CN105002439A - Wear-resistant steel with 400-level Brinell hardness and manufacturing method thereof - Google Patents
Wear-resistant steel with 400-level Brinell hardness and manufacturing method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 102
- 239000010959 steel Substances 0.000 title claims abstract description 102
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 28
- 238000010791 quenching Methods 0.000 claims abstract description 21
- 238000000034 method Methods 0.000 claims abstract description 20
- 238000010438 heat treatment Methods 0.000 claims abstract description 18
- 230000000171 quenching effect Effects 0.000 claims abstract description 17
- 229910052742 iron Inorganic materials 0.000 claims abstract description 13
- 239000000126 substance Substances 0.000 claims abstract description 13
- 238000001816 cooling Methods 0.000 claims abstract description 10
- 238000005096 rolling process Methods 0.000 claims abstract description 10
- 238000005496 tempering Methods 0.000 claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 239000000203 mixture Substances 0.000 claims description 16
- 229910052748 manganese Inorganic materials 0.000 claims description 15
- 238000002791 soaking Methods 0.000 claims description 14
- 229910052759 nickel Inorganic materials 0.000 claims description 13
- 229910052804 chromium Inorganic materials 0.000 claims description 12
- 229910052796 boron Inorganic materials 0.000 claims description 11
- 229910052698 phosphorus Inorganic materials 0.000 claims description 10
- 229910052719 titanium Inorganic materials 0.000 claims description 10
- 229910052710 silicon Inorganic materials 0.000 claims description 9
- 238000003801 milling Methods 0.000 claims description 4
- 238000009749 continuous casting Methods 0.000 claims description 3
- 238000003723 Smelting Methods 0.000 claims description 2
- 238000007664 blowing Methods 0.000 claims description 2
- 230000003009 desulfurizing effect Effects 0.000 claims description 2
- 238000005336 cracking Methods 0.000 abstract description 6
- 238000002844 melting Methods 0.000 abstract 1
- 230000008018 melting Effects 0.000 abstract 1
- 239000011572 manganese Substances 0.000 description 18
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 18
- 229910052799 carbon Inorganic materials 0.000 description 14
- 239000011651 chromium Substances 0.000 description 13
- 239000000463 material Substances 0.000 description 13
- 239000010936 titanium Substances 0.000 description 12
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 11
- 229910052750 molybdenum Inorganic materials 0.000 description 9
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 8
- 238000009826 distribution Methods 0.000 description 8
- 229910052720 vanadium Inorganic materials 0.000 description 8
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 7
- 229910001566 austenite Inorganic materials 0.000 description 7
- 239000010703 silicon Substances 0.000 description 7
- 239000013078 crystal Substances 0.000 description 6
- 238000009413 insulation Methods 0.000 description 6
- 229910000734 martensite Inorganic materials 0.000 description 6
- 229910000859 α-Fe Inorganic materials 0.000 description 5
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 4
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 4
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 4
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 4
- 239000005864 Sulphur Substances 0.000 description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 239000011733 molybdenum Substances 0.000 description 4
- 239000011574 phosphorus Substances 0.000 description 4
- 230000002829 reductive effect Effects 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- GPPXJZIENCGNKB-UHFFFAOYSA-N vanadium Chemical compound [V]#[V] GPPXJZIENCGNKB-UHFFFAOYSA-N 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 229910001567 cementite Inorganic materials 0.000 description 2
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 2
- 238000005457 optimization Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 description 2
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 1
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- 238000005275 alloying Methods 0.000 description 1
- -1 and after tempering Substances 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 230000002929 anti-fatigue Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
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- 235000003599 food sweetener Nutrition 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- CNEOGBIICRAWOH-UHFFFAOYSA-N methane;molybdenum Chemical compound C.[Mo] CNEOGBIICRAWOH-UHFFFAOYSA-N 0.000 description 1
- QMQXDJATSGGYDR-UHFFFAOYSA-N methylidyneiron Chemical compound [C].[Fe] QMQXDJATSGGYDR-UHFFFAOYSA-N 0.000 description 1
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- 229920001296 polysiloxane Polymers 0.000 description 1
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- 239000003765 sweetening agent Substances 0.000 description 1
- 238000007669 thermal treatment Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
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Abstract
The invention discloses wear-resistant steel with 400-level Brinell hardness and a manufacturing method thereof. The steel comprises, by mass, 0.14-0.21% of C, 0.20-0.40% of Si, 0.9-1.4% of Mn, 0.015% of P or less, 0.008% of S or less, 0.5-0.8% of Cr, 0.05-0.08% of Ni, 0.2-0.4% of Mo, 0.02-0.05% of Als, 0.02-0.03% of Ti, 0.02% of V or less, 0.005% of B or less, and the balance iron and inevitable impurities. The manufacturing method includes the following steps that the chemical components are proportionally subjected to vacuum melting and cast into blanks, and then plate blank heating, rolling, cooling, quenching and low-temperature tempering are performed to obtain finished steel plates. The wear-resistant steel is good in residual stress uniformity, free of cracking or deformation in the use process, resistant to wear and long in service life.
Description
Technical field
The invention belongs to iron and steel and manufacture field, be specifically related to a kind of Brinell hardness 400 grade wear-resisting steel and manufacture method thereof.
Background technology
Wear resisting steel is the class ferrous materials be widely used under various wear working condition, its object is to the attrition slowing down mechanical part, improve the life-span of product, there is the time of failure behaviour in prolonged mechanical product, requires to have higher hardness value to ensure the wear resistance under bad working environments because of wearing and tearing.
Unrelieved stress is the key parameter affecting wear resisting steel use, has direct relation with the cracking of steel plate and the wear resistance on surface.And common wear resisting steel hardness value is high, in it, unrelieved stress is large, and homogeneity is bad, is easy to the problem that steel plate cracking in use occurs; In addition, the unrelieved stress on surface also has certain relation with wear resistance, and surface of steel plate if stress, then has castering action to the wear resisting property and fatigue property that improve steel plate.
Summary of the invention
The object of the present invention is to provide a kind of Brinell hardness 400 grade wear-resisting steel and manufacture method thereof, manufacture method is by there being the control of the element such as important chemical composition C, Si, Mn, Cr, B of considerable influence to unrelieved stress, and adopt reasonably quenching, tempering heat treatment process, make wear resisting steel while having excellent wear and higher toughness, on its surface, there is even stress, strengthen its wear resisting property and anti-fatigue performance further; , in use there is not cracking and distortion in the unrelieved stress good uniformity of this wear resisting steel, wear-resisting, long service life.
The present invention is achieved in that
A kind of Brinell hardness 400 grade wear-resisting steel, the chemical composition of steel is by mass percentage: C 0.14 ~ 0.21%, Si0.20 ~ 0.40%, Mn 0.9 ~ 1.4%, P≤0.015%, S≤0.008%, Cr 0.5 ~ 0.8%, Ni 0.05 ~ 0.08%, Mo 0.2 ~ 0.4, Als 0.02 ~ 0.05%, Ti 0.02 ~ 0.03, V≤0.02%, B≤0.005%, all the other are iron and inevitable impurity.
Carbon of the present invention (C) content is 0.14 ~ 0.21%.Carbon is the important element affecting wear resisting steel intensity, hardness, toughness and hardening capacity, and being also affects the of paramount importance element of steel microscopic structure; Along with carbon content increases, the hardness of steel increases, and impelling strength significantly declines, and wear resistance improves gradually; Carbon content is too high, and the carbide amount in steel is too much, and what formed after thermal treatment is high-carbon plate 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 wear resistance is not enough.
Silicon of the present invention (Si) content is 0.20 ~ 0.40%.In steelmaking process, silicon is used as reductive agent and reductor.Silicon is non-carbide forming element, is to be present in ferrite or austenite with the form of sosoloid.Therefore can reinforced ferrite, improve intensity and the hardness of steel, the critical cooling velocity of steel can be reduced simultaneously, improve the hardening capacity of steel.Silicon also can improve steel belt roof bolt stability and oxidation-resistance, and it is extremely strong that its improves the intensity of sosoloid and the effect of cold deformation cementation index in steel, is only second to phosphorus, but also reduces toughness and the plasticity of steel to a certain extent simultaneously.In addition, silicon makes steel be banded structure, makes the lateral performance of steel lower than longitudinal performance.But silicone content is too high there will be granular ferrite, the toughness of steel is made to reduce and easily produce quenching crack; And residual austenite significantly increases, the hardness of steel is reduced.When the content of silicon is higher, iron carbide (Fe may be made
3c) decompose, make carbon free and exist in non-graphitic state, namely having so-called graphitizing.When annealing, surface is easily decarburization also.
The content of manganese of the present invention (Mn) is 0.9 ~ 1.4%.Manganese is good reductor and sweetening agent, can eliminate or weaken because of the red brittleness caused by sulphur, thus improve the hot workability of steel.Manganese and iron form sosoloid, improve ferrite and austenitic hardness and intensity in steel, strengthening matrix; Be again carbide forming element simultaneously, enter in cementite and replace a part of iron atom, generate manganess carbide (Mn
3c), it and iron carbide (Fe
3c) mutually can dissolve, in steel, be formed in alloy (carbide (Fe Mn)
3c type compound), thus the intensity of raising steel, hardness and wear resistance.Manganese can reduce critical cooling velocity, promotes that martensite is formed, improves the hardening capacity of steel.Manganese owing to reducing critical transition temperature, plays the effect of refine pearlite in steel, also indirectly plays the effect improving perlitic steel intensity.Manganese expands the γ phase region in carbon iron balance phasor, and it makes steel be formed and the ability of stable austenite tissue is only second to nickel.Be easy to get after quenching martensitic stucture.But manganese is superheated susceptivity element, during quenching, the too high meeting of Heating temperature causes coarse grains; Manganese segregation coefficient when solidifying is comparatively large, is easy at Grain Boundary Segregation, has a negative impact to the performance of steel, and remained austenite content in the quenching structure of steel can be caused to increase, so Fe content controls between 0.9 ~ 1.4%.
Content≤0.015% of phosphorus of the present invention (P), content≤0.008% of sulphur (S).Sulphur is present in iron and steel steel can be made to become hot-short, and phosphorus easily produces segregation in crystallisation process, thus the regional area in steel produces cold short.Sulphur, phosphorus are detrimental impurity elements for wear resisting steel residual stress control, should eliminate as possible.
The content of chromium of the present invention (Cr) is 0.5 ~ 0.8%.Chromium is conducive to the solution strengthening of steel and the formation of suitable carbide, and then the hot strength of raising steel, hardness and wear resisting property.Chromium increases the hardening capacity of steel, especially with manganese, silicon is reasonably combined greatly can improve hardening capacity, but also increases steel belt roof bolt fragility tendency simultaneously.Chromium 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%, weld metal toughness can be made obviously to decline.
The content of nickel of the present invention (Ni) is 0.05 ~ 0.08%.Nickel and carbon do not form carbide, and be the main alloy element of formation and stable austenite, adding certain nickel can improve hardening capacity, makes organizing of steel retain a small amount of residual austenite at normal temperatures, to improve its toughness.Nickel element can improve the impelling strength of steel itself, especially improves larger to the low-temperature impact of steel.
The content of molybdenum of the present invention (Mo) is 0.2 ~ 0.4.Molybdenum exists with the form of solid solution phase and Carbide Phases in steel.Can critical cooling velocity be reduced, promote that martensite is formed, improve the hardening capacity of steel.Form molybdenum carbide (MoC) with carbon (C), improve the hardness of steel; And strengthen matrix by solution strengthening, improve the density of sclerosis phase, also improve the stability of carbide simultaneously, favourable effect is produced to the intensity of steel.Molybdenum is rather complicated on the impact of temper brittleness, exists as single alloying element, improves steel belt roof bolt fragility, but when causing the element of temper brittleness with other and deposit, molybdenum reduces again or suppress the temper brittleness that other elements cause.
The content of dissolved aluminum of the present invention (Als) is 0.02 ~ 0.05%.A small amount of dissolved aluminum is added in steel, can crystal grain thinning, improve impelling strength.
The content of titanium of the present invention (Ti) is 0.02 ~ 0.03.Titanium improves the intensity of steel by crystal grain thinning and precipitation strength, titanium generates titanium carbide (TiN) particle of disperse under continuous casting cooling conditions, because its fusing point is very high, at welded heat affecting zone energy significantly inhibiting grain growth, add the toughness that trace amount of titanium significantly can improve heat affected zone.
Content≤0.02% of vanadium of the present invention (V).Vanadium improves the intensity of steel by crystal grain thinning, and appropriate content of vanadium can improve the wear resistance of matrix, but the increase On Impact Toughness of content of vanadium also has impact.
Content≤0.005% of boron of the present invention (B).The boron of trace can be adsorbed on austenite grain boundary, reduces the energy of crystal boundary, improves the hardening capacity of steel.
The present invention also provides the manufacture method of above-mentioned Brinell hardness 400 grade wear-resisting steel, comprise the steps: ultra-clean steel technique carry out smelting → desulfurizing iron → converter top bottom blowing → vacuum-treat → continuous casting becomes slab → heating of plate blank → rolling → cooling → quenching → low-temperaturetempering → steel plate finished product, wherein
In heating of plate blank step, in order to ensure that microalloy element fully dissolves and has certain autstenitic grain size, reduce the uneven possibility of residual stress distribution, soaking temperature adopts 1190 DEG C ~ 1250 DEG C, and heating rate is 8 ~ 10min/cm;
In milling step, start rolling temperature >=1050 DEG C of milling step, finishing temperature >=980 DEG C, single pass draft is greater than 20%, and minuent is suppressed can refinement steel plate heart portion crystal grain, makes tissue and residual stress distribution on sheet metal thickness be tending towards even;
In quenching Step, quenching temperature is 870 DEG C, and soaking time is 1.0 ~ 2.0min/mm* thickness of slab;
In low-temperaturetempering step, tempering temperature is 190 DEG C, and soaking time is 3 ~ 4min/mm* thickness of slab, and what low-temperaturetempering remained plate surface presses to stress, sufficient tempering time plays an important role for the homogenizing of residual stress distribution in sheet material, obtains tempered martensite after tempering.
Present method is carried out vacuum metling by proportioning chemical composition and is cast into base, and then by heating of plate blank to 1190 DEG C ~ 1250 DEG C, be rolled again subsequently, be cooled to room temperature again, carry out quenching more subsequently and low-temperaturetempering obtains the good steel plate of wear resistance, what low-temperaturetempering remained plate surface presses to stress, has obvious castering action to the wear resisting property and fatigue property improving steel plate.
The present invention is while optimization unrelieved stress, and ensure that wear resisting steel superficial hardness number is about 390, tensile strength is about 1300Mpa, has higher surface hardness, ensure that its wear resisting property, has higher tensile strength and good toughness; Sufficient tempering time makes unrelieved stress in sheet material more even, is conducive to the tearing tendency reducing sheet material.
In the present invention, carbon (C) content is 0.14 ~ 0.21%, and carbon content is too high, then the hardness of steel is high and toughness is low, and easily ftracture in heat treatment process, carbon content is too low, and the hardenability of steel is not enough, and hardness is too low, and wear resistance is not enough.The Mn contained in composition, Cr, Ni, B element can improve the hardening capacity of steel, thus reduce the residual stress gradient of product at thickness direction, suppress cracking.Ti, Als, V in composition play Grain refinement, make residual stress distribution in steel evenly.
Beneficial effect of the present invention is:
(1) in heating of plate blank step, soaking temperature adopts 1190 DEG C ~ 1250 DEG C, and heating rate is 8 ~ 10min/cm, ensure that microalloy element fully dissolves, and make slab have certain autstenitic grain size, reduce the possibility of residual stress distribution inequality;
(2), in the operation of rolling, single pass draft is greater than 20%, can refinement steel plate heart portion crystal grain, makes tissue and residual stress distribution on sheet metal thickness even;
(3), in low-temperaturetempering, tempering temperature is 190 DEG C, and soaking time is every 1 millimeter of thickness of slab insulation 3 ~ 4 minutes.What low-temperaturetempering remained plate surface presses to stress, and sufficient tempering time plays an important role for the homogenizing of residual stress distribution in sheet material, and after tempering, steel plate obtains tempered martensite, adds wear resistance;
(4), the Mn, the Cr that contain in steel plate composition, Ni, B element can improve the hardening capacity of steel, thus reduce the residual stress gradient of product at thickness direction, suppresses cracking; Ti, Als, V in composition play Grain refinement, make residual stress distribution in steel evenly.
Accompanying drawing explanation
Fig. 1 is the unrelieved stress point layout figure of the steel plate obtained after using present method.
Embodiment
Below in conjunction with accompanying drawing, the present invention is described further.
Embodiment 1
Thickness is Brinell hardness 400 grade wear-resisting steel of 30mm, and its chemical composition is by mass percentage: C 0.18%, Si0.25%, Mn 1.05%, P 0.014%, S≤0.005%, Cr 0.78%, Ni 0.07%, Mo 0.31%, Als 0.038%, Ti 0.024%, V 0.013%, B 0.002, all the other are iron and inevitable impurity.
Carry out vacuum metling by proportioning chemical composition and be cast into base, adopting 1200 DEG C of high temperature to heat slab, heating 240min; And then adopting the start rolling temperature of 1060 DEG C to be rolled, finishing temperature is 980 DEG C, adopts single pass draft to be greater than 20% pair of slab and is rolled; Cool subsequently; Cooled sheet material is carried out 870 DEG C of quench hots, insulation 30min; Sheet material after quenching is carried out 190 DEG C of low-temperaturetemperings, and insulation 100min, completes the making of wear resisting steel.Table 1 and table 2 are respectively mechanical property table and the surface residual stress analytical table that the thickness adopting aforesaid method to obtain is Brinell hardness 400 grade wear-resisting steel of 30mm.
Table 1 mechanical property
Table 2 surface residual stress (see Fig. 1)
Embodiment 2
Thickness is Brinell hardness 400 grade wear-resisting steel of 20mm, and its chemical composition is by mass percentage: C 0.19%, Si0.31%, Mn 1.2%, P 0.013%, S≤0.005%, Cr 0.68%, Ni 0.07%, Mo 0.29%, Als 0.032%, Ti 0.026%, V 0.017%, B 0.002, all the other are iron and inevitable impurity.
Carry out vacuum metling by proportioning chemical composition and be cast into base, adopt 1200 DEG C and carry out soaking to slab, heat-up time is 160min; Be rolled by slab after heating, start rolling temperature is 1060 DEG C, and finishing temperature is 980 DEG C, and single pass draft is greater than 20%; Cooling; Cooled sheet material is carried out 870 DEG C of quench hots, insulation 20min; Sheet material after quenching is carried out 190 DEG C of low-temperaturetemperings, soaking time 70min, completes the making of wear resisting steel.
Table 3 and table 4 are respectively mechanical property table and the surface residual stress analytical table that the thickness adopting aforesaid method to obtain is Brinell hardness 400 grade wear-resisting steel of 20mm.
Table 3 mechanical property
Table 4 surface residual stress
Embodiment 3
Thickness is Brinell hardness 400 grade wear-resisting steel of 25mm, and its chemical composition is by mass percentage: C 0.17%, Si0.31%, Mn 0.9%, P 0.013%, S≤0.008%, Cr 0.68%, Ni 0.07%, Mo 0.29%, Als 0.032%, Ti 0.026%, V 0.017%, B 0.002, all the other are iron and inevitable impurity.
Carry out vacuum metling by proportioning chemical composition and be cast into base, adopt 1250 DEG C and carry out soaking to slab, heat-up time is 200min; Be rolled by slab after heating, start rolling temperature is 1200 DEG C, and finishing temperature is 980 DEG C, and single pass draft is greater than 30%; Cooling; Cooled sheet material is carried out 870 DEG C of quench hots, insulation 50min; Sheet material after quenching is carried out 190 DEG C of low-temperaturetemperings, soaking time 100min, completes the making of wear resisting steel.
Table 5 and table 6 are respectively mechanical property table and the surface residual stress analytical table that the thickness adopting aforesaid method to obtain is Brinell hardness 400 grade wear-resisting steel of 25mm.
Table 5 mechanical property
Table 6 surface residual stress
Embodiment 4
Thickness is Brinell hardness 400 grade wear-resisting steel of 22mm, and its chemical composition is by mass percentage: C 0.14%, Si0.31%, Mn 0.9%, P 0.013%, S≤0.006%, Cr 0.68%, Ni 0.07%, Mo 0.29%, Als 0.032%, Ti 0.026%, V 0.017%, B 0.002, all the other are iron and inevitable impurity.
Carry out vacuum metling by proportioning chemical composition and be cast into base, adopt 1250 DEG C and carry out soaking to slab, heat-up time is 176min; Be rolled by slab after heating, start rolling temperature is 1200 DEG C, and finishing temperature is 980 DEG C, and single pass draft is greater than 30%; Cooling; Cooled sheet material is carried out 870 DEG C of quench hots, insulation 33min; Sheet material after quenching is carried out 190 DEG C of low-temperaturetemperings, soaking time 77min, completes the making of wear resisting steel.
Table 7 and table 8 are respectively mechanical property table and the surface residual stress analytical table that the thickness adopting aforesaid method to obtain is Brinell hardness 400 grade wear-resisting steel of 22mm.
Table 7 mechanical property
Table 8 surface residual stress
As can be seen from table 1 to table 8, adopt present method while optimization unrelieved stress, ensure that wear resisting steel superficial hardness number is about 390, tensile strength is about 1300Mpa,-20 DEG C of ballistic works are more than 30J, therefore there is higher surface hardness and ensure that its wear resisting property, there is higher tensile strength and good toughness simultaneously.
Wuhan Iron and Steel Plant Brinell hardness 400 rank wear resisting steel output in 2014 is about 8000 tons, and volume of business is about 4,800 ten thousand yuan.The present invention can prevent product from ftractureing, and significantly improves Wear Resistance energy and fatigue property, only calculates by the marginal contribution of 1%, and the about 4,800 ten thousand yuan of * 1%,=48 ten thousand yuan that bring benefits are annual.
Claims (2)
1. Brinell hardness 400 grade wear-resisting steel, is characterized in that the chemical composition of steel is by mass percentage: C 0.14 ~ 0.21%, Si 0.20 ~ 0.40%, Mn 0.9 ~ 1.4%, P≤0.015%, S≤0.008%, Cr 0.5 ~ 0.8%, Ni 0.05 ~ 0.08%, Mo0.2 ~ 0.4, Als 0.02 ~ 0.05%, Ti 0.02 ~ 0.03, V≤0.02%, B≤0.005%, all the other are iron and inevitable impurity.
2. the manufacture method of Brinell hardness 400 grade wear-resisting steel as claimed in claim 1, comprise the steps: ultra-clean steel technique carry out smelting → desulfurizing iron → converter top bottom blowing → vacuum-treat → continuous casting becomes slab → heating of plate blank → rolling → cooling → quenching → low-temperaturetempering → steel plate finished product, it is characterized in that:
In heating of plate blank step, soaking temperature is 1190 DEG C ~ 1250 DEG C, and heating rate is 8 ~ 10min/cm;
In milling step, start rolling temperature >=1050 DEG C of milling step, finishing temperature >=980 DEG C, single pass draft is greater than 20%;
In quenching Step, quenching temperature is 870 DEG C, and soaking time is 1.0 ~ 2.0min/mm* thickness of slab;
In low-temperaturetempering step, tempering temperature is 190 DEG C, and soaking time is 3 ~ 4min/mm* thickness of slab.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201510459563.1A CN105002439B (en) | 2015-07-30 | 2015-07-30 | A kind of grade wear-resisting steel of Brinell hardness 400 and its manufacture method |
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| Application Number | Priority Date | Filing Date | Title |
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| CN201510459563.1A CN105002439B (en) | 2015-07-30 | 2015-07-30 | A kind of grade wear-resisting steel of Brinell hardness 400 and its manufacture method |
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| Publication Number | Publication Date |
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| CN105002439A true CN105002439A (en) | 2015-10-28 |
| CN105002439B CN105002439B (en) | 2017-11-17 |
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| CN105821300A (en) * | 2016-04-08 | 2016-08-03 | 太仓市沪太热处理厂 | Heat treatment process of low-alloy large mold steel |
| CN105970110A (en) * | 2016-05-04 | 2016-09-28 | 武汉钢铁股份有限公司 | Low-alloy high-strength abrasion-resistant steel and preparation method thereof |
| CN106244920A (en) * | 2016-08-08 | 2016-12-21 | 武汉钢铁股份有限公司 | Brinell hardness 450 grade wear-resisting steel and manufacture method thereof |
| CN107217202A (en) * | 2017-07-19 | 2017-09-29 | 武汉钢铁有限公司 | The abrasion-resistant stee and its manufacture method of a kind of 500 grades of Brinell hardness |
| CN110184545A (en) * | 2019-05-24 | 2019-08-30 | 武汉钢铁有限公司 | A kind of Brinell hardness is half through hardening abrasion-resistant stee of 400HB rank low temperature and production method |
| CN110527808A (en) * | 2019-08-26 | 2019-12-03 | 武汉科技大学 | The low temperature residual stress of hot-rolled high-strength strip regulates and controls method |
| CN110646306A (en) * | 2019-11-06 | 2020-01-03 | 湖南华菱湘潭钢铁有限公司 | Method for evaluating segregation of continuous casting billet through hardness |
| CN111621717A (en) * | 2020-07-17 | 2020-09-04 | 攀钢集团研究院有限公司 | Method for controlling surface hardness fluctuation of titanium-containing pickled plate |
| CN114770049A (en) * | 2022-05-13 | 2022-07-22 | 无锡华美新材料有限公司 | Manufacturing method of superhard template for manufacturing 5G communication PCB |
| CN114892089A (en) * | 2022-05-21 | 2022-08-12 | 湖南华菱湘潭钢铁有限公司 | Method for improving hardness uniformity of wear-resistant steel section |
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| CN105821300A (en) * | 2016-04-08 | 2016-08-03 | 太仓市沪太热处理厂 | Heat treatment process of low-alloy large mold steel |
| CN105970110A (en) * | 2016-05-04 | 2016-09-28 | 武汉钢铁股份有限公司 | Low-alloy high-strength abrasion-resistant steel and preparation method thereof |
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| CN106244920B (en) * | 2016-08-08 | 2019-01-22 | 武汉钢铁有限公司 | 450 grade wear-resisting steel of Brinell hardness and its manufacturing method |
| CN107217202A (en) * | 2017-07-19 | 2017-09-29 | 武汉钢铁有限公司 | The abrasion-resistant stee and its manufacture method of a kind of 500 grades of Brinell hardness |
| CN110184545B (en) * | 2019-05-24 | 2020-11-20 | 武汉钢铁有限公司 | Low-temperature semi-through quenched wear-resistant steel with Brinell hardness of 400HB and production method thereof |
| CN110184545A (en) * | 2019-05-24 | 2019-08-30 | 武汉钢铁有限公司 | A kind of Brinell hardness is half through hardening abrasion-resistant stee of 400HB rank low temperature and production method |
| CN110527808A (en) * | 2019-08-26 | 2019-12-03 | 武汉科技大学 | The low temperature residual stress of hot-rolled high-strength strip regulates and controls method |
| CN110527808B (en) * | 2019-08-26 | 2021-05-18 | 武汉科技大学 | Low-temperature residual stress regulation and control method for hot-rolled high-strength strip steel |
| CN110646306A (en) * | 2019-11-06 | 2020-01-03 | 湖南华菱湘潭钢铁有限公司 | Method for evaluating segregation of continuous casting billet through hardness |
| CN111621717A (en) * | 2020-07-17 | 2020-09-04 | 攀钢集团研究院有限公司 | Method for controlling surface hardness fluctuation of titanium-containing pickled plate |
| CN114770049A (en) * | 2022-05-13 | 2022-07-22 | 无锡华美新材料有限公司 | Manufacturing method of superhard template for manufacturing 5G communication PCB |
| CN114770049B (en) * | 2022-05-13 | 2023-12-15 | 无锡华美新材料有限公司 | Manufacturing method of superhard template for manufacturing 5G communication PCB |
| CN114892089A (en) * | 2022-05-21 | 2022-08-12 | 湖南华菱湘潭钢铁有限公司 | Method for improving hardness uniformity of wear-resistant steel section |
| CN114892089B (en) * | 2022-05-21 | 2023-09-05 | 湖南华菱湘潭钢铁有限公司 | Method for improving hardness uniformity of wear-resistant steel section |
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