CN105714188A - Medium-carbon alloy steel wear-resistant material and preparing method thereof - Google Patents
Medium-carbon alloy steel wear-resistant material and preparing 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
- C22C38/02—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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
- C22C33/06—Making ferrous alloys by melting using master alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—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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- 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
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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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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
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Abstract
The invention relates to the field of wear-resistant cast steel, in particular to a medium-carbon alloy steel wear-resistant material and a preparing method thereof. The wear-resistant cast steel comprises, by mass percentage, 0.25%-0.45% of C, 0.5%-1.5% of Si, 0.5%-1.0% of Mn, 1.0%-2.0% of Cr, 1.0%-2.0% of Ti, 1.0%-1.5% of B, 0.1%-0.3% of Mo, smaller than or equal to 0.04% of S, smaller than or equal to 0.04% of P and the balance iron. The Ti element is added so that enough nucleation mass points TiC can be generated by molten steel, and the number of particles of the molten steel is greatly increased; the shape of carbide particles in the wear-resistant material can be more spheroidized, and distribution is more uniform; and the defects that in the prior art, carbide is in several non-ideal forms such as a bulk shape, a flowering shape, a bar shape, a rod shape and a worm shape, and the particles are distributed in the forms such as a chrysanthemum shape are overcome, and the comprehensive performance of the material is improved.
Description
Technical field
The present invention relates to wear-resistant cast steel Material Field, specifically abrasion resistant Mn-W-Ti casting steel and preparation method thereof.
Background technology
nullIt is mostly that application has martensite or the high-abrasive material of bainite matrix or except martensite and bainite at present in high-abrasive material field、Also there is beyond retained austenite matrix the third generation high-abrasive material-cast steel with high chromium exploitation wear-resisting spare part of particulates reinforcements，Owing to also having enhancing phase Cr7C3 of high rigidity in cast steel with high chromium，Its carbide microhardness has reached HV1300～1600，Therefore it has had than front two generation high-abrasive materials-spoken parts in traditional operas cast steel and potassium steel performance and has promoted by a relatively large margin，Hardness can reach HRC60～65，But typically exhibit strip due to its carbide and comparison is thick，Therefore its impact flexibility is general all between 3～7J/cm2，Some also has less than 3J/cm2，Generally ratio is relatively low，Material is the most crisp，Resistance to impact is poor，Thus its comprehensive anti-wear performance is not the most especially desirable.
Along with the operating modes such as some engineering machinery, mining machinery, metallurgical machinery are severe further and equipment maximizes, such as in EQUIPMENT MARKET GUIDE such as sand making machine equipment, hot rolls, more and more urgent to the high-abrasive material demand with more high-wearing feature.In this case, forefathers, through lot of experiments, develop multiple high-abrasive material to manufacture wear-resisting key components and parts, to meet the service demand improving workpiece actual life under bad working environments.
Start to walk to research and develop based on composite abrasion resistance materials such as chromium, manganese, silicon in China, and successfully started to be applied to hot roll wearing piece.Although the research of the aspects such as the coagulating property of composite abrasion resistance material, metamorphic mechanism and the Technology for Heating Processing feature of the exploitation of currently used casting technique tends to ripe substantially.In high-abrasive material, carbide particle form has a variety of, presents several forms such as group's bulk spherical, big, shape of blooming, strip, shaft-like and vermiform；The spherical primary phase of group that wherein border is rounder and more smooth is optimal form, beneficially performance boost.Therefore, by optimizing carbide particle form and distribution further, anti-wear performance and its stability to raising high-abrasive material are highly beneficial.
The metamorphism treatment method that high-abrasive material is used by prior art mainly uses rare earth silicon and magnesium or (containing B, containing Zr) potassium salt as inoculation modificator, and usage amount is all between 0.5～1.0.Using conventional rare earth silicon, magnesium as alterant, on the one hand rare earth has the effect of cleaning molten steel, can generate compound with the oxygen in molten steel, nitrogen etc., and these compounds are also used as forming core particle and play the effect of refined carbides simultaneously；On the other hand rare earth is a kind of surface active element, can be enriched in the surface of carbide, thus suppress carbide to grow up along crystal boundary, make carbide refinement in process of setting.
Frequently with rare earth as alterant in prior art, when utilizing rare earth cleaning molten steel, produce the forming core particle as carbide such as a large amount of rare earth oxide, nitride；But the lattice types of these rare earth oxides, nitride is different from the lattice types of carbide.So these rare earth oxides, nitride can not be as the effective heterogeneous forming core cores of carbide carbon compound, its effect is extremely limited.
Summary of the invention
For above-mentioned technical problem, the present invention provides the medium carbon alloy steel high-abrasive material of a kind of dependable performance, the component of this material is formed by following mass percent: C:0.25-0.45%, Si:0.5-1.5%, Mn:0.5-1.0%, Cr:1.0-2.0%, Ti:1.0-2.0%, B:1.0--1.5%, Mo:0.1--0.3%, S :≤0.04%, P :≤0.04%, surplus is ferrum；The present invention adds Ti element, makes molten steel generate abundant forming core particle TiC so that it is amounts of particles is greatly increased.
The present invention also provides for the preparation method of a kind of medium carbon alloy steel high-abrasive material, sequentially includes the following steps:
1) steel scrap, ferro-boron, ferromanganese, molybdenum-iron, ferrotianium and ferrochrome are cleaned out, carry out dispensing, sorting placement by above-mentioned mass percent requirement, and by stand-by after the drying of ferro-boron, ferromanganese, ferrotianium, molybdenum-iron and ferrochrome, drying is in order to avoid bringing gas in molten steel into；
2) in stove, then add steel scrap, add ferromanganese, molybdenum-iron and ferrochrome and carry out melting；
3) add ferro-boron in the melting later stage, treat melting down backward stove adds ferrotianium；
4) come out of the stove after being subsequently adding aluminum shot deoxidation；
5) molten steel after coming out of the stove is poured into a mould, and then carries out heat treatment.
As preferably, smelting temperature is 1550～1650 DEG C.
As preferably, the aluminum shot mass fraction that deoxidation uses accounts for the 0.1%-0.15% of quality of molten steel.
As preferably, pouring temperature is 1500 DEG C.
As preferably, heat treatment uses three quenchings to be once tempered.
As preferably, first with 950～1000 DEG C of quenching 30min, then use air cooling, then to carry out water-cooled after 900～950 DEG C of quenching 30min, then to carry out water-cooled after 600～800 DEG C of quenching 5min, finally with 200～300 DEG C of tempering 2h laggard line space air coolings.
As can be known from the above technical solutions, above-mentioned preparation method can make carbide particle form in anti-friction material more roll into a ball nodularization, it is distributed more uniform, overcome in prior art carbide to there are several less-than-ideal forms such as big bulk, shape of blooming, strip, shaft-like and vermiform and distribution of particles exists form and the deficiencies of distribution such as Flos Chrysanthemi shape distribution, the combination property of raising material.
Detailed description of the invention
The present invention is described more detail below, and illustrative examples and explanation in this present invention are used for explaining the present invention, but not as a limitation of the invention.
The abrasion resistant Mn-W-Ti casting steel of the present invention is formed by following mass percent: C:0.25-0.45%, Si:0.5-1.5%, Mn:0.8-1.5%, Cr:1.0-2.0%, Ti:1.0-2.0%, B:1.0--1.5%, Mo:0.1--0.3%, S :≤0.04%, P :≤0.04%, surplus is ferrum；Wherein,
Carbon C is most important for the microstructure and property of composite abrasion resistance material, and it both can be solid-solution in matrix and play solution strengthening effect, is again to form carbide to strengthen the basic element of phase, moreover it is possible to promote martensite transfor mation, improve the hardenability of composite abrasion resistance material.Carbon content can increase material fragility too much, the most then the quantity reducing carbide enhancing phase causes its wearability to reduce.Therefore, this material controls C content at 0.20-0.35%%.
Chromium Cr also can react formation Cr with C6C、Cr7C3And Cr23C6Deng carbide, but owing to the carbide microhardness of chromium is low, and its pattern is due to elongated and cause its toughness poor, preferentially forms in matrix process of setting；Therefore, in the present invention, the addition of Cr element is less, and a small amount of Cr can also make it be solid-solution in austenite, acts primarily as hardenability and the quenching degree effect improving matrix.
Boron is Fe2B granule primarily form element, easily formed with Fe element reaction during solidification of molten steel and present netted Fe in a large number2B granule, is distributed in high-boron wear-resistant alloy material and plays wear-resisting skeleton function.
Chromium Cr and molybdenum Mo, can play stable Fe by adding Cr and Mo2The effect of B, Cr can reduce Fe2B phase essence fragility；Cr also can react formation Cr with C6C、Cr7C3And Cr23C6Deng carbide, but owing to Cr element addition is less, can only be solid-solution in austenite, mainly improve hardenability and the quenching degree of matrix and play stable Fe2The effect of B.Mo also can form Mo2C carbide, but owing to addition is little, be merely able to be solid-solution in matrix.Therefore, matrix adds Cr and Mo and can play stable Fe2The effect of B.
Titanium Ti is that the C element in carbide, with molten steel reacts the most tiny, the TiC particle of Dispersed precipitate of formation, can refine austenite dendrites, improve form and the distribution of eutectic carbide.Therefore in composition designs, directly Ti content is controlled at 1.0-2.0%, directly alloy is added in molten steel, in order to it is prone to fusing, passes through used medium frequency induction melting furnace electromagnetic field stirring action and make it produce the most relatively uniform TiC particle.But, in molten steel, too little or too much being all unfavorable for of Ti constituent content reaches actual effect, cross and be unfavorable at least making the matrix abundant crystallization nuclei particle of generation and eutectic carbide carry out refined carbides, cross and make the mobility of molten steel and mold-filling capacity reduce at most, it is unfavorable for improving workpiece compactness, anti-wear performance there is negative effect, so controlling its upper limit in its composition designs is 2.0%.
The heat treatment of the present invention uses three quenchings to be once tempered, i.e. first with 950～1000 DEG C of quenching 30min, then air cooling is used, again to carry out water-cooled after 900～950 DEG C of quenching 30min, then to carry out water-cooled after 600～800 DEG C of quenching 5min, finally with 200～300 DEG C of tempering 2h laggard line space air coolings；This mode not only can obtain more austenite, and can increase the carbide hard particle formed in tissue drawing process, to improve hardness.
Embodiment 1
Steel scrap, ferro-boron, ferromanganese, ferrotianium, molybdenum-iron and ferrochrome are cleaned out, by mass fraction be 0.25% C, 1.5% Si, 1.0% Mn, 1.0% Cr, 1.0% Ti, 1.0% B, 0.1% Mo, 0.04% S, 0.04% P, surplus be that the stoicheiometry of ferrum carries out dispensing, and sorting placement is stand-by after ferro-boron, ferromanganese, ferrotianium, molybdenum-iron and ferrochrome being dried；Steel scrap good for the most above-mentioned configuration, ferromanganese, ferrochrome, molybdenum-iron dispensing being put in stove and heated, add ferro-boron in the melting later stage, treat to add in melting down backward stove ferrotianium, smelting temperature is 1550 DEG C, and the aluminum shot deoxidation adding 0.1% after about 2min is come out of the stove；Pouring into a mould, pouring temperature is 1500 DEG C again；Then with 950 DEG C of quenching 30min, air cooling is then used, then to carry out water-cooled after 900 DEG C of quenching 30min, then to carry out water-cooled after 800 DEG C of quenching 5min, then with 300 DEG C of tempering 2h laggard line space air coolings, it is thus achieved that medium carbon alloy steel.This medium carbon alloy steel being carried out performance test obtain: hardness 50.3HRC, yield limit is 1710MPa, and strength degree is 1805 MPa, and impact toughness is 54J/cm2, extensibility is 5.3%.
Embodiment 2
Steel scrap, ferro-boron, ferromanganese, ferrotianium, molybdenum-iron and ferrochrome are cleaned out, by mass fraction be 0.35% C, 1% Si, 0.8% Mn, 1.5% Cr, 1.5% Ti, 1.2% B, 0.2% Mo, 0.03% S, 0.03% P, surplus be that the stoicheiometry of ferrum carries out dispensing, and sorting placement is stand-by after ferro-boron, ferromanganese, ferrotianium, molybdenum-iron and ferrochrome being dried；Steel scrap good for the most above-mentioned configuration, ferromanganese, ferrochrome, molybdenum-iron dispensing being put in stove and heated, add ferro-boron in the melting later stage, treat to add in melting down backward stove ferrotianium, smelting temperature is 1600 DEG C, and the aluminum shot deoxidation adding 0.15% after about 2min is come out of the stove；Pouring into a mould, pouring temperature is 1500 DEG C again；Then with 970 DEG C of quenching 30min, air cooling is then used, then to carry out water-cooled after 940 DEG C of quenching 30min, then to carry out water-cooled after 700 DEG C of quenching 5min, then with 260 DEG C of tempering 2h laggard line space air coolings, it is thus achieved that medium carbon alloy steel.This medium carbon alloy steel being carried out performance test obtain: hardness 54.6HRC, yield limit is 1790MPa, and strength degree is 1830 MPa, and impact toughness is 51.1J/cm2, extensibility is 5.9%.
Embodiment 3
Steel scrap, ferro-boron, ferromanganese, ferrotianium, molybdenum-iron and ferrochrome are cleaned out, by mass fraction be 0.45% C, 0.5% Si, 0.5% Mn, 2.0% Cr, 2.0% Ti, 1.5% B, 0.3% Mo, 0.02% S, 0.03% P, surplus be that the stoicheiometry of ferrum carries out dispensing, and sorting placement is stand-by after ferro-boron, ferromanganese, ferrotianium, molybdenum-iron and ferrochrome being dried；Steel scrap good for the most above-mentioned configuration, ferromanganese, ferrochrome, molybdenum-iron dispensing being put in stove and heated, add ferro-boron in the melting later stage, treat to add in melting down backward stove ferrotianium, smelting temperature is 1650 DEG C, and the aluminum shot deoxidation adding 0.1% after about 2min is come out of the stove；Pouring into a mould, pouring temperature is 1500 DEG C again；Then with 1000 DEG C of quenching 30min, air cooling is then used, then to carry out water-cooled after 950 DEG C of quenching 30min, then to carry out water-cooled after 600 DEG C of quenching 5min, then with 200 DEG C of tempering 2h laggard line space air coolings, it is thus achieved that medium carbon alloy steel.This medium carbon alloy steel being carried out performance test obtain: hardness 49.3HRC, yield limit is 1650MPa, and strength degree is 1780 MPa, and impact toughness is 46J/cm2, extensibility is 4.3%.
The technical scheme provided the embodiment of the present invention above is described in detail, principle and the embodiment of the embodiment of the present invention are set forth by specific case used herein, and the explanation of above example is only applicable to help to understand the principle of the embodiment of the present invention；Simultaneously for one of ordinary skill in the art, according to the embodiment of the present invention, all will change in detailed description of the invention and range of application, in sum, this specification content should not be construed as limitation of the present invention.
Claims (7)
1. medium carbon alloy steel high-abrasive material, its component is formed by following mass percent: C:0.25-0.45%, Si:0.5-1.5%, Mn:0.5-1.0%, Cr:1.0-2.0%, Ti:1.0-2.0%, B:1.0--1.5%, Mo:0.1--0.3%, S :≤0.04%, P :≤0.04%, surplus is ferrum.
2. a preparation method for medium carbon alloy steel high-abrasive material described in claim 1, sequentially includes the following steps:
1) steel scrap, ferro-boron, ferromanganese, ferrotianium, molybdenum-iron and ferrochrome are cleaned out, carry out dispensing by above-mentioned mass percent requirement, sorting placement, and stand-by after ferro-boron, ferromanganese, ferrotianium, molybdenum-iron and ferrochrome are dried；
2) in stove, then add steel scrap, add ferromanganese, molybdenum-iron and ferrochrome and carry out melting；
3) add ferro-boron in the melting later stage, after melting down, add ferrotianium；
4) come out of the stove after being subsequently adding aluminum shot deoxidation；
5) molten steel after coming out of the stove is poured into a mould, and then carries out heat treatment.
3. preparation method as claimed in claim 2, it is characterised in that: smelting temperature is 1550～1650 DEG C.
4. preparation method as claimed in claim 2, it is characterised in that: the mass fraction of the aluminum shot that deoxidation uses accounts for the 0.1%-0.15% of quality of molten steel.
5. preparation method as claimed in claim 2, it is characterised in that: pouring temperature is 1500 DEG C.
6. preparation method as claimed in claim 5, it is characterised in that: heat treatment uses three quenchings to be once tempered.
7. preparation method as claimed in claim 6, it is characterized in that: first with 950～1000 DEG C of quenching 30min, then air cooling is used, again to carry out water-cooled after 900～950 DEG C of quenching 30min, then to carry out water-cooled after 600～800 DEG C of quenching 5min, finally with 200～300 DEG C of tempering 2h laggard line space air coolings.
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