
Wherein phi represents the dosage of cooling water, L/min; vPulling deviceThe drawing speed of molten steel continuous casting is shown in m/min.
Optionally, the rolling comprises heating before rolling, rough rolling and finish rolling;
the initial rolling temperature of the rough rolling is more than or equal to 1080 ℃, and the final rolling temperature of the finish rolling is 780-820 ℃;
the rolling also comprises final three-pass rolling, and the cumulative reduction rate of the final three-pass rolling is more than or equal to 25%.
Optionally, the heating end point temperature before rolling is 1140-1200 ℃, and the coiling temperature is 580-620 ℃.
Compared with the prior art, the technical scheme provided by the embodiment of the application has the following advantages:
according to the high fatigue resistance and high corrosion resistance steel for the train bogie, provided by the embodiment of the application, the low-temperature toughness of Cu is utilized to increase the fatigue cracking resistance and corrosion resistance of the steel through the composite effect of Cu, Ni, Sb and Ca added into chemical components, the low-temperature toughness of Ni is utilized to increase the fatigue cracking resistance and corrosion resistance of the steel, Sb is utilized to form a compact protective film on the surface of the steel, the corrosion resistance of the steel is improved, CaO and CaS formed by Ca are utilized, and when the CaO and CaS are dissolved in a thin liquid film on the surface of the steel, the corrosion resistance of the steel is improved, so that the steel with high fatigue resistance and high corrosion resistance is obtained.
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 present invention or the technical solutions in the prior art, the drawings used in the description of the embodiments or the prior art will be briefly described below, and it is obvious for those skilled in the art that other drawings can be obtained according to the drawings without inventive exercise.
Fig. 1 is a schematic flow chart of a preparation method of high fatigue resistance and high corrosion resistance steel for a train bogie according to an embodiment of the present application.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present application clearer, the technical solutions in the embodiments of the present application will be clearly and completely described below with reference to the drawings in the embodiments of the present application, and it is obvious that the described embodiments are some embodiments of the present application, but not all embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present application.
The idea of the invention is as follows: in recent years, in section repair, the phenomenon that the surface corrosion is over-limited is found in more and more welding bogies in the first or second repair period, particularly, main load-bearing parts such as a framework crossbeam and a spring joist of the bogie form a great safety hidden danger, the corrosion of the bogie mainly occurs at positions lower than the ground, paint films are extremely easy to damage due to the impact of flying stones and the like when a vehicle runs at high speed, a passenger department generally uses a strong-acid cleaning agent to clean the outer skin of a vehicle body, so that the corrosion damage of the bogie is aggravated, and in addition, the positions are close to a sewage discharge port, dirt and water are easy to adhere, so that the local severe environment is easy to damage a protective coating, and the corrosion is caused. In addition, the bogie frame is connected with the vehicle body and the wheel set, so that the interaction force between the vehicle body and the wheel set is transmitted, and the load of parts such as a motor, a gear box, a shock absorber and the like mounted on the bogie frame is borne, and the fatigue failure of the bogie is caused by long-term alternate load, so that the bogie frame becomes another great potential safety hazard influencing the safety of the train.
In one embodiment of the application, the high fatigue performance and high corrosion resistance steel for the train bogie comprises the following chemical components in percentage by mass: c: 0.03% -0.05%, Si: 0.30-0.50%, Mn: 0.70-1.20%, P is less than or equal to 0.012%, S is less than or equal to 0.003%, Cu: 0.25% -0.55%, Ni: 0.15% -0.40%, Nb: 0.020% -0.050%, Mo: 0.10% -0.20%, Sb: 0.05-0.15%, Ca: 0.0012 to 0.0060 percent of Fe and the balance of inevitable impurities.
In the application, the positive effect that the mass fraction of C is 0.03-0.05% is to improve the strength of the steel, and the C can react with Nb in the steel to form a precipitation phase to play a role in precipitation strengthening; when the mass fraction is larger than the maximum value of the end point of the range, the adverse effect is that the C content is higher, the elongation and impact toughness of the steel are reduced, the hardening phenomenon can also occur in a welding heat affected zone, the tendency of cracking during welding is aggravated, meanwhile, the corrosion resistance of the steel is reduced due to the excessively high carbon content, and when the mass fraction is smaller than the minimum value of the end point of the range, the adverse effect is that the strength of the steel is insufficient.
The positive effect that the mass fraction of Si is 0.03-0.05% is that the strength of the steel can be improved in a solid solution strengthening mode, a medium-temperature phase transition region can be enlarged, carbide precipitation can be inhibited, the fatigue crack propagation resistance of the steel can be improved, and the corrosion resistance of the steel can be improved; when the mass fraction value is larger than the maximum value of the end point of the range, the adverse effect is that the content of Si is higher at this time, the segregation of the steel plate, the low-temperature toughness and the weldability of the steel plate are seriously deteriorated, and when the mass fraction value is smaller than the minimum value of the end point of the range, the adverse effect is that the strength, the fatigue crack propagation resistance and the corrosion resistance of the steel are insufficient.
The positive effects of 0.70-1.20% of Mn are that the phase transition temperature of austenite transformed into ferrite can be reduced, the austenite area in an iron-carbon phase diagram is enlarged, the medium-temperature structure transformation of steel is promoted, and a uniform microstructure is obtained, so that the steel has excellent corrosion resistance and higher strength; when the mass fraction value is larger than the maximum value of the end point of the range, the resulting adverse effect is that the degree of center segregation is increased, both the corrosion resistance and the fatigue resistance are adverse, and when the mass fraction value is smaller than the minimum value of the end point of the range, the resulting adverse effect is that the strength is insufficient.
The positive effect of P less than or equal to 0.012 percent is that the phosphorus is easy to cause segregation in the steel and has great damage to the impact toughness, the elongation and the fatigue performance of the steel, so the content of the phosphorus is reduced as much as possible and the adverse effect of the phosphorus is reduced.
The positive effect that S is less than or equal to 0.003 percent is that the sulfur is easy to combine with manganese to generate MnS inclusion, which is unfavorable to the impact property, the fatigue property and the corrosion resistance of steel, thereby reducing the sulfur content as much as possible and reducing the adverse effect of phosphorus.
The positive effect that the mass fraction of Cu is 0.25-0.55% is beneficial to obtaining good low-temperature toughness, increasing the fatigue crack propagation resistance of steel and simultaneously obviously improving the corrosion resistance of the steel; when the mass fraction value is larger than the maximum value of the end point of the range, the adverse effect is that the toughness of the welding heat affected zone of the steel plate is reduced, and the phenomenon of copper brittleness is generated in the rolling process of the steel plate.
The positive effects that the mass fraction of Ni is 0.15-0.40% are that the low-temperature toughness of steel can be obviously improved, the risk of generating copper brittleness defects on the surface of copper-containing steel is reduced, and the surface fatigue crack source is reduced, so that the fatigue performance is improved, the notch sensitivity of a product is reduced, and the corrosion resistance of steel can be obviously improved; when the mass fraction is greater than the maximum value at the end of the range, an adverse effect is caused that the addition amount of Ni is excessive, and the excessive Ni increases the production cost because Ni is expensive, and when the mass fraction is less than the minimum value at the end of the range, an adverse effect is caused that the too low Ni content causes the impact toughness, fatigue properties and corrosion resistance of the steel to be insufficient.
The positive effect that the mass fraction of Nb is 0.020-0.050% is that because Nb is the most effective microalloy element, the recrystallization temperature of steel can be improved, the load of a rolling mill is reduced, and meanwhile, the austenite grain size can be effectively refined by inhibiting recrystallization and preventing grain growth, thereby being beneficial to improving the fatigue performance; when the mass fraction is larger than the maximum value of the end point of the range, an excessively high Ni content will result in an excessively high cost, and when the mass fraction is smaller than the minimum value of the end point of the range, an excessively low Nb content will result in insufficient strength and corrosion resistance of the steel.
The positive effect that the mass fraction of Mo is 0.10-0.20% is that Mo exists in solid solution and carbide of steel and has the effect of solid solution strengthening, when Mo and Nb are added simultaneously, Mo can increase the inhibition on austenite recrystallization in the controlled rolling process, and further promote the refinement of austenite microstructure, so that the fatigue performance is improved, and Mo can inhibit the segregation of other elements in grain boundaries, and further improve the fatigue performance of steel; when the mass fraction is greater than the maximum of the end point of the range, an adverse effect will be caused in that an excessively high Mo content will cause an excessively high cost of the steel material, and when the mass fraction is less than the minimum of the end point of the range, an excessively low Mo content will cause an insufficient strength and fatigue property of the steel material.
The positive effect that the mass fraction of Sb is 0.05-0.15% is that a compact protective film can be formed on the surface of steel, and simultaneously, the enrichment of Cu and P elements in a compact inner rust layer is promoted, and the corrosion resistance of the steel is obviously improved; when the mass fraction is larger than the maximum value of the end point of the range, the adverse effect is that Sb is easily enriched in grain boundaries at the time to influence the formability and toughness of the steel, and when the mass fraction is smaller than the minimum value of the end point of the range, the adverse effect is that too low Sb causes insufficient corrosion resistance of the steel.
The active effect that the mass fraction of Ca is 0.0012% -0.0060% is that a trace amount of Ca can form CaO and CaS, when the CaO and CaS are dissolved in a steel surface thin liquid film, the DH value of a corrosion interface is increased, the corrosivity of acid substances in the environment is reduced, a rust layer is promoted to be converted into compact alpha-FeOOH with good protection, and the corrosion resistance of the steel can be obviously improved; when the mass fraction is larger than the maximum value of the end point of the range, an adverse effect will be caused in that excessively high Ca will cause excessively high cost, and when the mass fraction is smaller than the minimum value of the end point of the range, an adverse effect will be caused in that corrosion resistance is insufficient.
As an alternative embodiment, the metallographic structure of the high fatigue resistance and high corrosion resistance steel comprises 96.23-98.95% of ferrite and 1.05-3.77% of pearlite in terms of volume fraction.
In the application, the positive effect that the volume fraction of the pearlite is 1.05-3.77% is that nickel in the range of the volume fraction can enable the steel plate to have good mechanical property and corrosion resistance; when the mass fraction value is larger than the maximum value of the end point of the range, the adverse effect is that the content of pearlite is too large, the strength of the steel is too high, and the elongation, impact toughness and corrosion resistance are insufficient; when the mass fraction is less than the minimum value of the end point of the range, there is a negative effect that the pearlite content is too low, resulting in insufficient strength of the steel material.
As an alternative embodiment, the grain size of the ferrite is 11-13 grades, wherein the grain size is measured according to GB/T6394 Metal average grain size measurement method.
In the application, the positive effect that the grain size of ferrite is 11-13 grade is that the steel has good toughness in the range of the grain size; when the grain size is larger than the maximum value at the end of the range, the adverse effect is high production cost, and when the grain size is smaller than the minimum value at the end of the range, the adverse effect is that grains are coarse at this time, resulting in insufficient strength and toughness of the steel.
As an optional embodiment, the yield strength of the high-fatigue-resistance and high-corrosion-resistance steel is more than or equal to 450MPa, the tensile strength is more than or equal to 550MPa, the elongation is more than or equal to 22 percent, and the fatigue limit is more than or equal to330MPa, impact energy AKVNot less than 100J, corrosion rate not more than 0.8g/m2·h。
As an alternative embodiment, the carbon equivalent of the high fatigue resistance and high corrosion resistance steel satisfies:
CEV＝[C]+[Mn]/6+([Cr]+[Mo]+[V])/5+([Ni]+[Cu])/15≤0.35％，
wherein [ C ] represents the mass fraction of C, [ Mn ] represents the mass fraction of Mn, [ Cr ] represents the mass fraction of Cr, [ Mo ] represents the mass fraction of Mo, [ V ] represents the mass fraction of V, [ Ni ] represents the mass fraction of Ni, [ Cu ] represents the mass fraction of Cu.
In the application, the positive effect that the carbon equivalent CEV is less than or equal to 0.35 percent is that the steel plate has good welding performance; when the carbon equivalent CEV is greater than the maximum of the end of the range, an adverse effect will result in too high CEV indicating insufficient weldability of the steel, and when the carbon equivalent CEV is less than the minimum of the end of the range, an adverse effect will result in too low CEV indicating insufficient strength of the steel.
In one embodiment of the present application, there is provided a method of preparing a high fatigue resistance and high corrosion resistance steel for a train bogie, the method comprising:
s1, obtaining molten iron containing the chemical components;
s2, sequentially carrying out desulfurization, converter smelting, external refining, continuous casting and hot rolling on the molten iron to obtain high-fatigue-resistance and high-corrosion-resistance steel;
the hot rolling comprises heating before rolling, cooling after rolling and coiling;
the post-rolling cooling comprises: and carrying out laminar cooling after rolling.
As an alternative embodiment, the molten steel continuous casting includes:
carrying out molten steel continuous casting in an electromagnetic stirring and forced cooling mode;
the superheat degree of the molten steel of the tundish for continuous casting of the molten steel is 10-25 ℃, the drawing speed is 0.9-1.3 m/min, and the soft reduction rate is 2-5%.
In the application, the positive effect that the superheat degree of the molten steel of the tundish for continuous casting of the molten steel is 10-25 ℃ is that in the temperature range, the center segregation of a casting blank can be reduced, so that the structure distribution of steel is more uniform, and the strength and the hardness are high enough; when the temperature value is greater than the maximum value of the end point of the range, the adverse effect is that the excessive superheat degree aggravates the center segregation of the casting blank, the uniform degree of the structure of the steel is damaged, the strength and the hardness of the steel are influenced, and when the temperature value is less than the minimum value of the end point of the range, the adverse effect is that the excessive superheat degree increases the production difficulty.
The positive effect of the pulling speed of 0.9 m/min-1.3 m/min is that the center segregation of the casting blank can be reduced within the pulling speed range; when the pulling rate is greater than the maximum end value of the range, the adverse effect is that the center segregation of the casting blank is aggravated when the pulling rate of the casting blank is too high, and when the pulling rate is less than the minimum end value of the range, the adverse effect is that the pulling rate of the casting blank is too low, and the production efficiency is reduced.
The soft reduction rate of 2-5% has the positive effects of improving the center segregation and center porosity and improving the fatigue performance of the steel plate; when the value of the light reduction ratio is larger than the maximum value of the end point of the range, the adverse effect that the load of the equipment is too large will be caused, and when the value of the light reduction ratio is smaller than the minimum value of the end point of the range, the adverse effect that the center segregation and the center porosity cannot be effectively prevented will be caused.
As an optional embodiment, the dosage of the cooling water and the drawing speed of the molten steel continuous casting satisfy the following conditions:
Φ＝3.64×103pulling the glass fiber at a temperature of x V,
wherein phi represents the dosage of cooling water, L/min; vPulling deviceThe drawing speed of molten steel continuous casting is shown in m/min.
In the application, the consumption of cooling water and the drawing speed of molten steel continuous casting satisfy phi being 3.64 multiplied by 103×VPulling deviceThe positive effect of the method is that under the limited condition, the casting blank can be kept from generating cracks while the casting blank has enough cooling speed.
As an alternative embodiment, the rolling comprises heating before rolling, rough rolling and finish rolling;
the initial rolling temperature of the rough rolling is more than or equal to 1080 ℃, and the final rolling temperature of the finish rolling is 780-820 ℃;
the rolling also comprises final three-pass rolling, and the cumulative reduction rate of the final three-pass rolling is more than or equal to 25%.
In the application, the positive effect that the initial rolling temperature of rough rolling is more than or equal to 1080 ℃ is that uniform and fine tissues can be obtained in the temperature condition range, and when the temperature value is less than the minimum value of the end point of the range, the adverse effect is that the mixed crystals are generated due to the excessively low temperature.
The finish rolling temperature of the finish rolling is 780-820 ℃, and the positive effects are that the accumulated deformation of the steel plate in an austenite non-recrystallization region can be increased by adopting a lower rolling temperature, the dislocation in the deformed austenite is increased, the fine grain transformation structure is promoted to be obtained, and the strength and the fatigue performance are improved.
The positive effects that the accumulated reduction rate of the final three-pass reduction rolling is more than or equal to 25 percent are grain refinement and strength mechanical property improvement; when the value of the cumulative reduction is larger than the maximum value of the end point of the range, the adverse effect is that the excessive cumulative reduction causes the excessive load of the rolling mill and the steel plate is likely to be cracked, and when the value of the cumulative reduction is smaller than the minimum value of the end point of the range, the adverse effect is that the crystal grains are coarse and the mechanical property is deteriorated.
As an alternative embodiment, the heating end point temperature before rolling is 1140-1200 ℃, and the coiling temperature is 580-620 ℃.
In the application, the positive effect that the heating end temperature before rolling is 1140-1200 ℃ is that the heating temperature is an important factor influencing the fatigue performance, and when Nb element with lower solid solution temperature is selected and the corresponding heating end temperature before rolling is set, the complete solid solution of alloy elements can be ensured, and meanwhile, the defects that austenite crystal grains are too large and thick, precipitates are large and the surface of a steel plate generates copper brittleness due to overhigh heating end temperature before rolling are avoided, so that the adverse influence on the fatigue performance is avoided.
The positive effect that the coiling temperature is 580-620 ℃ is that Nb is more fully precipitated, so that the strength and the fatigue performance are improved; when the temperature is too high or too low, precipitation strengthening effect is affected, and strength and fatigue performance are reduced.
The chemical compositions of each example and comparative example are shown in table 1.
TABLE 1 chemical composition
Figure BDA0003280169780000081
The process parameters in the preparation process of each example are shown in table 2.
TABLE 2 Process parameters
Figure BDA0003280169780000082
Correlation experiments
The steel materials for a bogie obtained in examples 1 to 5 and comparative examples 1 to 2 were subjected to performance tests, and the results of the tests are shown in tables 3 to 5.
The related test method comprises the following steps:
the mechanical property testing method comprises the following steps: according to GB/T228.1 part 1 of the tensile test of metal materials: the test method of the room temperature, the test method of the Charpy pendulum impact of the GB/T229 metal material, the test method of the bending of the GB/T232 metal material and the test method of the rotating bending fatigue of the GB/T4337 metal material are used for carrying out tensile, impact, cold bending and fatigue tests.
The detection method of the microscopic structure comprises the following steps: GB/T6394 Metal average Crystal grain size determination method.
The detection method of periodic infiltration corrosion comprises the following steps: carrying out a periodic infiltration corrosion test according to a weathering steel periodic infiltration corrosion test method for a TB/T2375-93 railway, wherein the solution is 0.01mol/L NaHSO3The temperature is 45 +/-2 ℃, the relative humidity is 70 +/-5 percent, and the test time is 72h, and the results are shown in Table 4.
The detection method of the full-infiltration corrosion comprises the following steps: the full immersion corrosion test is carried out according to JB/T7901-1999 Metal materials laboratory Uniform Corrosion full immersion test method, the temperature is 23 +/-2 ℃, and the H content is 10%2SO4+ 3.5% NaCl solution, and soaking for 24 hr.
The mechanical properties of the steels obtained in the examples and comparative examples are shown in Table 3.
TABLE 3
Figure BDA0003280169780000091
The results of the periodic wet corrosion test of each example and comparative example are shown in table 4.
TABLE 4
Figure BDA0003280169780000092
Figure BDA0003280169780000101
The results of the full immersion corrosion test of each example and comparative example are shown in table 5.
TABLE 5
Figure BDA0003280169780000102
The yield strength refers to the yield limit of the prepared steel when the yield phenomenon occurs, and when the yield strength is higher, the higher the pressure bearing capacity of the steel is
The tensile strength is a critical value of the transition of uniform plastic deformation and local concentrated plastic deformation of the prepared steel, and is also the maximum bearing capacity of the steel under a static stretching condition, and when the tensile strength is higher, the toughness of the steel is better.
The elongation is the percentage of the ratio of the elongation of the original gauge length to the original gauge length of the prepared steel after tensile fracture, and represents that the material is uniformly deformed or stably deformed, and when the elongation is higher, the material quality of the steel is more uniform.
-40℃KV2The steel material has the capacity of absorbing plastic deformation work and fracture work under the action of impact load at the temperature of minus 40 ℃, and the higher the impact work is, the stronger the impact resistance of the steel material is.
The fatigue limit refers to the maximum stress value when the steel is not damaged after infinite stress cycles, and is also called a endurance limit, and when the fatigue limit is higher, the steel is more fatigue-resistant.
Grain size is a measure of the size of the grains, with higher ratings indicating finer grain sizes.
The periodic infiltration corrosion rate refers to the corrosion rate of steel in a periodic infiltration corrosion experiment, and when the periodic infiltration corrosion rate is smaller, the corrosion resistance of the steel is higher.
The relative corrosion rate refers to the corrosion rate of the steel material relative to the blank sample Q345B, and the smaller the relative corrosion rate, the more corrosion resistant the steel material.
The full-immersion corrosion rate refers to the corrosion rate of the steel in a full-immersion corrosion experiment, and when the full-immersion corrosion rate is smaller, the steel is more corrosion-resistant.
From the data of examples 1-6, it can be seen that:
(1) as shown in Table 2, by the composite effect of Cu, Ni, Sb and Ca, and by defining the heating temperature parameter before rolling, the process parameter during rolling, the coiling parameter, the superheat degree of the tundish molten steel, the drawing speed and the soft reduction ratio, steels with different corrosion resistance and fatigue resistance can be obtained.
From the data of comparative examples 1-2, it can be seen that:
(1) the yield strength, tensile strength and fatigue limit data of the conventional SMA490 and S355J2W steels are lower than those of the steels in the examples of the application, and the cycle immersion corrosion and full immersion corrosion data are higher, which shows that the steels in the examples have the characteristics of corrosion resistance and fatigue resistance.
One or more technical solutions in the embodiments of the present application at least have the following technical effects or advantages:
(1) the yield strength of the steel prepared by the method is more than or equal to 450MPa, the tensile strength is more than or equal to 550MPa, the elongation is more than or equal to 22%, and the fatigue limit is more than or equal to 330MPa, so that the mechanical capacity of the steel is excellent, and the steel especially has outstanding fatigue performance.
(2) The corrosion rate of the steel prepared by the embodiment of the application in the periodic infiltration corrosion test relative to Q345B is less than or equal to 50%, and the corrosion rate in the full infiltration corrosion testCorrosion rate less than or equal to 0.8g/m2H, better than the SMA490 steel of comparative example 1 and the S355J2W steel of comparative example 2, demonstrating excellent corrosion resistance in both atmospheric and acidic media environments.
(3) The steel provided by the embodiment of the application also has good welding performance and forming performance, and can obviously improve the safety and prolong the service life of the high-speed train bogie.
(4) According to the embodiment of the application, the steel is ensured to have excellent fatigue performance, sufficient strength, good obdurability and forming performance through the technologies of clean steel smelting, homogenization solidification, solid solution strengthening, structure strengthening, precipitation strengthening, grain refining, surface quality control and the like, so that the safety and the service life of the high-speed train bogie are improved.
(5) The preparation method provided by the embodiment of the application can integrate the technological parameters of molten steel continuous casting, heating before rolling, cooling after rolling and coiling into the production line of the steel for the bogie, and can carry out automatic control, thereby further optimizing and shortening the production process.
It is noted that, in this document, relational terms such as "first" and "second," and the like, may be 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. Also, 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 an … …" does not exclude the presence of other identical elements in a process, method, article, or apparatus that comprises the element.
The foregoing are merely exemplary embodiments of the present invention, which enable those skilled in the art to understand or practice the present 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 (10)

1. The high-fatigue-performance and high-corrosion-resistance steel for the train bogie is characterized by comprising the following chemical components in percentage by mass: c: 0.03% -0.05%, Si: 0.30-0.50%, Mn: 0.70-1.20%, P is less than or equal to 0.012%, S is less than or equal to 0.003%, Cu: 0.25% -0.55%, Ni: 0.15% -0.40%, Nb: 0.020% -0.050%, Mo: 0.10% -0.20%, Sb: 0.05-0.15%, Ca: 0.0012 to 0.0060 percent of Fe and the balance of inevitable impurities.
2. The high fatigue resistance and high corrosion resistance steel according to claim 1, wherein the metallographic structure of the high fatigue resistance and high corrosion resistance steel comprises 96.23 to 98.95% of ferrite and 1.05 to 3.77% of pearlite by volume fraction.
3. The steel of claim 2, wherein the ferrite has a grain size of 11 to 13 grades.
4. The steel of claim 1, wherein the steel has a yield strength of 450MPa or more, a tensile strength of 550MPa or more, an elongation of 22% or more, a fatigue limit of 330MPa or more, and a work of impact AKVNot less than 100J, corrosion rate not more than 0.8g/m2·h。
5. The high fatigue resistance and high corrosion resistance steel as claimed in claim 1, wherein the carbon equivalent of said high fatigue resistance and high corrosion resistance steel satisfies:
CEV＝[C]+[Mn]/6+([Cr]+[Mo]+[V])/5+([Ni]+[Cu])/15≤0.35％，
wherein [ C ] represents the mass fraction of C, [ Mn ] represents the mass fraction of Mn, [ Cr ] represents the mass fraction of Cr, [ Mo ] represents the mass fraction of Mo, [ V ] represents the mass fraction of V, [ Ni ] represents the mass fraction of Ni, [ Cu ] represents the mass fraction of Cu.
6. A method for producing a high fatigue resistance and high corrosion resistance steel as claimed in any one of claims 1 to 5, characterized in that the method comprises:
obtaining molten iron containing the chemical components;
sequentially carrying out desulfurization, converter smelting, external refining, continuous casting and hot rolling on the molten iron to obtain high-fatigue-resistance and high-corrosion-resistance steel;
the hot rolling comprises heating before rolling, cooling after rolling and coiling;
the post-rolling cooling comprises: and carrying out laminar cooling after rolling.
7. The method of claim 6, wherein the continuous casting of the molten steel comprises:
carrying out continuous casting of molten steel under the condition of electromagnetic stirring, and then cooling with cooling water;
the superheat degree of the molten steel of the tundish for continuous casting of the molten steel is 10-25 ℃, the drawing speed is 0.9-1.3 m/min, and the soft reduction rate is 2-5%.
8. The method according to claim 7, wherein the amount of the cooling water and the drawing rate of the molten steel continuous casting satisfy:
Φ＝3.64×103×Vpulling device，
Wherein phi represents the dosage of cooling water, L/min; vPulling deviceThe drawing speed of molten steel continuous casting is shown in m/min.
9. The method of claim 6, wherein said rolling comprises rough rolling and finish rolling;
the initial rolling temperature of the rough rolling is more than or equal to 1080 ℃, and the final rolling temperature of the finish rolling is 780-820 ℃;
the rolling also comprises final three-pass rolling, and the cumulative reduction rate of the final three-pass rolling is more than or equal to 25%.
10. The method according to claim 6, wherein the temperature of the end point of heating before rolling is 1140-1200 ℃ and the temperature of coiling is 580-620 ℃.
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