CN108004457B - The preparation method of the iron-based inovulant of high-speed steel - Google Patents
The preparation method of the iron-based inovulant of high-speed steel Download PDFInfo
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- CN108004457B CN108004457B CN201711396363.1A CN201711396363A CN108004457B CN 108004457 B CN108004457 B CN 108004457B CN 201711396363 A CN201711396363 A CN 201711396363A CN 108004457 B CN108004457 B CN 108004457B
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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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
- C22C1/1047—Alloys containing non-metals starting from a melt by mixing and casting liquid metal matrix composites
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
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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
- C22C33/08—Making cast-iron alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C37/00—Cast-iron alloys
Abstract
The preparation method of the iron-based inovulant of high-speed steel of the present invention, is related to manufacturing ferrous alloy with smelting process, is a kind of high-speed steel NbC-VC-Yb2C3The thin ribbon shaped inovulant of/Fe nanometers of two-dimentional in-situ authigenic iron base composite material, the inovulant is made by in-situ authigenic method and rapid solidification metal technology, the wetability for overcoming inovulant made from the prior art is poor, pregnant effect is uneven and enhancing particle size is larger, does not have elimination or weakens the defect of the function of the illeffects of element sulphur in steel.
Description
Technical field
Technical solution of the present invention is related to manufacturing ferrous alloy, the specifically iron-based inovulant of high-speed steel with smelting process
Preparation method.
Background technique
1900, the blank Cr-W steel (C1.85%, W8%, Cr3.8%) of high-speed steel was in the World Expo of Paris with 20m/
The speed of min cuts carbon steel, and obtains success, this has also caused a sensation entire metallurgical boundary, before this speed of Tool in Cutting carbon steel
Degree is no more than 10m/min.From there on, large quantities of metallurgists have carried out unremitting research and improvement to high-speed steel, by 100
The production technology of the development of many years, high-speed steel is significantly optimized, while its mechanical property is greatly improved.In recent years,
The application of powder metallurgy (PM) and injection forming (RS/PM) technology in manufacture high-speed steel, makes the alloying type of high-speed steel more
Add diversity, and mechanical property is significantly improved.However there are manufacturing process complexity, energy utilization for PM HSS
The low defect low with powder collection rate of rate, and the finished product of larger size can not be prepared, it is difficult to industrially promote the use of at present；
Spray forming high-speed steel is in positive development phase, and technology is simultaneously immature.Therefore, molten to high-speed steel at this stage in industrial production
It is most widely used modified method that inovulant, which is added, in body.
To high-speed steel carry out inoculation be it is a kind of generally acknowledged, can effectively refine As-Cast Structure in High Speed Steels and improve it
The method of mechanical property.The additional amount of inovulant only needs some thousandths of of substrate quality, therefore inoculation is a kind of ten merogenesis
The method of cost-saving.Deficiency existing for inovulant is in the prior art: be on the one hand inovulant form have substantially filament shape,
It is granular, blocky or rodlike, but the crystallite dimension in these inovulants all in micron level more than, it can be appreciated that if pregnant
Nano grade can be refine to by educating agent crystallite dimension, and the promotion of pregnant effect can be very significant；On the other hand, most of at present pregnant
The wetting effect for educating agent and high-speed steel is poor, is unable to give full play the pregnant effect of alloying element；Furthermore it is noted that
The inovulant industrially used at present does not have elimination or weakens the function of the illeffects of element sulphur.
Paper " The effect of amorphous nanocrystalline inoculants on structures
And properties of high speed steel. " (Materials Research Express, 2017) reports benefit
The inovulant synthesized with in-situ authigenic method；CN201010531574.3 discloses " High Speed Steel for Roller tissue modifying-refining
The methods for making and using same of inovulant " is made in the quick solidification FeVNb for High Speed Steel for Roller alloy structure modifying-refining
Between alloy inovulant.Inovulant obtained reported above does not have elimination still or weakens element sulphur to the illeffects of high-speed steel
Function, be unable to improve the toughness of high-speed steel, to Toughness of High Speed Steels promoted very little.
Summary of the invention
It is a kind of high the technical problems to be solved by the present invention are: providing the preparation method of the iron-based inovulant of high-speed steel
Fast steel NbC-VC-Yb2C3The thin ribbon shaped inovulant of/Fe nanometers of two-dimentional in-situ authigenic iron base composite material, which is to pass through
In-situ authigenic method and rapid solidification metal technology are made, and the wetability for overcoming inovulant made from the prior art is poor, breeds
Effect is uneven and enhancing particle size is larger, does not have elimination or weakens lacking for the function of the illeffects of element sulphur in steel
It falls into.
The present invention solves technical solution used by the technical problem: the preparation method of the iron-based inovulant of high-speed steel,
It is that high-speed steel NbC-VC-Yb is made by in-situ authigenic method and rapid solidification metal technology2C3/ Fe nanometers of two-dimentional in-situ authigenic
The thin ribbon shaped inovulant of iron base composite material, the specific steps are as follows:
The first step, preparation raw material:
Desired amount of cast iron, pure niobium, pure vanadium and pure ytterbium are weighed, according to the ratio 10.5~11.0% pure niobiums, 4.5~5.5%
Pure vanadium, 9.5~10.5% pure ytterbiums and remaining as cast iron carry out ingredient, the carbon containing quality percentage score of medium cast iron be 2.0~
3.0%, above-mentioned percentage is quality percentage score；
Second step prepares Fe-Nb-V-Yb-C bulk intermediate alloy:
Whole raw materials that the above-mentioned first step is prepared are put into II type non-consumable formula vacuum arc furnace ignition of WK-, are taken out to furnace body true
Sky is to vacuum degree 5 × 10-3Pa heats melting, until raw material all fusings, until all material compositions are uniformly distributed, then
It is 5~7 minutes cooling, Fe-Nb-V-Yb-C bulk intermediate alloy is made；
Third step prepares high-speed steel NbC-VC-Yb2C3The thin ribbon shaped of/Fe nanometers of two-dimentional in-situ authigenic iron base composite material
Inoculant products；
Fe-Nb-V-Yb-C bulk intermediate alloy made from above-mentioned second step is put into the earthenware of LZK-12A type vacuum quick quenching furnace
In crucible, furnace body vacuum degree is evacuated to 5 × 10-3Pa then passes to argon gas protection, and roller speed is 30~40m/s, adds in crucible
The Fe-Nb-V-Yb-C bulk intermediate alloy that heat is put into all fusings again, inclination crucible makes Fe-Nb-V-Yb-C molten mass exist
Quickly solidification is completed on roller, preparing width is 2.0~4.0 millimeters and with a thickness of 0.2~0.5 millimeter of high-speed steel NbC-
VC-Yb2C3The thin ribbon shaped inoculant products of/Fe nanometers of two-dimentional in-situ authigenic iron base composite material.
The preparation method of the iron-based inovulant of above-mentioned high-speed steel, used raw material and equipment are obtained by known approach,
Operating procedure is that those skilled in the art will appreciate that.
Beneficial effects of the present invention are as follows:
Compared with prior art, present invention substantive distinguishing features outstanding are as follows:
(1) the in-situ authigenic method in the method for the present invention and rapid solidification metal technology are special using the chemistry of Nb, V and Yb
Property, reaction in-situ generates NbC and VC nano-particle reinforcement phase and Yb2C3Nano particle phase, both types nanometer in the inovulant
Particle mutually plays two-dimentional inoculation(effect) in the high process of setting of high speed, i.e., the generation product of two-dimentional reaction in-situ can play heterogeneous
Forming core effect.It further illustrates, is to generate NbC and VC nano-particle reinforcement using in-situ authigenic reaction in inovulant synthesis
Phase, this is that basic dimension i.e. first is tieed up, the Yb in inovulant2C3It is in situ anti-that nano particle is added in high-speed steel generation again
Yb should be generated2S3Reinforced phase and its can play the effect of heterogeneous forming core, this is tieed up for higher-dimension i.e. second.High-speed steel iron of the invention
NbC and VC nano-particle reinforcement phase fusing point in base inovulant be higher than high-speed steel melt temperature and in density with high speed steel melt
It is closer to, after inovulant is added to high speed steel melt, a large amount of and Dispersed precipitate NbC and VC nano-particle reinforcement mutually conduct
Heterogeneous forming core core in primary crystal precipitation process, hence it is evident that improve nucleation rate；Yb in situ in inovulant2C3Nanometer is mutually 1470
Displacement in situ occurs with S at DEG C and reacts generation nanometer two dimension reaction in-situ product Yb2S3, nanometer two dimension reaction in-situ product Yb2S3
As leading phase, and again as the heterogeneous forming core core of secondary phase, the nucleation rate of remaining liquid phase is improved again, to make
It obtains As-Cast Structure in High Speed Steels and crystal grain is significantly refined, comprehensive mechanical property is remarkably improved.
(2) the related patents technology CN201010531574.3 previous with first invention people of the invention " roll high speed
The methods for making and using same of the inovulant of structure of steel modifying-refining " and CN201110081520.6 are " for refining spring steel casting
The preparation method and application method of the inovulant of state tissue " is compared, and the present invention has following substantive distinguishing features outstanding:
1) disclosed in the CN201010531574.3 in technical solution, only reaction in-situ product (Nb, V) C is as heterogeneous
Forming core core, and do not have elimination still or weaken element sulphur to the function of the illeffects of high-speed steel, to Toughness of High Speed Steels
Very little is promoted, the strengthening effect of high-speed steel comprehensive mechanical property improves there is still a need for further.
2) in the technical solution disclosed in CN201110081520.6, one is dimension reaction in-situ, flake obtained
Quickly its enhancing phase size of solidification FeVNbAl intermediate alloy inovulant can only achieve micron level, does not have elimination or weakens sulphur
Element can not significantly improve the toughness of metal material to the function of the illeffects of metal material.
3) high-speed steel of the present invention is those skilled in the art never in inovulant with the Yb being added in iron-based inovulant
The middle element being added, even if combining common knowledge to obtain the original position in inovulant on the basis of CN201010531574.3
Yb2C3The technical solution of nano particle phase, those skilled in the art can accomplish easily by no means.Yb is also the present invention
The key element of the second dimension reaction in-situ is played, it belongs to group of the lanthanides penultimate element, because relative atomic mass reaches
173.04, rear product density and molten steel are close in conjunction with sulphur, can disperse in molten steel and play the role of heterogeneous forming core.
4) after inovulant produced by the present invention being added in high-speed steel melting, As-Cast Structure in High Speed Steels thinning effect ratio
CN201010531574.3 significantly improves many, and this is mainly due to inovulant two dimension reaction in-situ products of the present invention to play
The made contribution of heterogeneous forming core effect.Inovulant enhancing particle size produced by the present invention reaches Nano grade, nano particle
Because its surface can be very high, there is stronger adsorptivity, wetting effect is obviously improved, and the reinforced phase particle of more tiny more disperse is to gold
The strengthening effect for belonging to material is higher；It is heterogeneous that in-situ authigenic reaction generation can occur using element sulphur for inovulant produced by the present invention
Forming core core, and then improve metal material comprehensive mechanical property.
5) the method for the present invention is not merely with the spontaneous reinforced phase of nanometer in situ in inovulant as in high-speed steel process of setting
Heterogeneous forming core core, and displacement reaction in situ occurs using element sulphur harmful in steel, generation can be used as heterogeneous forming core core
Two-dimentional reaction in-situ product, be refined high-speed steel as cast condition and crystal grain, to improve the comprehensive mechanical property of high-speed steel.
(3) so far, there has been no the relevant report by improving high speed steel mechanical property using two-dimentional inovulant,
The document report for not utilizing in steel harmful element sulphur that reaction in-situ occurs to modifying-refining As-Cast Structure in High Speed Steels.
Compared with prior art, marked improvement of the invention is as follows:
(1) the enhancing particle size in the inovulant that the present invention obtains is Nano grade, and nano-particle reinforcement mutually has
Very high surface-active, therefore have better wetability than the inovulant of the prior art.
(2) under the conditions of adding equal amount inovulant, nanometer inovulant is equivalent to reinforced phase numbers of particles and improves 1000 times,
Heterogeneous forming core core number is greatly improved, and substantially reduces production cost.
(3) high-speed steel of the present invention makes it to height with iron-based inovulant is ingenious in preparation process using harmful element sulphur in steel
Fast structure of steel plays advantageous effects.All it is to carry out desulfurization process for harmful element sulphur in steel under the prior art, works as sulfur content
Lower than one threshold value is difficult to reduce again.The chemistry spy of heavy rare earth element Yb is then utilized with iron-based inovulant for high-speed steel of the present invention
Property, the Yb in situ in inovulant2C3Nanometer, which is mutually reacted at 1470 DEG C with S generation displacement in situ, generates nanometer two dimension reaction in-situ
Product Yb2S3, the product is because density is close with high speed steel melt without occurring to float or sink, in high-speed steel process of setting
In play heterogeneous forming core central role；NbC-VC-Yb2C3Reinforced phase NbC, VC in/Fe nanometers of two-dimentional in-situ authigenic inovulant and
Yb2C3As-Cast Structure in High Speed Steels and crystal grain is set to obtain gradient refinement, " High Speed Steel for Roller tissue becomes compared with CN201010531574.3
The inovulant containing only single Nano-size Reinforced Particle (Nb, V) C in the methods for making and using same of the inovulant of matter refinement " has
The ability of stronger thinning microstructure and crystal grain.
(4) in-situ authigenic reaction generation can occur using element sulphur in metal material for inovulant produced by the present invention heterogeneous
Forming core core, and then improve compared with the inovulant of the prior art comprehensive mechanical property of metal material.
Detailed description of the invention
Present invention will be further explained below with reference to the attached drawings and examples.
Fig. 1 is NbC-VC-Yb made from the embodiment of the present invention 12C3/ Fe nanometers of two-dimentional in situ composites inovulant
X-ray diffractogram.
Fig. 2 is NbC-VC-Yb made from the embodiment of the present invention 12C3/ Fe nanometers of two-dimentional in situ composites inovulant
Matrix as-cast structure scanning electron microscope image.
Fig. 3 is the high speed steel curved beam as cast condition metallographic that inovulant is not added and inovulant made from the embodiment of the present invention 1 is added
Comparative diagram, wherein:
Fig. 3 (a) is the high speed steel curved beam as cast condition metallographic microscope that inovulant is not added；
Fig. 3 (b) is the high speed steel curved beam as cast condition metallographic microscope of inovulant made from this addition inventive embodiments 1.
Specific embodiment
Embodiment 1
The first step, preparation raw material:
Desired amount of cast iron, pure niobium, pure vanadium and pure ytterbium are weighed, according to the ratio 11.0% pure niobium, 5.5% pure vanadium, 10.5%
Pure ytterbium and remaining as cast iron carry out ingredient, the carbon containing quality percentage score of medium cast iron be 2.0~3.0%, above-mentioned percentage is equal
For quality percentage score；
Second step prepares Fe-Nb-V-Yb-C bulk intermediate alloy:
Whole raw materials that the above-mentioned first step is prepared are put into II type non-consumable formula vacuum arc furnace ignition of WK-, are taken out to furnace body true
Sky is to vacuum degree 5 × 10-3Pa heats melting, until raw material all fusings, until all material compositions are uniformly distributed, then
It is 5 minutes cooling, Fe-Nb-V-Yb-C bulk intermediate alloy is made；
Third step prepares high-speed steel NbC-VC-Yb2C3The thin ribbon shaped of/Fe nanometers of two-dimentional in-situ authigenic iron base composite material
Inoculant products；
Fe-Nb-V-Yb-C bulk intermediate alloy made from above-mentioned second step is put into the earthenware of LZK-12A type vacuum quick quenching furnace
In crucible, furnace body vacuum degree is evacuated to 5 × 10-3Pa, then passes to argon gas protection, and roller speed 30m/s is heated in crucible and put
The Fe-Nb-V-Yb-C bulk intermediate alloy entered to all fusings again, inclination crucible makes Fe-Nb-V-Yb-C molten mass in roller
Upper completion quickly solidification, preparing width is 2.0 millimeters and with a thickness of 0.5 millimeter of high-speed steel NbC-VC-Yb2C3/ Fe nanometer two
Tie up the thin ribbon shaped inoculant products of in-situ authigenic iron base composite material.
With the alcohol wipe strip inoculant products, surface impurity is removed, Bruker D8 type X-ray diffractometer pair is used
Sample scans detection, then strip inovulant is ground with 1200# and 2000#SiC sand paper, it is washed later with ultrasonic vibration method
Surface impurity carries out the observation of surface topography with PhilipsXL30 scanning electron microscope to sample.In the inovulant that the present embodiment obtains
About 8.43 nanometers of enhancing particle mean size.
Fig. 1 is NbC-VC-Yb made from the present embodiment2C3The X of/Fe nanometers of two-dimentional in situ composites inovulant is penetrated
Ray diffraction diagram.There it can be seen that the phase constituent that the present embodiment is made in inovulant includes α-Fe, NbC, VC and Yb2C3, and
And the diffraction maximum of α-Fe occupies the peak position of main phase, NbC, VC and Yb2C3Diffraction maximum occupy the peak position of secondary phase, illustrate at this
Matrix is mutually α-Fe, precipitated phase NbC, VC and Yb in inovulant made from embodiment2C3。
Fig. 2 is NbC-VC-Yb made from the present embodiment2C3The matrix of/Fe nanometers of two-dimentional in situ composites inovulant
As-cast structure scanning electron microscope image.There it can be seen that a large amount of tiny spheric granules inovulant bases made from the present embodiment
Disperse educt on body illustrates that these particles are NbC, VC and Yb in conjunction with the conclusion of Fig. 12C3Phase；Calculate through Image-Pro software
NbC, VC and Yb out2C3The average-size of spheric granules phase is about 8.4 nanometers.
Fig. 3 is that inovulant is not added to compare with the high speed steel curved beam as cast condition metallographic that inovulant made from the present embodiment is added
Figure, wherein Fig. 3 (a) is the high speed steel curved beam as cast condition metallographic microscope that inovulant is not added, and Fig. 3 (b) is to be added made from the present embodiment
The high speed steel curved beam as cast condition metallographic microscope of inovulant.As comparison it can be found that after inovulant made from addition the present embodiment, as cast condition
The crystallite dimension of high-speed steel, interdendritic away from and crystal boundary net thickness all obviously refined, obtained through the measuring and calculating of Image-Pro software: not
Add the crystallite dimension in the As-Cast Structure in High Speed Steels of inovulant, interdendritic away from being respectively 31.22 microns, 28.43 with crystal boundary net thickness
Micron and 12.36 microns, be added the present embodiment in inovulant high speed steel curved beam as-cast structure in crystallite dimension, interdendritic away from
It is respectively 20.01 microns, 13.28 microns and 8.11 microns with crystal boundary net thickness.
Embodiment 2
The first step, preparation raw material:
Desired amount of cast iron, pure niobium, pure vanadium and pure ytterbium are weighed, according to the ratio 10.5% pure niobium, 5.0% pure vanadium, 10.5%
Pure ytterbium and remaining as cast iron carry out ingredient, the carbon containing quality percentage score of medium cast iron be 2.0~3.0%, above-mentioned percentage is equal
For quality percentage score；
Second step prepares Fe-Nb-V-Yb-C bulk intermediate alloy:
Whole raw materials that the above-mentioned first step is prepared are put into II type non-consumable formula vacuum arc furnace ignition of WK-, are taken out to furnace body true
Sky is to vacuum degree 5 × 10-3Pa heats melting, until raw material all fusings, until all material compositions are uniformly distributed, then
It is 6 minutes cooling, Fe-Nb-V-Yb-C bulk intermediate alloy is made；
Third step prepares high-speed steel NbC-VC-Yb2C3The thin ribbon shaped of/Fe nanometers of two-dimentional in-situ authigenic iron base composite material
Inoculant products；
Fe-Nb-V-Yb-C bulk intermediate alloy made from above-mentioned second step is put into the earthenware of LZK-12A type vacuum quick quenching furnace
In crucible, furnace body vacuum degree is evacuated to 5 × 10-3Pa, then passes to argon gas protection, and roller speed 30m/s is heated in crucible and put
The Fe-Nb-V-Yb-C bulk intermediate alloy entered to all fusings again, inclination crucible makes Fe-Nb-V-Yb-C molten mass in roller
Upper completion quickly solidification, preparing width is 4.0 millimeters and with a thickness of 0.2 millimeter of high-speed steel NbC-VC-Yb2C3/ Fe nanometer two
Tie up the thin ribbon shaped inoculant products of in-situ authigenic iron base composite material.
Surface impurity is removed with alcohol wipe strip inovulant, using Bruker D8 type X-ray diffractometer to sample scans
Detection, then strip inovulant is ground with 1200# and 2000#SiC sand paper, it is miscellaneous to wash surface with ultrasonic vibration method later
Matter carries out the observation of surface topography with PhilipsXL30 scanning electron microscope to sample.The enhancing in inovulant that the present embodiment obtains
About 11.5 nanometers of particle mean size.
Embodiment 3
The first step, preparation raw material:
Desired amount of cast iron, pure niobium, pure vanadium and pure ytterbium are weighed, according to the ratio 10.8% pure niobium, 5.2% pure vanadium, 10.5%
Pure ytterbium and remaining as cast iron carry out ingredient, the carbon containing quality percentage score of medium cast iron be 2.0~3.0%, above-mentioned percentage is equal
For quality percentage score；
Second step prepares Fe-Nb-V-Yb-C bulk intermediate alloy:
Whole raw materials that the above-mentioned first step is prepared are put into II type non-consumable formula vacuum arc furnace ignition of WK-, are taken out to furnace body true
Sky is to vacuum degree 5 × 10-3Pa heats melting, until raw material all fusings, until all material compositions are uniformly distributed, then
It is 6 minutes cooling, Fe-Nb-V-Yb-C bulk intermediate alloy is made；
Third step prepares high-speed steel NbC-VC-Yb2C3The thin ribbon shaped of/Fe nanometers of two-dimentional in-situ authigenic iron base composite material
Inoculant products；
Fe-Nb-V-Yb-C bulk intermediate alloy made from above-mentioned second step is put into the earthenware of LZK-12A type vacuum quick quenching furnace
In crucible, furnace body vacuum degree is evacuated to 5 × 10-3Pa, then passes to argon gas protection, and roller speed 35m/s is heated in crucible and put
The Fe-Nb-V-Yb-C bulk intermediate alloy entered to all fusings again, inclination crucible makes Fe-Nb-V-Yb-C molten mass in roller
Upper completion quickly solidification, preparing width is 3.0 millimeters and with a thickness of 0.3 millimeter of high-speed steel NbC-VC-Yb2C3/ Fe nanometer two
Tie up the thin ribbon shaped inoculant products of in-situ authigenic iron base composite material.
Surface impurity is removed with alcohol wipe strip inovulant, using Bruker D8 type X-ray diffractometer to sample scans
Detection, then strip inovulant is ground with 1200# and 2000#SiC sand paper, it is miscellaneous to wash surface with ultrasonic vibration method later
Matter carries out the observation of surface topography with PhilipsXL30 scanning electron microscope to sample.The enhancing in inovulant that the present embodiment obtains
About 9.9 nanometers of particle mean size.
Embodiment 4
The first step, preparation raw material:
Desired amount of cast iron, pure niobium, pure vanadium and pure ytterbium are weighed, according to the ratio 11.0% pure niobium, 4.5% pure vanadium, 9.5% pure
Ytterbium and ingredient is carried out remaining as cast iron, the carbon containing quality percentage score of medium cast iron is 2.0~3.0%, and above-mentioned percentage is
Quality percentage score；
Second step prepares Fe-Nb-V-Yb-C bulk intermediate alloy:
Whole raw materials that the above-mentioned first step is prepared are put into II type non-consumable formula vacuum arc furnace ignition of WK-, are taken out to furnace body true
Sky is to vacuum degree 5 × 10-3Pa heats melting, until raw material all fusings, until all material compositions are uniformly distributed, then
It is 7 minutes cooling, Fe-Nb-V-Yb-C bulk intermediate alloy is made；
Third step prepares high-speed steel NbC-VC-Yb2C3The thin ribbon shaped of/Fe nanometers of two-dimentional in-situ authigenic iron base composite material
Inoculant products；
Fe-Nb-V-Yb-C bulk intermediate alloy made from above-mentioned second step is put into the earthenware of LZK-12A type vacuum quick quenching furnace
In crucible, furnace body vacuum degree is evacuated to 5 × 10-3Pa, then passes to argon gas protection, and roller speed 40m/s is heated in crucible and put
The Fe-Nb-V-Yb-C bulk intermediate alloy entered to all fusings again, inclination crucible makes Fe-Nb-V-Yb-C molten mass in roller
Upper completion quickly solidification, preparing width is 4.0 millimeters and with a thickness of 0.2 millimeter of high-speed steel NbC-VC-Yb2C3/ Fe nanometer two
Tie up the thin ribbon shaped inoculant products of in-situ authigenic iron base composite material.
Surface impurity is removed with alcohol wipe strip inovulant, using Bruker D8 type X-ray diffractometer to sample scans
Detection, then strip inovulant is ground with 1200# and 2000#SiC sand paper, it is miscellaneous to wash surface with ultrasonic vibration method later
Matter carries out the observation of surface topography with PhilipsXL30 scanning electron microscope to sample.The enhancing in inovulant that the present embodiment obtains
About 12.3 nanometers of particle mean size.
In above-described embodiment, used raw material and equipment are obtained by known approach, and operating procedure is the art
Technical staff will appreciate that.
Claims (2)
1. the high-speed steel preparation method of iron-based inovulant, it is characterised in that: be by in-situ authigenic method and rapid solidification metal
High-speed steel NbC-VC-Yb is made in technology2C3The thin ribbon shaped inovulant of/Fe nanometers of two-dimentional in-situ authigenic iron base composite material, specifically
Steps are as follows:
The first step, preparation raw material:
Weigh desired amount of cast iron, pure niobium, pure vanadium and pure ytterbium, according to the ratio 10.5~11.0% pure niobiums, 4.5~5.5% pure vanadium,
9.5~10.5% pure ytterbiums and remaining as cast iron carry out ingredient, the carbon containing quality percentage score of medium cast iron be 2.0~3.0%, on
Stating percentage is quality percentage score；
Second step prepares Fe-Nb-V-Yb-C bulk intermediate alloy:
Whole raw materials that the above-mentioned first step is prepared are put into II type non-consumable formula vacuum arc furnace ignition of WK-, are evacuated to furnace body
Vacuum degree 5 × 10-3Pa heats melting, until then raw material all fusings cool down 5 until all material compositions are uniformly distributed
~7 minutes, Fe-Nb-V-Yb-C bulk intermediate alloy is made；
Third step prepares high-speed steel NbC-VC-Yb2C3The thin ribbon shaped of/Fe nanometers of two-dimentional in-situ authigenic iron base composite material is bred
Agent product；
Fe-Nb-V-Yb-C bulk intermediate alloy made from above-mentioned second step is put into the crucible of LZK-12A type vacuum quick quenching furnace
In, furnace body vacuum degree is evacuated to 5 × 10-3Pa then passes to argon gas protection, and roller speed is 30~40m/s, heats in crucible
The Fe-Nb-V-Yb-C bulk intermediate alloy being put into all fusings again, inclination crucible makes Fe-Nb-V-Yb-C molten mass in roller
Quickly solidification is completed on wheel, preparing width is 2.0~4.0 millimeters and with a thickness of 0.2~0.5 millimeter of high-speed steel NbC-VC-
Yb2C3The thin ribbon shaped inoculant products of/Fe nanometers of two-dimentional in-situ authigenic iron base composite material.
2. the preparation method of the iron-based inovulant of high-speed steel according to claim 1, it is characterised in that: the in-situ authigenic method
It is the chemical characteristic using Nb, V and Yb with rapid solidification metal technology and two-dimentional in-situ authigenic, reaction in-situ generates NbC and VC
Nano-particle reinforcement phase and Yb2C3Nano particle phase, both types nano particle is mutually in the high process of setting of high speed in the inovulant
In play the role of two-dimentional inoculation(effect), i.e., the generation product of two-dimentional reaction in-situ can play heterogeneous forming core, be in inovulant conjunction
NbC and VC nano-particle reinforcement phase is generated using in-situ authigenic reaction at middle, this is that basic dimension i.e. first is tieed up, in inovulant
Yb2C3Nano particle is added in high-speed steel occurs reaction in-situ generation Yb again2S3Reinforced phase and its can play heterogeneous shape
Core effect, this is the dimension of higher-dimension i.e. second.
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| CN106521296A (en) * | 2016-11-17 | 2017-03-22 | 石卫东 | Amorphous nucleating agent for nodular cast iron and preparation method and using method thereof |
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| CN102031442A (en) * | 2010-11-04 | 2011-04-27 | 河北工业大学 | Preparation and application method of inoculant for tissue deterioration refinement of high-speed steel for roller |
| CN102168220A (en) * | 2011-04-01 | 2011-08-31 | 河北工业大学 | Method for preparing inoculant for refining as-cast structure of spring steel and application method thereof |
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