WO2012153645A1 - PROCÉDÉ DE FABRICATION D'UNE CÉRAMIQUE EN SOLUTION SOLIDE À BASE DE ZrO2-Al2O3,À RÉSISTANCE ÉLEVÉE, À TÉNACITÉ ÉLEVÉE - Google Patents
PROCÉDÉ DE FABRICATION D'UNE CÉRAMIQUE EN SOLUTION SOLIDE À BASE DE ZrO2-Al2O3,À RÉSISTANCE ÉLEVÉE, À TÉNACITÉ ÉLEVÉE Download PDFInfo
- Publication number
- WO2012153645A1 WO2012153645A1 PCT/JP2012/061196 JP2012061196W WO2012153645A1 WO 2012153645 A1 WO2012153645 A1 WO 2012153645A1 JP 2012061196 W JP2012061196 W JP 2012061196W WO 2012153645 A1 WO2012153645 A1 WO 2012153645A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- solid solution
- zro
- sintering
- mol
- temperature
- Prior art date
Links
Images
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
- C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
- C04B35/48—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on zirconium or hafnium oxides, zirconates, zircon or hafnates
- C04B35/486—Fine ceramics
- C04B35/488—Composites
- C04B35/4885—Composites with aluminium 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
- 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
- C04B35/624—Sol-gel processing
-
- 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
- C04B35/626—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B
- C04B35/62605—Treating the starting powders individually or as mixtures
- C04B35/62645—Thermal treatment of powders or mixtures thereof other than sintering
- C04B35/62675—Thermal treatment of powders or mixtures thereof other than sintering characterised by the treatment temperature
-
- 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
- C04B35/645—Pressure 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
- 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
- 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
- C04B2235/3231—Refractory metal oxides, their mixed metal oxides, or oxide-forming salts thereof
- C04B2235/3244—Zirconium oxides, zirconates, hafnium oxides, hafnates, or oxide-forming salts thereof
- C04B2235/3246—Stabilised zirconias, e.g. YSZ or cerium stabilised zirconia
-
- 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
- C04B2235/50—Constituents or additives of the starting mixture chosen for their shape or used because of their shape or their physical appearance
- C04B2235/54—Particle size related information
- C04B2235/5418—Particle size related information expressed by the size of the particles or aggregates thereof
- C04B2235/5445—Particle size related information expressed by the size of the particles or aggregates thereof submicron sized, i.e. from 0,1 to 1 micron
-
- 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
- C04B2235/604—Pressing at temperatures other than sintering temperatures
-
- 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
- C04B2235/66—Specific sintering techniques, e.g. centrifugal sintering
- C04B2235/665—Local sintering, e.g. laser 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
- 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
- C04B2235/66—Specific sintering techniques, e.g. centrifugal sintering
- C04B2235/666—Applying a current during sintering, e.g. plasma sintering [SPS], electrical resistance heating or pulse electric current sintering [PECS]
-
- 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
- C04B2235/76—Crystal structural characteristics, e.g. symmetry
-
- 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
- C04B2235/76—Crystal structural characteristics, e.g. symmetry
- C04B2235/765—Tetragonal symmetry
-
- 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
- C04B2235/785—Submicron sized grains, i.e. from 0,1 to 1 micron
-
- 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
- C04B2235/96—Properties of ceramic products, e.g. mechanical properties such as strength, toughness, wear resistance
Definitions
- the present invention relates to a method for making high strength toughness ZrO 2 -Al 2 O 3 based solid solution ceramics.
- Non-Patent Document 1 ZrO 2 -25 mol% Al 2 O 3 solid solution powder was prepared, solid solution ceramics of this system were prepared by HIP sintering, and the ceramic with a fracture toughness value K IC of 23 MPa ⁇ m 1/2 is an astonishing value. reported.
- the bending strength ( ⁇ b ) remains at about 570 MPa, and it does not reach practical use where ⁇ b is 1 GPa or more, and simultaneously satisfies high strength ( ⁇ 1 GPa) and toughness ( ⁇ 15 MPa ⁇ m 1/2 ).
- ⁇ b the bending strength
- the present invention solves the above-mentioned problems in the prior art, and a high-strength toughness ZrO 2 -Al 2 O 3 system that simultaneously satisfies high strength ( ⁇ 1 GPa) and toughness ( ⁇ 15 MPa ⁇ m 1/2 ). It is an object of the present invention to provide a method capable of producing solid solution ceramics. As a result of various studies, the present inventors have found that ZrO 2 (98.5 mol% ZrO 2 -1.5 mol% Y) in which 1.5 mol% Y 2 O 3 is added to ZrO 2 using a sol-gel method.
- ZrO 2 (1.5Y) -25 mol% Al 2 O 3 solid solution powder was prepared, and this solid solution was prepared.
- a high strength toughness ZrO that satisfies the above-mentioned strength (bending strength) and fracture toughness values when the powder is calcined at a temperature higher than the crystallization temperature and then sintered under a certain condition.
- the present inventors have found that 2- Al 2 O 3 based solid solution ceramics can be produced and studied the optimum range of the amount of Y 2 O 3 added, thereby completing the present invention.
- the method for producing the high-strength toughness ZrO 2 -Al 2 O 3 solid solution ceramics of the present invention capable of solving the above-mentioned problems is the following steps A and B: Step A: Sol - to ZrO 2 using a gel method 0.3 ⁇ 1.7mol% Y 2 O 3 ZrO 2 was added (99.7 ⁇ 98.3mol% ZrO 2 -0.3 ⁇ 1.7mol % Y 2 O 3 ) -20-30 mol% Al 2 O 3 amorphous solid solution powder, and the resulting solid solution powder is calcined at a temperature equal to or higher than the crystallization temperature to obtain crystalline ZrO 2 solid solution powder.
- step B forming the crystalline ZrO 2 solid solution powder obtained in the step A, and then heating in an inert gas atmosphere at a heating rate of 50 ° C./min or more and a pressure of 30 to 100 MPa. And a sintering step at a sintering temperature of 1250 to 1350 ° C. for 3 to 30 minutes.
- the present invention performs the molding in the step B by cold isostatic pressing (CIP), and the sintering in the step B is performed by pulsed electric pressure sintering. It is also characterized by carrying out by a sintering method (Pulsed Electric-Current Pressure Sintering: PECPS) or a discharge plasma sintering method (Spark Plasma Sintering: SPS). Furthermore, the present invention is characterized in that, in the manufacturing method having the above characteristics, the sintering in the step B is mainly performed in an argon gas atmosphere or a nitrogen gas atmosphere.
- Toughness is achieved by uniformly precipitating fine aluminum oxide Al 2 O 3 fine particles from the solid solution powder during sintering.
- High strength toughness ZrO 2 -Al 2 O 3 system with bending strength ⁇ b ⁇ 1 GPa and fracture toughness value K IC ⁇ 15 MPa ⁇ m 1/2 by using the production method of the present invention.
- Solid solution ceramics can be produced.
- A is an XRD pattern of ZrO 2 -25 mol% Al 2 O 3 solid solution ceramics sintered at 1100 ° C.
- B is a ZrO 2 -25 mol% Al 2 O 3 solid solution ceramics sintered at 1200 ° C.
- (A) in (C) is an XRD pattern of ZrO 2 (1.5Y) -25 mol% Al 2 O 3 solid solution powder calcined at 820 ° C.
- (b), (c) ), (D), (e), and (f) are ZrO 2 (1.5Y) -25 mol% Al 2 O 3 solid solution ceramics sintered at 1100 ° C., 1200 ° C., 1250 ° C., 1300 ° C., and 1350 ° C., respectively. This is an XRD pattern.
- (A) -1 is an SEM photograph of ZrO 2 -25 mol% Al 2 O 3 solid solution ceramic powder calcined at 800 ° C.
- (A) -2 is ZrO 2 -25 mol% Al sintered at 1200 ° C. It is a SEM photograph of a fracture surface of 2 O 3 solid solution ceramics.
- (B) -1 is an SEM photograph of ZrO 2 (1.5Y) -25 mol% Al 2 O 3 solid solution ceramic powder calcined at 820 ° C.
- (B) -2 is sintered at 1200 ° C.
- FIG. 3 is a SEM photograph of the fracture surface of the ZrO 2 (1.5Y) -25 mol% Al 2 O 3 solid solution ceramics, and the average particle diameter of each is shown on the right side of the photograph.
- A SEM photograph of fracture surface of ZrO 2 (1.5Y) -25 mol% Al 2 O 3 solid solution ceramics sintered at 1200 ° C.,
- B 1250 ° C.,
- C 1300 ° C. The diameter is also listed.
- sintering temperature is a graph showing ZrO 2 (1.5Y) -25mol% Al 2 O 3 solid solution ceramics bending strength sigma b, fracture toughness K IC, the relationship between the Vickers hardness H v.
- ZrO 2 was using a solid solution powder prepared at various sintering temperatures (1.5Y) -25mol% Al 2 O 3 solid solution ceramics and, ZrO 2 that by using the mixed powder was made in a variety of sintering temperatures (3.0Y) -25mol% Al 2 O 3 composite mechanical properties (flexural strength, Vickers hardness, fracture toughness value) of ceramics is a graph showing a. It is a graph which shows the change of the fracture toughness value and the Vickers hardness of the ceramic sintered at 1300 ° C. in which the amount of Y 2 O 3 added to ZrO 2 is changed in ZrO 2 -25 mol% Al 2 O 3 solid solution ceramics.
- Mechanical properties of ZrO 2 (1.5Y) -25 mol% Al 2 O 3 solid solution ceramics prepared from raw materials obtained using the sol-gel method, and those obtained using water-soluble raw materials It is the table which compared.
- Step A and Step B in the method of the present invention capable of producing a high-strength toughness ZrO 2 -Al 2 O 3 solid solution ceramic will be described.
- step in the present invention A step Preparation of ZrO 2 solid solution powder
- a solid solution powder prepared by adding 30 to 20 mol% of Al 2 O 3 is prepared.
- such a solid solution powder is prepared by a process described in the flowchart shown in FIG. Done. However, it is not limited to the raw material and conditions used in the process shown in FIG.
- the amount of Y 2 O 3 added to ZrO 2 is limited to 0.3 to 1.7 mol%, even if the amount added is less than 0.3 mol%, or conversely exceeds 1.7 mol%, This is because the bending strength ⁇ b at room temperature is smaller than 1000 Ma and the fracture toughness value K IC is smaller than 15 MPa ⁇ m 1/2 , and the addition amount of Al 2 O 3 is limited to 20 to 30 mol%. This is because even if the addition amount is less than 20 mol%, or conversely, the addition strength exceeds 30 mol%, the bending strength ⁇ b becomes less than 1000 MPa.
- the temperature at which the solid solution powder is calcined to prepare a tetragonal ZrO 2 solid solution powder may be higher than the crystallization temperature, and preferably 700 ° C. to 900 ° C.
- the crystalline ZrO 2 solid solution powder obtained in the step A is molded, and then the heating rate is 50 ° C./min or more in an inert gas atmosphere.
- High strength toughness ZrO 2 -Al 2 O 3 based solid solution ceramics are produced by sintering at a pressure of 30 to 100 MPa and a sintering temperature of 1250 to 1350 ° C. for 3 to 30 minutes.
- a cold isostatic press is suitable for forming a ZrO 2 solid solution powder, and a pulsed current pressure sintering method in an argon gas or nitrogen gas atmosphere is used to sinter the obtained molded body.
- a discharge plasma sintering method is suitable.
- the pulsed current pressure sintering method in which a pulsed direct current is applied at a low voltage under uniaxial pressure and high energy is instantaneously generated by the spark discharge phenomenon, is suitable for the rapid joule. This is because melting and high-speed diffusion occur by heating, and high-speed sintering can be achieved in a short time, so that a dense sintered body (relative density of 90% or more) with relatively suppressed grain growth can be obtained. The law is suitable for the same reason.
- Particularly preferred conditions for pulsed current pressure sintering in the present invention are the conditions of a heating rate of 50 to 100 ° C./min, an applied pressure of 60 MPa, a sintering temperature of 1270 to 1330 ° C., and a holding time of 10 minutes in an argon gas atmosphere. .
- a heating rate of 50 to 100 ° C./min
- an applied pressure of 60 MPa
- a sintering temperature of 1270 to 1330 ° C.
- a holding time 10 minutes in an argon gas atmosphere.
- the applied pressure is less than 30 MPa
- the sintering density is low, and conversely if it exceeds 100 MPa, the upper limit is imposed on the strength of the mold used for the electric current pressure sintering.
- the rate of temperature increase if it is less than 50 ° C./minute, the heat treatment takes a long time and the manufacturing cost becomes high.
- it exceeds 100 ° C./minute the microstructure inside the sintered body becomes uneven, resulting in a homogeneous and large Since preparation of a sample becomes difficult, it is not preferable.
- the bending strength ⁇ b is a three-point bending strength value measured under the conditions of a span length of 8 mm and a crosshead feed of 0.5 mm / min
- the fracture toughness value K IC is a load of 10 kg. (98N) Indentation (IF) method (K. Niihara et al., J. Master), in which a diamond indenter with a square pyramid is pushed into the ceramic surface for 5 seconds and evaluated from the length of cracks generated at the four corners Sci. Lett., 1, 13-16 (1982)).
- the crystalline solid solution powder is sized and then molded (98 MPa), followed by cold isostatic pressing (245 MPa), and then a commercially available pulse current pressure sintering apparatus (SPS Syntex). (Uses Co., Ltd./SPS-510A) and pulsed energization under an argon gas atmosphere at a pressure of 60 MPa, a sintering temperature of 1100 to 1350 ° C., a holding time of 10 minutes, and a heating rate of 100 ° C./min. Pressure sintering was performed to obtain a sintered body (ZrO 2 (1.5Y) -Al 2 O 3 solid solution ceramics).
- FIG. 2 shows an XRD pattern of the solid solution ceramic sintered body thus obtained.
- (A) is an XRD of ZrO 2 -25 mol% Al 2 O 3 solid solution ceramic sintered at 1100 ° C.
- the pattern (B) is an XRD pattern of ZrO 2 -25 mol% Al 2 O 3 solid solution ceramics sintered at 1200 ° C.
- (A) in (C) is an XRD pattern of ZrO 2 (1.5Y) -25 mol% Al 2 O 3 solid solution powder calcined at 820 ° C., and (b) to (f) are sintered An XRD pattern of ZrO 2 (1.5Y) -25 mol% Al 2 O 3 solid solution ceramics obtained by changing the temperature from 1100 ° C.
- FIG. 3 shows SEM photographs of the calcined powder thus obtained and the fracture surface of the solid solution ceramic sintered body.
- A -1 is ZrO calcined at 800 ° C. a SEM photograph of 2 -25mol% Al 2 O 3 solid solution ceramic powder
- (a) -2 is an SEM photograph of the fracture surface of the ZrO 2 -25mol% Al 2 O 3 solid solution ceramics sintered at 1200 ° C.
- (B) -1 is an SEM photograph of ZrO 2 (1.5Y) -25 mol% Al 2 O 3 solid solution ceramic powder calcined at 820 ° C.
- B) -2 is sintered at 1200 ° C.
- FIG. 4 shows an SEM photograph of the fracture surface of ZrO 2 (1.5Y) -25 mol% Al 2 O 3 solid solution ceramics when the firing temperature is changed, and (A) shows a firing temperature of 1200 ° C.
- the firing temperature is 1250 ° C.
- (C) is the case where the firing temperature is 1300 ° C. From these SEM photographs, it can be seen that the firing temperature is 1200 ° C. to 1300 ° C. and that the structure is denser. From the comparison of the respective average particle diameters, the firing temperature increases slightly from 180 to 200 nm. I understand that.
- Tables 1 and 2 below show the squares of the ZrO 2 -25 mol% Al 2 O 3 solid solution ceramics and the ZrO 2 (1.5Y) -25 mol% Al 2 O 3 solid solution ceramics prepared in the above experiment.
- the volume ratio (t / m), theoretical density, bulk density and relative density of crystalline zirconium oxide (t-ZrO 2 ) / monoclinic zirconium oxide (m-ZrO 2 ) are summarized.
- FIG. 5 shows the sintering temperature, bending strength ⁇ b , and fracture toughness value K IC for the ZrO 2 (1.5Y) -25 mol% Al 2 O 3 solid solution ceramic when the firing temperature is changed. , the relationship of Vickers hardness H v is shown in a graph.
- a bending strength ⁇ b of 1 GPa or higher can be achieved (1.33 GPa when the sintering temperature is 1300 ° C.), and the sintering temperature is about 1230 ° C.- in the case of 1360 ° C. 18 MPa ⁇ m 1/2 or more, 21.3MPa ⁇ in the case of about 1270 °C ⁇ 1330 °C 20MPa ⁇ m 1/2 or more fracture toughness K IC (sintering temperature 1300 ° C. in the case of m 1/2 ) can be achieved.
- the Vickers hardness H v is the sintering temperature was above 13GPa to not less than about 1230 °C (13.4GPa when the sintering temperature is 1300 ° C.).
- Comparative product 1 ZrO 2 (1.5Y-ZrO 2 ) powder added with commercially available 1.5 mol% Y 2 O 3 (98.5 mol% ZrO 2 -1.5 mol% Y 2 O 3 ) and commercially available Al 2 O 3 fine particles was mixed with a planetary ball mill to obtain a mixed powder (Z
- High pressure sintering was performed under the conditions of 1 GPa, a sintering temperature of 900 ° C., and a holding time of 30 minutes to obtain a sintered body.
- the bending strength ⁇ b was 1.125 GPa and the fracture toughness value K IC was 15.8 MPa ⁇ m 1/2 .
- a forming process under a very high pressure, a cold isostatic press It was found that a treatment process and a sintering process are necessary.
- Example 3 ZrO 2 (1.5Y) -25mol% Al 2 O 3 solid solution ceramics produced using the solid solution powder, ZrO 2 (3.0Y) produced by using the mixed powder -25mol% Al 2 Comparison of mechanical properties with O 3 composite ceramics ZrO 2 (1.5Y) -25 mol% Al 2 O 3 solid solution ceramics produced by using a solid solution powder by changing the sintering temperature in the range of 1100 to 1350 ° C., The mechanical properties (bending strength, Vickers hardness, fracture toughness value) of each of the ZrO 2 (3.0Y) -25 mol% Al 2 O 3 composite ceramics produced by sintering the mixed powder were measured.
- the Vickers hardness increases (16 GPa or more), but the bending strength becomes 1000 MPa or less.
- the fracture toughness value is 7 MPa ⁇ m 1/2 or less.
- Example 4 Y 2 O 3 amount when changing the addition, when the amount of change Y 2 O 3 of fracture toughness and Vickers hardness was varied in the range of 0 ⁇ 3 mol%, the fracture toughness value and The change in Vickers hardness was measured.
- the sintering conditions were a pressure of 50 to 60 MPa, a sintering temperature of 1300 ° C., and a holding time of 10 minutes.
- the result is shown in FIG. From the graph of FIG. 7A, regarding the fracture toughness value K IC , the amount of Y 2 O 3 added is 15 MPa ⁇ m 1/2 or more in the range of 0.3 to 1.7 mol%, and 0.7 to 1.5 mol. % Range was found to be 18 MPa ⁇ m 1/2 or more.
- the bending strength in the range of such addition amount is 1 GPa or more.
- the Vickers hardness is 12 GPa or more when the Y 2 O 3 addition amount is in the range of 0.3 to 1.7 mol%, and 14 GPa in the range of 0.7 to 1.5 mol%. It turns out that it becomes the above. Therefore, the amount of Y 2 O 3 added for producing high strength toughness ZrO 2 —Al 2 O 3 based solid solution ceramics is in the range of 0.3 to 1.7 mol%, and a particularly preferable range is 0.8. It was found to be 7 to 1.5 mol%.
- Example 5 Mechanical properties of ZrO 2 (1.5Y) -25 mol% Al 2 O 3 solid solution ceramics (product of the present invention) prepared from raw materials obtained using the sol-gel method, and water-soluble raw materials Mechanical properties of the product obtained by using the three types of ZrO 2 (1.5Y) -25 mol% Al 2 O 3 solid solution ceramics manufactured under the manufacturing conditions shown in FIG. 8 and measuring various mechanical properties for each. did. From the measurement results shown in FIG. 8, in the case of using the raw material by the sol-gel method (the manufacturing method of the present invention), the crystal structure of the produced solid solution ceramic is more tetragonal than monoclinic (m).
- the ZrO 2 -Al 2 O 3 solid solution ceramics obtained using the production method of the present invention has a bending strength of 1 GPa or more and a fracture toughness value of 15 MPa ⁇ m 1/2 or more. It can be used for various applications that require toughness, such as ceramic machine parts, biological ceramics (artificial roots, artificial joints, artificial bones), household knives, cutting boards, and the like.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Ceramic Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Materials Engineering (AREA)
- Structural Engineering (AREA)
- Organic Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Composite Materials (AREA)
- Compositions Of Oxide Ceramics (AREA)
- Thermal Sciences (AREA)
- Physics & Mathematics (AREA)
- Dispersion Chemistry (AREA)
Abstract
L'invention concerne un procédé de fabrication d'une céramique en solution solide, à base de ZrO2-Al2O3, à résistance élevée, à ténacité élevée. Y2O3 dans une quantité de 0,3-1,7 % en moles est ajouté à ZrO2 à l'aide d'un procédé sol-gel pour préparer une poudre en solution solide de ZrO2 amorphe-(20-30 % en moles d'Al2O3), et la poudre en solution solide amorphe résultante est préfrittée à une température égale ou supérieure à une température de cristallisation, permettant ainsi de préparer une poudre de solution solide de ZrO2 cristallin (étape A). La poudre de solution solide de ZrO2 cristallin résultante est moulée, et le produit moulé est ensuite fritté dans une atmosphère de gaz inerte dans les conditions d'une allure de montée en température de 50ºC/min ou plus, une pression de 30-100 MPa et d'une température de frittage de 1250-1350˚C pendant 3-30 minutes (étape B). Dans ce procédé, on préfère effectuer le moulage dans l'étape B au moyen d'une presse isostatique à froid et effectuer le frittage par un procédé de frittage sous pression et courant pulsé ou un procédé de frittage à plasma d'étincelles dans une atmosphère d'argon ou azote gazeux.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2013513978A JP5930317B2 (ja) | 2011-05-12 | 2012-04-26 | 高強度強靱性ZrO2‐Al2O3系固溶体セラミックスの作製法 |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2011-107228 | 2011-05-12 | ||
JP2011107228 | 2011-05-12 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2012153645A1 true WO2012153645A1 (fr) | 2012-11-15 |
Family
ID=47139129
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2012/061196 WO2012153645A1 (fr) | 2011-05-12 | 2012-04-26 | PROCÉDÉ DE FABRICATION D'UNE CÉRAMIQUE EN SOLUTION SOLIDE À BASE DE ZrO2-Al2O3,À RÉSISTANCE ÉLEVÉE, À TÉNACITÉ ÉLEVÉE |
Country Status (2)
Country | Link |
---|---|
JP (1) | JP5930317B2 (fr) |
WO (1) | WO2012153645A1 (fr) |
Cited By (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2014189474A (ja) * | 2013-03-28 | 2014-10-06 | Doshisha | 高強度強靱性ZrO2−Al2O3系固溶体セラミックスの作製法 |
KR20170039225A (ko) | 2015-04-20 | 2017-04-10 | 스미토모덴키고교가부시키가이샤 | 소결체 및 그것을 포함하는 절삭 공구 |
US9902654B2 (en) | 2016-06-20 | 2018-02-27 | The Doshisha | ZrO2-Al2O3-based ceramic sintered compact and production method thereof |
US9988314B2 (en) | 2015-05-29 | 2018-06-05 | Sumitomo Electric Hardmetal Corp. | Sintered compact and cutting tool |
CN108409312A (zh) * | 2018-03-26 | 2018-08-17 | 淄博畅安陶瓷科技有限公司 | 对辊机筒体瓷件及其制备方法 |
US10532951B2 (en) | 2016-05-27 | 2020-01-14 | Sumitomo Electric Industries, Ltd. | Sintered material and cutting tool including same |
CN115819079A (zh) * | 2022-12-02 | 2023-03-21 | 中南大学湘雅二医院 | 一种人造牙齿用材料及其制备方法 |
JP7438501B1 (ja) | 2023-01-24 | 2024-02-27 | 学校法人 龍谷大学 | アルミナ-ジルコニア混合材料及びその製造方法 |
Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH06306352A (ja) * | 1993-04-27 | 1994-11-01 | Tosoh Corp | ジルコニア質グリットおよびその製造方法 |
JPH11147762A (ja) * | 1997-11-11 | 1999-06-02 | Fine Ceramics Gijutsu Kenkyu Kumiai | 酸化ジルコニウム系焼結体およびその製造方法 |
JP2002255642A (ja) * | 2001-03-02 | 2002-09-11 | National Institute Of Advanced Industrial & Technology | 高密度イットリア安定化ジルコニア焼結体及びその製造方法 |
JP2004075532A (ja) * | 2002-08-01 | 2004-03-11 | Kobe Steel Ltd | 高強度・高靱性ジルコニア焼結材およびそれを用いた生体材料 |
JP2006225205A (ja) * | 2005-02-17 | 2006-08-31 | Osaka Univ | 導電性ジルコニア焼結体及びその製造方法 |
-
2012
- 2012-04-26 JP JP2013513978A patent/JP5930317B2/ja not_active Expired - Fee Related
- 2012-04-26 WO PCT/JP2012/061196 patent/WO2012153645A1/fr active Application Filing
Patent Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH06306352A (ja) * | 1993-04-27 | 1994-11-01 | Tosoh Corp | ジルコニア質グリットおよびその製造方法 |
JPH11147762A (ja) * | 1997-11-11 | 1999-06-02 | Fine Ceramics Gijutsu Kenkyu Kumiai | 酸化ジルコニウム系焼結体およびその製造方法 |
JP2002255642A (ja) * | 2001-03-02 | 2002-09-11 | National Institute Of Advanced Industrial & Technology | 高密度イットリア安定化ジルコニア焼結体及びその製造方法 |
JP2004075532A (ja) * | 2002-08-01 | 2004-03-11 | Kobe Steel Ltd | 高強度・高靱性ジルコニア焼結材およびそれを用いた生体材料 |
JP2006225205A (ja) * | 2005-02-17 | 2006-08-31 | Osaka Univ | 導電性ジルコニア焼結体及びその製造方法 |
Non-Patent Citations (1)
Title |
---|
O. YAMAGUCHI ET AL.: "Fabrication and mechanical properties of Zr02 solid solution and composite ceramics in the system ZrO2 (Y203)-A1203.", ADVANCED SYNTHESIS AND PROCESSING OF COMPOSITES AND ADVANCED CERAMICS, 1995, pages 353 - 360 * |
Cited By (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2014189474A (ja) * | 2013-03-28 | 2014-10-06 | Doshisha | 高強度強靱性ZrO2−Al2O3系固溶体セラミックスの作製法 |
KR20170039225A (ko) | 2015-04-20 | 2017-04-10 | 스미토모덴키고교가부시키가이샤 | 소결체 및 그것을 포함하는 절삭 공구 |
US9988315B2 (en) | 2015-04-20 | 2018-06-05 | Sumitomo Electric Industries, Ltd. | Sintered body and cutting tool including the same |
US9988314B2 (en) | 2015-05-29 | 2018-06-05 | Sumitomo Electric Hardmetal Corp. | Sintered compact and cutting tool |
US10532951B2 (en) | 2016-05-27 | 2020-01-14 | Sumitomo Electric Industries, Ltd. | Sintered material and cutting tool including same |
US9902654B2 (en) | 2016-06-20 | 2018-02-27 | The Doshisha | ZrO2-Al2O3-based ceramic sintered compact and production method thereof |
CN108409312A (zh) * | 2018-03-26 | 2018-08-17 | 淄博畅安陶瓷科技有限公司 | 对辊机筒体瓷件及其制备方法 |
CN115819079A (zh) * | 2022-12-02 | 2023-03-21 | 中南大学湘雅二医院 | 一种人造牙齿用材料及其制备方法 |
JP7438501B1 (ja) | 2023-01-24 | 2024-02-27 | 学校法人 龍谷大学 | アルミナ-ジルコニア混合材料及びその製造方法 |
Also Published As
Publication number | Publication date |
---|---|
JPWO2012153645A1 (ja) | 2015-04-27 |
JP5930317B2 (ja) | 2016-06-08 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP5930317B2 (ja) | 高強度強靱性ZrO2‐Al2O3系固溶体セラミックスの作製法 | |
CN109879669A (zh) | 一种具有高强度的高熵陶瓷复合材料及其制备方法和应用 | |
JP6052735B2 (ja) | 高強度強靱性ZrO2−Al2O3系固溶体セラミックスの作製法 | |
CN114315359B (zh) | 一种利用固溶耦合法制备高强韧复相高熵陶瓷的方法和应用 | |
RU2744543C1 (ru) | Способ получения керамического композиционного материала на основе карбида кремния, армированного волокнами карбида кремния | |
CN106904977B (zh) | 一种两步烧结法制备表硬心韧Si3N4陶瓷材料的方法 | |
CN108640672A (zh) | 一种镁铝尖晶石透明陶瓷的制备方法 | |
JP6908248B2 (ja) | 被覆SiCナノ粒子を用いたSiCセラミックス及びその製造方法 | |
JP6436905B2 (ja) | 炭化ホウ素セラミックス及びその作製法 | |
Chen et al. | Fabrication of YAG transparent ceramics by two-step sintering | |
US7833922B2 (en) | Method of forming aluminum oxynitride material and bodies formed by such methods | |
JP4518020B2 (ja) | 窒化ケイ素質焼結体およびそれを用いた回路基板。 | |
JP3775335B2 (ja) | 窒化ケイ素質焼結体および窒化ケイ素質焼結体の製造方法、並びにそれを用いた回路基板 | |
Yin et al. | Microstructure evolution and densification kinetics of Al2O3/Ti (C, N) ceramic tool material by microwave sintering | |
CN111943682B (zh) | 一种高韧性耐氧化的织构化高熵陶瓷及其制备方法和应用 | |
KR100936016B1 (ko) | 초미세 결정립 Mo 스퍼터링 타겟의 제조방법, 및 이로써얻어진 Mo 스퍼터링 타겟 | |
WO2020202878A1 (fr) | Composite de borure de zirconium/carbure de bore et procédé pour la fabrication de celui-ci | |
JP2016147780A (ja) | 導電性高強度高硬度コンポジットセラミックス及びその作製法 | |
JP7116234B1 (ja) | 複合セラミックスの製造方法 | |
JP5408591B2 (ja) | 高密度金属ホウ化物の製造方法 | |
JP5245081B2 (ja) | 高硬度高密度立方晶窒化ホウ素系焼結体およびその製造方法 | |
JP5698568B2 (ja) | 酸化アルミニウム焼結体およびその製造方法 | |
Toksoy et al. | Densification and microstructural properties of boron-carbide in spark plasma sintering | |
WO2018038252A1 (fr) | Corps de substrat en céramique de trioxyde de di-titane et son procédé de production | |
JP2021181384A (ja) | 炭化ジルコニウム/ホウ化ジルコニウム/炭素コンポジット及びその製造方法 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 12783001 Country of ref document: EP Kind code of ref document: A1 |
|
DPE1 | Request for preliminary examination filed after expiration of 19th month from priority date (pct application filed from 20040101) | ||
ENP | Entry into the national phase |
Ref document number: 2013513978 Country of ref document: JP Kind code of ref document: A |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
122 | Ep: pct application non-entry in european phase |
Ref document number: 12783001 Country of ref document: EP Kind code of ref document: A1 |