CN109576547A - A kind of ternary boride enhancing Ti(C, N) base metal-ceramic material and preparation method thereof - Google Patents
A kind of ternary boride enhancing Ti(C, N) base metal-ceramic material and preparation method thereof Download PDFInfo
- Publication number
- CN109576547A CN109576547A CN201811570740.3A CN201811570740A CN109576547A CN 109576547 A CN109576547 A CN 109576547A CN 201811570740 A CN201811570740 A CN 201811570740A CN 109576547 A CN109576547 A CN 109576547A
- Authority
- CN
- China
- Prior art keywords
- powder
- phase
- base metal
- ternary boride
- ceramic material
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
- C22C29/04—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbonitrides
-
- 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
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
- C22C1/051—Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material therefor
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/005—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides comprising a particular metallic binder
Abstract
The invention discloses a kind of ternary borides to enhance Ti(C, N) base metal-ceramic material and preparation method thereof.Main preparation process are as follows: with Ti (C, N) cermet raw material powder, carbide and nitride boride powder, binder phase material powder；Binary borides powder is raw material, Ti (C is made by ball milling mixing, drying, molding and sintering step, N) based ceramic metal, in the Binder Phase for being distributed in cermet material of the second ceramic phase particle small and dispersed wherein generated through reaction in-situ, the presence of the phase can effectively improve the hardness and toughness of cermet material.Compared with the technology of the enhancing wearability such as existing coating and surface treatment, obtained Ti (C, N) base metal-ceramic material Rockwell hardness is up to 91.5~94HRA, and bending strength is up to 1800~2800MPa, and fracture toughness is up to 12~15MPam‑1/2, in addition, Wear track depth measured by Ti (C, N) base metal-ceramic material of this method preparation relatively reduces about 70% with Binder Phase cermet, coefficient of friction reduces about 0.1.
Description
Technical field
Present invention relates particularly to a kind of generated in-situ ternary boride enhancing Ti (C, N) base metal-ceramic material and its systems
Preparation Method belongs to field of metal matrix composite.
Background technique
After Ti (C, N) base metal-ceramic material is found for the first time from nineteen seventies, because higher hardness,
Excellent wearability and red hardness is to get the attention.Ti (C, N) base metal-ceramic material is with TiC, TiN or Ti
(C, N) is used as ceramic phase, and metal Co and Ni is as Binder Phase, the densified composite being prepared by liquid phase sintering technology.
Currently, the development of Ti (C, N) base metal-ceramic material is maked rapid progress, it is mainly reflected in High speed finish machining and semifinishing cutter
Using upper, compared to WC-Co hard alloy cutter material, the optimum cutting speed of Ti (C, N) based ceramic metal can usually be mentioned
It is 3~10 times high, and good chemical stability can be kept in cutting process.However, the hard brittleness of ceramic matrix is still
It is to restrict the widely applied key factor of Ti (C, N) base metal-ceramic material.So far, most common cermet increases
Tough method is improved Binder Phase content and addition nanometer phase, although wherein the content for improving Binder Phase can have significant toughening to make
With, but high metal phase also greatly compromises the hardness of material, in addition, addition nanometer can mutually pass through dispersion-strengthened action toughening
Metallic matrix, but in the agglomeration and liquid sintering process of nanometer phase nanometer phase reaction so that nanometer addition phase selection tool
There is larger difficulty.
Ternary boride has excellent mechanical property and wear and corrosion behavior, however is but rarely reported for as Ti
The activeness and quietness phase of (C, N) based ceramic metal, this is because B is easily inclined in hard phase and Binder Phase interface in liquid-phase sintering
It is poly-, or brittleness third phase is formed, or be solid-solution in metallic binding phase, cause the penalty of material.
Patent (CN104630591A) discloses a kind of Ti (C, N) the Base Metal pottery of strip ternary boride activeness and quietness
Fe and B element are introduced into Ti (C, N) based ceramic metal in the form of ferro-boron powder, and control additive amount and technological parameter by porcelain,
The generation of the problems such as to avoid Fe and B element from being solid-solution in metallic binding phase, makes Mo during the sintering process2FeB2Particle occurs preferentially
Growth, generates the Mo of strip2FeB2Hard phase.By this strip ternary boride hard phase with this toughening Ti (C, N) base
Cermet.But the strip ternary boride of this preferred growth will cause stress concentration, in application process easily by
It is produced fracture in yield limit, causes component failure, while strip ternary boride, due to being preferred growth, partial size is excessive,
It is easy to fall off in friction process to become Hard Inclusion, to increase abrasion.In addition, in high-temperature sintering process, due to generating ternary
The reaction of boride is acutely and its reaction temperature is lower than liquidus temperature point, therefore, in the process of strip ternary boride growth
The middle Mo and Ni element that can largely consume surrounding, however, Mo element is Mo2C's primarily forms element and Mo2C can pass through solid solution
The transitional face that precipitation mechanism is formed between hard phase and Binder Phase improves the wetability of this two-phase, and Ni element is the master of Binder Phase
That wants element provides certain toughness together for material；After boride addition, because reacting the preferential of the ternary boride generated
Fast-growth, Mo the and Ni concentration of element around ternary boride phase drastically reduce, this results in hard around ternary boride
The shell phase of matter phase particle formed it is insufficient, liquid phase filling it is also insufficient；The distribution for also resulting in material entirety Binder Phase is also uneven
It is even.
Summary of the invention
In view of the deficiencies of the prior art, the first purpose of this invention is to provide the three of a kind of uniform fine grain dispersion-strengtherning
First boride enhances Ti (C, N) base metal-ceramic material.
Second object of the present invention is to provide a kind of reaction in-situ generation ternary boride enhancing Ti (C, N) Base Metal
The preparation method of ceramic material.
To achieve the goals above, the invention provides the following technical scheme:
A kind of ternary boride of the present invention enhances Ti (C, N) base metal-ceramic material, Ti (C, N) the based ceramic metal material
Material is made of the ternary boride of hard phase, Binder Phase and even dispersion in Binder Phase and/or hard phase, the hard phase
It is mutually made of with Ti (C, N) cermet addition, the addition is mutually carbide and/or nitride；The ternary boride
Partial size is 0.1~5 μm.
What the present invention initiated provides disperse containing uniform fine grain in Binder Phase and/or the Ti of the ternary boride of hard phase
(C, N) base metal-ceramic material, the cermet material can be under the premise of keeping high Binder Phase excellent in toughness effectively
The hardness of material is improved, enhances wearability, and can be by the granularity, content and type of ternary boride to the performance of material
Regulated and controled.
Preferred scheme, Ti (C, the N) base metal-ceramic material is by hard phase, Binder Phase and even dispersion in bonding
Ternary boride composition in phase, the hard phase are mutually made of with Ti (C, N) cermet addition, and the addition is mutually carbonization
Object and/or nitride；The partial size of the ternary boride is 1~2 μm.
Preferred scheme, the raw material components of the base titanium carbonitride material and the weight percent of each component
Are as follows:
45~60wt% of Ti (C, N) cermet raw material；Add 15~35wt% of phase raw material；Binder phase material 10~
25%；0.05~5wt% of binary borides powder；
Ti (C, N) the cermet raw material is selected from titanium carbide powder and titanium nitride powder；Or it is dissolved selected from titanium carbonitride
Body powder；
The addition is mutually selected from WC, Mo2C、TaC、NbC、HfC、W2C、VC、Cr3C2, ZrC, AlN, NbN, TaN, ZrN powder
At least one of；
The binder phase material is selected from cobalt powder and/or nickel powder；
The binary borides powder is selected from WB2、Mo2B、MoB、CrB2At least one of.
As a further preference, the weight hundred of the raw material components of the base titanium carbonitride material and each component
Score are as follows:
48~52wt% of Ti (C, N) cermet raw material；Add 26~30wt% of phase raw material；Binder phase material 18~
22%；1~3wt% of binary borides powder.
As a further preference, the binary borides powder is selected from WB2, at least one of MoB.
In the present invention, the selection gist of binary borides is its crystal structure and formation of initial stage, according to Fe2The pattern of B
To be needle-shaped, thus can rodlike, the TiB of preferential growth growth in subsequent reaction growth course2Pattern be bulk, pass through burning
Reaction growth during knot will form the facts such as plate shape, by CrB2Crystal structure observed after can be obtained, CrB2
Crystal structure be hexagonal structure, microstructure is columnar crystal morphology, therefore it can grow into column structure after sintering, this
It is larger so as to cause big distortion of lattice with the crystal structure difference of Binder Phase, while column precipitated phase may hinder Binder Phase
Continuity, influence the performance of material.MoB2Similar with graphene layer structure with lamellar structure, which has layer
Between the weak feature of binding force therefore select the WB with orthorhombic crystalline structure2And metastable phase MoB preferably reacts former
Material.
As further preferably, the binary borides powder is selected from WB2。
As a further preference, the addition is mutually selected from WC, MoC, at least one of TaC.
Preferred scheme, the partial size of the hard phase are 1 μm~10 μm.
As a further preference, the partial size of the hard phase is 1 μm~5 μm.
Binder Phase in generation liquid phase in high-temperature sintering process by being filled between hard particles to play densification
Effect, so Binder Phase is continuously distributed between hard-phase particles, it is not existing in granular form.
A kind of preparation method of ternary boride enhancing Ti (C, N) base metal-ceramic material of the present invention, includes the following steps:
Match by design proportion and takes Ti (C, N) cermet raw material powder, addition phase raw material powder, binder phase material powder；
Binary borides powder；Binary borides powder is first placed in ultrasonic disperse in ethanol solution, then will be scattered in anhydrous
Binary borides powder and other three classes raw material powders and reduction carbon dust in ethyl alcohol, forming agent ball milling mixing, dry acquisition
Mixed-powder；Mixed-powder is pressed into green compact, then green compact is placed in sintering furnace in 400~580 DEG C of degreasing removal moldings
Then agent carries out vacuum pressure sintering again, sintering temperature is 1400~1600 DEG C, and final air pressure is 2~10MPa.
Inventors have found that in the preparation process for carrying out ternary boride enhancing Ti (C, N) base metal-ceramic material, binary
The fully dispersed molding for material of boride powder be it is vital, by the way that binary borides powder is placed in anhydrous second
Alcoholic solution disperses effectively guarantee the fully dispersed of binary borides powder with the common ball milling of other powder again in advance.
Preferred scheme, the time of the ultrasonic disperse are 12~48h.
Preferred scheme, 45 DEG C of the temperature < of the ultrasonic disperse.
Preferred scheme, when the ultrasonic disperse, the mass volume ratio of binary borides powder and dehydrated alcohol is 1g:6
~24ml.
In the present invention, for ultrasonic disperse using conventional ultrasonic cleaning instrument, intensity of acoustic wave used is 0.5W/cm2, should
The generation that visually can see water flow under intensity, in this way can be with dispersion of the powder quick in dehydrated alcohol.
In the actual operation process, carrier of the cover-type container as powder and alcohol should be used in ultrasonic procedure, kept away
The volatilization for exempting from alcohol leads to the reduction of wet grinding media total amount, while the temperature of strict control medium is wanted during ultrasonic disperse, because
It will lead to temperature of the fever of aqueous medium to improve dehydrated alcohol for the fever of machine, therefore, it is necessary to real-time by thermometer
The temperature for reading medium needs to suspend instrument when temperature reaches 45 DEG C, and dispersion powders and anhydrous are reduced by replacement cold water
The temperature of ethyl alcohol, control temperature are to reduce the gasification volatilization of dehydrated alcohol lower than 45 DEG C of main purposes.
Preferred scheme, the partial size of Ti (C, N) the cermet raw material powder are 2~10 μm, the binder phase material
The partial size of powder is 5~15 μm, and the partial size of the addition phase raw material powder is 1~15 μm, and the partial size of binary borides powder is 1
~15 μm.
In cermet material, hard phase Ti (C, N) particle is insoluble in entire sintering process, therefore, Ti (C,
N) partial size of powder should select relatively fine particle, and main purpose is hard-phase particles mistake in the material for avoiding obtaining sintering
Greatly, in addition, added carbide powder is also required to lesser partial size, purpose be promote its in liquid sintering process more rapidly
Adequately be diffused transfer, the powder diameter of Binder Phase then can choose compared to it is lower relatively it is thick a bit, the thicker particle of one side
The oxygen content of powder can be reduced, on the other hand, the good fluidity of coarse grain powder, can to avoid agglomeration generation and energy
Enough to be more uniformly present in material, metallic binding phase will form liquid phase in sintering process, therefore, even if powder diameter is thicker
It also can completely be filled into the gap between all hard particles during the sintering process, make densifying materials.Boride mutually belongs to
In micro addition phase, if the state of Dispersed precipitate can be not achieved because particle is grown up after reaction using thicker particle,
But using sub-micron or micron-sized powder, there will be the generations of agglomeration, in order to avoid part caused by this agglomeration
The case where formation of region ternary boride ceramic phase and the poor Binder Phase in part, occurs, which need to be divided in advance
Dissipate processing.
As a further preference, the partial size of Ti (C, N) the cermet raw material powder is 2~4 μm, the Binder Phase
The partial size of raw material powder is 6~8 μm, and the partial size of the addition phase raw material powder is 1~3 μm, the partial size of binary borides powder
It is 0.1~1 μm.
The additional amount of preferred scheme, the reduction carbon dust is 0.05~2wt% of raw material powder gross mass.
Preferred scheme, the forming agent is selected from one of polyethylene, rubber, stearic acid, paraffin, SBS, PVA, described
The additive amount of forming agent is the 3-4.5% of raw material powder gross mass.
Preferred scheme, the mode of the ball milling mixing are wet ball-milling, and the wet grinding media is dehydrated alcohol, and ball milling turns
Speed is 50~200r/min；Ratio of grinding media to material is (2~10): 1, Ball-milling Time is 48~96h.
In the actual process, ball-milling medium dehydrated alcohol used in usual ball milling has 1/3 to derive from binary borides powder
The dispersing agent of body, in addition 2/3 dehydrated alcohol derives from the dispersing agent of forming agent, when such as using paraffin as forming agent, forming agent
The adding manner of paraffin is first to weigh suitable paraffin block, by pouring into the ethanol solution kept stirring after heating and melting
In obtain the paraffin little particle of tiny dispersion, then mixed together with dehydrated alcohol with other material powders.
Preferred scheme, the ball milling ball are selected from one of stainless steel ball, sintered carbide ball, cermet ball.
Preferred scheme, described dry using vacuum drying, drying temperature is 60~90 DEG C, and drying time is 3~5h.
Preferred scheme, described to be compressed to two-way compacting, used pressing pressure is 100~180MPa.
Preferred scheme, the degreasing are carrier gas degreasing, and gases used is nitrogen or argon gas.
Preferred scheme, vacuum pressure sintering process are to be sintered under vacuum environment first, the vacuum degree be 0.005~
0.01Pa, heating rate be 6-15 DEG C/min, respectively 550-600 DEG C, 750-850 DEG C, 1050-1130 DEG C at a temperature of keep the temperature
1~3h is finally warming up to 1430~1600 DEG C, keeps the temperature 0.5~1h, and being then re-filled with inert gas to air pressure is 2~10MPa,
Continue 0.5~5h of heat preservation, cools to room temperature with the furnace.
In the present invention, sintering procedure is vital, and the present invention is by many experiments, by the way that multiple heat preservation temperature are arranged
Area, and effective control heating efficiency, the sintering effect being finally obtained.The present invention is first in 550-600 DEG C of temperature range
Heat preservation, it is therefore an objective to remove forming agent paraffin etc., can avoid that material will be present in the form of carbon residue because paraffin removing is not thorough
In, damage the performance of material；Then the temperature range at 750-850 DEG C is kept the temperature, and makes the change brought into raw material powder in material
The removing for closing oxygen carries out deoxidation with reacting for oxygen using carbon；Then the temperature range at 1050-1130 DEG C is kept the temperature: in the temperature
Solid phase reaction occurs for segment material, and diffusion takes place between element, and the heat preservation regular hour is to promote solid phase reaction more
It adequately carries out, makes material initial densification；Finally 1430~1600 DEG C temperature range keep the temperature purpose: the temperature range
For final sintering temperature section, carry out at such a temperature pressure heat-preserving be then in order to promote the complete progress of liquid reactive sintering with
Liquid metal is sufficient filling with pellet pores, densifies material entirely.
Why need to strict control sintering procedure, the Exploration on mechanism that inventor passes through many experiments is due to binary
Boride has and can generate the characteristic of vigorous reaction with metal Co/Ni, thus be sintered in preparation process flow, what which occurred
Temperature range needs are strictly regulated and controled, this is because the reaction occurs in metal phase liquidus point temperature hereinafter, being reaction
When material also in the solid-phase sintering stage, but the generation of the reaction then will lead to the reaction zone and partial liquid phase occurs, if this
Overlong time existing for partial liquid phase area will certainly promote the element on periphery largely to spread to the partial liquid phase area, lead to part
The enrichment of element, and when this local limited carbon element content in section can not meet the demand for diffusing into the element come, then can
Occur lacking carbon phase, directly results in the penalty of material.
Specifically, the reaction temperature of ternary boronation boron is 1200 DEG C or so in the present invention, can be sent out higher than 1200 DEG C
Raw reaction in-situ forms ternary boride, but just will appear liquid in 1400 DEG C or more Co/Ni, can just have in material violent
Liquid phase reactor occurs, and inventor has found that violent liquid phase reactor can generate certain inhibiting effect to growing up for ternary boride,
Therefore final sintering temperature will be set as by 1430 DEG C~1600 DEG C in the present invention, it can sintering densification is completed, it can also
To avoid growing up for ternary boride, the ternary boride of uniform fine grain Mass is finally obtained.And 1200 DEG C to 1430 DEG C it
Between do not kept the temperature in the present invention, but directly heat up, be not occur because of this stage Co/Ni liquid phase, be equivalent to original occurred
Position reaction is unable to get inhibition, if kept the temperature in this stage, it will ternary boride is made to have time enough to grow up.Thus
It cannot get required fine-graded ternary boride.Therefore, the present invention is only to have carried out heating not protect at 1130 DEG C~1430 DEG C
Temperature, in the actual operation process, sintering heating rate can generally also be improved to 1.2-1.5 times of former heating rate.Until Co/Ni
After reaching liquid phase, heat preservation sintering is just carried out.The size and distribution of ternary boride ceramic phase can be effectively controlled in this way.
As a further preference, the inert gas is argon gas
Material phase analysis is carried out to Ti (C, the N) base metal-ceramic material using above method preparation, through in-situ preparation three
First boride, this is mutually generated by the binary borides powder and bonding phase reaction that add.
Structure observation is carried out to Ti (C, the N) base metal-ceramic material using above method preparation, through generated in-situ
Ternary boride even dispersion is distributed in Binder Phase.
The principle of the present invention and advantage:
What the present invention initiated provides disperse containing uniform fine grain in Ti (C, N) the Base Metal pottery of the ternary boride of Binder Phase
Ceramic material, the cermet material can effectively improve the hard of material under the premise of keeping high Binder Phase excellent in toughness
Degree enhances wearability.
Disperse containing uniform fine grain provided by the present invention is in Ti (C, N) based ceramic metal material of the ternary boride of Binder Phase
Material fills mainly by the way that specific binary borides powder and addition phase (carbide or nitride) is added in these materials
After dividing mixing dispersion, it is sintered and is prepared and effectively controlling sintering procedure, specific formation basic theory is as follows:
After binary borides addition, it can occur first to react as follows in the sintering process of material: MB+Co →
MCoB；MB+Ni→MNiB；With the raising of sintering temperature, reaction process becomes: MCoB+Co → M2CoB2+ Co, MNiB+Ni
→M2NiB2+Ni.After generating stable reaction product, liquid phase reactor acutely occurs in material, and added carbide formers are not
Disconnected solid solution enters in Binder Phase, and is that core is precipitated with Ti (C, N) hard-phase particles, by the crystalline substance of added carbide
Body structure is cubic structure, and Ti (C, N) particle is face-centred cubic structure, therefore each carbide formers tend to Ti (C, N) hard
It is precipitated that hard phase is made to grow up on phase particle, however, the crystal structure of ternary boride ceramic phase and added carbide
Crystal structure difference is larger, and to be precipitated in the phase, the larger required energy of distortion of lattice that will lead on interface is higher, institute
With in liquid sintering process, the reaction process in material is based on the formation of shell phase and growing up, and ternary boride Xiang Zeji
Continue to stablizing phase transition.In addition, the visibly homogeneous dispersion of binary borides particle after ultrasonic disperse is in the base, or even
It is also difficult to be moved to similar distance between two particles in liquid sintering process, phase crystal grain avoided of this just high degree
Between combination grow up so that the form that is distributed with small and dispersed of the ternary boride ceramic particle is to be retained.
In whole preparation process of the invention, the existence form of B element is binary borides or ternary boride always,
And binary borides will pass through reaction in-situ and generate with dystectic ternary boride phase before liquid phase occurs in Binder Phase,
Therefore, B element has no chance to be dissolved into Binder Phase during the sintering process, and transfer segregation more occurs not over liquid phase process,
Even if promoting the appearance of partial liquid phase in reaction process in situ, but its evenly dispersed distribution form and entire reaction process
Duration it is shorter, will not cause to have an impact the uniformity of material each element and composition of object phase etc..
The present invention is that the ternary boron that reaction in-situ generates small and dispersed occurs by the binary borides and Binder Phase of addition
Compound carrys out the wearability and toughness of reinforcing material, compared with existing coating, surface treatment etc. improve the technology of wearability, this hair
Bright feature is:
1) raw material used is extensive, and simple production process is of relatively low cost；
2) production equipment required for is less, easy to operate；
3) cermet material core and surface property uniformity produced, the peeling on surface layer do not influence its globality
Energy.
4) Wear track depth measured by Ti (C, N) base metal-ceramic material of this method preparation is relatively the same as Binder Phase cermet
About 70% is reduced, coefficient of friction reduces about 0.1.
Detailed description of the invention
X-ray diffraction (XRD) map of sample obtained by Fig. 1 embodiment 1-3 and comparative example 1.
Scanning electron microscope (SEM) shape appearance figure of obtained sample in Fig. 2 embodiment 1-3 and comparative example 1-5, should
Picture is tissue topography observed under back-scattered electron mode (BSE).
The SEM that wherein Fig. 2 (a) is 1 gained sample A1 of embodiment schemes；
The SEM that Fig. 2 (b) is 1 gained sample A2 of embodiment schemes；
The SEM that Fig. 2 (c) is 1 gained sample A3 of embodiment schemes；
The SEM that Fig. 2 (d) is 1 gained sample A4 of comparative example schemes；
The SEM that Fig. 2 (e) is 2 gained sample A5 of comparative example schemes；
The SEM that Fig. 2 (f) is 4 gained sample A7 of comparative example schemes；
The SEM that Fig. 2 (g) is 5 gained sample A8 of comparative example schemes；
In sample A1 and comparative example 1 obtained by Fig. 3 embodiment 1 after the obtained rubbed wear test of sample A4
Worn-out surface SEM microstructure figure and power spectrum (EDS) result.
Specific embodiment
Below in conjunction with specific example, the present invention is further explained, these examples are merely to illustrate the present invention rather than limitation
Protection scope of the present invention.
Embodiment 1
Ti (C, N) 49g, WC 16g, MoC 4g, TaC 8g, WB are weighed respectively23g, Co 11g, Ni 9g, carbon dust 1g, at
Type agent (paraffin) 4g；Wherein the partial size of each powder is respectively 2.28 μm of Ti (C, N), and 3.66 μm of WC, 2 μm of MoC, 3.4 μm of TaC,
WB20.5 μm, 7.5 μm of Co, 8.9 μm of Ni, 11.4 μm of carbon dust.Sintered carbide ball is abrading-ball, ratio of grinding media to material 5:1, dehydrated alcohol
70mL, by load weighted 3gWB2Powder is mixed with 20mL dehydrated alcohol, is placed in closed container, and WB will be filled2With anhydrous second
The container of mixed alkoxide solution is placed in supersonic wave cleaning machine, and temperature measuring set is placed in the water of container exterior, opens ultrasonic wave
Cleaning machine takes out container when temperature reaches 40 DEG C, replaces cold water, places into container and continues ultrasound, then repeated temperature reaches
Cold water this operation is replaced at 40 DEG C, until total ultrasonic time reaches for 24 hours.Mixing time is 48h；Mixed material is at 80 DEG C
At a temperature of be dried in vacuo 5h, then dry uniformly mixed material is sieved with 100 mesh sieve；It is pressed under the pressure of 100MPa
Type pressure maintaining 5 seconds, then carries out removing forming agent in vacuum environment at 550 DEG C, soaking time 3h, then with 10 DEG C/
The heating rate of min is successively warming up to 600 DEG C, 800 DEG C, 1100 DEG C and 1430 DEG C, and on often rising to one of temperature spot
Shi Baowen 1h, finally 1430 DEG C at a temperature of lead to air pressure in inert gas argon gas to furnace in furnace and reach 6MPa, and keep the temperature guarantor
2h is pressed, then cools to room temperature with the furnace and obtains sintered sample A1.Gained sample A1 is dissolved by complicated carbonitride solid solution and Co-Ni
The three kinds of object phase compositions of body and WCoB ternary boride ceramic particle.
Cermet material in embodiment 1 is detected, shows that its Rockwell hardness is 91.5HRA, fracture toughness is
12.6MPa·m-1/2, bending strength 1800MPa, dry type reciprocating friction wear results are shown, are 300r/min in revolving speed, are carried
Lotus is 50N, is opposite grinding 10min in the case where YG6 trade mark sintered carbide ball to abrading-ball, the coefficient of friction of obtained material is 0.61
~0.63, Wear track depth is 14~16 μm.Shown in its microstructure such as Fig. 2 (a), ternary boride is mutually present in white bright in figure
Part, it can be seen that the ternary boride for reacting generation is distributed with the distribution of the Binder Phase of material, and that disperses is present in
In material, partial size is 2 μm or so.
Embodiment 2
Ti (C, N) 51g, WC 16g, MoC 4g, TaC 8g, WB are weighed respectively21g, Co 11g, Ni 9g, carbon dust 1g, at
Type agent 4g；Wherein the partial size of each powder is respectively 2.28 μm of Ti (C, N), and 3.66 μm of WC, 2 μm of MoC, 3.4 μm of TaC, WB2
0.5 μm, 7.5 μm of Co, 8.9 μm of Ni, 11.4 μm of carbon dust.Load weighted 1gWB2 powder is mixed with 20mL dehydrated alcohol, is placed in
In closed container, the container for filling WB2 and dehydrated alcohol mixed solution is placed in supersonic wave cleaning machine, by temperature measuring set
It is placed in the water of container exterior, opens supersonic wave cleaning machine, when temperature reaches 40 DEG C, take out container, replace cold water, place into
Container continues ultrasound, replaces cold water this operation when then repeated temperature reaches 40 DEG C, until total ultrasonic time reaches for 24 hours.Firmly
Matter alloying pellet is abrading-ball, and ratio of grinding media to material 5:1 adds dehydrated alcohol 50mL, then the WB2 for completing dispersion and dehydrated alcohol are mixed
Solution is added in ball grinder together, mixing time 48h；Mixed material 80 DEG C at a temperature of be dried in vacuo 5h, then will
Dry uniformly mixed material sieves with 100 mesh sieve；The compression moulding under the pressure of 100MPa, pressure maintaining 5 seconds, then in vacuum environment
In removing forming agent is carried out at 550 DEG C, soaking time 3h is then successively warming up to 600 with the heating rate of 10 DEG C/min
DEG C, 800 DEG C, 1100 DEG C and 1430 DEG C, and 1h is kept the temperature when often rising on one of temperature spot, finally in 1430 DEG C of temperature
Air pressure reaches 6MPa, and heat-insulation pressure keeping 2h in lower inert gas argon gas to furnace logical in furnace, then cools to room temperature with the furnace and burnt
Tie sample A2.Gained sample A2 is by complicated carbonitride solid solution and Co-Ni solid solution and WCoB ternary boride ceramics
Three kinds of object phase compositions of grain.
Cermet material in embodiment 2 is detected, shows that its Rockwell hardness is 91.2HRA, fracture toughness is
12.5MPa·m-1/2, bending strength 2200MPa, dry type reciprocating friction wear results are shown, are 300r/min in revolving speed, are carried
Lotus is 50N, is opposite grinding 10min in the case where YG6 trade mark sintered carbide ball to abrading-ball, the coefficient of friction of obtained material is 0.61
~0.63, Wear track depth is 16~18 μm.Shown in its microstructure such as Fig. 2 (b), ternary boride is mutually present in white bright in figure
Part, as shown by arrows, the generation are mutually comparatively fine, and for partial size at 1 μm or so, distribution is also more dispersed, this illustrates ultrasound point
WB2 after dissipating can more evenly be present in material.
Embodiment 3
Ti (C, N) 51g, WC 16g, MoC 4g, TaC 8g, MoB 1g, Co 11g, Ni 9g, carbon dust 1g are weighed respectively, at
Type agent 4g；Wherein the partial size of each powder is respectively 2.28 μm of Ti (C, N), and 3.66 μm of WC, 2 μm of MoC, 3.4 μm of TaC, 3 μ of MoB
7.5 μm of m, Co, 8.9 μm of Ni, 11.4 μm of carbon dust.
Load weighted 1gMoB powder is mixed with 20mL dehydrated alcohol, is placed in closed container, MoB and nothing will be filled
The container of water-ethanol mixed solution is placed in supersonic wave cleaning machine, and temperature measuring set is placed in the water of container exterior, is opened super
Sound wave cleaning machine takes out container when temperature reaches 40 DEG C, replaces cold water, places into container and continues ultrasound, then repeated temperature
Cold water this operation is replaced when reaching 40 DEG C, until total ultrasonic time reaches for 24 hours.Sintered carbide ball is abrading-ball, ratio of grinding media to material 5:
1, dehydrated alcohol 50mL is added, then the MoB for completing dispersion and dehydrated alcohol mixed solution are added in ball grinder together, mixing
Time is 48h；Mixed material 80 DEG C at a temperature of be dried in vacuo 5h, then dry uniformly mixed material is crossed 100
Mesh；The compression moulding under the pressure of 100MPa pressure maintaining 5 seconds, then carries out removing molding in vacuum environment at 550 DEG C
Agent, soaking time 3h are then successively warming up to 600 DEG C, 800 DEG C, 1100 DEG C and 1430 DEG C with the heating rate of 10 DEG C/min,
And 1h is kept the temperature when often rising on one of temperature spot, finally 1430 DEG C at a temperature of in furnace lead to inert gas argon gas extremely
Air pressure reaches 6MPa, and heat-insulation pressure keeping 2h in furnace, then cools to room temperature with the furnace and obtain sintered sample A3.Gained sample A3 is by complexity
Carbonitride solid solution and Co-Ni solid solution and the three kinds of object phase compositions of MoNiB ternary boride ceramic particle.
Cermet material in embodiment 3 is detected, shows that its Rockwell hardness is 90.8HRA, fracture toughness is
12.7MPa·m-1/2, bending strength 2400MPa, dry type reciprocating friction wear results are shown, are 300r/min in revolving speed, are carried
Lotus is 50N, is opposite grinding 10min in the case where YG6 trade mark sintered carbide ball to abrading-ball, the coefficient of friction of obtained material is 0.60
~0.64, Wear track depth is 15~17 μm.Shown in its microstructure such as Fig. 2 (c), ternary boride is mutually present in white bright in figure
Part, the partial size of the generation phase is at 4-5 μm or so, but the distribution that the reaction generates mutually in the base is more dispersed, however, anti-
It answers in growth course, which does not grow up along the distribution mode of Binder Phase, this may be the MoB after stablizingxFor
Lamellar structure differs larger with the crystal structure of Binder Phase.
Comparative example 1
Ti (C, N) 52g, WC 16g, MoC 4g, TaC 8g, Co 11g, Ni 9g, carbon dust 1g, forming agent 4g are weighed respectively；
Wherein the partial size of each powder is respectively 2.28 μm of Ti (C, N), and 3.66 μm of WC, 2 μm of MoC, 3.4 μm of TaC, 7.5 μm of Co, Ni
8.9 μm, 11.4 μm of carbon dust.Sintered carbide ball is abrading-ball, ratio of grinding media to material 5:1, dehydrated alcohol 70mL, mixing time 48h；Mixing
Material afterwards 80 DEG C at a temperature of be dried in vacuo 5h, then dry uniformly mixed material is sieved with 100 mesh sieve；100MPa's
Compression moulding under pressure pressure maintaining 5 seconds, then carries out removing forming agent in vacuum environment at 550 DEG C, soaking time 3h,
Then 800 DEG C, 1100 DEG C, 1300 DEG C and 1430 DEG C are successively warming up to the heating rate of 10 DEG C/min, and often risen to wherein
Keep the temperature 1h when on one temperature spot, finally 1430 DEG C at a temperature of in furnace lead to inert gas argon gas to furnace in air pressure reach
6MPa, and heat-insulation pressure keeping 2h, then cool to room temperature with the furnace and obtain sintered sample A4.Gained sample A4 is dissolved by complicated carbonitride
The two object phase composition of body and Co-Ni solid solution, Rockwell hardness 90.2HRA, fracture toughness 12.7MPam-1/2, bending strength
For 2300MPa, dry type reciprocating friction wear results are shown, are 300r/min, load 50N in revolving speed, are the YG6 trade mark to abrading-ball
Opposite grinding 10min in the case where sintered carbide ball, the coefficient of friction of obtained material are 0.65~0.72, and Wear track depth is 52~56
μm.Shown in its microstructure such as Fig. 2 (d).
Comparative example 2
Other conditions are same as Example 1, are only WB be added2, FeB is replaced with, weighs Ti (C, N) 49g, WC respectively
16g, MoC 4g, TaC 8g, FeB 3g, Co 11g, Ni 9g, carbon dust 1g, forming agent 4g；Wherein the partial size of each powder is respectively
3.66 μm of 2.28 μm of Ti (C, N), WC, 2 μm of MoC, 3.4 μm of TaC, 0.5 μm of FeB, 7.5 μm of Co, 8.9 μm of Ni, carbon dust
11.4μm.Sintered carbide ball is abrading-ball, ratio of grinding media to material 5:1, dehydrated alcohol 70mL, non-ultrasonic disperse, mixing time 48h；It is mixed
Material after conjunction 80 DEG C at a temperature of be dried in vacuo 5h, then dry uniformly mixed material is sieved with 100 mesh sieve；In 100MPa
Pressure under compression moulding, pressure maintaining 5 seconds, removing forming agent is then carried out at 550 DEG C in vacuum environment, soaking time is
3h is then successively warming up to 600 DEG C, 800 DEG C, 1100 DEG C and 1430 DEG C with the heating rate of 10 DEG C/min, and is often rising to it
In on a temperature spot when keep the temperature 1h, finally 1430 DEG C at a temperature of lead to air pressure in inert gas argon gas to furnace in furnace and reach
6MPa, and heat-insulation pressure keeping 2h, then cool to room temperature with the furnace and obtain sintered sample A5.Gained sample A5 is dissolved by complicated carbonitride
Body and Co-Ni solid solution and the three kinds of object phase compositions of FeMoB ternary boride ceramic particle.
Cermet material in embodiment 1 is detected, shows that its Rockwell hardness is 90.7HRA, fracture toughness is
10.6MPa·m-1/2, bending strength 1470MPa.Its microstructure such as Fig. 2 (e).
Comparative example 3
Ti (C, N) 54g, WC 19g, MoC 2g, TaC 6g, WB are weighed respectively21g, Co 9g, Ni 9g, carbon dust 1g, at
Type agent 4g；Wherein the partial size of each powder is respectively 2.28 μm of Ti (C, N), and 3.66 μm of WC, 2 μm of MoC, 3.4 μm of TaC, WB2
0.5 μm, 7.5 μm of Co, 8.9 μm of Ni, 11.4 μm of carbon dust.By load weighted 1gWB2Powder is mixed with 20mL dehydrated alcohol, is placed in
In closed container, WB will be filled2It is placed in supersonic wave cleaning machine with the container of dehydrated alcohol mixed solution, by temperature measuring set
It is placed in the water of container exterior, opens supersonic wave cleaning machine, when temperature reaches 40 DEG C, take out container, replace cold water, place into
Container continues ultrasound, replaces cold water this operation when then repeated temperature reaches 40 DEG C, until total ultrasonic time reaches for 24 hours.Firmly
Matter alloying pellet is abrading-ball, and ratio of grinding media to material 5:1 adds dehydrated alcohol 50mL, then the WB that will complete dispersion2It is mixed with dehydrated alcohol
Solution is added in ball grinder together, mixing time 48h；Mixed material 80 DEG C at a temperature of be dried in vacuo 5h, then will
Dry uniformly mixed material sieves with 100 mesh sieve；The compression moulding under the pressure of 100MPa, pressure maintaining 5 seconds, then in vacuum environment
In removing forming agent is carried out at 550 DEG C, soaking time 3h is then successively warming up to 600 with the heating rate of 10 DEG C/min
DEG C, 800 DEG C, 1100 DEG C and 1430 DEG C, and 1h is kept the temperature when often rising on one of temperature spot, finally in 1430 DEG C of temperature
Air pressure reaches 6MPa, and heat-insulation pressure keeping 2h in lower inert gas argon gas to furnace logical in furnace, then cools to room temperature with the furnace and burnt
Tie sample A6.Gained sample A6 is by complicated carbonitride solid solution and Co-Ni solid solution and WCoB ternary boride ceramics
Three kinds of object phase compositions of grain,
Cermet material in comparative example 3 is detected, shows that its Rockwell hardness is 91.8HRA, fracture toughness is
9.7MPa·m-1/2, bending strength 1700MPa.
Comparative example 4
Ti (C, N) 49g, WC 16g, MoC 4g, TaC 8g, WB are weighed respectively23g, Co 11g, Ni 9g, carbon dust 1g, at
Type agent 4g；Wherein the partial size of each powder is respectively 2.28 μm of Ti (C, N), and 3.66 μm of WC, 2 μm of MoC, 3.4 μm of TaC, WB2
0.5 μm, 7.5 μm of Co, 8.9 μm of Ni, 11.4 μm of carbon dust.Sintered carbide ball is abrading-ball, ratio of grinding media to material 5:1, dehydrated alcohol 70mL,
Ultrasonic disperse, mixing time 48h are not carried out；Mixed material 80 DEG C at a temperature of be dried in vacuo 5h, then will be dry
Uniformly mixed material sieves with 100 mesh sieve；The compression moulding under the pressure of 100MPa, pressure maintaining 5 seconds, then in vacuum environment in
Carry out removing forming agent at 550 DEG C, soaking time 3h, then with the heating rate of 10 DEG C/min be successively warming up to 600 DEG C,
800 DEG C, 1100 DEG C and 1430 DEG C, and 1h is kept the temperature when often rising on one of temperature spot, finally 1430 DEG C at a temperature of
Lead to air pressure in inert gas argon gas to furnace in furnace and reach 6MPa, and heat-insulation pressure keeping 2h, then cools to room temperature with the furnace and be sintered
Sample A7.Gained sample A7 is by complicated carbonitride solid solution and Co-Ni solid solution and WCoB ternary boride ceramic particle
Three kinds of object phase compositions, shown in microstructure such as Fig. 2 (f), ternary boride is mutually present in the white bright part in figure, it can be seen that
The ternary boride that reaction generates is distributed with the distribution of the Binder Phase of material, more serious agglomeration occurs, this
Illustrate that the ternary boride generated has crystal structure similar with Binder Phase, can there is certain solid solubility, energy with Binder Phase
Enough grow up along the distribution arrangement of Binder Phase.
Comparative example 5
Ti (C, N) 51g, WC 16g, MoC 4g, TaC 8g, WB are weighed respectively21g, Co 11g, Ni 9g, carbon dust 1g, at
Type agent 4g；Wherein the partial size of each powder is respectively 2.28 μm of Ti (C, N), and 3.66 μm of WC, 2 μm of MoC, 3.4 μm of TaC, WB2
0.5 μm, 7.5 μm of Co, 8.9 μm of Ni, 11.4 μm of carbon dust.Load weighted 1gWB2 powder is mixed with 20mL dehydrated alcohol, is placed in
In closed container, the container for filling WB2 and dehydrated alcohol mixed solution is placed in supersonic wave cleaning machine, by temperature measuring set
It is placed in the water of container exterior, opens supersonic wave cleaning machine, when temperature reaches 40 DEG C, take out container, replace cold water, place into
Container continues ultrasound, replaces cold water this operation when then repeated temperature reaches 40 DEG C, until total ultrasonic time reaches for 24 hours.Firmly
Matter alloying pellet is abrading-ball, and ratio of grinding media to material 5:1 adds dehydrated alcohol 50mL, then the WB2 for completing dispersion and dehydrated alcohol are mixed
Solution is added in ball grinder together, mixing time 48h；Mixed material 80 DEG C at a temperature of be dried in vacuo 5h, then will
Dry uniformly mixed material sieves with 100 mesh sieve；The compression moulding under the pressure of 100MPa, pressure maintaining 5 seconds, then in vacuum environment
In removing forming agent is carried out at 550 DEG C, soaking time 3h is then successively warming up to 800 with the heating rate of 10 DEG C/min
DEG C, 1000 DEG C and 1150 DEG C, and 1h is kept the temperature when often rising on one of temperature spot, finally 1250 DEG C at a temperature of toward furnace
Air pressure reaches 6MPa, and heat-insulation pressure keeping 2h in interior logical inert gas argon gas to furnace, then cools to room temperature with the furnace and obtain sintered sample
A8.Gained sample A8 is by complicated carbonitride solid solution and Co-Ni solid solution and three kinds of WCoB ternary boride ceramic particle
Object phase composition, shown in microstructure such as Fig. 2 (g), ternary boride is mutually present in the white bright part in figure, illustrates anti-in situ
If answering the temperature range inside holding long period, reaction product is grown up obviously.
Claims (10)
1. a kind of ternary boride enhances Ti (C, N) base metal-ceramic material, it is characterised in that: Ti (C, N) the Base Metal pottery
Ceramic material is made of the ternary boride of hard phase, Binder Phase and even dispersion in Binder Phase and/or hard phase, described hard
Matter is mutually mutually made of with Ti (C, N) cermet addition, and the addition is mutually carbide and/or nitride；The ternary boronation
The partial size of object is 0.1~5 μm.
2. a kind of ternary boride according to claim 1 enhances Ti (C, N) base metal-ceramic material, it is characterised in that:
Ternary boride group of Ti (C, the N) base metal-ceramic material by hard phase, Binder Phase and even dispersion in Binder Phase
At the hard phase is mutually made of with Ti (C, N) cermet addition, and the addition is mutually carbide and/or nitride；It is described
The partial size of ternary boride is 1~2 μm.
3. a kind of ternary boride according to claim 1 enhances Ti (C, N) base metal-ceramic material, it is characterised in that:
The raw material components of the base titanium carbonitride material and the weight percent of each component are as follows: Ti (C, N) cermet is former
Expect 45~60wt%；Add 15~35wt% of phase raw material；Binder phase material 10~25%；Binary borides powder 0.05~
5wt%；
Ti (C, N) the cermet raw material is selected from titanium carbide powder and titanium nitride powder；Or it is selected from titanium carbonitride solid solution powder
End；
The addition is mutually selected from WC, Mo2C、TaC、NbC、HfC、W2C、VC、Cr3C2, in ZrC, AlN, NbN, TaN, ZrN powder
It is at least one；
The binder phase material is selected from cobalt powder and/nickel powder；
The binary borides powder is selected from WB2、Mo2B、MoB、CrB2At least one of.
4. preparing a kind of ternary boride as described in Claims 1 to 4 any one enhances Ti (C, N) base metal-ceramic material
Method, which comprises the steps of:
Match by design proportion and takes Ti (C, N) cermet raw material powder, addition phase raw material powder, binder phase material powder；Binary
Boride powder；Binary borides powder is first placed in ultrasonic disperse in ethanol solution, then will be scattered in dehydrated alcohol
In binary borides powder and other three classes raw material powders and reduction carbon dust, forming agent ball milling mixing, drying mixed
Powder；Mixed-powder is pressed into green compact, then green compact is placed in sintering furnace and removes forming agent in 400~580 DEG C of degreasings, so
Carry out vacuum pressure sintering again afterwards, sintering temperature is 1400~1600 DEG C, and final air pressure is 2~10MPa.
5. a kind of preparation method of ternary boride enhancing Ti (C, N) base metal-ceramic material according to claim 4,
Be characterized in that: the time of the ultrasonic disperse is 12~48h.
6. a kind of preparation method of ternary boride enhancing Ti (C, N) base metal-ceramic material according to claim 4,
Be characterized in that: the partial size of Ti (C, N) the cermet raw material powder is 2~10 μm, the partial size of the binder phase material powder
It is 5~15 μm, the partial size of the addition phase raw material powder is 1~15 μm, and the partial size of binary borides powder is 1~15 μm.
7. a kind of preparation method of ternary boride enhancing Ti (C, N) base metal-ceramic material according to claim 4,
Be characterized in that: the additional amount of the reduction carbon dust is 0.05~2wt% of raw material powder gross mass.
The forming agent is selected from one of polyethylene, rubber, stearic acid, paraffin, SBS, PVA, the additive amount of the forming agent
It is the 3~4.5% of raw material powder gross mass.
8. a kind of preparation method of ternary boride enhancing Ti (C, N) base metal-ceramic material according to claim 4,
Be characterized in that: the mode of the ball milling mixing is wet ball-milling, and the wet grinding media is dehydrated alcohol, rotational speed of ball-mill is 50~
200r/min；Ratio of grinding media to material is (2~10): 1, Ball-milling Time is 48~96h.
9. a kind of preparation method of ternary boride enhancing Ti (C, N) base metal-ceramic material according to claim 4,
Be characterized in that: described dry using vacuum drying, drying temperature is 60~90 DEG C, and drying time is 3~5h；
Described to be compressed to two-way compacting, used pressing pressure is 100~180MPa；
The degreasing is carrier gas degreasing, and gases used is nitrogen or argon gas.
10. a kind of preparation method of ternary boride enhancing Ti (C, N) base metal-ceramic material according to claim 4,
It is characterized by: vacuum pressure sintering process is to be sintered under vacuum environment first, the vacuum degree is 0.005~0.01Pa, is risen
Warm rate be 6-15 DEG C/min, respectively 550-600 DEG C, 750-850 DEG C, 1050-1130 DEG C at a temperature of keep the temperature 1~3h, most
After be warming up to 1430~1600 DEG C, keep the temperature 0.5~1h, being then re-filled with inert gas to air pressure is 2~10MPa, heat preservation 0.5~
5h cools to room temperature with the furnace.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201811570740.3A CN109576547B (en) | 2018-12-21 | 2018-12-21 | Ternary boride reinforced Ti (C, N) -based metal ceramic material and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201811570740.3A CN109576547B (en) | 2018-12-21 | 2018-12-21 | Ternary boride reinforced Ti (C, N) -based metal ceramic material and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN109576547A true CN109576547A (en) | 2019-04-05 |
| CN109576547B CN109576547B (en) | 2021-06-04 |
Family
ID=65930495
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201811570740.3A Active CN109576547B (en) | 2018-12-21 | 2018-12-21 | Ternary boride reinforced Ti (C, N) -based metal ceramic material and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN109576547B (en) |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110541102A (en) * | 2019-08-30 | 2019-12-06 | 广东技术师范大学 | coating gradient hard alloy cutter directly coated with CBN coating and preparation method thereof |
| CN111793761A (en) * | 2019-08-09 | 2020-10-20 | 中南大学 | Island-shaped structure hardened high-toughness titanium carbonitride base metal ceramic and preparation method thereof |
| CN111945050A (en) * | 2020-08-19 | 2020-11-17 | 燕山大学 | Composite material and preparation method thereof |
| CN112024890A (en) * | 2020-11-06 | 2020-12-04 | 宁波新宇硬质合金密封有限公司 | Hard alloy stop block and compression molding process |
| CN113462944A (en) * | 2021-06-30 | 2021-10-01 | 厦门理工学院 | Boron-doped (Ti, W, Mo, Nb, Ta) (C, N) -Co-Ni powder, cermet and preparation method |
| CN115369300A (en) * | 2021-09-01 | 2022-11-22 | 弗克森切削技术(苏州)有限公司 | Containing AlN and TiB 2 Ti (C, N) -based metal ceramic cutting tool material and preparation method thereof |
| CN115448740A (en) * | 2022-09-21 | 2022-12-09 | 湖南大学 | High-strength high-toughness high-entropy carbonitride ceramic and preparation method thereof |
Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60131867A (en) * | 1983-12-16 | 1985-07-13 | 東洋鋼鈑株式会社 | High abrasion resistance superhard material |
| JPH02232336A (en) * | 1989-03-07 | 1990-09-14 | Sumitomo Electric Ind Ltd | High-hardness sintered body for tool |
| CN1609052A (en) * | 2004-10-29 | 2005-04-27 | 华中科技大学 | Submicron grain Ti(C,N)-base cermet and its prepn process |
| CN101302595A (en) * | 2008-07-08 | 2008-11-12 | 湖南科技大学 | High-wear resistant Ti (C, N)-base ceramet tool bit and preparation thereof |
| CN101701311A (en) * | 2009-09-29 | 2010-05-05 | 武汉科技大学 | WCoB ternary boride cermet material and preparation method thereof |
| CN102191420A (en) * | 2011-05-26 | 2011-09-21 | 株洲钻石切削刀具股份有限公司 | Tungsten-free and cobalt-free Ti (C, N)-based metal ceramic and preparation method thereof |
| CN102191393A (en) * | 2010-03-18 | 2011-09-21 | 中国科学院上海硅酸盐研究所 | Preparation method of nickel molybdenum boron ternary boride base hard alloy |
| CN104630591A (en) * | 2015-01-29 | 2015-05-20 | 南京航空航天大学 | Stripe type ternary boride reinforced and toughened Ti(C, N)-based metal ceramic and preparation method thereof |
| CN104694807A (en) * | 2013-12-09 | 2015-06-10 | 青岛平度市旧店金矿 | Ternary boride metal ceramic preparation process |
| CN105734382A (en) * | 2016-01-29 | 2016-07-06 | 重庆文理学院 | Superfine metalloceramics material and preparation method thereof |
-
2018
- 2018-12-21 CN CN201811570740.3A patent/CN109576547B/en active Active
Patent Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60131867A (en) * | 1983-12-16 | 1985-07-13 | 東洋鋼鈑株式会社 | High abrasion resistance superhard material |
| JPH02232336A (en) * | 1989-03-07 | 1990-09-14 | Sumitomo Electric Ind Ltd | High-hardness sintered body for tool |
| CN1609052A (en) * | 2004-10-29 | 2005-04-27 | 华中科技大学 | Submicron grain Ti(C,N)-base cermet and its prepn process |
| CN101302595A (en) * | 2008-07-08 | 2008-11-12 | 湖南科技大学 | High-wear resistant Ti (C, N)-base ceramet tool bit and preparation thereof |
| CN101701311A (en) * | 2009-09-29 | 2010-05-05 | 武汉科技大学 | WCoB ternary boride cermet material and preparation method thereof |
| CN102191393A (en) * | 2010-03-18 | 2011-09-21 | 中国科学院上海硅酸盐研究所 | Preparation method of nickel molybdenum boron ternary boride base hard alloy |
| CN102191420A (en) * | 2011-05-26 | 2011-09-21 | 株洲钻石切削刀具股份有限公司 | Tungsten-free and cobalt-free Ti (C, N)-based metal ceramic and preparation method thereof |
| CN104694807A (en) * | 2013-12-09 | 2015-06-10 | 青岛平度市旧店金矿 | Ternary boride metal ceramic preparation process |
| CN104630591A (en) * | 2015-01-29 | 2015-05-20 | 南京航空航天大学 | Stripe type ternary boride reinforced and toughened Ti(C, N)-based metal ceramic and preparation method thereof |
| CN105734382A (en) * | 2016-01-29 | 2016-07-06 | 重庆文理学院 | Superfine metalloceramics material and preparation method thereof |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111793761A (en) * | 2019-08-09 | 2020-10-20 | 中南大学 | Island-shaped structure hardened high-toughness titanium carbonitride base metal ceramic and preparation method thereof |
| CN111793761B (en) * | 2019-08-09 | 2021-09-10 | 中南大学 | Island-shaped structure hardened high-toughness titanium carbonitride base metal ceramic and preparation method thereof |
| CN110541102A (en) * | 2019-08-30 | 2019-12-06 | 广东技术师范大学 | coating gradient hard alloy cutter directly coated with CBN coating and preparation method thereof |
| CN111945050A (en) * | 2020-08-19 | 2020-11-17 | 燕山大学 | Composite material and preparation method thereof |
| CN112024890A (en) * | 2020-11-06 | 2020-12-04 | 宁波新宇硬质合金密封有限公司 | Hard alloy stop block and compression molding process |
| CN113462944A (en) * | 2021-06-30 | 2021-10-01 | 厦门理工学院 | Boron-doped (Ti, W, Mo, Nb, Ta) (C, N) -Co-Ni powder, cermet and preparation method |
| CN115369300A (en) * | 2021-09-01 | 2022-11-22 | 弗克森切削技术(苏州)有限公司 | Containing AlN and TiB 2 Ti (C, N) -based metal ceramic cutting tool material and preparation method thereof |
| CN115369300B (en) * | 2021-09-01 | 2023-09-26 | 弗克森切削技术(苏州)有限公司 | AlN and TiB-containing material 2 Ti (C, N) -based cermet tool material and preparation method thereof |
| CN115448740A (en) * | 2022-09-21 | 2022-12-09 | 湖南大学 | High-strength high-toughness high-entropy carbonitride ceramic and preparation method thereof |
| CN115448740B (en) * | 2022-09-21 | 2023-11-21 | 湖南大学 | High-strength and high-entropy carbonitride ceramic and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN109576547B (en) | 2021-06-04 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109576547A (en) | A kind of ternary boride enhancing Ti(C, N) base metal-ceramic material and preparation method thereof | |
| Fang et al. | High-temperature oxidation resistance, mechanical and wear resistance properties of Ti (C, N)-based cermets with Al0. 3CoCrFeNi high-entropy alloy as a metal binder | |
| CN104862510B (en) | A kind of high-entropy alloy particle enhanced aluminum-based composite material and preparation method thereof | |
| US6214079B1 (en) | Triphasic composite and method for making same | |
| JPH06506502A (en) | Method for manufacturing cemented carbide articles | |
| US6090343A (en) | Triphasic composite and method for making same | |
| CN107739950A (en) | A kind of WC Co cBN composite hard alloys and preparation method thereof | |
| Peng et al. | Microstructures and mechanical properties of FeCoCrNi-Mo High entropy alloys prepared by spark plasma sintering and vacuum hot-pressed sintering | |
| CN1312078C (en) | Submicron grain Ti(C,N)-base cermet and its prepn process | |
| JP2006299396A (en) | Solid-solution powder and its producing method; ceramic using the solid-solution powder and its producing method; cermet powder including the solid-solution powder and its producing method; and cermet using the cermet powder and its producing method | |
| CN110396632A (en) | A kind of Ti (C, N) based ceramic metal and preparation method thereof with homogeneous ring core structure | |
| US20140178139A1 (en) | Method of manufacturing super hard alloy containing carbon nanotubes, super hard alloy manufactured using same, and cutting tool comprising super hard alloy | |
| CN101591194A (en) | A kind of composite material for superhard cutting tool | |
| CN110438384B (en) | Iron-nickel-based ultrafine-grained hard alloy and preparation method thereof | |
| CN113699406A (en) | High-strength and high-toughness extra-coarse-grain WC hard alloy with average grain size larger than 8 microns and preparation method thereof | |
| CN110029261A (en) | A kind of preparation method of Micro-Nano Hardmetal cutter material | |
| Ma et al. | Study on strengthening mechanism and high temperature mechanical properties of TiC-Fe-HEA cemented carbide | |
| Rosinski et al. | Properties of WCCO/diamond composites produced by PPS method intended for drill bits for machining of building stones | |
| CN106316398A (en) | Tungsten titanium carbide-based ceramic tool material added with cubic boron nitride and preparation method of material | |
| Yan et al. | Ti (C, N)-based cermets with two kinds of core-rim structures constructed by β-Co microspheres | |
| Viljus et al. | Structure formation in Ti-C-Ni-Mo composites during reactive sintering | |
| CN112846170B (en) | (Ti, W) C solid solution powder and preparation method thereof | |
| CN113528879B (en) | Polycrystalline diamond combined by compounds generated by in-situ reaction and preparation method thereof | |
| CN113319742B (en) | Preparation method of abrasive with grinding and polishing functions | |
| Zhang et al. | Effect of WС content on the mechanical properties and high temperature oxidation behavior of Ti (С, N)-based cermets |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |