CN105948761B - Shaft-like β-the Si such as a kind of3N4+ TiN+O '-Sialon diphase ceramic materials and preparation method thereof - Google Patents
Shaft-like β-the Si such as a kind of3N4+ TiN+O '-Sialon diphase ceramic materials and preparation method thereof Download PDFInfo
- Publication number
- CN105948761B CN105948761B CN201610279603.9A CN201610279603A CN105948761B CN 105948761 B CN105948761 B CN 105948761B CN 201610279603 A CN201610279603 A CN 201610279603A CN 105948761 B CN105948761 B CN 105948761B
- Authority
- CN
- China
- Prior art keywords
- sio
- tin
- sialon
- shaft
- tio
- 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.)
- Active
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
- C04B35/58—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides
- C04B35/584—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on silicon nitride
- C04B35/591—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on silicon nitride obtained by reaction sintering
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/64—Burning or sintering processes
- C04B35/65—Reaction sintering of free metal- or free silicon-containing compositions
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3217—Aluminum oxide or oxide forming salts thereof, e.g. bauxite, alpha-alumina
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3224—Rare earth oxide or oxide forming salts thereof, e.g. scandium oxide
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3224—Rare earth oxide or oxide forming salts thereof, e.g. scandium oxide
- C04B2235/3225—Yttrium oxide or oxide-forming salts thereof
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3224—Rare earth oxide or oxide forming salts thereof, e.g. scandium oxide
- C04B2235/3227—Lanthanum oxide or oxide-forming salts thereof
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3224—Rare earth oxide or oxide forming salts thereof, e.g. scandium oxide
- C04B2235/3229—Cerium oxides or oxide-forming salts thereof
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3231—Refractory metal oxides, their mixed metal oxides, or oxide-forming salts thereof
- C04B2235/3232—Titanium oxides or titanates, e.g. rutile or anatase
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/34—Non-metal oxides, non-metal mixed oxides, or salts thereof that form the non-metal oxides upon heating, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3418—Silicon oxide, silicic acids, or oxide forming salts thereof, e.g. silica sol, fused silica, silica fume, cristobalite, quartz or flint
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/42—Non metallic elements added as constituents or additives, e.g. sulfur, phosphor, selenium or tellurium
- C04B2235/428—Silicon
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/60—Aspects relating to the preparation, properties or mechanical treatment of green bodies or pre-forms
- C04B2235/602—Making the green bodies or pre-forms by moulding
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/65—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes
- C04B2235/656—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes characterised by specific heating conditions during heat treatment
- C04B2235/6562—Heating rate
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/65—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes
- C04B2235/656—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes characterised by specific heating conditions during heat treatment
- C04B2235/6567—Treatment time
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/65—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes
- C04B2235/658—Atmosphere during thermal treatment
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/74—Physical characteristics
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/74—Physical characteristics
- C04B2235/77—Density
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/74—Physical characteristics
- C04B2235/78—Grain sizes and shapes, product microstructures, e.g. acicular grains, equiaxed grains, platelet-structures
- C04B2235/786—Micrometer sized grains, i.e. from 1 to 100 micron
Abstract
The invention discloses the shaft-like β Si such as a kind of3N4+ TiN+O'Sialon diphase ceramic materials and preparation method thereof are to introduce TiO2Colloidal sol introduces Re as Si powder nitrided catalysts, in-situ preparation nano TiN reinforced phase2O3‑Al2O3‑SiO2Sintering aid promotes Si3N4Sintering densification, the shaft-like β Si such as formation3N4Crystal grain, and generate O'Sialon.The β Si of the present invention3N4+ TiN+O'Sialon diphase ceramic materials have excellent mechanical property, high-temperature behavior, anti-oxidant and corrosion resistance.
Description
Technical field
The present invention relates to ceramic material field, more particularly to a kind of etc. shaft-like β-Si3N4+ TiN+O'-Sialon complex phase ceramics
Material and preparation method thereof.
Background technology
Si3N4Powder there are two types of crystal form, etc. shaft-like α-Si3N4With the β-Si of long column shape3N4Crystal form.Have been generally acknowledged that α-Si3N4Belong to
Low-temperature stabilization crystal form, β-Si3N4Belong to high-temperature stable crystal form.α-Si3N4To β-Si3N4Phase transformation category structural remodeling, about 1420
It DEG C undergoes phase transition.Due to β-Si3N4The through-hole structure of distinctive ABAB accumulations, this β phases have long column shape or acicular crystal shape
Looks.Lange etc. (J.Am.Ceram.Soc., 62,1979,428-430) is put forward for the first time long column shape β-Si3N4Crystal grain is in tiny crystalline substance
Grain α-Si3N4The bending strength and fracture toughness of material can be improved by being precipitated in matrix.β Phase Proportions are higher, and fracture toughness is better,
But intensity has maximum value, the β-Si of high length-diameter ratio3N4The presence of crystal grain can improve intensity and toughness, but β-Si3N4Grain aspect
Than being greatly different growth very much, it is unfavorable for material mechanical performance raising.
Invention content
It is an object of the invention to overcome disadvantage existing in the prior art, provide a kind of intensity is high, abrasion resistance properties are good,
High temperature resistant and antioxygenic property it is good etc. shaft-like β-Si3N4+ TiN+O'-Sialon diphase ceramic materials.
Another object of the present invention is to provide the shaft-like β-Si such as above-mentioned3N4+ TiN+O'-Sialon diphase ceramic materials
Preparation method.
The purpose of the invention is achieved by the following technical solution:
Shaft-like β-the Si such as a kind of3N4The preparation method of+TiN+O'-Sialon diphase ceramic materials is to introduce TiO2Colloidal sol is made
For Si powder nitrided catalysts, in-situ preparation nano TiN reinforced phase introduces Re2O3-Al2O3-SiO2Sintering aid promotes Si3N4It burns
Knot densification, the shaft-like β-Si such as formation3N4Crystal grain, and O'-Sialon is generated, specifically include following step:
(1) using Si powder as raw material, with TiO2Colloidal sol, Re2O3-Al2O3-SiO2For sintering aid, according to Si:TiO2:
Re2O3-Al2O3-SiO2Mass fraction ratio is 60~98%:1~10%:1~30% proportioning obtains after batch mixing, drying
Si-TiO2-Re2O3-Al2O3-SiO2Mixed powder, wherein Re be Sc, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy,
Any one of Ho, Er, Tm, Yb or Lu, the Re2O3-Al2O3-SiO2In Re2O3:Al2O3:SiO2Mass fraction ratio is 1
~98%:1~98%:1~98%;
(2) by Si-TiO2-Re2O3-Al2O3-SiO2Mixed powder be put into mold carry out it is dry-pressing formed after, by cold etc.
Hydrostatic profile obtains Si-TiO2-Re2O3-Al2O3-SiO2Green body;
(3) by Si-TiO2-Re2O3-Al2O3-SiO2Green body passes through the shaft-like β-Si such as gas pressure sintered reaction preparation3N4+TiN+
O'-Sialon diphase ceramic materials.
In step (1), by Si powder, TiO2Colloidal sol and Re2O3-Al2O3-SiO2By the mass fraction than carrying out dispensing, with
Ethyl alcohol is solvent, with Si3N4Ball is ball-milling medium, and 4~20h is mixed on ball mill, Si-TiO is obtained after dry2-Re2O3-
Al2O3-SiO2Mixed powder.
In step (1), ball mill is planetary ball mill, and 10h is mixed on planetary ball mill.
In step (1), Si:TiO2:Re2O3-Al2O3-SiO2Mass fraction than preferably 74.5%:4%:21.5%,
Wherein Re=Y;The Re2O3-Al2O3-SiO2In Re2O3:Al2O3:SiO2Mass fraction ratio be 35%:35%:30%.
In step (2), 100~300MPa of pressure of cold isostatic compaction, the dwell time is 1~10min.
In step (2), the pressure preferred 200MPa, dwell time 5min of cold isostatic compaction.
In step (3), gas pressure sintered reaction is:By Si-TiO2-Re2O3-Al2O3-SiO2Green body is put into boron nitride crucible,
Temperature is risen to 1000~1250 DEG C with the heating rate of 20 DEG C/min, then is risen to temperature with the heating rate of 10 DEG C/min
1300~1600 DEG C, and 1~4h is kept the temperature, insulating process nitrogen pressure is 0.1~5MPa, then with the heating rate of 5 DEG C/min
Temperature is risen to 1600~2000 DEG C, and keeps the temperature 1~4h, insulating process nitrogen pressure is 0.1~5MPa, is reacted by air pressure
Shaft-like β-the Si such as sintering acquisition3N4+ TiN+O'-Sialon diphase ceramic materials.
In step (3), gas pressure sintered reaction is preferably:By Si-TiO2-Re2O3-Al2O3-SiO2Green body is put into boron nitride earthenware
Temperature is raised to 1200 DEG C with the heating rate of 20 DEG C/min, then temperature is raised to 1400 with the heating rate of 10 DEG C/min by crucible
DEG C, and 2h is kept the temperature, insulating process nitrogen pressure is 0.5MPa, and temperature is then raised to 1850 DEG C with the heating rate of 5 DEG C/min,
And 1h is kept the temperature, insulating process nitrogen pressure is 3.0MPa, passes through the shaft-like β-Si such as gas pressure sintered reaction acquisition3N4+TiN+O'-
Sialon diphase ceramic materials.
Using the above method be prepared etc. shaft-like β-Si3N4+ TiN+O'-Sialon diphase ceramic materials, it is relatively close
Degree is higher than 95%, and hardness is 10~22GPa, and fracture toughness is 3~8MPam1/2, bending strength is 600~1200MPa, TiN
Grain size is 100~1000nm, β-Si3N4The average diameter of crystal grain is 1.33~2.58um.
Preferably, the present invention be prepared etc. shaft-like β-Si3N4+ TiN+O'-Sialon diphase ceramic materials are opposite
Density is 99%, hardness 14GPa, fracture toughness 4.5MPam1/2, bending strength 1000MPa, TiN grain size is
500nm, β-Si3N4The average diameter of crystal grain is 1.90 ± 0.51um.
In the present invention, TiO2Colloidal sol at high temperature with Si3N4Reaction generates TiN reinforced phases, as shown in reaction equation (1);
Part SiO in sample2With Re2O3、Al2O3Reaction forms glass phase, improves densification, extra SiO2With Si3N4、Al2O3Occur
Solid solution reaction forms O'-Sialon phases, as shown in reaction equation (2):
6TiO2(s)+2Si3N4(s)→6TiN(s)+6SiO2(s or l)+N2(g) (1)
0.49Si3N4(s)+0.49SiO2(s)+0.02Al2O3(s)→Si1.96Al0.04O1.04N1.96(s) (2)
The present invention has the following advantages that compared with prior art and effect:
(1) present invention prepare etc. shaft-like β-Si3N4+ TiN+O'-Sialon diphase ceramic materials, be with etc. shaft-like β-
Si3N4For main phase, using TiN+O'-Sialon as the phase constitution structure of reinforced phase, which has more preferable, closer
Crystal structure.
(2) present invention introduces TiO2Colloidal sol is as Si powder nitrided catalyst and in-situ preparation nano TiN reinforced phase, further
The intensity and abrasion resistance properties of ceramic material are improved, Al is introduced2O3-Re2O3-SiO2Sintering aid promotes Si3N4Sintering densification,
Shaft-like β-the Si such as formation3N4Crystal grain, and in-situ preparation O'-Sialon further increase the high-temperature behavior of ceramic material and anti-oxidant
Performance.
(3) the TiN grain sizes that material in situ of the present invention generates are 100~1000nm, have superior mechanical property, high temperature
Performance, anti-oxidant and corrosion resistance.
Description of the drawings
Fig. 1 be the present invention prepare etc. shaft-like β-Si3N4The XRD of+TiN+O'-Sialon diphase ceramic materials schemes.
Fig. 2 be the present invention prepare etc. shaft-like β-Si3N4The SEM of+TiN+O'-Sialon diphase ceramic materials schemes.
Specific implementation mode
Further detailed description is done to the present invention with reference to embodiment, embodiments of the present invention are not limited thereto.
Be the existing conventional method of the art if experimental methods are without specified otherwise used in following, used dispensing or
Material is unless otherwise specified by the available dispensing of commercial sources or material.
Embodiment 1
(1) using Si powder as raw material, with TiO2Colloidal sol, Y2O3-Al2O3-SiO2For sintering aid, gross mass is accounted for according to Si powder
Mass fraction be 74.5%, TiO2Mass fraction is 4%, Y2O3-Al2O3-SiO2Mass fraction is 21.5% progress dispensing,
Middle Y2O3:Al2O3:SiO2Mass fraction ratio is 35%:35%:30%, using ethyl alcohol as solvent, with Si3N4Ball is ball-milling medium,
10h is mixed on planetary ball mill, and Si-TiO is obtained after dry2-Y2O3-Al2O3-SiO2Mixed powder.
(2) by Si-TiO2-Y2O3-Al2O3-SiO2Mixed powder is put into mold cold etc. quiet by carrying out after dry-pressing formed
Pressure obtains Si-TiO2-Y2O3-Al2O3-SiO2Green body, cold isostatic compaction pressure 200MPa, dwell time 5min.
(3) by Si-TiO2-Y2O3-Al2O3-SiO2Green body is put into boron nitride crucible, will be warm with the heating rate of 20 DEG C/min
Degree is raised to 1200 DEG C, then temperature is raised to 1400 DEG C with the heating rate of 10 DEG C/min, and keeps the temperature 2h, insulating process nitrogen pressure
Power is 0.5MPa, temperature is then raised to 1850 DEG C with the heating rate of 5 DEG C/min, and keep the temperature 1h, insulating process nitrogen pressure
For 3.0MPa, pass through the shaft-like β-Si such as gas pressure sintered reaction acquisition3N4+ TiN+O'-Sialon diphase ceramic materials.
The relative density of ceramic material manufactured in the present embodiment is 99%, hardness 14GPa, and fracture toughness is
4.5MPa·m1/2, bending strength 1000MPa, TiN grain size position 500nm, β-Si3N4The average diameter of crystal grain be 1.90 ±
0.51um。
Fig. 1 be etc. shaft-like β-Si3N4The XRD spectrum of+TiN+O'-Sialon diphase ceramic materials.From Fig. 1 as can be seen that
For sample after gas pressure sintered reaction, Si powder is completely converted into β-Si3N。
Fig. 2 be etc. shaft-like β-Si3N4The SEM of+TiN+O'-Sialon diphase ceramic materials schemes.Figure it is seen that β-
Si3N4Crystal grain is the shaft-like crystal grain such as uniform, and average diameter is 1.90 ± 0.51um.
Embodiment 2
It is 71%, TiO according to Si mass fractions2Mass fraction is 4%, Y2O3-Al2O3-SiO2Mass fraction be 25% into
Row dispensing, wherein Y2O3:Al2O3:SiO2Mass fraction ratio is 30%:30%:40%, prepare Si- according to 1 method of embodiment
TiO2-Y2O3-Al2O3-SiO2Then temperature is raised to 1200 DEG C by green body with the heating rate of 20 DEG C/min, then with 10 DEG C/min
Heating rate temperature is raised to 1400 DEG C, and keep the temperature 2h, insulating process nitrogen pressure is 0.5MPa, then with 5 DEG C/min's
Temperature is raised to 1700 DEG C by heating rate, keeps the temperature 1h, and insulating process nitrogen pressure is 3.0MPa, is obtained by gas pressure sintered reaction
Etc. shaft-like β-Si3N4+ TiN+O'-Sialon diphase ceramic materials.
The relative density of ceramic material manufactured in the present embodiment is 99%, hardness 13.5GPa, fracture toughness 4MPa
m1/2, bending strength 950MPa, TiN grain size is 450nm, β-Si3N4The average diameter of crystal grain is 1.46 ± 0.26um.
Embodiment 3
It is 81%, TiO according to Si mass fractions2Mass fraction is 4%, Y2O3-Al2O3-SiO2Mass fraction be 15% into
Row dispensing, wherein Y2O3:Al2O3:SiO2Mass fraction ratio is 33.3%:33.3%:33.3%, it is prepared according to 1 method of embodiment
Si-TiO2-Y2O3-Al2O3-SiO2Then temperature is raised to 1200 DEG C, then with 10 by green body with the heating rate of 20 DEG C/min
DEG C/temperature is raised to 1400 DEG C, and keeps the temperature 2h by the heating rate of min, insulating process nitrogen pressure is 0.5MPa, then with 5 DEG C/
Temperature is raised to 1750 DEG C by the heating rate of min, and keeps the temperature 1h, and insulating process nitrogen pressure is 3.0MPa, is reacted by air pressure
Shaft-like β-the Si such as sintering acquisition3N4+ TiN+O'-Sialon diphase ceramic materials.
The relative density of ceramic material manufactured in the present embodiment is 99%, hardness 14GPa, and fracture toughness is
3.5MPa·m1/2, bending strength 850MPa, TiN grain size is 500nm, β-Si3N4The average diameter of crystal grain be 1.53 ±
0.32um。
Embodiment 4
It is 77.5%, TiO according to Si powder mass fractions2Mass fraction is 4%, Y2O3-Al2O3-SiO2Mass fraction is
18.5% carries out dispensing, wherein Y2O3:Al2O3:SiO2Mass fraction ratio is 27%:27%:46%, according to 1 method system of embodiment
Standby Si-TiO2-Y2O3-Al2O3-SiO2Then temperature is raised to 1200 DEG C by green body with the heating rate of 20 DEG C/min, then with
Temperature is raised to 1400 DEG C by the heating rate of 10 DEG C/min, and keeps the temperature 2h, and insulating process nitrogen pressure is 0.5MPa, then with 5
DEG C/temperature is raised to 1800 DEG C, and keeps the temperature 1h by the heating rate of min, insulating process nitrogen pressure is 3.0MPa, anti-by air pressure
Shaft-like β-the Si such as acquisition should be sintered3N4+ TiN+O'-Sialon diphase ceramic materials.
The relative density of ceramic material manufactured in the present embodiment is 98.5%, hardness 14.5GPa, and fracture toughness is
4MPa·m1/2, bending strength 950MPa, TiN grain size is 550nm, β-Si3N4The average diameter of crystal grain is 1.73 ± 0.45um.
Claims (8)
1. the shaft-like β-Si such as a kind of3N4The preparation method of+TiN+O'-Sialon diphase ceramic materials, it is characterised in that including following
Step:
(1) using Si powder as raw material, with TiO2Colloidal sol, Re2O3-Al2O3-SiO2For sintering aid, according to Si:TiO2:Re2O3-
Al2O3-SiO2Mass fraction ratio is 60~98%:1~10%:1~30% proportioning obtains Si- after batch mixing, drying
TiO2-Re2O3-Al2O3-SiO2Mixed powder, wherein Re be Sc, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er,
Any one of Tm, Yb or Lu, the Re2O3-Al2O3-SiO2In Re2O3:Al2O3:SiO2Mass fraction ratio is 1~98%:
1~98%:1~98%;
(2) by Si-TiO2-Re2O3-Al2O3-SiO2Mixed powder be put into mold carry out it is dry-pressing formed after, pass through isostatic cool pressing
Molding obtains Si-TiO2-Re2O3-Al2O3-SiO2Green body;
(3) by Si-TiO2-Re2O3-Al2O3-SiO2Green body passes through the shaft-like β-Si such as gas pressure sintered reaction preparation3N4+TiN+O'-
Sialon diphase ceramic materials;The gas pressure sintered reaction is:By Si-TiO2-Re2O3-Al2O3-SiO2Green body is put into boron nitride
Temperature is risen to 1000~1250 DEG C by crucible with the heating rate of 20 DEG C/min, then with the heating rate of 10 DEG C/min by temperature
1300~1600 DEG C are risen to, and keeps the temperature 1~4h, insulating process nitrogen pressure is 0.1~5MPa, then with the heating of 5 DEG C/min
Temperature is risen to 1600~2000 DEG C by rate, and keeps the temperature 1~4h, and insulating process nitrogen pressure is 0.1~5MPa, anti-by air pressure
Shaft-like β-the Si such as acquisition should be sintered3N4+ TiN+O'-Sialon diphase ceramic materials.
2. the shaft-like β-Si such as according to claim 13N4The preparation method of+TiN+O'-Sialon diphase ceramic materials,
It is characterized in that:In step (1), by Si powder, TiO2Colloidal sol and Re2O3-Al2O3-SiO2By the mass fraction than carrying out dispensing, with
Ethyl alcohol is solvent, with Si3N4Ball is ball-milling medium, and 4~20h is mixed on ball mill, Si-TiO is obtained after dry2-Re2O3-
Al2O3-SiO2Mixed powder.
3. the shaft-like β-Si such as according to claim 23N4The preparation method of+TiN+O'-Sialon diphase ceramic materials,
It is characterized in that:In step (1), ball mill is planetary ball mill, and 10h is mixed on planetary ball mill.
4. the shaft-like β-Si such as according to claim 13N4The preparation method of+TiN+O'-Sialon diphase ceramic materials,
It is characterized in that:In step (1), Si:TiO2:Re2O3-Al2O3-SiO2Mass fraction ratio be 74.5%:4%:21.5%, wherein
Re is Y;The Re2O3-Al2O3-SiO2In Re2O3:Al2O3:SiO2Mass fraction ratio be 35%:35%:30%.
5. the shaft-like β-Si such as according to claim 13N4The preparation method of+TiN+O'-Sialon diphase ceramic materials,
It is characterized in that:In step (2), 100~300MPa of pressure of cold isostatic compaction, the dwell time is 1~10min.
6. the shaft-like β-Si such as according to claim 13N4The preparation method of+TiN+O'-Sialon diphase ceramic materials,
It is characterized in that:In step (3), gas pressure sintered reaction is:By Si-TiO2-Re2O3-Al2O3-SiO2Green body is put into boron nitride crucible,
Temperature is raised to 1200 DEG C with the heating rate of 20 DEG C/min, then temperature is raised to 1400 DEG C with the heating rate of 10 DEG C/min,
And 2h is kept the temperature, insulating process nitrogen pressure is 0.5MPa, and temperature is then raised to 1850 DEG C with the heating rate of 5 DEG C/min, and
1h is kept the temperature, insulating process nitrogen pressure is 3.0MPa, passes through the shaft-like β-Si such as gas pressure sintered reaction acquisition3N4+TiN+O'-
Sialon diphase ceramic materials.
7. it is a kind of using any one of claim 1~6 the method be prepared etc. shaft-like β-Si3N4+TiN+O'-Sialon
Diphase ceramic material, it is characterised in that:Relative density is higher than 95%, and hardness is 10~22GPa, and fracture toughness is 3~8MPa
m1/2, bending strength is 600~1200MPa, and TiN grain sizes are 100~1000nm, β-Si3N4The average diameter of crystal grain be 1.33~
2.58μ m 。
8. the shaft-like β-Si such as according to claim 73N4+ TiN+O'-Sialon diphase ceramic materials, it is characterised in that:Phase
It is 99% to density, hardness 14GPa, fracture toughness 4.5MPam1/2, bending strength 1000MPa, TiN grain size is
500nm, β-Si3N4The average diameter of crystal grain is 1.90 ± 0.51 μm.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN201610279603.9A CN105948761B (en) | 2016-04-29 | 2016-04-29 | Shaft-like β-the Si such as a kind of3N4+ TiN+O '-Sialon diphase ceramic materials and preparation method thereof |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN201610279603.9A CN105948761B (en) | 2016-04-29 | 2016-04-29 | Shaft-like β-the Si such as a kind of3N4+ TiN+O '-Sialon diphase ceramic materials and preparation method thereof |
Publications (2)
Publication Number | Publication Date |
---|---|
CN105948761A CN105948761A (en) | 2016-09-21 |
CN105948761B true CN105948761B (en) | 2018-09-07 |
Family
ID=56916489
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
CN201610279603.9A Active CN105948761B (en) | 2016-04-29 | 2016-04-29 | Shaft-like β-the Si such as a kind of3N4+ TiN+O '-Sialon diphase ceramic materials and preparation method thereof |
Country Status (1)
Country | Link |
---|---|
CN (1) | CN105948761B (en) |
Families Citing this family (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN108863396B (en) * | 2018-06-14 | 2021-04-06 | 广东工业大学 | Silicon nitride-based continuous functional gradient ceramic ball and preparation method and application thereof |
CN113929471A (en) * | 2021-11-08 | 2022-01-14 | 西安交通大学 | High-temperature-resistant oxidized Si3N4O' -sialon composite ceramic and preparation method thereof |
CN115611636B (en) * | 2022-09-30 | 2023-07-28 | 广东工业大学 | Surface modified cubic boron nitride powder and preparation method and application thereof |
CN116693303A (en) * | 2023-03-31 | 2023-09-05 | 江苏东浦精细陶瓷科技股份有限公司 | TiN-Si 3 N 4 Near net shape forming method for composite material |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103833370A (en) * | 2014-01-08 | 2014-06-04 | 西北工业大学 | Near shape preparation method of multiphase ceramic Si3N4-SiC |
CN104926317A (en) * | 2015-06-01 | 2015-09-23 | 广东工业大学 | High-toughness Si3N4 ceramic preparation method |
CN105254307A (en) * | 2015-10-21 | 2016-01-20 | 广东工业大学 | Method for preparing Si3N4- O'-Sialon-TiN ceramic ball material |
-
2016
- 2016-04-29 CN CN201610279603.9A patent/CN105948761B/en active Active
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103833370A (en) * | 2014-01-08 | 2014-06-04 | 西北工业大学 | Near shape preparation method of multiphase ceramic Si3N4-SiC |
CN104926317A (en) * | 2015-06-01 | 2015-09-23 | 广东工业大学 | High-toughness Si3N4 ceramic preparation method |
CN105254307A (en) * | 2015-10-21 | 2016-01-20 | 广东工业大学 | Method for preparing Si3N4- O'-Sialon-TiN ceramic ball material |
Also Published As
Publication number | Publication date |
---|---|
CN105948761A (en) | 2016-09-21 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
CN105948761B (en) | Shaft-like β-the Si such as a kind of3N4+ TiN+O '-Sialon diphase ceramic materials and preparation method thereof | |
Suehiro et al. | Powder synthesis of Ca-α ‘-SiAlON as a host material for phosphors | |
CN104909765B (en) | A kind of low cost, quick preparation high-performance Si3N4The method of Ceramic Balls | |
CN109206141A (en) | A kind of high hard high-ductility silicon nitride ceramics and its preparation method and application | |
KR20170061755A (en) | Alumina complex ceramics composition and manufacturing method thereof | |
JP5836522B2 (en) | Method for manufacturing silicon nitride substrate | |
Suehiro et al. | Powder synthesis of Y-α-SiAlON and its potential as a phosphor host | |
CN103130508A (en) | Method for preparing texturing boride super-high-temperature ceramic | |
Al Malki et al. | Effect of Al metal precursor on the phase formation and mechanical properties of fine-grained SiAlON ceramics prepared by spark plasma sintering | |
CN104926317A (en) | High-toughness Si3N4 ceramic preparation method | |
CN110218096A (en) | A kind of high hard high abrasion silicon nitride ceramics and its preparation method and application | |
Nekouee et al. | Sintering behavior and mechanical properties of spark plasma sintered β–SiAlON/TiN nanocomposites | |
JP5046221B2 (en) | Manufacturing method of highly reliable silicon nitride ceramics with high reliability | |
CN110156476A (en) | A kind of high hard high-ductility silicon-nitride-based ceramic and its preparation method and application | |
CN105254307B (en) | One kind prepares Si3N4The method of O ' Sialon TiN ceramics ball materials | |
CN101734920B (en) | Titanium nitride porous ceramics and preparation method thereof | |
CN107651964A (en) | A kind of AlN base composite ceramics and preparation method thereof | |
CN109942310A (en) | A kind of preparation method of high-performance porous SiN ceramic | |
Sun et al. | Effect of LiYO2 on the synthesis and pressureless sintering of Y2SiO5 | |
Zabelina et al. | SiC composites containing carbon nanotubes and oxide additives based on organoelementoxanes. Preparation by spark plasma sintering | |
CN108863395A (en) | A kind of high heat conductance, high strength silicon nitride ceramic material and preparation method thereof | |
CN109970454A (en) | A kind of transition metal oxide inhibit silicon nitride phase transformation method and its silicon nitride ceramics obtained | |
CN104609864B (en) | A kind of method utilizing ferro-silicon nitride powder to prepare block body ceramic material | |
Tatli et al. | Low temperature densification of silicon nitride using Li2O-based surface coatings | |
CN109400176A (en) | A kind of high-performance silicon nitride ceramics and its preparation method and application |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
C06 | Publication | ||
PB01 | Publication | ||
C10 | Entry into substantive examination | ||
SE01 | Entry into force of request for substantive examination | ||
GR01 | Patent grant | ||
GR01 | Patent grant | ||
TR01 | Transfer of patent right |
Effective date of registration: 20210922 Address after: 130000 building F2, phase 2-1, Beihu science and Technology Industrial Park, Beihu science and Technology Development Zone, Changchun City, Jilin Province Patentee after: JILIN CHANGYU TETAO NEW MATERIAL TECHNOLOGY Co.,Ltd. Address before: 510062 Dongfeng East Road, Yuexiu District, Guangzhou, Guangdong 729 Patentee before: GUANGDONG University OF TECHNOLOGY |
|
TR01 | Transfer of patent right |