JP2006159216A - Material for powder plasma arc welding, and wear resistive member at high temperature - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a coating material which is effective for a member which needs the wear resistance at a high temperature. <P>SOLUTION: A material for powder plasma welding contains matrix powder and hard powder. The matrix powder is made of γ' precipitation strengthening type Ni group super alloy. The hard powder contains 25 to 35 wt.% of Cr<SB>3</SB>C<SB>2</SB>powder and 5 to 10 wt.% of NbC powder. It is preferable that the material for powder plasma welding further contains 5 to 10 wt.% of Cr<SB>3</SB>B<SB>2</SB>powder as the hard powder, and the γ' precipitation strengthening type Ni group super alloy contains 15 to 25 wt.% of Cr, 5 to 10 wt.% of Mo, 10 to 15 wt.% of Co, 0.5 to 1 wt.% of W, 1 to 5 wt.% of Al, 1 to 5 wt.% of Ti, and the balance substantially being Ni. <P>COPYRIGHT: (C)2006,JPO&NCIPI

Description

  The present invention relates to an overlay welding material having excellent corrosion resistance and wear resistance under a high temperature environment of 600 to 900 ° C., and particularly wear resistance by providing a coating layer on an air nozzle installed in a circulating fluidized bed boiler. It relates to a technology that improves safety.

  The circulating fluidized bed boiler blows combustion air into the circulating fluidized bed boiler by an air nozzle, coal supplied from the outside and unburned ash returned from the downstream, and a fluidized material previously stored in the circulating fluidized bed boiler ( Inactive particles such as silica sand or a desulfurizing agent such as limestone are mixed and fluidized to form a fluidized bed to promote combustion (for example, JP 2004-28430 A (Patent Document 1)). ).

  When the operation of the circulating fluidized bed boiler is continued, the air nozzle is worn by the collision of the fluidized material. Due to this wear, the diameter of the hole through which the air is ejected is enlarged, and the air ejection pressure and the fluidity of the fluidized material are changed. Moreover, the base material itself constituting the air nozzle is thinned by wear. Conventionally, the air nozzle is made of stainless steel such as SUS304, but the stainless steel itself cannot secure sufficient corrosion resistance at a fluidized bed temperature of 600 to 900 ° C.

JP 2004-28430 A JP 2002-239713 A

  The present invention has been made based on such a technical problem, and an object thereof is to provide an effective coating material for a member such as an air nozzle which requires wear resistance in a high temperature environment. And It is another object of the present invention to provide a high temperature wear resistant member provided with such a coating material.

The present inventors examined materials used for powder plasma overlay welding, particularly materials for dispersing hard particles in a matrix, on the premise that powder plasma overlay welding is used as a coating technique. As a result, it has been found that Cr ₃ C ₂ , NbC or Cr ₃ B ₂ is effective as hard particles in order to obtain wear resistance at high temperatures. That is, as the hard particles, even those having high hardness at normal temperature, those having poor oxidation resistance at high temperature do not meet the object of the present invention. For example, VC, WC, and the like are difficult to use as the hard particles of the present invention because the oxidation resistance is poor at about 500 ° C. On the other hand, Cr ₃ C ₂ , NbC or Cr ₃ B ₂ can be used up to a temperature range of about 900 ° C.

  The material constituting the matrix is required to have oxidation resistance in a temperature range of about 600 to 900 ° C. Moreover, even if hard particles are dispersed, it is necessary for the matrix itself to have a predetermined hardness in the temperature range in order to have wear resistance as a coating. From this viewpoint, the present inventor is effective to use a γ ′ precipitation strengthened Ni-base superalloy or a Ni-base alloy previously proposed by the applicant in Japanese Patent Laid-Open No. 2002-239713 (Patent Document 2). It was confirmed.

The present invention has been made based on the above knowledge, and includes a matrix powder and a hard powder, the matrix powder is made of a γ ′ precipitation strengthened Ni-base superalloy, and the hard powder is 25 to 35 wt% Cr. A powder plasma welding material (hereinafter sometimes referred to as a first welding material) characterized by comprising ₃ C ₂ powder and 5-10 wt% NbC powder.

In the first welding material, it is desirable to further include 5 to 10 wt% of Cr ₃ B ₂ powder as the hard powder in order to improve wear resistance.
In the first welding material, as the γ ′ precipitation strengthened Ni-base superalloy, Cr: 15 to 25 wt%, Mo: 5 to 10 wt%, Co: 10 to 15 wt%, W: 0.5 to 1 wt% It is desirable to use an alloy consisting of Al: 1 to 5 wt%, Ti: 1 to 5 wt%, and the balance substantially Ni.

In addition to the first welding material, the present invention includes a matrix powder and a hard powder, and the matrix powder is made of Cr: 25 to 45 wt%, Al: 5 to 20 wt%, and the balance being substantially Ni alloy powder, Provided is a powder plasma welding material (hereinafter sometimes referred to as a second welding material), characterized in that the hard powder comprises 25 to 35 wt% Cr ₃ C ₂ powder. The second welding material is different from the first welding material in the alloy constituting the matrix.

The present invention provides a high temperature wear resistant member using the first welding material and the second welding material. That is, a high-temperature wear-resistant member using the first welding material (hereinafter referred to as a first high-temperature wear-resistant member) includes a base material and a coating layer formed on the surface of the base material. In addition, 25 to 35 wt% Cr ₃ C ₂ particles and 5 to 10 wt% NbC particles are dispersed in a matrix made of a γ ′ precipitation strengthened Ni-base superalloy.

It is desirable that the first high temperature wear resistant member further disperse 5 to 10 wt% Cr ₃ B ₂ powder in the matrix.
In the first high-temperature wear-resistant member, the γ ′ precipitation strengthened Ni-base superalloy is Cr: 15 to 25 wt%, Mo: 5 to 10 wt%, Co: 10 to 15 wt%, W: 0.5 to It is desirable that 1 wt%, Al: 1 to 5 wt%, Ti: 1 to 5 wt%, and the balance be substantially Ni.

The high temperature wear resistant member using the second welding material (hereinafter, the second high temperature wear resistant member) includes a base material and a coating layer formed on the surface of the base material. Cr: 25 to 45 wt%, Al: 5 to 20 wt%, and the rest being 5 to 10 wt% of Cr ₃ C ₂ particles dispersed in a matrix substantially made of a Ni alloy.
In the first high-temperature wear-resistant member and the second high-temperature wear-resistant member, the coating layer is preferably formed by powder plasma overlay welding.

  ADVANTAGE OF THE INVENTION According to this invention, while being able to provide an effective coating material with respect to the member by which abrasion resistance in a high temperature environment is requested | required, the high temperature abrasion resistant member provided with such a coating material is provided. can do. Therefore, if the present invention is applied to the above-described air nozzle, it is possible to suppress the diameter of the air hole from expanding or thinning.

<First welding material, first high temperature wear resistant member>
In the first welding material, the matrix powder is composed of a γ ′ precipitation strengthened Ni-base superalloy.
The γ 'precipitation strengthened Ni-base superalloy is an alloy that ensures strength in a high temperature range by precipitating a fine intermetallic compound γ' phase (Ni ₃ (Al · Ti)) in a matrix mainly composed of Ni. It is. This alloy contains 10 to 20 wt% of Cr, and further contains about 10 to 20 wt% of Co from the viewpoint of ensuring heat resistance and corrosion resistance. In addition, this alloy contains a predetermined amount of Al and Ti for γ ′ phase (Ni ₃ (Al · Ti)) precipitation.

  As a material constituting the matrix in the first welding material, Cr: 15 to 25 wt%, Mo: 5 to 10 wt%, Co: 10 to 15 wt%, W: 0.5 to 1 wt%, Al: 1 to 5 wt %, Ti: 1 to 5 wt%, and the balance is preferably an alloy substantially made of Ni. This alloy is known as Udimet 520 (trade name). Further, this alloy has a representative composition of 56 wt% Ni-19 wt% Cr-12 wt% Co-6 wt% Mo-3 wt% Ti-2 wt% Al-1 wt% W, and has a high temperature strength at 750 to 950 ° C. It has been known.

As a material constituting the matrix in the first welding material, for example, a γ ′ precipitation strengthened Ni-base superalloy having the following representative composition can be applied.
Nimonic 90 (trade name): 60 wt% Ni-19.5 wt% Cr-16.5 wt% Co-2.5 wt% Ti-1.5 wt% Al
Nimonic 105 (trade name): 52 wt% Ni-15 wt% Cr-5 wt% Mo-20 wt% Co-1.3 wt% Ti-4.7 wt% Al
Nimonic 115 (trade name): 60 wt% Ni-14.2 wt% Cr-3.2 wt% Mo-13.2 wt% Co-3.8 wt% Ti-4.9 wt% Al
Nimonic 263 (trade name): 51 wt% Ni-20 wt% Cr-5.9 wt% Co-20 wt% Co-2.2 wt% Ti-0.4 wt% Al

M252 (trade name): 55 wt% Ni-20 wt% Cr-10 wt% Co-10 wt% Mo-2.6 wt% Ti-1 wt% Al
Waspaloy (trade name): 58 wt% Ni-19.5 wt% Cr-13.5 wt% Co-4.3 wt% Mo-3 wt% Ti-1.3 wt% Al
Rene 41 (trade name): 55 wt% Ni-19 wt% Cr-11 wt% Co-10 wt% Mo-3.1 wt% Ti-1.5 wt% Al
Udimet 500 (trade name): 54 wt% Ni-18 wt% Cr-18.5 wt% Co-4 wt% Mo-2.9 wt% Ti-2.9 wt% Al

Udimet 700 (trade name): 55 wt% Ni-15 wt% Cr-17 wt% Co-5 wt% Mo-3.5 wt% Ti-4.0 wt% Al
Udimet 710 (trade name): 55 wt% Ni-18 wt% Cr-15 wt% Co-3 wt% Mo-1.5 wt% W-5.0 wt% Ti-2.5 wt% Al
Udimet 720 (trade name): 55 wt% Ni-17.9 wt% Cr-14.7 wt% Co-3 wt% Mo-1.5 wt% W-5.0 wt% Ti-2.5 wt% Al

The first welding material contains 25 to 35 wt% Cr ₃ C ₂ powder and 5 to 10 wt% NbC powder as hard powder in addition to the above matrix powder. As described above, this hard powder has sufficient oxidation resistance even in the temperature range of 600 to 900 ° C.
The reason why the amount of Cr ₃ C ₂ powder is 25 to 35 wt% is that if it is less than 25 wt%, sufficient wear resistance cannot be obtained, and if it exceeds 35 wt%, cracks occur during welding. . A desirable amount of Cr ₃ C ₂ powder is 27 to 33 wt%, and a more desirable amount of Cr ₃ C ₂ powder is 28 to 32 wt%.
The reason why the amount of NbC powder is 5 to 10 wt% is that if it is less than 5 wt%, sufficient wear resistance cannot be obtained, and if it exceeds 10 wt%, cracks occur during welding. A desirable amount of NbC powder is 6-9 wt%, and a more desirable amount of NbC powder is 7-8 wt%.

In the first welding material, it is desirable to further contain 5 to 10 wt% of Cr ₃ B ₂ powder in addition to Cr ₃ C ₂ powder and NbC powder, in order to improve wear resistance. The reason why the Cr ₃ B ₂ powder is 5 to 10 wt% is that if it is less than 5 wt%, the effect of improving wear resistance is not sufficient, and if it exceeds 10 wt%, cracks occur during welding. A desirable Cr ₃ B ₂ powder amount is 6-9 wt%, and a more desirable Cr ₃ B ₂ powder amount is 7-8 wt%.

In the first welding material, the particle sizes of the matrix powder and the hard powder are not particularly limited. However, if the particle diameter is in the range of 50 to 200 μm, there is no problem in performing the powder plasma overlay welding.
In the first welding material, the manufacturing method of the matrix powder and the hard powder is not particularly limited, and a conventionally known manufacturing method such as an atomizing method or a pulverizing method may be used.
Furthermore, the presence form before the matrix powder and the hard powder are welded by powder plasma overlay welding is not particularly limited. That is, the matrix powder and the hard powder may be mixed in advance before the powder plasma overlay welding, or the matrix powder and the hard powder may be simultaneously supplied during the powder plasma overlay welding. Moreover, it is also possible to mix at the time of welding so that either the matrix powder or the hard powder is supplied in advance and the other is supplied to the molten part.

The first high-temperature wear-resistant member obtained as described above has a coating layer formed on the surface of the base material in a matrix made of γ ′ precipitation-strengthened Ni-base superalloy with a content of 25 to 35 wt% Cr. ₃ C ₂ particles and 5-10 wt% NbC particles are dispersed. The contents of the γ ′ precipitation strengthened Ni-base superalloy, Cr ₃ C ₂ particles, and NbC particles constituting the matrix are as described above. Further, it is desirable that the first high temperature wear resistant member further disperse 5 to 10 wt% Cr ₃ B ₂ particles in the matrix.

  In the first high-temperature wear-resistant member, the material of the base material is not particularly limited, but it is preferable to use stainless steel, heat-resistant steel or the like because it is premised on use in a high-temperature region. As a specific example of the wear-resistant member, the above-described air nozzle can be mentioned, but it goes without saying that it can be used for other members.

<Second welding material, second high-temperature wear-resistant member>
In the second welding material, the matrix powder is composed of Cr: 25 to 45 wt%, Al: 5 to 20 wt%, and the balance is substantially Ni alloy powder. In the second welding material, Ni ₃ Al having high hardness, which is an intermetallic compound of Ni and Al, is precipitated, which contributes to improvement of wear resistance.
In the matrix of the second welding material, Cr is an element effective for improving the corrosion resistance, particularly the oxidation resistance. However, if it is less than 25 wt%, this effect cannot be fully enjoyed. If it exceeds 50%, the toughness deteriorates and cracking is likely to occur during welding. Therefore, the Cr amount is 25 to 45 wt%. A desirable Cr amount is 28 to 42 wt%, and a more desirable Cr amount is 30 to 40 wt%.

  Al is also an element effective for improving the oxidation resistance like Cr, but if it is less than 5 wt%, this effect cannot be fully enjoyed. Conversely, if it exceeds 20 wt%, cracks occur during welding. It becomes easy to do. Therefore, the Al amount is 5 to 20 wt%. A desirable Al amount is 8 to 17 wt%, and a more desirable Al amount is 10 to 15 wt%.

The second welding material contains 25 to 35 wt% Cr ₃ C ₂ powder as a hard powder in addition to the above matrix powder. As described above, this hard powder has sufficient oxidation resistance even in the temperature range of 600 to 900 ° C.
The reason why the amount of Cr ₃ C ₂ powder is 25 to 35 wt% is that sufficient wear resistance cannot be obtained if it is less than 25 wt%, and cracking occurs during welding if it exceeds 35 wt%. . A desirable amount of Cr ₃ C ₂ powder is 27 to 33 wt%, and a more desirable amount of Cr ₃ C ₂ powder is 28 to 32 wt%.
In addition, also in the second welding material, addition of NbC and Cr ₃ B ₂ was examined in the same manner as in the first welding material, but cracking occurred during welding with the addition of about 1 wt%.

  In the second welding material, the particle size and manufacturing method of the matrix powder and the hard powder are the same as those of the first welding material, and are not particularly limited. The same applies to the presence state of the matrix powder and the hard powder before the powder plasma overlay welding.

The second high-temperature wear-resistant member obtained as described above has a coating layer formed on the surface of the base material with Cr: 25 to 45 wt%, Al: 5 to 20 wt%, and the balance being substantially Ni alloy powder. 25 to 35 wt% of Cr ₃ C ₂ particles are dispersed in a matrix made of The contents of the Ni alloy and Cr ₃ C ₂ particles constituting the matrix are as described above.
In the second high-temperature wear-resistant member, the material of the base material and specific examples of the wear-resistant member are the same as those of the first welding material.

Matrix powder (average particle size: 80 μm) and hard powder (average particle size: 100 μm) shown in Table 1 were blended and powder plasma overlay welding was performed on a SUS304 plate. The welding conditions are as follows. The presence or absence of cracks in the weld metal was visually confirmed after welding. The weld metal was then evaluated for high temperature wear resistance. In this evaluation, the maximum wear depth was measured after the silica sand No. 7 continued to collide with the weld metal for 20 hours at an angle of 30 ° and a speed of 30 m / s in an environment heated to 650 ° C.
The above results are also shown in Table 1. When Cr ₃ C ₂ powder, NbC powder and Cr ₃ B ₂ powder are within the scope of the present invention, excellent wear resistance is obtained without causing weld cracks. It turns out that the prepared weld metal is obtained.

Powder plasma overlay welding conditions Current: 140-160A
Welding speed: 90-100mm / min
Powder supply amount: 15-25 g / min
Wiving width: 8-12mm
Plasma gas: 1.5 to 2.0 L / min
Powder gas: 5L / min
Shielding gas: 1.0-2.0 L / min
Preheating temperature: 350-400 ° C

No. in Table 1 6 is a cross-sectional microstructure photograph of the weld metal in FIG. A cross-sectional microstructure photograph of the weld metal according to 10 is shown in FIG. As shown in FIGS. 1 and 2, precipitates are dispersed in the matrix. This precipitate was confirmed to contain Cr ₃ C ₂ particles, NbC particles, and Cr ₃ B ₂ particles (FIG. 2).

As shown in Table 2, the matrix powder and the hard powder were blended and powder plasma overlay welding was performed on the SUS304 plate. The welding conditions are the same as in Example 1. In addition, as in Example 1, the presence or absence of cracks in the weld metal was visually confirmed after welding, and the weld metal was evaluated for high-temperature wear resistance.
The above results are also shown in Table 2. When the Cr ₃ C ₂ powder is within the scope of the present invention, a weld metal having excellent wear resistance can be obtained without causing weld cracking. Recognize.

No. in Table 2 A cross-sectional microstructure photograph of the weld metal according to 14 is shown in FIG. As shown in FIG. 3, precipitates are dispersed in the matrix. This precipitate was confirmed to contain Cr ₃ C ₂ particles and NbC particles.

No. in Table 1 6 is a cross-sectional microstructure photograph of a weld metal according to 6; No. in Table 1 10 is a cross-sectional microstructure photograph of a weld metal according to FIG. No. in Table 2 14 is a cross-sectional microstructure photograph of a weld metal according to FIG.

Claims (8)

Including matrix powder and hard powder,
The matrix powder is composed of a γ ′ precipitation strengthened Ni-base superalloy,
The hard powder, the powder plasma welding material characterized in that it consists 25～35Wt% of Cr ₃ C ₂ powder and 5 to 10 wt% of NbC powder. The material for powder plasma welding according to claim 1, further comprising 5 to 10 wt% of Cr ₃ B ₂ powder as the hard powder.   The γ ′ precipitation strengthened Ni-base superalloy is Cr: 15-25 wt%, Mo: 5-10 wt%, Co: 10-15 wt%, W: 0.5-1 wt%, Al: 1-5 wt%, Ti The material for powder plasma welding according to claim 1, wherein the material consists essentially of Ni with a balance of 1 to 5 wt%. Including matrix powder and hard powder,
The matrix powder is Cr: 25 to 45 wt%, Al: 5 to 20 wt%, the balance being substantially Ni alloy powder,
The material for powder plasma welding, wherein the hard powder is composed of 25 to 35 wt% Cr ₃ C ₂ powder. A substrate;
A coating layer formed on the surface of the substrate;
The coating layer is characterized in that 25 to 35 wt% Cr ₃ C ₂ particles and 5 to 10 wt% NbC particles are dispersed in a matrix made of a γ ′ precipitation strengthened Ni-base superalloy. Wear member. The high-temperature wear-resistant member according to claim 5, wherein 5 to 10 wt% of Cr ₃ B ₂ particles are dispersed in the matrix.   The γ ′ precipitation strengthened Ni-base superalloy is Cr: 15-25 wt%, Mo: 5-10 wt%, Co: 10-15 wt%, W: 0.5-1 wt%, Al: 1-5 wt%, Ti The high-temperature wear-resistant member according to claim 5 or 6, wherein the high-temperature wear-resistant member consists of 1 to 5 wt% and the balance being substantially Ni. A substrate;
A coating layer formed on the surface of the substrate;
The coating layer is characterized in that Cr: 25 to 45 wt%, Al: 5 to 20 wt%, and 5 to 10 wt% of Cr ₃ C ₂ particles are dispersed in a matrix consisting essentially of a Ni alloy. High temperature wear resistant member.

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