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
• • 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
  • C04B35/56—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 carbides or oxycarbides
  • C04B35/565—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 carbides or oxycarbides based on silicon carbide
• • 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
• • 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
  • C04B35/597—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 oxynitride, e.g. SIALONS

Definitions

• the present invention relates Ri to ⁇ of Sera Mi 3 ⁇ 4 click scan structure, suitable ⁇ impact to be employed in the turbine blade or the like, especially Ceramic
• the strength tends to fluctuate due to defects in the sintered body and surface defects, and it is difficult to design the strength as a structural material.
• tool materials such as cermet, sintered carbide mainly made of boron carbide, boron nitride, etc. are so-called tough materials that are hard to grow even once cracked, and are tough, so tough.
• these materials have the drawback that when exposed to high temperatures in an oxidizing atmosphere, they deteriorate and their mechanical strength is significantly reduced.
• the aspect ratio is as large as about 5.0 or more, it is difficult for the fibers to be entangled with each other and it is difficult to obtain a uniform sintered body.
• An object of the present invention is to use a highly reliable and versatile structural ceramic member suitable for use as a high-temperature member such as a turbocharger gas turbine. Another object of the present invention is to provide a shochu heat-shockable structure.
• the present invention is characterized in that a portion exposed to a heat cycle at a maximum use temperature of 1100 or more is made of ceramics.
• the ceramic mix is
• Fragile fine particles are found in the sintered ceramics matrix.
• Fracture toughness value evaluated by K 1C is 10 MN / m 3 Z 2 or more
• the object of the present invention is a rotating body (structure), such as a turbine or a turbocharger, or a combustion gas or an explosion gas.
• a structure exposed to light is typical.
• OMPI Is based on the strength design allowance of the rotating structure. Known to date, at most 8 in the Si 3 N 4 series ceramics
• the shochu maturity standard was set at 3 O kg / min 2 or more for the following reasons.
• ceramics are susceptible to cracks, including cracks, on the inside and / or on the surface, resulting in reduced strength. Inspection (ultrasonic deep wound) is limited to a defect size of about 100 itm.
• K 1C is 1 0 MN / m 3/2 or more, even keep the 3 0 kg / mm 2 or more strength for Ketsu ⁇ of its size. In the current situation, it is expected that even if the inspection passes, it will break.
• the structural ceramic member that can be used in the present invention desirably has a heat resistance of maintaining high strength of about 30 kgf Zmm 2 or more up to 1100 or more and a fracture toughness value evaluated by K 1C of 10 M NZ.
• m 3/2 or more has a toughness, and is characterized that you made of silicon co emissions based sintered body having a substantially isotropic mechanical properties.
• the silicon-based ceramic used in the present invention includes at least one of silicon carbide, silicon nitride, and sialon.
• the periodic table ffl a, IV a, Va or V a has a structure in which sintering mainly composed of borides, nitrides or carbides in the base table is dispersed, and the constituent particles of the sintered body Aspect ratio is
• silicon silicon nitride, sialon, etc.
• a ceramic having a structure in which a sintered body mainly composed of borides, nitrides, and carbides is dispersed may be used.
• TaB a was dispersed sintered body mainly comprising such WB structure
• Ceramics can be used.
• Silicon carbide as the base material is silicon carbide.
• the gas boundary is more scattered than in the case of using silicon nitride and sialon.
• the structural products of the present invention using carbonized steel as the base material include parts that rotate at high speed in an atmosphere with a gas temperature of about 1500, such as blades of a high-temperature gas turbine, and sports power. Maintains high level of reliability even when used in high-temperature, high-speed conditions such as turbocharger rotors.
• a firing temperature of about 1700 to 1850 is sufficient, but when silicon carbide is used, the firing temperature is 1900 ° C. It is indispensable to raise the above. If the firing temperature is lower than this, the sinterability of the ceramics is enhanced and open pores remain in the ceramics.
• borides, nitrides, and carbides of the IEa, IVa, Va, and VIa elements are covered and protected by the silicon-based ceramic as the base material. If such a structure cannot be realized, that is, the sintering temperature is too low to leave open pores in the ceramic or the amount of the above-mentioned borides, nitrides and carbides is too large, and When these are continuously connected from the surface to the inside in the box, the oxidizing properties of shochu at a high temperature are remarkably reduced, so that they cannot be applied to the high-temperature structural parts aimed at by the present invention.
• borides, nitrides, and carbides of the Periodic Tables ⁇ a, IVa, Va, and 3 ⁇ 4Ta elements are mixed at a high sintering temperature and mixed with the silicon-based ceramic as the base material. Connect and elaborate.
• the sintering temperature is preferably as high as possible without decomposition.
• sintering temperature cannot be raised any more because gay nitride and sialon are separated at 1850 to 1900 or more,
• the oxidation properties at high temperatures are particularly large, and the silicon-based ceramics used as the base material during sintering.
• fracture toughness value l OMNZ m 3/2 or more and to order the 5 vo J2% or more may be dispersed 1 0 VO JS% higher for the 1 5 MNZ m 3/2 or more .
• the amount of the inorganic substance is too large, the oxidation property of high-temperature shochu generally decreases.
• a compound with low Young's modulus is produced by the reaction during sintering.
• the dispersed sintered body is about 1
• the cracks are dispersed
• the sintered particles must have an aspect ratio of 10 or less.
• fiber-shaped particles which are about 50 or more larger
• the structural ceramic member of the present invention has substantially isotropic strength, even when a large force is applied in the radial direction, such as a rotor, a substantially isotropic force is applied.
• the members can be used easily and effectively, and their versatility as structural members is low.
• the ceramic members usable in the present invention include, in addition to silicon-based ceramics and dispersed inorganic substances, about 10 wt% or less of ⁇ , ⁇ ,, MgO, Y, O,, A ⁇ ⁇ , ⁇ ⁇ ⁇ or the like may be added as a sintering aid.
• the present invention When the present invention is applied to a rotating body structure such as a turbine or a turbocharger and / or a structure exposed to combustion and explosive gas, it is possible to use only the blades as a ceramic.
• the shaft will be embedded in the metal.
• the shaft, the combustor, and the like also include the ceramic structure of the present invention.
• the dispersion form of the particles may be such that the particles are not uniformly dispersed, but may be dispersed, for example, as a group of particles or coexistence of the particles and the group of particles. However, it is desirable that it be dispersed evenly over almost the entire area of the structure. In other words, it is desirable that the properties be isotropic. In addition, if the particles are large, cracks will be formed at the particle interface, and if the particles are small, the particles will be detoured or bent at the particle interface due to the cleavage of the particles, and it is difficult for the particles to be branched. Further, the present invention can be used in combination with fiber dispersion. BRIEF DESCRIPTION OF THE FIGURES
• FIG. 1 to FIG. 5 are micrographs showing the results of a viscart driving test of the shochu thermo-shock ceramic composition shown in Examples of the present invention.
• An Si 3 N 4 powder having an average particle size of 0.7 m and an average particle size of 2; im ( ⁇ , CM p. 3250) were blended in the proportions shown in Table 1.
• the average particle diameter in the al thereto 0. 5 ii m of Y ⁇ Oa and Alpha beta 2 ⁇ 3 was added respectively 6 wt% and 3 wt%, to obtain a uniform mixed powder.
• an organic binder such as low-polymerized polyethylene of 10 to 15 wt% was added to this, and a load of 1500 kg / cin 2 was applied by an injection molding method to obtain a molded body.
• the molded body was heated at a rate of 2 Zh to remove the binder, and then fired in a gas at 1700 to 1800 ° C. for 1 hour to obtain a sintered body.
• Table 1 shows the flexural strength of the obtained sintered body and the flexural strength at room temperature after oxidizing for 2000 h at 1100 and 2000 h at 1300 ° C at K 1C and 1100, respectively.
• the fracture toughness value K was calculated by the following formula after measuring the flexural strength and strength after scratching the sample with a V. hardness tester.
• the power sale by is Kon in Table 1, the amount for 5-7 0 of Hf B 2
• the number of particles in the particle aggregates depends on the particle size of the raw material Hf B 2, the raw material Hf B 2
• the average number of particles is about 10, 40, 150,
• the fracture toughness value of the sintered body increases to 10, 12, 17, and 18 MN nom 3/2, respectively, with the average number of particles. all right.
• This rotor was continuously rotated at a speed of 300,000 rpm for 1000 h at a gas temperature of 1100 to 1200, but problems such as breakage occurred.
• the rotor blades and the shaft are separately injection-molded and fired, and then the raw material powder of the same composition is put between the rainy people and re-joined by hot pressing. Prototype made.
• the mechanical properties of the sintered body obtained by the injection molding and firing are almost isotropic, the reliability of the obtained joint of the rotor is extremely high. No damage was found in the continuous rotation test in a gas at ⁇ 1200 ° C or the repeated test of start / stop by turning on / off the gas. Therefore, even for a complicated product which is difficult to produce by a general injection molding method, the ceramic member for metal structure of the present invention can be applied by combining it with a joining method.
• the photo shows that the crack splits when the Vickers is driven
• Figure 3 is a 1.
• Table 2 shows the characteristics of the obtained sintered body.
• the consolidation exhibited isotropic mechanical properties.
• the aspect ratio of the constituent particles is
• the sintered body has substantially isotropic mechanical strength
• a prototype rotor was manufactured in the same manner as in Example 1, but this rotor
• the binder is removed at a heating speed of 2 Zh, and Ar
• S i C was the major axis 2 to: LO tf ni , Uniaxial l ⁇ 5iim elliptical (as-cut; cut ratio 1 ⁇ 4), and the above-mentioned borides, nitrides and carbides are mainly aggregates of particles with a particle size of 1 ⁇ 5itm It was found that it was dispersed in SiC as a body. The number of particles in the particle aggregate depends on the particle size of the raw material.
• the average particle size of the raw material is 1, 5, 15, 50, or 8 ⁇
• the average number of particles is Is about 1, 5, 100, 1000, and 5000, respectively
• the fracture toughness value of the ceramic is lSM M NZm 3 / ' 2 when the particle size of the particle aggregate is about 100 or more. It turns out that it becomes especially large.
• Example 2 Using samples with f3 ⁇ 43, 4, 7, 13 and 16 as in Example 1, a prototype rotor for a turbocharger with a blade diameter of 4 Omm (integrated blade and shaft) was fabricated. A test piece was cut out from the prototype rotor and examined. As a result, it was found that the ceramics constituting the obtained rotor had isotropic mechanical properties.
• the rotor was continuously rotated for 1000 hours at a speed of 300,000 m3 at a gas temperature of 1300 to 1500 and no abnormality such as breakage was observed.
• the rotor blades and the shaft are separately injection-molded and fired, and then the raw material powder of the same composition is packed between the rainy people.
• Fig. 4 shows the base consisting of SiC 96 wt% and AJ2N 4 wt%.
• Fig. 5 is a scanning micrograph of the ceramics obtained under the same conditions as in Fig. 4 at a magnification of 220 times, and shows how cracks are branched and absorbed when Vickers is driven.
• niobium nitride is added, injection molded at a pressure of 1500 kg / cra 2 and binder is removed at a heating rate of 2 h.
• a prototype rotor for a turbocharger with a blade diameter of 40 mm was manufactured using samples of Na 3 to 6.
• the rotor was continuously operated for 1000 hours at a speed of 300,000 rpm out of 1500 at a gas temperature of 1300 to 1500. No abnormalities such as breakage were observed.
• Niobium nitride is a sintering aid in these samples
• Niobium nitride dioxidized oxide, ca.
• Niobium nitride Niobium nitride, oxidized oxide, cadmium oxide, etc.
• the number of particles in the particle aggregate is the raw material powder of niobium nitride.
• the average particle size of the raw material is 1, 5, 15,
• the number of particles varies to about 1, 5, 100, 1000, and 5000, respectively.
• ISMNZ m 3/2 or more in number of particles is from about 1 0 0 or more (nitriding two
• the major axis is 2-5 / i in and the minor axis is 2-3 / im
• the periodic table V a with a particle size of 1-2 ⁇
• Borides of group VIa elements are dispersed either alone or as an aggregate.
• Average particle size 0.5 111 2 ⁇ 3 3 1%, average particle size ⁇ ⁇ ⁇
• Table 8 shows the characteristics of the obtained samples.
• the particles had a structure dispersed in a Si 3 N 4 sintered body having a particle size of about 5 m.
• the number of particles in the particle assembly depends on the raw material particle size of the boride of the periodic table Va and Wa elements, and the average particle size of the raw material is 1, 5, 15, 50 or 80 Am When these were used, the average number of particles would change to about 1, 5, 100, 1000, and 5000, respectively, and the fracture toughness value of the ceramics was about 100 It was found to be particularly large at 15 MN / m 3/2 or more above the value.
• Alpha beta 2 0 3 of sintering aid, Upsilon 2 ⁇ 3 amounts to vary the results of an experiment, ⁇ ⁇ 2 0 3, ⁇ 2 0 amount of 3 respectively 0.5 wt%
• M g O amount misplacement and results of the experiments the bending strength is 3 0 kgZnn 2 or less at room temperature is M g ⁇ less than 0.5 wt%, also, M g O 1 0
• the mixture was mixed and the mold was pressed at a pressure of 100 kg kg.
• the growth body is

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• Structural Engineering (AREA)
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• 1983
  • 1983-07-27 JP JP58135887A patent/JPS6027643A/ja active Granted
• 1984
  • 1984-07-25 EP EP84902939A patent/EP0152488B1/en not_active Expired
  • 1984-07-25 WO PCT/JP1984/000377 patent/WO1985000588A1/ja active IP Right Grant
  • 1984-07-25 US US06/718,018 patent/US4705761A/en not_active Expired - Fee Related
  • 1984-07-25 DE DE8484902939T patent/DE3478431D1/de not_active Expired
  • 1984-07-26 KR KR1019840004431A patent/KR890002156B1/ko not_active Expired

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