Patent Application
20100230871
The present invention relates to sintering of ceramic materials, in particular for sintering ceramic materials for solid oxide fuel cell components or ceramic materials for gas turbine engine components and more particularly for ceramic coatings on gas turbine engine components or ceramic layers in solid oxide fuel cell components.
In a conventional process for sintering ceramic materials the temperature of a ceramic powder is increased at a predetermined rate and then the temperature is held constant at the maximum temperature until maximum density is achieved. The grain size of the ceramic material increases continuously with the density. This sintering process comprises three stages. A first stage, prior to sintering, in which an organic binder is burned out of the ceramic material and gaseous products of decomposition and oxidation are eliminated from the ceramic material. A second stage, sintering, in which the ceramic material is sintered at elevated temperature, greater than half the melting point of the ceramic material, for a predetermined time to produce a dense ceramic body. A third stage, post sintering, in which the ceramic material is cooled to ambient temperature and this step may include thermal and chemical annealing.
A relatively high rate of increase of temperature reduces grain coarsening of the ceramic material. The isothermal hold at the maximum temperature reduces the porosity and the grains of the ceramic material grow. As the grains grow the strength of the ceramic body becomes weaker and thus is less tolerant to stresses from changes in temperature and environment. As the grains grow and become equal in thickness to the thickness of the sintered layer the driving force for densification is greatly reduced and therefore the driving force for grain growth decreases with increasing grain size. The cooling rate is selected to produce a ceramic body without damage.
There are two different types of sintering, constrained sintering and unconstrained sintering. In unconstrained sintering the ceramic grains are free to move in all directions equally, i.e. in mutually perpendicular x, y and z directions. In constrained sintering the ceramic grains are constrained by a fixed substrate and the ceramic grains are free to move in only one direction, i.e. the x and y directions are fixed and movement only in the z direction. The different sintering types produce different sizes of interstices between the ceramic grains, e.g. the unconstrained sintering produces smaller interstices between the ceramic grains.
Thus, the sintering of ceramic layers, or ceramic coatings, on other components suffers from an inability to provide adequate density for the ceramic layers or ceramic coatings.
Accordingly the present invention seeks to provide a novel method of sintering a ceramic material that reduces, preferably overcomes, the above- mentioned problem.
Accordingly the present invention provides a method of sintering a ceramic material comprising the steps of
Preferably step a) increases the temperature of the ceramic material at a rate between 0.1° C. min−1 and 20° C. min−1.
Preferably step c) increases the temperature of the ceramic material at a rate between 0.1° C. min−1 and 20° C. min−1.
The ceramic material may comprise alumina, step a) comprises increasing the temperature of the alumina to a first predetermined temperature of 1080° C., step b) comprises maintaining the temperature of the alumina at the first predetermined temperature of 1080° C. for a first predetermined time period of 4 hours to increase the grain size of the alumina, step c) comprises increasing the temperature of the alumina to a second predetermined temperature of 1750° C., step d) comprises decreasing the temperature of the alumina to a third predetermined temperature of 1550° C. to freeze the grain size of the alumina, step e) comprises maintaining the temperature of the alumina at the third predetermined temperature of 1550° C. for a third predetermined time period of 8 hours to densify the alumina and step f) comprises decreasing the temperature of the alumina to ambient temperature.
Preferably step a) increases the temperature at a rate of 20° C. min−1.
Preferably step a) includes a preliminary increase in temperature to burn out organic binder and remove gaseous products.
Preferably step c) increases the temperature at a rate of 20° C. min−1.
Preferably step d) decreases the temperature at a rate of 40° C. min−1 over time period t4.
Preferably step f) decreases the temperature at a rate of 20° C. min−1.
The ceramic material may comprise zirconia, step a) increases the temperature of the zirconia to a first predetermined temperature of 950° C. to 1200° C., step b) maintains the temperature of the zirconia at the first predetermined temperature of 950° C. to 1200° C. for a first predetermined time period of 4 to 20 hours to increase the grain size of the zirconia, step c) increases the temperature of the zirconia to a second predetermined temperature of 1200° C. to 1600° C., step d) decreases the temperature of the zirconia to a third predetermined temperature of 1000° C. to 1500° C. to freeze the grain size of the zirconia, step e) maintains the temperature of the zirconia at the third predetermined temperature of 1000° C. to 1500° C. for a third predetermined time period of 4 to 20 hours to densify the zirconia, step f) decreases the temperature of the zirconia to ambient temperature.
Preferably step a) increases the temperature at a rate of 1° C. min−1 to 20° C. min−1.
Preferably step a) includes a preliminary increase in temperature to burn out organic binder and remove gaseous products.
Preferably step c) increases the temperature at a rate of 1° C. min−1 to 20° C. min−1.
Preferably step d) decreases the temperature at a rate of 40° C. min−1.
Preferably step f) decreases the temperature at a rate of 1° C. min−1 to 20° C. min−1.
Preferably a solid oxide fuel cell has a ceramic material sintered according to the method of the present invention. Preferably the ceramic material is a ceramic layer of the solid oxide fuel cell. Preferably the ceramic layer is an electrolyte layer of the solid oxide fuel cell.
Alternatively a gas turbine engine component has a ceramic material sintered according to the method of the present invention. The ceramic material may be a ceramic coating on the gas turbine engine component. The gas turbine engine component may be a turbine blade, a turbine vane or a combustion chamber.
The present invention will be more fully described by way of example with reference to the accompanying drawings in which:
A method of sintering ceramic materials according to the present invention, as illustrated in
In more detail the method of sintering the ceramic material comprises a first step, which increases the temperature of the ceramic material over time period t1 to a first predetermined temperature TC. The first step generally increases the temperature at a rate between 0.1° C. min−1 and 20° C. min−1 and this may include a preliminary increase in temperature to burn out organic binder and remove gaseous products. A second step maintains the temperature of the ceramic material at the first predetermined temperature TC for a first predetermined time period t2 to increase the grain size of the ceramic material. The first predetermined time period is purely dependent on the properties of the ceramic material. A third step increases the temperature of the ceramic material over a time period t3 to a second predetermined maximum temperature TM, wherein the second predetermined maximum temperature TM is greater than the first predetermined temperature TC. The third step generally increases the temperature at a rate between 0.1° C. min−1 and 20° C. min−1. A fourth step decreases the temperature of the ceramic material over time period t4 to a third predetermined temperature TD to freeze the grain size of the ceramic material. Ideally the time period t4 is zero. However, the time period t4 is as small as practically possible and is determined by the sintering equipment employed. A fifth step maintains the temperature of the ceramic material at the third predetermined temperature TD for a third predetermined time period t5 to densify the ceramic material. The third predetermined time period is purely dependent on the properties of the ceramic material. A sixth step decreases the temperature of the ceramic material over time period t6 to ambient temperature. The cooling rate for the ceramic material is determined by the ceramic materials tolerance to thermal shock, i.e. the ceramic material must be cooled at a rate such that the ceramic material is not damaged due to cracking etc.
As an example for sintering alumina, a first step increases the temperature of the alumina over time period t1 to a first predetermined temperature TC of 1080° C. The first step generally increases the temperature at a rate of 20° C. min−1 and this may include a preliminary increase in temperature to burn out organic binder and remove gaseous products. A second step maintains the temperature of the alumina at the first predetermined temperature TC, of 1080° C., for a first predetermined time period t2, of 4 hours, to increase the grain size of the alumina. A third step increases the temperature of the alumina over a time period t3 to a second predetermined maximum temperature TM, of 1750° C., wherein the second predetermined maximum temperature TM, 1750° C., is greater than the first predetermined temperature TC, 1080° C. The third step generally increases the temperature at a rate of 20° C. min−1. A fourth step decreases the temperature of the alumina over time period t4 to a third predetermined temperature TD, 1550° C., to freeze the grain size of the alumina. The temperature is decreased at a rate of 40° C. min−1 over time period t4. A fifth step maintains the temperature of the alumina at the third predetermined temperature TD, 1550° C., for a third predetermined time period t5, 8 hours, to densify the alumina. A sixth step decreases the temperature of the alumina over time period t6 to ambient temperature. The cooling rate for the alumina is 20° C. min−1 such that the alumina is not damaged due to cracking etc.
As an example for sintering yttria stabilised zirconia, a first step increases the temperature of the zirconia over time period t1 to a first predetermined temperature TC of 950° C. to 1200° C. The first step generally increases the temperature at a rate of 1° C. min−1 to 20° C. min−1 and this may include a preliminary increase in temperature to burn out organic binder and remove gaseous products. A second step maintains the temperature of the zirconia at the first predetermined temperature TC, of 950° C. to 1200° C., for a first predetermined time period t2, of 4 to 20 hours, to increase the grain size of the zirconia. A third step increases the temperature of the zirconia over a time period t3 to a second predetermined maximum temperature TM, of 1200° C. to 1600° C., wherein the second predetermined maximum temperature TM, 1200° C. to 1600° C., is greater than the first predetermined temperature TC, 950° C. to 1200° C. The third step generally increases the temperature at a rate of 1° C. min−1 to 20° C. min−1. A fourth step decreases the temperature of the zirconia over time period t4 to a third predetermined temperature TD, 1000° C. to 1500° C., to freeze the grain size of the zirconia. The temperature is decreased at a rate of 40° C. min−1 over time period t4. A fifth step maintains the temperature of the zirconia at the third predetermined temperature TD, 1000° C. to 1500° C., for a third predetermined time period t5, 4 to 20 hours, to densify the zirconia. A sixth step decreases the temperature of the zirconia over time period t6 to ambient temperature. The cooling rate for the zirconia is 1° C. min−1 to 20° C. min−1 such that the zirconia is not damaged due to cracking etc.
A solid oxide fuel cell 10, as shown in
A gas turbine engine turbine blade 20, as shown in
The present invention is also applicable to piezo-electric components for example comprising barium titanate (BaTiO3). The present invention is also applicable to magnetic components for example comprising iron-copper-nickel ferrite (Fe—Cu—Ni-ferrite).
The advantage of the present invention is that the coarsening provides a homogeneous distribution of small pores, interstices, in the ceramic material and the grains of the ceramic material have been coarsened allowing the small pores, interstices, which are smaller than the ceramic grains to shrink at a relatively fast rate during freezing and densifying. The densifying maintains the ceramic material at a predetermined temperature, such that the pores, interstices, between the ceramic grains are reduced in size, thus homogenising the pore structure of the ceramic material increasing the density of the ceramic material.
The sintering process of the present invention may be used to sinter ceramic layers of solid oxide fuel cells, for example the electrolyte layer. The electrolyte layer of a solid oxide fuel cell is required to be a physical barrier between a gaseous fuel on an anode side of the electrolyte layer and a gaseous oxidant on a cathode side of the electrolyte layer. Any gaseous leak path through the electrolyte layer will allow fuel and oxidant to come into contact. This will cause a reduction in solid oxide fuel cell performance in terms of fuel utilisation and could be detrimental to the mechanical integrity and durability of the solid oxide fuel cell structure.
The sintering process of the present invention provides reduced porosity of the ceramic material in the electrolyte layer and therefore reduces the risk of gaseous fuel leakage through the electrolyte layer from the anode side to the cathode side of the electrolyte layer. In addition the ceramic material of the electrolyte layer has smaller grain size and has reduced stress and strain.
Thus the present invention has the ability to provide a dense microstructure in a layer, film or coating of ceramic material, which has been deposited onto a pre-existing layer, substrate or component with a reduced risk of defects, such as cracks and large pores, being present in the final sintered layer, film or coating of ceramic material.
The present invention is also applicable to ceramic coatings applied to gas turbine engine components, for example turbine blades, turbine vanes, combustion chambers etc.
| Number | Date | Country | Kind |
|---|---|---|---|
| 0605907.5 | Mar 2006 | GB | national |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/GB2007/000573 | 2/20/2007 | WO | 00 | 1/15/2009 |
