Turbine blade with coating for deterrence of reactivity of superalloy on basis of ni

FIELD: engines and pumps.

SUBSTANCE: invention is related to turbine blade with coating for deterrence of Ni-based superalloy reactivity. Specified coating is made by application of material for reactivity deterrence on Ni-based superalloy surface prior to application of diffusion aluminium coating. Material for reactivity deterrence represents pure Ru, alloy Co-Ru, alloy Cr-Ru or solid solution, the main component of which is Ru, at that creation of secondary reaction zones is deterred. Turbine blades are produced with higher resistance to Ni-based superalloy oxidation by deterrence of secondary reaction zones creation.

EFFECT: higher resistance to Ni-based superalloy oxidation.

7 cl, 4 tbl, 13 dwg, 2 ex

 

Background of the invention

The technical field to which the invention relates.

The present invention relates to a turbine blade. A turbine blade having a coating to deter reactivity of supersplash from Ni to increase the resistance to oxidation of supersplash based on Ni containment (control) formation of secondary reaction zone (SRZ).

Description of the prior art,

To improve the thrust and efficiency of aircraft engine requires its constituent high-temperature materials have superior high temperature properties and improved strength. In particular, superslow on the basis of Ni used in turbine blades, has exceptional high temperature strength, high temperature ductility and resistance to oxidation, thus improving the properties of supersplash makes a significant contribution to the improvement of engine operation. Further improvement of high temperature properties of supersplash on the basis of Ni was carried out to achieve the desired compliance associated with the increase in temperature in the inlet of the turbine or reducing the amount of cooling air.

Method of casting supersplash based on Ni has been the traditional casting, but was developed healthy lifestyles is fair cured casting, and then by casting a single crystal. In particular, to single-crystal supersplash add a heavy element, to strengthen it γ' crystallizing phase or solid solution. Improvement of single-crystal (SC) supersplash led to the creation of the first generation of supersplash (not containing Re), the second generation of supersplash (containing're about 3 wt.%) and the third generation of supersplash (containing Re from 5 to 6 wt.%) As you progress in the improvement increased the content of Re in superslave. Table 1 shows the single-crystal superalloys, typical for each supersplash from first generation to third generation and their compounds.

Table 1
Typical SC super alloys based on Ni and their chemical composition
MaterialELEMENT (%)
AlTiTaNbMoWReYHfCrCoENNi
The first generation SCPWA14805,01,5to 12.0-4,0that 0 ---10,05,0-The remaining part
CMSX-26,01,06,0-1,08,0---8,05,0-The remaining part
Rene N43,74,24,00,52,06,0---9,08,0-The remaining part
The second generation SCPWA14845,6-9,0-2,06,03,0-0,105,010,0-The remaining part
CMSX-45,61,06,5-0,66,03,0-0,106,510,0-The remaining part
Rene N56,2-6,5-1,55,03,00,010,157,0 7,5-The remaining part
The third generation SCCMSX-10the 5.70,28,00,10,45,06,0-0,032,03,0-The remaining part
Rene N66,0-7,00,31,06,05,00,010,204,013,0-The remaining part
TMS-756,0-6,0-2,06,05,0-0,103,0to 12.0-The remaining part
TMS-1216,0-6,0-3,06,05,0-0,103,06,0-The remaining part

Single crystal superalloys of the third generation have the high temperature settings and they are applied to turbine blades of the latest models of aircraft engines. However, these superalloys face p is allemani, which is illustrated in figa, namely, harmful needle phase called "phase TCP"is highlighted (deposited) after prolonged exposure to high temperatures and the strength of supersplash decreases with increase in the content of the specified phase of TCP.

The authors of the present invention and the other authors of inventions have already developed the fourth generation single crystal supersplash TMS-138, which, as a result of suppressing the formation of TCP by adding Ru, characterized by improved stability of the composition even after prolonged exposure to high temperatures. Figv illustrates the microstructure of TMS-138 after the test to rupture at a creep. From the image it is necessary that the formation of TCP phase is suppressed. It was confirmed that TMS-138, in particular, is characterized by exceptional advantages associated with temperature creep, vysokotehnicheskoe fatigue strength and nizkotoksichnoe fatigue strength. Table 2 shows the composition of the monocrystalline supersplash TMS-138.

Mo
Table 2
The chemical composition of TMS-138
MaterialELEMENT (wt.%)
AlTiTaNbWReYHfCrCoENNi
TMS-1385,9-5,6-2,95,9a 4.9-0,102,95,92,0The remaining part

About the above single-crystal superslave reported in patent document 1 and non-patent document 1, when a phase of TCP and SRZ reported in patent documents 2 and 3 and non-patent document 2.

In "DIFFUSION BARRIER LAYER according to patent document 2, the diffusion barrier coating is applied on single crystal alloy (SC) based on Ni and additional aluminum diffusion coating is applied so that the coating layer can have improved resistance to oxidation.

In A method of aluminising a superalloy" according to patent document 3, the phase of TCP or SRZ, which tends to be formed at the boundary between the aluminum diffusion coating and SC, modify by using the barrier layer.

[Patent Document 1]

Lined patent application of Japan No. 131163/1999, "Ni base single crystal alloy and manufacturing method there of".

[Patent Document 2]

U.S. patent No. 6306524.

[Patent Document 3]

European patent application No. 0821076.

[Non-patent Document is NT 1]

Yasuhiro Aoki, et al., "Present situation and problems in development of turbine blade materials for aircraft engine". Research Report of Heat-resistant Metal Material 123 Committee, Vo. 43, No.3.

[Non-patent Document 2]

W.S. Walston, et al., "A NEW TYPE OF MICROSTRUCTURAL INSTABILITY IN SUPERALLOYS-SRZ", Superalloys, 1996.

Resistant to oxidation coating must be deposited on the surface of the turbine blade to prevent its high-temperature oxidation. Traditionally was used for this aluminum diffusion coating. In the test result on the oxidation and burst tests, using as a test material above monocrystalline superslow (TMS-138), which was applied aluminum diffusion coating, it was found that the coating causes a homogeneous formation of SRZ as shown in figa and 2B and greatly reduces damage during creep as shown in figure 4.

The essence of the invention.

The present invention is made to overcome the above problems. Therefore, the present invention relates to a turbine blade having a coating to deter reactivity, can improve the resistance to oxidation of supersplash based on Ni and at the same time to control the formation of SRZ.

Thus, according to the present invention is proposed turbine blade coated to deter reactivity, which is formed on what esteem material for containment (control) reactivity on the surface of supersplash based on Ni before applying the aluminum diffusion coating on superslab based on Ni, when this material to control the reactivity represents Co, Cr or Ru, or an alloy, the main component of which is selected from the group consisting of Co, Cr, Ru.

In one preferred embodiment of the present invention, the material for containment (control) reactivity is any material of pure Co, pure Cr, EN pure, alloy Co-Cr alloy, Co - Ru alloy Cr-Ru solid solution, solid solution of Cr in solid solution of Ru. Preferably, the material for the control of the reactivity of an alloy or solid solution, the main component of which is Co, Ru, or combinations thereof, and the alloy or solid solution contains from 0 to 10 wt.% With and from 90 to 100 wt.% Ru, or contains from 50 to 80 wt.% With and from 20 to 50 wt.% EN. More preferably, the material for the control of the reactivity of an alloy or solid solution, the main component of which is Co, Ru, or combinations thereof, and the alloy or solid solution contains Co and Ru with respect With to EN equal 5:95, 10:90, 50:50 or 80:20.

Preferably, superslow based on Ni, is monocrystalline superslam containing from 5 to 6 wt.% Re or single-crystal superslam, not only containing from 5 to 6 wt.% Re, but also containing Ru. In addition, preferably, superslow on the basis of Ni is monocrystalline soup is splawa, containing at least about 6 wt.% Re or single-crystal superslam, not only containing at least 6 wt.% Re, but also containing Ru.

Particularly preferably, superslow based on Ni, an alloy TMS-138, containing 5 wt.% Re and 2 wt.% EN, and material for containment (control) reactivity of the alloy is the Co-Ru, with the main components of Co and Ru. Preferably, superslow on the basis of the Ni alloy is TMS containing from 5 to 7 wt.% Re and from 4 to 7 wt.% EN, and materials to control the reactivity of the alloy is the Co-Ru, with the main components of Co and Ru.

Using examples confirmed that the oxidation resistance of supersplash based on Ni, which is the turbine blade may be increased, and the formation of SRZ can be controlled by using a coating supersplash based on Ni material for control of reactivity according to the present invention before application of the aluminum diffusion coating.

The said coating to control the reactivity is particularly effective when it is applied to the third generation and fourth generation single crystal superalloys, which have a tendency to form SRZ due to the aluminum diffusion coating.

Other objectives and preferred features of the present izopet the Deposit will be clearly understood from the detailed description with reference to the accompanying drawings.

A brief description of the drawings.

Each of figa and 1B shows typical microstructure after the test to rupture at a creep.

Each of figa and 2B shows the results of tests on the oxidation of the test sample subjected to traditional aluminum diffusion coating.

On figa shows SEM image of the cross representstartar test sample, subjected to diffusion coating of Al after the test for oxidation and FIGU is a map of the distribution of Ru in the sample.

Figure 4 illustrates the relationship between the plate thickness and the time of destruction during creep.

Figa and 5B are images of the cross-section microstructure of the test sample, which was covered with pure Ru in terms of B, and then was caused to aluminum diffusion coating, before and after the test for oxidation, respectively.

Figa and 6B are images of the cross-section microstructure of the test sample, which was covered by the alloy Co-EN in conditions B, and then was caused to aluminum diffusion coating, before and after the test for oxidation, respectively.

Figa and 7B are images of the cross-section microstructure of the test sample, which covered only the aluminum diffusion coating, before and after the test for oxidation according to the state.

Fig is a comparative chart of the thickness of the additional layers after the test for oxidation.

Fig.9 is the first comparative chart of the different thickness of the diffusion zones (layers) after the test for oxidation.

Figure 10 is the first comparative chart of different thickness SRZ (secondary reaction zones) after the test for oxidation.

11 is a comparative graph of mass loss of the test specimens after testing oxidation.

Fig is the second comparative chart of the different thickness of the diffusion zone after the test for oxidation; and

Fig is the second comparative chart of different thickness SRZ (secondary reaction zones) after the test for oxidation.

Description of preferred examples

The previously described concept of the present invention.

Typically monocrystalline-based superalloys Ni is called precipitation hardening alloys, and they have γ' phase, released in γ phase, which is the matrix. On the other hand, SRZ has γ phase and the phase of TCP, released in γ' phase, which is the matrix.

Diffusion coating of Al on the surface of the monocrystalline supersplash change the structural type from supersplash structural type SRZ. Phase γ', which is segregated phase su is erslev, coarsens and becomes a matrix SRZ.

In the present invention Ru is used not only to monitor the education phase of TCP, but also to control the escalation phase γ'.

On figa shows SEM image of the cross-section microstructure of the test sample, subjected to diffusion coating of Al after the test for oxidation and FIGU is a map of the distribution of Ru in the sample. On FIGU part, which is shown in relation to other parts, white, characterized by excessive levels of Ru.

As follows from the above image, with Ru are the problem, lies in its move to the adjacent side surface diffusion coatings of Al. In this regard, in the present invention, Co and Cr are used to suppress the movement EN (not only EN, which is used in coating for control of the reactivity, but also EN contained in superslave). However, Co and Cr are used to improve adhesion Ru.

These elements (Ru, Co, and Cr) is also used to suppress diffusion of Al.

In the blade of the turbine to control the reactivity according to the present invention, these elements can achieve their assigned roles additives as needed, when they are added in the corresponding optimal quantities. Floor to control the reaction pursue the activity, applied to obtain the coating thickness is preferably from 1 to 60 μm, more preferably from 1 to 20 μm, more preferably from 1 to 10 microns.

Preferred examples of the present invention will hereinafter be described with reference to accompanying figures. In all figures, the common parts will be marked with the same numeric symbol and duplicate description will be omitted.

[Example 1]

You must install the oxidation resistance system with floor to use monocrystalline superslab, such as alloy TMS-138, in the blade of the turbine aircraft engine. So I performed the test in order to establish that the reduction in fatigue life under creep of the base material is a consequence of the resistance of the coating to oxidation and to estimate coverage for reactivity control.

As described above, investigated the influence of the aluminum diffusion coating on the alloy TMS-138 using for testing thin plate. In the result, it was found that the decrease in fatigue life if the creep is associated with the formation of SRZ.

Therefore, in the specified test, the relationship between the decrease in durability due to the coverage and thickness of the plate explain, using the test samples, varying the plate thickness of the base material. At the same time, meet the t application of various coatings, having the ability to control the formation of SRZ, which would otherwise be formed due to the deposition of aluminum diffusion coating and assess the impact of coatings to control the formation of SRZ. Floor to control the formation of SRZ in the future will be called "coating for control of reactivity " (cover RC).

(Test conditions).

(1) the Test to determine that the decrease in fatigue life under creep of the base material caused by the coating, which is resistant to oxidation.

There were prepared test samples, varying in thickness from 1 to 3 mm, and were subjected to aluminum diffusion coating (including diffusion during aging). Testing to destruction when creep was performed in accordance with ASTM E139. Test conditions corresponded to 1373 K and 137 MPa. A comparative test was performed under similar conditions, using the sample to test (model test in the form of unsecured material) is not subjected to aluminum diffusion coating.

(2) Test coverage for reactivity control.

There were prepared test samples by applying the seven coatings RC with control SRZ, samples of alloy TMS-138 having a diameter of 20 mm and a thickness in the range of 2 to 3 mm, matched with the public, and then they were applied aluminum diffusion coating in a similar way as described in (1). Types of coatings RC are given in Table 3.

Table 3
Conditions coatings RC
RC material
100 at.% Co
40 at.% Co-60 at.% Cr
100 at.% Cr
80 at.% Cr-20 at.% EN
100 at.% EN*
80 at.% Co-20 at.% EN
60 at.% Co-25 at.% Cr-15 at.% W

After coating RC, which was carried out before applying the aluminum diffusion coating, the coating material RC was diffundiruet into the basic material in accordance with each of the two conditions A: long-time diffusion, B: a short time diffusion). It was completed a 500-hour oxidation test to confirm the presence of control over the formation of SRZ. Also measured the change in mass, which took place after 500 hour test on oxidation.

Before coating RC, the surface of the test sample was polished with emery paper #800 to reduce the influence of surface roughness and is enough stress in the initial state. The test conditions for oxidation will be described below. After the test for oxidation, monitoring the status of the SRZ was assessed by examining cross-sectional structure.

The test conditions for oxidation:

Temperature tests: 1373 K.

Test time: 0, 500 h

Atmosphere: air.

(The test results)

(1) the Decrease in fatigue life under creep of the base material a consequence of the resistance to oxidation of the coating.

Figure 4 shows the relationship between the plate thickness and the fatigue durability, while creep. Durability is expressed by a value obtained by dividing the measured durability on average durability unprotected material. Durability unprotected material is practically constant, regardless of changes in the thickness of the plate, but the durability of the material subjected to the coating decreases as the plate becomes thinner. The relationship between the logarithm of the thickness of the coated material and the logarithm of durability can be expressed by a linear function in the following diagram. When the value at which the coating effect can be neglected, extrapolate, we expect that the minimum plate thickness and the minimum area will be approximately 6 mm and 18 mm2.

(2) the Evaluation of the coating to control the reactivity.

On figa and 5 and figa and 6B show examples of results of research conducted before and after the test for oxidation. That is, in these figures shows a longitudinal cross-section test specimens subjected to coating RC + aluminum diffusion coating. For comparison, figa and 7B shows a longitudinal cross-section test specimens subjected only to the application of aluminum diffusion coating. To test for oxidation in the longitudinal cross-sections of any of the tested samples did not observe the presence of SRZ. After testing the presence of oxidation SRZ observed in longitudinal sections for each of the test samples.

For quantitative evaluation, the thickness of the coating layer (additional layer, the diffusion zone (layer)and the thickness of SRZ in their longitudinal sections calculated in relative units with the corresponding values in longitudinal section of the test sample subjected to the application of only aluminum diffusion coating.

On Fig-10 respectively shows the values of the additional layer, diffusion layer and SRZ, which are similarly calculated in relative units. The values given are in accordance with the types of coatings RC. On each graph, if the coating RC is not applied, the result is designated as 100, along the transverse axis. Respectively (A) and (B) indicate the time of diffusion to the deposition of the WPPT is usinage aluminum coating (A: a long time diffusion, B: a short time diffusion).

According to the assessment materials to cover approximately can be categorized into three groups, i.e. materials Co (Co, Co-Cr and Co-EN), proceedings of the Cr (Cr, Co-Cr and Cr-Ru), proceedings of the Ru (Ru, Co-Ru, and Cr-Ru) and three-component material (Co-Cr-W). These coatings will continue to be called "materials for control of reactivity".

Fig is a comparative chart of the different thickness of the additional layers after the test for oxidation. From the above chart it was found that additional layers of pure Co (B) and alloy Co-Ru only have a small thickness.

Fig.9 is the first comparative chart of the different thickness of the diffusion layer after the test for oxidation. From the above chart it was found that the diffusion zone of pure Co (A) and (B) and alloy Co-Ru (A) and (B) have an extremely small thickness.

Figure 10 is the first comparative chart of different thickness SRZs (secondary reaction zones) after the test for oxidation. From the above chart it was found that the secondary reaction zone of the alloy Co-Ru (B) and Co-Cr-W alloy (B) have an extremely small thickness.

As shown in figure 10, when the thickness of SRZ in longitudinal section of the test sample subjected to coating RC using Co-Ru, compared with the thickness in the longitudinal Sich, the research Institute of the test sample, subjected to the application of only aluminum diffusion coating, the first thickness is controlled by about 30%. It can be assumed that the formation of SRZ control in the diffusion suppressing aluminum element or stabilization of the coating layer. Similar effects can be expected when conditions change coating (thickness, temperature or the like) other materials to control reactivity.

11 is a comparative graph of weight loss of various test specimens after the test for oxidation. As weight loss, used the measured mass loss calculated in relative units on the weight loss of unprotected test sample (material without coating). The mass loss of any of the test specimens subjected to coating RC, was approximately 1% in comparison with the mass loss of the test sample unprotected material. On the basis of a small absolute value of weight loss, it follows that each layer of the coating has excellent resistance to oxidation.

[Example 2]

Using cover RC, which are shown in Table 4, the test coatings for control of reactivity were performed under similar conditions to those used in Example 1.

The table is 4
Conditions coatings RC
RC material
50 at.% Co-50 at.% EN
10 at.% With 90 at.% EN

Fig is the second comparative chart of the different thickness of the diffusion zone after the test for oxidation. From this chart, it was found that the diffusion zone 50 at.% Co-50 at.% EN only have a small thickness.

Fig is the second comparative chart of different thickness SRZ (secondary reaction zones) after the test for oxidation. From this chart, it was found that the secondary reaction zone of each of the 50 at.% Co-50 at.% Ru and 10 at.% Co-90 at.% EN only have a small thickness.

As shown above, using the above examples, it was confirmed that the oxidation resistance of supersplash based on Ni constituting the turbine blades may be increased, and at the same time can be controlled by the formation of secondary reaction zone by applying the material to control the reactivity of superslow before applying the aluminum diffusion coating. In other words, it was found that the coating (the coating to control reactivity) can not only control the phase of TCP and SRZ, but also can improve the ü oxidation resistance layer, subject to application of the aluminum diffusion coating. The said coating to control the reactivity is especially effective for the third generation and fourth generation single crystal superalloys, which have a tendency to form secondary reaction zone by diffusion of the aluminum coating.

Accordingly, the turbine blade with the control of the reactivity according to the present invention has excellent effects such as increased resistance to oxidation of supersplash based on Ni and control over the formation of a secondary reaction layer (zone).

There is no doubt that the present invention is not limited to the above examples and options for implementation and can be modified without going beyond the scope of the present invention.

1. A turbine blade having a coating to deter reactivity of supersplash on the basis of Ni formed by applying the material for containment reactivity on the surface of supersplash based on Ni before applying the aluminum diffusion coating, in which the material for containment reactivity represents net Ru alloy Co-Ru alloy Cr-Ru or solid solution, the main component of which is EN, while constrained by the formation of secondary PE is czynnik zones.

2. The turbine blade according to claim 1, in which the material for containment reactivity of an alloy or solid solution, the main component of which is Co, Ru, or a combination, with the solid solution contains from 0 to 6.1 wt.% With and from 93,9 to 100 wt.% Ru, or contains from 36,8 to 70 wt.% With and between 30 to 63.2 wt.% Eng.

3. The turbine blade according to claim 1, in which the material for containment reactivity of an alloy or solid solution, the main component of which is Co, Ru, or a combination, the alloy or solid solution contains Co and Ru with With respect to EN, equal 5:95, 10:90, 50:50 or 80:20.

4. The turbine blade according to claim 1, in which superslab on the basis of Ni is monocrystalline superslam containing from 5 to 6 wt.% Re, or single-crystal superslam, not only containing from 5 to 6 wt.% Re, but also containing Ru.

5. The turbine blade according to claim 1, in which superslab on the basis of Ni is monocrystalline superslam containing at least 6 wt.% Re, or single-crystal superslam, not only containing at least 6 wt.% Re, but also containing Ru.

6. The turbine blade according to claim 1, in which superslow based on Ni is the alloy TMS-138, containing 5 wt.% Re and 2 wt.% EN, a material for containment reactivity of the alloy is the Co-Ru, with the main components of Co and Ru.

7. The blade that is Bina according to claim 1, in which superslab on the basis of the Ni alloy is TMS containing from 5 to 7 wt.% Re and from 4 to 7 wt.% EN, and material for containment reactivity of the alloy is the Co-Ru, with the main components of Co and Ru.



 

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EFFECT: enhanced wear resistance of tool, improved quality of rolled tubes.

FIELD: metallurgy, namely chemical and heat treatment of refractory alloys, possibly used for applying protective coatings onto blades of gas-turbine engines.

SUBSTANCE: method comprises steps of applying onto inner and outer surfaces of parts diffusion aluminide coating in circulating gaseous medium; applying coating in low-active system at relation of reaction surfaces Fн/Fo = 0.3 - 0.7, where Fн - total surface of parts to be coated; Fo - total surface of saturating mixture; then applying onto outer surfaces of parts cladding coating, namely MeCrAlY, where Me - Ni, Co, NiCo by ion-plasma process or electron beam evaporation in vacuum.

EFFECT: improved fire and corrosion resistance of coating, increased resource of blades of gas-turbine engine.

1 cl, 1 ex, 1 tbl

Method of coating // 2199605
The invention relates to the field of metallurgy, in particular to methods of diffusion saturation of the surface layers of materials, and can be used in aviation, shipbuilding and power engineering industry

The invention relates to methods for coating of metals, in particular aluminum using a solid source materials

The invention relates to electrical engineering and the production of elektroprovodnyh of intermetallic compounds, in particular of spirals used as heaters

FIELD: forming inter-metallic layer on metal part, especially on parts of jet engine at air flow over it.

SUBSTANCE: proposed method includes application of modifier on at least one selected section of metal part surface. Then metal part is placed in sedimentation medium and donor material acts on selected section of part surface during period of time sufficient for forming inter-metallic layer containing metal obtained from donor material. Modifier forms inter-metallic layer on this modified section of surface. Thickness of inter-metallic layer exceeds thickness of inter-metallic layer formed on said section of surface subjected to action of donor material in sedimentation medium without modifier applied on it preliminarily. Modifier is selected from group consisting of metal halogen Lewis acid, silane material and colloid silicon oxide.

EFFECT: facilitated procedure of forming inter-metallic layer of required thickness.

41 cl, 13 dwg

The invention relates to a thermal diffusion process and can be used for coating a building structure, as well as in the engineering and chemical industries
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