CN107217202B - A kind of 500 grades of Brinell hardness of abrasion-resistant stee and its manufacturing method - Google Patents
A kind of 500 grades of Brinell hardness of abrasion-resistant stee and its manufacturing method 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
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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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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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
- C22C38/44—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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
The invention discloses a kind of 500 grade wear-resisting steels of Brinell hardness, and the chemical component of steel is by mass percentage are as follows: C 0.25~0.28%, Si 0.22~0.28%, Mn 1.15~1.24%, P≤0.01%, S≤0.005%, Cr 0.2~0.25%, Cu 0.01~0.015%, Al 0.03~0.05%, Ni 0.04~0.045%, Mo 0.01~0.02%, Ti 0.03~0.04%, V 0.007~0.018%, B≤0.004%, remaining is iron and inevitable impurity.The present invention also provides a kind of manufacturing methods of 500 grade wear-resisting steel of Brinell hardness.The present invention makes abrasion-resistant stee have excellent wear and higher toughness, and its surface is made to have uniform compression, enhances its wear-resisting property and anti-fatigue performance.
Description
Technical field
The invention belongs to steel and iron manufacturing fields, and in particular to a kind of 500 grade wear-resisting steel of Brinell hardness and its manufacturing method.
Background technique
Abrasion-resistant stee is a kind of steel material being widely used under various wear working conditions, and its object is to slow down mechanical part
Attrition, improve life of product, the time of failure behaviour occurs because of abrasion for prolonged mechanical product, it is desirable that with higher
Hardness number is to guarantee the wear resistance under bad working environments.
Residual stress is the key parameter for influencing abrasion-resistant stee and using, and is had directly with the cracking of steel plate and the wearability on surface
Relationship.And common abrasion-resistant stee hardness number is high, interior residual stress is big, and uniformity is bad, it is easy to occur in use
The problem of steel plate cracking and deformation and welding performance difference；In addition, the residual stress on surface also has certain relationship with wearability,
Surface of steel plate then has castering action to the wear-resisting property and fatigue behaviour that improve steel plate if it is compression.Existing Brinell hardness
500 grade wear-resisting steels are there are interior residual stress is big, the bad problem of uniformity.
Summary of the invention
It is an object of the invention to for there are residual stress for tensile stress or to answer in existing 500 grade wear-resisting steel of Brinell hardness
Force value is smaller, and uniformity is bad, and steel plate cracking easily occurs in use and deformation, the disadvantage of welding performance difference provide
A kind of 500 grade wear-resisting steel of Brinell hardness and its manufacturing method, the abrasion-resistant stee and manufacturing method are by having larger shadow to residual stress
The control of the elements such as loud important chemical component C, Si, Mn, Cr, B, and using reasonable quenching, tempering heat treatment process, make resistance to
Steel is ground while possessing excellent wear and higher toughness, there is uniform compression on its surface, it is wear-resisting to further enhance its
Performance and anti-fatigue performance.
The technical scheme adopted by the invention is that:
A kind of 500 grade wear-resisting steel of Brinell hardness, the chemical component of steel is by mass percentage are as follows: C 0.25~0.28%, Si
0.22~0.28%, Mn 1.15~1.24%, P≤0.01%, S≤0.005%, Cr 0.2~0.25%, Cu 0.01~
0.015%, Al 0.03~0.05%, Ni 0.04~0.045%, Mo 0.01~0.02%, Ti 0.03~0.04%, V
0.007~0.018%, B≤0.004%, remaining is iron and inevitable impurity.
According to the above scheme, the yield strength of the abrasion-resistant stee be 1400Mpa~1520Mpa, tensile strength be 1730~
The ball hardness number of 1800Mpa, abrasion-resistant stee reach 510 or so.
Carbon (C) content of the invention is 0.25~0.28%.Carbon is to influence wear-resisting hardness of steel, hardness, toughness and harden ability
Important element, and influence the mostly important element of steel microscopic structure.As carbon content increases, the hardness of steel increases, impact
Toughness is remarkably decreased, and wearability is gradually increased.Carbon content is excessively high, and the carbide content in steel is excessive, and what is formed after heat treatment is high
Carbon lamellar martensite, the hardness of steel is high and toughness is low, and cracking is easy in heat treatment process, this point especially it is noted that；Carbon contains
Measure too low, the hardenability of steel is insufficient, and hardness is too low, and wearability is insufficient.
Silicon (Si) content of the invention is 0.22~0.28%, in steelmaking process, is used as reducing agent and deoxidier.Si
It is non-carbide forming element, is to be present in ferrite or austenite in the form of solid solution.Therefore it can be mentioned with reinforced ferrite
The intensity and hardness of Gao Gang, while the critical cooling rate of steel can be reduced, improve the harden ability of steel.Returning for steel also can be improved in Si
Fiery stability and inoxidizability.The intensity of solid solution and the effect of cold deformation hardening ratio are extremely strong in its raising steel, are only second to
Phosphorus, but also reduce the toughness and plasticity of steel to a certain extent simultaneously.In addition, silicon makes steel in banded structure, make the transverse direction of steel
Performance is lower than longitudinal performance.But silicone content is excessively high to will appear granular ferrite, reduces the toughness of steel and is also easy to produce hardening flaw；
And retained austenite dramatically increases, and reduces the hardness of steel.When the content of Si is higher, Fe3C may be made to decompose, keep C free
And exist in non-graphitic state, that is, there is so-called graphitizing.In annealing, surface is also easy decarburization.
The content of manganese (Mn) of the invention is 1.15~1.24%.Mn is good deoxidier and desulfurizing agent, can eliminate or
Red brittleness caused by weakening because of sulphur, so as to improve the hot-working character of steel.Mn and iron form solid solution, improve ferrite in steel
With the hardness and strength of austenite, strengthen matrix；It is again simultaneously carbide former, into replacing a part of iron in cementite
Atom generates Mn3C, it and Fe3C can be mutually dissolved, and (Fe Mn) is formed in steel3C-type compound, to improve the strong of steel
Degree, hardness and wearability.Mn can reduce critical cooling rate, promote martensite to be formed, improve the harden ability of steel.Manganese in steel by
In reducing critical transition temperature, plays the role of refining pearlite, also play indirectly and improve pearlitic steel intensity.Manganese
Expand the γ phase region in carbon iron balance phasor, it makes, and steel is formed and the ability of stable austenite tissue is only second to nickel.After quenching easily
Obtain martensitic structure.But manganese is superheated susceptivity element, and heating temperature is excessively high when quenching can cause coarse grains；Manganese is solidifying
When segregation coefficient it is larger, it is easy in crystal boundary segregation, have an adverse effect to the performance of steel, and will lead in the quenching structure of steel
Remained austenite content increases, so manganese content control is between 1.15~1.24%.
Content≤0.01% of phosphorus (P) of the invention, content≤0.005% of sulphur (S).Sulphur, which is present in steel, can make steel
What is become is hot-short, and phosphorus is also easy to produce segregation in crystallization process, so that the regional area generation in steel is cold short.Sulphur, phosphorus are for resistance to
Grinding for residual stress of steel controls is objectionable impurities elements, and should do the best elimination.
The content of chromium (Cr) of the invention is 0.2~0.25%.Chromium is conducive to the solution strengthening of steel and is suitable for carbide
It is formed, and then improves elevated temperature strength, hardness and the wear-resisting property of steel.Chromium increases the harden ability of steel, especially reasonably combined with manganese, silicon
Harden ability can be greatly improved, but also increases steel belt roof bolt brittleness tendency simultaneously.Chromium can be solid-solution in ferrite and generate solid solution by force
Change effect, improves the tensile strength and yield point of weld metal.But its content is more than 0.8%, and weld metal toughness can be made obvious
Decline.
The content 0.01~0.015% of copper (Cu) of the invention.It is rotten that copper can improve the anti-atmosphere of ordinary low-alloy steel in steel
Corrosion energy improves weldability, mouldability and machinability etc..But it is easy to produce that " copper brittleness is existing when copper content is more than 0.015
As ".The Morrison of the polite western University material engineering department of Britain is pointed out, when steel billet is added with 0.5% total amount in Cu and Ni simultaneously,
Impact property in steel is without damage.
The content of nickel (Ni) of the invention is 0.04~0.045%.Nickel and carbon do not form carbide, are to form and stablize Austria
The main alloy element of family name's body, certain nickel, which is added, can be improved harden ability, retain the tissue of steel at normal temperature a small amount of remaining difficult to understand
Family name's body, to improve its toughness.Nickel element can be improved the impact flexibility of steel itself, especially improve to the low-temperature impact of steel
It is larger.
The content of molybdenum (Mo) of the invention is 0.01~0.02%.Mo is in steel in the form of solid solution phase and Carbide Phases
In the presence of.Critical cooling rate can be reduced, promotes martensite to be formed, improves the harden ability of steel.MoC is formed with C, improves the hard of steel
Degree.And strengthen matrix by solution strengthening, the density of hardening phase is improved, while also improving the stability of carbide, to steel
Intensity generates advantageous effect.Influence to temper brittleness is rather complicated, exists as single alloying element, improves returning for steel
Fiery brittleness, but when leading to the element of temper brittleness with other and deposit, molybdenum reduces again or inhibits Temper brittleness caused by other elements
Property.
The content of aluminium (Al) of the invention is 0.03~0.05%.Aluminium is that deoxidier is commonly used in steel.It is added on a small quantity in steel
Aluminium can refine crystal grain, improve impact flexibility.
The content of titanium (Ti) of the invention is 0.03~0.04%.Titanium improves the strong of steel by refinement crystal grain and precipitation strength
Degree, titanium generates the TiN particle of disperse under continuous casting cooling condition, can be significant in welding heat affected zone since its fusing point is very high
Inhibit crystal grain to grow up, adds trace amount of titanium that can significantly improve the toughness of heat affected area.
The content 0.007~0.018% of vanadium (V) of the invention.Vanadium improves the intensity of steel, suitable V by refinement crystal grain
Content can be improved the wearability of matrix, but the increase On Impact Toughness of V content also has an impact.
Content≤0.004% of boron (B) of the invention.Trace B can be adsorbed on austenite grain boundary, reduce the energy of crystal boundary
Amount, improves the harden ability of steel.
The present invention also provides the manufacturing methods of above-mentioned 500 grade wear-resisting steel of Brinell hardness comprising smelting process and rolling work
Two steps of skill；
The step of smelting process are as follows: blast-melted → desulfurizing iron → converter top bottom blowing → Argon → LHF
It is sent under furnace processing (three subsidiary factories) → RH (SiCa) processing → continuous casting → slab inspection → slab；
The step of rolling mill practice are as follows: slab examination → slab secondary cut → slab cleaning → slab heating → rolling
→ cooling → quenching → lonneal → finishing → inspection storage；
It is characterized by:
In heating of plate blank step, in order to guarantee that microalloy element sufficiently dissolves and certain autstenitic grain size, subtract
Low residual stress is unevenly distributed possibility, and soaking temperature uses 1180 DEG C~1240 DEG C, and the rate of heat addition is 8~12min/cm；
In milling step, start rolling temperature >=1035 DEG C of milling step, finishing temperature >=990 DEG C, single pass reduction ratio
Greater than 20%, minuent, which is suppressed, can refine steel plate center portion crystal grain, so that tissue and residual stress distribution tend to be equal in plate thickness
It is even；
In quenching Step, hardening heat is 860 DEG C -880 DEG C, soaking time 9-12min；
In lonneal step, 190 DEG C -225 DEG C of tempering temperature, soaking time 6.0~7.5min/mm* plate thickness, low temperature
Tempering remains the stress that presses to of plate surface, and sufficient tempering time plays the homogenization of residual stress distribution in plate
Important function obtains tempered martensite after tempering.
The beneficial effects of the present invention are:
The present invention ensure that abrasion-resistant stee superficial hardness number 510 or so, yield strength is while optimizing residual stress
1400Mpa~1520Mpa, tensile strength about 1730~1800Mpa, therefore surface hardness with higher ensure that its wearability
Can, while tensile strength with higher and preferable toughness；
Carbon (C) content is 0.25~0.28% in present component, and carbon content is excessively high, then the hardness of steel is high and toughness is low,
Cracking is easy in heat treatment process, carbon content is too low, and the hardenability of steel is insufficient, and hardness is too low, and wearability is insufficient；Contain in ingredient
Mn, Cr, Ni, B element the harden ability of steel can be improved, to reduce product in the residual stress gradient of thickness direction, inhibit
Cracking；Ti, Al, V in ingredient play Grain refinement, make in steel residual stress distribution more evenly；
The present invention is using 860 DEG C of -880 DEG C of quenchings, soaking time 9-12min, and is returned using 190 DEG C of -225 DEG C of low temperature
Fire, soaking time 6.0~7.5min/mm* plate thickness, so that remain surface of steel plate presses to stress, to improving the wear-resisting of steel plate
Performance and fatigue behaviour are obviously improved effect, and sufficient tempering time makes residual stress in plate more uniform, is conducive to
Reduce the tearing tendency of steel plate.
Detailed description of the invention
Present invention will be further explained below with reference to the attached drawings and examples, in attached drawing:
Fig. 1 is the residual stress measuring point value arrangement map using the steel plate obtained after this method；
Fig. 2 is metallographic textura epidermoidea of the embodiment 1 using the steel plate obtained after this method；
Fig. 3 is metallographic core tissue of the embodiment 1 using the steel plate obtained after this method；
Fig. 4 is metallographic textura epidermoidea of the embodiment 2 using the steel plate obtained after this method；
Fig. 5 is metallographic core tissue of the embodiment 2 using the steel plate obtained after this method.
Specific embodiment
In order to make the objectives, technical solutions, and advantages of the present invention clearer, with reference to the accompanying drawings and embodiments, right
The present invention is further elaborated.It should be appreciated that described herein, specific examples are only used to explain the present invention, not
For limiting the present invention.
Embodiment 1
A kind of 500 grade wear-resisting steel of Brinell hardness with a thickness of 15mm, chemical component is by mass percentage are as follows: C
0.26%, Si 0.22%, Mn 1.23%, P≤0.005, S≤0.003%, Cr 0.22%, Cu 0.015%, Al
0.05%, Ni 0.043%, Mo 0.015%, Ti 0.03%, V 0.016%, B 0.003, remaining is for iron and inevitably
Impurity.
According to the ratio chemical component carry out 500 grade wear-resisting steel of Brinell hardness manufacture, manufacturing method include smelting process and
Two steps of rolling mill practice；
The step of smelting process are as follows: at blast-melted → desulfurizing iron → converter top bottom blowing → Argon → LHF furnace
It is sent under reason → RH processing → continuous casting → slab inspection → slab；
The step of rolling mill practice are as follows: slab examination → slab secondary cut → slab cleaning → slab heating → rolling → cold
But → quenching → lonneal → finishing → inspection storage；
In the slab heating period, slab is heated using 1210 DEG C of high temperature, heats 150min, the rate of heat addition is
11min/cm；It is rolled using 1040 DEG C of start rolling temperature, finishing temperature is 1200 DEG C, is greater than using single pass reduction ratio
20% pair of slab rolls；Slab after rolling is cooled down；Slab after cooling is subjected to 880 DEG C of high temperature quenchings, is protected
Warm 10min；Quenched slab is subjected to 198 DEG C of lonneals, keeps the temperature 100min.
Tables 1 and 2 is respectively the mechanics for using above method Brinell hardness 500 grade wear-resisting steel obtained with a thickness of 15mm
Performance table and surface residual stress analytical table.
1 mechanical property of table
2 surface residual stress of table
Embodiment 2
A kind of 500 grade wear-resisting steel of Brinell hardness with a thickness of 6mm, chemical component is by mass percentage are as follows: C 0.25%,
Si 0.24%, Mn 1.16%, P≤0.004, S≤0.005%, Cr 0.21%, Cu 0.011%, Al 0.032%, Ni
0.041%, Mo 0.013%, Ti 0.032%, V 0.008%, remaining is iron and inevitable impurity.
According to the ratio chemical component carry out 500 grade wear-resisting steel of Brinell hardness manufacture, manufacturing method include smelting process and
Two steps of rolling mill practice；
The step of smelting process are as follows: at blast-melted → desulfurizing iron → converter top bottom blowing → Argon → LHF furnace
It is sent under reason → RH processing → continuous casting → slab inspection → slab；
The step of rolling mill practice are as follows: slab examination → slab secondary cut → slab cleaning → slab heating → rolling → cold
But → quenching → lonneal → finishing → inspection storage；
In the slab heating period, slab is heated using 1200 DEG C of high temperature, heats 50min, rate of heat addition 9min/
cm；It is rolled using 1070 DEG C of start rolling temperature, finishing temperature is 995 DEG C, is greater than 20% pair of casting using single pass reduction ratio
Base is rolled；Slab after rolling is cooled down；Slab after cooling is subjected to 875 DEG C of high temperature quenchings, keeps the temperature 12min；
Quenched slab is subjected to 195 DEG C of lonneals, keeps the temperature 40min.
Table 3 and table 4 are respectively the mechanics using above method Brinell hardness 500 grade wear-resisting steel obtained with a thickness of 15mm
Performance table and surface residual stress analytical table.
3 mechanical property of table
4 surface residual stress of table
Embodiment 3
A kind of 500 grade wear-resisting steel of Brinell hardness with a thickness of 8mm, chemical component is by mass percentage are as follows: C 0.27%,
Si 0.25%, Mn 1.19%, P≤0.002, S≤0.001%, Cr 0.24%, Cu 0.013%, Al 0.04%, Ni
0.042%, Mo 0.019%, Ti 0.038%, V 0.011%, remaining is iron and inevitable impurity.
According to the ratio chemical component carry out 500 grade wear-resisting steel of Brinell hardness manufacture, manufacturing method include smelting process and
Two steps of rolling mill practice；
The step of smelting process are as follows: at blast-melted → desulfurizing iron → converter top bottom blowing → Argon → LHF furnace
It is sent under reason → RH processing → continuous casting → slab inspection → slab；
The step of rolling mill practice are as follows: slab examination → slab secondary cut → slab cleaning → slab heating → rolling → cold
But → quenching → lonneal → finishing → inspection storage；
In the slab heating period, slab is heated using 1230 DEG C of high temperature, heats 30min, rate of heat addition 8min/
cm；It is rolled using 1080 DEG C of start rolling temperature, finishing temperature is 1155 DEG C, is greater than 20% pair of casting using single pass reduction ratio
Base is rolled；Slab after rolling is cooled down；Slab after cooling is subjected to 868 DEG C of high temperature quenchings, keeps the temperature 11min；
Quenched slab is subjected to 220 DEG C of lonneals, keeps the temperature 50min.
Table 5 and table 6 are respectively the mechanics using above method Brinell hardness 500 grade wear-resisting steel obtained with a thickness of 8mm
Performance table and surface residual stress analytical table.
5 mechanical property of table
6 surface residual stress of table
From table 1 to table 6 as can be seen that ensure that wear-resisting steel surface is hard using this method while optimizing residual stress
For angle value 510 or so, the yield strength of abrasion-resistant stee is 1400Mpa~1520Mpa, and tensile strength is 1730~1800Mpa, -20
DEG C ballistic work is more than 25J, therefore surface hardness with higher ensure that its wear-resisting property, while tensile strength with higher
And preferable toughness.
Find out from Fig. 1 to Fig. 5, microstructure is tempered martensite, and is distributed more uniform.
It should be understood that for those of ordinary skills, it can be modified or changed according to the above description,
And all these modifications and variations should all belong to the protection domain of appended claims of the present invention.
Claims (2)
1. a kind of manufacturing method of 500 grade wear-resisting steel of Brinell hardness, it is characterised in that: 500 grades of the Brinell hardness is wear-resisting
The chemical component of steel is by mass percentage are as follows: C 0.25%, Si 0.22 ~ 0.28%, Mn 1.15 ~ 1.24%, P≤0.01%, S≤
0.005%, Cr 0.2 ~ 0.25%, Cu 0.01 ~ 0.015%, Al 0.03 ~ 0.05%, Ni 0.04 ~ 0.045%,
Mo0.01 ~ 0.02%, Ti 0.03 ~ 0.04%, V 0.007 ~ 0.018%, B 0.003 ~ 0.004%, remaining is for iron and unavoidably
Impurity；
The manufacturing method includes two steps of smelting process and rolling mill practice；
The step of smelting process are as follows: at blast-melted → desulfurizing iron → converter top bottom blowing → Argon → LHF furnace
It is sent under reason → RH processing → continuous casting → slab inspection → slab；
The step of rolling mill practice are as follows: slab examination → slab secondary cut → slab cleaning → slab heating → rolling → cold
But → quenching → lonneal → finishing → inspection storage；
In heating of plate blank step, soaking temperature is 1180 DEG C ~ 1240 DEG C, and the rate of heat addition is 8 ~ 12min/cm；
In milling step, start rolling temperature >=1035 DEG C of milling step, finishing temperature >=990 DEG C, single pass reduction ratio is greater than
20%；
In quenching Step, hardening heat is 860 DEG C -880 DEG C, soaking time 9-12min；
In lonneal step, 190 DEG C -225 DEG C of tempering temperature, soaking time 6.0 ~ 7.5min/mm* plate thickness.
2. the manufacturing method according to claim 1, it is characterised in that: the yield strength of the abrasion-resistant stee is 1400Mpa
~ 1520 Mpa, tensile strength are 1730 ~ 1800Mpa.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710591249.8A CN107217202B (en) | 2017-07-19 | 2017-07-19 | A kind of 500 grades of Brinell hardness of abrasion-resistant stee and its manufacturing method |
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| CN108179350B (en) * | 2017-12-25 | 2019-12-31 | 南京钢铁股份有限公司 | Low-cost short-production-period preparation method of wear-resistant steel |
| CN108754330A (en) * | 2018-06-21 | 2018-11-06 | 武汉钢铁有限公司 | 550 grade wear-resisting steel of Brinell hardness and manufacturing method |
| CN109182666A (en) * | 2018-11-12 | 2019-01-11 | 南京钢铁股份有限公司 | A kind of width thin gauge NM450 abrasion-resistant stee steel plate and manufacturing method |
| CN113637894A (en) * | 2021-06-30 | 2021-11-12 | 武汉钢铁有限公司 | Leveling-free and tempering-free HB 450-grade wear-resistant steel and production method thereof |
| CN114737128A (en) * | 2022-04-21 | 2022-07-12 | 南京钢铁股份有限公司 | NM 300-grade wear-resistant steel and production method thereof |
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