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
  • C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
  • C04B41/53—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone involving the removal of at least part of the materials of the treated article, e.g. etching, drying of hardened concrete
• • 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 to the vacuum heat treatment of nitrogen ceramic materials, such as silicon nitride and sialon ceramics, in order to remove grain-boundary phase material by volatilization.
• nitrogen ceramic materials such as silicon nitride and sialon ceramics
• Silicon nitride and sialon ceramics are engineering ceramic materials which are characterized by an excellent combination of mechanical properties (stiffness, strength, hardness and toughness) ; properties which can, in theory, be retained to very high (>1000°C) temperatures.
• the sialons are based on compositions containing the elements Si, Al, 0, N, hence the acronym.
• the most successful commercial sialon ( / 9-sialon) has the -Si_N. crystal structure, but with some of the silicon atoms replaced by aluminium atoms and the same number of nitrogen atoms replaced by oxygen atoms to give a general composition of the type where 0 ⁇ Z ⁇ 4.2.
• the other common sialon phases are O-sialon, which has the general composition Si__ ⁇ Al ⁇ O ⁇ N , where
• ⁇ -sialon which has the general composition M v XSi_1,2_- m m-nAlm+,nOnN1.
• c 6-n where m represents the number of Si-N bonds replaced by Al-N per unit cell, n represents the number of Si-N bonds replaced by Al-0 per unit cell, 0 ⁇ X ⁇ 2, and M is one of the cations Li,Mg,Ca,Y and rare earths
• O-Sialon has an expanded silicon oxynitride (Si N.O) crystal structure and ⁇ -sialon has an expanded ⁇ -Si_N. crystal structure.
• ⁇ -Sialon is a strong engineering ceramic with good oxidation resistance and creep resistance up to 1300 C.
• the 0-sialon has approximately two thirds the strength of fl-sialon, but has very much improved oxidation resistance up to 1400 C.
• ⁇ -Sialon has excellent hardness, but slightly worse strength, toughness and oxidation resistance than the other two sialons.
• Sialons are usually formed by mixing Si-N. ,A1 2 0_ ,A1N powders with one or more metal oxides (often including Y p O_) . compacting the powder to the desired shape, and then firing the component at 1750 C for a few hours.
• the function of the metal oxide is to react with the silica (which is always present on the surface of each silicon nitride particle) and the alumina (which is always present on the surface of each aluminium nitride particle) , to form a liquid phase which dissolves the reactants and precipitates the product.
• the liquid phase (which still contains dissolved nitrogen) , cools to form a glass between the sialon grains.
• a Y ? 0 densified 3-sialon contains about 15 volume percent of Y-Si-Al-O-N glass and 85 volume percent / 9-sialon. At temperatures above -950°C this glass begins to soften and the strength decreases.
• the material can be heat treated at -1300 C to crystallise the glass. In the case of 0-sialon containing Y-Si-Al-O-N glass, the glass crystallises to give Y A O.. (yttro garnet or YAG) and a small amount of additional ⁇ -sialon.
• the present invention provides a method for the production of nitrogen ceramic materials which comprises adding to the starting powdered ceramic material an oxide of a metal which has a boiling point of less than 1700°C, or a mixture of such oxides, sintering the powder at a te perature of up to 1800°C and post-sintering the product in a reducing atmosphere under a reduced pressure at a temperature of up to 1700 C, the said metal oxide being included in the mixture in an amount sufficient to densify the material and then to remove the glassy phase from the grain boundaries of the nitrogen ceramic material.
• the method of the present invention enables dense, refractory, silicon nitride and sialon ceramics to be produced which have good chemical and mechanical properties which are retained to significantly higher temperatures than current commercial materials which, because they contain M-Si-O-N or M-Si-Al-O-N glassy or crystalline boundary phases, fail at temperatures below 1400°C.
• the method of the present invention also enables essentially pure, fully dense ⁇ -sialon, -sialon, O-sialon and ⁇ -silicon nitride to be produced which materials could not previously be prepared by the methods known in the art.
• silicon nitride produced by chemical vapour deposition is essentially pure it is always ⁇ -Si N. and it is not possible to produce -Si.N. by this route.
• Other routes for the preparation of silicon nitride have an additional grain boundary phase and thus are not essentially pure.
• the metal oxide having a boiling point of less than 1700°C, which is added to the powdered ceramic starting material, is totally removed.
• the present invention includes within its scope an essentially pure, fully dense / 9-sialon, O-sialon or ⁇ -silicon nitride which has a density of at least 98.0% and a purity of above 99% of the theoretical.
• This material has substantially no grain boundary phase material therein.
• the invention includes within its scope an essentially pure, fully dense 9-sialon or O-sialon containing substantially only silicon, aluminium, oxygen and nitrogen which has a density of at least 99.5% and a purity of above 99% of the theoretical.
• the invention also includes within its scope an essentially pure, fully dense ⁇ -silicon nitride containing substantially only silicon and nitrogen which has a density of at least 98.5% and a purity of substantially 100% of the theoretical.
• the invention further includes within its scope an essentially pure, fully dense mixture of ⁇ -sialon and / 9-sialon comprising from 5 to 99% by weight of / 9-sialon which has a density of at least 98% and a purity of at least 99% of the theoretical.
• the invention still further includes within its scope essentially pure, fully dense mixture of ⁇ -sialon and O-sialon comprising from 5 to 99% by weight of ⁇ -sialon which has a density of at least 98% and a purity of at least 99% of the theoretical.
• the amount of ⁇ -sialon in the above mixed compositions is preferably in the range of from 40 to 60% by weight.
• the preferred nitrogen ceramic materials used in the method of the present invention are silicon nitride, ⁇ , ⁇ or O-sialon, or mixtures thereof.
• the metal oxide is preferably Li_0,MgO or SrO, these metals having boiling points of 1324°, 1100° and 1381 C, respectively.
• Less preferred metal oxides for use in the invention are Na_0, CaO or Yb_0_ these metals having boiling points of 882°, 1484° and 1194°C, respectively.
• the reducing atmosphere under which the reduced pressure post-sintering is carried out is preferably provided by using a carbon resistance furnace.
• a carbon resistance furnace When a carbon resistance furnace is used the reducing species is carbon monoxide and the reaction proceeds according to the following equation:
• M represents any metal species which has a boiling point of less than 1700 C.
• the carbon dioxide then reacts with hot graphite components in the furnace to produce further carbon monoxide.
• the carbon environment also reduces the partial pressure of oxygen in the gas atmosphere to that specified by the equilibrium
• the reduced pressure post-sintering is preferably carried out by placing the sample in a carbon crucible and surrounding the sample with a packing bed of powdered carbon or powdered boron nitride, the packing material preventing the formation of Sic by reaction between Si_N. and C above 1600 C and preventing the loss of volatiles from the outside of the samples.
• the metal oxide, MO is generally added to the nitrogen ceramic material in the minimum amount needed for densification.
• MgO is used as the additive it is generally added in an amount of less than 2% by weight and preferably less than 1% by weight. It is beneficial to use the minimum amount of additive (consistent with achieving full density) , because after the reduced pressure heat treatment there is some residual porosity, and the less grain boundary glass, the smaller is the residual porosity.
• the mixture of the starting powder and metal oxide is preferably hot pressed, pressureless sintered, gas pressure sintered or hot-isostatically pressed to form a dense sample prior to the reduced pressure heat treatment.
• Hot pressing is the preferred technique for silicon nitride ceramic materials and pressureless sintering for sialon materials.
• the reduced pressure post-sintering step is preferably carried out under a partial vacuum, and more preferably under a partial vacuum pressure of 10 ⁇ atmospheres, or below, which may be achieved, for example, by the use of a rotary pump.
• the method of the present invention provides silicon nitride and sialon ceramics with improved high temperature properties, such as creep resistance, oxidation resistance and hot hardness.
• the reduced pressure treatment may result in some decrease in strength and also some reduction in toughness, but at acceptable levels.
• the hot hardness of the material is good and it is anticipated that the materials retain about 50% of their room temperature hardness at 1400 C.
• Figure 1 is a graph showing the creep behaviour of a 1% MgO hot pressed typical commercial silicon nitride (containing a high level of iron impurities) in which trace (a) shows the creep resistance for a sample as received, trace (b) shows the creep resistance for a sample after heat treatment at 1250 C and trace (c) shows the creep resistance for a sample after vacuum heat treatment at 1600°C for 4 hours.
• trace (a) shows the creep resistance for a sample as received
• trace (b) shows the creep resistance for a sample after heat treatment at 1250 C
• trace (c) shows the creep resistance for a sample after vacuum heat treatment at 1600°C for 4 hours.
• the improvement in the creep resistance of the vacuum heat treated sample is significant.
• Figure 2 is a graph illustrating the microhardness of silicon nitride as a function of the MgO additive content.
• the two zero additive points correspond to the 1% and 2% MgO materials after vacuum heat treatment.
• the vacuum heat treatment results in a significant increase in microhardness.
• Figure 3 shows the EDX analyses of sintered and vacuum heat treated 1% MgO densified ⁇ -sialon as (a) hot-pressed and (b) after 3 hours vacuum heat treatment at 1625°C.
• Figure 4 shows the EDX analyses of sintered and vacuum heat treated 2.8% CaO densified 9-sialon as (a) hot-pressed and (b) after 3 hours vacuum heat treatment at 1575°C.
• Figure 5 shows the EDX analyses of sintered and vacuum heat treated 2% MgO densified ⁇ -silicon nitride (a) hot-pressed and (b) after 3 hours vacuum heat treatment.
• FIGS 3, 4 and 5 show that the metals are lost from the samples on vacuum heat treatment.
• Magnesium oxide was added in amounts of l%.or 2% by weight to silicon nitride or / 9-sialon and the mixture hot pressed or pressureless sintered, respectively.
• a sample of the pressed mixture 5mm in thickness was placed in a carbon crucible and surrounded with a packing bed of boron nitride. The mixture was then heat treated at a temperature of 1575°C for silicon nitride, or 1625°C for / 9-sialon, in a carbon resistance furnace under a vacuum of 10 atmospheres for periods of time of 1,
• Oxidation resistance tests were performed at 1250°, 1400° and 1650°C for 24 hours in air for samples of ⁇ -sialon and hot pressed silicon nitride which, with the addition of 1% by weight of MgO, had been subjected to vacuum heat treatment in accordance with the present invention. The results were compared with the oxidation resistance at the same temperatures for samples of a commercial 201 SYALON material.

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• 1992
  • 1992-10-01 GB GB929220695A patent/GB9220695D0/en active Pending
• 1993
  • 1993-09-30 JP JP6508842A patent/JPH08508458A/ja active Pending
  • 1993-09-30 EP EP93921028A patent/EP0663894A1/de not_active Withdrawn
  • 1993-09-30 WO PCT/GB1993/002032 patent/WO1994007811A1/en not_active Application Discontinuation

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