CN105970110A - Low-alloy high-strength abrasion-resistant steel and preparation method thereof - Google Patents
Low-alloy high-strength abrasion-resistant steel 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
- C22C38/18—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
- 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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- 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
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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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- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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Abstract
The invention provides low-alloy high-strength abrasion-resistant steel and a preparation method thereof. The low-alloy high-strength abrasion-resistant steel comprises, by mass, 0.14%-0.17% of C, 0.20%-0.50% of Si, 1.1%-1.5% of Mn, no larger than 0.02% of P, no larger than 0.01% of S, 0.5%-0.7% of Cr, 0.25%-0.32% of Ni, 0.2%-0.3% of Mo, 0.01%-0.04% of Als, 0.005%-0.02% of Ti, 0.002%-0.004% of B and the balance Fe and unavoidable impurities. By means of chemical composition design and improvement of the preparation method, the obtained low-alloy high-strength abrasion-resistant steel not only has high hardness, excellent abrasion resistance, high tenacity and high tensile strength, but also enables distribution of residual stress in a steel plate to be even, the tendency of cracking of the steel plate is reduced, the quality of the steel plate is improved, and the practicability is high.
Description
Technical field
The invention belongs to field of steel metallurgy, specifically refer to a kind of low-alloy high-strength abrasion-resistant stee and preparation method thereof.
Background technology
Abrasion-resistant stee is the class ferrous materials being widely used under various wear working condition, its object is to slow down the attrition of mechanical part, improve the life-span of product, there is the time of failure behaviour in prolonged mechanical product, it is desirable to have higher hardness number to ensure the wear resistance under bad working environments because of abrasion.
Residual stress is to affect the key parameter that abrasion-resistant stee uses, and has direct relation with the cracking of steel plate and the wearability on surface.And common abrasion-resistant stee hardness number is high, in it, residual stress is big, and uniformity is bad, it is easy to the problem that steel plate cracking in use occurs；It addition, the residual stress on surface also has certain relation with wearability, surface of steel plate if compressive stress, then has castering action to the anti-wear performance and fatigue behaviour improving steel plate.
At present, all there is certain deficiency in the domestic pertinent literature about reduction low-alloy high-strength abrasion-resistant stee residual stress, such as patent document 1 discloses that a kind of process eliminating high-speed steel grinding skin residual stress, it is characterized in that processing step is: 1. blank is carried out roughing, i.e. carries out turning and corase grind；2. by after the workpiece heat after roughing to 1210 DEG C～1240 DEG C of quenchings, cool to room temperature again, carry out 160 DEG C～196 DEG C of subzero treatment 8h～10h with 3 DEG C～5 DEG C of cooling rates again, then return to room temperature, be again heated to tri-tempering of 540 DEG C～560 DEG C × (1～4) h；3. ground finish is carried out；4., after the workpiece after fine grinding being carried out 160 DEG C～196 DEG C of subzero treatment 8h～10h with the cooling rate of 5 DEG C/min, recover to room temperature.Patent document 2 discloses that a kind of high strength low alloy wear resistance steel plate and manufacture method thereof, the chemical composition of steel is by weight percentage: C 0.18～0.22%, Si 0.2～0.5%, Mn 1.0～1.6%, P≤0.010%, S≤0.005%, Al 0.02～0.03%, Ti 0.016～0.022%, Cr 0.16～0.20%, B 0.0005～0.0015%, remaining is Fe and inevitable impurity.And carbon equivalent Ceq (%)≤0.5, simultaneously and meet: Ceq (%)=C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14.Manufacture method includes ultra-clean steel processing step, it is characterised in that design parameter control is: heating of plate blank to 1180～1200 DEG C, heat time heating time >=150min；Rolling every time reduction ratio is 15～30%, accumulative reduction ratio >=70%, and hot rolling starts temperature 1050～1100 DEG C, and end temp is more than 950 DEG C；Steel plate carries out heat treatment (quenching+lonneal) after rolling；Quenching system is: be heated to 910～950 DEG C, temperature retention time 3min/mm；Tempering system is: be heated to 250 DEG C, temperature retention time 2.5min/mm.Improve steel plate anti-wear performance, welding performance, intensity and hardness, and simplify production technology, reduce steel plate cost.nullPatent document 3 discloses that 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:0.010-0.080%，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%，Meet: (Si+Mn)≤1.10% the most simultaneously，(Cr+Mo) >=0.80%，0.04%≤(Al+Ti)≤0.11%，Surplus is Fe and inevitable impurity.Its manufacture method, including: smelt, cast and steel billet 1000-1300 DEG C of heating, carry out free rolling, roll rear air cooling；(Ac3-10) DEG C-(Ac3+g0) DEG C of temperature quenching, then it is tempered 100-400 DEG C of temperature.The hardness representative value of the wear-resisting steel plate obtained is 650HB, has hard and good toughness high-strength, high and matches, and ensures that wear-resisting steel plate has good application performance, such as wearability, weldability and machining etc., is of value to the abrasion-resistant stee extensive application in engineering.Patent document 4 discloses that a kind of engineering machinery high-strength abrasion-proof steel plate, described steel plate chemical composition composition by weight percentage is as follows: C 0.14～0.21%, Si 0.15～0.50%, Mn 0.90～1.50%, P≤0.020%, S≤0.010%, Ni 0.05～0.80%, Cr 0.20～0.70%, V 0.03～0.08%, Nb 0.01～0.060%, Al 0.02～0.08%, Mo 0.01～0.50%, Ti 0.010～0.060%, B 0.0005～0.0030%, remaining is Fe and inevitable impurity.The present invention, to alloying component appropriate design, adds that thickness can reach 60mm, and ball hardness number is 235～289, and hardness is evenly distributed to mainly quenching and the control of tempering process, prepared steel plate；Yield strength height, good welding performance, cold-bending property are good, steel plate template good, unevenness≤3mm/m, have excellent combination property, can be widely used for construction machinery production, have a extensive future.Patent document 5 discloses that a kind of low cost HB400 grade wear-resisting steel and production method thereof.Its chemical component weight degree is: C:0.08～0.19%, Si:0.20～0.50%, Mn:1.30～1.60%, P :≤0.015%, S :≤0.015%, Cr:0.30～0.65%, Nb:0.02～0.05%, Ti:0.005～0.025%, B:0.001～0.005%, Als:0.010～0.040%, and remaining is Fe and micro impurity element.Steel plate thickness specification limit is 10～50mm, Rm >=1300MPa, elongation percentage >=15% ,-20 DEG C of Akv >=47J, HBW/10/3000 >=400.Manufacturing cost being not only greatly reduced, solves a difficult problem for martensite wear-resistant hardness of steel high-ductility difference, steel plate can directly be delivered goods.Therefore there is the strongest market competitiveness and wide application prospect, economic benefit and social benefit are obvious.Document 6 describes oneNovelMulti-element low alloy high-strength high-toughness wear-resistant steel；First with Mn, Si, Cr as main alloy element, add a small amount of Mo, Cu, RE and carry out microalloying and compound modification treatment, having carried out the Design of Chemical Composition of liner plate, its main component (W%) is: C:0.42～0.48, Cr:1.9～2.4, Mn:1.0～1.3, Si:0.9～1.4, Mo:0.1～0.3, Cu:0.3～0.6, RE:0.4～0.6, P, S≤0.03；Casting technique uses the negative-pressure los mould casting of iron ore moulding, and Technology for Heating Processing is+250 DEG C of tempering of 910 DEG C of quenchings.Result of the test shows, the low-alloy abrasion-proof steel hardenability of design is good, and intensity and wearability have reached the requirement of lining board of crusher.Comprehensive mechanical property after+250 DEG C of tempering of 890～920 DEG C of quenchings reaches optimal: hardness reaches more than 50HRC, impact flexibility ak > 18J/cm2.Microscopic structure is tempering lath martensite+lower bainite+retained austenite+diffusion carbide, and this tissue is compared with abrasion-resistant stee liner plate former with disintegrating machine, the main cause that mechanical performance improves.Document 7 describes employing Nb-Cr-B microalloying ingredient design, two-stage control rolling and the Technology for Heating Processing of press quenching+lonneal, develops the NM400 high-strength low-alloy abrasion-resistant stee of low cost.This product has good intensity, hardness and toughness coupling, and every mechanical performance index is satisfied byCountryStandard-required.Patent document 8 discloses that a kind of method for removing residual stress of hot-rolling high-strength steel, production procedure includes that (1) enters burial pit slow cooling and processes the coil of strip of thickness >=8mm；(2) coil of strip for thickness ＜ 8mm carries out air cooling, after coilcooling to room temperature, carries out skin pass rolling, again batches rolling.Use roll straightening unit that the above-mentioned high-strength steel carrying out processing is involved in capable aligning and open flat, scale, crosscutting one-tenth steel plate.The split flat steel plate of roller hearth heat-treated furnace is used to carry out stress relief annealing, eliminate steel plate internal stress, the stacking type of cooling is used to carry out slow cooling after coming out of the stove, the aligning of steel plate is finally carried out with aligning unit, high strength steel plate is made to obtain good plate shape stability, it is possible to meet the strict demand less than or equal to 2mm/m of user's flatness to high strength steel plate.Existing heat-treatment furnace and roll straightening equipment can be utilized, reduce cost of investment and processing cost, shorten the annealing time, it is possible to the plate shape reaching bell-type annealing improves effect, for the exploitation of high-strength steel, there is important economy and social meaning.Patent document 9 discloses that a kind of hundred meters of rail residual stress control methods, belong to the fields such as hundred meters of rail pre-bending Deformation control, compound straightening Deformation control technique.The present invention uses universal rolling, roller repairing, compound straightening method, and hundred meters of rail during roller repairing are used big radian pre-bending, and action when making rail be cooled to room temperature controls in the range of 30～40mm.In conjunction with the 8+1 multi-roll straightening machine straightening deformation code optimized, in conjunction with the control rectifying antecurvature curvature, the present invention has efficiently controlled the flange of rail residual stress after hundred meters of steel rail straightenings, flange of rail residual-stress value averagely reduces 70MPa, residual-stress value all≤250MPa, improve steel rail straightness, make seamed high-speed steel rail qualification rate improve, meet the standard-required of hundred meters of seamed high-speed steel rails.
1. eliminate the process of high-speed steel grinding skin residual stress. application number: CN201110425660.0
2. a high strength low alloy wear resistance steel plate and manufacture method thereof. application number: CN200910013569.0
3. a 650HB grade wear-resisting steel plate and manufacture method thereof. application number: CN201110247523.2
4. high-strength abrasion-proof steel plate and preparation method thereof. application number: CN200710193025.8
5. low cost HB400 grade wear-resisting steel and production method thereof. application number: CN201410737934.3
6. profit of rectifying China. low-alloy wear-resistant steel lining board of crusher manufacturing process and performance study. University Of Science and Technology Of Taiyuan Master's thesis .2010.-1-59
7. Song Hong space；Li Canming；Zhou Ping. the exploitation of low cost NM400 high-strength low-alloy abrasion-resistant stee. steel rolling .2012 (4) .-1-3
8. a method for removing residual stress of hot-rolling high-strength steel. application number: CN201010162933.2
9. hundred meters of rail residual stress control methods. application number: CN201110121768.0
But above steel and preparation method the most not can solve the uniform problem of residual stress distribution, make abrasion-resistant stee still can have excellent wear and higher toughness and tensile strength when Brinell hardness 360 grades.
Summary of the invention
It is an object of the invention to provide a kind of low-alloy high-strength abrasion-resistant stee and preparation method thereof according to the deficiencies in the prior art, this low-alloy high-strength abrasion-resistant stee residual stress distribution is uniform, when hardness reaches more than 360, remain to keep good tensile strength and anti-wear performance, toughness.
Technical scheme is as follows: a kind of low-alloy high-strength abrasion-resistant stee, it is characterised in that: the mass percent of described low-alloy high-strength abrasion-resistant stee chemical composition is: C:0.14～0.17%, Si:0.20～0.50%, Mn:1.1～1.5%, P≤0.02%, S≤0.01%, Cr:0.5～0.7%, Ni:0.25～0.32%, Mo:0.2～0.3%, Als:0.01～0.04%, Ti:0.005～0.02, B:0.002～0.004%, surplus is Fe and inevitable impurity.
Further, described low-alloy high-strength abrasion-resistant stee thickness is 10～50mm.
A kind of method preparing above-mentioned low-alloy high-strength abrasion-resistant stee, it is carried out by following operation: desulphurised hot metal → converter smelting → application of vacuum → continuous casting → strand heating → rolling → cooling → quenching → tempering → finishing, it is characterized in that: in tempering process, temperature is 220～250 DEG C, and temperature retention time is 3.2～4.0min/mm × thickness of slab.
Further, in described quenching process, hardening heat is 880 DEG C～910 DEG C, and temperature retention time is 1.4～2.0min/mm × thickness of slab.
Further, in described strand heating process, soaking temperature is 1190 DEG C～1250 DEG C, and the rate of heat addition is 7～10min/cm.
Further, in described rolling process, roughing start rolling temperature >=1080 DEG C, finishing temperature >=980 DEG C, single pass reduction ratio is more than 20%；Finish rolling start rolling temperature≤960 DEG C, finishing temperature 810 DEG C～890 DEG C, single pass reduction ratio is more than 20%.
The C content of the present invention selects 0.14～0.17%.Carbon is the important element affecting abrasion-resistant stee intensity, hardness, toughness and quenching degree, is also to affect the of paramount importance element of steel microscopic structure.Along with carbon content increases, the hardness of steel increases, and impact flexibility is remarkably decreased, and wearability gradually steps up.Carbon content is too high, and the carbide amount in steel is too much, and formed after heat treatment is high-carbon lamellar martensite, and the hardness of steel is high and toughness is low, and easily ftractures in heat treatment process；Carbon content is too low, and the hardenability of steel is not enough, and hardness is too low, and wearability is not enough.
The Si content of the present invention is 0.20～0.50%.In steelmaking process, Si is used as reducing agent and deoxidizer.Si is non-carbide former, is to be present in ferrite or austenite with the form of solid solution, therefore with reinforced ferrite, can improve intensity and the hardness of steel, can reduce the critical cooling rate of steel simultaneously, improve the quenching degree of steel.Si also can improve steel belt roof bolt stability and non-oxidizability.It is extremely strong that it improves the intensity of solid solution and the effect of cold deformation hardening ratio in steel, is only second to phosphorus, but reduces toughness and the plasticity of steel simultaneously the most to a certain extent.It addition, silicon makes steel be banded structure, make the lateral performance of steel less than longitudinal performance.But silicone content is too high there will be granular ferrite, the toughness of steel is made to reduce and be easily generated hardening flaw；And retained austenite dramatically increases, the hardness of steel is made to reduce.When the content of Si is higher, Fe may be made3C decomposes, and makes C free and exists in non-graphitic state, i.e. has so-called graphitizing.When annealing, surface also easily decarburization.
The Mn content of the present invention is 1.1～1.5%.Mn is good deoxidizer and desulfurizing agent, can eliminate or weaken because of the red brittleness caused by sulfur, thus improve the hot-working character of steel.Mn and ferrum form solid solution, can improve ferrite and the hardness of austenite and intensity in steel, strengthen matrix；Carbide can be formed again simultaneously, enter and cementite replaces a part of iron atom, generate Mn3C, it and Fe3C can be mutually dissolved, and is formed at (Fe Mn) in steel3C-type compound, thus improve the intensity of steel, hardness and wearability.Mn can reduce critical cooling rate, promotes that martensite is formed, improves the quenching degree of steel.Mn owing to reducing critical transition temperature, plays the effect of refinement pearlite, the most indirectly plays the effect improving pearlitic steel intensity in steel.Mn expands carbon iron balance phaseIn figureγ phase region, it makes steel be formed and the ability of stable austenite tissue is only second to Ni, and be easy to get after quenching martensitic structure.But Mn is superheated susceptivity element, during quenching, the too high meeting of heating-up temperature causes coarse grains；Mn segregation coefficient when solidification is bigger, it is easy at Grain Boundary Segregation, have a negative impact the performance of steel, and remained austenite content in the quenching structure of steel can be caused to increase, so Mn content controls between 0.9～1.4%.
P≤0.02% of the present invention, S≤0.01%, sulfur is present in iron and steel steel can be made to become hot-short, and phosphorus is easily generated segregation in crystallization process, thus the regional area in steel produces cold short.Sulfur, phosphorus are objectionable impurities element for abrasion-resistant stee residual stress control, should eliminate as possible.
The Cr content of the present invention is 0.5～0.7%.Cr is conducive to solution strengthening the formation of suitable carbide of steel, and then improves the elevated temperature strength of steel, hardness and anti-wear performance.Cr increases the quenching degree of steel, especially with manganese, the reasonably combined quenching degree that can be greatly improved of silicon, but the most also increases steel belt roof bolt fragility tendency.Cr can be solid-solution in ferrite and produce solution strengthening effect, improves tensile strength and the yield point of weld metal, but its content is more than 0.8%, and weld metal toughness can be made to be decreased obviously.
The Ni content of the present invention is 0.25～0.32%.Ni and carbon are formed without carbide, are to be formed and the main alloy element of stable austenite, add certain Ni and can improve quenching degree, make the tissue of steel retain a small amount of retained austenite at normal temperatures, to improve its toughness.Ni element can improve the impact flexibility of steel itself, the especially low-temperature impact to steel and improve bigger.
The Mo content of the present invention is 0.2～0.3%.Mo in steel presented in solid solution phase and Carbide Phases.Critical cooling rate can be reduced, promote that martensite is formed, improve the quenching degree of steel.Mo becomes MoC with C-shaped, improves the hardness of steel.And strengthen matrix by solution strengthening, improve the density of hardening phase, also improve the stability of carbide simultaneously, the intensity of steel is produced favourable effect.Impact on temper brittleness is the most complicated, exists as single alloying element, improves steel belt roof bolt fragility, but when causing the element of temper brittleness with other and deposit, Mo reduces again or suppress the temper brittleness that other elements are caused.
The steel Als content of the present invention controls 0.01～0.04%.Al is the main deoxidant element in steel.Steel adds a small amount of Al, impact flexibility can be improved with crystal grain thinning.
The steel Ti content of the present invention controls≤0.02%.Ti improves the intensity of steel by crystal grain thinning and precipitation strength, and Ti generates the TiN granule of disperse under continuous casting cooling condition, owing to its fusing point is the highest, can significantly inhibit crystal grain in welding heat affected zone and grow up, add trace Ti and can significantly improve the toughness of heat affected area.
The steel B content of the present invention controls≤0.004%.Trace B can be adsorbed on austenite grain boundary, reduces the energy of crystal boundary, improves the quenching degree of steel.
The present invention, by the chemical Composition Control to low-alloy high-strength abrasion-resistant stee, makes steel of the present invention on the premise of keeping its hardness, moreover it is possible to ensure its wearability and wilfulness, makes residual stress distribution in steel uniform simultaneously, and steel plate is the most easy to crack.C content 0.14～0.17% in chemical composition, C content is too high, then the hardness of steel is high and toughness is low, easily ftractures in heat treatment process, and C content is too low, and the hardenability of steel is not enough, and hardness is too low, and wearability is not enough.The Mn that contains in chemical composition, Cr, Ni, B element can improve the quenching degree of steel, thus reduce the product residual stress gradient at thickness direction, suppression cracking.Ti, Al, V in composition play Grain refinement, make in steel residual stress distribution evenly.Chemically the angle of composition design makes residual stress distribution in steel uniform, thus reduces the residual stress at each position.
Meanwhile, in the preparation method of the low-alloy high-strength abrasion-resistant stee of the present invention, use quenching process after rolling process, and carry out lonneal process for a long time.What lonneal remained surface of steel plate presses to stress, and the anti-wear performance and fatigue behaviour improving steel plate is obviously improved effect.Meanwhile, under low temperature, sufficient tempering time makes steel plate, residual stress is more uniform, obtains tempered martensite, advantageously reduce the tearing tendency of steel plate after tempering.
The present invention passes through Design of Chemical Composition and the improvement of preparation method, the low-alloy high-strength abrasion-resistant stee obtained is made not only to have high rigidity, excellent wear, high tenacity and tensile strength, in making steel plate, residual stress distribution is uniform simultaneously, reduce the tendency of steel plate cracking, improve plate quality, there is the strongest practicality.
Accompanying drawing explanation
Figure 1Residual stress test point for embodiment 1 is distributedFigure；
Figure 2Metallographic structure for embodiment 1Figure；
Wherein: 1～7 detect distributed points for residual stress.
Detailed description of the invention
The present invention is further illustrated below by way of specific embodiment:
Embodiment 1
A kind of low-alloy high-strength abrasion-resistant stee 1, thickness is 20mm, and the mass percent of its chemical composition is: C:0.16%, Si:0.37%, Mn:1.42%, P:0.014%, S:0.005%, Cr:0.57%, Ni:0.26%, Mo:0.3%, Als:0.038%, Ti:0.017, B:0.002%, surplus is Fe and inevitable impurity.
Described low-alloy high-strength abrasion-resistant stee 1 is prepared by following operation: desulphurised hot metal → converter smelting → application of vacuum → continuous casting → strand heating → rolling → cooling → quenching → tempering → finishing.Wherein, in strand heating process, soaking temperature is 1200 DEG C, and the rate of heat addition is 10min/cm.In rolling process, point rough rolling step and finish rolling stage are carried out, and roughing start rolling temperature is 1090 DEG C, and finishing temperature is 980 DEG C, and single pass reduction ratio is more than 20%；Finish rolling start rolling temperature is 960 DEG C, finishing temperature 880 DEG C, and single pass reduction ratio is more than 20%.In quenching process, hardening heat is 880 DEG C, and temperature retention time is 30min.In tempering process, temperature is 220 DEG C, and temperature retention time is 70min.
Embodiment 2
A kind of low-alloy high-strength abrasion-resistant stee 2, thickness is 40mm, and the mass percent of its chemical composition is: C:0.15%, Si:0.32%, Mn:1.39%, P:0.013%, S:0.005%, Cr:0.61%, Ni:0.27%, Mo:0.28%, Als:0.032%, Ti:0.015%, B:0.002%, surplus is Fe and inevitable impurity.
Described low-alloy high-strength abrasion-resistant stee 2 is prepared by following operation: desulphurised hot metal → converter smelting → application of vacuum → continuous casting → strand heating → rolling → cooling → quenching → tempering → finishing.Wherein, in strand heating process, soaking temperature is 1200 DEG C, and the rate of heat addition is 8min/cm.In rolling process, point rough rolling step and finish rolling stage are carried out, and roughing start rolling temperature is 1090 DEG C, and finishing temperature is 980 DEG C, and single pass reduction ratio is more than 20%；Finish rolling start rolling temperature is 960 DEG C, and finishing temperature is 810 DEG C, and single pass reduction ratio is more than 20%.In quenching process, hardening heat is 880 DEG C, and temperature retention time is 60min.In tempering process, temperature is 220 DEG C, and temperature retention time is 140min.
Embodiment 3
A kind of low-alloy high-strength abrasion-resistant stee 3, thickness is 50mm, and the mass percent of its chemical composition is: C:0.17%, Si:0.50%, Mn:1.5%, P:0.015%, S:0.01%, Cr:0.7%, Ni:0.32%, Mo:0.2%, Als:0.01%, Ti:0.02, B:0.004%, surplus is Fe and inevitable impurity.
Described low-alloy high-strength abrasion-resistant stee 3 is prepared by following operation: desulphurised hot metal → converter smelting → application of vacuum → continuous casting → strand heating → rolling → cooling → quenching → tempering → finishing.Wherein, in strand heating process, soaking temperature is 1250 DEG C, and the rate of heat addition is 8min/cm.In rolling process, point rough rolling step and finish rolling stage are carried out, and roughing start rolling temperature is 1080 DEG C, and finishing temperature is 980 DEG C, and single pass reduction ratio is more than 20%；Finish rolling start rolling temperature is 950 DEG C, and finishing temperature is 890 DEG C, and single pass reduction ratio is more than 20%.In quenching process, hardening heat is 900 DEG C, and temperature retention time is 70min.In tempering process, temperature is 250 DEG C, and temperature retention time is 175min.
Embodiment 4
A kind of low-alloy high-strength abrasion-resistant stee 4, thickness is 10mm, and the mass percent of its chemical composition is: C:0.14%, Si:0.20%, Mn:1.1%, P:0.02%, S:0.008%, Cr:0.5%, Ni:0.25%, Mo:0.25%, Als:0.04%, Ti:0.005, B:0.003%, surplus is Fe and inevitable impurity.
Described low-alloy high-strength abrasion-resistant stee 4 is prepared by following operation: desulphurised hot metal → converter smelting → application of vacuum → continuous casting → strand heating → rolling → cooling → quenching → tempering → finishing.Wherein, in strand heating process, soaking temperature is 1190 DEG C, and the rate of heat addition is 7min/cm.In rolling process, point rough rolling step and finish rolling stage are carried out, and roughing start rolling temperature is 1100 DEG C, and finishing temperature is 990 DEG C, and single pass reduction ratio is more than 20%；Finish rolling start rolling temperature is 960 DEG C, and finishing temperature is 810 DEG C, and single pass reduction ratio is more than 20%.In quenching process, hardening heat is 910 DEG C, and temperature retention time is 20min.In tempering process, temperature is 230 DEG C, and temperature retention time is 50min.
The low-alloy high-strength abrasion-resistant stee 1～4 of embodiment 1～4 is detected case hardness, then tension test has been carried out by GB228-87 " metal stretching experimental technique " regulation, with the average results carrying out series of temperatures impact test, mechanical property and low-temperature impact work by GB/T229-2007 " metal material Charpy pendulum impact test method " regulationSuch as table 1Shown in:
Table 1Embodiment 1～4 mechanics properties testing result
FromTable 1It can be seen that in the case of ensureing high intensity, the low-alloy high-strength abrasion-resistant stee 1-4 of the present invention also has higher ductility and the contraction percentage of area while ensureing case hardness, and low-temperature impact work can be more than 30J.
The low-alloy high-strength abrasion-resistant stee 1 of embodiment 1 is being taken 0.2mm thin slice at distance surface 1/4, is making sample for use in transmitted electron microscope through twin-jet electropolishing is thinning, in JEM-200FX III type transmission electron microscope, observe its metallographic structure, resultSuch as figure 2Shown in, for tempered martensite.
By the low-alloy high-strength abrasion-resistant stee 1 of embodiment 1 according toFigure 1The 1-7 point arranged carries out residual stress detection, resultSuch as table 2Shown in:
Table 2The low-alloy high-strength abrasion-resistant stee 1 residual stress at 1～No. 7 point
Low-alloy high-strength abrasion-resistant stee 2～4 is carried out same detection and can obtain similar results.FromTable 2It can be seen that the present invention is optimizing the colleague of residual stress, make residual stress distribution uniform.
In sum, the low-alloy high-strength abrasion-resistant stee of the present invention is while optimizing residual stress, ensure that abrasion-resistant stee superficial hardness number is more than 360, tensile strength is at more than 1200Mpa,-20 DEG C of ballistic works are more than 30J, therefore there is higher case hardness, it is ensured that its anti-wear performance, there is higher tensile strength and preferable toughness simultaneously.
On the premise of without departing from claims of the present invention protection domain, it is adjusted falling within the scope of protection of the invention to the numerical value in embodiment.
Claims (6)
1. a low-alloy high-strength abrasion-resistant stee, it is characterised in that: described low-alloy high-strength
The mass percent of abrasion-resistant stee chemical composition is: C:0.14～0.17%, Si:0.20～0.50%,
Mn:1.1～1.5%, P≤0.02%, S≤0.01%, Cr:0.5～0.7%, Ni:0.25～0.32%,
Mo:0.2～0.3%, Als:0.01～0.04%, Ti:0.005～0.02, B:0.002～0.004%,
Surplus is Fe and inevitable impurity.
Low-alloy high-strength abrasion-resistant stee the most according to claim 1, it is characterised in that: institute
Stating low-alloy high-strength abrasion-resistant stee thickness is 10～50mm.
3. preparing a method for low-alloy high-strength abrasion-resistant stee described in claim 1, it is pressed
Following operation is carried out: desulphurised hot metal → converter smelting → application of vacuum → continuous casting → strand heating →
Rolling → cooling → quenching → tempering → finishing, it is characterised in that: in tempering process, tempering temperature
Degree is 220 DEG C～250 DEG C, and temperature retention time is 3.5～5.0min/mm × thickness of slab.
The most according to claim 3, the preparation method of low-alloy high-strength abrasion-resistant stee, it is special
Levying and be: in described quenching process, hardening heat is 880 DEG C～910 DEG C, and temperature retention time is
1.4～2.0min/mm × thickness of slab.
The most according to claim 3, the preparation method of low-alloy high-strength abrasion-resistant stee, it is special
Levying and be: in described strand heating process, soaking temperature is 1190 DEG C～1250 DEG C, heating speed
Rate is 7～10min/cm.
The most according to claim 3, the preparation method of low-alloy high-strength abrasion-resistant stee, it is special
Levy and be: in described rolling process, roughing start rolling temperature >=1080 DEG C, finishing temperature >=980
DEG C, single pass reduction ratio is more than 20%；Finish rolling start rolling temperature≤960 DEG C, finishing temperature 810
DEG C～890 DEG C, single pass reduction ratio be more than 20%.
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107058882A (en) * | 2017-04-26 | 2017-08-18 | 山东钢铁股份有限公司 | A kind of special think gauge wear-resisting steel plate and preparation method thereof |
| CN113227432A (en) * | 2018-12-19 | 2021-08-06 | 株式会社Posco | Steel material for motor vehicle brake disc having excellent wear resistance and high temperature strength and method for manufacturing same |
| CN113249644A (en) * | 2021-03-24 | 2021-08-13 | 江阴兴澄特种钢铁有限公司 | Thin NM450 steel plate and manufacturing method thereof |
| CN114525450A (en) * | 2022-02-08 | 2022-05-24 | 南京钢铁股份有限公司 | Wear-resistant steel and production method thereof |
| CN117327985A (en) * | 2023-10-24 | 2024-01-02 | 包头钢铁（集团）有限责任公司 | B, ti microalloyed hot rolled bainite steel rail and manufacturing method thereof |
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| JP2009030093A (en) * | 2007-07-26 | 2009-02-12 | Jfe Steel Kk | Wear resistant steel sheet excellent in low temperature tempering brittle crack resistance |
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| JP2009030093A (en) * | 2007-07-26 | 2009-02-12 | Jfe Steel Kk | Wear resistant steel sheet excellent in low temperature tempering brittle crack resistance |
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN107058882A (en) * | 2017-04-26 | 2017-08-18 | 山东钢铁股份有限公司 | A kind of special think gauge wear-resisting steel plate and preparation method thereof |
| CN113227432A (en) * | 2018-12-19 | 2021-08-06 | 株式会社Posco | Steel material for motor vehicle brake disc having excellent wear resistance and high temperature strength and method for manufacturing same |
| CN113227432B (en) * | 2018-12-19 | 2023-07-11 | 浦项股份有限公司 | Steel material for motor vehicle brake disc having excellent wear resistance and high temperature strength and method for producing the same |
| CN113249644A (en) * | 2021-03-24 | 2021-08-13 | 江阴兴澄特种钢铁有限公司 | Thin NM450 steel plate and manufacturing method thereof |
| CN114525450A (en) * | 2022-02-08 | 2022-05-24 | 南京钢铁股份有限公司 | Wear-resistant steel and production method thereof |
| CN117327985A (en) * | 2023-10-24 | 2024-01-02 | 包头钢铁（集团）有限责任公司 | B, ti microalloyed hot rolled bainite steel rail and manufacturing method thereof |
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