WO2005040064A1 - セラミックス複合材料およびその製造方法 - Google Patents
セラミックス複合材料およびその製造方法 Download PDFInfo
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- WO2005040064A1 WO2005040064A1 PCT/JP2004/016077 JP2004016077W WO2005040064A1 WO 2005040064 A1 WO2005040064 A1 WO 2005040064A1 JP 2004016077 W JP2004016077 W JP 2004016077W WO 2005040064 A1 WO2005040064 A1 WO 2005040064A1
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- Prior art keywords
- ceramic
- powder
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- composite material
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- 239000000919 ceramic Substances 0.000 title claims abstract description 114
- 239000002131 composite material Substances 0.000 title claims abstract description 89
- 238000004519 manufacturing process Methods 0.000 title claims description 12
- 238000005245 sintering Methods 0.000 claims abstract description 81
- 239000000843 powder Substances 0.000 claims abstract description 77
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 63
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 34
- 239000013078 crystal Substances 0.000 claims abstract description 32
- 150000004767 nitrides Chemical class 0.000 claims abstract description 18
- 239000000463 material Substances 0.000 claims abstract description 14
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 12
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 12
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 11
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 11
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 11
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 11
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 10
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 10
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 10
- 150000001247 metal acetylides Chemical class 0.000 claims abstract description 9
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 9
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 4
- 239000002245 particle Substances 0.000 claims description 58
- 239000011148 porous material Substances 0.000 claims description 24
- 239000012298 atmosphere Substances 0.000 claims description 22
- 239000011812 mixed powder Substances 0.000 claims description 15
- 229910052751 metal Inorganic materials 0.000 claims description 14
- 239000002184 metal Substances 0.000 claims description 14
- 230000001590 oxidative effect Effects 0.000 claims description 6
- 238000005498 polishing Methods 0.000 claims description 4
- BVKZGUZCCUSVTD-UHFFFAOYSA-L Carbonate Chemical compound [O-]C([O-])=O BVKZGUZCCUSVTD-UHFFFAOYSA-L 0.000 claims description 3
- 150000004649 carbonic acid derivatives Chemical class 0.000 claims description 3
- 238000000034 method Methods 0.000 claims description 3
- 239000004065 semiconductor Substances 0.000 claims 1
- 229910010293 ceramic material Inorganic materials 0.000 abstract description 3
- 238000005520 cutting process Methods 0.000 abstract description 3
- 238000005299 abrasion Methods 0.000 abstract description 2
- 239000002994 raw material Substances 0.000 abstract 1
- 239000011521 glass Substances 0.000 description 28
- 238000012360 testing method Methods 0.000 description 27
- 239000011246 composite particle Substances 0.000 description 24
- 238000000465 moulding Methods 0.000 description 23
- RZVAJINKPMORJF-UHFFFAOYSA-N Acetaminophen Chemical compound CC(=O)NC1=CC=C(O)C=C1 RZVAJINKPMORJF-UHFFFAOYSA-N 0.000 description 15
- 230000005540 biological transmission Effects 0.000 description 15
- 239000005297 pyrex Substances 0.000 description 15
- 230000000052 comparative effect Effects 0.000 description 14
- 229910002804 graphite Inorganic materials 0.000 description 14
- 239000010439 graphite Substances 0.000 description 14
- 230000001133 acceleration Effects 0.000 description 10
- 238000011156 evaluation Methods 0.000 description 9
- 238000000227 grinding Methods 0.000 description 9
- 230000003746 surface roughness Effects 0.000 description 9
- 239000005304 optical glass Substances 0.000 description 8
- 239000010936 titanium Substances 0.000 description 8
- 238000012546 transfer Methods 0.000 description 8
- 238000005452 bending Methods 0.000 description 7
- 239000000203 mixture Substances 0.000 description 7
- 239000012299 nitrogen atmosphere Substances 0.000 description 7
- 238000004451 qualitative analysis Methods 0.000 description 7
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 description 7
- 229910010271 silicon carbide Inorganic materials 0.000 description 7
- 239000007789 gas Substances 0.000 description 5
- 238000002156 mixing Methods 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 238000006243 chemical reaction Methods 0.000 description 4
- 238000005259 measurement Methods 0.000 description 4
- QSHDDOUJBYECFT-UHFFFAOYSA-N mercury Chemical compound [Hg] QSHDDOUJBYECFT-UHFFFAOYSA-N 0.000 description 4
- 229910052753 mercury Inorganic materials 0.000 description 4
- 238000003825 pressing Methods 0.000 description 4
- 239000011347 resin Substances 0.000 description 4
- 229920005989 resin Polymers 0.000 description 4
- 150000002739 metals Chemical class 0.000 description 3
- 229910052581 Si3N4 Inorganic materials 0.000 description 2
- 239000002134 carbon nanofiber Substances 0.000 description 2
- 239000002041 carbon nanotube Substances 0.000 description 2
- 229910021393 carbon nanotube Inorganic materials 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 230000002950 deficient Effects 0.000 description 2
- 238000007496 glass forming Methods 0.000 description 2
- 229910021397 glassy carbon Inorganic materials 0.000 description 2
- 238000007689 inspection Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical compound N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 description 2
- XMWRBQBLMFGWIX-UHFFFAOYSA-N C60 fullerene Chemical compound C12=C3C(C4=C56)=C7C8=C5C5=C9C%10=C6C6=C4C1=C1C4=C6C6=C%10C%10=C9C9=C%11C5=C8C5=C8C7=C3C3=C7C2=C1C1=C2C4=C6C4=C%10C6=C9C9=C%11C5=C5C8=C3C3=C7C1=C1C2=C4C6=C2C9=C5C3=C12 XMWRBQBLMFGWIX-UHFFFAOYSA-N 0.000 description 1
- BPQQTUXANYXVAA-UHFFFAOYSA-N Orthosilicate Chemical compound [O-][Si]([O-])([O-])[O-] BPQQTUXANYXVAA-UHFFFAOYSA-N 0.000 description 1
- 101001012040 Pseudomonas aeruginosa (strain ATCC 15692 / DSM 22644 / CIP 104116 / JCM 14847 / LMG 12228 / 1C / PRS 101 / PAO1) Immunomodulating metalloprotease Proteins 0.000 description 1
- BQCADISMDOOEFD-UHFFFAOYSA-N Silver Chemical compound [Ag] BQCADISMDOOEFD-UHFFFAOYSA-N 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 238000009529 body temperature measurement Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 239000010432 diamond Substances 0.000 description 1
- 229910003460 diamond Inorganic materials 0.000 description 1
- 229910003472 fullerene Inorganic materials 0.000 description 1
- 239000007770 graphite material Substances 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 150000002506 iron compounds Chemical class 0.000 description 1
- 230000001050 lubricating effect Effects 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000010303 mechanochemical reaction Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 229910052575 non-oxide ceramic Inorganic materials 0.000 description 1
- 239000011225 non-oxide ceramic Substances 0.000 description 1
- 238000013001 point bending Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 229930000044 secondary metabolite Natural products 0.000 description 1
- 229910052709 silver Inorganic materials 0.000 description 1
- 239000004332 silver Substances 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000004154 testing of material Methods 0.000 description 1
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 description 1
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- C04B35/64—Burning or sintering processes
- C04B35/645—Pressure sintering
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- B82—NANOTECHNOLOGY
- B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
- B82Y30/00—Nanotechnology for materials or surface science, e.g. nanocomposites
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Definitions
- the present invention relates to various structural members ⁇ High wear resistance used for cutting tools, sliding members, mold materials, etc. ⁇ As a low friction ceramic material, ceramic composites with excellent mechanical properties from room temperature to medium to low temperature The present invention relates to a material and a method for manufacturing the same. Background art
- Japanese Patent Application Laid-Open No. 2003-34580 reports a material having excellent friction characteristics and abrasion resistance characteristics using a composite material of silicon nitride and titanium nitride, a graphite material of 0.5 to 20 wt%, and carbon. I have.
- JP-A-2003-34580 observation using a SEM at 2,000 times revealed that the open pore ratio was as large as 3% or more and the diameter was 20%. Many pores of ⁇ or more were observed, and it was found that it was impossible to use them as molds.
- Japanese Patent Application Laid-Open No. 60-100646 discloses that alumina, zircoair powder contains 0.5 to 6 wt% of C, Cr, Mo, W, A1, Ti, and Ni as oxidation resistant alloys. Although high toughness materials have been reported, the C content is as low as 0.1 to 0.2 wt%, and lacks lubricity as a mold.
- Japanese Patent Application Laid-Open No. 09-87029 reports that a material obtained by adding 2 to 5 wt% of carbon having a particle size of 5 ⁇ or more to silicon carbide has excellent wear resistance.
- the publication discloses a material in which graphite having an average crystal grain size of 3 to 6 m is dispersed in a titanium carbide matrix by 3 to 3 wt%.
- the average crystal grain size of carbon is as large as 3 ⁇ or more, and when processed into a desired shape, the surface roughness is affected by the grain size, making it difficult to obtain a mirror surface shape with an average surface roughness of 10 nm or less. is there.
- Hei 10-231 174 discloses that graphite and BN are dispersed in non-oxide ceramics and an iron compound (oxide, silicate, etc.) is interposed in the boundary layer. Although it has been reported that it contains iron, it is not suitable for use as a mold because it contains iron and is degraded by oxidation and lacks stability at high temperatures. Disclosure of the invention
- the present invention provides a ceramic composite material having excellent releasability from glass, resin, ceramics, and the like, in addition to having excellent mechanical properties from room temperature to medium to high temperatures, and a method for producing the same. To do.
- the present inventors have found that, in a ceramics composite material containing a phase containing carbon as a main component, the average crystal grain size of the ceramics composite material is 3 ⁇ m or less, preferably 30 nm or less. It can be seen that the above problem can be solved by doing! /, And the present invention has been completed.
- the present invention has the following configuration.
- a ceramic composite material comprising a carbon-based phase and a ceramic phase (excluding carbon) having an average crystal grain size of 3 ⁇ or less, preferably 30 nm or less.
- Sintering temperature 800-1500 ° C, sintering pressure 20 OMPa or more A method for producing a ceramic composite material, comprising a phase mainly composed of carbon and a ceramic phase, having an average crystal grain size of 3 m or less, preferably 3 O nm or less, characterized by being sintered.
- the ceramic powder is A1, Si, Ti, Zr, Hf'V, Nb, Ta, Cr, Mo, W nitride, carbide, oxidized nitride, composite nitride
- a method for producing a ceramic composite material comprising a carbon phase and a ceramic phase, each having a size of ⁇ m or less, preferably 30 nm or less.
- a method for producing a ceramic composite material comprising: the ceramic phase comprising a phase mainly containing carbon having an average crystal grain size of 3 ⁇ m or less, preferably 30 nm or less, according to (7).
- the present invention is a ceramic composite material comprising a phase mainly composed of carbon and a ceramic phase having an average crystal grain size of 3 ⁇ m or less, preferably 30 nm or less.
- the phase mainly composed of carbon exhibits high mold release properties with glass, resin, ceramics, etc. If the average crystal grain size of the phase of the ceramic composite material exceeds 3 ⁇ m, the average surface roughness is too large to obtain a mirror-like shape when processed into a desired shape.
- the carbon in the present invention may be composed of S-carbon, which is a constituent material.
- S-carbon which is a constituent material.
- the carbon content is 2 to 98 wt% .If the content is less than this, it is not preferable because the releasability is reduced.If the content is more than this, sintering is not performed. Not preferred.
- Force S Preferably this content-carbon is 30 ⁇ 8 Ow t%, particularly preferably 40 ⁇ 6 Ow t 0/0. If the carbon content is within this range, glass, resin, ceramic The releasability from a mix or the like is further improved.
- the ceramic phase in the ceramic composite material of the present invention is a group consisting of nitrides, carbides and oxides of A 1, Si, Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, and W. It is desirable to be formed by at least one member selected from the group consisting of:
- the ceramic phase may be a composite nitride, a composite carbide, or a composite oxide of the above-mentioned metals, or may be a carbonitride, an oxynitride, a carbonitride, or a carbonate of the above-mentioned metals.
- One or more ceramic phases are appropriately selected depending on the partner material to be formed, and the content thereof is desirably 2 to 98 wt%.
- a known sintering aid may be used to improve the sinterability.
- the amount of the oxide-based sintering aid is increased, the reaction with carbon becomes violent, It is not preferable because it is difficult to produce a dense material and the mechanical properties are deteriorated.
- the ceramic composite material of the present invention has an average particle size of 3 ⁇ m or less, preferably 30 nm or less, Al, Si, Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W
- a mixed powder of at least one kind of ceramic powder of nitride, carbide and oxide and carbon powder is formed, and the obtained compact is sintered in a non-oxidizing atmosphere at a sintering temperature of 800 to 15
- the above mixed powder further contains A1, S
- It may contain at least one metal selected from 1, Ti, Zr, Hf, V, Nb, Ta, Cr, Mo and W. These metals react with the carbon in the mixed powder or to form a carbide, or a non-oxidizing atmosphere if N 2, react with N 2 to form a nitride. In some cases, carbides or nitrides may be formed by a mechanochemical reaction during mixing.
- the sintering temperature is lower than 800 ° C, it is difficult to obtain a ceramic composite material without promoting the sintering reaction. On the other hand, when the temperature exceeds 15 ° C., the sintering reaction is promoted too much, the particle size becomes coarse, and the mechanical properties decrease.
- the sintering temperature is particularly preferably from 1000 to 140 ° C.
- sintering pressure is less than 20 OMPa, the sintering reaction is not accelerated and a ceramics composite material cannot be obtained.
- a suitable pressure is at least 500 MPa.
- the measuring method used in the examples is as follows.
- a mercury porosimeter (Shimadzu 9420) was used.
- Mercury is injected into the pore, and the pore volume and pore diameter are calculated from the volume of the injected mercury.
- the obtained secondary composite particles were subjected to qualitative analysis by XRD. As a result, peaks of Si 3 N 4 , ZrN, ZrCN, ZrC and C could be confirmed. Further, as a result of observing this secondary composite particle powder with a transmission electron microscope, the average particle size was 3 ⁇ or less.
- a ceramic composite material was obtained by sintering in a vacuum atmosphere under the conditions shown in Table 1. In this case, the temperature of the surface of the die was measured with a two-color thermometer. table
- the average crystal grain size of the ceramic composite material obtained under the conditions of sintering temperature 800 to: 1500 ° C and sintering pressure 200 to 5000 MPa is 3 ⁇ or less. It has been found. When the sintering temperature reaches 1700 ° C, grain growth is remarkably accelerated and The average crystal grain size was larger than 3 m, and the surface roughness of the lap polished surface of the ceramic composite material could not maintain the desired accuracy.
- the open pore ratio of the sintered body using the above sintering conditions was as good as less than 1%. If the open pore ratio is greater than 1%, for example, when used as a glass mold, glass will enter the pores, causing problems such as mold releasability and projections on the transfer surface.
- a powder obtained by adding a graphite powder having an average particle size of 5 ⁇ at a ratio shown in Table 3 was mixed in a nitrogen atmosphere of 0.IMP a. were mixed in acceleration 10 G by Po / remills device using the S ia N 4 balls.
- sintering was performed in a vacuum atmosphere at a sintering temperature of 1150 ° C./a sintering pressure of 1000 MPa to obtain a ceramic composite material.
- the temperature of the die surface was measured with a two-color thermometer.
- the average crystal grain size, open pore ratio, and bending strength were evaluated.
- a product made by He111111 & Company was used. The evaluation was performed using ex glass. The evaluation method is as follows.
- the above Pyrex glass of 1 Omm was pressed at a molding temperature of 720 ° C and a molding pressure of 1 OMPa for 60 seconds.
- a glass forming test was performed 100 times, and the releasability was evaluated as follows. First, Pyre X glass separates from the mold without external force after molding is completed, and there is no chipping, cracking or clouding in the appearance inspection of the Pyre X glass, and the surface roughness of the transferred surface of the Pyre X glass after molding. Those with a force S 0.03 ⁇ m (R a) or less were judged to be good. The number of non-defective products was harmed by the number of molding tests. For example, if 50 good products are obtained in .100 molding tests, the releasability will be 50%. Table 4 shows the above results. Table 4
- Pyrex force Pressed for 60 seconds under the pressurization condition of 72 ° C./10 MPa.
- the ceramic composite material with a graphite content of 2 to 98 wt% satisfied the open pore ratio of less than 1% and the average crystal grain size of 3 ⁇ m or less.
- the releasability from Pyrex glass is very good at 90% or more at a graphite content of 20 to 98 wt%, and the releasability is close to 60% even at a content of 2%, and it is sufficiently used as a mold. Useable results were obtained.
- the graphite content is 1 wt%, the releasability is poor. Very bad.
- a carbon powder having a particle size of ⁇ m or less and a sintering aid to be added as required were mixed in the composition shown in Table 5, and mixed at an acceleration of 1 OG using a ball mill to obtain a mixed powder.
- the secondary composite particles were used and sintered in a vacuum atmosphere under the conditions of a sintering temperature of 1150 ° C./a sintering pressure of 1 000 MPa to produce a ceramic composite material.
- the temperature of the die surface was measured with a two-color thermometer.
- a ceramic powder having an average particle size of 0.5 ⁇ m was used, and the remainder was converted into a carbon powder having an average particle size of 5 / im or less, to which a sintering aid was added as necessary.
- the mixture was blended with the composition shown in 7, and mixed at an acceleration of 10 G using a ball mill to obtain a mixed powder.
- this mixed powder is sintered under the conditions of a sintering degree of 1 15 CTCZ and a sintering pressure of 100 OMPa, in an N 2 gas atmosphere when the ceramic powder is Si 3 N 4 or A 1 N, and when the ceramic powder is S i C, the a 1 2 ⁇ 3, 3 YZ r 0 2 ceramic composite material and each sintered in a r gas atmosphere in the case of (3 seven percent of 2 0 3 Z r 0 2 stabilized) Obtained. In this case, the temperature of the die surface was measured with a two-color thermometer.
- the obtained secondary composite particles were subjected to qualitative analysis by XRD. As a result, peaks of SiC, CrN, CrCN, CrC and C could be confirmed. Further, as a result of observing the secondary composite particle powder with a transmission electron microscope, the average crystal grain size was 3 ⁇ or less.
- the secondary composite particle powder was sintered in a vacuum atmosphere under the conditions shown in Table 9 to obtain a ceramic composite material. Sintered. In this case, the temperature of the die surface was measured with a two-color thermometer. Table 9
- the obtained secondary composite particles were subjected to qualitative analysis by XRD, and broad peaks of Si 3 N 4 , Tin, TiCN, TiC and C could be confirmed. . Further, as a result of observing this secondary composite particle powder with a transmission electron microscope, the average particle size was 30 nm or less.
- the open pore ratio of the sintered body using the above sintering conditions was as good as less than 1%. If the open pore ratio is more than 1%, for example, when used as a glass mold, the glass enters the pores and causes problems such as releasability and projections on the transfer surface.
- the S i 3 N 4 powder of a commercially available average particle diameter 0. 5 ⁇ , 2. a 5 wt% of Y 2 0 3 powder and 1 wt% of A 1 2 0 3 powder as sintering aid further average
- a powder obtained by adding a graphite powder having an average particle size of 5 / m at a ratio shown in Table 13 was mixed with a powder having a particle size of 0.
- mixing was performed at an acceleration of 150 G for 12 hours by a ball mill using Si 3 N 4 balls.
- sintering was performed in a vacuum atmosphere at a sintering temperature of 1200 ° C./a sintering pressure of 1000 MPa to obtain a ceramic composite material.
- the temperature of the die surface was measured with a two-color thermometer.
- the average crystal grain size, open pore ratio, and bending strength were evaluated.
- evaluation was performed using Pyrex glass manufactured by Helmma. The evaluation method is as follows: using this ceramic composite material, which has been cut into ⁇ 2 Omm and then subjected to surface lap polishing to a surface roughness of 0.02 ⁇ m (Ra), as a mold, the above Pyrex glass of ⁇ 10 mm is formed at a molding temperature. Pressing was performed at 720 ° C and a molding pressure of 1 OMPa for 60 seconds. A glass forming test was performed 500 times, and the releasability was evaluated as follows.
- the ceramic composite material with a graphite content of 2 to 98 wt% satisfied the open pore ratio of less than 1% and the average particle size of 30 nm or less. Furthermore, mold release with Pyrex glass is very good at 95% or more at a graphite content of 20 to 98 wt%, and the mold releasability is 60% or more even at a content of 2%. A result that can be used as a mold was obtained. When the graphite content was 1 wt%, the releasability was extremely deteriorated. If the graphite content exceeds 9 wt%, sintering becomes difficult.If the graphite content is 98 wt%, a sintered body can be produced once every few times. It becomes impossible to obtain a sintered body.
- ceramic powder (1) with an average particle size of 40 wt% 0.5 ⁇ , ceramic powder (2) with an average particle size of 20 wt% 0.5 ⁇ m, and the average of the rest are blended with the composition shown in Table 15 and mixed using a pole mill at a power P speed of 150 G for 12 hours. A mixed powder was obtained.
- sintering was performed in a vacuum atmosphere at a sintering temperature of 1200 ° C./a sintering pressure of 1000 MPa to produce a ceramic composite material.
- the temperature at this time As a rule, the temperature of the die surface was measured with a two-color thermometer.
- Pyrex force pressed at 720 ° C / 10MPa for 60 seconds.
- a ceramic powder with an average particle size of 0.5 m as shown in Table 17 was used, and the remainder was carbon powder with an average particle size of 5 ⁇ or less, and a sintering aid was added if necessary.
- the composition was mixed, and the mixture was vigorously mixed with a ball mill at an acceleration of 150 G for 12 hours to obtain a mixed powder. Observation of the obtained secondary compound-containing powder with a transmission electron microscope revealed that the average particle size was 30 nm or less.
- the above composite powder is sintered at a sintering temperature of 1200, a sintering pressure of 100 OMPa, a ceramic powder of Si 3 N 4 or A 1 N in an N 2 gas atmosphere, and a ceramic powder of In the case of S i C, A 1 2 0 3 YZ r 0 2 ( ⁇ r 0 2 stabilized with 3 wt% Y 2 0 3 ), the ceramic composite material is sintered by sintering in an Ar gas atmosphere. Obtained. In this case, the temperature of the die surface was measured with a two-color thermometer.
- Pressing was performed for 60 seconds under the pressurizing condition of 720 ° C / 10MPa.
- the S i C powder commercially available having an average particle size of 0. 5 mu m, 2. a 5 wt% of Y 2 0 3 powder and 1 wt% of eight 1 2 0 3 powder as sintering aid further the average particle 20 wt% of metal CrN powder with a diameter of 3 ⁇ m and 40 wt% of graphite powder with an average particle diameter of 5 ⁇ m were added.
- the powder was mixed in a nitrogen atmosphere of 0.1 IMP a at an acceleration of 1500 for 12 hours using a ball mill using a ball made of SiC.
- the obtained secondary composite particles were subjected to qualitative analysis by XRD, and broad peaks of SiC, CrN, CrCN, CrC and C could be confirmed. Further, as a result of observing this secondary composite particle powder with a transmission electron microscope, the average particle size was found to be 3 Onm or less.
- the secondary composite particles were sintered in a vacuum atmosphere under the conditions shown in Table 19 to obtain a ceramic composite material.
- the temperature of the die surface was measured with a two-color thermometer.
- Pyrex force pressed at 720 ° C / 10MPa for 60 seconds.
- Table 2 1 A commercially available powder obtained by adding a graphite powder having an average particle size of 5 ⁇ to a commercially available SiC powder having an average particle size of 0.5 ⁇ m without adding a sintering agent and adding a ratio shown in Table 21 to the powder, In a nitrogen atmosphere of 0.1 MPa, mixing was performed for 12 hours at an acceleration of 150 G using a ball mill using Si 3 N 4 balls. Table 2 1
- the obtained secondary composite particles were subjected to qualitative analysis by XRD, broad peaks of SiC and C could be confirmed. Further, as a result of observing this secondary composite particle powder with a transmission electron microscope, the average particle size was 30 nm or less.
- a ceramic composite material was obtained by sintering in a vacuum atmosphere at a sintering temperature of 1200 ° C. and a sintering pressure of 1000 MPa.
- the temperature of the die surface was measured with a two-color thermometer.
- the evaluation method was as follows: The ceramic composite material, which had been cut into ⁇ 20 mm and then subjected to surface lap polishing to a surface roughness of 0.02 m (R a), was The ceramic was pressed at a sintering temperature of 100 ° C. and a molding pressure of 50 MPa. A molding test was performed 100 times, and the releasability was evaluated in the following manner.
- the ZnS ceramics separates from the mold without applying external force, and the molded ZnS ceramics are not chipped, cracked or discolored, and the surface roughness of the molded ZnS ceramic transfer surface is reduced.
- the following products were judged as non-defective products.
- the percentage value obtained by dividing the number of conforming products by the number of molding tests is defined as the releasability (%). For example, if 50 good products are obtained in 100 molding tests, the releasability will be 50%. Table 22 shows the above results. Table 2 2
- the ceramic composite material of the present invention has excellent wear resistance, low friction properties, and high releasability from glass, resin, ceramics, etc., it can be used as a cutting tool, a sliding member, and a mold type material. high.
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Abstract
Description
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EP04793185A EP1679293A4 (en) | 2003-10-29 | 2004-10-22 | CERAMIC COMPOSITE MATERIAL AND METHOD OF MANUFACTURING THE SAME |
US10/595,577 US7723248B2 (en) | 2003-10-29 | 2004-10-22 | Ceramic composite material and method for producing same |
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JP2004282952A JP2005154258A (ja) | 2003-10-29 | 2004-09-29 | セラミックス複合材料およびその製造方法 |
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WO2007029588A1 (ja) * | 2005-09-07 | 2007-03-15 | National University Corporation Tohoku University | 高機能複合材料及びその製造方法 |
JP4694358B2 (ja) * | 2005-11-30 | 2011-06-08 | トヨタ自動車株式会社 | 鋳造方法と鋳造型の製造方法 |
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- 2004-10-22 CN CNB2004800322601A patent/CN100425572C/zh not_active Expired - Fee Related
- 2004-10-22 KR KR1020067008248A patent/KR20060116807A/ko not_active Application Discontinuation
- 2004-10-22 US US10/595,577 patent/US7723248B2/en not_active Expired - Fee Related
- 2004-10-22 WO PCT/JP2004/016077 patent/WO2005040064A1/ja active Application Filing
- 2004-10-22 EP EP04793185A patent/EP1679293A4/en not_active Withdrawn
- 2004-10-28 TW TW093132842A patent/TW200526540A/zh unknown
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Also Published As
Publication number | Publication date |
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EP1679293A4 (en) | 2011-01-26 |
JP2005154258A (ja) | 2005-06-16 |
CN1874973A (zh) | 2006-12-06 |
KR20060116807A (ko) | 2006-11-15 |
EP1679293A1 (en) | 2006-07-12 |
CN100425572C (zh) | 2008-10-15 |
US7723248B2 (en) | 2010-05-25 |
US20070129233A1 (en) | 2007-06-07 |
TW200526540A (en) | 2005-08-16 |
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