CN113930669A - HB 450-grade conditioning-free wear-resistant steel for self-discharging carriage body and production method thereof - Google Patents
HB 450-grade conditioning-free wear-resistant steel for self-discharging carriage body and production method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 64
- 239000010959 steel Substances 0.000 title claims abstract description 64
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 24
- 238000007599 discharging Methods 0.000 title claims abstract description 7
- 238000000034 method Methods 0.000 claims abstract description 28
- 239000000126 substance Substances 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 5
- 238000005096 rolling process Methods 0.000 claims description 84
- 238000001816 cooling Methods 0.000 claims description 51
- 238000010438 heat treatment Methods 0.000 claims description 30
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 12
- 238000003723 Smelting Methods 0.000 claims description 8
- 238000009489 vacuum treatment Methods 0.000 claims description 7
- 229910001566 austenite Inorganic materials 0.000 claims description 5
- 238000005516 engineering process Methods 0.000 claims description 5
- 229910052742 iron Inorganic materials 0.000 claims description 5
- 238000007670 refining Methods 0.000 claims description 5
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 4
- 239000011575 calcium Substances 0.000 claims description 4
- 238000005266 casting Methods 0.000 claims description 4
- 238000001953 recrystallisation Methods 0.000 claims description 4
- 230000002441 reversible effect Effects 0.000 claims description 4
- 238000005204 segregation Methods 0.000 claims description 4
- 238000007664 blowing Methods 0.000 claims description 3
- 238000009749 continuous casting Methods 0.000 claims description 3
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 claims description 2
- 229910000604 Ferrochrome Inorganic materials 0.000 claims description 2
- 229910000592 Ferroniobium Inorganic materials 0.000 claims description 2
- 229910001200 Ferrotitanium Inorganic materials 0.000 claims description 2
- 229910052786 argon Inorganic materials 0.000 claims description 2
- 229910052791 calcium Inorganic materials 0.000 claims description 2
- 230000003009 desulfurizing effect Effects 0.000 claims description 2
- 238000005098 hot rolling Methods 0.000 claims description 2
- 238000003825 pressing Methods 0.000 claims description 2
- 238000010079 rubber tapping Methods 0.000 claims description 2
- 239000002893 slag Substances 0.000 claims description 2
- 239000011593 sulfur Substances 0.000 claims description 2
- 238000010791 quenching Methods 0.000 abstract description 9
- 230000000171 quenching effect Effects 0.000 abstract description 9
- 238000005496 tempering Methods 0.000 abstract description 5
- 229910045601 alloy Inorganic materials 0.000 abstract description 3
- 239000000956 alloy Substances 0.000 abstract description 3
- 238000003466 welding Methods 0.000 abstract 1
- 230000000052 comparative effect Effects 0.000 description 10
- 239000000463 material Substances 0.000 description 5
- 238000005299 abrasion Methods 0.000 description 4
- 229910000734 martensite Inorganic materials 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
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- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 238000005275 alloying Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- 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
- C22C33/06—Making ferrous alloys by melting using master alloys
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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
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
The invention discloses HB450 grade conditioning-free wear-resistant steel for a self-discharging carriage body and a production method thereof, wherein the steel comprises the following chemical components in percentage by weight: 0.19-0.22%, Si: 0.30-0.50%, Mn: 1.35-1.55%, P: less than or equal to 0.012%, S: less than or equal to 0.003 percent, Nb: 0.015-0.035%, Ti: 0.010-0.030%, Cr: 0.30-0.50%, B: 0.0005-0.0015%, Al: 0.020-0.050%, H: 2ppm or less, O: less than or equal to 30ppm, N: less than or equal to 50ppm, and the balance of Fe and inevitable impurities. The wear-resistant steel has good forming, welding and wearing properties, simple alloy elements, short process flow and greatly reduced production cost, and does not need off-line quenching and tempering treatment.
Description
Technical Field
The invention relates to the field of wear-resistant steel, in particular to HB 450-grade quality-adjustment-free wear-resistant steel for a self-discharging carriage body and a production method thereof.
Background
With the trend of light weight development, higher requirements are put on the load and fuel consumption of vehicles, and light weight, safety and reliability become key development directions. At present, the dumper carriage body is made of materials with the strength of 520-750MPa, and the requirements for light weight cannot be met, so that the steel for the dumper carriage body turns to thin-specification wear-resistant steel, the material thickness can be effectively reduced while the strength is improved, the weight of the dumper carriage body is reduced by more than 30%, the dynamic property of an automobile is improved, the fuel consumption is reduced, the exhaust pollution is reduced, and the environment-friendly, economic and social benefits are remarkable. The price of the wear-resistant steel plate is improved compared with that of the existing material, but the cost performance of the wear-resistant steel plate is far higher than that of the existing material by comprehensively considering the service life, the maintenance cost, the spare part cost, the parking loss and the like of the product.
The traditional production process of the wear-resistant steel adopts an off-line heat treatment (quenching and tempering) process after rolling, the matrix structure of the process is lath martensite, high strength and hardness are obtained, but the martensite has high brittleness, the process is long in flow, the requirement on heat treatment equipment is high, the cost is high, the production efficiency is low, the yield cannot meet the market demand, and a lot of obstacles are increased for popularization and application of thin-specification high-strength wear-resistant steel.
Therefore, the application of the short-process online quenching and tempering-free process technology in the production of wear-resistant steel is an important research and development direction, the controlled rolling and cooling online quenching technology is adopted, a ferrite and metastable austenite composite soft phase structure is introduced to a harder martensite matrix, the toughness and plasticity and the formability are increased, and the wear-resistant steel with low cost, high performance, good plate shape and excellent machinability is produced.
Patent publication No. CN 110964979A discloses a wear-resistant steel for a dumper carriage body with good formability and a production method thereof, and patent publication No. CN 112048672A discloses a HB 450-grade high-wear-resistant thin steel plate and a production method thereof, wherein the two methods both adopt an off-line heat treatment process after rolling, the process flow is long, and the production cost is high.
Disclosure of Invention
Aiming at the problems that the prior wear-resistant steel adopts an offline heat treatment (quenching and tempering) process, the production flow is long, the requirement on heat treatment equipment is high, and the cost is high, the invention aims to provide the short-flow non-quenched and tempered HB450 grade wear-resistant steel and the production method thereof, the alloy elements are simple, the offline quenching and tempering treatment is not needed, the process flow is short, and the production cost is greatly reduced.
In order to solve the technical problems, the invention adopts the following technical scheme:
an HB450 grade conditioning-free wear-resistant steel for a self-discharging carriage body comprises the following chemical components in percentage by weight: 0.19-0.22%, Si: 0.30-0.50%, Mn: 1.35-1.55%, P: less than or equal to 0.012%, S: less than or equal to 0.003 percent, Nb: 0.015-0.035%, Ti: 0.010-0.030%, Cr: 0.30-0.50%, B: 0.0005-0.0015%, Al: 0.020-0.050%, H: 2ppm or less, O: less than or equal to 30ppm, N: less than or equal to 50ppm, and the balance of Fe and inevitable impurities.
A production method of HB450 grade quality-adjustment-free wear-resistant steel for a self-discharging carriage body comprises the following process routes:
smelting: molten iron pretreatment, converter top and bottom combined blowing smelting, LF external refining, RH vacuum treatment, slab continuous casting, stacking and slow cooling rolling: heating a plate blank, descaling by high-pressure water, rough rolling by E1R1, rough rolling by E2R2, flying shear, descaling by high-pressure water, finish rolling by F1-F7, cooling by dense laminar flow, coiling, marking and warehousing;
the main process comprises the following steps:
1) smelting and casting
The KR method is adopted to desulfurize molten iron and high-quality scrap steel in the smelting process, and the S content of the molten iron fed into the converter is ensured to be less than or equal to 0.003 percent; when smelting in a converter, adopting self-produced low-sulfur scrap steel, wherein the tapping temperature is more than or equal to 1620 ℃; the LF refining adopts large slag amount for slagging and desulfurizing, the S is ensured to be less than or equal to 0.003 percent, ferrochromium and ferrocolumbium are added in the refining process, the RH vacuum treatment time is more than 20min, and ferrotitanium and ferroboron are added in the vacuum treatment process; carrying out calcium treatment on the molten steel after vacuum treatment, wherein the content of Ca is 0.0010-0.0030%, and the soft blowing time of argon is more than 12min, so that impurities are fully denatured and float; the whole process is protected to pour when the slab is continuously cast, the superheat degree is controlled at 15-30 ℃, the drawing speed is 0.90-1.10m/min, and technologies such as dynamic light pressing are adopted to reduce the center segregation of the continuous casting slab, wherein the center segregation of the casting slab is not more than C3.0 level, and the center porosity is not more than 2.0 level;
2) heating and rolling
The slab heating adopts a stepping heating furnace, the heating temperature is 1190 and 1230 ℃, the heating time is more than or equal to 120min, and the temperature uniformity of the steel slab is ensured; the manufacturing process is controlled to be carried out in two stages of hot rolling, all the stages are longitudinal rolling, the first stage is austenite recrystallization zone rolling, namely a rough rolling stage, the rough rolling is carried out for 3+5 times by adopting an R1 two-roller horizontal reversible rolling mill and an R2 four-roller horizontal reversible rolling mill, and the thickness of an intermediate billet is 40-50 mm; the second stage is rolling in an austenite non-recrystallization region, namely a finish rolling stage, wherein the finish rolling is performed by adopting a seven-stand four-roller finish rolling unit, the rolling speed is constant, the start rolling temperature of the finish rolling is 980-;
3) cooling down
And after the controlled rolling is finished, the steel strip enters a dense laminar cooling area, the cooling mode is two-stage cooling, the front section adopts dense rapid cooling, the cooling temperature is 600-.
Further, the heating temperature of the plate blank is 1200 ℃, the heating time is 120min, the rough rolling is performed for 3+5 times by adopting R1 and R2, the finish rolling start temperature is 1000 ℃, the finish rolling temperature is 850 ℃, the steel strip enters a laminar flow cooling device after the rolling is finished, the cooling mode is two-section cooling, the front section is encrypted and rapidly cooled to 610 ℃, and the steel strip is rapidly cooled to 100 ℃ after air cooling and coiled.
Further, the heating temperature of the plate blank is 1210 ℃, the heating time is 130min, the rough rolling is performed for 3+5 times by adopting R1 and R2, the initial rolling temperature of the finish rolling is 1020 ℃, the final rolling temperature is 830 ℃, the steel strip enters a laminar cooling device after the rolling is finished, the cooling mode is two-section cooling, the front section is encrypted and rapidly cooled to 630 ℃, and the steel strip is rapidly cooled to 150 ℃ after air cooling and coiled.
Further, the heating temperature of the plate blank is 1200 ℃, the heating time is 120min, the rough rolling is performed for 3+5 times by adopting R1 and R2, the initial rolling temperature of the finish rolling is 1010 ℃, the final rolling temperature is 870 ℃, the steel strip enters a laminar cooling device after the rolling is finished, the cooling mode is two-section cooling, the front section is encrypted and rapidly cooled to 650 ℃, and the steel strip is rapidly cooled to 200 ℃ after air cooling and coiled.
Compared with the prior art, the invention has the beneficial technical effects that:
according to the invention, the thin-specification conditioning-free HB 450-grade wear-resistant steel coil is produced by low-alloy component design, the TMCP online quenching technology and the two-stage cooling process, the technical difficulty of toughness matching under high hardness is broken through, accurate regulation and control of an online complex phase structure are realized, a ferrite soft phase structure is introduced on a harder martensite matrix, the toughness and plasticity and formability are increased, the straightness of the steel coil after being uncoiled and straightened is less than 5mm/1m, and the steel coil is applied to a dump truck carriage, the thickness of the material is reduced, and the light weight is realized. The problems of long production process flow, high requirement on heat treatment equipment, high production cost and low efficiency of the thin-specification wear-resistant steel are effectively solved, and a larger space is created for the low-cost high-benefit production of the thin-specification wear-resistant steel.
Drawings
The invention is further illustrated in the following description with reference to the drawings.
FIG. 1 is a metallographic structure of a wear-resistant steel according to example 1 of the present invention.
Detailed Description
The present invention is described in more detail by the following examples, which are merely illustrative of the best mode of carrying out the invention and do not limit the scope of the invention in any way.
Example 1
The chemical components are shown in the weight percentage in table 1. The heating temperature of the plate blank is 1200 ℃, and the heating time is 120 min. And (3) carrying out 3+5 times of rolling on the rough rolling by adopting R1 and R2, wherein the initial rolling temperature of the finish rolling is 1000 ℃, the final rolling temperature is 850 ℃, the steel strip enters a laminar cooling device after the rolling is finished, the cooling mode is two-section cooling, the front section is encrypted and rapidly cooled to 610 ℃, and the steel strip is rapidly cooled to 100 ℃ after air cooling and coiled to obtain the steel strip.
Example 2
The chemical components are shown in the weight percentage in table 1. The heating temperature of the plate blank is 1210 ℃, and the heating time is 130 min. And (3) carrying out 3+5 times of rolling by adopting R1 and R2 in rough rolling, wherein the initial rolling temperature of finish rolling is 1020 ℃, the final rolling temperature is 830 ℃, the steel strip enters a laminar cooling device after the rolling is finished, the cooling mode is two-section cooling, the front section is encrypted and rapidly cooled to 630 ℃, and the steel strip is rapidly cooled to 150 ℃ after air cooling and coiled to obtain the steel strip.
Example 3
The chemical components are shown in the weight percentage in table 1. The heating temperature of the plate blank is 1200 ℃, and the heating time is 120 min. And (3) carrying out 3+5 times of rolling on the rough rolling by adopting R1 and R2, wherein the initial rolling temperature of the finish rolling is 1010 ℃, the final rolling temperature is 870 ℃, the steel strip enters a laminar cooling device after the rolling is finished, the cooling mode is two-section cooling, the front section is encrypted and rapidly cooled to 650 ℃, and the steel strip is rapidly cooled to 200 ℃ after air cooling and coiled to obtain the steel strip.
The chemical compositions of examples 1-3 of the present invention and comparative examples 1-2 are shown in Table 1.
TABLE 1 chemical composition (wt%) of inventive examples 1-3 and comparative examples 1-2
The preparation processes of examples 1-3 of the present invention and comparative examples 1-2 are shown in Table 2.
TABLE 2 preparation Processes of examples 1-3 of the present invention and comparative examples 1-2
The properties of inventive examples 1-3 and comparative examples 1-2 are shown in Table 3.
TABLE 3 mechanical Properties of inventive examples 1-3 and comparative examples 1-2
The abrasion wear tests of the abrasion wear steels in the examples 1 to 3 were carried out by using an MLS-225 type wet rubber wheel abrasion wear tester, wherein the normal load applied to the test piece in the test process was 70N, the rubber wheel rotation speed was 250r/min, the pre-grinding friction stroke was 1000r, the finish grinding friction stroke was 2000r, the abrasion loss was about 0.045g, and the difference from the comparative example was not large.
As can be seen from the above table, in examples 1-3, the alloying elements are mainly Nb, Ti and B, the total amount of Nb and Ti is not much different, and the B content is higher in examples 1-2, compared with comparative examples 1-2. The examples 1-3 adopt TMCP on-line quenching process, the comparative examples 1-2 adopt TMCP + heat treatment (quenching + tempering) process, the process flow is long, and the cost is high. The tensile strength, impact strength and hardness of the steel are higher than those of comparative examples 1-2, and the steel has better performance.
The above-described embodiments are merely illustrative of the preferred embodiments of the present invention, and do not limit the scope of the present invention, and various modifications and improvements of the technical solutions of the present invention can be made by those skilled in the art without departing from the spirit of the present invention, and the technical solutions of the present invention are within the scope of the present invention defined by the claims.
Claims (5)
1. The HB 450-grade conditioning-free wear-resistant steel for the self-discharging carriage body is characterized by comprising the following chemical components in percentage by weight: 0.19-0.22%, Si: 0.30-0.50%, Mn: 1.35-1.55%, P: less than or equal to 0.012%, S: less than or equal to 0.003 percent, Nb: 0.015-0.035%, Ti: 0.010-0.030%, Cr: 0.30-0.50%, B: 0.0005-0.0015%, Al: 0.020-0.050%, H: 2ppm or less, O: less than or equal to 30ppm, N: less than or equal to 50ppm, and the balance of Fe and inevitable impurities.
2. The method for producing the HB450 grade no-conditioning wear-resistant steel for the dump body of claim 1, comprising:
1) smelting and casting
The KR method is adopted to desulfurize molten iron and high-quality scrap steel in the smelting process, and the S content of the molten iron fed into the converter is ensured to be less than or equal to 0.003 percent; when smelting in a converter, adopting self-produced low-sulfur scrap steel, wherein the tapping temperature is more than or equal to 1620 ℃; the LF refining adopts large slag amount for slagging and desulfurizing, the S is ensured to be less than or equal to 0.003 percent, ferrochromium and ferrocolumbium are added in the refining process, the RH vacuum treatment time is more than 20min, and ferrotitanium and ferroboron are added in the vacuum treatment process; carrying out calcium treatment on the molten steel after vacuum treatment, wherein the content of Ca is 0.0010-0.0030%, and the soft blowing time of argon is more than 12min, so that impurities are fully denatured and float; the whole process is protected to pour when the slab is continuously cast, the superheat degree is controlled at 15-30 ℃, the drawing speed is 0.90-1.10m/min, and technologies such as dynamic light pressing are adopted to reduce the center segregation of the continuous casting slab, wherein the center segregation of the casting slab is not more than C3.0 level, and the center porosity is not more than 2.0 level;
2) heating and rolling
The slab heating adopts a stepping heating furnace, the heating temperature is 1190 and 1230 ℃, the heating time is more than or equal to 120min, and the temperature uniformity of the steel slab is ensured; the manufacturing process is controlled to be carried out in two stages of hot rolling, all the stages are longitudinal rolling, the first stage is austenite recrystallization zone rolling, namely a rough rolling stage, the rough rolling is carried out for 3+5 times by adopting an R1 two-roller horizontal reversible rolling mill and an R2 four-roller horizontal reversible rolling mill, and the thickness of an intermediate billet is 40-50 mm; the second stage is rolling in an austenite non-recrystallization region, namely a finish rolling stage, wherein the finish rolling is performed by adopting a seven-stand four-roller finish rolling unit, the rolling speed is constant, the start rolling temperature of the finish rolling is 980-;
3) cooling down
And after the controlled rolling is finished, the steel strip enters a dense laminar cooling area, the cooling mode is two-stage cooling, the front section adopts dense rapid cooling, the cooling temperature is 600-.
3. The production method of claim 2, wherein the slab is heated at 1200 ℃ for 120min, the rough rolling is performed for 3+5 passes by using R1 and R2, the start rolling temperature of the finish rolling is 1000 ℃, the finish rolling temperature is 850 ℃, the steel strip enters a laminar cooling device after the rolling is finished, the cooling mode is two-stage cooling, the front section is encrypted and rapidly cooled to 610 ℃, and the steel strip is rapidly cooled to 100 ℃ after air cooling and then coiled.
4. The production method of claim 2, wherein the slab is heated at 1210 ℃ for 130min, rough rolling is performed for 3+5 passes by using R1 and R2, the initial rolling temperature of finish rolling is 1020 ℃, the final rolling temperature is 830 ℃, after the rolling is finished, the steel strip enters a laminar cooling device, the cooling mode is two-stage cooling, the front section is encrypted and rapidly cooled to 630 ℃, and after air cooling, the steel strip is rapidly cooled to 150 ℃ for coiling.
5. The production method of claim 2, wherein the slab is heated at 1200 ℃ for 120min, the rough rolling is performed for 3+5 passes by using R1 and R2, the initial rolling temperature of the finish rolling is 1010 ℃, the final rolling temperature is 870 ℃, the steel strip enters a laminar cooling device after the rolling is finished, the cooling mode is two-stage cooling, the steel strip is encrypted at the front section and rapidly cooled to 650 ℃, and the steel strip is rapidly cooled to 200 ℃ after air cooling and then coiled.
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