Patent Application
20080057189
This invention relates to coatings for turbine blades and particularly to the simultaneous treatment of the internal and external surfaces of turbine blades.
Today the modern industrial gas turbine operates under conditions that are very aggressive for the nickel and cobalt alloys that are typically used in an engine's hot section. Therefore these alloys are attacked rapidly by the atmosphere in this region of the turbine causing them to degrade and necessitate their premature replacement. The metals that are added to nickel or cobalt alloys to improve the alloys' resistance to corrosive and oxidative environments cannot be added in sufficient concentrations without having a detrimental effect on the alloys' mechanical properties. It is for this reason that protective coatings have been developed thus producing the properties that are required at the surface of the component without having a detrimental effect on the mechanical properties of the base material.
Nowadays the surface engineering solutions used on industrial gas turbines are very diverse and several coating systems may be utilized on an individual turbine blade.
The chemically aggressive environment within land-based power generation gas turbines may lead to corrosion involving alkali and transition metal sulphates at temperatures from 600 to 800° C. (Type II corrosion), corrosion involving molten sulphates from 750 to 950° C. (Type I corrosion), and gaseous oxidation at higher temperatures. Protection of the base material under such conditions is difficult and requires the use of corrosion resistant coatings. Separate coating compositions need to be used for the differing corrosion environments, typically a chromia former (e.g. a chromide diffusion coating) to protect against Type II attack and an alumina former (e.g. an aluminide diffusion coating) for Type I and high temperature attack.
It is standard in the art to employ aluminide coatings to protect turbine blades from high-temperature oxidation and corrosion. It is also currently accepted that enrichment of the surface layer with aluminum provides satisfactory protection against Type I sulphidation. This is the result of the formation of an alumina scale that provides an effective barrier to the penetration of corrosive elements, such as sulphur and oxygen. Chromium cannot be used at the elevated temperatures that are experienced when Type I sulphidation is seen since the oxide scale formed by chromium has a significant vapour pressure at these temperatures. This means that the scale effectively evaporates from the surface and the protection is lost. This is the typical situation observed on the external surface of a gas turbine blade.
At elevated temperatures the turbine blades must be cooled. Cooling may be achieved by forcing compressed air, which may contain sulphur besides oxygen, through cooling channels in the turbine blade. Accordingly, the temperatures experienced on the metal surfaces in this internal region are lower than the temperatures experienced on the external surfaces. Aluminum scales do not form readily at these temperatures where Type II sulphidation occurs and hence aluminum does not provide effective protection against this type of attack. However, chromium oxide scales form readily at this temperature and are also physically stable and hence do provide effective protection against this type of attack.
Therefore the preferred coating system on a turbine blades where Type II sulphidation occurs on the internal surfaces and Type I sulphidation occurs on the external surfaces is aluminum coatings on the external surface and chromium coatings on the internal surfaces.
As well as the turbine blades, the vanes are also made from similar materials to the blades and may also have cooling channels. They are, therefore, subject to similar attacks as the blades.
It is common in the industry that chemical vapour deposition (also termed “diffusion coatings”) is used to apply these protective coatings to industrial gas turbines. In general these coatings are formed when the surface that requires protection is brought into contact with an atmosphere that is rich in the metal to be deposited on the surface. The metal species is usually in the form of a volatile halide. This deposition occurs generally at elevated temperatures (i.e. in excess of 800° C.) and in the presence of a reducing atmosphere, such as hydrogen.
Diffusion coatings of chromium and aluminum are applied in two separate coating runs However there are several disadvantages to this approach as a viable industrial process. For example, two consecutive processes increases the cost for protecting the turbine blade, it adds significantly to the time that it takes to carry out the process, and the second process to be carried out affects the results of the first coating process.
Accordingly, the present invention provides a process for coating an external and an internal surface of a turbine blade or vane with aluminum and chromium, respectively, at substantially the same time comprising the following steps (i) and (ii) in either order: (i) applying to the external surface an aluminizing compound comprising aluminum, a moderator, an energizer and a diluent; (ii) applying to the internal surface a chromizing compound comprising chromium, an energizer and a diluent; followed by: (iii) heating the turbine blade or vane to form an aluminum layer on the external surface and a chromium layer on the internal surface.
There is a distinct commercial and technical advantage in applying the chromium and aluminum protective coatings at the same time.
The present invention will now be described with reference to the accompanying drawing, in which the Fig. shows a schematic representation of a turbine blade with internal cooling channels suitable for use with the process of the present invention.
With reference to the Fig., area A (external surfaces) is to be coated with an aluminum diffusion coating and area B (internal surfaces) is to be coated with chromium diffusion coating. The applicant has found that by modifying both the aluminizing compound and chromizing compound both coatings may be applied substantially simultaneously.
The external aluminum diffusion coating is applied by immersing the complete blade or vane in an aluminizing compound (or “pack”). The aluminizing compound comprises aluminum metal powder, a moderator, a ceramic diluent and an energizer.
For aluminization, an aluminum halide is generated in situ. Accordingly, the aluminizing compound contains aluminum in an amount to produce sufficient aluminum halide to coat the external surface of the blade or vane. The aluminum content is preferably 3-20 wt % based on the total weight of the aluminizing compound.
A moderator, usually a metal powder such as chromium, nickel or iron, is required to absorb the aluminum halide vapour produced in situ to provide a reduced vapour pressure of aluminum halide vapour at the surface of the blade or vane which encourages diffusion into the surface alloy rather than deposition of a layer of aluminum on the surface of the alloy. The amount of moderator must be sufficient to provide diffusion rather than deposition. However, since diffusion is temperature controlled, as the temperature increases, diffusion is favoured and hence less moderator is required. In addition, the aluminizing compound of the present invention employs a greater than usual content of moderator so that aluminizing may take place under the same conditions as chromizing. Preferably the moderator is present at 10-50 wt %, based on the total weight of the aluminsing pack. The ratio of aluminium to moderator is typically 1:2 to 1:5, preferably 1:2.5 to 1:3.5, more preferably 1:2.5.
The energizer used for the aluminizing process generally contains a halide element such as bromide, chloride or fluoride. The preferred halides are alkali metals, e.g. sodium, and ammonium, ammonium chloride being particularly preferred. The energizer is generally present at 0.1-2 wt %, preferably 0.5 wt %, based on the total weight of the aluminising pack.
The diluent is generally a refractory oxide powder that makes up the balance of the ingredients in the aluminizing pack. The diluent is preferably Al2O3 (alumina), TiO2 (titania), MgO or Cr2O3. The most preferred refractory diluent is calcined alumina. The diluent content must be sufficient to keep the aluminizing pack free flowing which is typically at least 20 wt %, preferably at least 25 wt %, based on the total weight of the aluminising pack.
The aluminizing compound is present in a sufficient amount to generate a sufficiently thick coating of aluminum. A sufficiently thick coating is typically 60 to 100 μm. The aluminum concentration at the surface blade or vane is generally 25 to 45 wt %, the remainder being the base alloy.
Such an aluminizing compound is not known in the art and hence the present invention also provides an aluminizing compound comprising 3-20 wt % aluminium, 10-50 wt % moderator, 0.1-2 wt % energiser and at least 20 wt % diluent, wherein the weight ratio of aluminium to moderator is from 1:2 to 1:5.
The external surface of the turbine blade or vane may be pre-treated, e.g. sprayed with an additional coating, before aluminization if required.
The internal surface is chromized at substantially the same time as the external surface by also charging the internal cooling channels with a chromizing compound. By substantially the same time, it is meant that the aluminizing compound and the chromizing compound are both initially applied to the turbine blade or vane and then both coatings are then formed during the subsequent diffusion heat treatment.
The chromizing compound comprises chromium metal powder, a ceramic diluent and an energizer.
For chromization, a chromium halide is also generated in situ. Accordingly, the chromizing compound contains chromium in an amount to produce sufficient chromium halide to coat the internal surface of the blade or vane, i.e. the cooling holes. The chromium content is preferably 15-65 wt % based on the total weight of the chromising compound.
The energizer used for the chromizing process generally contains a halide element such as iodide, bromide, chloride or fluoride. The preferred halides are alkali metals, e.g. sodium, and ammonium, ammonium chloride being particularly preferred. The energizer is generally present at 0.1-5 wt %, preferably 1 wt %, based on the total weight of the chromising compound.
The diluent is generally a refractory oxide powder that makes up the balance of the ingredients in the chromizing compound. The diluent is preferably Al2O3 (alumina), TiO2 (titania), MgO or Cr2O3. The most preferred refractory diluent is calcined alumina. The diluent content must be sufficient to keep the chromizing pack free flowing which is typically at least 20 wt %, preferably at least 25 wt %, based on the total weight of the chromising pack.
The particles of the chromizing compound must have a sufficiently small particle size to allow a sufficient amount of the chromizing compound to access the internal surfaces, i.e. to get into the cooling holes, and therein to generate a sufficiently thick coating of chromium. A sufficiently thick coating is typically 10 to 60, preferably 10 to 50, most preferably 10 to 20 μm. The chromium concentration at the surface of the cooling hole is generally 30 to 60 wt %, the remainder being the base alloy. The particle size of the chromizing compound is preferably 200 μm mesh size or less, preferably 100 μm mesh size or less, most preferably 75 μm mesh size or less. Any minimum value (excluding zero) may be used although as the particle size gets lower the pack becomes more expensive and the benefits of the reduced particle size decreases.
Such a chromizing compound is not known in the art and hence the present invention also provides a chromizing compound comprising 15-65 wt % chromium, 0.1-5 wt % energiser and at least 20 wt % diluent, wherein the particle size of the chromising compound is such that the chromising compound is capable of passing through a 200 μm mesh or less.
During the substantially simultaneous aluminizing and chromizing processes the aluminizing and chromizing compounds should be protected from attack by atmospheric oxygen. Protection may involve an inert atmosphere, which may be produced by ammonium salts present in the compounds which decompose at elevated temperatures to liberate hydrogen. Alternatively, or in addition, protection may be provided by a reducing atmosphere, such as hydrogen or a hydrogen-containing gas mixture, e.g. 5% hydrogen in argon.
The retort containing the various coating compounds and the turbine blade or vane is placed in a furnace that is provided with an inert or reducing atmosphere, typically 5% hydrogen in argon or pure hydrogen. The turbine blade or vane in the furnace is then heated to a temperature from 850 to 1150° C., preferably 900 to 1100° C., more preferably 1000 to 1050° C., for 1 to 24 hours, preferably 2 to 10 hours, under the above protective atmosphere. After this treatment cycle the component is allowed to cool to ambient temperature under the protective atmosphere. The blade or vane is then removed from the aluminizing compound and gentle tapping or vibration removes the chromizing compound. After the removal of the excess coating compounds from the surface of the blade it is desirable to heat treat the blade so that the required mechanical properties can be achieved in the base material.
The cooling holes of a turbine blade are charged with a chromizing compound containing 30 wt % chromium metal powder, 69 wt % calcined alumina and 1 wt % ammonium chloride. The blade is then immersed in an aluminising compound containing 18 wt % aluminium metal powder, 45 wt % chromium metal powder and 0.5 wt % ammonium chloride, the balance being calcined alumina. The retort containing the various coating compounds and the turbine blade is placed in a furnace under a reducing atmosphere of 5% hydrogen in argon. The turbine blade in the furnace is then heated at a temperature of 1040° C. for 6 hours under the above protective atmosphere. After this treatment cycle the turbine blade is allowed to cool to ambient temperature under the protective atmosphere. The blade is then removed from the aluminizing compound and the chromizing compound removed by gentle tapping. After the removal of the excess coating compounds from the surface of the blade, the blade is heat treated so that the required mechanical properties can be achieved in the base material.
The resulting blade has its internal surfaces coated with chromium to a sufficient thickness to resist type II corrosion and its external surfaces coated with aluminum to a sufficient thickness to resist type I corrosion
| Number | Date | Country | Kind |
|---|---|---|---|
| 0409486.8 | Apr 2004 | GB | national |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/GB05/00374 | 2/4/2005 | WO | 4/13/2007 |
