CERAMIC PRODUCTION PROCESS

Abstract: A process for the production of O'-SiAlON ceramics from silicon metal, nitrogen and clay, the process comprising heating the silicon metal and the clay in a flowing nitrogen atmosphere to a temperature sufficient to react the components to form O'-SiAlON and wherein the clay participates in the reaction as a source of aluminium and silicon.

Description: CERAMIC PRODUCTION PROCESS Technical Field The invention comprises a process for the production of O'-SiAlON's and composite ceramic materials containing O'-SiAlON's. Background Art The term SiAlON, or silicon aluminium oxynitride, encompasses a family of compounds or phases comprised of the elements: silicon, aluminium, oxygen and nitrogen. Each phase is described by a composition range for which that particular structure is stable. O'-SiAlON is stable over the composition range: Si 2 . x Al x 0 1+x N 2 . x where 0 < x < 0.4. O'-SiAlON has a similar structure to silicon oxynitride with equal amounts of aluminium and oxygen substituting for silicon and nitrogen respectively into the silicon oxynitride structure. The amounts of aluminium and oxygen which can be substituted into the structure increase with temperature. At 1600°C, x can be as high as 0.2. At 1900°C, x can be as high as 0.4. SiAlON's are advanced ceramic materials which exhibit useful properties such as high strength and hardness, low density, wear resistance and corrosion resistance, and are able to retain these properties at high temperatures. SiAlON's are used in refractories and for a variety of engineering applications such as cutting tools, spray nozzles and pump seals. The exact properties of a given SiAlON depend on the chemical composition and fabrication variables, such as purity, grain size and shape, and the method of fabrication. O'-SiAlON has similar properties to silicon oxynitride which include excellent resistance to oxidation and thermal shock. Silicon oxynitride is commonly used as a refractory material. SiAlON's and O'-SiAlON's are known compounds and common methods for producing them include: (i) Reaction Sintering. Mixtures of two or more of the following: Si 3 N 4 , Si0 2 , Si 2 N 2 0, A1 2 0 3 and A1N, are sintered at > 1600°C under a nitrogen atmosphere, usually in the presence of a rare earth sintering aid such as Y 0 3 or Ce0 2 . This process involves expensive raw materials and high temperatures, but allows good control over the composition and purity of the product. (ii) Carbothermal Reduction. Aluminosilicate materials are blended with carbon and fired at > 1350°C under a flowing nitrogen atmosphere. This process is described as carbothermal reduction because the carbon acts by reducing the aluminosilicate, allowing nitridation to occur. This process involves cheap raw materials and lower firing temperatures than for reaction sintering but impurities in the aluminosilicate can degrade the properties of the product. The process is difficult to control because it involves stopping a reaction at a specific point prior to completion. (iii) Combustion Synthesis. A mixture containing silicon metal powder is ignited under a nitrogen atmosphere. The energy evolved by this strongly exothermic nitridation of silicon propagates a reaction front through the reaction mixture. This method is very rapid and energy efficient but is difficult to control. Methods (ii) and (iii) both yield SiAlON powders which must then be formed and sintered to obtain a ceramic body. Method (i) is the most commonly used method for preparing O'-SiAlON. As is apparent from the above known methods, in order to get good control over the composition and purity of the produα expensive raw materials and/or extreme reaction conditions are required. European patent application EP 0153000 to Kennecott Corporation discloses a bonded material consisting of granular silicon carbide and a bonding phase comprising Si 3 N 4 which has been modified by the presence of oxygen and aluminium. Also disclosed is a method for the manufacture of the bonded material which includes the use of bentonite clay as a temporary binder. The amount of this bentonite clay in the raw starting material is disclosed as being about 0.5% by weight. The starting materials are disclosed as being silicon carbide, aluminium powder, silicon powder plus optional processing aids and temporary binders. The use of temporary binders, and thus the bentonite clay, is optional. There is no disclosure of the use of a clay material as a basic aluminium and silicon source, nor is there disclosure of the use of clay to facilitate slipcasting or extrusion. Canadian patent 1,156,685 to Dresser Corporation is directed to a method for producing nitride bonded refractory shapes in situ from a mixture comprising silicon, crude clay, and a graded refractory aggregate. The intention is to form nitride phases in situ to avoid the cost of purchasing silicon nitride for example. The amount of crude clay used in the process is stated as being between 1 and 5% and the refractory aggregate may be fire clay amongst other options. The refractory aggregate used in the process is a non-reactive bulking agent and the crude clay facilitates densification during pressing and facilitates the formation of ϊ' -SiAlON and silicon oxynitride. The examples (see Table 1) do not form a SiAlON when reacting the basic components together. There is no disclosure of the production of O'-SiAlON. There is no disclosure of the intention to form O'-SiAlON as the major or sole product. Clay is deliberately added at very low levels and there is no intention to use clay as a basic source of silicon and aluminium in the production of O'-SiAlON or to facilitate slipcasting or extruding. United States patent No 4360506 to Societe Europeenne des Produits Refractaries. This United States patent discloses a method for producing j3-SiAlON's by heating in a nitrogen atmosphere agglomerated elements obtained by drying a paste comprising a silico-aluminous material, carbon, and fine particles of a ligneous material. The silico-aluminous material can be a clay such as a kaolin clay. It is essential to the process that carbon, preferably carbon black, and a ligneous material, such as sawdust be used. There is no disclosure of the use of silicon metal and the process relies on the reduction of the silica-aluminous material by carbon. There is no disclosure of the intention to form O'-SiAlON as a major or sole product. European patent application 0317980 to The Norton Company discloses a process for the manufacture of a refractory material by mixing appropriate amounts of silicon metal powder, fine reactive alumina, a fine silica source (eg bentonite clay), a binder and a liquid dispersant, forming a shape and heating the shaped body in a nitrogen atmosphere. The bentonite clay is disclosed as being used in only a 0.5-2 w/o amount. Fine reactive alumina is an essential component of the process. There is no disclosure of the clay component being an essential part of the reaction sequence or as the source of the alumina component. The process of the present invention relies on the use of a clay material as a basic source of process components and the ability of the clay material to react with the other process components to form O'-SiAlON under suitable reaction conditions. Further, the use of clay in the process facilitates the formation of shaped ceramic bodies comprising O'-SiAlON. It is an object of the invention to provide an improved process for the manufaαure of O'-SiAlON ceramic materials and composite ceramic materials containing O'- SiAlON. Summary of the Invention In broad terms the invention in a first aspeα comprises a process for the produαion of O'-SiAlON from a mixture of silicon metal, nitrogen and clay, wherein the process comprises heating the silicon metal and clay in a flowing nitrogen atmosphere to a temperature sufficient to reaα the components to form O'-SiAlON and wherein the clay participates in the reaαion as a source of aluminium and silicon. In broad terms the invention in a second aspeα comprises a process for the produαion of O'-SiAlON from a mixture of silicon metal, nitrogen and clay, wherein the process comprises dehydroxylating the clay, mixing the dehydroxylated clay with the silicon metal, and heating the combination under a flowing nitrogen atmosphere to a temperature sufficient to reaα the mixture to form O'-SiAlON and wherein the dehydroxylated clay participates in the reaαion as a source of aluminium and silicon. Preferably the clay is the sole source of aluminium. Preferably silica is included in the mixture. Preferably the clay is a hydrated layer aluminosilicate. Preferably the clay is seleαed from kaolin, montmorillonite, halloysite, bentonite and pyrophyllite clays. Preferably the clay is dehydroxylated by precalcining. Preferably the clay is dehydroxylated by heating to a temperature between about 500°C and about 800°C. Preferably the components of the mixture are present as fine powders. Preferably the mixture contains between about 5% and about 60% by weight of clay and more preferably between 10% to 40% by weight of clay. Preferably the mixture contains, by weight, about 20% to 50% clay, 0% to about 25% silica and about 40% to about 60% silicon metal and, more preferably, 30%-40% clay, 10%-20% silica, and 40%-55% silicon metal. Preferably the flowing N 2 atmosphere comprises < 0.5% oxygen and < 0.5% water vapour, and more preferably < 10ppm oxygen and <25ppm water vapour. Preferably the N 2 flow rate is between about 3 and about 20 ml. min "1 . g "1 by weight of silicon in the sample, and more preferably between 3 and 15 ml.min "1 .g '1 . Preferably the mixture is heated to between about 1100°C and about 1900°C, more preferably between 1300°C and 1900°C, more preferably between 1300°C and 1600°C and most preferably to 1450°C to form the O'-SiAlON. Preferably the components are heated at a rate of up to about 10°C per minute, more preferably between about 0.2°C and about 10°C per minute, more preferably between 1°C and 7°C per minute, more preferably between 1°C and 6°C per minute, and most preferably between 2 and 5°C per minute. Preferably the components are held at the required temperature until the reaαion is complete, preferably between about 4 and about 60 hours and more preferably between about 4 and 12 hours. Preferably additive compounds are included to enhance the reaαion and/or to promote sintering. Preferably the additive compounds are selected from Y 2 0 3 , Fe 3 0 4 , Zr0 2 , ZrSi0 4 , MgO and /3-SiAlON. Preferably the produα formed contains greater than 75% O'-SiAlON by weight of product and more preferably greater than 80% O'-SiAlON. In more limited terms a third aspect of the invention comprises a process for the produαion of O'-SiAlON from a component mixture comprising, by weight, 40%- 60% silicon metal, 20%-50% clay, and 0%-25% silica, the process comprising the steps of: (a) dehydroxylating the clay prior to inclusion in the component mixture; (b) heating the component mixture at a rate of 1°C to 6°C per minute, to a temperature of between substantially 1300°C to 1900°C under a flowing N 2 atmosphere having preferably < 0.5% oxygen and preferably < 0.5% water vapour and more preferably < 10 ppm oxygen and <25 ppm water vapour; (c) holding the temperature between 1300°C and 1900°C for up to 12 hours; and (d) recovering the produα. In broad terms the invention in a fourth aspeα comprises a process for the produαion of a composite ceramic material including O'-SiAlON from a mixture of components comprising a ceramic material and an O'-SiAlON forming component combination of silicon metal, clay and nitrogen wherein the process comprises heating the ceramic material, silicon metal and clay in a flowing nitrogen atmosphere to a temperature sufficient to form the O'-SiAlON composite ceramic and wherein the clay participates in the reaαion as a source of silicon and aluminium. Preferably the component combination further comprises silica. Preferably the clay is the sole source of aluminium in the manufacture of the O'-SiAlON. Preferably the ceramic material included in the mixture is selected from silicon carbide (SiC), alumina (A1 2 0 3 ), silicon nitride (Si 3 N 4 ), SiAlON, zirconia (Zr0 2 ), zircon (ZrSi0 4 ) and silica (Si0 2 ). Preferably the ceramic material included in the mixture is coarser than the other mixture components which reaα to form the O'-SiAlON. Preferably the ceramic material included in the mixture will constitute up to 75% by weight of the mixture and more preferably between about 40% and about 70% by weight of the mixture. In more limited terms a fifth aspeα of the invention comprises a process for the produαion of a composite ceramic including O'-SiAlON from a mixture of components comprising, by weight, up to 75% of a ceramic material and 25% or more of an O'-SiAlON forming mixture, wherein the O'-SiAlON forming mixture comprises, by weight, 40%-60% silicon metal, 20%-60% clay, and 10%-25% silica, the process comprising the steps of: (a) heating the component mixture at a rate of between substantially 1.0°C to 6°C per minute, to a temperature of between substantially 1300°C to 1900°C under a flowing N 2 atmosphere having < 0.5% oxygen and < 0.5% water vapour; (b) holding the temperature between 1300°C and 1900°C for up to 12 hours; and (c) recovering the produα. Description of the Drawings The attached Figures show X-ray diffraction patterns of O'-SiAlON produαs formed by the process of the invention. The standard O'-SiAlON and SiC X-ray diffraαion XRD patterns were supplied by the International Centre for Diffraαion Data, USA and the produα X-ray diffraαion patterns were obtained from a Phillips 1700 Series Diffractometer controlled by Phillips APD1700 software. In the Figures: Fig 1 shows a comparison between the X-ray diffraαion pattern for the produα formed by the process of Example 2 and a standard O'-SiAlON pattern; and Fig 2 shows a comparison between the X-ray diffraαive pattern for the composite product formed by the process of Example 5 and standard O'-SiAlON and SiC patterns. Fig 3 shows the mass curves of the O'-SiAlON reaαion using raw and dehydroxylated clays. Figs 4 and 5 show XRD peak intensity v temperature for the O'-SiAlON reaαion. Fig 6 shows the effeα of the heating rate on the O'-SiAlON reaαion profile. Fig 7 shows XRD peak intensity v heating rate of the produαs of the O'-SiAlON reaαion in Example 8. Fig 8 shows the effeα of increasing the SiC content in the produαion of SiC/O'- SiAlON composites produced in Example 9. Fig 9(a) and (b) show XRD analyses of the produαs of the reaαions in Fig 8. Fig 10 (a) (b) and (c) show behaviour diagrams for the SiAlON family of compounds. Fig 11 shows XRD results of O'-SiAlON formed in Example 10 and plotted in Fig 10. Figs 12 and 13 show the effeα of additives on O'-SiAlON produαion. Fig 14 shows the XRD analysis for (a) O'-SiAlON fired with no Y 2 0 3 and (b) O'-SiAlON fired with 2wt% Y 2 0 3 . Figs 15 and 16 show the effeα of a second ceramic component in the produαion of O'-SiAlON composite produαs. Fig 17 shows the XRF analyses of the samples processed in Example 16. Fig 18 shows the composition of O'-SiAlON reaαion mixtures prepared for the various clay minerals in Example 16, the weight changes during reaαion, and XRD analyses of the products. Fig 19 shows the effeα of firing temperature on the produαion of O'-SiAlON from Example 17. Detailed Description of the Invention The process of the present invention is a novel process directed to the preparation of O'-SiAlON from silicon metal, clay and silica (Si0 2 ). The raw material should be in fine powder form. The clay may be dehydroxylated prior to use, however retention of the clay in its natural plastic form will allow the mixture to be more readily formed into a desired shape prior to firing. The raw materials may be blended by standard techniques such as ball milling or the like as will be known in the art. Following blending, if the clay is retained in its natural form, the raw materials can be fabricated into the desired shape by traditional methods of pressing, slip casting, or extruding and the more advanced methods including isostatic pressing and injeαion moulding as is known in the art. These methods may involve the use of pressing aids, binders, dispersants and lubricants for example. The mixture is then placed in a furnace or kiln or the like and heated under a flowing nitrogen atmosphere to temperatures greater than 1300°C at an appropriate rate and held at this temperature until the reaαion is complete. Four to eight hours is generally sufficient although longer times may be required at lower temperatures. For commercial processes, to ensure complete reaαion the sample may be held at temperature for times as long as 60 hours or more, although it is likely 12 hours will probably be sufficient. This will depend on a number of factors, such as the size of the sample and temperature and atmospheric variations within the furnace, as will be apparant to a person skilled in the art. It may also be beneficial to hold the material at a lower temperature than desired to form the O'-SiAlON for a period of up to 8 hours. This will result in a two tiered firing regime which may be desirable commercially to allow completion of the surface nitridation reaction. This lower holding temperature will preferably be between 1100°C and 1300°C. The nitrogen flow rate should be as low as possible, but should be sufficient to replace nitrogen consumed by the reaαion, and maintain an atmosphere with preferably < 0.5% oxygen and preferably < 5% water vapour inside the furnace or kiln. To form very pure O'-SiAlON the flowing nitrogen atmosphere should have as low a level of oxygen and water vapour as possible. Levels of 10 ppm oxygen and 25 ppm water vapour or below, are preferred. For the sample sizes as used in the examples, nitrogen flow rates of between about 3 and 20 ml. min "1 . g "1 by weight of silicon in the sample were found to suffice. The oxygen and water vapour content of the atmosphere should be kept to a minimum as these faαors can affeα the process by attacking the unreaαed silicon powder. During the reaαion the nitrogen in the furnace atmosphere becomes incorporated into the produα via a nitridation reaαion giving an increase in density. The produα formed is primarily O'-SiAlON although small amounts of silicon nitride, mullite, and other SiAlON phases may also be formed. It has been found that dehydroxylation of the clay prior to mixing with the silicon metal is beneficial to the produαion of O'-SiAlON in pure form. For example at about 500-800°C, clay undergoes this dehydroxylation reaction and forms a reaαive intermediate as is well known in the art. This dehydroxylation will also occur when the process is carried out in a single firing (ie without dehydroxylation of the clay prior to mixing with the other process components). For example, if kaolin clay is used in the process then a reaαive amorphous intermediate is formed which is commonly referred to as meta-kaolin. This amorphous intermediate reaαs with silicon metal and nitrogen from the flowing nitrogen atmosphere, to form silicon aluminium oxynitrides (SiAlON's) under suitable conditions. Formation of the reaαive clay intermediate facilitates the use of relatively low temperatures in the process. The dehydroxylation of the clay prior to mixing with the other raw materials may be achieved by methods such as precalcining as will be known in the art. If the dehydroxylation step is not done prior to mixing the clay with the silicon metal and silica it appears that the water released as the clay dehydroxylates on heating can partially prevent the silicon from reaαing (see Example 6). While the removal of water from the clay prior to mixing with the other components in the mixture will enhance the produαion of the O'-SiAlON produα this step is not essential to the process. Dehydroxylating the clay prior to mixing increases the purity of the O'-SiAlON formed in the process however the benefits of clay with regard to slip-casting and extruding for example, will no longer be available. In the process of the invention the clay material provides a source of silicon and aluminium for the reaαion. While it is possible to include other sources of aluminium, the process of the present invention does not require this and the clay used is preferably the sole source of aluminium for the reaαion. As a result of the extensive use of clay the provision of raw material for the process is cheaper than for prior art processes and the complexity of the procedures involved in producing O'- SiAlON produαs is lowered. Some reaαion between the reaαion components occurs during the heating stage, and therefore the holding step for up to eight hours is optional. However, the reaαion accelerates between 1400°C and 1450°C as the silicon begins to melt (at approximately 1414°C). Holding the furnace at a temperature greater than 1450°C is also optional but may be used to force the reaαion to completion, or to sinter the body to obtain better densities. A heating rate of between 1°C per minute and 10°C per minute has been found to be suitable however the heating rate should preferably be between 1°C and 7°C per minute. More preferably the heating rate should be between 1°C per minute and 6°C per minute and most preferably between 2°C and 5°C per minute. The process will however work at heating rates as low as 0.2°C per minute and this may in faα occur as, on a commercial scale, large furnaces can be slow to heat resulting in such lower heating rates. The preferred temperature range to which the mixture of components is heated is between 1300°C and 1600°C as, at higher temperatures, specialised furnaces or kilns may be required. If impurities are present in the silicon then it's melting point may be lowered and in such cases reaαion may proceed at lower temperatures. Temperatures as low as about 1100°C are envisaged as being possible. For example, in the case of Fe particularly, there is a euteαic between Fe and Si at about 1190°C which would allow the Si to melt at the lower temperature and thus allow the reaαion to proceed. While it has been found that natural clay produαs containing iron impurities may be usefully used in the process of the invention, the presence of Ca, Na, and Ba impurities have been found to hinder the reaαion. Addition of small amounts of Zr0 2 also permits the reaαion to proceed at lower temperatures. As will be readily apparent to a person skilled in the art, the type of furnace or kiln used must be able to maintain a controlled internal atmosphere at the temperatures required. Any type of furnace or kiln which is capable of this may be used. Ceramic or ceramic composite bodies formed and reaαed at 1300-1600°C can be sintered at higher temperatures (1600-1900°C) to increase the density and reduce the porosity of the produα. This sintering can be performed in a second firing or as a second, higher temperature, stage of a single firing step. Sintering will be accompanied by an amount of shrinkage in the produα. Examples of reaαions to produce O'-SiAlON (x=0.2) from New Zealand China Clays (NZCC) premium grade halloysite and BDH light kaolin are shown in equations in (i) and (ii) respeαively. The amount of each raw material must be balanced to provide the correct Si:Al:0:N ratio for the desired O'-SiAlON as will be known in the art. Si0 2 is required to achieve the appropriate stoichiometry. In some cases where clays are particularly siliceous or contain large amounts of native free silica, it may not be necessary to add silica to achieve the appropriate stoichiometry, as in the case of the pyrophyllite, bentonite and rheogel clays in Example 16. -2H 2 0,+N 2 (1) 2(A1 2 0 3 . 2.41 Si0 2 .2H 2 0) + 27 Si + 4.18 Si0 2 = 2Si 18 Al 2 0 12 N 18 NZCC halloysite clay heat (including native free Si0 2 ) -2H 2 0,+N 2 (2) 2(A1 2 0 3 . 2.09 Si0 2 .2H 2 0) + 27 Si + 4.82 Si0 2 = 2Si 18 Al 2 0 12 N 18 BDH light kaolin clay heat (including native free Si0 2 ) If the correct balance of raw materials is used then the produαion of O'-SiAlON in the resultant ceramic is maximised. This balance of material will be able to be calculated readily by a person skilled in the art and will depend largely on the type of clay used in the reaction. The process of the present invention can produce a produα containing over 75% O'-SiAlON and is capable of producing a produα containing over 80% of O'-SiAlON. The percentage of clay used can be as low as 5% by weight and, in such a case, the proportions by weight of silica and silicon metal will be approximately 40% and 55% respeαively. The preferred percentage makeup of the starting component mixture is however between 20%-45% clay, 10%-25% silica and 40%-60% silicon metal. As will be apparent to a person skilled in the art a variety of clays may be used in the process. Clays that can be used are the hydrated layer aluminosilicates generally. The preferred clays are the kaolin clays however the pyrophyllite and the montmorillonite clays, such as bentonite, may also be used. Other types of clay, such as illites for example, may also be used however most will contain a variety of impurities such as K, Na, Ca, Mg and Fe together with the aluminosilicate content. These impurities may detrimentally affeα the purity of the SiAlON produα formed by the process of the invention. In some cases however, for example with Mg and Fe, the impurities may have positive effect. The process can also be used to fabricate composite ceramics containing O'-SiAlON. In these processes the O'-SiAlON is used to bond together grains of other ceramic materials such as silicon carbide (SiC) (see Example 5), alumina (Al 2 0 3 ), silicon nitride (Si 3 N 4 ), SiAlON, zirconia (Zr0 2 ), zirconia (ZrSi0 4 ) or silica (Si0 2 ). These bonded materials take little or no part in the reaαion chemistry. They will preferably be coarser than the raw materials which reaα to form the bonding phase, and will preferably constitute up to 75% of the starting mixture and thus of the resultant fired ceramic. Preferably the additional ceramic will constitute between 40% and 70% of the mixture. The additional ceramic is preferably coarser in order to get better packing of the grains prior to firing which allows higher fired densities to be obtained. Further, as the additional ceramic is coarser it is less likely to influence the O'-SiAlON reaαion. This is particularly relevant in the case of silicon carbide and silica. The additional ceramic material is bonded by a matrix of O'-SiAlON formed by the other components in the starting mixture (ie the clay, silica (if present), and silicon). These other components will therefore constitute between 25% and 99% of the total starting mixture and will be present in the preferred percentage amounts that have been discussed previously. When proceeding with the process of manufaαuring a composite ceramic containing O'-SiAlON there appears to be no significant benefit in dehydroxylating the clay material used prior to mixing the raw materials. Dehydroxylation of the clay material prior to manufacture of the non-composite O'-SiAlON ceramic, as has been discussed previously, enhances the produαion of the O'-SiAlON ceramic by removing water which can attack the silicon and thus detrimentally affeα the process. It is thought that the water content of the clay has less effeα when manufaαuring the composite ceramic materials due to a dilution effeα based on the presence of additional materials (ie the additional grains of the other ceramic materials). When using lower amounts of additional ceramic however, dehydroxylation of the clay prior to mixing may be of benefit. This can be seen in Example 9 and in Figures 8 and 9a. The natural properties of the clay material can thus be more readily utilised to preform the desired shape of the composite ceramic prior to firing. The reaαion to form the non-composite O'-SiAlON is generally accompanied by an amount of shrinkage when the natural clay material is used in the process. When the clay material has been dehydroxylated prior to use in the process such shrinkage is reduced. When the process is used to form the composite ceramic material and natural (non-dehydroxylated) clay is used this shrinkage can become negligible allowing near nett size shapes to be formed. As a result of the use of natural clay in the process there is a great flexibility in the shape and size of ceramic components which can be produced by the process of the present invention. The method of the present invention is capable of producing either ceramic bodies or ceramic powder containing the O'-SiAlON in a single firing step. As will be apparent when clay material is dehydroxylated prior to use the process will then have two firing steps. The first to dehydroxylate the clay and the second to form the ceramic material containing O'-SiAlON. To make a ceramic powder the reaαion will proceed without an emphasis on the densification of the resulted ceramic. For example, the starting materials can be formed into pellets, reaαed to form a soft ceramic pellet of O'- SiAlON which is then ground into a powder. This may be used as a supply of O'- SiAlON powder for use in other processes. For example the powder could be formed and sintered with or without sintering aids such as Y 2 0 3 or the like, to form fully densified ceramic bodies. Various additives can be used in order to enhance the process of the invention or to promote sintering. It has been found that iron oxides (such as Fe 3 0 4 ) zirconia (Zr0 2 ), zircon (ZrSi0 4 ) and /3-SiAlON promote the reaαion. Yttria (Y 2 0 3 ) is known to be a useful sintering aid for O'-SiAlON. Examples EXAMPLE 1 A lOg mixture of: 36.9% New Zealand China Clays Premium Grade Halloysite Clay; 49.1% Permascand 4D Silicon; and 14.0% Superfine Quartz Powder (supplied by Commercial Minerals Ltd); was blended by ball-milling with ca. 400 g of 10 mm diameter Si 3 N 4 balls and 70 g of hexane in a one litre high density polyethylene (HDPE) bottle for 20 hours at ca. 150 rpm. The hexane solvent was removed by rotary evaporation. Samples of powder were blended with 5% oleic acid to aα as a pressing aid and binder. Ethanol was used to disperse the acid, and was later allowed to evaporate off under ambient conditions. The powder was brushed through a 295 μm sieve to granulate it, and then pressed at ca. 75 MPa in a 20 mm diameter die. The pressed discs were heated at 0.5°C.min '1 to 400°C for 30 minutes under nitrogen atmosphere to remove the oleic acid. Two 1.3 g discs were fired in a tube furnace on a bed of sialon granules under an atmosphere of "oxygen-free" nitrogen (<10 ppm 0 2 , < 25 ppm H a O, supplied by BOC) - flowing at ca 50 ml min "1 . The samples were heated at 2°C.min *1 to 1450°C and held at that temperature for 2 hours. The discs increased in mass by ca. 18% during the firing, and an analysis of the produαs by X-ray powder diffraαion (XRD) revealed primarily O'-SiAlON with traces of β-SiAlON and X-Phase SiAlON. EXAMPLE 2 A mixture of: 30.7% dehydroxylated BDH Light Kaolin Clay (dehydroxylated at 800°C for one hour); 50.1% Permascand 4D Silicon; and 19.2% Superfine Quartz Powder (supplied by Commercial Minerals Ltd); was prepared and fired as in Example 1. The discs increased in mass by ca. 11% during the firing, and a linear shrinkage of 4.5% was measured. An analysis of the produαs by X-ray powder diffraαion (XRD) (see Fig 1) revealed primarily O'-SiAlON with a trace of X-Phase SiAlON. The bulk density and open porosity of the fired pellets were measured by evacuation and water saturation: bulk density = 2.06 g.cm "3 (74% of theoretical) open porosity = 26.8% EXAMPLE 3 A lOg mixture of: 30.4% dehydroxylated BDH Light Kaolin Clay (dehydroxylated at 800°C for one hour); 49.6% Permascand 4D Silicon; 19.0% Superfine Quartz Powder (supplied by Commercial Minerals Ltd); and 1.0% Sigma Yttrium Oxide (Y 2 O a ); was prepared and fired as in Example 1. The discs increased in mass by ca. 11% during the firing, and a linear shrinkage of 10.8% was measured. An analysis of the produαs by X-ray powder diffraαion (XRD) revealed primarily O'-SiAlON with β-Si 3 N 4 and a trace of X-Phase SiAlON. The bulk density and open porosity of the fired pellets were measured by evacuation and water saturation in water: bulk density = 2.51 g.cm "3 open porosity = 9.0% EXAMPLE 4 A mixture of: 30.4% dehydroxylated BDH Light Kaolin Clay (dehydroxylated at 800°C for one hour); 49.6% Permascand 4D Silicon; 19.0% Superfine Quartz Powder (supplied by Commercial Minerals Ltd); and 1.0% Pronalys AR Magnesium Oxide (MgO); was prepared and fired as in Example 1. The discs decreased in mass by ca. 1.5% during the firing, and a linear shrinkage of 10.8% was measured. An analysis of the produαs by X-ray powder diffraαion (XRD) revealed primarily O'-SiAlON with traces of β-Si 3 N 4 and X-Phase SiAlON. The bulk density and open porosity of the fired pellets were measured by evacuation and water saturation: bulk density = 2.39 g.cm '3 open porosity = 4.7% EXAMPLE 5 This example demonstrates the fabrication of a composite ceramic produα (SiC/SiAlON) formed by slip casting. The proportions of clay, silicon and silica used in the starting mixture being sufficient to form O'- SiAlON which bonds to the additional ceramic (SiC) to form a near nett size composite ceramic shape. A mixture of: 60% Navarro 36-grit silicon carbide (SiC) 14.4% New Zealand China Clays Premium Grade Halloysite Clay 19.2% Simcoa Silicon Dust (mean size = 3.5 μm) 6.4% Pemco-325 Fused Silica (Si0 2 ) was blended to a slurry with cα 15% water and 0.2% Dispex N40 dispersant in a Hobart mixer. This slip was used to cast a 425 mm long closed end tube (cα 1.6 kg). This slip was used to cast 5 bars (175 x 25 x 25 mmm, cα 300 g dry weight) and 5 cubes (50 x 50 x 50 mm, cα 240 g dry weight). The pieces were heated under flowing "oxygen free" nitrogen (45 l.min '1 ) to 1450°C and held at that temperature for 6 hours. A shrinkage of cα 0.5% was measured during drying, but there was no significant size change during firing. Analysis of the produαs by X-ray powder diffraαion (XRD) (see Fig 2) revealed primarily SiC and O'-SiAlON with a trace of -Si 3 N 4 . The bulk density and open porosity of the fired pieces were measured by evacuation and water saturation. The 5 bars were used to determine the modulus of rupture by the 3-point method (ASTM C 133), and the 5 blocks were used to determine the cold crushing strength. A piece (50 x 8 x 8 mm) cut from one of the broken bars was used for measuring the thermal expansion, using a Harrop Laboratories dilatometer. average bulk density 2.60 g.cm" 3 (85% of theoretical) average open porosity 13.4% modulus of rupture 27 MPa cold crushing strength 138 MPa thermal expansion 2.6 x lO- C 1 from 25°C to 100°C 3.8 x lO- C 1 from 25°C to 1000°C EXAMPLE 6 At temperatures below 1600°C, O'-SiAlON is stable over the following composition range: 0 < x < 0.2. Mixtures (24g) containing Permascand 4D silicon, Superfine Quartz Powder (from Commercial Minerals), and either BDH kaolin, NZCC halloysite, dehydroxylated BDH kaolin or dehydroxylated NZCC halloysite, were prepared with the correα stoichiometry to give O'-SiAlON with x=0.2. For example: 2(Al 2 O 3 .2.09SiO 2 .2H 2 O) + 27Si + 4.82Si0 2 2Si 18 Al 2 0 12 N 18 BDH kaolin (including free quartz) These mixtures were blended by ball milling in 1 litre HDPE bottles for 20 h under hexane (170g) with Si 3 N 4 balls (95 Og, 10 mm diam). The solvent was removed by rotary evaporation, and samples of the dried powders were lightly pressed (8 MPa) to form pellets (1 g, 10 mm diam.), and heated under "oxygen-free" nitrogen at 2°Cmin '1 to 1450°C for 2 h in a Mettler Thermobalance. The resulting mass curves are plotted in Figure 3. These mass curves show 3 main features: (i) weight loss between room temperature and 500°C. (ii) an initial nitridation reaction beginning at ca 1200°C, which by comparison with the well known silicon nitride reaαion bonding process, is probably due to surface nitridation of the silicon powder, (iii) a rapid nitridation reaαion at ca 1400°C, comparable with that observed in the silicon nitride reaαion bonding process. The samples containing raw (non-dehydroxylated) clays showed a weight loss at ca 500°C consistent with the loss of struαural water from the clays. The initial nitridation reaαion at 1200-1300°C is stronger for the dehydroxylated clays, and appears to be suppressed for the non-dehydroxylated clay, particularly when ball-milled. This is probably due to a water-silicon reaαion during milling or the early stages of firing (<500°C), giving the silicon an impermeable oxide coating which prevents surface nitridation. Suppression of the surface nitridation reaαion was also accompanied by the formation of unreaαed silicon nodules in the produα, and therefore should be avoided where possible. These nodules can be greater than 1 mm in diameter and, once they form, have such a low surface area that if any nitridation does occur it is extremely slow. EXAMPLE 7 Samples of the reaαion mixtures containing raw kaolin and dehydroxylated kaolin prepared as described in Example 6 were heated at 2°C min "1 under nitrogen to various temperatures between room temperature and 1450°C. XRD analyses of the produαs are shown in Figures 4 and 5. The intensities of the strongest XRD peaks for all identified phases are plotted on a log scale. The results are non-quantitative but give an indication of the appearance and disappearance of different phases during the nitridation reaαion. For simplicity, α-silicon nitride and α-SiAlON, and . -silicon nitride and 3-SiAlON have been grouped together as α-phase and . -phase, respectively. Notable features of these graphs shown in Figures 4 and 5 are: (i) the appearance of O'-SiAlON by 1250°C, (ii) the disappearance of quartz by 1350°C, without the appearance of cristobalite, (iii) the appearance and disappearance of mullite and α-phase between 1050 and 1450°C, except in Figure 6 where some mullite remained in the final produα, (iv) the appearance of . -phase at 1250-1350°C, (v) the appearance of X-phase at 1350-1450°C, and (vi) the residual silicon in the final produα when using raw kaolin (see Example 6). The α-phase probably represents the silicon nitride surface coating which forms on the silicon grains early in the nitridation reaαion and is associated with the weight gain at 1200-1250°C (see Example 6). Alpha-silicon nitride is the expeαed produα from this surface reaαion. This α-phase disappears at higher temperatures and is probably reabsorbed into the melting silicon and reformed as -phase, X-phase and O-SiAlON. In the sample containing raw kaolin, where the 1200-1250°C weight gain is suppressed, less α-phase was expeαed, and was observed, but the difference is not great. EXAMPLE 8 Samples were fired at different rates to examine the effect of the heating rate on the reaαion chemistry. The O'-SiAlON reaαion mixture containing dehydroxylated kaolin as used in Examples 6 and 7 was lightly pressed (8 MPa) to form discs (1 g, 10 mm diam), and heated under "oxygen-free" nitrogen at 0.5, 2, 4, 6, 8 and 10°Cmin "1 , to 1450°C for 2 h in a Mettler Thermobalance. The resulting mass curves are plotted in Figure 6, and XRD analyses of the produαs are shown in Figure 7. As the heating rate increases towards 5°C.min "1 , the relative amounts of mullite, β- phase and X-phase impurities in the produαs decline, and then begin to inαease again at higher heating rates. At heating rates greater than 6°C.min "1 , nodules of residual silicon begin to appear in the produα, and this can again be associated with the suppression of the surface nitridation reaαion. The overall reaαion proceeds so rapidly that this surface reaαion does not have a chance to occur. These results suggests that the ideal heating rate is ca 5°C.min "1 . EXAMPLE 9 Effect of SiC on the Nitridation Reaction The O'-SiAlON reaαion mixture containing raw kaolin (as used in Example 6 and 7), was blended with 0%, 50% and 80% silicon carbide (H C Starck, A20, 0.5 μm) in a mortar and pestle, and the resulting mixtures were heated at 2°Cmin" 1 to 1450°C for 2 h under "oxygen-free" nitrogen in a Mettler Thermobalance. The resulting mass curves are given in Figure 8, and the results of XRD analyses of the produαs are given in Figure 9a. As the proportion of SiC in the mixture increases, the amount of residual silicon in the produα decreases (Figure 9a), and the weight gain at ca 1200°C associated with surface nitridation increases (Figure 8). If a reaαion between the water of dehydroxylation and the silicon is preventing the surface nitridation of the silicon, then the presence of SiC may be aαing to dilute the mixture and lower the water vapour pressure, or it may itself be reaαing with the water vapour. The addition of alumina in place of SiC had a similar effeα, suggesting that it is simply a dilution effeα. As the proportion of SiC in the mixture increases, the proportions of α-phase and β- phase impurities in the produαs also increase significantly. This implies that the SiC is aαively participating in the reaαion, and therefore the effeα should decline with coarser grades of SiC. To confirm this, the O'-SiAlON reaαion mixture containing raw kaolin was blended with different sizes of silicon carbide: 0.5 μm (H C Starck A20), 32 μm (Navarro C5 80 grit) and 180 μm (Navarro C5 400 grit); and fired as above. The results of the XRD analyses of the produαs are given in Figure 9b. As expeαed, as the size of the SiC increases it becomes less reaαive and the proportion of 3-phase formed in the product decreases. Note that small samples fired in a Mettler Thermobalance experience very fresh gas and this tends to enhance the amounts of impurities such as -phase and mullite in the produαs. This is a size effect, and in produαion scale furnaces it is negated by the sheer bulk of sample. EXAMPLE 10 This example illustrates the range over which the proportions of clay, silica and silicon can be varied, while still producing predominantly O'-SiAlON as the produα. At temperatures below 1600°C, O'-SiAlON is stable over the following composition range: Si 2 . x Al x 0 1+x N 2 . x where 0 < x < 0.2. This range of compositions is represented in the SiAlON behaviour diagram (Figure 10). The behaviour diagram in Figure 10 has been construαed by reaαing 3 or 4 component mixtures of Si0 2 , Si 3 N 4 , Al 2 0 3 and A1N at 1700°C. In the case of the present invention a different process is used and the firing temperature is lower, so the behaviour diagram may not apply. Mixtures containing NZCC halloysite clay, Permascand 4D silicon and Commercial Minerals superfine quartz powder in varying proportions, were hand blended in a mortar and pestle under ethanol, and the solvent was removed by evaporation. The theoretical fired compositions of these mixtures are plotted on the SiAlON behaviour diagram (Figure 10a). Note that the process of the present invention is restriαed to the triangular section of the diagram defined by the raw materials; Si0 2 , clay (in the case of this example, NZCC Halloysite) and Si (equating to Si 3 N 4 ). The dried powders were lightly pressed (8 MPa) to form pellets (10 mm diam., 2g), and heated under "oxygen free" nitrogen at 2°Cmin "1 to 1450°C for 2 h in a tube furnace. The produαs were analyzed by X-ray Powder Diffraαion (XRD), and the amount of O'- SiAlON in each of the products was estimated from XRD peak heights. The results are presented in Figure 11 (sample codes refer to compositions indicated in Figure 10a). All of the samples were completely reaαed in that no unreaαed silicon remained in any of the produαs. The produαs formed from each mix, and their relative proportions, were largely consistent with what was expeαed from the behaviour diagram. The estimated percentage yields of O'-SiAlON are plotted in Figure 10b. From this plot, the target composition needs to be within the range: 0 . 333) 0 (0 . 78 - 1 . 56) ^ (15 . 6 ^ 0.6) to obtain > 80% O'-SiAlON. The exaα amounts of silicon, silica and clay needed to achieve this will depend upon the exaα composition of the particular clay being used. EXAMPLE 11 The effeαs of various additives on the formation of O'-SiAlON were investigated to assess their potential as catalysts or sintering aids, and to examine the effect of common clay impurities such as Ca and Na. A standard O'-SiAlON reaαion mixture was prepared by ball-milling Permascand 4D Si, dehydrated NZCC halloysite clay and superfine quartz powder for 20 h under hexane with Si 3 N 4 balls as described in Example 6. Samples of this mix (5.8g) were remilled for 4 hours with BaO, CaO, Zr0 2 , Na 2 C0 3 , Fe 3 0 4 and Y 2 0 3 at a level of 1.5 mol% of cation by theoretical weight of O'-SiAlON produα. The dried powders were lightly pressed (8 MPa) to form pellets (1 g, 10 mm diam.), and heated under "oxygen free" nitrogen at 2°Cmin "1 to 1450°C for 2 h in a Mettler thermobalance. The products were analyzed by XRD. The results are presented in Figure 12, and mass curves are plotted in Figure 13. Of the additives that were tried, only Fe 3 0 4 and Zr0 2 promoted reaαion. Na 2 C0 3 , BaO and CaO appeared to hinder the O'-SiAlON reaαion, and large amounts of unreaαed silicon remained in the produαs. One possibility is that the Ba, Ca and Na are fluxing the clay at such a low temperature that the pellet sinters before it can nitride. Nitrogen is then unable to get to the silicon. In support of this is the observation that these three pellets showed the greatest shrinkage during firing (see Figure 12). Y 2 0 3 appeared to retard the reaαion slightly, but the XRD analysis indicated that it gave a more pure O'-SiAlON produα (Figure 14). Significant shrinkage during firing (14.4%) was also observed. It may therefore be valuable as a sintering aid for the O'- SiAlON reaαion. EXAMPLE 12 O'-SiAlON composites were investigated by preparing and firing mixtures of the raw O'-SiAlON mix with various ceramic materials. These were combined in a ratio to give a 50:50 mix of O'-SiAlON and the second ceramic component. Fine powders were used to highlight possible interference of the second ceramic component in the O'-SiAlON reaction. A standard O'-SiAlON reaαion mixture was prepared by ball-milling Permascand 4D Si, halloysite clay and superfine quartz powder for 20 h under hexane with Si 3 N 4 balls as described in Example 6, Samples of this mix were hand-blended with alumina (Buehler 0.3 μm γ-Al 2 0 3 ), silicon nitride (HC Starck LC10), sialon (Bensalon S-011), zircon (opaciline) and zirconia (Tosoh TZ-0) under ethanol using a mortar and pestle. The dried powders were lightly pressed (8 MPa) to form discs (1 g, 10 mm diam.), and heated under nitrogen at 2°Cmin '1 to 1450°C for 2 h in a Mettler Thermobalance. The produαs were analyzed by XRD. The results are presented in Figure 15 and mass curves are plotted in Figure 16. In each case, the reaαion yielded predominantly O'-SiAlON, ie none of the ceramic materials that were tried significantly hindered the formation of O'-SiAlON. The possible exception was A1 2 0 3 which increased the amount of /3 -phase in the produα. This may not occur with coarser A1 2 0 3 . In contrast, the /3-SiAlON, Zr0 2 and ZrSi0 4 greatly accelerated the reaction to form O'-SiAlON (Figure 16). EXAMPLE 13 This example demonstrates the fabrication of a composite ceramic produα (SiC/O'- SiAlON), formed by extrusion. To a mixture of: 50% Navarro 220-grit silicon carbide (SiC); 16% New Zealand China Clays Premium Grade Halloysite Clay; 2% Bentonite SM23 supplied by Commercial Minerals; 24% Simcoa Silicon Dust (mean size = 3.5 μm); and 8% Pemco - 325 mesh Fused Silica (Si0 2 ); was added sufficient pressing soap (a mixture of water, kerosine, oleic acid and TEA as is known in the art) to give a consistency suitable for extrusion. This mix was used to extrude 5 cylindrical rods (25 mm diam x ca 200 mm, ca 175 g dry weight). These rods were heated under flowing "oxygen free" nitrogen (45 l.min "1 ) to 1450°C and held at that temperature for 6 hours. Analysis of the produαs by X-ray powder diffraαion (XRD) revealed primarily SiC and O'-SiAlON with a trace of X-phase SiAlON. The bulk density and open porosity of the fired rods were measured by evacuation and water saturation. The modulus of rupture of the 5 rods was measured by the 3-point method. average bulk density 2.28 g.cm 3 (76% of theoretical) average open porosity 23.3% modulus of rupture 71 MPa EXAMPLE 14 This is an example of O'-SiAlON reaction bonded body, which is sintered in a second firing to form a fully dense body. A standard O'-SiAlON reaction mixture was prepared by ball-milling Permascand 4D Si, dehydroxylated BDH kaolin clay and superfine quartz powder, as described in Example 6. A sample of the dried powder was formed into a bar (62.6 x 8.8 x 7.0 mm, 4.98 g) by uniaxial pressing at 25 MPa. The bar was fired in a graphite resistance furnace on a bed of SiAlON granules under a flowing "oxygen free" nitrogen atmosphere at 2°C.min '1 to 1450°C and held at that temperature for 2 hours. During reaαion bonding, the bar increased in mass by ca 11%, and a linear shrinkage of 7.7% was measured. The bulk density and open porosity of the sintered bar was measured by evacuation and water saturation: bulk density 2.11 g.cm "3 (75% of theoretical) open porosity 24.8% The bar was then sintered by firing in a Si 3 N 4 powder bed under "oxygen free" nitrogen in a graphite resistance furnace to 1700°C for 1 hour. During sintering, the bar decreased in mass by ca 13%, and a linear shrinkage of 8.7% was measured. An analysis of the products by X-ray powder diffraαion (XRD) revealed O'-SiAlON with faint traces of mullite and X-phase SiAlON. The bulk density and open porosity of the sintered bar was measured by evacuation and water saturation. Thermal expansion was measured using a Harrop Laboratories dilatometer. The modulus of rupture was measured by 4-point method. bulk density = 2.80 g.cm "3 (100% of theoretical) open porosity = 0.0% thermal expansion = 2.2 x lO "6 .^ 1 from 25 to 100°C 3.3 x 10 " β .°C Λ from 25 to 1000°C modulus of rupture = 375 MPa EXAMPLE 15 This is an example of fully dense O'-SiAlON body prepared by sintering preformed O'-SiAlON powder. A standard O'-SiAlON reaαion mixture was prepared by ball-milling Permascand 4D Si, dehydroxylated BDH kaolin clay and superfine quartz powder, as described in Example 6. The dried powder (23.42g) was blended with water (14.35g, 38%), extruded through an 8 mm diameter hole, dried, and broken into pellets ca 10-25 mm in length. A 10 g sample of these pellets was fired in a 50 mm diameter tube furnace on a bed of SiAlON granules under flowing "oxygen free" nitrogen (ca 150 ml.min "1 ) at 2°Cmin' 1 to 1450°C and held at that temperature for 2 hours. A weight gain of 23.9% was observed, and the produα was found to be primarily O'-SiAlON with traces of mullite and /3-phase. The fired pellets were crushed to 1.5 mm in a WC percussion mortar, and ball-milled in a 1 litre HDPE bottle for 20 h under ethanol (170 g) with Si 3 N 4 balls (950 g, 10 mm diam). Oleic acid (5% by weight of O'- SiAlON) was added and the mixture milled for a further 15 min. The milled slurry was filtered through a 10 μm filter cloth, and the solvent was removed from the filtrate by rotary evaporation. The dried powder was brushed through a 295 μm sieve to granulate it. A sample of the powder was formed into a bar (58.5 x 8.2 x 6.0 mm, 4.68 g) by uniaxial pressing at 25 MPa, followed by cold isostatic pressing at 350 MPa. The bar was heated at 0.5°C min" 1 to 400°C for 30 min under nitrogen atmosphere to remove the oleic acid, and sintered in a Si 3 N 4 powder bed under "oxygen free" nitrogen in a graphite resistance furnace to 1700°C for 1 hour. During sintering, the bar decreased in mass by ca 11%, and a linear shrinkage of 18% was measured. O'-SiAlON was the only phase deteαable by X-ray powder diffraαion (XRD). The bulk density and open porosity of the sintered bar was measured by evacuation and water saturation. The modulus of rupture was measured by the 4 point method. bulk density = 2.79 g.cm "3 (100% of theoretical) open porosity = 0.0% modulus of rupture = 424 MPa EXAMPLE 16 This example illustrates the variety of clay minerals that can be used to prepare O'SiAlON. Nine clay mineral samples were selected and analysed for major oxides by X-Ray fluorescence (XRF) (Figure 17). These minerals were calcined at 1000°C for 1 hour, and hand-blended in a mortar and pestle under ethanol, with appropriate amounts of Permascand 4D Si and Commercial Minerals superfine quartz powder to give O'- SiAlON (Si 2-X A1 X 0 1+X N 2 . X ) with x = 0.2 where possible. In some cases, the Al 2 0 3 :Si0 2 ratio in the mineral was too low to form x = 0.2 O'-SiAlON. The dried powders were lightly pressed (8 MPa) to form discs (0.5g, 10 mm diam), and fired in a tube furnace at 2°C min '1 to 1450°C for 2 h on a bed of SiAlON granules under a flowing atmosphere of "oxygen free" nitrogen (30 ml.min^g" 1 ). The weight change was measured, and the produαs were analysed by X-ray powder diffraαion (XRD) (see Fig 18). EXAMPLE 17 This example illustrates the range of firing temperatures which can be used to form O'-SiAlON. The O'-SiAlON reaαion mixture containing dehydroxylated kaolin as used in Examples 6 and 7 was lightly pressured (8 MPa) to form discs (0.5 g 10 mm diam.). Discs were heated on a bed of SiAlON granules, under a flowing "oxygen free" nitrogen atmosphere (50 ml.min^.g "1 ) at a heating rate of 2°C.min' : to the following temperatures: 1175°C, 1200°C, 1250°C, 1300°C, 1350°C and 1450°C, and held at those temperatures for 8 hours. The results from XRD analyses of the produαs are shown in Figure 19. In general, discs fired at higher temperatures gave more pure O'SiAlON. Discs fired for 8 hours at temperatures less than 1300°C did not reaα to completion; unreaαed silicon remained in the produαs. However the reaαion may go to completion at temperatures lower than 1300°C if the furnace is held at temperature for periods longer than 8 hours. The foregoing describes preferred forms of the invention and it is to be understood that the scope of the invention is not to be limited to the specific forms described. Modifications and variations as will be obvious to a person skilled in the art may be made to the forms of the invention as described without departing from the spirit or scope of the invention as defined in the attached claims.

Claims: CLAIMS 1. A process for the produαion of O'-SiAlON from silicon metal, nitrogen, and clay, the process comprising heating the silicon metal and the clay in a flowing nitrogen atmosphere to a temperature sufficient to reaα the components to form O'-SiAlON and wherein the clay participates in the reaαion as a source of aluminium and silicon. . 1.. The process according to claim 1 wherein the clay is the sole source of aluminium. 3. The process according to claim 1 or claim 2 comprising dehydroxylating the clay and mixing the dehydroxylated clay with the silicon metal and heating the combination under a flowing nitrogen atmosphere to a temperature sufficient to reaα the mixture to form O'-SiAlON. 4. The process according to any one of the preceding claims further comprising the addition of silica. 5. The process according to any one of the preceding claims wherein the clay is a hydrated layer aluminosilicate mineral. 6. The process according to claim 5 wherein the clay is a kaolin, montmorillonite, pyrophyllite, bentonite or halloysite clay. 7. The process according to claim 3 wherein the clay is dehydroxylated by precalcining. 8. The process according to claim 3 wherein the clay is dehydroxylated by heating the clay to a temperature between about 500°C and about 800°C. 9. The process according to any one of the preceding claims wherein the components of the mixture are present as fine powders. 10. The process according to any one of the preceding claims wherein the clay is present in an amount of between about 5% and about 60% by weight. 11. The process according to claim 10 wherein the clay is present in an amount of between about 20% and about 60% by weight. 12. The process according to any one of the preceding claims including by weight, about 20% to about 50% clay, 0% to about 25% silica and about 40% to about 60% silicon metal. 13. The process according to any one of claims 4 to 12 including about 30% to about 40% clay, about 10% to about 20% silica, and about 40% to about 55% silicon metal. 14. The process according to any one of the preceding claims wherein the flowing N 2 atmosphere comprises < 0.5% oxygen and 0.5% water vapour. 15. The process according to any one of claims 1 to 13 wherein the flowing N 2 atmosphere comprises < 10 ppm 0 2 and < 25 ppm water vapour. 16. The process according to any one of the preceding claims wherein the mixture is heated to between about 1100°C and about 1900°C. 17. The process according to any one of the preceding claims wherein the heating rate is between about 0.2°C and about 10°C per minute. 18. The process according to claim 17 wherein the heating rate is between about 2°C and about 5°C per minute. 19. The process according to any one of the preceding claims wherein the components are held at the required temperature for between about 4 and about 60 hours. 20. The process according to any one of the preceding claims wherein additive compounds are included to enhance the reaαion and/or to promote sintering. 21. The process according to claim 20 wherein the additive compounds are seleαed from Y 2 0 3 , Fe 3 0 4 , Zr0 2 , ZrSi0 4 , MgO and /3-SiAlON. 22. The process according to any one of the preceding claims further comprising the addition of a ceramic material to produce a composite ceramic including O'-SiAlON. 23. The process according to claim 22 wherein the added ceramic material is seleαed from silicon carbide (SiC), alumina (Al 2 0 3 ), silicon nitride (Si 3 N 4 ), SiAlON, zirconia (Zr0 2 ), zircon (ZrSi0 4 ) and silica (Si0 2 ). 24. The process according to claim 22 or claim 23 wherein the ceramic material is coarser than the other mixture components which reaα to form the O'- SiAlON. 25. The process according to any one of claims 22 to 24 wherein the ceramic material is present in an amount of up to about 75% by weight of the mixture. 26. The process according to claim 25 wherein the ceramic material is present in an amount of between about 40% and about 70% by weight of the mixture. 27. A process for the produαion of O'-SiAlON from a component mixture comprising, by weight, 40%-60% silicon metal, 20%-45% clay, and 10%-25% silica, the process comprising the steps of: (a) dehydroxylating the clay prior to inclusion in the component mixture; (b) heating the component mixture at a rate of 1°C to 6°C per minute, to a temperature of between substantially 1300°C to 1900°C under a flowing N 2 atmosphere having < 0.5% oxygen and < 0.5% water vapour; (c) holding the temperature between 1300°C and 1900°C for up to 12 hours; and (d) recovering the produα. 28. A process for the produαion of a composite ceramic material including O'- SiAlON from a mixture of components comprising a ceramic material, and an O'-SiAlON forming combination of silicon metal, clay and nitrogen wherein the process comprises heating the ceramic material, silicon metal and clay in a flowing nitrogen atmosphere to a temperature sufficient to form the O'-SiAlON composite ceramic and wherein the clay participates in the reaαion as a source of aluminium and silicon. 29. The process according to claim 28 wherein the O'-SiAlON forming combination further comprises silica. 30. The process according to claim 18 or claim 29 wherein the clay is the sole source of aluminium for the produαion of O'-SiAlON. 31. The process according to claim 18 or 19 wherein the ceramic material is selected from silicon carbide (SiC), alumina (Al 2 0 3 ), silicon nitride (Si 3 N 4 ), SiAlON, zirconia (Zr0 2 ), zircon (ZrSi0 4 ) and silica (Si0 2 ). 32. A process for the produαion of a composite ceramic including O'-SiAlON from a mixture of components comprising, by weight, up to 75% of a ceramic material and 25% or more of an O'-SiAlON forming mixture, wherein the O'- SiAlON forming mixture comprises, by weight, 40%-60% silicon metal, 20%- 45% clay, and 10%-25% silica, the process comprising the steps of: (a) heating the component mixture at a rate of between substantially 1°C to 6°C per minute, to a temperature of between substantially 1300°C to 1900°C under a flowing N 2 atmosphere having < 0.5% oxygen and < 0.5% water vapour; (b) holding the temperature between 1300°C and 1900°C for up to 12 hours; and (c) recovering the produα. 33. An O'-SiAlON containing produα when produced by the process of any one of the preceding claims.

Inventors: BARRIS GLEN CLIFTON, HODREN GREGORY MICHAEL, BARRIS, GLEN, CLIFTON, HODREN, GREGORY, MICHAEL
Applicants: BARRIS GLEN CLIFTON, HODREN GREGORY MICHAEL, IND RES LTD, PYROTEK PRODUCTS LIMITED, BARRIS, GLEN, CLIFTON, HODREN, GREGORY, MICHAEL, INDUSTRIAL RESEARCH LIMITED
Application year: 1995
Main classification: C04B35
IPC codes: C01B21, C04B35