CN111804907A - Modified ceramic particle reinforced iron-based composite material and preparation method thereof - Google Patents

Modified ceramic particle reinforced iron-based composite material and preparation method thereof Download PDF

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CN111804907A
CN111804907A CN202010693590.6A CN202010693590A CN111804907A CN 111804907 A CN111804907 A CN 111804907A CN 202010693590 A CN202010693590 A CN 202010693590A CN 111804907 A CN111804907 A CN 111804907A
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zta
ceramic
ceramic particles
composite material
cooling
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CN111804907B (en
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李烨飞
李聪
李博
高义民
郑巧玲
李月辉
赵四勇
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Guangxi Changcheng Mechanical Ltd By Share Ltd
Xian Jiaotong University
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Guangxi Changcheng Mechanical Ltd By Share Ltd
Xian Jiaotong University
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/17—Metallic particles coated with metal
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D23/00—Casting processes not provided for in groups B22D1/00 - B22D21/00
    • B22D23/04—Casting by dipping
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/10—Sintering only
    • B22F3/1003—Use of special medium during sintering, e.g. sintering aid
    • B22F3/1007—Atmosphere
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/10—Sintering only
    • B22F3/11—Making porous workpieces or articles
    • B22F3/1103—Making porous workpieces or articles with particular physical characteristics
    • B22F3/1115—Making porous workpieces or articles with particular physical characteristics comprising complex forms, e.g. honeycombs
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0242—Making ferrous alloys by powder metallurgy using the impregnating technique
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
    • C23C14/06—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the coating material
    • C23C14/14—Metallic material, boron or silicon
    • C23C14/18—Metallic material, boron or silicon on other inorganic substrates
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
    • C23C14/22—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the process of coating
    • C23C14/24—Vacuum evaporation
    • C23C14/32—Vacuum evaporation by explosion; by evaporation and subsequent ionisation of the vapours, e.g. ion-plating
    • C23C14/325—Electric arc evaporation

Abstract

The invention discloses a modified ceramic particle reinforced iron-based composite material and a preparation method thereof, and relates to ZTAPPreheating ceramic particles, and then obtaining the ZTA of the nickel-chromium alloy plating by adopting a physical vapor deposition methodPCeramic particles; plating nickel-chromium alloy ZTAPMixing and stirring the ceramic particles, micron-sized NiCrAlY alloy powder and alcohol, and shaping and drying to obtain a prefabricated body with a honeycomb structure; placing the preform inAnd (3) carrying out vacuum sintering treatment at the high temperature of 1250-1450 ℃, casting high-chromium cast iron liquid metal after cooling, and cooling to obtain the modified ceramic particle reinforced iron-based composite material. The invention is realized by the pair ZTAPThe ceramic surface metallization effectively improves the interface bonding performance and the wear resistance of the composite material.

Description

Modified ceramic particle reinforced iron-based composite material and preparation method thereof
Technical Field
The invention belongs to the technical field of wear-resistant material preparation, and particularly relates to a modified ceramic particle reinforced iron-based composite material and a preparation method thereof.
Background
The ceramic particle reinforced steel-iron-based composite material is widely applied to key wear-resistant parts in the fields of mines, metallurgy, cement, electric power and the like, and at present, domestic large-scale wear-resistant parts become key factors influencing the powder yield in the field of material grinding application due to poor stability and wear resistance and short service life, so domestic large-scale wear-resistant parts are still mainly made of foreign imported products.
The ceramic particle reinforced steel composite material shows excellent wear resistance due to the introduction of the reinforcing phase, and the high-chromium cast iron matrix provides the advantages of good toughness, high strength, high hardness, high wear resistance and the like, and has good service performance under the service working condition. Carbide ceramics and oxide ceramics, which are the most widely used reinforcing particles at present, wherein the tungsten carbide ceramics can form Fe with a metallic iron matrix at an interface3W3C, metallurgical bonding of the interface is guaranteed, but the tungsten carbide ceramic is expensive and high in manufacturing cost, and cracks are easily generated at the interface due to thermal stress; the alumina ceramic has higher hardness and is matched with the physical properties of the iron and steel matrix, but the alumina and the iron matrix are not wetted and have large brittleness; ZTA ceramic is prepared from ZrO2The self-toughening effect of the ceramic can be used as an ideal reinforcing phase for replacing alumina ceramic, but the ZTA ceramic and the metal matrix iron interface are still mechanically combined to be main, and the service life of the composite material is seriously influenced.
Disclosure of Invention
The technical problem to be solved by the invention is to provide a modified ceramic particle reinforced iron-based composite material and a preparation method thereof aiming at the defects in the prior art, wherein ZTA is preparedPThe ceramic surface metallization effectively improves the interface bonding performance and the wear resistance of the composite material.
The invention adopts the following technical scheme:
a preparation method of a modified ceramic particle reinforced iron-based composite material comprises the following steps:
s1, for ZTAPPreheating ceramic particles, and preparing the ZTA of the nickel-chromium alloy plating by adopting a physical vapor deposition methodPCeramic particles;
s2, plating ZTA of nickel-chromium alloyPMixing and stirring ceramic particles, micron-sized NiCrAlY alloy powder and alcohol, and shaping and drying to obtain a ceramic prefabricated body with a honeycomb structure;
s3, performing vacuum sintering treatment on the ceramic preform at the high temperature of 1250-1450 ℃, casting high-chromium cast iron liquid metal after cooling, and cooling to obtain the modified ceramic particle reinforced iron-based composite material.
Specifically, in step S1, ZTAPThe particle size of the ceramic particles is 3-5 mm.
Specifically, in step S1, prior to the preheating process, ZTA is subjected toPCarrying out surface micro-roughening on the ceramic particles to obtain ZTA with the roughness of 4-10 mu mPCeramic particles.
Specifically, in step S1, the temperature of the preheating treatment is 300 to 400 ℃.
Specifically, in step S1, the vacuum multi-arc ion plating method is adopted in ZTAPPlating Ni-Cr alloy on the surface of ceramic grains, and continuously rotating to hold ZTA during platingPA rotating disk of ceramic particles.
Specifically, in step S2, the micron-sized NiCrAlY alloy powder has a particle size of 40 to 60 μm, and the NiCrAlY alloy powder accounts for nickel-chromium alloy plating ZTAP10-30% of the mass of the ceramic particles, and the alcohol accounts for the nickel-chromium alloy plated ZTAPCeramic particles and NiCrAlY powder5 to 10 percent of the total weight of the powder.
Specifically, in step S3, the vacuum high-temperature sintering heat treatment specifically includes:
heating from room temperature to 800-900 ℃ at a heating rate of 5-15 ℃/min, then heating to 1000-1150 ℃ at a heating rate of 6-8 ℃/min, then heating to 1250-1450 ℃ at a heating rate of 3-5 ℃/min, preserving heat for 0.5-2 h, then cooling to 1000-1150 ℃ at a temperature of 3-5 ℃/min, then cooling to 800-900 ℃ at a cooling rate of 6-8 ℃/min, finally cooling to 400-500 ℃ at a cooling rate of 5-15 ℃/min, and finally cooling to room temperature.
Specifically, in step S3, the high-chromium cast iron liquid metal is cast by a bottom casting method, the heating temperature is 1550-1650 ℃, and the cooling time is 18-24 hours.
According to another technical scheme, the modified ceramic particle reinforced iron-based composite material comprises a high-chromium cast iron matrix and NiCrAlY modified ZTAPCeramic particles, high-chromium cast iron matrix and ZTAPThe volume fractions of the ceramic particles are 60-90% and 10-40%, respectively.
Specifically, the modified ceramic particle reinforced iron-based composite material is prepared by the method of claim 1.
Compared with the prior art, the invention has at least the following beneficial effects:
the invention relates to a preparation method of a modified ceramic particle reinforced iron-based composite material, which is applied to ZTA by a physical vapor deposition methodPThe nickel-chromium alloy is deposited on the surface of the ceramic particles, and the chromium and the nickel can be effectively dissolved in the matrix, so that the solid solution strengthening effect is achieved, and the strength, the hardness and the wear resistance of the matrix are improved; ZTA after multi-arc ion platingPThe ceramic particles are sintered with micron-sized NiCrAlY powder, a sintering neck is formed among the particles, the thickness of an interface transition layer can be effectively increased, and Al generated by reaction at the interface is2O3And Y2O3The oxidation resistance of the interface layer is increased and the toughening effect is generated, thereby improving ZTAPThe bonding strength of the interface between the substrate and the substrate; ZTA modified by NiCrAlYPCeramic particles of NiCrAlY to ZTAPThe surface of the ceramic particle is coated, NiCr solid solution is formed at the interface, the wettability of the ceramic and the substrate is improved, and Al is formed in situ near the interface2O3The ceramic particles further improve the mechanical property and the wear resistance of the composite material.
Further, filtering with a 5-60 mesh screen to obtain ZTA with micro-roughened surfacePCeramic particles with increased specific surface area and surface energy, and smooth ZTAPCompared with the surface of the ceramic particle, ionized NiCr ions are easy to deposit on a rough surface, and a compact metal coating is obtained after continuous deposition, so that the coating efficiency is improved.
Further, ZTA is treated by ball millingPThe ceramic particles obtain a micro-roughened surface, increasing deposition sites of the NiCr alloy during subsequent plating, and improving plating efficiency.
Further, the ZTA is first plated during the plating processPPreheating ceramic particles at 300-400 ℃, and further improving ZTAPThe surface activity of the ceramic particles enables them to better complex with metals.
Further, due to ZTAPThe ceramic particles are irregular in shape, and the uniformity of the deposited coating is difficult to satisfy by fixed unidirectional deposition, so that the ZTA is continuously rotated and contained in the coating processPThe rotary table of ceramic particles enables the rotating particles to deposit a metal coating in a multi-angle and all-directional manner, and the bonding performance of the coating and a substrate is improved by controlling the duty ratio, the current, the deposition time and the cavity temperature.
Further, micron-sized NiCrAlY powder accounts for ZTA of nickel-chromium alloy platingP10-30% of the mass of the ceramic particles, and the alcohol accounts for ZTA of the nickel-chromium alloy platingPThe total mass of the ceramic particles and the micron-sized NiCrAlY powder is 5-10%, and the viscosity and the surface tension of the NiCrAlY powder can be improved by a proper amount of alcohol, so that pasty metal powder is uniformly coated on the surfaces of the ceramic particles.
Further, the ZTA is improved by high-temperature sintering treatmentPThe bonding strength among the ceramic particles is used for completing the high-temperature sintering heat treatment of the honeycomb-shaped prefabricated bodySintering necks are formed between the particles, thereby improving the bonding strength thereof and ensuring corresponding porosity thereof.
Furthermore, a casting system is optimized by adjusting the heating temperature and the cooling time, the traditional sand casting process is improved by adopting a bottom casting type casting method, the quality of the composite material is improved, the thickness limit of a composite layer is greatly increased, and compared with pressure casting, the method is low in cost and safe and reliable in operation.
The honeycomb structure of the modified ceramic particle reinforced iron-based composite material is favorable for improving the casting infiltration effect of molten metal in a ceramic preform, and ZTAPThe surface of the ceramic particles is deposited with a nickel-chromium alloy layer, which plays a role in solid solution strengthening, improves the strength, hardness and wear resistance of the matrix, and greatly reduces the preparation cost.
The technical solution of the present invention is further described in detail by the accompanying drawings and embodiments.
Drawings
FIG. 1 is a schematic view of example 1 of the present invention showing a pair of ZTA using multi-arc ion platingPA schematic surface treatment;
FIG. 2 shows NiCr alloy layer ZTA plating in example 1 of the present inventionPTissue photographs of the sections;
FIG. 3 is a photograph of a macrostructure of a composite material according to example 1 of the present invention;
FIG. 4 is a photograph of the surface texture of the composite material of example 1 of the present invention after abrasion.
Wherein, 1.ZTAPCeramic particles; 2. a sample stage; 3. an auxiliary heating device; 4. a vacuum chamber; 5. a bias power supply; 6. argon gas; a NiCr alloy target; NiCr ion; 9. an electric motor.
Detailed Description
The invention provides a modified ceramic particle reinforced iron-based composite material and a preparation method thereof, wherein ZTA is adopted for increasing the multi-arc ion nickel-chromium alloy plating by ball milling treatmentPContact points are used for improving deposition efficiency; for ZTAPMetallizing the surface of ceramic particles, and then carrying out surface modification on the nickel-chromium-plated ZTAPUniformly mixing the ceramic particles and micron-sized NiCrAlY alloy powder to prepare a prefabricated body with a honeycomb structure; tong (Chinese character of 'tong')Sintering necks are formed among the particles through high-temperature vacuum sintering treatment so as to improve the bonding strength of the particles; and finally, casting molten metal iron into the prefabricated body with the honeycomb structure, and cooling to obtain the composite material with high wear resistance. The invention is realized by the following method in ZTAPThe surface of the ceramic particle is plated with a nickel-chromium alloy coating, and the ZTA can be obviously improved after the nickel-chromium alloy coating and NiCrAlY alloy powder are sinteredPThe bonding performance between the ceramic particles and the iron matrix; the metal transition layer of the prepared composite material at the material interface ensures the metallurgical bonding interface, thereby improving the bonding strength of the ceramic and the matrix, further improving the wear resistance of the composite material and ensuring the service safety of the wear-resistant composite material under the harsh working condition.
The invention relates to a modified ceramic particle reinforced iron-based composite material, which comprises the following steps:
s1, for ZTAPThe ceramic particles are preheated and then subjected to physical vapor deposition in ZTAPDepositing nickel-chromium alloy on the surface of the ceramic particles to obtain ZTA of the nickel-chromium alloyPCeramic particles;
wherein, for ZTAPThe temperature for preheating the ceramic particles is 300-400 ℃.
Preferably, the ZTA is treated before the preheating treatmentPBall milling the ceramic particles to obtain ZTAPThe surface of the ceramic particles is micro-roughened, and then the particles are filtered to obtain ZTA with the particle size of 3-5 mm and the roughness of 4-10 mu mPCeramic particles.
Wherein, the ZTA is processed by ball millingPThe micro-roughening of the surface of the ceramic particles comprises the following specific steps:
will ZTAPPutting the ceramic particles into a three-dimensional ball mill, and performing ball milling treatment at the rotating speed of 50-150 r/min for 1-10 h to ensure that ZTAPThe surface of the ceramic particles is micro-roughened, so that the deposition sites of the nickel-chromium alloy in the subsequent plating process are increased, and the plating efficiency is improved; after ball milling treatment, filtering by using a 5-60 mesh screen to obtain the ZTA with the micro-roughened surfacePCeramic particles.
Preferably, ZTA is first treated by ball millingPCeramic particle in wineSoaking in the fine powder for 10-20 min, then cleaning the fine powder for 5-25 min by using ultrasonic waves, and further drying in a vacuum drying oven.
Referring to fig. 1, the physical vapor deposition method adopts a vacuum multi-arc ion plating method, a nichrome target is used as a cathode, after arc discharge, a uniform nichrome layer with a required thickness is obtained by controlling the bias voltage, current, duty ratio and plating time of the multi-arc ion plating, so that ZTAPMetallizing the surface of the ceramic particles, and finally carrying out ultrasonic cleaning and drying treatment;
the technological parameters of the vacuum multi-arc ion plating are as follows:
preferably, Ar with a purity of 99.99% is used as a protective gas during plating, and ZTA is continuously rotated and contained in the plating process in order to further improve the bonding performance of the plating layer and the substratePA rotating disk of ceramic particles.
S2, preparing the ZTA of the nickel-chromium alloy plated with the nickel obtained in the step S1PMixing and stirring ceramic particles, micron-sized NiCrAlY powder and alcohol, and shaping and drying to obtain a prefabricated body with a honeycomb structure;
wherein the particle size of the micron-sized NiCrAlY powder is 40-60 mu m, and the micron-sized NiCrAlY powder accounts for nickel-chromium alloy plated ZTAP10-30% of the mass of the ceramic particles, and the alcohol accounts for the nickel-chromium alloy plated ZTA P5 to 10 percent of the total mass of the ceramic particles and the micron-sized NiCrAlY powder.
By subjecting the surface-treated ZTA to a surface treatment during the preparation of the preform and the subsequent preparation of the compositePThe surface of the ceramic particle is coated with a layer of metal NiCrAlY coating, the thickness of the coating is further increased, the interface bonding strength of the composite material is further improved, the preparation cost is greatly reduced, and Cr is formed in situ in the metal coating in the composite process2O3，Y2O3And Al2O3And the addition of Cr plays a role in solid solution strengthening in the iron matrix.
And S3, performing vacuum sintering treatment on the prefabricated body at the high temperature of 1250-1450 ℃, casting high-chromium cast iron liquid metal after cooling, and cooling to obtain the modified ceramic particle reinforced iron-based composite material.
Wherein, the vacuum high-temperature sintering heat treatment is carried out by adopting a vacuum tube furnace, which comprises the following specific steps:
putting a prefabricated body with a honeycomb structure into a vacuum tube furnace, heating the prefabricated body from room temperature to 800-900 ℃ at a heating rate of 5-15 ℃/min, then heating the prefabricated body to 1000-1150 ℃ at a heating rate of 6-8 ℃/min, then heating the prefabricated body to 1250-1450 ℃ at a heating rate of 3-5 ℃/min, preserving heat for 0.5-2 h, then cooling the prefabricated body to 1000-1150 ℃ at a temperature of 3-5 ℃/min, cooling the prefabricated body to 800-900 ℃ at a cooling rate of 6-8 ℃/min, then cooling the prefabricated body to 400-500 ℃ at a cooling rate of 5-15 ℃/min, finally cooling the prefabricated body along with the furnace to obtain a treated prefabricated body, and improving ZTA through vacuum sintering high-temperature heat treatmentPBond strength between ceramic particles, so that ZTAPThe ceramic particles form sintering necks therebetween, thereby improving the bonding strength thereof and ensuring ZTAPThe ceramic particles have corresponding porosity;
and (3) placing the obtained prefabricated body in a sand mold for fixing, then casting high-chromium cast iron liquid metal, and cooling to obtain the modified ceramic particle reinforced iron-based composite material.
And (3) placing the honeycomb-shaped prefabricated body in a sand mold for fixing, heating the high-chromium cast iron substrate raw material to 1550-1650 ℃, casting the high-chromium cast iron liquid metal, and cooling for 18-24 hours to obtain the composite material with high wear resistance.
The modified ceramic particle reinforced iron-based composite material prepared by the method comprises a matrix and NiCrAlY modified ZTAPCeramic particles, matrix and ZTAPThe relative contents of the ceramic particles are respectively 60-90% and 10-40%.
In order to make the objects, technical solutions and advantages of the embodiments of the present invention clearer, the technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it is obvious that the described embodiments are some, but not all, embodiments of the present invention. Thus, the following detailed description of the embodiments of the present invention is not intended to limit the scope of the invention as claimed, but is merely representative of selected embodiments of the invention. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Example 1
Firstly ZTAPSoaking in alcohol for 10min, ultrasonic cleaning for 5min, and oven drying in a vacuum drying oven for 1 h; shape irregular ZTAPBall milling in a three-dimensional ball mill at 50r/min for 1 hr, stopping milling for 30min and 15min, and filtering with 5 mesh sieve ZTAP；
In ZTA by vacuum multi-arc ion platingPPlating Ni-Cr alloy on the surface, Ar (purity 99.99%) as protective gas for plating to metallize the surface, continuously rotating and placing ZTA in the deposition processPThen ultrasonically cleaning for 15min and drying;
please refer to fig. 1, the ZTAPCeramic particles 1 are flatly paved on a sample table 2 in a vacuum chamber 4, a maintaining pump maintaining valve is opened before a NiCr coating is coated, the pressure is pre-pumped to 5Pa, a molecular pump is opened, the coating is carried out by vacuumizing, a grating valve is closed, the gas flow is adjusted, argon 6a is filled, a bias power supply 5 is opened, the bias is adjusted, and NiCr ions 8 are released through a NiCr alloy target 7 to start coating; the sample stage 2 is driven to rotate continuously by a bias power supply and a motor 9 during NiCr coating, and heating assistance is performed by an auxiliary heating device 3 in order to make the ceramic particles and the coating layer well combined.
ZTA to be plated with NiCr alloyPStirring and mixing ceramic particles, NiCrAlY powder accounting for 10 percent of the mass of the ceramic and alcohol accounting for 5 percent of the total mass of the mixed powder, wherein the particle size of the NiCrAlY powder is 40 mu m, and putting the NiCrAlY powder into a mould with a specific shape to solidify in a vacuum drying oven; placing the preform into a vacuum tube furnace, heating to 800 deg.C at a heating rate of 5 deg.C/min, heating to 1000 deg.C at a heating rate of 6 deg.C/min, heating to 1250 deg.C at a heating rate of 3 deg.C/min, maintaining for 0.5h, and increasing ZTAPThe bonding strength is reduced to 1000 ℃ at the temperature of 3 ℃/min, reduced to 800 ℃ at the cooling rate of 6 ℃/min, reduced to 400 ℃ at the cooling rate of 5 ℃/min, and finally cooled along with the furnace;
and finally, placing the honeycomb-shaped prefabricated body in a sand mold with a specific size for fixing, heating the raw material of the matrix to 1550 ℃, casting liquid metal into the prefabricated body, and cooling for 18 hours to obtain the composite material with high wear resistance.
Referring to FIG. 2, ZTA after platingPPhotographs of the texture of the cross-section of the particles in ZTAPThe surface of the ceramic body is provided with a uniform and compact NiCr coating which is silvery white, and the ceramic and the coating are tightly combined together. The coating can promote the formation of a sintering neck in the sintering process, so that the bonding strength of the prefabricated body is improved, and the casting infiltration effect of the subsequent iron-based composite material is ensured.
The obtained composite material is subjected to three-body abrasive wear, and the abrasive is selected from 70-mesh soft abrasive SiO2The load is 3Kg, the ultrasonic cleaning is carried out for 5 times and 30 min/time, the experiment after each abrasion is carried out for 30min in alcohol, the drying is carried out, the mass is respectively weighed on a precision balance, and the average volume loss rate is 5.14mm3。
Referring to FIGS. 3 and 4, surface-treated ZTAPThe prepared composite ceramic particles are well combined with a matrix, and obvious defects, insufficient pouring and other phenomena are not found. As shown in FIG. 4, after abrasion, the ceramic particles are obviously protruded from the matrix, bear main abrasion, and play a role in double shadow effect, thereby protecting the surrounding matrix material and preventing the matrix material from further abrasion. There are a large number of crush pits and a small number of furrows in the matrix, further illustrating that the wear mechanism is dominated by fatigue wear.
Example 2
Firstly ZTAPSoaking in alcohol for 15min, then performing ultrasonic cleaning for 10min, and further placing in a vacuum drying oven for drying for 1 h; shape irregular ZTAPBall milling in a three-dimensional ball mill at 80r/min for 3 hr, stopping milling for 15min every 30min, and filtering with 15 mesh sieve ZTAP；
In ZTA by vacuum multi-arc ion platingPPlating Ni-Cr alloy on the surface, Ar (purity 99.99%) as protective gas for plating to metallize the surface, continuously rotating and placing ZTA in the deposition processPThen ultrasonically cleaning for 10min and drying;
ZTA to be plated with NiCr alloyPStirring and mixing with micron NiCrAlY powder 15% of the ceramic and alcohol 5% of the mixed powder, the particle size of the NiCrAlY powder is 45 μm, putting into a mould with a specific shape, and curing in a vacuum drying oven; placing the preform into a vacuum tube furnace, heating to 820 deg.C at a heating rate of 10 deg.C/min, heating to 1100 deg.C at a heating rate of 7 deg.C/min, heating to 1300 deg.C at a heating rate of 4 deg.C/min, maintaining for 1h, and increasing ZTAPThe bonding strength is reduced to 1100 ℃ at the temperature of 4 ℃/min, reduced to 850 ℃ at the temperature reduction rate of 7 ℃/min, reduced to 450 ℃ at the temperature reduction rate of 10 ℃/min, and finally cooled along with the furnace;
and finally, placing the honeycomb-shaped prefabricated body in a sand mold with a specific size for fixing, heating the matrix raw material to 1600 ℃, casting liquid metal into the prefabricated body, and cooling for 20 hours to obtain the composite material with high wear resistance.
The obtained composite material is subjected to three-body abrasive wear, and the abrasive is selected from 70-mesh soft abrasive SiO2The load is 3Kg, the ultrasonic cleaning is carried out for 5 times and 30 min/time, the experiment after each abrasion is carried out for 30min in alcohol, the drying is carried out, the mass is respectively weighed on a precision balance, and the average volume loss rate is obtained to be 4.95mm3。
Example 3
Firstly ZTAPSoaking in ethanol for 20min, ultrasonic cleaning for 10min, oven drying in vacuum drying oven for 1 hr, and drying irregular ZTAPBall milling in a three-dimensional ball mill at 100r/min for 5 hr, stopping milling for 30min, filtering with 30 mesh sieve ZTAP；
In ZTA by vacuum multi-arc ion platingPPlating Ni-Cr alloy on the surface, Ar (purity 99.99%) as protective gas for plating to metallize the surface, continuously rotating and placing ZTA in the deposition processPThen ultrasonically cleaning for 20min and drying;
ZTA to be plated with NiCr alloyPWith micron-sized NiCr accounting for 15 percent of the mass of the ceramicStirring and mixing AlY powder and alcohol accounting for 5 percent of the total mass of the mixed powder, putting NiCrAlY powder with the particle size of 50 mu m into a mould with a specific shape and curing in a vacuum drying oven; placing the preform into a vacuum tube furnace, heating to 850 deg.C at a heating rate of 10 deg.C/min, heating to 1000 deg.C at a heating rate of 7 deg.C/min, heating to 1350 deg.C at a heating rate of 4 deg.C/min, maintaining for 1h, and increasing ZTAPThe bonding strength is reduced to 1150 ℃ at the temperature of 4 ℃/min, 850 ℃ at the temperature reduction rate of 7 ℃/min, 450 ℃ at the temperature reduction rate of 10 ℃/min, and finally, the materials are cooled along with the furnace;
and finally, placing the honeycomb-shaped prefabricated body in a sand mold with a specific size for fixing, heating the matrix raw material to 1600 ℃, casting liquid metal into the prefabricated body, and cooling for 21 hours to obtain the composite material with high wear resistance.
The obtained composite material is subjected to three-body abrasive wear, and the abrasive is selected from 70-mesh soft abrasive SiO2The load is 3Kg, the ultrasonic cleaning is carried out for 5 times and 30 min/time, the experiment after each abrasion is carried out for 30min in alcohol, the drying is carried out, the mass is respectively weighed on a precision balance, and the average volume loss rate is 5.43mm3。
Example 4
Firstly ZTAPSoaking in ethanol for 15min, ultrasonic cleaning for 20min, oven drying in vacuum drying oven for 1 hr, and drying irregular ZTAPBall milling in a three-dimensional ball mill at 100r/min for 7 hr, stopping milling for 30min, filtering with 45 mesh sieve ZTAP；
In ZTA by vacuum multi-arc ion platingPPlating Ni-Cr alloy on the surface, Ar (purity 99.99%) as protective gas for plating to metallize the surface, continuously rotating and placing ZTA in the deposition processPThen ultrasonically cleaning for 15min and drying;
ZTA to be plated with NiCr alloyPMixing with micron NiCrAlY powder 20% of ceramic mass and alcohol 5% of mixed powder total mass, NiCrAlY powder particle size is 55 μm, placing into mold with specific shape, and vacuum dryingCuring in a drying box; putting the prefabricated body into a vacuum tube furnace, heating to 850 ℃ at the heating rate of 10 ℃/min, heating to 1150 ℃ at the heating rate of 7 ℃/min, heating to 1400 ℃ at the heating rate of 4 ℃/min, preserving heat for 1h, and increasing ZTAPThe bonding strength is reduced to 1000 ℃ at the temperature of 3 ℃/min, to 850 ℃ at the temperature reduction rate of 7 ℃/min, to 450 ℃ at the temperature reduction rate of 10 ℃/min, and finally, the temperature is cooled along with the furnace;
and finally, placing the honeycomb-shaped prefabricated body in a sand mold with a specific size for fixing, heating the matrix raw material to 1600 ℃, casting liquid metal into the prefabricated body, and cooling for 22 hours to obtain the composite material with high wear resistance.
The obtained composite material is subjected to three-body abrasive wear, and the abrasive is selected from 70-mesh soft abrasive SiO2The load is 3Kg, the ultrasonic cleaning is carried out for 5 times and 30 min/time, the experiment after each abrasion is carried out for 30min in alcohol, the drying is carried out, the mass is respectively weighed on a precision balance, and the average volume loss rate is 5.31mm3。
Example 5
Firstly ZTAPSoaking in ethanol for 20min, ultrasonic cleaning for 15min, oven drying in vacuum drying oven for 1 hr, and drying irregular ZTAPBall milling in a three-dimensional ball mill at 120r/min for 9 hr, stopping milling for 30min, filtering with 50 mesh sieve ZTAP；
In ZTA by vacuum multi-arc ion platingPPlating Ni-Cr alloy on the surface, Ar (purity 99.99%) as protective gas for plating to metallize the surface, continuously rotating and placing ZTA in the deposition processPThen ultrasonically cleaning for 15min and drying;
ZTA to be plated with NiCr alloyPStirring and mixing with micron NiCrAlY powder accounting for 25 percent of the mass of the ceramic and alcohol accounting for 5 percent of the total mass of the mixed powder, wherein the particle size of the NiCrAlY powder is 58 mu m, and then putting the NiCrAlY powder into a mould with a specific shape to solidify in a vacuum drying oven; placing the preform in a vacuum tube furnace, heating to 850 deg.C at a heating rate of 10 deg.C/min, heating to 1150 deg.C at a heating rate of 7 deg.C/min, and heating to 4 deg.CHeating to 1400 deg.C at a temperature rise rate of 1400 deg.C/min, maintaining for 1 hr, and increasing ZTAPThe bonding strength is reduced to 1000 ℃ at the temperature of 3 ℃/min, to 850 ℃ at the cooling rate of 8 ℃/min, to 500 ℃ at the cooling rate of 5 ℃/min, and finally, the temperature is cooled along with the furnace;
and finally, placing the honeycomb-shaped prefabricated body in a sand mold with a specific size for fixing, heating the matrix raw material to 1600 ℃, casting liquid metal into the prefabricated body, and cooling for 23 hours to obtain the composite material with high wear resistance.
The obtained composite material is subjected to three-body abrasive wear, and the abrasive is selected from 70-mesh soft abrasive SiO2The load is 3Kg, the ultrasonic cleaning is carried out for 5 times and 30 min/time, the experiment after each abrasion is carried out for 30min in alcohol, the drying is carried out, the mass is respectively weighed on a precision balance, and the average volume loss rate is 5.64mm3。
Example 6
Firstly ZTAPSoaking in ethanol for 20min, ultrasonic cleaning for 25min, oven drying in vacuum drying oven for 1 hr, and drying irregular ZTAPBall milling in a three-dimensional ball mill at 150r/min for 10 hr, stopping milling for 30min, filtering with 60 mesh sieve ZTAP；
In ZTA by vacuum multi-arc ion platingPPlating Ni-Cr alloy on the surface, Ar (purity 99.99%) as protective gas for plating to metallize the surface, continuously rotating and placing ZTA in the deposition processPThen ultrasonically cleaning for 15min and drying;
ZTA to be plated with NiCr alloyPStirring and mixing with micron NiCrAlY powder accounting for 30 percent of the mass of the ceramic and alcohol accounting for 10 percent of the total mass of the mixed powder, wherein the particle size of the NiCrAlY powder is 60 mu m, and then putting the NiCrAlY powder into a mould with a specific shape to solidify in a vacuum drying oven; putting the prefabricated body into a vacuum tube furnace, heating to 900 ℃ at a heating rate of 15 ℃/min, heating to 1150 ℃ at a heating rate of 8 ℃/min, heating to 1450 ℃ at a heating rate of 5 ℃/min, keeping the temperature for 2h, and increasing ZTAPThen reduced to 1150 ℃ at a temperature of 5 ℃/min, and then reduced to 8 ℃/minThe temperature reduction rate is reduced to 900 ℃, the temperature reduction rate is reduced to 500 ℃ at the speed of 15 ℃/min, and finally, the furnace is cooled;
and finally, placing the honeycomb-shaped prefabricated body in a sand mold with a specific size for fixing, heating the matrix raw material to 1650 ℃, casting liquid metal into the prefabricated body, and cooling for 24 hours to obtain the composite material with high wear resistance.
The obtained composite material is subjected to three-body abrasive wear, and the abrasive is selected from 70-mesh soft abrasive SiO2The load is 3Kg, the ultrasonic cleaning is carried out for 5 times and 30 min/time, the experiment after each abrasion is carried out for 30min in alcohol, the drying is carried out, the mass is respectively weighed on a precision balance, and the average volume loss rate is obtained to be 4.82mm3。
Compared with the wear resistance of the traditional Cr15 working condition corresponding to the six embodiments, the wear resistance of the composite material prepared by the invention is 12 times that of the traditional single material Cr15, and the ZTA is provedPThe ceramic effectively improves the wear resistance of the composite material, ZTAPThe hardness is high, the toughness is good, the heat matching with the matrix is good, and the ceramic particles play a role in resisting abrasion under the support of the matrix; the modified ceramic particle reinforced iron-based composite material prepared by the invention designs the reinforcement into a porous honeycomb shape, and the cylindrical metal substrate extending into the ceramic reinforcement increases the bonding surface area and bonding performance of the ceramic reinforcement and the substrate, reduces the overall brittleness of the composite layer, plays a role in pinning, effectively prevents the composite layer from being broken and even from being peeled off integrally, and further improves the mechanical property of the composite material. Along with the abrasion, the ceramic particles gradually protrude from the matrix to play a double shadow effect, so that the matrix material around is protected. The ceramic particles and the metal matrix are abraded simultaneously in the early period of abrasion, but because the hardness of the matrix is low, the abrasion loss is large, and the matrix is gradually sunken, the ceramic particles protruding out of the metal matrix bear main abrasion, so that the surrounding matrix is protected, the ceramic particles are prevented from being further abraded, and compared with the traditional single metal material, the abrasion resistance of the composite material is greatly improved.
The invention is realized by the pair ZTAPThe NiCr metal is plated on the surface of the ceramic, so that the ZTA is effectively improvedPThe interface wettability of the ceramic and the metal matrix, NiCrAlY powder is used in the process of sintering the prefabricated body, sintering necks are formed among particles after sintering, the bonding strength among the particles is improved, the casting infiltration effect in the subsequent casting process is met, and the method is compared with the ZTA which is generally used at present and is obtained by changing the preparation processPFe composite material and chemically nickel-plated modified ZTAPCompared with the composite material, the interface layer of the composite material obtained by the invention forms Cr2O3，Y2O3And Al2O3And Cr element is solid-dissolved in the iron matrix to play a role of strengthening.
In summary, the invention deals with ZTAPThe metallization of the ceramic surface converts the mechanical bonding interface of the original ceramic and the metal matrix into metallurgical bonding between the metal transition layer and the metal matrix, and further effectively improves the bonding strength of the interface and the mechanical property and tribological property of the composite material, thereby obtaining the novel wear-resistant material with high impact resistance and high wear resistance. The novel high-performance wear-resistant part is tried to be popularized and applied in a large scale under actual harsh working conditions.
The above-mentioned contents are only for illustrating the technical idea of the present invention, and the protection scope of the present invention is not limited thereby, and any modification made on the basis of the technical idea of the present invention falls within the protection scope of the claims of the present invention.

Claims (10)

1. The preparation method of the modified ceramic particle reinforced iron-based composite material is characterized by comprising the following steps of:
s1, for ZTAPPreheating ceramic particles, and preparing the ZTA of the nickel-chromium alloy plating by adopting a physical vapor deposition methodPCeramic particles;
s2, plating ZTA of nickel-chromium alloyPMixing and stirring ceramic particles, micron-sized NiCrAlY alloy powder and alcohol, and shaping and drying to obtain a ceramic prefabricated body with a honeycomb structure;
s3, performing vacuum sintering treatment on the ceramic preform at the high temperature of 1250-1450 ℃, casting high-chromium cast iron liquid metal after cooling, and cooling to obtain the modified ceramic particle reinforced iron-based composite material.
2. The method of claim 1, wherein the ZTA is performed in step S1PThe particle size of the ceramic particles is 3-5 mm.
3. The method of claim 1, wherein step S1 is preceded by preheating for ZTAPCarrying out surface micro-roughening on the ceramic particles to obtain ZTA with the roughness of 4-10 mu mPCeramic particles.
4. The method according to claim 1, wherein the temperature of the preheating treatment in step S1 is 300-400 ℃.
5. The method of claim 1, wherein in step S1, the vacuum multi-arc ion plating method is adopted in ZTAPPlating Ni-Cr alloy on the surface of ceramic grains, and continuously rotating to hold ZTA during platingPA rotating disk of ceramic particles.
6. The method of claim 1, wherein in step S2, the micron-sized NiCrAlY alloy powder has a particle size of 40-60 μm, and the NiCrAlY alloy powder comprises nickel-chromium-plated alloy ZTAP10-30% of the mass of the ceramic particles, and the alcohol accounts for the nickel-chromium alloy plated ZTAP5 to 10 percent of the total mass of the ceramic particles and the NiCrAlY powder.
7. The method according to claim 1, wherein in step S3, the vacuum high-temperature sintering heat treatment is specifically:
heating from room temperature to 800-900 ℃ at a heating rate of 5-15 ℃/min, then heating to 1000-1150 ℃ at a heating rate of 6-8 ℃/min, then heating to 1250-1450 ℃ at a heating rate of 3-5 ℃/min, preserving heat for 0.5-2 h, then cooling to 1000-1150 ℃ at a temperature of 3-5 ℃/min, then cooling to 800-900 ℃ at a cooling rate of 6-8 ℃/min, finally cooling to 400-500 ℃ at a cooling rate of 5-15 ℃/min, and finally cooling to room temperature.
8. The method according to claim 1, wherein in step S3, the high-chromium cast iron liquid metal is cast by a bottom casting method, the heating temperature is 1550-1650 ℃, and the cooling time is 18-24 h.
9. The modified ceramic particle reinforced iron-based composite material is characterized by comprising a high-chromium cast iron matrix and NiCrAlY modified ZTAPCeramic particles, high-chromium cast iron matrix and ZTAPThe volume fractions of the ceramic particles are 60-90% and 10-40%, respectively.
10. The composite material of claim 9, wherein the modified ceramic particle reinforced iron-based composite material is prepared by the method of claim 1.
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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112456980A (en) * 2020-12-11 2021-03-09 西安交通大学 Array type ceramic prefabricated body sintering unit monomer and high-flux pressureless sintering method
CN112872351A (en) * 2021-01-13 2021-06-01 太原理工大学 Preparation method of hybrid synergistic reinforced iron-based wear-resistant material

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN104177070A (en) * 2014-09-12 2014-12-03 淄博启明星新材料有限公司 Preparation method of microcrystal zirconium aluminum composite grinding medium
CN104525949A (en) * 2014-12-30 2015-04-22 广东省工业技术研究院(广州有色金属研究院) High abrasion-resisting copper-based friction composite material and preparing method thereof
CN106735101A (en) * 2016-11-10 2017-05-31 西安交通大学 A kind of preparation method of the ZTA particle enhanced steel iron-based composite grinding rolls based on chemical activation treatment
CN109513905A (en) * 2018-12-28 2019-03-26 西安交通大学 A kind of preparation method being surface-treated the iron-based composite wear-resistant part of ZTA particle enhanced steel
CN109706438A (en) * 2018-12-28 2019-05-03 西安交通大学 A kind of preparation method of the modified ZTA ceramic particle enhancing steel-based composite material in surface
CN110935864A (en) * 2019-12-04 2020-03-31 西安交通大学 Preparation method of surface-treated ZTA particle-reinforced steel-based composite grinding roller
CN111394702A (en) * 2020-04-03 2020-07-10 北航（四川）西部国际创新港科技有限公司 Thermal barrier coating and preparation method and application thereof

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN104177070A (en) * 2014-09-12 2014-12-03 淄博启明星新材料有限公司 Preparation method of microcrystal zirconium aluminum composite grinding medium
CN104525949A (en) * 2014-12-30 2015-04-22 广东省工业技术研究院(广州有色金属研究院) High abrasion-resisting copper-based friction composite material and preparing method thereof
CN106735101A (en) * 2016-11-10 2017-05-31 西安交通大学 A kind of preparation method of the ZTA particle enhanced steel iron-based composite grinding rolls based on chemical activation treatment
CN109513905A (en) * 2018-12-28 2019-03-26 西安交通大学 A kind of preparation method being surface-treated the iron-based composite wear-resistant part of ZTA particle enhanced steel
CN109706438A (en) * 2018-12-28 2019-05-03 西安交通大学 A kind of preparation method of the modified ZTA ceramic particle enhancing steel-based composite material in surface
CN110935864A (en) * 2019-12-04 2020-03-31 西安交通大学 Preparation method of surface-treated ZTA particle-reinforced steel-based composite grinding roller
CN111394702A (en) * 2020-04-03 2020-07-10 北航（四川）西部国际创新港科技有限公司 Thermal barrier coating and preparation method and application thereof

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
齐宝森: "《新型材料及其应用》", 30 September 2007, 哈尔滨工业大学 *

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112456980A (en) * 2020-12-11 2021-03-09 西安交通大学 Array type ceramic prefabricated body sintering unit monomer and high-flux pressureless sintering method
CN112872351A (en) * 2021-01-13 2021-06-01 太原理工大学 Preparation method of hybrid synergistic reinforced iron-based wear-resistant material
CN112872351B (en) * 2021-01-13 2023-07-14 太原理工大学 Preparation method of hybrid synergistic reinforced iron-based wear-resistant material

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