CN115198196A - Ultrahigh-strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel and preparation method and application thereof - Google Patents

Ultrahigh-strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel and preparation method and application thereof Download PDF

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CN115198196A
CN115198196A CN202210952401.1A CN202210952401A CN115198196A CN 115198196 A CN115198196 A CN 115198196A CN 202210952401 A CN202210952401 A CN 202210952401A CN 115198196 A CN115198196 A CN 115198196A
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steel
percent
niobium
molybdenum
tungsten
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马鸣图
李波
李靖伟
周鹏
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Zhongxin Chongqing Ultra High Strength Material Research Institute Co ltd
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Zhongxin Chongqing Ultra High Strength Material Research Institute 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • 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
    • 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
    • C21D8/0242—Flattening; Dressing; Flexing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/06—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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron

Abstract

The invention relates to the technical field of microalloyed steel, and discloses ultrahigh-strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel, a preparation method and application thereof, wherein the ultrahigh-strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel comprises the following raw materials in percentage by mass: 0.05 to 0.15 percent of tungsten, 0.05 to 0.2 percent of molybdenum, 0.02 to 0.04 percent of niobium and 0.02 to 0.04 percent of vanadium. The tungsten-molybdenum-niobium-vanadium composite microalloyed steel prepared by the scheme has the advantages that the types and the using amounts of metals with higher cost are remarkably reduced, and the mechanical properties of the prepared steel are excellent, such as the yield strength of the steel is not less than 1300MPa, the tensile strength of the steel is not less than 1500MPa, the elongation of the steel is not less than 8%, and the ultimate sharp cooling bend angle of the steel is not less than 65 degrees; the hydrogen-induced delayed fracture resistance is high (the fracture time is more than or equal to 300 hours), and the delayed fracture and the service time of the steel plate are obviously improved. Compared with the wheel made of the existing high-strength steel (the weight is 36-38 kg), the wheel made of the steel grade reduces the weight by 8-10 kg, and has obvious effects of light weight, energy conservation and emission reduction.

Description

Ultrahigh-strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel and preparation method and application thereof
Technical Field
The invention relates to the technical field of microalloyed steel, in particular to ultrahigh-strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel and a preparation method and application thereof.
Background
The increase of the automobile output and the holding capacity brings convenience to the automobile, and simultaneously, the problems of energy consumption, safety, emission and the like are caused. If 2.25-2.5 kilograms of carbon dioxide is discharged when one liter of gasoline is consumed, the energy conservation and emission reduction of the automobile industry are not slow. The light weight of the automobile is an effective means for energy conservation and emission reduction, and energy can be saved by 6-8% when each passenger vehicle loses 10% weight and each commercial vehicle loses 1 ton weight. Based on the fact that the current commercial vehicle accounts for 55% -60% of the oil consumption of the whole automobile, the automobile needs to grab a passenger car and a commercial vehicle for energy conservation and emission reduction. The wheels are important components of commercial vehicles and passenger vehicles, the total number of the wheels of the trailer and the commercial vehicle is about 20, the wheels are tied to the mass below the sprung load, the weight reducing effect of the mass below the sprung load is usually 5-13 times of the mass above the sprung load, and the weight reducing effect is more remarkable, so the weight reduction of the wheels is a more effective means for energy conservation and emission reduction.
Because the steel material is a basic material in the vehicle/wheel manufacturing industry, the steel material has the advantages of adjustable strength, high cost performance and the like, and is beneficial to realizing the requirements of weight reduction and light weight of the wheel.
The prior art CN105121674B discloses a cold-rolled flat steel product for deep drawing applications and a method for its manufacture, the steel produced having a yield point of more than 400MPa, in particular more than 420MPa, and at the same time reaching values above 500MPa, and a tensile strength of more than 500MPa, in particular more than 520MPa, and at the same time reaching values above 600MPa, and an elongation a50 of at least 16%.
However, in the face of increasingly strict requirements for light weight of wheels, the wheels made of the existing high-strength steel plates still have the defects of low yield strength and tensile strength and the like, so that the performance requirements of the wheels can be met only by making the wheels with thicker steel plate thickness by using the existing steel plates, but the requirements for light weight of the wheels cannot be met, for example, the weight of the wheels of a commercial vehicle made of the existing steel plates is 36-38 KG, the total amount of the wheels of a commercial vehicle and a trailer is about 20, so that the total weight of the wheels is 720-760 KG, and the running load of the commercial vehicle is increased. Therefore, the high-strength steel with high yield strength, high tensile strength, high elongation, high ultimate sharp cold bending angle and high hydrogen-induced delayed fracture resistance can make up for the deficiency of the performance of the steel in the market, and has important significance for realizing light weight of the wheel.
Disclosure of Invention
The invention aims to provide ultrahigh-strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel so as to solve the technical problem of low strength of the existing steel.
In order to achieve the purpose, the invention adopts the following technical scheme: the ultrahigh-strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel comprises the following raw materials in percentage by mass: 0.05 to 0.15 percent of tungsten, 0.05 to 0.2 percent of molybdenum, 0.02 to 0.04 percent of niobium and 0.02 to 0.04 percent of vanadium.
The principle and the advantages of the scheme are as follows:
1. compared with the prior art of adding more types of elements to produce steel, the tungsten-molybdenum-niobium-vanadium composite microalloyed steel prepared by the scheme obviously reduces the types and the using amounts of metals with higher cost, fully exerts the characteristics and the effects of the elements of the steel-making raw materials and the tempering resistance stability under the composite effect by optimizing the proportion, and prepares and forms the tungsten-molybdenum-niobium-vanadium composite microalloyed steel with better service performance, wherein the mechanical property yield strength is more than or equal to 1300MPa, the tensile strength is more than or equal to 1500MPa, the elongation is more than or equal to 8 percent, and the ultimate sharp cold bending angle is more than or equal to 65 degrees (tests are carried out according to the test method of ultimate sharp cold bending established by Germany automobile industry society and the standard VDA 238-100).
2. Compared with the steel plate prepared by the prior art, the delayed fracture time of which is less than ten hours (such as 22MnB 5), the steel plate prepared by the scheme is tested by adopting a hydrogen-induced delayed fracture resistance measurement method under constant bending load (a hydrogen-induced delayed fracture sensitivity U-shaped constant bending test method of CSAE-155-2020 ultrahigh-strength automobile steel plate, published and implemented 12-31-2020-year and published by the China society of automotive engineering), the fracture time of the steel plate is more than or equal to 300 hours, and the delayed fracture and the service time of the steel plate are obviously prolonged.
3. According to the scheme, the tungsten-molybdenum-niobium-vanadium composite microalloyed steel prepared by adding multiple composite microalloyed elements can be prepared by adopting lower amount of raw materials under the synergistic effect of the multiple microalloyed elements, so that the tungsten-molybdenum-niobium-vanadium composite microalloyed steel with the grain size of more than or equal to 9-10 grade in a hot rolling state can be prepared, and the raw material cost is obviously reduced; in addition, the multi-component composite microalloying in the scheme fully exerts respective strengthening characteristics and composite strengthening comprehensive effects, and can obtain the advantage integration of various strengthening modes such as fine grain strengthening, precipitation strengthening, solid solution strengthening and the like, so that the steel grade has high hardenability, high wear resistance, high performance stability and high hydrogen-induced delayed fracture resistance, and the performance of the steel is remarkably improved.
Preferably, the feed also comprises the following raw materials in percentage by mass: 0.22 to 0.28 percent of carbon, 0.8 to 1.2 percent of manganese, less than or equal to 0.05 percent of rare earth, more than or equal to 0.02 percent of aluminum, 0.2 to 0.4 percent of chromium, 0.0005 to 0.003 percent of boron, 0.2 to 0.3 percent of silicon, less than or equal to 0.005 percent of sulfur, less than or equal to 0.01 percent of phosphorus, 0.03 to 0.04 percent of titanium and the balance of iron.
The scheme has the advantages that: compared with the prior art of adding more types of elements to produce steel, the tungsten-molybdenum-niobium-vanadium composite microalloyed steel prepared by the scheme obviously reduces the types and the using amounts of metals with higher cost, and fully exerts the characteristics and the effects of all elements of the steel-producing raw materials and the tempering resistance stability under the composite effect by optimizing the proportion to prepare the tungsten-molybdenum-niobium-vanadium composite microalloyed steel with better service performance.
Preferably, the preparation method of the ultrahigh-strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel specifically comprises the following steps:
s1: smelting and casting, namely, mixing the raw materials of the tungsten-molybdenum-niobium-vanadium composite microalloyed steel and then smelting, wherein the smelting process comprises the following steps: molten iron → converter smelting → RH refining → continuous casting → plate blank, and then slowly cooling;
s2: carrying out roll forming, namely heating the plate blank obtained in the step S1 and then carrying out roll forming to obtain a steel plate;
s3: coiling, namely coiling the steel plate obtained in the step S2, and slowly cooling to obtain a steel coil;
s4: and (4) pickling, namely pickling the steel coil obtained in the step (S3), cleaning and drying the steel coil after pickling, and coiling the steel coil into a steel plate coil.
The scheme has the advantages that: under the synergistic effect of multiple microalloying elements, the steel plate prepared by the scheme has shot blasting reinforcement on a sample in a tensile fatigue test with a stress ratio of 0.1, and the cycle number is 2 multiplied by 10 6 ～10 7 The lower fatigue limit is 600 +/-50 MPa, the radial fatigue and bending fatigue life obtained by computer simulation by adopting the fatigue data is more than 150 ten thousand times, and the lightweight effect and the service performance of the steel are both initiated in the world.
Preferably, in S2, the heating temperature is 1230-1320 ℃, and the heating time is 200-250 min.
The scheme has the advantages that: according to the scheme, the raw materials of the tungsten-molybdenum-niobium-vanadium composite microalloyed steel are smelted and cast to form a plate blank, and then the plate blank is heated to 1230-1320 ℃, so that the tungsten-molybdenum-niobium-vanadium composite microalloyed steel with the grain size not less than 9-10 grade in a hot rolling state can be obtained, the grain refinement and the structure uniformity are ensured, the banded structure is reduced, and the directionality of the performance of a steel plate in a rolling state and the formability during manufacturing of spokes and rims are improved.
Preferably, in S2, the rolling start temperature is more than or equal to 1150-1200 ℃, and the finishing temperature is 900-940 ℃.
The scheme has the advantages that: compared with the prior art that the initial rolling temperature is 950-1000 ℃, the initial rolling temperature is more than or equal to 1150-1200 ℃ and the final rolling temperature is 900-940 ℃ so that the grain size of the steel is improved, and meanwhile, the combination of the initial rolling temperature and the final rolling temperature obviously improves the hydrogen diffusion coefficient of the hot formed steel, thereby improving the hydrogen-induced delayed cracking resistance of the steel and further prolonging the fracture time of the steel.
Preferably, in S3, the coiling temperature is 650 to 720 ℃.
The scheme has the advantages that: the steel plate obtained by the preparation is coiled at the coiling temperature, so that the yield strength and tensile strength of the steel are obviously improved.
Preferably, in S3, the thickness of the steel coil is 3 to 14mm.
The scheme has the advantages that: compared with the prior art, the thickness of the steel plate is generally different from 2mm, the thickness of the steel coil in the scheme is 3-14mm, wherein the multi-component composite microalloying fully exerts respective strengthening characteristics and comprehensive functions of composite strengthening, and the advantage integration of various strengthening modes such as fine grain strengthening, precipitation strengthening, solid solution strengthening and the like can be obtained, so that the steel grade has high hydrogen-induced delayed fracture resistance, the brittleness of the steel is obviously reduced, the steel with the thickness of 3-14mm is convenient to manufacture, and the service performance of the steel is further improved.
Preferably, the ultrahigh-strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel is applied to preparation of light commercial vehicle wheels.
The scheme has the advantages that: the wheels are important components of commercial vehicles and passenger vehicles, the total number of the wheels of the trailer of the commercial vehicle is about 20, the wheels are tied to the mass below the sprung load, the weight reducing effect of the mass below the sprung load is usually 5-13 times of the mass above the sprung load, the weight reducing effect is more remarkable, and the weight reduction of the wheels is a more effective means for energy conservation and emission reduction.
Compared with the prior art that only traditional thermal forming boron steel is adopted or niobium and vanadium are added to increase the comprehensive service performance of steel, the scheme adds tungsten, molybdenum, niobium and vanadium to prepare the multi-element composite microalloyed steel for preparing the wheel, so that the wheel has better service performance and fully meets the light weight requirement of the wheel; for example, the strength and toughness matching, the extreme sharp cold bending performance, the hardenability of parts during hot forming quenching, high delayed fracture resistance, fatigue resistance and the like of the wheel under the ultrahigh strength can ensure that the wheel can meet the requirements of high and light weight. The applicant finds that the weight of the wheel prepared by the scheme is reduced by 8-10 kg compared with that of the wheel (the weight is 36-38 kg) made of the existing high-strength steel, the wheel has an obvious light weight effect, and the use reliability is ensured, so that the purposes of energy conservation and emission reduction are achieved.
Drawings
Fig. 1 is a schematic flow chart of a manufacturing process of the ultra-high strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel in example 1 of the invention.
Fig. 2 is a front view of the wheel of the present invention.
Fig. 3 is a radial fatigue behavior displacement simulation diagram of the wheel in embodiment 1 of the present invention.
Fig. 4 is a simulation diagram of the bending fatigue behavior displacement of the wheel in embodiment 1 of the present invention.
Fig. 5 is a simulation diagram of bending fatigue behavior stress of the wheel in embodiment 1 of the present invention.
Fig. 6 is a radial fatigue behavior stress simulation diagram of the wheel in embodiment 1 of the present invention.
FIG. 7 is a heat treatment process diagram of the wheel steel of the present invention.
Fig. 8 is a schematic flow chart of a manufacturing process of the wheel of the present invention.
FIG. 9 is a sectional view showing the penetration of the welded portion between the rim and the spoke in example 1 of the present invention.
Detailed Description
The present invention will be described in further detail with reference to examples, but the embodiments of the present invention are not limited thereto. Unless otherwise indicated, the technical means used in the examples described below are conventional means known to those skilled in the art, the experimental methods used are conventional, and the materials used are commercially available.
The differences in the steel sheet raw material composition and the content in examples 1 to 3 and comparative example 1 (conventional 22MnB 5) are shown in table 1. By taking example 1 as an example, an ultrahigh strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel and a preparation process thereof are described.
Example 1
The ultrahigh-strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel comprises the following raw materials in percentage by weight: 0.05 to 0.15 percent of tungsten (W), 0.05 to 0.2 percent of molybdenum (Mo), 0.02 to 0.04 percent of niobium (Nb), 0.02 to 0.04 percent of vanadium (V), 0.22 to 0.28 percent of carbon (C), 0.8 to 1.2 percent of manganese (Mn), less than or equal to 0.05 percent of rare earth (Re), more than or equal to 0.02 percent of aluminum (Al), 0.2 to 0.4 percent of chromium (Cr), 0.0005 to 0.0035 percent of boron (B), 0.2 to 0.3 percent of silicon (Si), less than or equal to 0.005 percent of sulfur (S), less than or equal to 0.01 percent of phosphorus (P), 0.03 to 0.04 percent of titanium (Ti) and the balance of iron. The embodiment specifically comprises the following raw materials in percentage by weight: 0.15% of tungsten, 0.2% of molybdenum, 0.04% of niobium, 0.04% of vanadium, 0.28% of carbon, 1.2% of manganese, 0.02% of rhenium rare earth alloy (Re), 0.08% of aluminum, 0.3% of chromium, 0.003% of boron, 0.2% of silicon, 0.002% of sulfur, 0.005% of phosphorus, 0.04% of titanium and the balance of iron.
The tungsten-molybdenum-niobium-vanadium composite microalloyed steel prepared in the scheme remarkably reduces the types and the using amounts of metals with higher cost, fully exerts the characteristics and the effects of various elements of steel-making raw materials and the tempering resistance stability under the composite effect by optimizing the proportion, and prepares and forms the tungsten-molybdenum-niobium-vanadium composite microalloyed steel with better service performance, wherein the mechanical property yield strength is more than or equal to 1300MPa, the tensile strength is more than or equal to 1500MPa, the elongation is more than or equal to 8 percent, and the ultimate sharp cooling bend angle is more than or equal to 65 degrees (tests are carried out according to the ultimate sharp cooling test method and the standard VDA238-100 established by the Germany automobile industry society); the fracture time is more than or equal to 300 hours (a hydrogen induced delayed fracture resistance measurement method under constant bending load is adopted, specifically, a hydrogen induced delayed fracture sensitivity U-shaped constant bending test method of the CSAE-155-2020 ultrahigh strength automobile steel plate is published and implemented in 12 and 31 months in 2020 and published by the China society for automotive engineering), and the delayed fracture and the service time of the steel plate are obviously improved.
A manufacturing method of ultrahigh-strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel adopts a flow chart shown in figure 1 to prepare a steel plate according to raw materials of examples 1-3 and a comparative example 1 in a table 1, and comprises the following manufacturing steps:
s1: smelting and casting, namely, mixing the raw materials of the tungsten-molybdenum-niobium-vanadium composite microalloyed steel and then smelting, wherein the smelting process comprises the following steps: molten iron → converter smelting → RH refining → continuous casting → plate blank, and then slowly cooling;
s2: rolling and forming, namely heating the cast plate blank obtained in the step S1 to 1230-1320 ℃ for 200-250 min; then rolling and forming are carried out under the conditions that the initial rolling temperature is more than or equal to 1150-1200 ℃ and the final rolling temperature is 900-940 ℃ to obtain a steel plate with the thickness of 3-14 mm;
s3: coiling, namely heating the steel plate obtained in the step S2 to 650-720 ℃ to finish coiling, and slowly cooling to obtain a steel coil;
s4: pickling, namely pickling the steel coil obtained in the step S3, specifically, carrying out pickling by using hot sulfuric acid, cleaning and drying the steel coil after pickling, and coiling the steel coil into a steel plate coil;
TABLE 1 difference in composition and content of raw materials for steel products in examples 1 to 3 and comparative example 1
Examples W/％ Mo/％ Nb/％ V/％ C/％ Mn/％ Re/％ Al/％ Cr/％ B/％ Si/％ S/％ P/％ Ti/％
Example 1 0.15 0.2 0.04 0.04 0.28 1.2 0.02 0.08 0.3 0.003 0.2 0.002 0.005 0.04
Example 2 0.05 0.1 0.02 0.02 0.22 0.8 0.05 0.02 0.2 0.0005 0.25 0.005 0.007 0.04
Example 3 0.1 0.15 0.03 0.03 0.22 1 0.02 0.05 0.4 0.0015 0.3 0.002 0.005 0.04
Comparative example 1 - - - - 0.24 1 0.02 0.05 0.3 0.0015 0.3 0.002 0.01 0.03
The steels prepared in examples 1 to 3 and comparative example 1 were subjected to a performance test according to the following method:
1) The steel sheets obtained in examples 1 to 3 and comparative example 1 were tested according to the test method and standard for extreme cold bending set by the German society for automotive industry (namely, VDA238 to 100, test specification draft plate binding test for metallic materials, published 12 months 2010); wherein, by tungsten-molybdenum-niobium-vanadium composite micro-alloying, the performance of the steel plate obtained by the scheme after heat treatment is as follows: the yield strength is more than or equal to 1300MPa, the tensile strength is more than or equal to 1500MPa, the elongation is more than or equal to 8 percent, and the ultimate sharp cooling bend angle is more than or equal to 65 degrees;
2) The steel plates obtained in examples 1-3 and comparative example 1 are tested by a hydrogen delayed fracture resistance measurement method under constant bending load (a hydrogen delayed fracture sensitivity U-shaped constant bending quenching test method of a CSAE-155-2020 ultrahigh strength automobile steel plate, which is published and implemented in 12 and 31 months in 2020 and published by the China society for automotive engineering), and the fracture time of the steel plate obtained by the scheme is more than or equal to 300 hours (the existing steel type is fractured in about 10 hours);
3) The steel plate obtained by the scheme has no surface coating, the hardness is 450 +/-9 HV, the tensile strength is 1780MPa, the elongation is 7.5 percent (A50 sample), the fracture toughness K1C is 190MPa.m 1/2 ；
4) The steel sheets obtained in examples 1 to 3 and comparative example 1 were subjected to a tensile fatigue test with a stress ratio of 0.1, and had a fatigue strength of 650. + -. 50MPa, a. DELTA.Kth of 4.5MPa/m and a crack propagation velocity of less than 10 -11 Range of time stress intensity factor, da/dn = A Δ K m (1) In the formula (1), a is the crack length, n is the cycle number, da/dn is the crack propagation rate, A and m are Paris formula constants, and the crack propagation rate can be obtained through experimental data and the formula (1); in the formula (1), Δ K is a stress intensity, and Δ K can be calculated from the linear elastic fracture mechanics by the formula (2): Δ K = Y Δ σ/(π a) (2), for which steel type a is 1.65 × 10 ﹣11 M is 2.52, y =1.13, which is the size factor.
The results of the performance tests obtained according to the above method are shown in table 2:
TABLE 2 results of testing the properties of the steel sheets obtained in examples 1 to 3 and comparative example 1
Figure BDA0003789730180000071
Experimental data show that compared with the comparative general hot forming steel (comparative example 1), the tungsten-molybdenum-niobium-vanadium multi-element composite microalloyed steel (examples 1 to 3) developed by the scheme has good toughness, high hydrogen-induced delayed fracture resistance and high fatigue life. The performance of the tungsten-molybdenum-niobium-vanadium micro alloy steel is far superior to that of general 22MnB5 hot forming steel (comparative example 1), which shows that in the tungsten-molybdenum-niobium-vanadium micro alloy steel prepared by the scheme, four elements of tungsten, molybdenum, niobium and vanadium are mutually synergistic, the strengthening characteristics of each element and the comprehensive effect of composite strengthening are fully exerted, and the advantage integration of various strengthening modes such as fine grain strengthening, precipitation strengthening, solid solution strengthening and the like can be obtained, so that the steel has the characteristics of high hardenability, high wear resistance, high performance stability and the like.
This scheme still provides the application of super high strength tungsten molybdenum niobium vanadium composite microalloyed steel in preparing lightweight commercial car wheel, and wherein the wheel includes fixed connection's rim and spoke, and this embodiment specifically is rim and spoke welding, and rim and spoke are made by above-mentioned super high strength tungsten molybdenum niobium vanadium composite microalloyed steel, and the wheel structure of making is as shown in figure 2, and the steel sheet that this scheme was prepared shows fatigue life 2X 10 of 600 50MPa in the tensile fatigue experiment that the stress ratio is 0.1 6 And finally, performing computer simulation on the prepared wheel by adopting the fatigue data to obtain the radial fatigue and bending fatigue life of the wheel which is more than 150 ten thousand times, so that the service life requirement of the wheel is met, and comparing with the relevant experimental test result of the steel grade in the prior art, the lightweight effect and excellent performance of the steel grade for the wheel prepared by the scheme are far beyond the prior art level (comparative example 1) and reach the world leading level.
Specifically, the structure of the wheel is shown in fig. 2, the radial stiffness of the wheel is shown in fig. 3, the bending stiffness of the wheel is shown in fig. 4, the bending fatigue simulation result of the wheel is shown in fig. 5, and the radial fatigue simulation result of the wheel is shown in fig. 6; the wheel is made to this scheme of adoption gained steel, fully provided wheel life requirement to be applicable to more and make high performance lightweight commercial car wheel, the material requirement of fully provided high performance lightweight wheel.
The heat treatment process range shown in FIG. 7 and the process flow for manufacturing the rim and the spoke and manufacturing the wheel assembly shown in FIG. 8 are adopted to prepare the wheel by using the steel materials obtained in the examples 1 to 3 and the comparative example 1, and the manufacturing of the rim and the spoke and the manufacturing of the wheel assembly are specifically carried out according to the following steps:
rim and spoke manufacturing stage
S5: pre-forming, namely cutting a steel plate blank according to the size of the materials required by the rim and the spoke, and pre-forming the steel plate blank into a rim and spoke blank according to the shapes of the rim and the spoke;
s6: hot forming, namely hot stamping the rim and spoke blank obtained in the step S5 into a rim and spoke product, and further modifying the surface of the product into a finished product; heating the rim blank obtained in the step S5 to 900 ℃, preserving heat for 4-8 min, transferring the rim blank into a hot forming die, closing the die by a press, introducing water for cooling, and performing water passage water introduction cooling or PAG spray cooling on the outside by adopting a special profiling module; stopping cooling when the cooling temperature is controlled to be 200 ℃, and then demoulding and cooling at room temperature to obtain the rim; the spoke thermoforming step comprises: and (4) heating the spoke blank obtained in the step (3) to 900 ℃, keeping the temperature for 8-15 min, transferring the spoke blank into a hot forming die within 5 seconds, closing the die by a press, and introducing water for cooling and quenching to obtain the spoke.
The hot forming process adopted by the scheme enables the austenite structure in the blank to be converted into the martensite structure, and the addition of the tungsten, molybdenum, niobium and vanadium elements increases the hardenability of the steel plate and reduces the critical cooling rate of the quenched martensite conversion, so that the cooling rate of the quenched full martensite is reduced, the heating process parameter window before hot forming is widened, and the hot forming process has stronger adaptability to industrial mass production. The hardness of the conical surface part after the spoke is hot-formed is more than or equal to HRC 45-50, and the plane part of the screw hole is controlled at HRC 42-46 according to the use requirement. Different parts of the same spoke have different hardness distributions, namely flexible distributions, so that the toughness requirements of different parts of the same spoke are met.
(III) wheel Assembly manufacturing stage
S7: assembling, namely assembling the rim and the spoke obtained in the step S7, and assembling the rim and the spoke into a hot-formed wheel, namely sleeving the rim on the large-diameter end part of the peripheral wall of the spoke, wherein the rim and the spoke are in interference fit, the interference magnitude between the outer diameter of the peripheral wall of the spoke and the inner diameter of the matched surface of the rim is less than or equal to 1mm, and the rim and the spoke are subjected to laser welding to form the wheel; the welding is to adopt laser welding to carry out circumferential full welding on the matching surfaces of the rim and the spoke, the power of a laser is selected to be 5-11 kilowatts, and the laser welding speed is 2-4 m/min.
Parameters of the welded weld joint and the heat affected zone meet the following conditions: the welding width of the welding is 1-3 mm, the fusion depth is more than or equal to 4mm, and the width of the heat affected zone is less than or equal to 0.5mmm, and the parameters show that the welding process used in the scheme obviously improves the welding effect and the strength of the welding surface of the wheel, and improves the fatigue life of the wheel; the sectional view of the wheel welding penetration of the embodiment is specifically shown in fig. 9, and the parameters of the welded seam and the heat affected zone are specifically: the weld penetration is 5.68mm, the weld width is 1.11mm, and the gap of the center of the weld of the welding surface deviating from the joint surface of the spoke rim is 0.25mm.
Thereby with the great intensity that leads to welding seam district rim and spoke of the heat affected zone of present general welding mode butt weld, it is different to reduce the fatigue life of connection effect and wheel, and this scheme adopts laser welding's mode to carry out the circumference full weld, and dedicated welding process makes the wheel that makes realize the stable connection of wheel when satisfying the welding department intensity, promotes the life of wheel.
S8: modifying, namely further processing and modifying the surface of the wheel obtained in the step S8, wherein the modifying comprises a shot peening strengthening process of the wheel, the shot diameter of shot peening is 0.4-0.7 mm to 60 percent, the shot diameter of shot peening is 0.8-1.0 mm to 40 percent, the shot flow is 140kg/min, the rotating speed of a shot peening impeller is 2500 revolutions per minute, the shot peening time is 80-120 seconds, the shot peening coverage rate is more than or equal to 98 percent, the shot peening strength is 0.6-0.72 according to the measured value of the deformation of an A test piece (Arman) in the standard of SAEJ441, 442a, J443 and 1980, a finished product of a commercial vehicle (22.5 multiplied by 9.00) is obtained, and the obtained wheel is weighed, and on the premise of meeting the service performance of the wheel, the weight of the wheel obtained in the embodiment 1-3 of the scheme is 27-28 kg (the weight of the wheel in the comparative example 1 is 32 kg, and the steel spoke of the wheel hardly meets the hardenability requirement during hot forming quenching), thereby obviously reducing the weight of the wheel compared with the common ultrahigh-strength steel spoke of the wheel (usually 36-38 kg) while meeting the technological performance of the wheel in the service performance of the prior art, obviously reducing the wheel, and realizing the overall energy-saving and reducing the emission and reducing the overall emission; and the excellent performance of the wheel steel grade prepared by the scheme is far beyond the prior art level (comparative example 1) and reaches the world leading level.
The foregoing is merely an example of the present invention and common general knowledge in the art of designing and/or characterizing particular aspects and/or features is not described in any greater detail herein. It should be noted that, for those skilled in the art, without departing from the technical solution of the present invention, several variations and modifications can be made, which should also be regarded as the protection scope of the present invention, and these will not affect the effect of the implementation of the present invention and the practicability of the patent. The scope of the claims of the present application shall be defined by the claims, and the description of the embodiments and the like in the specification shall be used to explain the contents of the claims.

Claims (8)

1. The ultrahigh-strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel is characterized in that: the material comprises the following raw materials in percentage by mass: 0.05 to 0.15 percent of tungsten, 0.05 to 0.2 percent of molybdenum, 0.02 to 0.04 percent of niobium and 0.02 to 0.04 percent of vanadium.
2. The ultra-high strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel as claimed in claim 1, wherein: the material also comprises the following raw materials in percentage by mass: 0.22 to 0.28 percent of carbon, 0.8 to 1.2 percent of manganese, less than or equal to 0.05 percent of rare earth, more than or equal to 0.02 percent of aluminum, 0.2 to 0.4 percent of chromium, 0.0005 to 0.0035 percent of boron, 0.2 to 0.3 percent of silicon, less than or equal to 0.005 percent of sulfur, less than or equal to 0.01 percent of phosphorus, 0.03 to 0.04 percent of titanium and the balance of iron.
3. The preparation method of the ultrahigh-strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel of any one of claims 1 to 2, characterized by comprising the following steps of: the method specifically comprises the following steps:
s1: smelting and casting, namely, mixing the raw materials of the tungsten-molybdenum-niobium-vanadium composite microalloyed steel and then smelting, wherein the smelting process comprises the following steps: molten iron → converter smelting → RH refining → continuous casting → plate blank, and then slowly cooling;
s2: carrying out roll forming, namely heating the plate blank obtained in the step S1 and then carrying out roll forming to obtain a steel plate;
s3: coiling, namely coiling the steel plate obtained in the step S2, and slowly cooling to obtain a steel coil;
s4: and (4) pickling, namely pickling the steel coil obtained in the step (S3), cleaning and drying the steel coil after pickling, and coiling the steel coil into a steel plate coil.
4. The method for preparing the ultra-high strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel according to claim 3, characterized in that: in S2, the slab heating temperature is 1230-1320 ℃, and the slab heating time is 200-250 min.
5. The method for preparing the ultra-high strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel according to claim 4, characterized in that: in S2, the rolling start temperature is more than or equal to 1150-1200 ℃, and the finishing temperature is 900-940 ℃.
6. The preparation method of the ultrahigh-strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel according to claim 5, characterized in that: in S3, the coiling temperature is 650-720 ℃.
7. The ultrahigh-strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel as claimed in claim 6, and the preparation method and the application thereof are characterized in that: in S3, the thickness of the steel coil is 3-14mm.
8. The use of the ultra-high strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel defined in any one of claims 1-2 in the preparation of light weight commercial vehicle wheels.
CN202210952401.1A 2022-08-09 2022-08-09 Ultrahigh-strength tungsten-molybdenum-niobium-vanadium composite microalloyed steel and preparation method and application thereof Pending CN115198196A (en)

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Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2007211334A (en) * 2006-02-13 2007-08-23 Sumitomo Metal Ind Ltd High-tensile hot-rolled steel sheet and its manufacturing method
CN104195443A (en) * 2014-05-19 2014-12-10 首钢总公司 High-flexural-behavior hot-formed steel used for automobiles and manufacturing method thereof
CN111235483A (en) * 2020-03-12 2020-06-05 中国汽车工程研究院股份有限公司 Niobium-vanadium composite microalloyed hot forming steel and production and hot stamping forming method thereof

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2007211334A (en) * 2006-02-13 2007-08-23 Sumitomo Metal Ind Ltd High-tensile hot-rolled steel sheet and its manufacturing method
CN104195443A (en) * 2014-05-19 2014-12-10 首钢总公司 High-flexural-behavior hot-formed steel used for automobiles and manufacturing method thereof
CN111235483A (en) * 2020-03-12 2020-06-05 中国汽车工程研究院股份有限公司 Niobium-vanadium composite microalloyed hot forming steel and production and hot stamping forming method thereof

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