Heat-resistant materials and method of producing them

Abstract: A novel solid solution has a composition of R y Zr₄Si x P 6-x O₂₄ (R is at least one element capable of forming bivalent or trivalent cation, 0≦x≦2, 2/3≦y≦2). Furthermore, heat-resistant sintered body and heat-­ resistant phosphate based compound sintered body comprises the above solid solution and has excellent heat resistance and high temperature stability. And also, a method of producing such sintered bodies is disclosed.

Description: This invention relates to heat resistant and low expansion materials, in particular phosphate based materials which can form heat-resistant sintered bodies. The invention also relates to methods of producing such materials and sintered bodies. Recently, with the advance of industrial technologies there has been strong demand for development of materials having excellent heat resistance and low expansion. Zirconyl phosphate [(ZrO)₂P₂O₇] has been thought promising as such a material having improved heat resistance and low expansion. Lately, zirconium phosphates of alkali metals such as sodium and the like have been proposed as a material having heat resistance and low thermal expansion coefficient [Mat. Res. Bull., Vol. 19, pp.1451-1456 (1984); Journal of Materials Science, 16, 1633-1642 (1981); and Yogyõ Kyokai-shi, 95(5), pp.531-537 (1987)]. Furthermore, phosphate compounds of alkaline earth metals having a particular composition are proposed to have a low expansion [Mat. Res. Bull, Vol. 20, pp.99-106 (1985); and J. Am, Ceram. Soc., 70[10] C-232∼C-236 (1987)]. Moreover, US Patent 4,675,302 discloses that ceramic materials having a basic composition of Ca 0.5 Ti₂P₃O₁₂ have excellent low expansion characteristics. However, although the above phosphate compounds such as zirconyl phosphate and so on have the merit of excellent low expansion, these phosphate compounds have a common problem that they are thermally decomposed at high temperature above 1,200°C to evaporate phosphorus component. For instance, when the heat treatment is carried out at 1,400°C for 100 hours, zirconyl phosphate reduces weight by 19%, while sodium zirconium phosphate reduces weight by 36%. Further, the ceramic material disclosed in US Patent 4,675,302 is mainly used as a substrate for a low expansion optical reflector in a man-made satellite causing no deformation or the like even under a temperature change. As shown in Fig. 2 of this patent, the temperature change is about 500°C at most, so that there is no need for the stability, heat resistance and the like at an elevated temperature of, for example, not lower than 1,200°C. On the other hand, a method using a combination of substances selected from Na₂CO₃, ZrO₂, ZrOCℓ₂·8H₂O, SiO₂, (NH₄)₂HPO₄, H₃PO₄, Nb₂O₅, Y₂O₃, SrCO₃, K₂CO₃, CaCO₃ and the like is known as a method for the production of phosphate compounds [T. Oota and I. Yamai, Journal of the American Ceramic Society, 69, 1, (1986)]. In this method, however, P₂O₅ component is produced alone during the decomposition of ammonium phosphate or H₃PO₄ to locally form portions having a high phosphorus concentration, resulting in the formation of a low melting compound in the sintering. Consequently, large pores (spaces) are formed in the sintered body, thereby causing serious defects. The inventors have made various studies in order to solve the aforementioned problems of the conventional techniques and found that firing with addition of a certain additive is effective for restraining the weight reduction due to the evaporation of phosphorus component and in this case a given crystalline phase is formed in the sintered body. Furthermore, it has been found that the heat resistance and high temperature stability of the crystalline phase are excellent when R in R y Zr₄Si x P 6-x O₂₄ system is an element capable of forming bivalent or trivalent cation such as Ca, Sr, Ba, Y or the like, and further various compounds of R y Zr₄P₆O₂₄ (2/3≦y≦1, and R is at least one element capable of forming bivalent or trivalent cation) such as CaZr₄P₆O₂₄, SrZr₄P₆O₂₄, BaZr₄P₆O₂₄ and the like form a whole solid solution, and also high strength and low expansion sintered bodies having heat resistance and high temperature stability can be obtained by controlling the properties of R y Zr₄P₆O₂₄ itself such as thermal expansion behavior, thermal properties and the like through solid solubilization. In addition, it has been found that it is possible to form a solid solution wherein a part of P ion is simultaneously replaced with Si ion and R ion as shown in the following reaction formula (1): R y Zr₄P₆O₂₄ + xSi⁴⁺ + 1/nR' n+ - xP 6+ → R y R' 1/n ZrSi x P 6-x O₂₄ (1) (where n is a valence number of R), and heat-resistant low expansion materials having heat resistance and strength and high temperature stability can be obtained by controlling the properties of R y Zr₄Si x P 6-x O₂₄ itself such as thermal expansion behavior, thermal properties and the like through solid solubilization. The invention is based on these findings. The invention in its various aspects is set out in the claims. The invention will be described below with reference to the accompanying drawings, wherein: Fig. 1 is a graph showing a relation between chemical composition and lattice constant in solid solutions of CaZr₄P₆O₂₄-SrZr₄P₆O₂₄ system and CaZr₄P₆O₂₄-BaZr₄P₆O₂₄ system; Fig. 2 is a graph showing a relation between chemical composition in a sintered body composed of a solid solution of CaZr₄P₆O₂₄-SrZr₄P₆O₂₄ system, thermal expansion coefficient within a range of room temperature to 1,400°C and four-point flexural strength; Fig. 3 is a graph showing a relation between chemical composition in a sintered body composed of a solid solution of CaZr₄P₆O₂₄-BaZr₄P₆O₂₄ system, thermal expansion coefficient within a range of room temperature to 1,400°C and four-point flexural strength; Fig. 4 is a bar chart showing the weight-loss percentage (weight-reduced percentage) in Examples 1-10 and 14-18 and Comparative Examples 21-25 after heat treatment at 1,400°C for 100 hours; Fig. 5 is a graph showing a relation between chemical composition of a sintered body composed of a solid solution of R y Zr₄Si x P 6-x O₂₄ system and thermal expansion coefficient over a temperature range of room temperature to 1,400°C; Fig. 6 is a graph showing a relation between open porosity and four-point flexural strength in the sintered body composed of a solid solution of R y Zr₄Si x P 6-x O₂₄ system; Fig. 7 is a graph showing a powder X-ray diffraction pattern at room temperature in Example 16; Fig. 8 is a graph showing a weight-reduced percentage in heat treatment at 1,400°C for 100 hours when various additives are added to the phosphate based compound sintered body; Fig. 9 is a graph showing a relation between amount of R y Zr₄Si x P 6-x O₂₄ crystalline phase in the phosphate based compound sintered body and weight-reduced percentage in heat treatment at 1,400°C for 100 hours; Fig. 10 is a graph showing a relation between amount of R y Zr₄Si x P 6-x O₂₄ crystalline phase in the phosphate based compound sintered body and dimensional change percentage in the heat treatment at 1,400°C for 100 hours; Fig. 11 is a graph showing a relation between open porosity and four-point flexural strength in the phosphate based compound sintered body; Fig. 12 is a graph showing an X-ray diffraction pattern in the phosphate compound of Example 33; and Fig. 13 is a view illustrating a method of measuring a self-weight softening percentage. The solid solution of R y Zr₄Si x P 6-x O₂₄ system according to the invention can be used not only as a sintered body alone but also as a compound constituting a composite body with a heat-resistant compound such as zircon, zirconia or the like. In the solid solution of R y Zr₄Si x P 6-x O₂₄ system according to the invention, it is necessary that R is at least one element capable of forming bivalent or trivalent cation, and x is a numerical value of 0 to 2, and y is a numerical value of 2/3 to 2. Particularly, R is at least one element, preferably at least two elements in Group IIa of Periodic Table i.e. barium (Ba), strontium (Sr) and calcium (Ca). When R contains a monovalent cation, the high temperature stability is poor, while when x is more than 2, the heat resistance is poor. When the above system satisfies the aforementioned requirements, there are obtained a solid solution having improved heat resistance and high temperature stability and a sintered body comprising this solid solution. In the phosphate based compound sintered body according to the invention, it is necessary to include a substance having the general formula of R y Zr₄Si x P 6-x O₂₄ as a crystalline phase. The heat stability at high temperature becomes largely different due to the presence or absence of this crystalline phase as mentioned later. With the sintered body of the invention, the weight- loss percentage due to the evaporation of phosphorus component and the four-point flexural strength can be not more than 10% and not less than 100 kg/cm² at an open porosity of not more than 50% after the heat treatment at 1,400°C for 100 hours. That is, when the open porosity exceeds 50%, the four-point flexural strength becomes less than 100 kg/cm² and the strength required as a practical ceramic material is not satisfied. Furthermore, the self-weight softening percentage of the sintered body after the heat treatment at 1,400°C for 5 hours can be not are than 0.3%, which satisfies the requirement as a heat-resistant material. Moreover, the above sintered body is small in the dimensional change percentage. That is, the dimensional change percentage is not more than 1% after the heat treatment at 1,400°C for 100 hours, which also satisfies the requirement as a heat-resistant material. And also, the thermal expansion coefficient of the sintered body over a temperature range of room temperature to 1,400°C is as low as not higher than 25×10⁻⁷/°C, which shows the excellent thermal shock resistance. Therefore, the sintered bodies according to the invention having the above properties are favorably applied to materials requiring the heat resistance and heat stability at high temperature such as ceramic honeycomb structural bodies, for instance, catalyst carrier for the purification of automobile exhaust gas and the like; rotary heat regenerating type ceramic heat exchangers, heat recuperative type ceramic heat exchangers, housings for turbocharger rotor, heat insulation materials for engine manifold, diesel particulate filters and so on. In the method of producing the heat-resistant sintered body according to the invention, the starting material lies in a batch mixture of powdery materials selected from ZrP₂O₇, (ZrO)₂P₂O₇, ZrO₂, Zr(OH)₄, ZrSiO₄, SiO₂, a phosphate of R, a silicate of R and RO (R is an element capable of forming bivalent or trivalent cation). Furthermore, in the method of producing the phosphate based compound sintered body according to the invention, the starting material lies in a batch mixture of powdery materials selected from ZrP₂O₇, (ZrO)₂P₂O₇, ZrO₂, ZrSiO₄, SiO₂, a phosphate of R, a silicate of R and RO (R is an element capable of forming bivalent or trivalent cation). These powdery materials of ZrP₂O₇, (ZrO)₂P₂O₇, ZrO₂, Zr(OH)₄, ZrSiO₄, SiO₂, a phosphate of R, a silicate of R and RO are stable compounds and hardly produce non-uniformity at the molding and firing step and are friable at the high temperature and can provide ceramics having an excellent heat resistance. On the other hand, if the conventionally used phosphoric acid is used as a P₂O₅ source, since phosphoric acid is liquid, non-uniformity is caused during the mixing to locally form portions having a high phosphorus concentration and to thereby produce a compound having a low melting point. Further, when the honeycomb structural body is obtained by extruding a body containing phosphoric acid, an extrusion die or a cylinder in an extruder rusts or corrodes due to corrosiveness of phosphoric acid, and consequently the extrusion molding becomes considerably difficult. Moreover, when such a body is made by pressing, it is essentially impossible to mold the body as a powder due to the presence of phosphoric acid. In the method of producing the heat-resistant sintered body according to the invention, the batch mixture usually comprises 0-82.9% by weight of ZrP₂O₇, 0-79.5% by weight of (ZrO)₂P₂O₇, 0-50.4% by weight of ZrO₂, 0-56.8% by weight of Zr(OH)₄, 0-38.0% by weight of ZrSiO₄, 0-12.5% by weight of SiO₂, 0-44.9% by weight of a phosphate of R, 0-35.5% by weight of a silicate of R, and 0-37.3% by weight of RO. In this case, the batch mixture must contain at least one of ZrP₂O₇, (ZrO)₂P₂O₇ and the phosphate of R as well as RO, the silicate of R and the phosphate of R. In the method of producing the heat-resistant phosphate based compound sintered body according to the invention, the batch mixture usually comprises 0-84.2% by weight of ZrP₂O₇, 0-82.3% by weight of (ZrO)₂P₂O₇, 0-51.7% by weight of ZrO₂, 0-77.2% by weight of ZrSiO₄, 0-37.8% by weight of SiO₂, 0-44.6% by weight of a phosphate of R, 0-53.0% by weight of a silicate of R, and 0-42.1% by weight of RO. In this case, the batch mixture must contain at least one of ZrP₂O₇, (ZrO)₂P₂O₇ and the phosphate of R as well as RO, the silicate of R and the phosphate of R. The RO as a starting component may be used by selecting from stable compounds such as hydroxides, carbonates, sulfates and the like converting into RO or an oxide during the firing. Moreover, the starting material is used desirably has an average particle size of not more than 50 µm, preferably not more than 10 µm. As the most suitable firing conditions for the sintered body according to the invention, the firing temperature is not lower than 1,400°C, preferably 1,400-1,800°C, and the firing time is 1-24 hours, preferably 2-10 hours. When the firing temperature is restricted to not lower than 1,400°C, the phosphate based compound sintered body containing not less than 10% by weight of R y Zr₄Si x P 6-x O₂₄ as a crystalline phase according to the invention can be obtained. Further, when the firing time is less than 1 hour, the sintering is insufficient, while when it exceeds 24 hours, the strength lowers due to abnormal grain growth and also the precipitate of different phase occurs due to the evaporation of phosphorus component. As mentioned above, the preferred embodiments of the invention, within the scope of the claims, will be summarized as follows: (a) a solid solution of R y Zr₄P₆O₂₄, wherein R is at least two elements capable of forming bivalent or trivalent cation and y is a numerical value of 2/3 to 2 satisfying an electrically neutral condition of the chemical formula, and a heat-resistant sintered body and heat-resistant phosphate based compound sintered body comprising the above solid solution. (b) a solid solution of R y Zr₄Si x P 6-x O₂₄, wherein R is at least one element of Ba, Sr and Ca and x is a numerical value of 0 to 2 and y is a numerical value of 1 to 2, and a heat-resistant sintered body and heat-resistant phosphate based compound sintered body comprising the above solid solution. (c) a heat-resistant sintered body comprising a solid solution of R y Zr₄Si x P 6-x O₂₄ system and having a weight-reduction percentage of not more than 10% after the heat treatment at 1,400°C for 100 hours. (d) a heat-resistant sintered body and a heat-resistant phosphate based compound sintered body each comprising a solid solution of R y Zr₄Si x P 6-x O₂₄ system and having an open porosity of not more than 50% and a four-point flexural strength of 100 kg/cm². (e) a heat-resistant sintered body and a heat-resistant phosphate based compound sintered body each comprising a solid solution of R y Zr₄Si x P 6-x O₂₄ system and having a self-weight softening percentage of not more than 0.3% after the heat treatment at 1,400°C for 5 hours. (f) a heat-resistant sintered body and a heat-resistant phosphate based compound sintered body each comprising a solid solution of R y Zr₄Si x P 6-x O₂₄ system and having a dimensional change percentage of not more than 1% after the heat treatment at 1,400°C for 100 hours. (g) a heat-resistant sintered body and a heat-resistant phosphate based compound sintered body each comprising a solid solution of R y Zr₄Si x P 6-x O₂₄ system and having a thermal expansion coefficient over a temperature range of room temperature to 1,400°C of not higher than 25×10⁻⁷/°C. (h) a heat-resistant sintered body and a heat-resistant phosphate based compound sintered body each comprising a solid solution of R y Zr₄Si x P 6-x O₂₄ system for use in a honeycomb structural body. (i) a heat-resistant composite body containing a solid solution of R y Zr₄Si x P 6-x O₂₄ system as a main crystalline phase and a heat-resistant compound such as zircon, zirconia or the like as a second crystalline phase. (j) a method of producing a heat-resistant sintered body and heat-resistant phosphate based compound sintered body comprising a solid solution of R y Zr₄Si x P 6-x O₂₄ system, wherein R is at least one element of Ba, Sr and Ca. (k) a method of producing a heat-resistant sintered body and heat-resistant phosphate based compound sintered body comprising a solid solution of R y Zr₄Si x P 6-x O₂₄ system, wherein RO is selected from hydroxides, carbonates and sulfates converting into RO during the firing. (ℓ) a method of producing a heat-resistant sintered body and heat-resistant phosphate based compound sintered body comprising a solid solution of R y Zr₄Si x P 6-x O₂₄ system, wherein the firing temperature is not lower than 1,400°C and the firing time is 1-24 hours. The following examples are given in illustration of the invention and are not intended as limitations thereof. According to a formulating recipe as shown in the following Tables 1 and 2 were mixed zirconyl phosphate [(ZrO)₂P₂O₇], ZrP₂O₇, calcium carbonate, strontium carbonate, barium carbonate, yttria, nickel oxide, zircon, sodium carbonate, ammonium dihydrogen phosphate, ceria, titania, silica, calcium phosphate and zirconia which were previously adjusted to a given particle size. In Comparative Example 25, a mixture shown in Table 1 was charged into an alumina crucible, held in an electric furnace in air at 1,000°C for 12 hours and pulverized to form a batch mixture. The adjustment of grain size in zirconyl phosphate was carried out by using a vibration mill filled with pebbles of ZrO₂ sintered body having a diameter of about 5 mm, but it may be carried out in a pot mill or an attriter. The pebbles of ZrO₂ sintered body were used by stabilizing with MgO and Y₂O₃. The chemical composition of the pebble used is shown in the following Table 3. Further, the chemical analysis values of the starting materials used are shown in the following Table 4. One hundred parts by weight of the batch mixture shown in Tables 1 and 2 was added and throughly mixed with 5 parts by weight of a 10% PVA aqueous solution, which was pressed in a mold of 25×80×6 mm at a pressure of 100 kg/cm², rubber-pressed at a pressure of 2 tons/cm² and then dried. After the drying, the molded body was fired in an electric furnace in air under conditions shown in Tables 1 and 2. The heating rate was 5-1,700°C/hr. After the firing, the resulting sintered body was worked into a test specimen of 3×4×40 mm defined in JIS R1601 (1981), which was then measured with respect to weight-reduction percentage (identified as weight-reduced percentage in the Tables) and dimensional change percentage after heat treatment at 1,400°C for 100 hours, thermal expansion coefficient over a temperature range of room temperature (RT) to 1,400°C, four-point flexural strength, self-weight softening percentage, open porosity, and melting point. The measurement of the thermal expansion coefficient was carried out by means of a push rod type differential dilatometer using a high purity alumina sintered body over a measuring temperature range of room temperature to 1,400°C. The four-point flexural strength was measured according to a method shown in JIS R1601. The self-weight softening percentage was determined by the following equation through placing the above test specimen on supports at a span of 30 mm shown in Fig. 13, heat-treating it in air at 1,400°C for 5 hours and measuring a self-weight deformation amount Δx: Self-weight softening percentage = Δx/ℓ x 100(%) The open porosity was measured according to an Archemedian process. The melting point was determined by visually observing whether or not a cut sample of the sintered body of 3×4×5 mm was melted by the heat treatment in an electric furnace at 1,700°C for 10 minutes. Further, amounts of crystalline phases in the sintered body were quantitatively determined by using a reflection peak value at (200) plane of zirconyl phosphate (β-(ZrO)₂P₂O₇) [Communications of the American Ceramic Society, C-80(1984)], a reflection peak value at (113) plane of R y Zr₄Si x P 6-x O₂₄ [after the index of the above crystalline phase composition was numbered according to JCPDS 33-321 of CaZr₄(PO₄)₆, JCPDS 33-1360 of SrZr₄(PO₄)₆ and JCPDS 34-95 of BaZr₄(PO₄)₆, a possible case for index numbering was judged to form a solid solution], a reflection peak value at (312) plane of JCPDS 6-266 of zircon, and a reflection peak value at (011) plane of JCPDS 34-95 of m-ZrO₂, provided that since a relative intensity of the reflection at (011) plane of m-ZrO₂ is as low as 18/100, a value of 5.6 times of the intensity was used as a peak value. With respect to the other different crystalline phases, presence or absence thereof was only identified by the X-ray diffraction pattern. The lattice constant of the solid solution was determined by calculating a and c according to the following simultaneous equations after interplanar spacings d₀₁₈ and d₂₀₈ were measured from a reflection peak angle 2ϑ at (018) plane and a reflection peak angle at (208) plane of R y Zr₄Si x P 6-x O₂₄: 1/d²₀₁₈ = 4/3a² + 64/c² 1/d²₂₀₈ = 16/3a² + 64/c² The products of Examples 16,17,18,19,36,37 and 42 are embodiments of the invention as defined in claim 1. The products of Examples 1-10,12,15,16,18,19,22 and 23 are embodiments of the invention as defined in claims 2 and 3. The products of Examples 11,13,17,31-37 and 42 are illustrative in relation to claim 2, but data for the self-weight softening percentage are not given. Examples 14,21,24-26,41 and 43-48 are comparative. MgO stabilized ZrO₂ pebbles Y₂O₃ stabilized ZrO₂ pebbles SiO₂ 0.28 <0.05 Aℓ₂O₃ 0.037 <0.02 Fe₂O₃ 0.14 0.10 TiO₂ 0.12 <0.01 CaO 0.29 <0.005 MgO 3.37 0.007 K₂O 0.010 <0.005 Na₂O 0.047 <0.01 Y₂O₃ - 5.04 ZrO₂ 94.19 92.90 HfO₂ 1.65 2.11 Total 100.13 100.16 As seen from the results of Table 1, the solid solution of R y Zr₄Si x P 6-x O₂₄ system according to the invention and the heat-resistant sintered body comprising the above solid solution can be obtained when R is at least one of elements capable of forming bivalent or trivalent cation and x is a numerical value of 0-2. Further, these solid solution and sintered body are obtained by sintering a batch mixture of materials selected from ZrP₂O₇, (ZrO)₂P₂O₇, ZrO₂, Zr(OH)₄, ZrSiO₄, SiO₂, a phosphate of R, a silicate of R and RO (R is an element capable of forming bivalent or trivalent cation ) under firing conditions shown in Table 1. In Fig. 1 is shown a relation between chemical composition and lattice constant in solid solutions of CaZr₄P₆O₂₄-SrZr₄P₆O₂₄ system and CaZr₄P₆O₂₄-BaZr₄P₆O₂₄ system. Fig. 2 shows a relation among chemical composition in a solid solution of CaZr₄P₆O₂₄-SrZr₄P₆O₂₄ system, and thermal expansion coefficient and four-point flexural strength of a sintered body thereof, and Fig. 3 shows a relation among chemical composition in a solid solution of CaZr₄P₆O₂₄-BaZr₄P₆O₂₄ system, and thermal expansion coefficient and four-point flexural strength of a sintered body thereof. Fig. 4 shows a relation between chemical composition in a solid solution of R y Zr₄Si x P 6-x O₂₄ system and a weight-reduced percentage when a sintered body comprising this solid solution is held at 1,400°C for 100 hours, and Fig. 5 shows a relation between chemical composition in a solid solution of R y Zr₄Si x P 6-x O₂₄ system and a thermal expansion coefficient of a sintered body comprising this solid solution. As seen from the above, when R is at least one of elements capable of forming bivalent or trivalent cation, the heat resistance and high temperature stability of the crystalline phase are excellent, and further the characteristics of solid solution of R y Zr₄P₆O₂₄ (2/3≦y≦1) itself can be maintained through solid solubilization, and also high strength and low expansion sintered bodies having excellent heat resistance and high temperature stability can be obtained. In addition, the solid solution wherein a part of P ion is simultaneously replaced with Sr ion and R ion is more excellent in the high temperature stability and the characteristic of the solid solution of R y Zr₄Si x P 6-x O₂₄ system itself can be controlled, whereby the heat-resistant sintered bodies having a further improved high temperature stability, a high strength and a low expansion are obtained. Further, Fig. 6 shows a relation between open porosity and four-point flexural strength in the sintered body comprising a solid solution of R y Zr₄Si x P 6-x O₂₄ system. Moreover, Fig. 7 shows a powder X-ray diffraction pattern of the sintered body in Example 16 at room temperature, which indicates that the sintered body consists of only the solid solution of Sr 1.5 Zr₄SiP₆O₂₄. As seen from the results of Examples 2, 6, 9, 10, 16 and 21-24 in Table 1 and Examples 31-37 and 41-48 in Table 2, when R y Zr₄Si x P 6-x O₂₄ (R is at least one element capable of forming bivalent or trivalent cation) is contained in an amount of not less than 10% by weight as a crystalline phase, the phosphate based compound sintered bodies having a weight-reduced percentage of not more than 10% after heat treatment at 1,400°C for 100 hours according to the invention can be obtained. Further, such sintered bodies are obtained by sintering a batch mixture of materials selected from ZrP₂O₇, (ZrO)₂P₂O₇, ZrO₂, ZrSiO₄, SiO₂, a phosphate of R, a silicate of R and RO under firing conditions shown in Tables 1 and 2. Fig. 8 shows a weight-reduced percentage when various additives are added to the phosphate compound, and Fig. 9 shows a relation between weight percentage of R y Zr₄Si x P 6-x O₂₄ system contained in the phosphate compound and weight-reduced percentage of the sintered body. Fig. 10 shows a relation between weight percentage of R y Zr₄Si x P 6-x O₂₄ crystalline phase and dimensional change percentage in the phosphate based compound sintered body. As seen from the above, when not less than 10% by weight of R y Zr₄Si x P 6-x O₂₄ crystalline phase is included into the phosphate based compound sintered body, the weight-reduced percentage and dimensional change percentage after the heat treatment in air at 1,400°C for 100 hours are considerably small and the heat resistance is excellent in the phosphate based compound sintered body. Furthermore, Fig 11 shows a relation between open porosity and four-point flexural strength in the phosphate based compound sintered body. Moreover, Fig. 12 shows an X-ray diffraction pattern of the phosphate based compound sintered body in Example 33, from which it is apparent that the sintered body contains (ZrO)₂P₂O₇ and CaZr₄(PO₄)₆ as a crystalline phase. As mentioned above, according to the invention, there can be obtained a solid solution of R y Zr₄Si x P 6-x O₂₄ system (where R is at least one of elements capable of forming bivalent or trivalent cation, and x is a numerical value of 0-2 and y is a numerical value of 2/3-2 satisfying an electrically neutral condition of the chemical formula), and a heat-resistant sintered body comprising the above solid solution and having high strength, low expansion and excellent high temperature stability, and a heat-resistant phosphate based compound sintered body containing not less than 10% by weight of the above solid solution and having a weight-reduced percentage of not more than 10% after the heat treatment at 1,400°C for 100 hours. Therefore, the solid solution of R y Zr₄Si x P 6-x O₂₄ system, and the heat-resistant sintered body and phosphate based compound sintered body comprising this solid solution can widely be applied to articles requiring the heat resistance, low expansion and high temperature stability, such as rotary heat regenerating type ceramic heat exchangers and heat recuperative type ceramic heat exchangers when being molded into a honeycomb structural body through extrusion molding, and diesel particulate filters, and housings for ceramic turbocharger rotor or heat insulating materials for engine manifold when being molded through slip casting, pressing, injection molding or the like.

Claims: A solid solution having a composition of the chemical formula R y Zr₄Si x P 6-x O₂₄ wherein R is at least one element capable of forming bivalent or trivalent cations, x has a numerical value of greater than 0 and not more than 2, and y has a numerical value in the range 2/3 to 2 satisfying the condition of electrical neutrality of the chemical formula. A heat-resistant sintered body comprising a solid solution of the chemical formula R y Zr₄Si x P 6-x O₂₄, wherein R is at least one element capable of forming bivalent or trivalent cations, x has a numerical value of 0 to 2, and y has a numerical value of 2/3 to 2 satisfying the condition of electrical neutrality of the chemical formula, said body having a self-weight softening percentage of not more than 0.3% after heat treatment at 1,400°C for 5 hours, and a dimensional change percentage of not more than 1% after heat treatment at 1,400°C for 100 hours. A heat-resistant phosphate based compound sintered body containing not less than 10% by weight of a solid solution of the chemical formula R y Zr₄Si x P 6-x O₂₄ wherein R is at least one element capable of forming bivalent or trivalent cations, x has a numerical value of 0 to 2, and y has a numerical value of 2/3 to 2 satisfying the condition of electrical neutrality of the chemical formula, and having a weight-reduction percentage of not more than 10% after heat treatment at 1,400°C for 100 hours, a self-weight softening percentage of not more than 0.3% after heat treatment at 1,400°C for 5 hours, and a dimensional change percentage of not more than 1% after heat treatment at 1,400°C for 100 hours. A method of producing a heat-resistant sintered body, which comprises molding and firing a batch mixture of materials selected from ZrP₂O₇, (ZrO)₂P₂O₇, ZrO₂, Zr(OH)₄, ZrSiO₄, SiO₂, a phosphate of R, a silicate of R and RO (where R is an element capable of forming bivalent or trivalent cations) to precipitate a solid solution of the chemical formula R y Zr₄Si x P 6-x O₂₄, wherein R is at least one said element capable of forming bivalent or trivalent cations, x has a numerical value of 0 to 2, and y has a numerical value of 2/3 to 2 satisfying the condition of electrical neutrality of the chemical formula, as a main crystalline phase of the sintered body, said firing being carried out at a temperature of not lower than 1,400°C for a time of 1 to 24 hours. A method of producing a heat-resistant phosphate based compound sintered body, which comprises molding and firing a batch mixture of materials selected from ZrP₂O₇, (ZrO)₂P₂O₇, ZrO₂, ZrSiO₄, SiO₂, a phosphate of R, a silicate of R and RO (where R is an element capable of forming bivalent or trivalent cations) to form a sintered body containing not less than 10% by weight of a solid solution of the chemical formula R y Zr₄Si x P 6-x O₂₄,wherein R is at least one said element capable of forming bivalent or trivalent cations, x has a numerical value of 0 to 2, and y has a numerical value of 2/3 to 2 satisfying the condition of electrical neutrality of the chemical formula, said firing being carried out at a temperature of not lower than 1,400°C for a time of 1 to 24 hours.

Inventors: MATSUHISA TADAAKI, OHASHI TSUNEAKI NGK TAKEMI-RYO, WATANABE KEIICHIRO E COOP NAKA, MATSUHISA, TADAAKI, OHASHI, TSUNEAKI NGK TAKEMI-RYO, WATANABE, KEIICHIRO 4E, COOP. NAKANOMACHI HOUSE
Applicants: NGK INSULATORS LTD, NGK INSULATORS, LTD.
Application year: 1988
Main classification: C04B35
IPC codes: C04B35