PORCELAIN COMPOSITION WITH NANOSIZED CERAMIC OXIDES

Abstract

The present invention is related to the development of a new formulation of electrical grade porcelain having improved mechanical and dielectric characteristics, and whose primary application is in electrical components, such as electric insulators.

This invention has as its main object to provide a new alternative to increase the final properties of an electrical grade porcelain, which is related to the incorporation of suitable concentrations of nanosized ceramic oxides, as part of the initial composition of porcelain paste.

This new nanotechnology alternative favors an increase in the final properties of electrical grade porcelain, such as flexural strength or cold rupture modulus, as well as dielectric strength, which is due to the incorporation of ceramic oxides such as alumina (α-Al.sub.2O.sub.3) and zirconia (ZrO.sub.2), in micrometer scale (i.e., less than 100 nanometers), favorably modify the microstructure of the base porcelain.

Mechanical strength, specifically the flexural strength at three points, of the porcelain compositions of the present invention is up to 38% greater than a silica based conventional porcelain composition. Furthermore, the insulating ability of the composition of this invention is up to 30% above the value of the reference siliceous porcelain.

Another important aspect of this invention is based on the concept that the ceramic nano-oxides of (α-Al.sub.2O.sub.3) and zirconia (ZrO.sub.2) strengthen the microstructure of siliceous porcelain, since the amount of crystalline phase increases and therefore the amorphous phase is reduced. Furthermore, the ceramic nano-oxides favor the increase in the concentration of the crystalline mullite phase (3Al.sub.2O.sub.3.2Si0.sub.2) in the microstructure, which is known to benefit the mechanical performance of triaxial porcelains.

Claims

1. A silica based porcelain composition characterized by comprising a mixture of 48 to 53% by weight of silicon oxide and sodium type feldspar material; a mixture of 43 to 47% by weight of clay and kaolin; and adding 0.1 to 8.0% by weight of a nanosized ceramic oxide.

2. The porcelain composition according to claim 1, wherein the nanosized ceramic oxide which is added to the porcelain is aluminum oxide (α-Al.sub.2O.sub.3) and whose particle size is 30 to 60 nanometers.

3. The porcelain composition according to claim 1, wherein the nanosized ceramic oxide which is added to the porcelain is zirconium oxide (ZrO.sub.2) and whose particle size is 30 to 60 nanometers.

Description

DESCRIPTION OF THE DRAWINGS

[0010] For a better understanding of the invention, reference is made to the following figures:

[0011] FIG. 1 corresponds to an image of scanning electron microscopy, without etching, of the base or reference porcelain composition;

[0012] FIG. 2 corresponds to an image of scanning electron microscopy, without etching, of the porcelain composition with the addition of a-alumina nano-oxides;

[0013] FIG. 3 corresponds to an image of scanning electron microscopy, without etching, of the porcelain composition with addition of zirconia nano-oxides;

[0014] FIG. 4 corresponds to the X-ray diffraction pattern of the base porcelain composition, as compared to the compositions of the present invention;

DETAILED DESCRIPTION OF THE INVENTION

[0015] The present invention will be described in greater detail with reference to the following examples.

EXAMPLE 1

[0016] Initial raw materials to produce the porcelain pastes are based on an electrical grade silica-based composition, that is, silicon oxide (SiO.sub.2) or quartz, sodium type feldspar, clay and kaolin, as well as the addition of nanosized ceramic oxides, aluminum oxide (α-Al.sub.2O.sub.3) or alumina and zirconium oxide (ZrO.sub.2) or zirconia. The chemical composition of the initial components used for the manufacture of porcelain pastes are shown in Table 1, while the average particle sizes are shown in Table 2.

TABLE-US-00001 TABLE 1 Chemical composition of the initial porcelain formulation components (% by weight) Quartz Feldspar Clay Kaolin α-Al.sub.2O.sub.3 ZrO.sub.2 SiO.sub.2 95.41 53.95 44.925 62.696 1.010 0.00 Al.sub.2O.sub.3 1.506 27.22 37.151 18.865 97.90 0.511 ZrO.sub.2 0.029 0.00 0.025 0.014 0.00 98.40 Fe.sub.2O.sub.3 0.083 1.49 0.578 0.273 0.864 0.255 K.sub.2O 0.267 0.64 0.166 4.294 0.00 0.00 Na.sub.2O 0.315 0.31 0.00 12.156 0.00 0.00 CaO 0.221 0.24 0.574 0.793 0.127 0.00 MgO 0.00 0.52 0.277 0.00 0.00 0.00 TiO.sub.2 0.00 0.00 1.482 0.00 0.00 0.769

TABLE-US-00002 TABLE 2 Initial porcelain formulation components Quartz Feldspar Clay Kaolin α-Al.sub.2O.sub.3 ZrO.sub.2 Average 40-50 70-80 70-80 70-80 0.03-0.06 0.01-0.04 particle size (μm)

[0017] Seven silicone porcelain compositions were defined (A-G), which are described in Table 3. Composition A corresponds to the base or reference porcelain paste, compositions B, C and D correspond to the base paste with additions of α-Al.sub.2O.sub.3 nanoparticles, while compositions E, F and G correspond to the base paste with ZrO.sub.2 nanoparticle aggregates.

TABLE-US-00003 TABLE 3 Chemical composition of the initial porcelain Initial formulation components (% by weight) components A B C D E F G Quartz + 52.8 52.2 50.0 48.6 52.2 50.0 48.6 feldespar Clay + 47.2 46.8 45.0 43.4 46.8 45.0 43.4 Kaolin n-Al.sub.2O.sub.3 0 1.0 5.0 8.0 0 0 0 n-ZrO.sub.2 0 0 0 0 1.0 5.0 8.0

[0018] The process of preparing reference pastes (A) consisted of mixing the initial components of the triaxial porcelain, quartz, clay, kaolin and feldspar, according to Table 3, using a semi-dry process, with the addition of 15% by weight water of the total mixture. In the case of compositions B-G, ceramic nano-oxides were previously prepared before adding them to the powder mixture of the initial porcelain base components. A dispersant additive based on an acrylic hydrophobic copolymer (OROTAN™ 681) was used for compositions B, C and D, while a polymeric dispersing agent (Zephrym™ PD 3315) was used for compositions E, F and G. Among other dispersants that may also be used are: Crodafos 03A, Crodafos 010A, Oratanm 850, Tritonm X-100, etc. The mixture of water, dispersing agent and nanoparticles was incorporated in the powder mixture comprised of quartz, clay, kaolin and feldspar, to form porcelain pastes B-G.

[0019] Each of the porcelain mixtures were shaped to obtain rectangular specimens (30×30×200 mm) using uniaxial pressure. Then they were dried in an electric oven at a maximum temperature of 120° C. and sintered at a maximum temperature of between 1250 and 1300° C. in a tunnel type industrial furnace.

[0020] Table 4 shows the final properties of the porcelain compositions after sintering. The bulk density of the porcelain specimens was obtained according to the test standard ASTM C373 (Standard Test Method for Water Absorption, Bulk Density, Apparent Porosity, and Apparent Specific Gravity of Fired Whiteware Products), using the Archimedes method. The flexural strength or cold rupture modulus (MOR) of the sintered rectangular specimens (26×26×180 mm) was measured according to standard ASTM C674 (Standard Test Methods for Flexural Properties of Ceramic Whiteware Materials) by the method of 3-point bending with a support span of 100 mm.

TABLE-US-00004 TABLE 4 Final properties of porcelain composition A B C D E F G Bulk 2.331 2.333 2.337 2.345 2.353 2.374 2.409 density (g/cm.sup.3) Flexural 32.5 43.3 42.5 44.2 38.3 41.1 44.8 strength after firing (N/mm.sup.2)

[0021] As shown in Table 4, the porcelain compositions of this invention B-G, exhibit flexural strength values higher than the reference composition (A). Particularly, compositions B, C and D, which include 1.0, 5.0 and 8.0% by weight of α-Al.sub.2O.sub.3 nanoparticles respectively, show an increase in flexural strength of 31-36% compared to composition A. On the other hand, compositions with additions of ZrO.sub.2 nanoparticles (compositions E, F and G) showed an increase in flexural mechanical performance from 18 to 38% compared to the reference composition.

[0022] FIG. 1 shows a micrograph obtained by electron microscopy (SEM) corresponding to the porcelain base composition (A) without etching, in which a microstructure formed by quartz crystals (1) embedded in a glass matrix (2) are shown, as well as the presence of porosity (3) derived from sintering treatment. FIGS. 2 and 3 show the microstructures corresponding to compositions D and G, wherein a microstructure modified by the nano-oxide ceramics of Al.sub.2O.sub.3 (4), and ZrO.sub.2 (5), respectively, are shown. As can be seen from comparing FIGS. 1, 2 and 3, the microstructure of porcelains made from the compositions of the present invention have a further crystalline phase, which is embedded in the glass phase.

[0023] FIG. 4 comparatively shows the X-ray diffraction patterns of the reference porcelain composition (marked as 1), the porcelain composition with additions of 8% by weight of nanoparticles of α-Al.sub.2O.sub.3 (shown as 2) and the composition with 8% by weight of nanoparticles of ZrO.sub.2 (indicated as 3). The main peaks correspond to crystal phases of quartz C, mullite M, as well as a-alumina A and zirconia Z phases.

[0024] It is clear that the intensity of mullite phase peak (3Al.sub.2O.sub.3.2SiO.sub.2) increases in compositions D and G compared to reference porcelain, which corresponds to increasing the flexural strength of the compositions the present invention. This indicates that the incorporation of alumina and zirconia ceramic nano-oxides favorably modifies the microstructure of silica base porcelain, giving improved mechanical strength tot he porcelain body.

EXAMPLE 2

[0025] The same concept of incorporating ceramic nano-oxides of α-Al.sub.2O.sub.3 and ZrO.sub.2, in the final performance of a composition of silica-based electrical porcelain, was investigated. The starting materials for the preparation of the experimental samples were quartz, clay, kaolin and feldspar, as well as α-alumina and zirconia nanoparticles. The chemical composition and particle size of the raw materials are shown in Tables 1 and 2.

[0026] Seven prototype porcelain compositions were defined which are described in Table 5. Composition H corresponds to the base or reference porcelain, compositions I, J and K correspond to the base paste with additions of α-Al.sub.2O.sub.3 nanoparticles, while compositions L, M and N correspond to the porcelain base with ZrO.sub.2 nanoparticle aggregates.

TABLE-US-00005 TABLE 5 Chemical composition of the initial porcelain Initial formulation components (% by weight) components H I J K L M N Quartz + 52.8 52.72 52.50 52.24 52.72 52.50 52.24 feldespar Clay + 47.2 47.17 46.98 46.74 47.17 46.98 46.74 Kaolin n-Al.sub.2O.sub.3 0 0.1 0.5 1.0 0 0 0 n-ZrO.sub.2 0 0 0 0 0.1 0.5 1.0

[0027] The method of preparing such compositions was by a wet process, where powders of raw materials are mixed with osmosis water (60-75% by weight of the total mixture) according to Table 5, and adding calcium chloride as an additive in a concentration of 0.01 to 0.08% by weight of the total mixture. The mixing process was performed at a speed of 650-750 rpm for a period of approximately 150 minutes. Subsequently, a magnetic cleaning of the porcelain mixture is made in order to remove residues of oxides, and a screening (150 and 120 mesh) to remove impurities or possible resulting agglomerations.

[0028] For compositions of the present invention I-N, to the porcelain base mixture were added the ceramic nano-oxides in concentrations according to Table 5. The nanoparticles were added in two loads, performing an additional mixing of minutes at a speed of 1100 and 1250 rpm. Once the porcelain mixtures were obtained, pastes or “cakes” were formed by a conventional filter-press process, applying a pressure of 1-1.2 MPa. This process allowed to remove excess moisture by leaving it in a range from 16 to 18%. The resulting pastes were formed by a plastic extrusion process, at a speed of 40 mm/min, to obtain cylindrical samples of 28.5 mm diameter×200 mm long. The porcelain specimens were dried at a maximum temperature of 120° C. and sintered at a maximum temperature of between 1250 and 1300° C. in a tunnel type industrial furnace.

[0029] The final properties of porcelain compositions are shown in Table 6. The bulk density of the samples was obtained by the Archimedes method, according to standard ASTM C373 (Standard Test Method for Water Absorption, Bulk Density, Apparent Porosity, and Apparent Specific Gravity of Fired Whiteware Products). The percentage of linear shrinkage of the test pieces was determined after the sintering process by measuring changes in length before and after drying and sintering process. The specimens were mechanically tested after the drying process and post-sintering, by 3 point flexural strength testing according to standard ASTM C674 (Standard Test Methods for Flexural Properties of Ceramic Whiteware Materials). The dielectric strength or insulating capacity of porcelain samples was obtained according to standard ASTM D149 (Standard Test Method for Dielectric Breakdown Voltage and Dielectric Strength of Solid Electrical Insulating Materials at Commercial Power Frequencies), using dielectric oil 11GBX (Nynas) as insulating means.

TABLE-US-00006 TABLE 6 Final properties of porcelain compositions H I J K L M N Bulk density (g/cm.sup.3) 2.360 2.372 2.378 2.382 2.368 2.370 2.370 Lineal shrinkage 11.02 11.29 11.33 11.31 10.15 10.18 10.46 after firing (%) Flexural dry 3.91 4.42 4.91 5.98 4.60 4.44 4.55 strength (N/mm.sup.2) Flexural strength 63.3 69.3 72.5 76.0 71.0 71.2 71.5 after firing (N/mm.sup.2) Dielectric strength 15.37 20.32 20.20 19.62 20.05 18.89 19.18 after firing (kV/mm)

[0030] The bulk density of the compositions of the invention (I-N) is comparable to the density of the reference composition. Porosity tests were made to small fragments of the sintered porcelain, by standard ASTM D116 (Standard Test Methods for Ceramic Materials for Electrical Vitrified Applications), using the fuchsin ink penetration method. The tests indicated that the ink did not penetrate the interior of the porcelain, which indicates that the compositions of the present invention have very low open porosity values, which is an indispensable characteristic for porcelains used in electrical insulators.

[0031] It can be clearly seen that the flexural strength of siliceous porcelain increases when ceramic nano-oxides are added. The compositions with additions of α-alumina nanoparticles (I, J, K) showed improved flexural strength of 9.5-20%, post-sintering with respect to the base formulation (H). The porcelain compositions with nano-zirconia (L, M, N) showed increases of 12 to 13%.

[0032] Table 7 shows the influence of the addition of ceramic nano-oxides of alumina and zirconia at the concentration of the phases present in the microstructure of the compositions of the present invention (K and N) with respect to the reference porcelain.

[0033] As can be seen in Table 7, the ceramic nano-oxides have a favorable influence on increasing the mullite phase, as well as the decrease in amorphous phase compared to the base or reference composition. This clearly corresponds to the increased mechanical flexural strength observed in compositions with additions of nanoparticles.

TABLE-US-00007 TABLE 7 Quantification of porcelain composition phases (% by weight) H K N Vitreous phase 65 60.3 61.6 Quartz 18.2 19.5 19.7 α-alúmin 0 0.86 0 Zirconia 0 0 1.01

[0034] The dielectric strength is also favored by the addition of nanoparticles. In particles, compositions I, J and K showed increases of 28 to 32% with respect to the base porcelain, while in compositions L, M and N the increase was 25 to 30%.