DVC-COATING WITH FULLY AND PARTIALLY STABILIZED ZIRCONIA

Abstract

A dense vertical cracked microstructure in a ceramic layer system made of an underline partially stabilized zirconia layer and an above laying fully stabilized zirconia layer show good erosion resistance and long life time is provided.

Description

CROSS-REFERENCE TO RELATED APPLICATIONS

This application claims priority to PCT Application No. PCT/EP2016/059828, having a filing date of May 3, 2016, based on European Application No. 15172884.7, having a filing date of Jun. 19, 2015, the entire contents both of which are hereby incorporated by reference.

FIELD OF TECHNOLOGY

The following relates to a ceramic layer-system with partially and fully stabilized zirconia which has also a dense vertical cracked microstructure (DVC).

BACKGROUND

Field feedback has shown that the current Thermal Barrier Coatings (TBC) of turbines suffer from issues related to:

1) Erosion: turbine blades with high porosity coatings containing a large number of unmolten or semimolten particles show low erosion resistance. The development during the last years has pushed thermal spray coatings porosity upwards. However, that has caused the shrinkage of the spray ability window that allows coatings to receive high porosity and good cohesion. As a result, erosion has started manifesting itself as a major issue for coatings in specific parts and engines.
2) Drilling damage: High porosity coatings contain less intimate contacts between splats or splat and substrate and thus the required energy for a crack to propagate is relatively low.
This problem has been addressed by drilling before the coating deposition and reopening of the holes after coating deposition. This approach minimizes the interaction between coating and laser and that reduces significantly the coating delamination around the drilled holes. However, since each part has to be processed twice, this solution is associated with longer drilling times that are reflected as increased cost.
3) Coating life: Thermal Spray porous coatings do not demonstrate at the same level the high strain tolerance along the coating thickness which can be seen in other coating types such as EB-PVD.
The thermal barrier coatings porosity has been increased to improve strain tolerance. However as mentioned above, that can reduce the spray ability process window and influence negatively the cohesion and erosion resistance of the coatings.
4) YSZ for TBC chemistries are currently limited to 1528° K maximum temperature due to phase transformation issues. New chemistries have been adopted that present phase stability in higher temperatures. However they show significantly lower fracture toughness compared to the partially stabilized zirconia and it is certain that their erosion resistance will be even less.

BRIEF DESCRIPTION

The FIGURE shows a DVC-coating with fully and partially stabilized zirconia

DETAILED DESCRIPTION

The problems named under point 1 are addressed by adopting Dense Vertical Cracked (DVC) coatings.

1) Erosion. DVC thermal barrier coatings have shown significantly lower rates compared to their porous counterparts. That means for the same chemistry a porous coating will show more than 3× the erosion rate compared to the DVC one.
2) DVC coatings have increased cohesion and adhesion compared to the typical porous coatings. The reason is that a very high ratio of fully molten particles deposit on hot substrate or hot previously deposited splats which promotes a good intimate bonding to develop between them. Improved adhesion requires high energy for a horizontal crack to propagate so that guarantees a lower delamination.
3) Coating life. Due to the intimate contact between splats, the DVC coatings show high fracture toughness along the parallel to the substrate plane. That, combined with their ability to accommodate thermal strain along the coating thickness due to their columnar microstructure ensures a high TBC life.
4) DVC microstructures can be adopted on the new coating chemistries. That will create a bilayer DVC with partially stabilized zirconia as a lower layer and fully stabilized zirconia as the upper layer. The lower layer will accommodate CTE mismatch with the bond coat and the TGO while the upper layer will provide the higher temperature capability.

The system consists of partially stabilized zirconia, especially 8YSZ as the high fracture toughness lower layer to accommodate the CTE mismatch with bond coat and TGO and a lower toughness upper layer of fully stabilized zirconia, especially 48YSZ to provide the high temperature capability.

Unlike other possible bilayer coating approaches, the similar chemistry between the two coatings enhances their bonding.

Appropriate preheating of the DVC PSZ will prepare its surface to receive the fully molten particles of FSZ and due to the high local temperatures during spraying allow diffusion between the two similar materials. Ideally a number of the vertical cracks will progress from one coating to the other demonstrating the continuity between the two coatings. In this manner the interface which has shown to be the weakest link in other bi-layer systems will be reinforced.

The advantages that arise are:

1) The low fracture toughness of the FSZ with the adoption of a DVC microstructure will significantly increase. That will improve the erosion resistance of the coating.
2) A good bonding between the two layers and as well with the bond coat will increase the drilling damage tolerance. Less delamination will be observed compared to other bilayer coating systems which have suffered in the past from drilling.
3) The columnar microstructure along the bilayer coating thickness will allow improved strain tolerance, thus increased coating life.
4) Higher temperature capability compared to single layer DVC coatings.

The FIGURE shows a layer system 1.

The layer system 1 comprises a substrate 4 which is preferably metallic and very preferably made of a nickel or cobalt based super alloy.

On the substrate 4 a bond coat especially a metallic bond coat 7 and very especially a NiCoCrAlY-based bond coat 7 is applied on.

On this bond coat 7 there is a thermally grown oxide (TGO, not shown) layer which is formed during further application of the ceramic layers or by an additional oxidation step or at least during use of the layer system 1.

On the bond coat 7 there is applied a first zirconia layer 10 made of a partially stabilized zirconia.

The thickness of the partially stabilized zirconia layer 10 is preferable between 75 μm-800 μm.

The porosity of the partially stabilized zirconia 10 is preferably lower than 5% and very preferably lower than 3%.

As an outer ceramic layer there is applied a fully stabilized zirconia layer 13, which is especially the outer most layer of the layer system 1.

This outer layer can also be made of a pyrochlore ceramic, such as gadolinium zirconate (GZO), which partially or fully replaces the fully stabilized zirconia (FSZ).

The porosity of the fully stabilized zirconia 13 is lower than 5% and preferably lower than 3%.

The thickness of the fully stabilized zirconia 13 is preferable between 50 μm-800 μm.

The same parameters for thickness and porosity are also valid for the pyrochlore layer or pyrochlore/FSZ layer.

The stabilization in this zirconia based system can be reached by yttria or by any other rare earth element as known by the state of the art or by a combination of that.

Preferably yttrium is used for stabilization.

In this layers 10, 13 there are cracks 16 present, which 19 are mostly present in the outer most layer 13 and preferably some of them 21 are present in both layers 10, 13.

Although the invention has been illustrated and described in greater detail with reference to the preferred exemplary embodiment, the invention is not limited to the examples disclosed, and further variations can be inferred by a person skilled in the art, without departing from the scope of protection of the invention.

For the sake of clarity, it is to be understood that the use of “a” or “an” throughout this application does not exclude a plurality, and “comprising” does not exclude other steps or elements.

Claims

1. A ceramic layer system, at least comprising:

a substrate made of a an inner partially stabilized zirconia layer and on it a fully stabilized zirconia layer, wherein vertical cracks are present.

2. The ceramic layer system according to claim 1, wherein the fully stabilized zirconia layer is replaced partially or fully by a layer comprising or consisting of a pyrochlore material.

3. The ceramic layer system according to claim 1, wherein the cracks are only present in the fully stabilized zirconia layer or the outer layer with the pyrochlore material.

4. The ceramic layer system according to claim 1, wherein the cracks are present in both ceramic layers.

5. The ceramic layer according to claim 1, wherein the porosity of the fully stabilized zirconia layer or the layer with the pyrochlore material is lower than 5%.

6. The ceramic layer system according to claim 1, wherein the thickness of the partially stabilized zirconia layer is between 75 μm-800 μm.

7. The ceramic layer system according to claim 1, wherein the thickness of the fully stabilized zirconia layer or the layer with the pyrochlore material is between 50 μm-800 μm.

8. The ceramic layer system according to claim 1, wherein the zirconia or the zirconia layers are stabilized by yttria.

9. The ceramic layer system according to claim 1, wherein the porosity of the partially stabilized zirconia layer is lower than 5%.

10. The ceramic layer system according to claim 1, wherein the partially stabilized zirconia is stabilized by yttria.

11. The ceramic layer system according claim 1, wherein the substrate is a metallic substrate.

12. The ceramic layer system according claim 1, wherein the substrate has a metallic bond on the substrate.

13. The ceramic layer system according claim 1, wherein the substrate is a NiCoCrAlY-based alloy.