JPH08176849A - Metal coated material and its production - Google Patents

Abstract

PURPOSE: To obtain a metal coated material preventing the peeling of the coating layer due to the formation of a nitride by improving nitriding resistance while satisfying heat resistance, corrosion and oxidation resistances. CONSTITUTION: In a metal coated material with a base material made of an alloy based on at least one kind of element selected from among Fe, Ni and Co and an M-Cr-Al-Y alloy layer (M is at least one kind of element selected from among Fe, Ni and Co) coating the surface of the base material, 0.3-7wt.% oxygen is allowed to exist in the M-Cr-Al-Y alloy layer. The objective metal coated material is produced, e.g. by plasma spraying using M-Cr-Al-Y alloy powder contg. 0.05-5wt.% oxygen.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a metal coating material suitable for a material which is required to have durability and reliability under high temperature and high stress, such as a constituent material of a moving or stationary blade of a gas turbine. .

[0002]

2. Description of the Related Art In recent years, energy devices typified by gas turbines have been energetically promoted to be highly efficient. The most effective means for achieving such high efficiency is to raise the operating temperature of equipment, but with this, the material properties required for equipment constituent materials are becoming more severe. Since high-temperature equipment is exposed to high-temperature oxidative / corrosive environments, high-temperature strength, corrosion resistance, oxidation resistance, etc. are important as the material properties required for the constituent materials of high-temperature equipment.

However, conventional heat-resistant alloys such as iron-based alloys, nickel-based alloys, and cobalt-based alloys are difficult to satisfy the above-mentioned high-temperature strength and corrosion / oxidation resistance at the same time. Heat and corrosion resistance to alloys
Oxidation resistant coating technology has been developed and has a considerable track record in actual equipment. M-Cr-Al-Y alloys (M is at least one element selected from Fe, Ni and Co) are generally used as such heat-resistant, corrosion-resistant and oxidation-resistant coating materials. This M-Cr-Al-Y alloy consists of the main element M, which has excellent high-temperature strength and compatibility with the base material, Al and Cr that form an oxide coating with high corrosion and oxidation resistance, and the coating layer and It is composed of Y, which enhances the adhesion of the oxide film.

Various methods such as a plasma spraying method, a PVD method and a CVD method have been studied as a method for forming the coating layer of the above-mentioned M-Cr-Al-Y alloy. Among them, the plasma spraying method can be used to form a thick film easily, and is therefore used as the most effective coating method for the M-Cr-Al-Y alloy layer.

By the way, the existing M-Cr-Al-Y alloys have been developed from the viewpoints of corrosion resistance and oxidation resistance, so that nitriding resistance is hardly considered. In other words, in the case of a metal coating material in which the surface of a heat-resistant alloy is coated with a conventional M-Cr-Al-Y alloy layer, M-Cr-Al-Y
From the inside of the alloy layer toward the inside of the heat-resistant alloy of the base material, there was a problem that nitrides such as Al and Ti were generated by nitrogen in the gas atmosphere, the protective coating on the surface was peeled off, and the base material was damaged.

[0006]

As described above, in the metal coating material using the conventional coating layer made of M-Cr-Al-Y alloy, the M-Cr-Al-Y alloy itself has oxidation resistance. Since it was developed with emphasis on it, it does not have sufficient nitriding resistance, and if it is operated for a long time, nitrides will grow from the inside of the M-Cr-Al-Y alloy layer toward the inside of the heat-resistant alloy of the base material. There was a problem that the protective coating layer on the surface was peeled off to damage the substrate. Therefore, there is a demand for a metal coating material that has improved corrosion resistance and oxidation resistance as well as nitriding resistance.

The present invention has been made in order to solve such problems, and it is possible to form a nitride by improving the nitriding resistance while satisfying the heat resistance and the corrosion / oxidation resistance. An object of the present invention is to provide a metal coating material that prevents the coating layer from peeling off due to the above, and a method for producing the metal coating material that enables such a metal coating material to be produced with good reproducibility.

[0008]

The metal coating material of the present invention comprises a base material made of an alloy containing at least one element selected from Fe, Ni and Co as a main component, and coating the surface of the base material. M-Cr-Al-Y alloy layer (where M represents at least one element selected from Fe, Ni and Co) It is characterized by the presence of 0.3 to 7% by weight of oxygen in the layer.

Further, the method for producing a metal coating material of the present invention comprises:
Using the M-Cr-Al-Y alloy powder containing oxygen in the range of 05 to 5% by weight, the surface of the substrate is M-Cr-Al-Y alloy in which 0.3 to 7% by weight of oxygen is present. It is characterized by coating with a layer.

Here, the nitriding that occurs in the conventional metal coating layer is because the oxygen partial pressure of the atmospheric gas that has penetrated into the metal coating layer decreases in the metal coating layer and the nitrogen partial pressure relatively rises. This is a phenomenon that occurs. On the other hand, for example, metal can form a solid solution of a certain amount of oxygen. Therefore, a certain amount of oxygen can be made to exist in the metal coating layer by solid solution or adsorption of oxygen in the constituent elements of the metal coating layer. Even if the oxygen partial pressure of the atmospheric gas invading the inside of the metal coating layer in which a certain amount of oxygen or more is present may decrease, the metal coating layer is preliminarily changed by the oxygen existing in the metal coating layer. The oxygen partial pressure inside can be kept above a certain level. This makes it possible to prevent nitriding of constituent elements of the metal coating layer and the base material, particularly Al and Ti.

The metal coating material of the present invention utilizes the nitriding prevention mechanism as described above, and has 0.3
A M-Cr-Al-Y alloy layer containing ~ 7 wt% oxygen is used. The amount of oxygen present in this M-Cr-Al-Y alloy layer is 0.3.
If it is less than 7% by weight, the above nitriding suppression effect cannot be obtained, and if it exceeds 7% by weight, oxidation of the M-Cr-Al-Y alloy becomes severe and the original function as a coating layer deteriorates. To do. The amount of oxygen present in the M-Cr-Al-Y alloy layer is 1 to 5% by weight.
It is more preferable that the range is
The range is up to 3% by weight.

By using the M-Cr-Al-Y alloy layer containing 0.3 to 7% by weight of oxygen as described above, M-Cr-
It is possible to suppress nitriding of the Al-Y alloy layer and thus the base material. As a result, when the metal coating material of the present invention is used as, for example, a high temperature member for a gas turbine, deterioration of the M-Cr-Al-Y alloy layer can be prevented even during long-term operation, and therefore high reliability is achieved. It is possible to provide a high-temperature member or the like that can be operated for a long time under the condition of heat.

The existing form of oxygen in the above-mentioned M-Cr-Al-Y alloy layer is not particularly limited, and may be, for example, M-Cr-Al.
-Oxygen dissolved in the constituent elements of the -Y alloy layer, oxygen adsorbed or combined as a simple substance or as an oxide on the surface of the crystal grains or the grain boundaries that constitute the M-Cr-Al-Y alloy layer, M-Cr Various forms such as oxygen existing in defects such as vacancies in the -Al-Y alloy layer can be used. Of these, MC
Oxygen dissolved in each constituent element of the r-Al-Y alloy layer is stable, so it is necessary to keep the oxygen partial pressure in the M-Cr-Al-Y alloy layer above a certain level under various conditions. It is valid. In this case, M
It is preferable to form a solid solution of oxygen that is 1/2 or more of the solid solution limit concentration of oxygen of the -Cr-Al-Y alloy layer constituent element. Also, M-Cr-Al
-The oxygen present in the Y alloy layer does not necessarily have to be distributed throughout the M-Cr-Al-Y alloy layer,
The surface side of the M-Cr-Al-Y alloy layer, the intermediate portion between the surface and the base material,
Alternatively, it may be distributed in a band shape on the substrate side. However, in the case where the oxygen existing region is distributed in a belt shape as described above, it is particularly preferable to distribute the oxygen existing region in the vicinity of the surface which is in direct contact with nitrogen.

The amount of oxygen in the above M-Cr-Al-Y alloy layer is
The M-Cr-Al-Y alloy layer can be measured using a direct chemical analysis method or a physical analysis method. Specifically, it is measured by a high sensitivity gas analyzer using an infrared detector or a heat conduction detector.

MC in the metal coating material of the present invention
The r-Al-Y alloy layer has a porosity of 1 depending on the manufacturing method.
It is preferably about 0% or less. If the porosity exceeds 10%, the performance as a heat resistant / corrosion resistant coating may be deteriorated, and the base material may be oxidized or nitrided.

The base material in the metal coating material of the present invention is F
Any alloy may be used as long as it is composed of an alloy containing at least one element selected from e, Ni and Co as a main component, and a known heat-resistant alloy can be appropriately selected and used depending on the application. Practically, such as IN738, IN939, Mar-M247, Rene80, etc.
It is effective to use Ni-based superalloys and Co-based superalloys such as FSX-414 and Mar-M509.

MC in the metal coating material of the present invention
The r-Al-Y alloy layer contains 0.1-20 wt% Al, 10-40 wt%
Cr, 0.1-1.5 wt.% Y, balance M substantially
It is preferable to use an alloy having a composition of Al and
Cr is an element responsible for corrosion resistance and oxidation resistance. If the contents of Al and Cr are less than the lower limit values of the above ranges, the corrosion resistance and oxidation resistance effects of the coating layer are reduced, and a sufficient function cannot be exhibited. On the other hand, when the content exceeds the upper limit of the above range, the formation of harmful intermetallic compound layers is promoted and the ductility of the coating layer is lowered, so that the life is shortened due to crack growth in the coating layer and the like. A more preferable composition ratio of Al and Cr is in the range of 3 to 15% by weight of Al and 15 to 35% by weight of Cr. Y is an element that improves the adhesiveness of the protective oxide film and the coating layer, and the effect is reduced in any case outside the above range. A more preferable composition ratio of Y is in the range of 0.3 to 1% by weight. The remaining M element may be at least one element selected from Fe, Ni and Co. However, from the viewpoint of compatibility with the base alloy and life, especially Ni or Co single element, or Ni and Co (Ni> C
o) or a combination of Co and Ni (Co> Ni) is preferable.

In the metal coating material of the present invention, M-Cr-
Ceramic layer on Al-Y alloy layer and thermal barrier layer (outermost coating layer)
It may be provided as. This ceramic layer has the effect of shielding external heat and reducing the temperature rise of the base alloy. The types of ceramics are Si ₃ N ₄ , SiC,
Al ₂ O ₃ , ZrO ₂ , TiN, AlN, sialon, etc. are exemplified, and any ceramic material may be used,
ZrO ₂ is suitable as the heat shield layer. As the stabilizer ZrO ₂ Y ₂ O _3, CaO, although MgO or the like is used, the most preferred of these Y ₂ O _3, in particular Y ₂ O
Partially stabilized zirconia containing about 8% by weight of ₃ shows extremely excellent properties. This ceramic layer usually contains many pores and allows an element on the environment side to easily pass through. Therefore,
By utilizing the M-Cr-Al-Y alloy layer of the present invention as the bonding layer between the base material and the ceramic layer, the material deterioration due to nitrogen is reduced, and a great effect is exerted in extending the life of the heat-shielding coating material. The metal coating material of the present invention as described above is produced, for example, as follows. That is, M containing oxygen
Using the -Cr-Al-Y alloy powder as a raw material powder, the substrate surface is coated by a PVD method such as a plasma spraying method or an EB-PVD method. For example, the plasma spraying method is a coating preparation method in which powder as a raw material is melted in plasma and sprayed on the surface of a base material, but generally, a sprayed coating layer having a composition close to that of the raw material powder is formed. From this, by using oxygen-containing M-Cr-Al-Y alloy powder as a raw material, an M-Cr-Al-Y alloy coating layer in which oxygen exists can be formed. Further, also in the EB-PVD method and the like, the M-Cr-Al-Y alloy coating layer containing oxygen therein is formed by using the oxygen-containing M-Cr-Al-Y alloy as the target material. be able to. In particular, the plasma spraying method can be said to be a suitable manufacturing method for the present invention because a thick film can be easily formed.

When the substrate surface is coated by the above-mentioned plasma spraying method or EB-PVD method, M-Cr- used as a raw material
The oxygen content of the Al-Y alloy powder is in the range of 0.05 to 5% by weight. Even if the oxygen content of the M-Cr-Al-Y alloy powder as a coating material is less than 0.05% by weight or more than 5% by weight, the M-Cr-Al-Y alloy coating layer contains It becomes difficult to keep the oxygen amount within a predetermined range. M-Cr- as coating material
The oxygen content of the Al-Y alloy powder is more preferably in the range of 0.1 to 3% by weight, whereby an M-Cr-Al-Y alloy layer having a higher nitriding suppression effect can be obtained.

The existence form of oxygen contained in the M-Cr-Al-Y alloy powder as the coating raw material is not particularly limited, and may be, for example, a solid constituent element of the M-Cr-Al-Y alloy. It is possible to apply various forms such as dissolved oxygen, oxygen adsorbed or bonded to the surface of M-Cr-Al-Y alloy particles as a simple substance or as an oxide. Of these, especially M-Cr-A
Oxygen dissolved in the constituent elements of the lY alloy is suitable because it is stable. In this case, it is preferable to use M-Cr-Al-Y alloy powder in which oxygen at a concentration not less than 1/2 of the solid solution limit concentration is dissolved.

The metal coating material of the present invention is not limited to the method using the oxygen-containing M-Cr-Al-Y alloy powder as described above, but may be, for example, a plasma spray method, a PVD method, a C method in an oxygen-containing atmosphere.
It can also be obtained by forming an M-Cr-Al-Y alloy coating layer by the VD method or the like. At this time, it is preferable that the oxygen pressure in the atmosphere during film formation be 10 ⁻² Pa or more. If the oxygen pressure is too low, oxygen cannot be sufficiently present in the M-Cr-Al-Y alloy layer. Further, by controlling the oxygen pressure, it is possible to control the amount of oxygen dissolved in the constituent elements of the M-Cr-Al-Y alloy, for example.

For example, the case of forming a film in an atmosphere of atmospheric pressure or more will be described in detail. It is preferable that the pressure of the film forming atmosphere is not less than atmospheric pressure and not more than 10 atmospheres. × 10 ⁴ Pa or more. As the atmosphere gas, the pressure of pure oxygen gas is adjusted or used, or a mixed gas of Ar, He, etc. and oxygen is used.
Further, in forming the film, the inside of the film forming chamber is purged with oxygen gas and then adjusted to a predetermined pressure. Note that it is preferable to prevent the metal from being excessively oxidized during the film formation. This is because the M-Cr-Al-Y alloy layer becomes brittle.

When the film is formed in a reduced pressure atmosphere below atmospheric pressure, the oxygen pressure is maintained at 10 ^-3 Pa or more, and then the atmospheric pressure is set to 10 ^-3 to 10 ^-1 Pa. Preferably. By performing film formation under such reduced pressure, MC
It is possible to suppress the oxidation of the r-Al-Y alloy. At this time, after purging the chamber with pure oxygen, the pressure is adjusted to a predetermined pressure.

The coating method using the M-Cr-Al-Y alloy layer as described above is not limited to the formation of the protective coating layer on the outermost surface, but a heat shield layer (outermost layer) made of a ceramic layer such as zirconium oxide or aluminum oxide. It can also be used as a method for forming an underlayer of a coating layer).

[0025]

Embodiments of the present invention will be described below.

Example 1 First, a Ni-base alloy IN738 was prepared as a substrate, processed into a blade shape, and then its surface was blasted.
Then, the blade-shaped base material was placed in the decompression chamber, and after the decompression chamber was replaced with oxygen gas, 10
^The pressure was reduced to ^-1 Pa. In such oxygen gas, Co-29
Alloy powder with a composition of% Cr-6% Al-0.4% Y (wt%), thickness 100μ
Low-pressure plasma spraying was performed to obtain m, and the surface of the blade-shaped substrate was coated with the M (Co) -Cr-Al-Y alloy layer.

The amount of oxygen in the M (Co) -Cr-Al-Y alloy layer thus obtained was analyzed by a high-sensitivity gas analyzer using an infrared detector. -Y alloy layer as a whole
There was 3% by weight of oxygen. Next, the above M (Co) -Cr-
A Ni-based alloy blade coated with an Al-Y alloy layer has a gas combustion temperature of
When the gas turbine was used as a 1373K gas turbine blade and the gas turbine was actually operated, no deterioration of the blade material was observed even after 10,000 hours.

In addition, as a comparative example with the present invention, an example in which the inside of the decompression chamber in which the same blade-shaped substrate as that of the above-mentioned Example 1 is arranged is depressurized from atmospheric pressure to a vacuum degree of 10 Pa 100 μm thick M (Co) -Cr-Al-Y alloy with the same composition as
Low pressure plasma spraying. The amount of oxygen in this M (Co) -Cr-Al-Y alloy layer was 0.1% by weight. Also, this M (Co) -Cr-A
The Ni-based alloy blade coated with the lY alloy layer has a gas combustion temperature of
When the gas turbine was used as a 1373 K gas turbine blade and the gas turbine was actually operated, the surface coating layer peeled off at 1000 hours, and deterioration of the substrate was observed. When the deteriorated portion was investigated, aluminum nitride was detected.

Example 2 After a surface of a base material made of a blade-shaped Ni-base alloy IN738 was blasted, the blade-shaped base material was placed in a decompression chamber. After replacing the inside of the decompression chamber with oxygen gas,
The atmospheric pressure was set to 10 ⁵ Pa. In oxygen gas like this,
Alloy powder of Co-32% Ni-21% Cr-8% Al-0.5% Y (wt%) composition,
Plasma spraying was performed to a thickness of 150 μm, and the surface of the blade-shaped substrate was coated with the M (Co, Ni) -Cr-Al-Y alloy layer.

The amount of oxygen in the M (Co, Ni) -Cr-Al-Y alloy layer thus obtained was analyzed in the same manner as in Example 1.
There was 5% by weight of oxygen. Next, the above M (Co) -Cr-
A Ni-based alloy blade coated with an Al-Y alloy layer has a gas combustion temperature of
When the gas turbine was used as a 1573K gas turbine rotor blade and the gas turbine was actually operated, no deterioration of the rotor blade material was observed even after 10,000 hours.

Further, as a comparative example with the present invention, an example in which the inside of the decompression chamber in which the same blade-shaped substrate as that of the above-mentioned Example 2 is arranged is depressurized from atmospheric pressure to a vacuum degree of 10 Pa Thickness of M (Co, Ni) -Cr-Al-Y alloy with the same composition as 2
Low pressure plasma spraying at m. The amount of oxygen in this M (Co, Ni) -Cr-Al-Y alloy layer was 0.2% by weight. Also, this M (Co, N
i) -Cr-Al-Y alloy layer-coated Ni-base alloy blade was used as a gas turbine blade with a gas combustion temperature of 1573K, and the actual operation of the gas turbine was performed. The coating layer was peeled off, and deterioration of the substrate was observed. When the deteriorated portion was investigated, aluminum nitride was detected.

Example 3 After a surface of a base material made of a blade-shaped Ni-base alloy IN738 was blasted, the blade-shaped base material was placed in a decompression chamber. After replacing the inside of the decompression chamber with oxygen gas,
The atmospheric pressure was in the 10 ^-1 Pa range. In oxygen gas like this,
Alloy powder of Co-32% Ni-21% Cr-8% Al-0.5% Y (wt%) composition,
Low-pressure plasma spraying was performed to a thickness of 150 μm, and the blade-shaped substrate surface was coated with an M (Co, Ni) -Cr-Al-Y alloy layer.

When the oxygen content in the M (Co, Ni) -Cr-Al-Y alloy layer thus obtained was analyzed in the same manner as in Example 1,
There was 4% by weight of oxygen. Next, the above M (Co, Ni) -C
A Ni-based alloy blade coated with an r-Al-Y alloy layer was used as a gas turbine blade with a gas combustion temperature of 1573K, and the actual operation of the gas turbine was performed. No deterioration was observed.

Further, as a comparative example with the present invention, an example in which the inside of the decompression chamber in which the same blade-shaped substrate as that of the above-mentioned Example 3 was arranged was depressurized from atmospheric pressure to a vacuum degree of 10 Pa The thickness of M (Co, Ni) -Cr-Al-Y alloy of the same composition as 3
Low pressure plasma spraying at m. The amount of oxygen in this M (Co, Ni) -Cr-Al-Y alloy layer was 0.07% by weight. Also, this M (Co, N
i) -Cr-Al-Y alloy layer-coated Ni-based alloy blades were used as gas turbine blades with a gas combustion temperature of 1573K, and the actual operation of the gas turbine was performed. The coating layer was peeled off, and deterioration of the substrate was observed. When the deteriorated portion was investigated, aluminum nitride was detected.

Example 4 After polishing the surface of a base material made of a blade-shaped Ni-based alloy MarM247, the blade-shaped base material was placed in a decompression chamber. After replacing the inside of the decompression chamber with oxygen gas, the atmospheric pressure was adjusted to the order of 2 × 10 ^-1 Pa. In such oxygen gas, Co-
Using an alloy target with a composition of 32% Ni-21% Cr-8% Al-0.3% Y (wt%), M (Co,
A Ni) -Cr-Al-Y alloy layer was formed. Furthermore, this M (Co, N
A heat shield layer made of Y-stabilized zirconium oxide was formed on the i) -Cr-Al-Y alloy layer by thermal spraying in the atmosphere to form a gas turbine blade.

When the amount of oxygen in the above M (Co, Ni) -Cr-Al-Y alloy layer was analyzed in the same manner as in Example 1, 1 wt% oxygen was present. Next, the Ni-based alloy blade coated with the M (Co, Ni) -Cr-Al-Y alloy layer and the Y-stabilized zirconium oxide heat shield layer was used as a gas turbine blade with a gas combustion temperature of 1773K. When the actual operation of the gas turbine was performed,
No deterioration of the blade material was observed even after 10,000 hours.

Further, as a comparative example with the present invention, the inside of the decompression chamber in which the same blade-shaped substrate as in Example 4 was placed was depressurized from atmospheric pressure to a degree of vacuum of the order of 10 ^-1 Pa. ,
M (Co, Ni) -Cr-Al-Y alloy layer having the same composition as in Example 4 (thickness 1
50 μm) was formed by sputtering. Then, in the same manner as in Example 4, the M (Co, Ni) -Cr-Al-Y alloy layer was formed.
A Y-stabilized zirconium oxide thermal barrier layer was formed. Got
The oxygen content in the M (Co, Ni) -Cr-Al-Y alloy layer was 0.05% by weight. Further, the Ni-based alloy blade coated with this M (Co, Ni) -Cr-Al-Y alloy layer and Y-stabilized zirconium oxide heat shield layer was used as a gas turbine blade with a gas combustion temperature of 1773K,
When the gas turbine was actually operated, the surface coating layer peeled off at 1500 hours and deterioration of the substrate was observed. When the deteriorated portion was investigated, aluminum nitride was detected.

Example 5 After the surface of a base material made of a blade-shaped Ni-based alloy MarM247 was blasted, the blade-shaped base material was placed in a decompression chamber, and the inside of the decompression chamber was changed from atmospheric pressure. The pressure was reduced to the level of 10 ^-1 Pa. In such an atmosphere, the oxygen content
0.1 wt% Co-29% Cr-6% Al-0.4% Y (wt%) alloy powder was low-pressure plasma sprayed to a thickness of 150 μm,
The blade-shaped substrate surface was coated with an M (Co) -Cr-Al-Y alloy layer.

When the amount of oxygen in the M (Co) -Cr-Al-Y alloy layer was analyzed in the same manner as in Example 1, 1% by weight of oxygen was present. Next, when the Ni-based alloy blade coated with the above M (Co) -Cr-Al-Y alloy layer was used as a gas turbine blade with a gas combustion temperature of 1573K, the actual operation of the gas turbine was performed. Deterioration of blade material and M (C
No peeling of the o) -Cr-Al-Y alloy layer was observed.

As a comparative example with the present invention, the inside of the decompression chamber in which the same blade-shaped substrate as in Example 5 was placed was depressurized from atmospheric pressure to a degree of vacuum of the order of 10 ^-1 Pa. ,
Oxygen content 0.01% by weight Co-29% Cr-6% Al-0.4% Y (weight
%) Alloy powder was sprayed with a low pressure plasma at a thickness of 150 μm. The amount of oxygen in this M (Co) -Cr-Al-Y alloy layer was 0.1% by weight. When the Ni-based alloy blade coated with this M (Co) -Cr-Al-Y alloy layer was used as a gas turbine blade with a gas combustion temperature of 1573K, the actual operation of the gas turbine was performed.
At 2000 hours, the M (Co) -Cr-Al-Y alloy layer peeled off. When the peeled portion was investigated, aluminum nitride and titanium nitride were detected.

[0041]

As described above, according to the metal coating material of the present invention, the oxygen partial pressure in the M-Cr-Al-Y alloy layer can be maintained at a certain level or higher, so that the base material and metal coating Deterioration of the layer due to nitriding can be significantly suppressed, and the life can be remarkably extended. Therefore, even in an environment where oxidation and nitriding, and stress are superimposed on the material, such as the usage environment of a gas turbine blade, excellent corrosion resistance, oxidation resistance, nitriding resistance, and high temperature strength can be obtained for a long time. It is possible to provide a metal coating material that can be maintained over the entire length. Also,
According to the method for producing a metal coating material of the present invention, such a metal coating material can be produced with good reproducibility.

[0042]

 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Shinji Arai, 1 Komukai Toshiba-cho, Sachi-ku, Kawasaki-shi, Kanagawa Incorporated, Toshiba Research and Development Center

Claims (3)

[Claims] 1. At least one selected from Fe, Ni and Co
A base material composed of an alloy containing one element as a main component and an M-Cr-Al-Y alloy layer coated on the surface of the base material (where M is F
and at least one element selected from Ni, Co) and 0.3 to 7% by weight of oxygen is present in the M-Cr-Al-Y alloy layer. A metal coating material characterized by the above. 2. The metal coating material according to claim 1, wherein a ceramics layer is further provided as a heat shield layer on the M-Cr-Al-Y alloy layer. 3. In producing the metal coating material according to claim 1, the M-Cr-Al-Y containing oxygen in the range of 0.05 to 5% by weight.
Using alloy powder, the surface of the base material is 0.3 to 7% by weight.
A method for producing a metal-coated material, which comprises coating with a M-Cr-Al-Y alloy layer containing oxygen of 1.