HIGH-TEMPERATURE SPRAY COATED MEMBER AND METHOD OF PRODUCTION THEREOF

Abstract: In order to advantageously solve problems such as lowering of the productivity, contamination of alloy coating due to the adoption of different metal, increase of the cost due to the adoption of different coating process, a coating of MCrAlX alloy is directly formed on a substrate surface of a member exposed to a high temperature at a thickness of 10∼300 µm through atmospheric plasma spraying process in air or flame spraying process (including low-velocity flame spraying process, high-velocity flame spraying process) and thereafter the same MCrAlX alloy is applied thereonto at a thickness of 100∼800 µm through low pressure plasma spraying process in a non-oxidizing atmosphere.

Description: TECHNICAL FIELD This invention relates to a high-temperature spray coated member having an excellent high-temperature oxidation resistance as a high-temperature member such as boiler, gas turbine, jet engine, diesel engine or the like and a method of producing the same. BACKGROUND ART As to a high power generator such as a boiler, a gas turbine, a jet engine, a diesel engine or the like, there are many studies for mainly improving a heat efficiency. However, the improvement of heat efficiency forces a severe thermal load to a constructional part (material). As a metal material used in a high temperature portion of the high power generator, therefore, it is required to have excellent high-temperature oxidation resistance and high-temperature corrosion resistance. Particularly, if it is intended to use a fuel containing impurities such as V, Na, S and the like, since inorganic compounds containing these impurities violently corrode and wear the metallic material at a high-temperature state, it is necessary to maintain the metallic material at a stable state for a long time under such an environment. In order to satisfy such a requirement, there have been developed many heat resistant alloys consisting essentially of nonferrous metallic elements such as Cr, Ni, Mo, Co, W, Ta, Al, Ti and the like from the old time, which are called as so-called super-alloys. In these heat resistant alloys, however, the high-temperature strength is most preferential, so that it tends to suppress an addition amount of a metal element not serving to the improvement of the strength as low as possible. A typical example of the metal element not serving to the improvement of the strength is Cr, Al, Si or the like, but these elements are excellent in the oxidation resistance and resistance to high-temperature corrosion. Therefore, it is ordinary that the super-alloy preferentially requiring the above high temperature strength is poor in the oxidation resistance and resistance to high-temperature corrosion. Heretofore, a metal elements such as Cr, Al, Si or the like or an alloy thereof has previously been applied to a surface of a super-alloy member used under a high temperature environment through a spraying process, a diffusion treatment method or the like to compensate for the lowering of resistance force to chemical damage of the super-alloy. In the spraying process, it is merit that the kind of the spraying material may optionally be selected, but there is a drawback that the resulting coating is porous and is poor in the corrosion resistance and adhesion property because the treatment is carried out in air. In this connection, there has recently been developed a method wherein plasma spraying is carried out in an argon gas atmosphere of a low pressure containing substantially no air (oxygen) (low-pressure plasma spraying process), whereby drawbacks inherent to the atnospheric-sprayed coating have largely been improved, but it can not be said that such a coating is still sufficient under recent environment exposed at higher temperature. On the other hand, the conventional diffusion treatment method is relatively easy when Cr, Al, Si and the like are treated individually, but it is hardly said that the oxidation resistance and the resistance to high-temperature corrosion are sufficient. And also, this treatment is required to be conducted at a higher temperature state of about 1000°C, so that it has a drawback that mechanical properties of super-alloy matrix lower. Under the above circumstances, JP-A-55-104471 proposes a method wherein Ni-Cr alloy as an oxidation-resistant metal is sprayed to conduct a diffusion treatment of Al, Cr or the like. In this method, however, the treatment at high temperature can not be avoided, so that it is inevitable to lower the mechanical properties of the matrix though the adhesion property and denseness of the sprayed coating are improved. On the other hand, the development of spraying materials is carried out for using under high-temperature environment. A typical material is a heat-resistant alloy material represented by MCrAlX (wherein M is a metal of Ni, Co or Fe or a mixture thereof. X is an element such as Y, Hf, Ta, Cs, Pt, Ce, Zr, La, Si, Th or the like). By plasma spraying the MCrAlX alloy under a low pressure, it is possible to form a sprayed coating having excellent oxidation resistance and resistance to high-temperature corrosion, and the performances of the high-temperature member are more improved. And also, there is proposed a method wherein the diffusion treatment of Cr, Al or the like is conducted after the formation of the MCrAlX alloy sprayed coating (e.g. JP-B-61-10034). The service life of the member for gas turbine is fairly improved by the above recent spraying process or the development of a technique combining the spraying process and the diffusion treatment method. However, the gas temperature of the gas turbine is anticipated to reach 1500∼1700°C in future. In the gas turbine member contacting with such a high temperature gas, even if it is reinforced with a cooling system through air or steam, it is anticipated that the temperature of the exposed member exceeds the existing 900°C and will be 950∼1050°C. For this end, it is studied to improve the high temperature strength of the member for the gas turbine (metal matrix). However, when the alloy sprayed coating is formed on such a high temperature member (metal substrate) by the conventional method, there is a fear of causing the following problems. (1) In the high temperature member (metal substrate), as the temperature becomes high, there is a strong tendency that an alloy component in a sprayed coating of, for example, MCrAlX alloy (wherein M is one or more of Ni, Co and Fe, X is one or more of Y, Hf, Ta, Cs, Pt, Ce, Zr, La, Si and Th) formed on the surface or a composite sprayed coating containing a diffusion layer therein diffuses and penetrates into the inside of the metal substrate and hence a thick brittle layer is created in a boundary portion between the sprayed coating and the substrate surface to easily peel the sprayed coating. (2) Among the components of the MCrAlX alloy penetrated into the inside of the metal substrate, Al particularly reacts with Ni included in the metal substrate to produce a brittle intermetallic compound such as AlNi, AlCo or the like and has an action disappearing a high temperature strength component or precipitate existing in the substrate. As a result, the high temperature strength of the substrate as a whole lowers and it is apt to cause crack or local breakage resulted from thermal fatigue. (3) Even in the MCrAlX alloy sprayed coating, Ni, Cr and the like being basic components diffuse to form a brittle layer, so that the resistance to thermal shock in the coating considerably lowers. It is said that these problems result from the feature that the components of the MCrAlX alloy sprayed coating applied to the surface of the substrate diffuse and penetrate into the substrate. As a countermeasure therefor, it is considered that the prevention of diffusing and penetrating the alloying components of the sprayed coating is an effective means. As such a means, there is a method wherein a high melting point metal (Nb, Ta) or a thin layer of (10∼100 µm) of an oxide film such as Al 2 O 3 is directly formed on the surface of the substrate through a spraying method or PVD method and the conventional MCrAlX alloy sprayed coating is formed thereon to control the internal diffusion of the MCrAlX alloying components. In this method, however, an expensive metal different from the MCrAlX alloying components is used, or the PVD method using an electron beam as a heat source is used in the formation of Al 2 O 3 film, so that the different film-forming process should be adopted and hence the lowering of the productivity is caused. And also, the prevention of the internal diffusion of the alloying components by this method loses the diffusion layer required for ensuring the adhesion property between the substrate and the sprayed coating and the adhesion property of the coating considerably lowers. US-A-4451496 discloses a spray coated member having an oxide-containing undercoat and a non-oxide topcoat sprayed coating, applied on a heat resistant substrate. Both coating layers are based on the material MCrAlX wherein M is one or more of nickel, cobalt and iron, and X is yttrium. It is an object of the present invention to solve the aforementioned problems of the conventional techniques and to propose a coating technique for advantageously solving problems such as lowering of productivity, contamination of alloy coating based on the adoption of different metal, cost up based on the adoption of different coating process and the like. DISCLOSURE OF THE INVENTION The invention does not lie in a method adopting a different film-forming means and using a different metal as in the conventional technique, but lies in a technique forming a coating having an excellent resistance to high-temperature oxidation by using same film-forming means, same metal and same metal oxide. That is, the invention is a technique based on the following thoughts. (1) To prevent that the components in the MCrAlX alloy sprayed coating formed on the surface of the member exposed to high temperature rapidly diffuse into the inside of the substrate through with the rise of temperature in the gas turbine. (2) To maintain good mechanical properties over a long time by preventing the formation and growth of a modified layer having poor mechanical strength and low strength to thermal strength on the surface of high temperature substrate. (3) To eliminate an adoption of a different film-forming method such as formation of Al 2 O 3 underlayer thin film through PVD process or the like and formation of MCrAlX alloy sprayed coating through spraying process. (4) To eliminate the necessity of spraying a different high-melting point metal such as Nb, Ta or the like as an undercoat prior to the spraying of MCrAlX alloy. (5) To eliminate the degradation of resistance to high-temperature oxidation resulted from the metal such as Nb, Ta or the like included in the MCrAlX alloy when the cleaning in the line is insufficient. (6) In the conventional technique, the thin film such as Al 2 O 3 , Nb, Ta or the like formed as a lower layer is apt to bring about the lowering of the adhesion property of the MCrAlX alloy coating as an upper layer, so that it is difficult to form the film (when the internal diffusion of the MCrAlX alloy is prevented by Al 2 O 3 or the like, it is apt to cause the peeling due to the lowering of the adhesion property, while when the adhesion property is improved, the diffusion of the alloy into the inside of the substrate becomes deeper, which results in the lowering of the mechanical properties of the substrate itself). In the invention, the film can be formed by a simple method without requiring the above complicated control. According to the present invention, there is provided a spray coated member for use in high-temperature, comprising a composite sprayed coating comprising: an oxide-containing undercoat sprayed coating obtained by spraying a MCrAlX alloy spraying material (wherein M is one or more of Ni, Co and Fe, and X is one or more of Y, Hf, Ta, Cs, Pt, Ce, Zr, La, Si and Th) containing a powder of one or more oxides selected from CoO, NiO, Cr 2 O 3 , Al 2 O 3 , Y 2 O 3 , MgO, SiO 2 and ZrO 2 onto a surface of a heat-resistant alloy substrate in air, wherein the total amount of oxide powder included in the undercoat sprayed coating is within the range of 0.2 to 20% by weight; a non-oxide topcoat sprayed coating obtained by spraying a MCrAlX alloy spraying material (wherein M is one or more of Ni, Co and Fe, and X is one or more of Y, Hf, Ta, Cs Pt, Ce, Zr, La, Si and Th) onto the undercoat under a low pressure containing substantially no oxygen; and an Al or Cr diffused layer formed on the outermost surface of the topcoat. The present invention also provides a method of producing a spray coated member for use at high temperature, wherein: (1) an oxide-containing undercoat sprayed coating is formed by spraying a mixture of a MCrAlX alloy material (wherein M is one or more of Ni, Co and Fe, and X is one or more of Y, Hf, Ta, Cs, Pt, Ce, Zr, La, Si and Th) and one or more oxides selected from CoO, NiO, Cr 2 O 3 , Al 2 O 3 , Y 2 O 3 , MgO, SiO 2 and ZrO 2 onto a surface of a heat-resistant alloy substrate in air by a film-formable spraying process, wherein the total amount of oxide powder included in the undercoat sprayed coating is within the range of 0.2 to 20% by weight; (2) a non-oxide topcoat sprayed coating is formed thereon by spraying a MCrAlX alloy material (wherein M is one or more of Ni, Co and Fe, and X is one or more of Y, Hf, Ta, Cs Pt, Ce, Zr, La, Si and Th) onto the undercoat under a low pressure containing substantially no oxygen by a film-formable spraying process; and (3) after the formation of the topcoat, an Al diffusion treatment or Cr diffusion treatment is further carried out thereon to increase the Al concentration or Cr concentration in the surface layer portion of the topcoat. In an embodiment of the method, the MCrAlX alloy is mixed with 0.2 to 20 wt% of various oxide powders and directly formed on a high-temperature exposed member at a thickness of 10 to 300 µm through the atmospheric plasma spraying process or flame spraying process and thereafter MCrAlX alloy containing no oxide is formed thereon at a thickness of 100 to 800 µm through the low-pressure plasma spraying process in a non-oxidizing atmosphere. The sprayed coating formed on the high-temperature exposed member by this method is subjected to a heat treatment in air or argon atmosphere or under vacuum, if necessary, to enhance bonding force of mutual particles constituting the MCrAlX alloy sprayed coating formed as the upper layer portion (topcoat) to conduct densification for preventing the invasion of corrosive gas component from exterior and improving the adhesion property to the lower layer portion (undercoat). The composite sprayed coating, after the heat treatment, is subjected to Al diffusion or Cr diffusion treatment, to give a higher resistance to high-temperature oxidation. In the invention, a powder of one or more oxides selected from CoO, NiO, Cr 2 O 3 , Al 2 O 3 , Y 2 O 3 , MgO, SiO 2 and ZrO 2 is included in the undercoat sprayed coating. The total amount of oxide powder included in the undercoat sprayed coating is within the: range of 0.2 to 20% by weight. In the invention, the topcoat sprayed coating has further a Al or Cr diffused layer at its surface side. In the invention, it is preferable that the undercoat sprayed coating has a thickness of 10 to 300 µm and the topcoat sprayed coating has a thickness of 100 to 800 µm. In the invention, it is preferable that a thin diffusion layer of an alloying component of not more than 70 µm is formed on the surface of the substrate when being heated under conditions of 1100°C for 8hr. In the invention, it is preferable that after the formation of the topcoat coating, a heat treatment is carried out in air or argon atmosphere or under vacuum, at 1000 to 1170°C for 1 to 5hr with respect to the topcoat coating. In the invention, after the formation of the topcoat, Al diffusion treatment or Cr diffusion treatment is further carried out thereon to increase the Al concentration or Cr concentration in the surface layer portion of the topcoat. BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a partial diagrammatic view of a sectional structure in the conventional MCrAlX alloy sprayed coating. Fig. 2 is a partial diagrammatic view of a sectional structure in a spray coated member of a reference example. Fig. 3 is a partial diagrammatic view of a sectional structure in another composite spray coated member according to the invention. BEST MODE FOR CARRYING OUT THE INVENTION The invention proposes a composite coating of MCrAlX alloy having a good adhesion property and an excellent resistance to high-temperature oxidation though an amount of diffusion into an inside of a substrate and a method of coating a surface thereof. The details of the structure of the composite coating will be described below. A. Undercoat MCrAlX alloy sprayed coating and the formation thereof; As a substrate to be treated, there is used Ni-based alloy, Co-based alloy or the like frequently used as a gas turbine blade. After the surface of the substrate is degreased and roughened by blast treatment, MCrAlX alloy is applied at a thickness of 10-300 µm in air to form an undercoat coating. When the undercoat coating sprayed in air is heated or rendered into a molten state by a heat source for the spraying, it is oxidized by air (oxygen) invaded from the periphery of the heat source to formed an oxide film on the surface of the MCrAlX alloy particle. That is, the undercoat coating is constructed by the aggregate of the MCrAlX alloy particles covered with the oxide film. As a result of the inventors' investigation, the content of oxide in the MCrAlX alloy sprayed coating is 0.9~1.5 wt% in case of the formation through the atmospheric plasma spraying process and 0.1-0.15 wt% (in this case, value converted to oxygen) in case of the formation through the high-velocity flame spraying process. The MCrAlX alloy particles covered at the surface with the oxide film are weak in the bonding force between mutual particles and are naturally insufficient in the adhesion property to the substrate and the coating itself is porous. Therefore, they are poor in the resistance to high-temperature oxidation and unsuitable as a coating for the gas turbine blade as it is. For this end, it is generally usual to solve the above drawback in the atmospheric plasma spraying process by applying a low pressure plasma spraying process containing substantially no oxygen. All of the sprayed coatings for the existing gas turbine blade are formed by the low pressure plasma spraying process. However, the MCrAlX alloy sprayed coating formed by the low pressure plasma spraying process does not contain an oxide and possesses a chemically strong active force, so that when the gas turbine is used at a higher temperature, it excessively diffuses into the substrate to cause the problems as previously mentioned. Under the above circumstance, the inventors have considered that if the oxide is previously included in the MCrAlX alloy coating, it obstructs the above diffusion and can solve the above problems accompanied with the use of the gas turbine at the higher temperature. That is, this point is a maximum reason why the atmospheric plasma spraying process or the high-velocity flame spraying process as a method of forming the undercoat is adopted in the invention. Furthermore, the oxides in the MCrAlX alloy sprayed coating sprayed in air are constituted with oxides of the alloying components, such as CoO or NiO when M is Co or Ni, Cr 2 O 3 , Al 2 O 3 and Y 2 O 3 when X is Y or the oxide having the same components. And also, all oxides are inactive as compared with the metal component thereof and do not diffuse into the alloy of the substrate and are excellent in the heat resistance. When the sprayed coating of the MCRAlX alloy containing the oxide as mentioned above is applied onto the surface of the substrate as an undercoat, even if the temperature of the use environment is not lower than 1000°C, the above oxide obstructs the diffusion of the MCrAlX alloy and hence the excessive diffusion into the inside of the substrate is eliminated. However, the oxide existing in the sprayed coating of the MCrAlX alloy formed in air is ununiform and the properties of the oxide itself become frequently incomplete state as compared with those of a stoichiometric oxide. On the other hand, many particles not oxidized are existent in the alloy. Therefore, when such a sprayed coating is heated to a higher temperature, the diffusion into the inside of the substrate somewhat occurs. However, the diffusion rate and amount are very less as compared with those of the coating formed by the low pressure plasma spraying process. Moreover, it may be rather favorable to somewhat cause the internal diffusion in order that the MCrAlX alloy sprayed coating is stably existent on the surface of the substrate over a long time of period, so that the undercoat sprayed coating of the MCrAlX alloy through the atmospheric plasma spraying process is required to be a coating adapted to the above conditions. When the content of the oxide is lacking only in the MCrAlX alloy sprayed coating through the atmospheric plasma spraying process, 0.2∼20 wt% of oxide powder (particle size: 5~10 µm) as a constituent component of the MCrAlX alloy is previously added to the spraying material, which is sprayed to further control the diffusion into the inside of the substrate. When the total amount of the oxide is less than 0.2 wt%, the action of obstructing the diffusion is less, while when it exceeds 20 wt%, the complete diffusion obstruction is inversely caused and the adhesion function as the undercoat is lost. The thickness of the undercoat sprayed coating is within a range of 10-300 µm, preferably a range of 50-100 µm. When it is less than 10 µm, it is difficult to form the coating at an equal thickness by the spraying process, while when it exceeds 300 µm, the function as the diffusion obstruction is not improved and it is not economical. B. Topcoat MCrAlX alloy sprayed coating and the formation thereof; The undercoat sprayed coating of the MCrAlX alloy containing the oxide is small in the diffusion rate into the inside of the substrate, but is weak in the bonding force between the particles constituting the coating as it is and is porous, so that when it is used under an operating environment of gas turbine at a high temperature, there is caused a problem that the body to be treated (e.g. a turbine blade) is oxidized at a high temperature or subjected to a high-temperature corrosion by a combustion gas component invaded from pores of the coating. In order to solve this problem, according to the invention, a topcoat sprayed coating of MCrAlX alloy is further formed on the undercoat sprayed coating by a low pressure plasma spraying process in a non-oxidizing atmosphere. The topcoat sprayed coating is strong in the bonding force between the particles and good in the adhesion property to the undercoat sprayed coating. After the formation of the topcoat sprayed coating, when the heat treatment is carried out in air or argon atmosphere or under vacuum at 1000∼1170°C for 1∼5 hours, the pores of the topcoat sprayed coating are completely disappeared, whereby the resistance to high-temperature oxidation and the resistance to high-temperature corrosion can sufficiently be improved. The surface of the coating after the formation of the topcoat sprayed coating is subjected to Al or Cr diffusion treatment, whereby a layer of a high Al or Cr concentration having an excellent oxidation resistance is formed on the outermost surface layer portion of the topcoat sprayed coating and also a stronger bonding force between the particles constituting the topcoat is developed. As the Al or Cr diffusion treatment, use may be made of a powder process (the body to be treated is embedded in powder made of metallic Al, Al alloy powder, Al 2 O 3 halide, metallic Cr, Cr alloy powder or the like and heated at 900∼1100°C for 3-10 hours), a chemical deposition process (metallic Al, metallic Cr are precipitated by subjecting an organic or inorganic Al, Cr compounds to heat decomposition or hydrogen reduction reaction and then adhered to the surface of the body to be treated), a physical deposition process (Al or Cr is evaporated by a heat source such as electron beam or the like and adhered to the surface of the body to be treated) and the like. The thickness of the topcoat sprayed coating is within a range of 100~800 µm, preferably a range of 200~500 µm. When it is less than 100 µm, the resistance to high-temperature oxidation is insufficient, while when it exceeds 800 µm, the performances as the coating are not extremely improved and it is uneconomical. Although the formation of the undercoat sprayed coating and the topcoat sprayed coating is described by taking the atmospheric plasma spraying process or the low-pressure plasma spraying process, the following process can be adopted as seen from the function and mechanism. 1 ○ In the formation of the undercoat, it is an essential condition that the oxide is included into the coating by spraying in air. In this meaning, combustion flame of combustible gas, explosion energy of combustible gas or the like may be used as a spraying heat source in addition to plasma. 2 ○ In the formation of the top coat, the low pressure plasma spraying process forming the coating in an atmosphere containing substantially no oxygen is optimum, but a pressure plasma spraying process or a spraying process using a laser as a heat source may be used if the atmosphere contains substantially no oxygen. And also, it can be said that it is possible to form the coating by a deposition process using an electron beam as a heat source in a vacuum vessel. 3 ○ The combination of MCrAlX alloy materials used in the undercoat and the topcoat is not particularly restricted because the object of the invention can be attained even in any combination when the alloy is same components or may be represented by MCrAlX. Fig. 1 diagrammatically shows a sectional structure of the MCrAlX alloy sprayed coating formed by the conventional low pressure plasma spraying process, in which a MCrAlX alloy coating 2 is formed on a substrate 1 of a high-temperature exposed member. When the alloy coating is heated to a higher temperature above, 1000°C, the alloying components deeply diffuse into the inside of the substrate 1. As shown in Fig. 2, in a reference example that an oxide-containing undercoat sprayed coating 4 of MCrAlX alloy is formed by the atmospheric plasma spraying process and then a topcoat sprayed coating 2 of MCrAlX alloy is formed thereon by a low pressure spraying process, the diffusion into the inside of the member to be exposed is slight even if it is heated to a higher temperature. That is, there is a state of producing a diffusion layer 3' having a very slight thickness of not more than 70 µm, preferably not more than 60 µm, more particularly not more than 40 µm on the substrate 1. Fig. 3 shows an example that Al diffusion layer 5 is provided on an outermost surface layer portion of a topcoat sprayed coating 2, according to the invention. Now, the chemical composition of the sprayed coating used in the invention is called as MCrAlX alloy as mentioned above, and a typical composition of this alloy is shown as follows. M component: Ni (0~75 wt%), Co (0∼70 wt%), Fe (0~30 wt%) Cr component: 5~10 wt% Al component: 1~29 wt% X component: Y (0~5 wt%), Hf (0∼10 wt%) In the invention, Ta (1~20 wt%), Si (0.1~14 wt%), B (0∼0.1 wt%), C (0∼0.25 wt%), Mn (0~10 wt%), Zr (0~3 wt%), W (0~5.5 wt%), Cs, Ce, La (0~5 wt%, respectively), Pt (0~20 wt%) and the like may be added, if necessary, in addition to the above components. EXAMPLES Reference Example (not in accordance with the invention) In this reference example, there are compared depths of diffusion layers into an inside of a Ni-based alloy substrate in composite sprayed coating which is formed on the surface of the Ni-based alloy substrate and consists of an undercoat sprayed coating of MCrAlX alloy formed by atmospheric plasma spraying process and a topcoat sprayed coating of MCrAlX alloy formed by low pressure plasma spraying process. And also, various kinds of the MCrAlX alloy spraying materials are used in the following examples and chemical compositions thereof are shown in Table 1. That is, the spraying materials can be roughly divided into an alloy spraying material containing no Ni (A), alloy spraying material containing no Co (B, C, D, E), alloy material containing Ni and Co (F, G) and a material obtained by adding 5 wt% of Ta, which is not included in the other alloys, to the alloy G. A. Test specimens: The Ni-based alloy (15.3 wt% Ni-7 wt% Fe-2.5 wt% Ti-2 wy% Mo-10 wt% Co-reminder Ni) is shaped into a rod test specimen having an outer diameter of 15 mm and a length of 50 mm, onto which is formed a coating having a thickness of 300 µm by using the MCrAlX alloy (A, C, E, F, G) shown in Table 1 through the following spraying process. 1 ○ Composite sprayed coating of MCrAlX alloy The MCrAlX alloy is applied at a thickness of 100 µm through the atmospheric plasma spraying process and then applied thereonto at a thickness of 200 µm through the low pressure plasma spraying process so as to have a total thickness of 300 µm. 2 ○ MCrAlX alloy sprayed coating for comparison The same MCrAlX alloy as mentioned above is applied at a thickness of 300 µm through the low-pressure plasma spraying process. B. Heating experimental method: After the test specimen of the MCrAlX alloy coating is heated in an electric furnace at 1100°C x 8 h while flowing argon gas, the test specimen is cut to observe a diffusion state of alloy coating components into the Ni-based alloy by means of an optical microscope. C. Results: In Table 2 are summarized results measured on the depth of the diffusion layer into the Ni-based alloy substrate by the above heating experiment. As seen from these results, the diffusion layer of single phase coating formed by the low pressure plasma spraying process of the comparative examples (Test specimen Nos. 6∼10) reaches 87-98 µm, which shows a very diffusability. The composite sprayed coating (Test specimen Nos. 1∼5) stop to a depth of 49-61 µm and there is recognized a state of shallowing the diffusion into the inside of the Ni-based alloy. Symbol Chemical composition (wt%) Ni Co Cr Al Y Ta A 63.4 23 13 0.6 B 76.5 17 6 0.5 C 67.0 22 10 1.0 D 70.6 23 6 0.4 E 77.2 16 6 0.8 F 32.0 38.5 21 8 0.5 G 10.0 52.8 25 7 0.6 5 No. McrAlX Alloy Structure and thickness of coating (µm) Thickness of diffusion layer (µm) (1100°C×8h) Remarks Kind of spraying Undercoat Topcoat Atmospheric plasma Low pressure plasma 1 A 100 200 49 Acceptable Example 2 C 100 200 60 3 E 100 200 61 4 F 100 200 54 5 G 100 200 50 6 A 300 88 Comparative Example 7 C 300 95 8 E 300 98 9 F 300 94 10 G 300 87 Note (1) A sprayed coating of McrAlX alloy in Specimens No.6-10 is only one layer of 300 µm formed by a low pressure plasma spraying process. Example 1 In this example, the adhesion properties of the coatings are compared by subjecting the composite sprayed coating formed on the Ni-based alloy substrate according to the invention or the coating consisting of the atmospheric plasma sprayed coating of MCrAlX alloy (undercoat) and low pressure plasma sprayed coating of the same alloy (topcoat) to a thermal shock test. A. Test specimen: 1 ○ Composite sprayed coating of MCrAlX alloy Onto the Ni-based alloy substrate used in the reference Example is formed the undercoat having a thickness of 100 µm by using four kinds of MCrAlX alloy (A, B, C, D) through the atmospheric plasma spraying process, and the topcoat having a thickness of 200 µm is formed thereon by using the same MCrAlX alloy through low pressure plasma spraying process. 2 ○ MCrAlX alloy sprayed coating of Comparative Example a. Onto the above Ni-based alloy substrate is formed the coating having a thickness of 300 µm by using the same four kinds of MCrAlX alloy (A, B, C, D) through the atmospheric plasma spraying process. b. Onto the above Ni-based alloy substrate is formed the coating having a thickness of 300 µm by using the same four kinds of MCrAlX alloy (A, B, C, D) through low pressure plasma spraying process. B. Al diffusion treatment: The Al diffusion treatment is applied to a half of test specimens of the composite sprayed coatings according to a reference and the atmospheric plasma sprayed coating of the comparative example and all of the low pressure plasma sprayed coatings for the topcoat. The conditions are as follows. Diffusion component (Ni-Al alloy 30 wt%, Al 2 O 3 69 wt%, NH 4 Cl 1 wt%) Treating conditions: 930°C x 4 h C. Results: The experimental results are shown in Table 3. As seen from this table, in the atmospheric plasma sprayed coatings of the comparative example (Test specimen Nos. 5∼8), the coating of the MCrAlX alloy is peeled off by repeating the thermal shock 12-16 times. When being subjected to the Al diffusion treatment, the effect is somewhat observed, but is insufficient. On the contrary, the low pressure plasma sprayed coatings (Test specimen Nos. 9-12) are durable to thermal shock of not less than 25 times and maintain a good sound state and show a good adhesion property even in the comparative example. However, these coatings have a drawback that the formation of the diffusion layer into the inside of the Ni-based alloy becomes large as shown in the reference Example (Table 2). The sprayed coatings according to the invention (Test specimen Nos. 1∼3) are durable to thermal shock of 25 times likewise the low pressure plasma sprayed coating and recognize the good adhesion property. This is considered due to the fact that the dense low pressure sprayed coating is formed on the atmospheric plasma sprayed coating having a low adhesion property, whereby air invaded from the pore portions of the coating is shut off to develop the effect of preventing the oxidation of the Ni-based alloy substrate. The thermal shock test in Table 3 is such a thermal shock test that an operation of heating each test specimen of the sprayed coating at 1000°C x 30 minutes in an electric furnace of an atmosphere and then charging into water at 25°C is one cycle, and the appearance of the coating is visually observed every one cycle to examine the presence or absence of the peeling. No McrAlX Alloy Structure and thickness of coating (µm) Results of thermal shock test Remarks Kind of spraying Al diffusion treatment 1000°C×30min charged into water at 25°C Undercoat Topcoat Number until peeling occurs Atmospheric plasma Low pressure plasma 1 A 100 200 Presence Not less than 25 times Acceptable Example 2 B 100 200 Absence Not less than 25 times 3 C 100 200 Presence Not less than 25 times 4 D 100 200 Absence Not less than 25 times 5 A 300 Presence Local peeling at 16 times Comparative Example 6 B 300 Absence Peeling at 14 times 7 C 300 Presence Local peeling at 16 times 8 D 300 Absence Peeling at 12 times 9 A 300 Presence Not less than 25 times 10 B 300 Presence Not less than 25 times 11 C 300 Presence Not less than 25 times 12 D 300 Presence Not less than 25 times Note (1) Each McrAlX alloy sprayed coating of test specimen Nos. 5-8 is a single coating of 300µm in thickness through atmospheric plasma spraying process. (2) Each McrAlX alloy sprayed coating of test specimen Nos. 9-12 is a single coating of 300µm in thickness through low pressure plasma spraying process. (3) Al diffusion treatment is carried out at 930°C×4h. (4) The judgement of thermal shock test is represented by the number when 5% of the coating area is peeled off. Example 2 In this example, test for high-temperature corrosion and test for high-temperature sulfurization are made with respect to products obtained by forming the composite sprayed coating of MCrAlX alloy according to the invention onto Ni-based alloy substrate or Co-based alloy substrate, and the resistance to high-temperature environment is compared with those of single sprayed coating of MCrAlX alloy formed by the atmospheric plasma spraying process or low pressure plasma spraying process as a comparative example. A. Test specimen: 1 ○ Composite sprayed coating of MCrAlX alloy A test specimen of 30 mm width x 50 mm length x 5 mm thickness is prepared by using the following two heat-resistant alloys as a substrate to be sprayed. a. Ni-based alloy: same as in the reference Example b. Co-based alloy: 29.5 wt% Cr-10.5 wt% Ni-7.0 wt% W-2 wt% Fe-reminder Co An undercoat of 100 µm in thickness is formed by using MCrAlX alloy (A, C, E, G) as a spraying material through the atmospheric plasma spraying process and a topcoat of 300 µm in thickness is formed thereon by using the same MCrAlX alloy. 2 ○ Single sprayed coating of MCrAlX alloy of Comparative Example a. A coating of 300 µm in thickness is formed on the above Ni-based alloy substrate or Co-based alloy substrate by using the same four MCrAlX alloys (A, C, E, G) through the atmospheric plasma spraying process. b. And also, a sprayed coating of 400 µm in thickness is formed by using the same MCrAlX alloy as in the invention through the low pressure plasma spraying process as a comparative example. B. Al diffusion treatment The Al diffusion treatment as shown below is applied to a half of test specimens of the composite sprayed coatings according to a reference and the atmospheric plasma sprayed coating of the comparative example and all of the low pressure plasma sprayed coatings for the topcoat. Diffusion component: same as in Example 1 Treating conditions: same as in Example 1 C. Results: In Table 4 are summarized the above test results for high-temperature corrosion. In the section of the atmospheric plasma sprayed coating of the comparative examples (Test specimen Nos. 5∼8), corrosion components (V and S in vanadium corrosion, S and Cl in high-temperature sulfurization corrosion) very deeply penetrates into the inside of the coating (65-135 µm), while the penetration of the corrosion components stops to a range of 20-70 µm in the composite sprayed coatings according to the invention (Test specimen Nos 1, 3), and the resistance to high-temperature corrosion is excellent. The resistance to high-temperature corrosion of the coating according to the invention is equal to those (20-71 µm) of the low pressure plasma sprayed coatings of the comparative examples (Test specimen Nos. 9-12) used in the existing technique. The coating according to the invention holds the sufficient resistance to high-temperature corrosion against the corrosion components constituting the combustion gas atmosphere. And also, the effect of the Al diffusion treatment is recognized in the vanadium corrosion test and the high-temperature sulfurization test. As seen from the above results, in the atmospheric plasma sprayed coating, the penetration of the corrosion components is easy due to many pores, which is a big cause of lowering the resistance to high-temperature corrosion, and also even if the Al diffusion treatment is conducted, the pores are not completely sealed. On the contrary, the low pressure plasma sprayed coating is dense at the film formed state and it is considered that the densification is more improved by the Al diffusion treatment to prevent the penetration of the corrosion components. The high-temperature corrosion test in Table 4 is carried out as follows. 1 ○ Vanadium corrosion test: composition of agent : 80%V 2 O 5 -20%NaCl temperature x time: 900°C x 3h 2 ○ High-temperature sulfurization test: composition of agent: 90%Na 2 SO 4 -10%NaCl temperature x time: 1000°C x 4h Moreover, the amount of the agent applied is 25 mg per 1 cm 2 of the sprayed coating in both the tests. The coating is held at given temperature and time in an electric furnace and then taken out therefrom to inspect the section of the coating at the corroded portion and observe the penetration depth of the corrosion components by means of an X-ray microanalyzer, whereby the resistance to high-temperature corrosion of the coating is examined. No McrAlX Alloy Structure and thickness of coating (µm) Penetration rate through corrosion (µm) Remarks Kind of spraying Al diffusion treatment High-temperature corrosion test High-temperature sulfurization test Undercoat Topcoat Atmospheric plasma Low pressure plasma 1 A 100 300 Presence 20 ∼ 55 26 ∼ 70 Acceptable Eample 2 C 100 300 Absence 28 ∼ 61 25 ∼ 68 3 E 100 300 Presence 22 ∼ 58 22 ∼ 70 4 G 100 300 Absence 25 ∼ 70 29 ∼ 55 5 A 400 Presence 80 ∼120 65 ∼130 Comparative Example 6 C 400 Absence 95 ∼130 80 ∼135 7 E 400 Presence 85 ∼120 95 ∼120 8 G 400 Absence 100 ∼130 98 ∼128 9 A 400 Presence 20 ∼ 60 28 ∼ 71 10 C 400 Presence 26 ∼ 65 28 ∼ 68 11 E 400 Presence 28 ∼ 68 25 ∼ 60 12 G 400 Presence 23 ∼ 60 25 ∼ 50 Note (1) The McrAlX alloy coating of test specimen Nos. 5-8 is a single coating of 400 µm in thickness through atmospheric plasma spraying process. (2) The McrAlX alloy sprayed coating of test specimen Nos. 9-12 is a single coating of 400 µm in thickness through atmospheric plasma spraying process. (3) Al diffusion test is carried out at 950°C×4h. (4) High-temperature corrpsion test: 80%V 2 O 5 -20%Na 2 O 4 , 900°C×3h (5) High-temperature sulfurization test: 90%Na 2 O 4 -10°aNaCl, 100°C×4h (6) The substrate of the test specimen in an even number is Co-based alloy (29.5%Cr-10.0%Ni-7. 0%W-2.0%W-reminder%Co), and that in an odd number is Ni-based alloy (described in Example 1). INDUSTRIAL APPLICABILITY As seen from the above explanations and the results of the examples, the composite sprayed coating of MCrAlX alloy consisting of the oxide sprayed coating and non-oxide sprayed coating and Al or Cr diffused layer according to the invention is small in the thickness of the diffusion layer into the inside of the member to be exposed even if the environment temperature becomes higher, so that it is shows a good resistance to thermal shock and develops an excellent performance to the resistance to high-temperature corrosion. As a result, the member sprayed with MCrAlX alloy according to the invention is possible to be produced in a good productivity and a low cost by using the same kind of the spraying process and the same kind of metal in a field of gas turbine anticipating the rise of the temperature in future. And also, the invention is suitable as a high temperature member used in a blast furnace, a heat treating furnace or the like, or a heat-resistant member used in rocket, space shuttle or the like.

Claims: A spray coated member for use in high-temperature, comprising a composite sprayed coating comprising: an oxide-containing undercoat sprayed coating obtained by spraying a MCrAlX alloy spraying material (wherein M is one or more of Ni, Co and Fe, and X is one or more of Y, Hf, Ta, Cs, Pt, Ce, Zr, La, Si and Th) containing a powder of one or more oxides selected from CoO, NiO, Cr 2 O 3 , Al 2 O 3 , Y 2 O 3 , MgO, SiO 2 and ZrO 2 onto a surface of a heat-resistant alloy substrate in air, wherein the total amount of oxide powder included in the undercoat sprayed coating is within the range of 0.2 to 20% by weight; a non-oxide topcoat sprayed coating obtained by spraying a MCrAlX alloy spraying material (wherein M is one or more of Ni, Co and Fe, and X is one or more of Y, Hf, Ta, Cs, Pt, Ce, Zr, La, Si and Th) onto the undercoat under a low pressure containing substantially no oxygen; and an Al or Cr diffused layer formed on the outermost surface of the topcoat. A spray coated member according to claim 1, wherein the undercoat sprayed coating has a thickness within the range of 10 to 300 µm. A spray coated member according to claim 1, wherein the topcoat sprayed coating has a thickness within the range of 100 to 800 µm. A spray coated member according to claim 1, wherein a thin diffusion layer of an alloying component of not more than 70 µm is formed on the surface of the substrate when being heated under conditions of 1100°C for 8 hr. A method of producing a spray coated member for use at high temperature, wherein: (1) an oxide-containing undercoat sprayed coating is formed by spraying a mixture of a MCrAlX alloy material (wherein M is one or more of Ni, Co and Fe, and X is one or more of Y, Hf, Ta, Cs, Pt, Ce, Zr, La, Si and Th) and one or more oxides selected from CoO, NiO, Cr 2 O 3 , Al 2 O 3 , Y 2 O 3 , MgO, SiO 2 and ZrO 2 onto a surface of a heat-resistant alloy substrate in air by a film-formable spraying process, wherein the total amount of oxide powder included in the undercoat sprayed coating is within the range of 0.2 to 20% by weight; (2) a non-oxide topcoat sprayed coating is formed thereon by spraying a MCrAlX alloy material (wherein M is one or more of Ni, Co and Fe, and X is one or more of Y, Hf, Ta, Cs, Pt, Ce, Zr, La, Si and Th) onto the undercoat under a low pressure containing substantially no oxygen by a film-formable spraying process; and (3) after the formation of the topcoat, an Al diffusion treatment or Cr diffusion treatment is further carried out thereon to increase the Al concentration or Cr concentration in the surface layer portion of the topcoat. The method according to claim 5, wherein after the formation of the top coating, a heat treatment is carried out in air or argon atmosphere or under vacuum at 1000 to 1170°C for 1 to 5 hr with respect to the topcoat coating.

Inventors: HARADA YOSHIO, SUIZU TATSUO, TERATANI TAKEMA, HARADA, YOSHIO, SUIZU, TATSUO, TERATANI, TAKEMA, TERATANI, Takema, 106 Sent. Uozaki
Applicants: TOCALO CO LTD, TOCALO CO. LTD.
Application year: 1998
Main classification: C23C4
IPC codes: C23C16, C23C4, C23C28