Sintered zirconia mullite refractory composite, methods for its production and use thereof

Abstract

The present invention relates to a zirconia mullite refractory composite comprising 55 wt.-% to 65 wt.-% Al.sub.2O.sub.3, 15 wt.-% to 25 wt.-% SiO.sub.2, 15 wt.-% to 25 wt.-% ZrO.sub.2 and less than 3 wt.-% raw material based impurities, whereby the mineralogical composition of the composite comprises 65 wt.-% to 85 wt.-% mullite and 15 wt.-% to 35 wt.-% zirconia.

Claims

1. A sintered zirconia mullite refractory composite based on aluminosilicate, alumina, and zircon sand, wherein the zirconia mullite refractory composite has a chemical composition comprising, in weight-percent: 55% to 65% Al.sub.2O.sub.3; 15% to 25% SiO.sub.2; 15% to 25% ZrO.sub.2; and less than 3% raw material-based impurities, the zirconia mullite refractory composite has a mineralogical composition comprising 65 wt.-% to 85 wt.-% mullite and 15 wt.-%-35 wt.-% zirconia, and the zirconia mullite refractory composite comprises zirconia particles essentially homogeneously distributed in a mullite matrix, wherein the average particle diameter of the zirconia particles is less than 2 μm.

2. A composite according to claim 1, wherein the aluminosilicate comprises andalusite, kyanite, and/or sillimanite.

3. A composite according to claim 2, wherein the raw material basis of the composite comprises 25 wt.-% to 35 wt.-% andalusite; 35 wt.-% to 45 wt.-% alumina; and 25 wt.-% to 35 wt.-% zircon sand.

4. A refractory castable for producing refractory bricks or cast pieces, comprising a refractory composite according to claim 1, wherein when sintered at a temperature between 1000° C. and 1700° C., the castable has a Cold Module of Rupture (CMOR), measured according to EN 1402-5, of more than 80 MPa, and a Cold Crushing Strength (CCS), measured according to EN 1402-6, of more than 500 MPa.

5. A refractory castable according to claim 4, wherein the castable is a low cement castable (LCC) having a cement content of about 5 wt.-% or an ultra-low cement castable (ULCC) having a cement content of less than 2 wt.-%.

6. A method for manufacturing a sintered zirconia mullite refractory composite according to claim 1, the method comprising the steps: homogeneously mixing of finely ground raw material powders; forming a shaped body from the homogeneous mixture of the raw material powders; sintering the shaped body at a temperature range between 1400° C. and 1700° C.; crushing the sintered body to obtain a desired particle size distribution.

7. A method according to claim 6, wherein the forming of the shaped body comprises the steps: adding 15 wt.-% to 50 wt.-% water and 0.1 wt.-% to 1.0 wt.-% of a dispersant, each based of the total weight of the raw material mixture; homogenising the mixture to obtain a homogeneous dispersion of finely ground raw material powders; casting the homogeneous dispersion into a mold; and drying and subsequently sintering the cast material.

8. A method according to claim 6, wherein the forming of the shaped body comprises the steps: compacting the powder mixture at pressures up to 300 MPa to obtain compacts, whereby optionally small amounts of water are added; optionally drying of the compacts; and sintering the compacts.

9. A method according to claim 6, wherein the finely ground raw material powders comprise 25 wt.-% to 35 wt.-% andalusite, 35 wt.-% to 45 wt.-% alumina, and 25 wt.-% to 35 wt.-% zircon sand, each having a particle size of less than 5 μm.

10. A refractory castable for producing refractory bricks or cast pieces, comprising a refractory composite according to claim 2, wherein when sintered at a temperature between 1000° C. and 1700° C., the castable has: a Cold Module of Rupture (CMOR), measured according to EN 1402 5, of more than 80 MPa, and a Cold Crushing Strength (CCS), measured according to EN 1402 6, of more than 500 MPa.

11. A refractory castable according to claim 10, wherein the castable is a low cement castable (LCC) having a cement content of about 5 wt.-% or an ultra-low cement castable (ULCC) having a cement content of less than 2 wt.-%.

12. A refractory castable for producing refractory bricks or cast pieces, comprising a refractory composite according to claim 3, wherein when sintered at a temperature between 1000° C. and 1700° C., the castable has: a Cold Module of Rupture (CMOR), measured according to EN 1402 5, of more than 80 MPa, and a Cold Crushing Strength (CCS), measured according to EN 1402 6, of more than 500 MPa.

13. A refractory castable according to claim 12, wherein the castable is a low cement castable (LCC) having a cement content of about 5 wt.-% or an ultra-low cement castable (ULCC) having a cement content of less than 2 wt.-%.

Description

SHORT DESCRIPTION OF THE FIGURES

(1) The present invention is additionally illustrated by reference to the following figures:

(2) FIG. 1 shows a graphic representation of the compressive strength at high temperatures,

(3) FIG. 2 shows a graphic representation of the thermal shock resistance of refractory bricks,

(4) FIG. 3 shows a graphic representation of the thermal shock resistance of a composite according to the present invention, and

(5) FIG. 4 shows an SEM picture of a polished section with 1500-fold magnification.

DETAILED DESCRIPTION OF THE INVENTION

(6) Below, the present invention is further explained by means of examples which should not be construed to unduly limit this invention.

Example 1

(7) As a start, 28.47 wt.-% andalusite (m-KF), 39.37 wt.-% aluminum oxide (CT 3000) and 32.16 wt.-% zircon sand were homogeneously mixed. 43 wt.-% distilled water and 0.6 wt.-% dispersant (Darvan C) were added to the powder mixture and the dispersion so obtained was homogenized for 24 hours by means of a stirrer. The homogenized dispersion was cast into a mold, dried and the obtained solid body was sintered. A sintering program was used for sintering, whereby the solid body was heated up to 150° C. within 30 minutes, kept for 30 minutes at this temperature, and heated up to 1600° C. within 180 minutes. The product was sintered at 1600° C. for 24 hours and then cooled down to room temperature within 2 hours.

(8) During sintering, the formation of mullite takes place in different ways. The primary mullite formation results from the decomposition of andalusite (SiO.sub.2.Al.sub.2O.sub.3) into mullite (2SiO.sub.2.3Al.sub.2O.sub.3) and silicon dioxide (SiO.sub.2). The secondary mullite formation is effected by the reaction of aluminum oxide (Al.sub.2O.sub.3) with the silicon dioxide (SiO.sub.2) from the decomposition of the zircon sand (ZrSiO.sub.4) and the excess silicon dioxide (SiO.sub.2) from the decomposition of andalusite (SiO.sub.2Al.sub.2O.sub.3). The total equation is:
3[SiO.sub.2.Al.sub.2O.sub.3]+3Al.sub.2O.sub.3+ZrSiO.sub.4.fwdarw.2[2SiO.sub.2.3Al.sub.2O.sub.3]+ZrO.sub.2

(9) Examples 2 and 3 were analogically produced.

(10) The chemical and mineralogical compositions of the examples are summarized in table 1:

(11) TABLE-US-00001 TABLE 1 chemical composition examples (percent by weight) 1 2 3 Al.sub.2O.sub.3 58.00 58.10 56.50 Fe.sub.2O.sub.3 0.36 0.30 0.42 SiO.sub.2 21.10 21.50 20.20 ZrO.sub.2 + HfO.sub.2 20.17 19.85 22.47 mineralogical composition (percent by weight) mullite 72 69 72 baddeleyite 19 19 19 ZrO.sub.2 (tetr. + cub.) 1 1 1 corundum 6 6 0 zircon 0 0 0 amorphous phases 2 5 8

(12) During thermal treatment, the zircon sand is transformed into small zirconia particles having an average particle size of less than 5 μm. Mullite acts as a binder and forms the matrix of the composite. The transformation is catalyzed by the presence of alkali oxides during the first hours of the heat treatment.

(13) Mechanical Properties

(14) Bars for measuring the bending strength (CMOR=Cold Module of Rupture) and samples for measuring the cold crushing strength (CCS) were produced for testing the mechanical properties of the zirconia mullite composite. Additionally, the true density and the open porosity were determined. The mechanical properties are described in table 2:

(15) TABLE-US-00002 TABLE 2 true density open porosity example (g/cm.sup.3) (%) CMOR (MPa) CCS (MPa) 1 3.32 <1 88 569 2 3.31 <1 76 481 3 3.51 <1 86 292
Standard Castable Formulation Test

(16) Furthermore, the sintered zirconia mullite refractory composite of example 1 (SZM) was, tested in a standard castable formulation in comparison to fused zirconia mullite (FZM). The recipe for the standard castable formulation is given in table 3.

(17) By means of the corresponding castables, test bodies were produced for further physical investigations. The test bodies were dried at 110° C. for 24 hours and sintered for 3 hours each at 1000° C., respectively 1500° C. The sintering cycles are described in table 4. The physical properties of the test bodies are summarized in table 5.

(18) TABLE-US-00003 TABLE 3 recipe component properties percentages (wt.-%) zirconia mullite 3-5 mm 16 SZM (example 1) 1-3 mm 20 FZM (comparison) 0-1 mm 24 0-0.09 mm   20 calcined alumina CT 9 FG 5 micro silica 971 U 5 reactive alumina RG 4000 5 cement Secar 71 5 sum 100 dispersant STPP 0.15

(19) TABLE-US-00004 TABLE 4 temperature range heating rate temperature range heating rate RT-750° C. 300° C./h RT-1250° C. 300° C./h 750° C.-950° C. 120° C./h 1250° C.-1450° C. 120° C./h 950° C.-1000° C. 60° C./h 1450° C.-1500° C.  60° C./h 1000° C.-1000° C. 3 h 1500° C.-1500° C. 3 h 1000° C.-RT 720° C./h 1500° C.-RT 720° C./h

(20) As evident from the results in table 5 below, the sintered zirconia mullite composite according to present invention (SZM) and the conventional fused zirconia mullite (FZM) have comparable properties. Only the cold modulus of rupture of SZM at 1500° C. shows a significant higher value. This remarkable discrepancy is the subject of further investigations.

(21) TABLE-US-00005 TABLE 5 zirconia mullite composite physical properties SZM FZM required water (H.sub.2O) (wt.-%) 5.5 5.3 flowability (%) 70 75 CMOR (MPa)  110° C. 15.8 14.3 1000° C. 31.7 26.2 1500° C. 37.4 21.9 CCS (MPa)  110° C. 120 143 1000° C. 195 205 1500° C. 186 179 density (g/cm.sup.3)  110° C. 2.76 2.83 1000° C. 2.80 2.97 1500° C. 2.81 3.02 open porosity (%)  110° C. 12.4 11.5 1000° C. 15.5 16.8 1500° C. 16.6 14.6 irreversible 1000° C. −0.29 −0.32 elongation (%) 1500° C. −0.79 −0.55
Thermal Properties

(22) To get an idea of the thermal properties of the composites according to the present invention (SZM), the refractoriness under load was measured in comparison to conventional fused zirconia mullite (FZM). The results are illustrated in FIG. 1 which shows that the conventional fused zirconia mullite and the sintered zirconia mullite according to the present invention behave comparably.

(23) Thermal Shock Resistance (Refractory Bricks)

(24) The thermal shock resistance of the zirconia mullite composite according to the present invention (SZM/example 1) was tested in comparison to commercially available fused zirconia mullite (FZM) and commercially available sintered zirconia mullite (standard) and is graphically illustrated in FIG. 2. There are significant differences to be realized between the composite according to the present invention and the commercially available materials, which can be explained with the different chemical and mineralogical compositions.

(25) The composite according to the present invention is characterized by a high amount of mullite, whereas the commercially available zirconia mullites have significant lower mullite contents. The mineralogical phase distributions are described in table 6.

(26) TABLE-US-00006 TABLE 6 zirconia mineralogical mullite composite phase (%) SZM FZM Standard mullite 74 54 61 baddeleyite 19 30 33 ZrO.sub.2 (kub. + tetr.) traces 1 1 corundum 1 0 1 amorphous 6 15 4

(27) The recipe for the production of refractory bricks for testing the thermal shock resistance is summarized in table 7:

(28) TABLE-US-00007 TABLE 7 recipe component properties share (%) clay 3.0 reactive alumina 8.5 zircon 5.5 zirconia mullite SZM 0-0.09 mm   13.0 FZM 0-1 mm 40.0 standard 1-3 mm 30.0 sum 100 H.sub.2O 4.5 additive 1.0

(29) Initially, a suspension was made from the raw materials, which suspension was pressed to refractory bricks by means of a hydraulic press. The bricks were sintered at 1600° C. for 5 hours. Then, the density and the open porosity of the bricks were measured. The sintering program is described in table 8. The physical data of the bricks are summarized in table 9.

(30) TABLE-US-00008 TABLE 8 temperature range heating rate RT-1450° C. 300° C./h 1450° C.-1550° C. 120° C./h 1550° C.-1600° C.  60° C./h 1600° C.-1600° C. 5 h hold 1600° C.-RT 720° C./h

(31) TABLE-US-00009 TABLE 9 sample density (g/cm.sup.3) open porosity (%) example 1 (SZM) 2.81 16.0 FZM 3.06 16.3 Standard 3.05 17.7

(32) The thermal shock resistance of the bricks was tested by heating the samples to 950° C. and subsequently cooling to room temperature (RT) by means of compressed air. The effect of the thermal shock was proved by means of ultrasonic transmission technic, whereby in each case an average value was established from three samples.

(33) The progression of the Young's modulus is graphically illustrated in FIG. 2. For refractory bricks, the composite according to the present invention shows a big decline of the E-modulus after the first thermal shock and remains constant at high level, whereas the comparative examples show a low decline at the beginning, however, the E-modulus is constantly lower compared to the composite according to the present invention.

(34) Thermal Shock Resistance (Composite)

(35) FIG. 3 illustrates the Young's modulus of the composite according to the present invention in comparison to cordierite and alumina. The thermal shock resistance of the composite was tested by heating the samples up to 1200° C. and subsequently cooling to room temperature (RT) by means of compressed air. The effect of the thermal shock was proved by means of the ultrasonic transmission technique. The thermal shock resistance of the composite according to the present invention increases with the first and second thermal cycles and stays constant afterwards, whereas the thermal shock resistance of the cordierite collapses after the second cycle and the one of alumina decreases with the first and second cycles and subsequently stays constant at a low level.

(36) Corrosion Resistance

(37) Furthermore, the corrosion resistance against molten slags was tested in comparison to the commercially available fused and sintered zirconia mullite, wherefore refractory bricks according to the above described process and recipe were produced as well. A two centimeter deep hole having a diameter of one centimeter was drilled into the bricks and filled with finely ground glass. The bricks were filled with glass were heated in a furnace for 10 hours at 1350° C. After cooling, the bricks were cut by means of a longitudinal section through the middle of the drill hole and subsequently investigated using a scanning electron microscope in order to determine the depth of molten glass penetration. It was found that the molten glass had penetrated the fused zirconia mullite brick deepest, whereas for both sintered zirconia mullite bricks a comparable, very low depth of penetration and with it a high corrosion resistance was measured, whereby the zirconia mullite brick according to the present invention showed little advantages compared to the standard.

(38) FIG. 4 shows a typical microstructure of a composite according to the present invention, whereby bright zirconia crystals 1 are embedded in a mullite matrix 2 (grey area). The dark areas are pores 3. Usually, the sintered composite has a microstructure comprising essentially homogeneously distributed zirconia particles 1 in a mullite matrix 2, wherein the average particle diameter of the zirconia particles 1 is preferably less than 5 μm, more preferably, less than 2 μm. With further investigations in the context of the present work, it was found that significantly finer and more homogeneous structures having fewer pores can be realized by carefully milling and processing the raw materials.

(39) In summary it can be stated that it is possible to provide an excellent composite for the production of refractories, starting from andalusite as a low-priced raw material, whereby the composite is characterized by high thermal shock resistance and excellent corrosion resistance.