CN107675090A - A kind of Brinell hardness 650HBW ranks high-wearing feature steel plate and preparation method thereof - Google Patents
A kind of Brinell hardness 650HBW ranks high-wearing feature steel plate and preparation method thereof Download PDFInfo
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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
- 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
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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
- C21D8/0221—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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- 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
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- 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
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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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- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
Abstract
The invention discloses a kind of Brinell hardness 650HBW grade high-strengths degree wear-resisting steel plate and preparation method thereof, the wear-resisting steel plate chemical composition is by weight percentage：C:0.41~0.50%；Si:≤ 0.25%；Mn:1.0~1.40%；P≤0.02%；S≤0.015%；Cr:0.5~1.2%；Mo:0.1~0.6%；Ti:0.1~0.2%；V:0.10~0.20%；Nb:0~0.07%；Ni:0~0.5%；Al:0.6 1.20%；N:≤ 0.006%；O:≤ 0.0025%；Also meet simultaneously：1.10%≤(Si+Mn)≤1.60%, (Cr+Mo) >=0.80%, 0.15%≤(V+Ti)≤0.3%, remaining is iron Fe and inevitable impurity.The present invention puies forward C content microalloying thinking in use, and adding appropriate Ti, V etc. has the alloying element of precipitation enhancement, using the TiC particles largely separated out, can increase hard phase content in the case of same rigidity to increase substantially wearability.
Description
Technical field
The present invention relates to a kind of Brinell hardness to reach more than 650HBW rank high-wearing feature steel plates and preparation method thereof, belongs to
Hot-rolled high-strength high abrasion steel plate production technical field.
Background technology
With the development of national economy, engineering field adapts to the requirement of special harsh environments for used material
More and more higher.Meanwhile the serial policy requirements of national environmental protection widelyd popularize in the engineering of various scales it is environmentally friendly
Material.The wearability of engineering material not only reduces the consumption of material, and has also been contributed for environmental protection.For engineering
For class high-abrasive material, the wear extent of equipment determines the service life of equipment, and the wear extent of equipment also ultimately depends on use
The wearability of material.Therefore, the new material such as higher steel of wearability, adapts to the development of current engineering machinery field, mainly should
For the high added value engineering goods such as engineering, metallurgy, mining, building, agricultural, manufacture of cement, harbour and electric power, manufacture pushes away
Native machine, loading machine, excavator, dumper and various mining machineries, grab bucket, stacker-reclaimer, conveying warp architecture etc., play raising
The effect of service life.
For the larger steel plate of engineering field usage amount, wearability depends primarily on its hardness, in addition, the modeling of steel
Property, toughness index are also one of important influence factor to the service life of steel.In general, the hardness number of steel depends on steel
The content of middle carbon and alloy.But too high carbon and alloy content causes welding performance, fatigue behaviour, bending property and mouldability
The combination properties such as energy are poorer, and which limits extensive use of the high hardness wear-resisting steel in engineering.
Brinell hardness reaches in 650HBW patent, and it is resistance to that Chinese patent CN102953016A is related to a kind of 650HB
Steel is ground, the present invention relates to a kind of wear-resisting steel plate, its composition by weight percent is：C：0.45-0.55%, Si：0.10-0.35%,
Mn:0.20-1.00%, P≤0.020%, S≤0.010%, Cr：0.20-1.00%, Mo:0.10-0.80%, Ni:0.50-
2.00%, Nb:0.010-0.08%, Ti:0.001-0.060%, Al:0.010-0.10%, B：0.0005-0.0040%, Mg：
0.001-0.010%, Ca:0.001-0.010%, also meet simultaneously：(Si+Mn)≤1.10%, (Cr+Mo) >=0.80%,
0.04%≤(Al+Ti)≤0.11%, surplus are Fe and inevitable impurity.Its preparation method, including：Smelt, casting and
Steel billet heats at 1000-1300 DEG C, carries out free rolling, rolls rear air cooling；In (Ac3-10) DEG C-(Ac3+80) DEG C of temperature quenching,
Then it is tempered in 100-400 DEG C of temperature.The hardness representative value of obtained wear-resisting steel plate is 650HB.Although hardness of the invention reaches
650HB levels, but C content is higher to be unfavorable for plasticity and toughness and welding performance, the alloying component including Mg, B, Ca etc. including element compared with
More, more Mo, Ni element significantly improve cost；Above-mentioned patent composition design limits abrasion-resistant stee in industrial volume production and pushed away
Wide application.
Therefore, the chemical composition for being adapted to industrial volume production is designed, the high alloying element content of increase wearability, is obtained every
The good low-alloy wear-resistant steel of excellent performance, applicability is the trend of development.With society and expanding economy, steel and iron industry institute face
The low-carbon economy development faced, to save resource, save the energy, environmental protection as main target.This is the important of abrasion-resistant stee development
Trend.Accordingly, the present invention relates to a kind of high-wearing feature hot rolled steel plate, there is good toughness and welding performance.
The content of the invention
In order to save resource, while meet that hardness reaches 650HBW high-wearing features and requires and have good forming property,
The present invention provides a kind of High wear-resistant steel and preparation method thereof, the C content microalloying thinking in, adds the tool such as appropriate Ti, V
There is the alloying element of precipitation enhancement, using the TiC particles largely separated out, hard phase can be increased in the case of same rigidity
Content is to increase substantially wearability.
The technical scheme is that：A kind of 650HB grade wear-resisting steel plates, its chemical composition are by weight percentage：C:
0.41~0.50%；Si:≤ 0.25%；Mn:1.0~1.40%；P≤0.02%；S≤0.015%；Cr:0.5~1.2%；
Mo:0.1~0.6%；Ti:0.1~0.2%；V:0.10~0.20%；Nb:0~0.07%；Ni:0~0.5%；Al:0.6-
1.20%；N:≤ 0.006%；O:≤ 0.0025%；Also meet simultaneously：1.10%≤(Si+Mn)≤1.60%, (Cr+Mo) >=
0.80%, 0.15%≤(V+Ti)≤0.3%, remaining is iron Fe and inevitable impurity.
The effect of element in the chemical composition of 650HB grade wear-resisting steel plates involved in the present invention：
Carbon：The important element of phase transformation strengthening is realized in abrasion-resistant stee, the intensity and hardness of steel can be significantly improved, is realized higher
Wearability.But the toughness and welding performance of the carbon of too high amount reduction steel.Therefore, select carbon content control 0.41~
In the range of 0.55%.
Silicon：Silicone content is too high to influence plate surface quality, and scale on surface is not easy to remove, so as to reduce its usability
Energy.Silicon is solid-solubilized in and their hardness and intensity is improved in ferrite and austenite, but the too high toughness that can cause steel of silicone content
Drastically decline.It is simultaneously stronger than iron in view of the affinity of silicon and oxygen, the silicate of low melting point is easily produced during welding, is added molten
The mobility of slag and fusing metal, weldquality is influenceed, therefore content is not easy excessively.Content is controlled in the range of 0.25%, excellent
Elect as, Si：0.1-0.2%.
Manganese：Effect in steel is solution strengthening and improves quenching degree, but Mn segregation tendency is higher, and manganese content is higher
When, too high Mn causes the toughness of steel plate to reduce；Have the tendency of to make grain coarsening simultaneously, and increase the crisp sensitiveness of steel belt roof bolt,
And easily cause to occur being segregated in strand and crackle, so as to reduce the performance of steel plate.Therefore the control of Mn contents 1.2~
1.45%.
Chromium：Chromium can reduce critical cooling rate, improve the quenching degree of steel, improve austenite conversion rates.Chromium is in steel
It can be formed (Fe, Cr)3C, (Fe, Cr)7C3(Fe, Cr)23C7Etc. a variety of carbide, intensity and hardness are improved.Chromium is in tempering
The precipitation and aggregation of carbide can be prevented or slowed down, steel belt roof bolt stability can be improved.Content is controlled in 0.5~1.2% model
In enclosing.
Aluminium：Content is controlled in the range of 0.02~0.20wt.%.Because aluminium also has the function that to suppress carbide formation,
Therefore available aluminium suppresses Carbide Precipitation so that for carbon with V in later stage ferrite, Ti, which is combined, largely separates out the phases of TiC, VC etc. second
Particle, improves the wearability of steel, and Al is controlled in 0.6-1.20% scopes；
Molybdenum：Quenching degree can be improved, crystal grain thinning, improves intensity and toughness.Molybdenum is present in solid solution phase and carbon in steel
In compound phase, therefore, there is solution strengthening and carbide dispersion-strengthened simultaneously containing molybdenum steel.Molybdenum is to reduce temper brittleness
Element, it is stable that tempering can be improved.It is preferably controlled in the range of 0.2~0.4%.
Nickel：Critical cooling rate can be reduced, improve the quenching degree of steel.Nickel can appoint in the range of 0~2.50% with iron
What ratio is dissolved each other, and improves the low-temperature flexibility of steel by fining ferrite grains, and with the obvious work for reducing Cold Brittleness Transition Temperature
With.For high-level and high/low temperature toughness abrasion-resistant stee, nickel is highly beneficial addition element.But too high levels are easily caused steel plate
Surface scale is difficult to come off, and cost dramatically increases, therefore need to control its content.It is preferably controlled in 0.2~0.4% scope
It is interior.
Titanium：It is one of carbide, trickle TiC particles is formed with carbon, on the one hand makees with precipitation strength
With raising intensity；The TiC particles of the small and dispersed distribution separated out in addition can be used as hard phase, hence it is evident that improve the wearability of steel.
TiC particles are tiny, are distributed in crystal boundary.Too high Ti can substantial amounts of TiN particles, be unfavorable for toughness plasticity raising, therefore, control
In the range of 0.1~0.2%.
Vanadium：It is one of new formation element of strong carbide, trickle VC particles is formed with carbon, on the one hand makees with precipitation strength
With raising intensity；The VC particles of the small and dispersed distribution separated out in addition, hence it is evident that improve the intensity of steel.In addition, VC particles can be made
For ferrite equiax crystal, thinning microstructure.Therefore, control in the range of 0.1~0.2%.
Aluminium：Content is controlled in the range of 0.001~0.10wt.%.Aluminium and nitrogen in steel can form AlN of tiny indissoluble
Grain, refinement microstructure.Aluminium is not only deoxidier, the effect for also promoting metastable austenite to be formed.Aluminium can suppress and delay
The carbide of overcooling austenite decomposes, and improves toughness.
Phosphorus and sulphur：In abrasion-resistant stee, sulphur and phosphorus are harmful element, and their content will be controlled strictly, involved by the present invention
And phosphorus content is less than 0.02wt.% in steel grade, sulfur content is less than 0.01wt.%.
Brinell hardness involved in the present invention reaches more than 650HBW steel plate, is set by the science of element species and content
Meter, while realizing high intensity on the basis of adding appropriate alloying element, high rigidity improves steel wearability, ensure steel plate tool
There is the matching of good plasticity, toughness.
The present invention relates to Brinell hardness 650HBW grade wear-resisting steel plates preparation method, including, the outer essence of converter smelting, stove
The processes such as refining, continuous casting, heating, rolling, cooling, quenching and tempering；Wherein,
1) in heating stepses, heating and temperature control is at 1230~1280 DEG C；Using slow temperature-boosting measure.
2) in the operation of rolling, 1100~1200 DEG C of roughing start rolling temperature, 900~960 DEG C of finishing temperature；The accumulative pressure of finish rolling
Rate is more than 60%, and last three percentage pass reduction is more than 10%, 850~900 DEG C of start rolling temperature, 800~830 DEG C of finishing temperature.
3) accelerate in cooling step：The rear strong cold technique of ACC coolings selection is rolled, cold 800~830 DEG C of temperature is opened, is cooled to 500
~560 DEG C of air coolings, 5~20 DEG C/S of cooling velocity.
4) it is heat-treated after rolling：
Quenching：Hardening heat control water cooling after coming out of the stove, is advantageous to thinning microstructure, carried in (Ac3+20) DEG C-(Ac3+80) DEG C
High-strength tenacity.Containing alloying elements such as higher carbon and a certain amount of Si, Mn, Cr, Mo and Ni, it is necessary to abundant at high temperature in steel
Solid solution, but temperature too high should not too be grown up to prevent austenite crystal and billet surface severe oxidation；The elements such as Cr, Mo can improve
Steel plate quenching degree, therefore high thickness steel plate can be produced under the conditions of water cooling.Therefore selective quenching temperature is at 850~900 DEG C.
Tempering：Temperature is less than 300 DEG C, slow cooling after coming out of the stove.Element Cr, Mo etc. can improve temper resistance, ensure
Steel plate has higher strong hardness, while has excellent plasticity and toughness.
Air cooling is cooled down using stacking or burial pit, can be slowed down cooling velocity, be prevented steel plate from ftractureing.
Compared with the present invention with oneself has technology, there is the advantages of following notable and effect：
1st, Design of Chemical Composition is simple, from appropriate C content and using Ti, V microalloying thinkings, relates to the present invention
And wear-resisting steel plate has higher solderability；
2nd, using Al " purification " ferritic structure of proper content, carbide is delayed to separate out too early so as to ensure later stage carbon
Si can be substituted with fully combination, Al such as Ti, V, improve plate surface quality.
3rd, by largely adding V, Ti elements, using a large amount of VC of precipitation, TiC particles, hard phase amount is added, significantly
Improve the intensity and wearability of steel matrix.
4th, chemical composition and rolling mill practice are reasonable in design, and process window is wide, can stablize and carry out industrial volume production.
5th, 1.10%≤(Si+Mn)≤1.60% need to be met during element of the invention design, (Cr+Mo) >=0.80%,
0.15%≤(V+Ti)≤0.3%, also only when meeting these conditions, it can be only achieved the technique effect of the present invention.Such as this
The 650HB grade wear-resisting steel plates Brinell hardness of invention production is more than 650HBW, has excellent anti-wear performance；Indulged under the conditions of -20 DEG C
It is more than 34J to Charpy-V impact power, impact flexibility is good, meets the requirement of high-end steel for engineering machinery.
Brief description of the drawings
Fig. 1 is the micro-organization chart of the 650HB grade wear-resisting steel plates of the embodiment of the present invention 3, and the steel plate is micro- as seen from the figure
Tissue is mainly the tissue such as tempered martensite；
Fig. 2 is the tiny Second Phase Precipitation thing micro-organization chart such as TiC in embodiment 2.
Embodiment
Being exemplified below specific embodiment, the present invention will be described.It is pointed out that embodiment is served only for the present invention
It is described further, does not represent protection scope of the present invention, the nonessential modification and adjustment that other people make according to the present invention,
Still fall within protection scope of the present invention.
Embodiment 1
The chemical composition of the 650HB grade wear-resisting steel plates of the present invention is as shown in table 1.Chemical composition as shown in table 1 is turned
Stove is smelted, and continuous casting billet is cast into after refining, continuous casting billet is heated into 1280 DEG C, start rolling temperature is 1160 DEG C, finished steel plate thickness
For 20mm, air cooling after rolling, quenching temperature is Ac3+70 DEG C, and temperature is 300 DEG C, stacking or burial pit after tempering
Cooling.
The chemical composition of the 650HB grade wear-resisting steel plates of the embodiment 1 of table 1
Embodiment 2
Embodiment is 1250 DEG C with embodiment 1, wherein heating-up temperature, and start rolling temperature is 1140 DEG C, finished steel plate thickness
For 16mm, quenching temperature is Ac3+50 DEG C, and temperature is 200 DEG C, stacking or burial pit cooling after tempering.Embodiment 2
The tiny Second Phase Precipitation thing micro-organization chart such as middle TiC is as shown in Figure 2.Figure it is seen that form trickle TiC with carbon
Grain is tiny, is distributed in crystal boundary, can be used as hard phase, hence it is evident that improve the wearability of steel.
The chemical composition of the 650HB grade wear-resisting steel plates of the embodiment 2 of table 2
Embodiment 3
Embodiment is 1240 DEG C with embodiment 1, wherein heating-up temperature, and start rolling temperature is 1130 DEG C, finished steel plate thickness
For 12mm, quenching temperature is Ac3+40 DEG C, and temperature is 180 DEG C, stacking or burial pit cooling after tempering.Its micro- group
Figure is knitted as shown in figure 1, the microscopic structure of the steel plate is mainly the tissue such as tempered martensite as seen from the figure.
The chemical composition of the 650HB grade wear-resisting steel plates of the embodiment 3 of table 3
Embodiment 4
Embodiment is 1210 DEG C with embodiment 1, wherein heating-up temperature, and start rolling temperature is 1120 DEG C, finished steel plate thickness
For 10mm, quenching temperature is Ac3+20 DEG C, and temperature is 170 DEG C, stacking or burial pit cooling after tempering.
The chemical composition of the 650HB grade wear-resisting steel plates of the embodiment 4 of table 4
The comparative example of table 5 is steel grade involved in existing patent
Performance test
The mechanical property of abrasion-resistant stee of the present invention and compared steel is referring to table 6.
The mechanical property of the embodiment of the present invention of table 6 and compared steel
As known from Table 6, abrasion-resistant stee of embodiment of the present invention hardness is more than 650HB, and -20 DEG C of Charpy impact of collision work(are more than 34J,
High-wearing feature steel plate involved in the present invention has excellent mechanical performance.Steel plate hardness involved in the present invention apparently higher than with contrast
The hardness of steel 2；The hardness of compared steel 1 is close with steel plate hardness involved in the present invention, but its wearability is relatively low compared with this steel grade, and ballistic work is inclined
It is low.
Oblique Y groove welding crack tests are carried out to the wear-resisting steel plate of the embodiment of the present invention 3, result of the test is referring to table 7.
The 650HB grade wear-resisting steel plate welding performance test results of the embodiment of the present invention 3 of table 7
As shown in Table 7, wear-resisting steel plate postwelding under 180 DEG C of preheating conditions is not cracked, and steel plate of the present invention has preferable
Welding performance.
Using identical experimental condition, abrasion test is carried out on ML-100 grain-abrasion testing machines.The present invention is implemented
The wear test of wear-resisting steel plate compared steel 1 of example 4 the results are shown in Table 8.
The embodiment 4 of table 8 and the abrasion resistance test results of contrast steel grade 1.
As shown in Table 7, the present invention relates to the wearability of a little higher than compared steel of steel grade.
It should be noted last that the above embodiments are merely illustrative of the technical solutions of the present invention and it is unrestricted.Although ginseng
The present invention is described in detail according to embodiment, it will be apparent to an ordinarily skilled person in the art that the technical side to the present invention
Case is modified or equivalent substitution, and without departure from the spirit and scope of technical solution of the present invention, it all should cover in the present invention
Right among.
Claims (4)
1. a kind of Brinell hardness 650HBW grade high-strengths degree wear-resisting steel plate, it is characterised in that the wear-resisting steel plate chemical composition is pressed
Percentage by weight is：C:0.41~0.50%；Si:≤ 0.25%；Mn:1.0~1.40%；P≤0.02%；S≤0.015%；
Cr:0.5~1.2%；Mo:0.1~0.6%；Ti:0.1~0.2%；V:0.10~0.20%；Nb:0~0.07%；Ni:0~
0.5%；Al:0.6-1.20%；N:≤ 0.006%；O:≤ 0.0025%；Also meet simultaneously：1.10%≤(Si+Mn)≤
1.60%, (Cr+Mo) >=0.80%, 0.15%≤(V+Ti)≤0.3%, remaining is iron Fe and inevitable impurity.
2. the preparation method of the Brinell hardness 650HBW grade wear-resisting steel plates described in claim 1, methods described include converter smelting,
External refining, continuous casting, heating, rolling, cooling, quenching and tempering；
Wherein,
1) in heating stepses：Heating and temperature control is at 1230~1280 DEG C；Using slow temperature-boosting measure；
2) in the operation of rolling：1100~1200 DEG C of roughing start rolling temperature, 900~960 DEG C of finishing temperature；It is big that finish rolling adds up reduction ratio
In 60%, last three percentage pass reduction is more than 10%, 850~900 DEG C of start rolling temperature, 800~830 DEG C of finishing temperature；
3) in cooling step：The rear strong cold technique of ACC coolings selection is rolled, cold 800~830 DEG C of temperature is opened, is cooled to 500~560 DEG C
Air cooling, 5~20 DEG C/S of cooling velocity；
4) it is heat-treated after rolling：
Quenching：Hardening heat control is in (Ac3+20) DEG C-(Ac3+80) DEG C, water cooling after coming out of the stove；
Tempering：Temperature is less than 300 DEG C, and air cooling cools down after coming out of the stove.
3. preparation method according to claim 2, it is characterised in that the hardening heat is 850~900 DEG C.
4. preparation method according to claim 2, it is characterised in that the air cooling is carried out cold using stacking or burial pit
But.
Priority Applications (1)
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| CN109825756A (en) * | 2019-03-11 | 2019-05-31 | 昆明理工大学 | A kind of preparation method of high-wear-resistant alloy Steel material |
| CN110157983A (en) * | 2019-05-28 | 2019-08-23 | 山东钢铁股份有限公司 | A kind of uniform endogenous TiC abrasion-resistant stee of particle and preparation method thereof |
| CN113831768A (en) * | 2021-09-24 | 2021-12-24 | 山东钢铁股份有限公司 | Anti-scaling coating for dry dedusting evaporative cooler |
| CN115161557A (en) * | 2022-07-07 | 2022-10-11 | 唐山天和环保科技股份有限公司 | Coal mine crusher tooth cap and preparation method thereof |
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