How eletrownia heat-resistant alloy with a high content of rhenium (options)

 

(57) Abstract:

The invention relates to the application of aluminide coatings on heat-resistant alloys, in particular on single-crystal heat-resistant alloys. How eletrownia heat-resistant alloy with a high content of rhenium includes the following steps: (a) modifying the surface of a heat-resistant alloy with a high content of rhenium by applying to the surface a layer of chromium or cobalt and heat treatment for diffusion of chromium or cobalt in high-temperature alloy with a high content of rhenium in order to reduce the content of rhenium on the surface of the heat-resistant alloy, and (b) eletrownia heat-resistant alloy with a high content of rhenium for education aluminide coating, the content of rhenium in the heat-resistant alloy is at least 3.5 wt.%. The technical result is to prevent the formation of topologically tightly Packed phases at the interface between aluminium coating and registertask monocrystalline heat-resistant alloy that promotes rapid degradation of protective coatings. 3 S. and 21 C.p. f-crystals, 6 ill.

The invention relates to the application of aluminide coatings on heat-resistant alloys, in particular on monoq the capacity turbines of gas turbine engines and guide vanes of turbines to provide high-temperature strength of the rotor blades and guide vanes of the turbines. However, changes in the composition of the single crystal alloys in comparison with previously known heat-resistant alloys leads to the fact that during operation increases the degradation of the surface. In addition, there is a requirement to ensure a long service life of turbine blades and guide vanes of the turbine. Therefore, these turbine blades and guide vanes of turbines from a single crystal superalloy not provide sufficient service life due to degradation due to corrosion and oxidation.

These single-crystal heat-resistant alloys usually contain rhenium, for example from 2 to 8 wt.%., together with relatively high levels of tungsten and tantalum for characterizing the high-temperature strength. These single-crystal heat-resistant alloys are very strong at high temperatures by taking advantage of rhenium, tungsten and tantalum.

To increase the durability of single-crystal turbine blades and guide vanes, it is desirable to protect the surface of single-crystal turbine blades and guide vanes protective coatings. One of the known types of protective coatings that obyavleniya coating is applied in two steps: first, cover the turbine blades or guide vanes platinum and then put on a platinum coating aluminum coating, using the plating process. The plating process can be performed by eletrownia in the coating protective coating, or by eletrownia in a gaseous environment without coating protective coating or by chemical vapour deposition or by any other means well known to specialists.

However, if the turbine blades or guide vanes of a single crystal of heat-resistant alloy with a high content of rhenium covered with a platinum-aluminum coating using known methods, on the boundary surface between the coating and the single-crystal heat-resistant alloy formed topologically densely Packed phase. A single crystal of heat-resistant alloys with a high content of rhenium are alloys containing more than ves.% rhenium. These topologically tightly Packed phases are formed immediately after eletrownia or after providing them exposure to high temperatures. Topologically densely Packed phase contain higher levels of rhenium, tungsten and chromium in comparison with single-crystal heat-resistant alloy, and they are easier formed with increasing levels of rhenium in monocrystalline jaroprochnykh temperatures. Topologically densely Packed phase have an adverse or harmful effect on the mechanical properties of single-crystal heat-resistant alloy. Therefore, the known platinum-aluminide coverage cannot be used to improve the resistance to degradation of single-crystal heat-resistant alloy with a high content of rhenium without deterioration of mechanical properties of single-crystal heat-resistant alloy.

Other types of protective coatings, which are widely used for turbine blades and guide vanes are aluminide-silicide coatings, platinum-aluminide-silicide coatings, just aluminide coverage and any other suitable aluminide coverage.

Aluminide coatings are applied using a plating process or eletrownia, for example, through processes eletrownia in a gaseous environment without coating protective coating, eletrownia in the coating protective coating, chemical vapour deposition and other processes well known to specialists.

One of the ways to get aluminide-silicide coatings is the deposition of organic suspensions with silicon filler on powertune USA 4 310 574. Aluminum silicon migrates from the suspension when difundieran in heat-resistant alloy. Another way to get aluminide-silicide coatings is the deposition of a suspension containing powders of elemental aluminum and silicon metal, on the surface of the heat-resistant alloy with subsequent heating to temperatures above 760oWith to melt the aluminum and silicon in suspension so that they are reacted with heat-resistant alloy and diffundiruet in heat-resistant alloy.

Another way of obtaining aluminide-silicide coatings is a repeated application of the suspension containing aluminum and silicon, and heat treatment, as described in U.S. patent 5 547 770. Another way of obtaining aluminide-silicide coatings is a process comprising applying a suspension of eutectic aluminum-silicon suspensions or powders of elemental aluminum and silicon metal on the surface of the heat-resistant alloy, the diffusion heat treatment for formation of the surface layer with increased thickness and reduced silicon content, and layering layer, which contains alternating contiguous layers sandwiched aluminide and silicide phases and diffusion of interfacial layer on the refractory is placed platinum-aluminide-silicide coatings is the way, including the application of platinum coatings on heat-resistant alloy, and then heating to ensure the diffusion of platinum in the turbine blades and then providing simultaneous diffusion of aluminum and silicon from the molten state in enriched platinum blades of the turbine, as described in European patent WO 95/23243 A. Another way of obtaining a platinum-aluminide-silicide coatings is a process involving the application of platinum coatings on superalloy turbine blades, and then applying a layer of silicon and then eletrownia (plating), as described in published European patent application 0654542 A. it is Also possible to diffuse silicon into the turbine blades, as described EP 0654542 A. Another way of obtaining a platinum-aluminide-silicide coatings is a method that includes electrophoretic deposition of platinum-silicon powder on the turbine blades, heat treatment for diffusion of platinum and silicon in the turbine blades, electrophoretic deposition of aluminum and chromium powder on the turbine blades and then heat treatment for the diffusion of aluminum and chromium in the turbine blades, as described in U.S. patent 5057196.

If on the turbine blades or napravleniya-silicide coating using method described in W 095/23243 And, on the boundary surface between the coating and the single-crystal heat-resistant alloy formed topologically densely Packed phase. It is believed that if the turbine blades or guide vanes platinum-aluminide-silicide coating applied through other described methods, it is topologically dense-Packed phase will be formed.

Also found that if the turbine blades or guide vanes of a single crystal of heat-resistant alloy aluminide-silicide coating deposited using the method described in U.S. patent 5 547 770, on the boundary surface between the coating and the single-crystal heat-resistant alloy formed topologically densely Packed phase. It is believed that if the turbine blades or guide vanes of a single crystal of heat-resistant alloy aluminide-silicide coating is applied by any other of the described method, it must be topologically densely Packed phase.

The authors believe that the high content of rhenium in single-crystal superalloys alloy is responsible for the formation of topologically densely Packed phase is, is there is no way to use a platinum-aluminide-silicide coatings to improve resistance to degradation of single-crystal heat-resistant alloy with a high content of rhenium without deterioration of mechanical properties of single-crystal heat-resistant alloy.

The present invention is directed to a method of eletrownia (plating) single-crystal heat-resistant alloy with a high content of rhenium, which overcomes the aforementioned problems.

According to the present invention provides a method for eletrownia (plating) heat-resistant alloy with a high content of rhenium, comprising the steps:

(a) modifying the surface of a heat-resistant alloy with a high content of rhenium,

(b) eletrownia (plating) heat-resistant alloy with a high content of rhenium for education aluminides coverage.

Alternative step (a) may include applying a layer corresponding to a suitable metal on the surface of the heat-resistant alloy with a high content of rhenium and heat treatment for diffusion of appropriate suitable metal heat-resistant alloy with a high content of rhenium to reduce the content of rhenium in the surface garorock Viceroy diffusion characteristics reduce the formation of zones with a high content of rhenium. Suitable metal can be any metal that is compatible with heat-resistant alloy, such as cobalt, chromium and the like metals.

Step (b) may include the deposition of a suitable metal heat-resistant alloy with a high content of rhenium by electrodeposition, by metallization by sputtering, diffusion metallization coating, diffusion metallization without coating, chemical vapor deposition or physical vapor deposition.

The invention applies in particular to platinum aluminide coatings, platinum-aluminide-silicide coatings and aluminide-silicide coatings, but can be applied to all aluminium coatings on heat-resistant alloys with a high content of rhenium.

The present invention will be further fully described by way of examples with reference to the attached drawings, in which:

Fig. 1 is a view in cross section of the known platinum-aluminide coatings on single crystal superalloys alloy with a low content of rhenium.

Fig. 2 is a view in cross section of the known platinum-aluminide coatings on single crystal superalloys alloy with a high content of rhenium.

Fig. 3 t the s alloy with a high content of rhenium after aging at high temperature.

Fig. 4 is a view in cross section of a modified chromium-platinum-aluminide coating according to the present invention on a single crystal of heat-resistant alloy with a high content of rhenium.

Fig. 5 is a view in cross section of a modified cobalt platinum coating according to the present invention on a single crystal of heat-resistant alloy with a high content of rhenium.

Fig. 6 is a view in cross section of a modified cobalt platinum coating according to the present invention on a single crystal of heat-resistant alloy with a high content of rhenium after aging at high temperature.

In known conventional platinum-literowe process for single-crystal heat-resistant alloy single crystal superalloy by electrodeposition or electroplating method put a layer of platinum, and then single-crystal superalloy coated with a layer of platinum is subjected to heat treatment in vacuum for diffusion of platinum single crystal superalloy. Heat-treated single crystal superalloy with platinum plated ultiroute using Alferova the or other suitable methods. Alteromonas, with prediffusion platinum plated single-crystal superalloy then subjected to heat treatment in a protective atmosphere to optimize the microstructure of platinum aluminide coverage and maximum improvement in mechanical properties of single-crystal heat-resistant alloy.

During the heat treatment for diffusion of platinum single crystal superalloy after deposition of the platinum layer on a single crystal superalloy between the platinum and the single-crystal heat-resistant alloy diffusion occurs with the formation of the surface layer containing platinum, Nickel and other elements of the heat-resistant alloy. Phase diffusion heat treatment is carried out over a period of time and at a temperature sufficient to ensure that progettogiovani platinum layer was acquired suitable composition for subsequent processing stages eletrownia and heat treatment was obtained the required platinum aluminide floor. In Fig.1 shows the well-known platinum-aluminide coating 12 on the substrate 10 of monocrystalline heat-resistant alloy.

However, the heat treatment of the single crystals is atiny creates a zone enriched rhenium and other refractory elements, such as tungsten and chromium, before him. In the following technological stages of eletrownia and heat treatment to obtain the desired platinum-aluminide coverage area, enriched rhenium and other refractory elements, is stored inside the cover. This enriched rhenium and other refractory elements area acts as the initiator of the formation of topologically tightly Packed phases. Topologically densely Packed phase have a needle shape.

Topologically tightly Packed phases are formed at the boundary or interface between a single crystal of heat-resistant alloy and a platinum-aluminium coating. Topologically tightly Packed phases are formed either after all processing steps for the formation of aluminide platinum or subsequent impact high temperaturea aluminum and platinum single-crystal superalloy with high content of rhenium. Topologically densely Packed phase have a high content of rhenium in comparison with single-crystal heat-resistant alloy and they are easier to form when the content of rhenium in single-crystal superalloys alloy HC is Ali from single-crystal heat-resistant alloy, because the sphere is topologically tightly Packed phases have lower creep resistance (or polucarbonate) than single-crystal superalloy. So they will be useful to reduce the load carrying section of the turbine blade or guide vane.

In Fig.3 shows the conventional platinum-aluminide coating 22 on a substrate of single-crystal heat-resistant alloy with a high content of rhenium after aging at high temperature. At the interface between the platinum-aluminium coating 22 and the substrate 20 of monocrystalline heat-resistant alloy with a high content of rhenium are more topologically densely Packed phase.

The present invention modifies the surface of a single crystal of heat-resistant alloy with a high content of rhenium in a manner that allows the platinum layer to diffuse into the single crystal superalloy with high content of rhenium in the subsequent step of heat treatment without the formation of zones enriched rhenium and other refractory elements, before platinum. Successive stages of eletrownia and heat treatment to create a platinum-aluminide floor without topologically the receiving rhenium.

EXAMPLE 1

The sample of the conventional single-crystal heat-resistant alloy based on Nickel with a low content of rhenium, for example CMSX4, subjected platinum-litrovuyu in accordance with the following procedure.

CSMX4 produced by the Corporation Cannon-Muskegon Corporetion of 2875 Lincoln Street, Musketon, Michigan MI 49443 - 0506, USA, had a passport composition of 6.4 wt.% tungsten of 9.5 wt.% cobalt, 6.5 wt.% chromium, 3.0 wt.% rhenium, 5,6 weight. % aluminum, about 6.5 wt.% tantalum, 1.0 wt.% titanium, 0.1 wt.% hafnium, 0.6 wt.% molybdenum, 0,006% wt. carbon and the rest Nickel.

The platinum layer was applied on single crystal superalloy with a low content of rhenium on the basis of Nickel by electrodeposition or electroplating method, by metallization by sputtering, CVD, PVD, or other suitable means to a thickness in the range from 2.5 to 12.5 μm and subjected to heat treatment in vacuum or protective atmosphere for from 1 to 4 hours at a temperature in the range from 900 to 1150oFor the diffusion of platinum single crystal superalloy with a low content of rhenium Nickel-based. Specifically, platinum was applied by electrodeposition (electroplating method) to a thickness of 7 μm and subjected to heat treatment in vacuum for 1 h at temperatur rhenium coated by electrodeposition and progettogiovani platinum, was literally by eletrownia in the coating, eletrownia without coating or CVD of eletrownia in the temperature range from 700 to 1150oC. more Specifically, a single crystal superalloy with a low content of rhenium Nickel-based coated by electrodeposition (electroplating method) and progettogiovani platinum was literally in the coating for 20 hours at a temperature of 875oC.

Then alteromonas platinum single-crystal superalloy based on Nickel with a low content of rhenium was subjected to heat treatment in vacuum or protective atmosphere for 1 h at a temperature of 1100oC and for 16 h at a temperature of 870oC.

Was obtained single crystal superalloy based on Nickel with a low content of rhenium to platinum aluminium coating shown in Fig. 1. Samples of single-crystal heat-resistant alloy based on Nickel with a low content of rhenium to platinum aluminium coating was subjected to tests to cyclic oxidation in air for 200 h at a temperature of 1050oAnd for 100 hours at a temperature of 1100oWith, and under the platinum alumininum the floor there was no topologically tightly Packed phases in any case, what uranium rhenium, for example CMSX10 subjected platinum-litrovuyu in accordance with the following procedure. Registergui monocrystalline superalloy based on Nickel, known as CMSX10, is made by the Corporation Cannon-Muskegon Corporation of 2875 Lincoln Street, Muskegon, Michigan MI 49443 - 0506, USA. This alloy had a passport composition in the range from 3.5 to 6.5 wt.% tungsten, from 2.0 to 5.0 wt.% cobalt, from 1.8 to 3.0 weight. % chromium, from about 5.5 to 6.0 wt.% rhenium, from 5.3 to 6.5 wt.% aluminum, from 8.0 to 10.0 wt.% tantalum, 0.2 to 0.8 wt.% titanium, from 0.25 to 1.5 wt.% molybdenum, from 0 to 0.03 wt.% niobium, from 0.02 to 0.05 wt.% hafnium, from 0 to 0.04 wt.% carbon and the rest Nickel.

The platinum layer was applied on samples of single-crystal heat-resistant alloy based on Nickel with a high content of rhenium by electrodeposition (electroplating method), by metallization by sputtering, CVD, PVD, or other suitable means to a thickness in the range from 2.5 to 12.5 μm and subjected to heat treatment in vacuum or protective atmosphere for from 1 to 4 hours at a temperature in the range from 900 to 1150oFor the diffusion of platinum single crystal superalloy based on Nickel with a high content of rhenium. More specifically, a platinum layer was applied by electrodeposition (electroplating with the eat samples of single-crystal heat-resistant alloy based on Nickel with a high content of rhenium coated progettogiovani platinum was literally, using eletrownia in the coating, eletrownia without coating or CVD eletrownia, at a temperature in the range from 700oWith up to 1150oC. In particular, samples of single-crystal heat-resistant alloy based on Nickel with a high content of rhenium coated progettogiovani platinum was literally using eletrownia without coating for 6 hours at a temperature of 1080oC.

Then platinum alteromonas samples of single-crystal heat-resistant alloy based on Nickel with a high content of rhenium was subjected to heat treatment in a protective atmosphere for 1 h at a temperature of 1100oC and for 16 h at 870oC.

In Fig. 2 shows the substrate 20 of monocrystalline heat-resistant alloy based on Nickel with a high content of rhenium to platinum aluminium coating 22.

One of the samples was investigated and it was found that the zone containing topologically densely Packed phase, are at a depth of 30 μm from the surface or boundary between aluminium platinum and registertask monocrystalline heat-resistant alloy based on Nickel.

Samples of single-crystal heat-resistant alloy based on Nickel with a high content and a temperature of 1100oWith, and subsequent verification was discovered growth topologically tightly Packed phases with the formation of a continuous zone depth of 160 μm at the boundary surface between aluminium platinum and registertask monocrystalline heat-resistant alloy.

In Fig. 3 shows the substrate 20 of monocrystalline heat-resistant alloy based on Nickel with a high content of rhenium to platinum aluminium coating 22, which is topologically dense-Packed phase 24, after aging at a temperature of 1100oC.

EXAMPLE 3

Samples of single-crystal heat-resistant alloy based on Nickel and high Nickel content covered platinum aluminium coating in accordance with the following procedure. Single-crystal superalloy based on Nickel with a high content of rhenium known as CMSX10 and produced by the Corporation Cannon-Muskegon Corporation of 2875 Lincoln Street, Muskegon, Michigan MI 49443 - 0506, USA. This alloy has a passport composition specified above.

Samples of single-crystal heat-resistant alloy based on Nickel with a high content of rhenium were surface modified by forming a chromium enriched surface layer, obtained by electro-deposition (galvanize the heat treatment in vacuum or protective atmosphere. In particular, the enrichment of chromium was carried out by plating without coating for 3 hours at a temperature of 1100oSince before the formation of the chromium enriched surface layer depth of 15 μm.

The platinum layer was applied to the chromium enriched registergui monocrystalline superalloy based on Nickel electrodeposition (electroplating), metallized by sputtering, CVD, PVD, or other suitable means to a thickness in the range from 2.5 to 12.5 μm and subjected to heat treatment in vacuum or protective atmosphere for from 1 to 4 hours at a temperature in the range from 900 to 1150oFor the diffusion of platinum in registergui monocrystalline superalloy based on Nickel. In particular, the platinum layer is applied by electroplating to a thickness of 7 μm and subjected to heat treatment for 1 h at a temperature of 1100oC.

Then chrome-plated, covered with progettogiovani platinum single-crystal superalloy based on Nickel with a high content of rhenium was literally by eletrownia in the coating, eletrownia without coating or CVD of eletrownia in the temperature range from 700 to 1150oC. In particular, chrome-plated, covered with prodifferentiating eletrownia without coating for 6 hours at a temperature of 1080oC.

Platinum alteromonas, chrome-plated single-crystal superalloy based on Nickel with a high content of rhenium was subjected to heat treatment for 1 h at a temperature of 1100oWith plus for 16 hours at a temperature of 870oC.

One of the samples investigated and at the interface between aluminium platinum and single-crystal heat-resistant alloy based on Nickel with a high content of rhenium was not detected zones containing topologically densely Packed phase.

Some samples were subjected to an oxidizing environment for 100 hours at a temperature of 1100oWith, and subsequent inspection found no topologically tightly Packed phases at the interface between aluminium platinum and registertask monocrystalline heat-resistant alloy based on Nickel.

In Fig.4 shows a substrate 30 of a single crystal of heat-resistant alloy based on Nickel and high Nickel modified with chromium platinum aluminium coating 32.

EXAMPLE 4

Samples of single-crystal heat-resistant alloy based on Nickel with a high content of rhenium coated platinum-aluminium coating in accordance with the following the ten as CMSX10 and produced by the Corporation Cannon-Muskegon Corporation of 2875 Lincoln Street, Muskegon, Michigan MI 49443 - 0506, USA. This alloy has a passport composition discussed above.

Samples of single-crystal heat-resistant alloy based on Nickel with a high content of rhenium were surface modified by the formation of enriched cobalt surface layer obtained by electrodeposition (electroplating), metallized by sputtering, CVD, PVD, or other suitable methods plus by a diffusion heat treatment in vacuum or protective atmosphere. The cobalt layer was applied on single crystal superalloy based on Nickel with a high content by electrodeposition (electroplating), metallized by sputtering, CVD, PVD, or other suitable means to a thickness of from 2.5 to 12.5 μm and subjected to heat treatment in vacuum or protective atmosphere for 1 h at a temperature in the range from 900 to 1150oC. In particular, the cobalt layer was applied on single crystal superalloy based on Nickel with a high content of rhenium in a galvanic way to a thickness of 7 μm and subjected to heat treatment in vacuum for 1 h at a temperature of 1100oC.

The platinum layer was applied to the enriched cobalt single crystal of europroc, VD or other suitable method to a thickness in the range from 2.5 to 12.5 μm and subjected to heat treatment in vacuum or protective atmosphere for from 1 to 4 hours at a temperature in the range from 900 to 1150oFor the diffusion of platinum single crystal superalloy based on Nickel with a high content of rhenium. In particular, the platinum layer is applied by electroplating to a thickness of 7 μm and subjected to heat treatment for 1 h at a temperature of 1100oC.

Then enriched with cobalt coated progettogiovani platinum single-crystal superalloy based on Nickel was literally by eletrownia in the coating, eletrownia without coating or CVD of eletrownia at a temperature in the range from 700 to 1150oC. In particular, the samples enriched with cobalt coated progettogiovani platinum single-crystal heat-resistant alloy based on Nickel with a high content of rhenium was literally using eletrownia without coating for 6 hours at a temperature of 1080oC.

Platinum alteromonas enriched with cobalt single crystal superalloy based on Nickel with a high content of rhenium was subjected to heat treatment for 1 h at Tata checks at the interface between the platinum-aluminium coating and single-crystal heat-resistant alloy based on Nickel with a high content of rhenium was not detected zones, containing topologically densely Packed phase.

In Fig.5 shows a substrate 40 of a single crystal of heat-resistant alloy based on Nickel with a high content of rhenium with modified cobalt platinum-aluminium coating 42.

Some of the samples were subjected to an oxidizing environment for 100 hours at a temperature of 1100oWith, and subsequent inspection found no topologically tightly Packed phases at the interface between aluminium platinum and single-crystal heat-resistant alloy based on Nickel with a high content of rhenium.

In Fig. 6 shows the substrate of a single crystal of heat-resistant alloy based on Nickel with a high content of rhenium with modified cobalt platinum-aluminium coating 42.

You can also prepare the surface of a single crystal of heat-resistant alloy with a high content of rhenium by reducing levels of rhenium on the surface of a single crystal of heat-resistant alloy based on Nickel with a high content of rhenium before applying platinum registergui single-crystal superalloy. Rhenium can be removed from the surface of single-crystal high-temperature alloy high when emperature removal of rhenium.

Although the present invention relates to a single crystal of heat-resistant alloys based on Nickel with a high content of rhenium, the invention is also applicable to any heat-resistant alloys based on Nickel with a high content of rhenium.

Although the present invention relates to platinum-aluminium coatings, the invention is also applicable to other aluminium coatings of platinum group metals, such as aluminide palladium, aluminide rhodium, or coatings of combinations of these aluminides of platinum group metals.

The invention is also applicable to coatings of aluminides of platinum group metals on single crystal superalloys based on Nickel with a high content of rhenium for ceramic insulating coatings or linings, for example obtained by plasma spraying or PVD ceramic insulating coatings.

Although the invention relates to platinum-aluminium coatings, it is also applicable to platinum aluminide-silicide coatings, aluminide-silicide coatings, simple aluminium coatings and other appropriate aluminium coatings.

In the case of platinum-aluminide-silicide coatings surface monocrystallic the example chromium or cobalt, and heat treatment or by reducing the amount of rhenium before applying platinum-aluminide-silicide coatings.

In the case of aluminide-silicide coatings and aluminide coating the surface of the heat-resistant alloy with a high content of rhenium modify by applying a suitable metal, for example chromium or cobalt, and heat treatment or by reducing the amount of rhenium before applying aluminide coating or aluminide-silicide coatings.

In the present description provides a more detailed description of these coatings, and additional details can be found by referring to the above-mentioned patents and published patent descriptions.

1. How eletrownia heat-resistant alloy with a high content of rhenium, comprising the following steps: (a) modifying the surface of a heat-resistant alloy with a high content of rhenium by applying to the surface a layer of chromium or cobalt and heat treatment for diffusion of chromium or cobalt in high-temperature alloy with a high content of rhenium in order to reduce the content of rhenium on the surface of the heat-resistant alloy, and (b) eletrownia heat-resistant alloy with a high content of rhenium for education aluminides coverage, PR is amino subsequent formation of topologically tightly Packed phases by means of modifying the surface of a heat-resistant alloy with a high content of rhenium.

2. The method according to p. 1 where the step of modifying includes applying a chromium or cobalt superalloy by deposition, metallization, sputtering, diffusion coating, the diffusion without coating, chemical vapor deposition or condensation from the gas phase.

3. The method according to p. 1 where the step of modifying includes heat treatment at a temperature in the range from 900 to 1150oC for 1 to 4 h

4. The method according to p. 1 where the step of modifying includes applying a layer of cobalt to a thickness of from 2.5 to 12.5 μm on the heat-resistant alloy with a high content of rhenium by electrodeposition and heat treated at a temperature in the range from 900 to 1150oC for 1 to 4 h

5. The method according to p. 1 where the step of modifying includes applying chromium on the surface of the aforementioned heat-resistant alloy at a temperature of 1100oC for 3 h

6. The method according to p. 1, in which the phase eletrownia carried out at a temperature in the range from 700 to 1150oC.

7. The method according to p. 1, in which the phase eletrownia includes eletrownia in the coating, eletrownia without coating in a gaseous environment, chemical vapor deposition or eletrownia in tx2">

9. The method according to p. 8, on which the heat-resistant alloy with a high content of rhenium is heat-resistant alloy based on Nickel.

10. The method according to p. 9, on which the heat-resistant alloy with a high content of rhenium contains from 3.5 to 6.5 wt.% tungsten, from 2.0 to 5.0 wt.% cobalt, from 1.8 to 3.0 wt.% chromium, from about 5.5 to 6.5 wt.% rhenium, from 5.3 to 6.5 wt.% aluminum, from 8.0 to 10.0 wt.% tantalum, 0.2 to 0.8 wt.% titanium, from 0.25 to 1.5 weight. % molybdenum, from 0 to 0.03 wt.% niobium, from 0.02 to 0.05 wt.% hafnium, from 0 to 0.04 wt.% carbon, the rest being Nickel and inevitable impurities.

11. The method according to p. 1, in which the phase eletrownia includes diffusion of silicon in high-temperature alloy with a high content of rhenium for the formation of aluminum-silicide coatings.

12. The method according to p. 1, which precipitated slurry containing elemental powder particles of aluminum and silicon, and perform heat treatment for diffusion of aluminum and silicon in high-temperature alloy with a high content of rhenium.

13. The method according to p. 12, which carry out the re-deposition of the suspension containing elemental powder particles of aluminum and silicon and the heat treatment for diffusion of aluminum and silicon in the above-mentioned heat-resistant woven pattern design education topologically closed-Packed phases and the subsequent formation of the interface between the aforementioned heat-resistant alloy and aluminium the floor.

15. How eletrownia heat-resistant alloy with a high content of rhenium, comprising the following steps: a) modifying the surface of a heat-resistant alloy with a high content of rhenium by applying to the surface a layer of chromium or cobalt and heat treatment for diffusion of chromium or cobalt in high-temperature alloy with a high content of rhenium in order to reduce the content of rhenium on the surface of the heat-resistant alloy; b) applying a layer of a platinum group metal on the modified surface of the heat-resistant alloy with a high content of rhenium; C) heat treatment mentioned heat-resistant alloy with a coating of platinum group metal to ensure the diffusion of platinum group metal in the above-mentioned heat-resistant alloy; g) eletrownia heat-resistant alloy for education aluminides coverage and d) heat treatment alteromonas with a coating of platinum group metal heat-resistant alloy with a high content of rhenium to form a coating of aluminide platinum group metal, the content of rhenium in the above-mentioned heat-resistant alloy is at least 3.5 wt.%, and essentially prevented the subsequent formation of topologically tightly Packed phases through which, what about that applying a layer of a platinum group metal are provided by deposition, metallization, sputtering, chemical deposition from the gas phase or by condensation from the gas phase to a thickness of from 2.5 to 12.5 microns.

17. The method according to p. 15, in which the step of applying a layer of platinum group metal comprises applying a layer of platinum.

18. The method according to p. 15, by which stage heat treatment is carried out at a temperature in the range from 900 to 1150oC for 1 to 4 h

19. The method according to p. 15, which further includes the step (e) deposition of a ceramic insulating coating on the coating of aluminide platinum group metal.

20. The method according to p. 19, by which the deposition of ceramic insulating coating is carried out by plasma spraying or condensation from the gas phase.

21. The method according to p. 15, in which during the step of heat treatment or stage of eletrownia carry out diffusion of silicon in high-temperature alloy with a high content of rhenium for education aluminide-silicicola coverage.

22. The method according to p. 21, which includes the deposition of a suspension containing elemental powder particles of aluminum and silicon, and termopan on p. 22, which includes the re-settling of the suspension containing powder particles of elemental aluminum and silicon, and heat treatment to ensure the diffusion of aluminum and silicon in the above-mentioned heat-resistant alloy.

24. How eletrownia heat-resistant alloy with a high content of rhenium, comprising the following steps: (a) modifying the surface of a heat-resistant alloy with a high content of rhenium by reducing the content of rhenium on the surface by exposure to the heat-resistant rhenium in the alloy gases at high temperatures, which interact with rhenium selectively, and (b) eletrownia mentioned heat-resistant alloy for education aluminide coating, the content of rhenium in the above-mentioned heat-resistant alloy is at least 3.5 wt.%.

Priority points:

18.12.1996 - PP.1-14 and 22-24;

23.07.1996 - PP.15-21.

 

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The invention relates to the field of superconductivity and can be used in the manufacture of high temperature superconducting wires and other superconductors, which can find application in computer engineering, electrical engineering, energy

The invention relates to the production of multilayer metallic materials and can be used in the production of corrosion-resistant and antifouling materials for ships, fixed and floating structures

The invention relates to a friction plate for a disc brake, in particular for road and rail vehicles, which are made of one or several parts and consists of a deposited on the carrier plate or sheet block of compacted friction material and carrier plate on the side of the block of friction material is applied substrate carrying the layer of the individual firmly linked to a block of friction material shaped protrusions with the extension to the top, and the block of friction material is pressed onto the supporting layer is attached with the filling of the grooves separate shaped protrusions

The invention relates to chemical-thermal processing parts in the circulating gas environment and may find wide application in power engineering, in particular in aerospace, and other industries

The invention relates to chemical-thermal treatment, mainly to the hardening of the cast cutting tools made of high speed steel for increased wear resistance and heat resistance of the surface layers

The invention relates to mechanical engineering and can be used in the manufacture of the instrument with chemical and thermal treatment (HTO) and final tempering at a temperature not exceeding 500oC

The invention relates to chemical-thermal treatment

The invention relates to chemical-thermal treatment

The invention relates to mechanical engineering and can be used in the manufacture of chemical-heat treatment (HTO) details of steels and other metals having a contact plane with the bumps and hollows, in particular, when testing the hardness of the diffusion layer

The invention relates to chemical-thermal treatment, in particular to the media for multicomponent diffusion saturation of the surface of metals

The invention relates to the field of chemical engineering, specifically to the high-temperature chemical vapor deposition of refractory coating from the gas phase on the carbon fibrous materials

The prior art method of applying a silicon carbide coating on the thread in a two-chamber setup at atmospheric pressure

The invention relates to techniques for the production of coatings, namely, chemical-thermal treatment of parts of iron - carbon alloys, and can be used to enhance the durability of parts operating under conditions of intensive corrosive and erosive wear surfaces, as well as to restore the above-mentioned parts

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

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