JP2003117687A - FILLER METAL FOR Ni BASED HEAT RESISTANT SUPERALLOY, AND MELTING WELDING METHOD FOR Ni BASED HEAT RESISTANT SUPERALLOY - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a filler metal for an Ni based heat resistant superalloy (Inconel 738LC) which enables the formation of a weld zone having reduced crack sensitivity, and excellent high temperature strength. SOLUTION: The filler metal 1 at least contains C, Ti and Al. C is incorporated into the filler metal 1 by an amount larger than that in a base material 4 consisting of Inconel 738LC, and, Ti and Al are incorporated therein by amounts smaller than those in the base material 4. The content of C is, by weight, >0.13 to 0.30%, the content of Ti is 1.70 to <3.20%, and, the content of Al is 1.70 to <3.20%.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a filler metal for Ni-base heat-resistant superalloys and a method for melting and welding Ni-base heat-resistant superalloys.

[0002]

2. Description of the Related Art Ni-base heat-resistant superalloys are excellent in corrosion resistance, heat resistance and mechanical properties, and are used in high temperature equipment such as parts of various jet engines and gas turbine blades.
In recent years, demand has been particularly high. And generally N
The i-base heat-resistant superalloy is roughly classified into a solid solution strengthening type alloy and a precipitation strengthening type alloy.

Solid solution strengthened alloys include Co, Cr, Mo,
It is an alloy in which elements such as W and Al are added in large amounts as solid solution strengthening elements, and the main strengthening mechanism is solid solution strengthening by the additional elements obtained in the solution treatment state. Of these elements, Cr forms a dense protective film of Cr2O3, Al improves oxidation resistance by forming Al2O3 at high temperature, and bears the characteristics of a Ni-based heat-resistant superalloy that can withstand high temperatures in the atmosphere. There is.

On the other hand, the precipitation-strengthened alloy occupies most of the Ni-base heat-resistant superalloys, and the γ-phase (Ni
The γ'phase is finely precipitated in the solid solution), and as a result, it is strengthened. The most typical γ'phase in Ni-based heat-resistant superalloy is Ni3Al. Ni3Al has a face-centered cubic structure in which Ni is located at the face center of a cube and Al is located at each vertex. For this reason, there is an action of forming a matching relationship with a matrix having a similar crystal structure and strengthening it. This γ'phase was conventionally considered to be superior in high temperature strength as the precipitation rate was higher, but in recent years, γ '
It was found that the maximum creep strength was obtained when the phase volume ratio was about 65%. On the other hand, it is known that when a large amount of Ti or Nb is added, Ni3Al is replaced with Al. Further, the γ'phase undergoes cohesive coarsening at high temperature, so that the transition is easily moved and the strength of the alloy is reduced. However, this coarsening can be significantly delayed by the addition of Co, Mo, W, etc., and this reduction in strength can be prevented. It was also found that this Ni3Al has a unique property that its strength increases as the temperature rises.

[0005]

As described above, the Ni-base heat-resistant superalloy has the most excellent heat resistance among heat-resistant superalloys at the present time, and is a developing material with the potential for more excellent properties. Can be said. However, if the addition amount of the precipitation strengthening element is increased to obtain high strength, the forgeability deteriorates, and Al +
Most of Ni-based alloys having a high Ti content are used in the state of cast alloys. Further, the weldability decreases with the addition amount of the precipitation strengthening element. For example, if the Al + Ti content exceeds 6%, weld cracking is likely to occur, and it is a great practical problem that fusion welding is extremely difficult. Has become.

A problem of weldability in the Ni-base heat-resistant superalloy is hot cracking during welding. Typical hot cracks are solidification cracks that occur during the condensation process of molten metal and liquefaction cracks that occur in the weld heat affected zone. The mechanism of solidification cracking is generally considered as follows. At the beginning of the solidification process, the solid phase is dispersed in the liquid phase and can move freely with respect to each other.Therefore, at this stage, the openings caused by the addition of strain are compensated by the movement of the liquid phase, No cracks occur. Then, as the solidification progresses, some solid phases become linked, but the position of the liquid phase can still be moved, and even if an opening due to strain occurs, the liquid phase will crack. Cracking does not occur due to the phenomenon of filling, so-called healing. Next, at the final stage of coagulation, cooperation between solid phases progresses, and the liquid phase is isolated and separated. When a crack is generated in the solid-liquid coexisting portion due to the addition of strain in this state, the melt is no longer filled and solidification cracking occurs. It can be considered that the smaller the region where the melt is present in the final process of solidification, the more strain is concentrated in that region, and cracking is more likely to occur. Therefore, it is considered that the relationship between the solidification temperature of the residual melt and the solidification temperature of the matrix has a great influence on the solidification cracking susceptibility. That is, it can be said that the greater the difference between the solidification temperature of the final residual melt and that of the matrix, the easier the cracking occurs.

On the other hand, liquefaction cracks that occur in the heat-affected zone (HAZ) of the weld are caused by a low melting point compound or eutectic formation reaction at grain boundaries heated to a high temperature below the solidus temperature (Ts).
It is said that local dissolution occurs due to component segregation and the like, and a grain boundary is liquefied by the melt, so that contraction strain acts on the grain boundary to cause opening and generation. Hastelloy, a typical commercial material, is the cause of liquefaction cracking in Ni-based heat-resistant superalloys.
M6C for X, NbC for Inconel 625, Waspal
In oy, it seems to be due to local melting due to the presence of TiC on the grain boundaries.

Further, in the precipitation strengthened alloy, the eutectic of the γ phase and the γ'phase is the cause of liquefaction cracking. Furthermore, as the crystal grain size increases, the grain boundary area per unit volume decreases, resulting in an increase in the grain boundary area covered by the liquid film and an increase in crack susceptibility. As described above, liquefaction cracks have complicated factors such as alloy composition, segregation state, and crystal grain size.

By the way, in the arc welding method or the like using a filler metal, solidification cracking in the weld metal can be reduced by using a filler metal having an appropriate composition, and moreover, the work is easy and the production accompanied therewith. It is expected that it will be possible to reduce costs. However, the precipitation-strengthened Ni-based heat-resistant superalloy has a very high susceptibility to solidification cracking, and therefore has the drawback that a material having the same composition as the base metal cannot be used as a welding material (a filler metal). For this reason, at present, solidification cracking that occurs in the weld metal is prevented by using a welding material with good weldability at the expense of high temperature strength. In this case, the strength of the weld metal was low in the high temperature environment and the characteristics of the base metal could not be exhibited.

The present invention has been made in order to solve the above-mentioned conventional drawbacks, and an object thereof is to make it possible to reduce high temperature cracking susceptibility while ensuring high temperature strength.
Another object of the present invention is to provide a eutectic filler metal for an i-base heat-resistant superalloy. Another object of the invention is to provide a Ni-base heat-resistant superalloy capable of forming a weld having low solidification cracking sensitivity and excellent high-temperature strength. It is to provide a fusion welding method.

[0011]

Therefore, the filler metal for Ni-base heat-resistant superalloy according to claim 1 is at least C in weight ratio.
Over 0.13% and 0.30% or less, Cr 1
5.7% or more and 16.3% or less, Co, 8.00% or more and 9.00% or less, Ta, 1.50% or more, 2.0
0% or less, at least one of Mo and W, 1.5%
5.0% or less by the above, Ti is 3.7% by 3.20% or more.
It is characterized by containing 0% or less Al and 1.70% or more and less than 3.20%.

In the filler material for the Ni-base heat-resistant superalloy according to claim 1, the amount of C is larger than that of the material to be welded, for example, Inconel 738LC material. That is, by adding C in excess of 0.13%, the eutectic amount of Ti carbide and γ phase increases at the grain boundaries and dendrite boundaries, and along with this, the eutectic phase of γ phase and γ ′ phase. Can be reduced, and as a result, the solidification brittleness temperature region is reduced, whereby solidification cracking susceptibility can be suppressed. On the other hand, if added over 0.30%, the ductility is impaired, so the content is set to 0.
It was set to 13 to 0.30%. Further, since the Al content is 1.70% or more and less than 3.20% as compared with the material to be welded, for example, Inconel 738LC material, the amount of Al is reduced, so that the solidification cracking susceptibility may be reduced. it can. Cr is effective in improving oxidation resistance and corrosion resistance. This effect is not sufficient if it is less than 15.7%, and if it exceeds 16.3%, the balance with other added Co, Mo, W, Ta, etc. may be lost and a harmful phase may be precipitated. Therefore, the Cr content is set to 15.7 to 16.3%. Co has a function of increasing the limit (solid solution limit) of solid solution of γ ′ forming elements such as Al and Ti in the base material under a high temperature environment. This action is effective when it is 8.0% or more, and when it exceeds 9.0%, the balance with other elements such as Cr, Mo, W, Ta, Al and Ti is lost, and the ductility is lowered due to the precipitation of harmful phases. Therefore, the Co content is set to 8.0 to 9.0%. Ta contributes to the improvement of high temperature strength by solid solution strengthening and γ'phase precipitation strengthening, and is effective at 1.5% or more. However, if added in excess of 2.0%, ductility decreases, so the Ta content was made 1.5 to 2.0%. Mo and W have the effect of forming a solid solution in the matrix to increase the high-temperature strength, and at the same time have the effect of contributing to the high-temperature strength by precipitation strengthening, but if their content is less than 1.5%, it is insufficient. If added in excess of 5.0%, the ductility decreases due to the precipitation of harmful phases.
The content of Mo + W was set to 1.5 to 5.0%.

The filler metal for a Ni-base heat-resistant superalloy according to claim 2 has a weight ratio of at least C of more than 0.13% and 0.30% or less and Cr of 15.7% or more and 16%. .3%
Below, Co is 8.00% or more and 9.00% or less, Ta
1.50% or more and 2.00% or less, at least one of Mo and W, 1.5% or more and 5.0% or less, Ti
Is 1.70% or more and less than 3.20%, and Al is 3.2.
It is characterized by containing 0% or more and 3.70% or less.

In the filler metal for the Ni-base heat-resistant superalloy according to the above-mentioned claim 2, as in the Ni-base heat-resistant superalloy according to the above-mentioned claim 1, as compared with the material to be welded, for example, Inconel 738LC material, the C content is large. Therefore, the solidification cracking susceptibility is suppressed. Further, since the Ti content is smaller than that of the material to be welded, for example, Inconel 738LC material such that Ti is 1.70% or more and less than 3.20%, solidification cracking susceptibility can be reduced. .

A filler metal for a Ni-base heat-resistant superalloy according to claim 3 has a weight ratio of at least C of more than 0.13% and 0.30% or less, and Cr of 15.7% or more and 16% by weight. .3%
Below, Co is 8.00% or more and 9.00% or less, Ta
1.50% or more and 2.00% or less, at least one of Mo and W, 1.5% or more and 5.0% or less, Ti
Is 1.70% or more and less than 3.20%, and Al is 1.7.
It is characterized by containing 0% or more and less than 3.20%.

The filler metal for Ni-base heat-resistant superalloy according to claim 3 is similar to the filler metal for Ni-base heat-resistant superalloy according to claim 1 in comparison with the material to be welded, for example, Inconel 738LC material. , And C, the solidification cracking susceptibility is suppressed. Further, Ti is 1.70% or more and less than 3.20%, and Al is 1.70% or more and less than 3.20%. As compared with the welded material, for example, Inconel 738LC material, Ti and Since the amount of Al is reduced, solidification cracking susceptibility can be reduced.

The filler metal for a Ni-base heat-resistant superalloy according to claim 4 further comprises Zr of 0.03% or more and 0.08% or less, and B of 0.007% or more and 0.012% or less. It is characterized by including.

In the filler metal for Ni-base heat-resistant superalloy according to claim 4, since Zr and B are grain boundary strengthening elements, grain boundary strengthening can be achieved. Zr contributes to the strengthening of the base material by increasing the bonding force at the crystal grain boundaries and increases the high temperature strength. This effect is effective at 0.03% or more. However, if added in excess of 0.08%, ductility may be impaired, so the amount of Zr added was set to 0.03 to 0.08%. Similar to Zr, B contributes to the strengthening of the base material by increasing the bonding force at the crystal grain boundaries and increases the high temperature strength. This effect is effective at 0.007% or more. But 0.0
If added in excess of 12%, the ductility may be impaired, so the B content was made 0.007 to 0.012%.

The filler metal for the Ni-base heat-resistant superalloy according to claim 5 is such that the Ni-base heat-resistant superalloy, that is, the base material, has a weight ratio of at least C of 0.09% or more and 0.13% or less. , Cr, 15.7% or more and 16.3% or less, Co
Is 8.00% or more and 9.00% or less, and Ta is 1.5
0% or more and 2.00% or less, at least one of Mo and W, 1.5% or more and 5.0% or less, and Ti 3.2.
0% or more and 3.70% or less, Al is 3.20% or more and 3.70% or less, and Zr is 0.03% or more and 0.08%.
Hereinafter, B is characterized by being contained in an amount of 0.007% or more and 0.012% or less.

The filler metal for Ni-base heat-resistant superalloy according to the above-mentioned claim 5 is most suitable for carrying out the invention, and is capable of forming a welded portion which is excellent in high temperature strength while reducing solidification cracking susceptibility. You can do it.

According to the method of fusion welding of a Ni-base heat-resistant superalloy according to claim 6, C is contained in a larger amount than in the base metal, and Ti and A are added.
It is characterized in that a filler material containing at least one of 1 and 1 is contained in a smaller amount than the base material.

In the fusion welding method for the Ni-base heat-resistant superalloy according to claim 6, the eutectic phase of the γ phase and the γ'phase decreases with an increase in the C content, and the solidification embrittlement temperature range decreases. The solidification crack susceptibility in the welded part is suppressed. Further, the solidification crack susceptibility of the welded portion can be reduced by reducing the content of Ti or Al.

[0023]

BEST MODE FOR CARRYING OUT THE INVENTION Specific embodiments of the filler metal for Ni-base heat-resistant superalloy according to the present invention will be described in detail with reference to the drawings. FIG. 1 is a simplified diagram showing a fusion welding method for a Ni-base heat-resistant superalloy using a filler material 1 made of the Ni-base heat-resistant superalloy according to the present invention. That is, this welding method is, for example, a TIG welding method, and an arc is generated between the electrode 3 (for example, a tungsten electrode) and the base material 4 in an atmosphere of an inert gas (for example, argon gas) ejected from the gas nozzle 2. This is a welding method in which the base material 4 and the filler material 1 are melted.

In this case, as the base material 4, for example, Inco
nel738LC material is used. This Inconel 738LC material has the chemical composition shown in Table 1. As the filler material 1, a common metal filler material based on Inconel 738LC material is used. In addition, all component contents in the following description are shown by weight ratio%.

[0025]

[Table 1]

By the way, in Ni-based heat-resistant superalloys, T
When the contents of i and Al are increased, the high temperature strength thereof is increased, but since there are many eutectic phases of the γ phase and the γ ′ phase, high temperature cracking easily occurs. Further, if the content (addition amount) of C is increased, the crystallization amount of the eutectic phase of Ti carbide and γ phase on the dendrite boundary is increased, and accordingly, the eutectic phase of γ phase and γ ′ phase is increased. The phase can be reduced. Therefore, if the increase of the content of C is increased, Ti
However, the eutectic phase of the γ phase and the γ ′ phase decreases, the solidification brittle temperature range decreases, and the solidification cracking susceptibility is suppressed. in this way,
It is necessary to determine the chemical composition of the filler metal 1 in consideration of evaluations such as high temperature strength, high temperature ductility, and solidification crack susceptibility.

Therefore, in this embodiment, the filler material 1
As an example, when using a common metal-based filler material based on Inconel 738LC material, the content of C, Ti, and Al components is adjusted. That is, a material containing more C than the base material 4 and less Ti and Al than the base material 4 is used. Specifically, in terms of weight ratio, C is more than 0.13% and 0.30% or less, Ti is 1.70% or more and less than 3.20%, and Al is 1. It was set to be 70% or more and less than 3.20%. In this case, at least one of Ti and Al may have the above content. That is, Ti is 1.70.
% And less than 3.20%, Al may not be 1.70% or more and less than 3.20%, and conversely, Al is 1.70%.
% Or more and less than 3.20%, Ti does not have to be 1.70% or more and less than 3.20%, and Ti is 1.7.
It is 0% or more and less than 3.20%, and Al is 1.70.
% Or more and less than 3.20% may be used.

The content of C is determined as described above because it is C
Is less than 0.13%, the solidification embrittlement temperature range is large as in the case of the Ni-based heat-resistant superalloy (Inconel 738LC material) in Table 1, so the solidification cracking susceptibility is not reduced, and conversely, C
Is more than 0.30%, more carbides are precipitated,
This is because the ductility decreases. Further, the content of Ti and Al is determined as described above, when Ti is less than 1.70% or Al is less than 1.70%,
If sufficient high temperature strength cannot be obtained and conversely Ti is 3.20% or more or Al is 3.20% or more, N in Table 1
This is because, like the i-based heat-resistant superalloy, high temperature cracking susceptibility is increased.

Further, in this filler material 1, as in the case of the Ni-base heat-resistant superalloy shown in Table 1, Cr is contained in a weight ratio of 15.7 to 1: 1.
6.3%, Mo 1.50 to 2.00%, Co 8.0
0-9.00%, W by 2.40-2.80% each, Ta by 1.50-2.00%, Zr by 0.03-
0.08% and 0.007 to 0.012% of B are included. This is because Cr, Mo, Co, and W are solid solution strengthening elements, and therefore solid solution strengthening can be achieved to improve high-temperature strength. Ta, Zr, and B are grain boundary strengthening elements. This is because grain boundary strengthening can be achieved.
Since Mo and W have similar properties, Mo + W may be 1.5 to 5.0%.

When welding is performed using the filler material 1 having the above chemical composition, solidification cracking can be suppressed while suppressing the occurrence of solidification cracking.
In the high temperature environment, the strength of the weld metal is not deteriorated, and the base material 4 can sufficiently exhibit its characteristics (corrosion resistance, heat resistance, etc.). Therefore, the high temperature strength is improved as compared with the case where a welding material having a low high temperature strength such as Inconel 625 is used, which leads to an improvement in the reliability of the welded portion.
Therefore, conventionally, the repair work of the welded portion has been frequently performed, but the number of repair work can be significantly reduced, which contributes to cost reduction.

Although the specific embodiments of the present invention have been described above, the present invention is not limited to the above-described embodiments, and various modifications can be carried out within the scope of the present invention. For example, Si, Mn, P, S, Cu, F, etc. may be contained. In this case, Si is 0.3% or less, Mn is 0.2% or less, P is 0.01% or less, S is 0.01% or less, Cu is 0.10% or less, and F is 0.50.
The content is preferably not more than%. Further, the welding method is not limited to the TIG welding method, and may be another fusion welding method such as laser welding.

[0032]

EXAMPLE Next, a sample having the chemical composition shown in Table 2 was produced,
A tensile test (test temperature: 850 ° C.) and a trans-barless train test were performed. In the test, for the sake of simplification, various materials are not used as the filler,
Used as a base material. In Table 2, the conventional example is the Inconel 738LC material itself having the chemical components shown in Table 1 above, and in Comparative Examples 1 to 3, the C content is Inconel 7
Comparative Example 4 is A.
The contents of 1 and Ti are set to the same level as the Inconel 738LC material. In addition, Comparative Examples 1 to 4 and Example 1
In Example 6, Cr is 15.7 to 1 as in the conventional example.
6.3%, Mo 1.50 to 2.00%, Co 8.0
0-9.00%, W 2.40-2.80%, Ta 1.50-2.00%, Zr 0.03-0.08%,
B is contained in the range of 0.007 to 0.012%. Furthermore, Si is 0.3% or less, Mn is 0.2% or less, P is 0.01% or less, S is 0.01% or less, Cu is 0.10% or less, and F is 0.50% or less. It remains due to its content.

[0033]

[Table 2]

The Transvarestrain test is
A test piece 9 as shown in FIG. 2 is formed, and tensile strain is applied to the test piece 9 by the test device 6 shown in FIG. 3 to cause hot cracking in the weld metal. That is, the test piece 9 has a long side length X of 100 mm and a short side length Y of 50 mm.
It is a plate-like body having a thickness t of 5 mm and a thickness t of 5 mm. Bead-on-plate welding by TIG arc is performed on the central portion of the plate-like body, and a welded portion 15 (having a length of about 45 mm and a width of about 10 mm is provided along the center line L). And) to form. Further, the test apparatus 6 includes a block body 7 on which the test piece 9 is placed, and a test piece 9
And a yoke 8 for applying a load to the ends of the. In this case, as shown in FIG. 2, the block body 7 has a short side length X1 of 30 mm and a long side length Y1 of 110 mm. In the case of setting, when the test piece 9 is placed on the block body 7 in a plan view, the center points of the test piece 9 and the block body 7 are arranged to be orthogonal to each other. To do. Therefore, the short sides 10 and 10 of the test piece 9 project from the long sides 11 and 11 of the block body 7, and the projection amount A is 35 mm. Then, the following Table 3 shows welding conditions. In addition, in FIG. 2, the arrow shows the welding direction.

[0035]

[Table 3]

In this case, the load applied by the yokes 8, 8 is such that the arcs are extinguished and the yokes 8, 8 at both ends of the test piece 9 are simultaneously formed.
By dropping. That is, tensile strain is applied to the upper surface of the test piece 9 to cause hot cracking in the welded portion 15, and when the yokes 8 fall, arcs are automatically extinguished by the switches provided on the yokes 8. It was set to arc. The amount of added strain was 0.4%. After the test was completed, the cracks were observed using an optical microscope, and the crack susceptibility based on the maximum crack length and the total crack length was quantitatively evaluated. The results are shown in Table 2 above.
The maximum crack length is the maximum length of each cracked test piece 9 and the total crack length is the total length of each cracked test piece 9.

Examining the results, although the conventional examples and the comparative examples 1 to 3 all have a small amount of C, they all have high high temperature strength, but the total crack length becomes remarkably long. It is clear that the solidification cracking has a high susceptibility. When the amount of C is small, the solidification cracking susceptibility is improved even if the amount of Al is reduced (Comparative Example 1), the amount of Ti is reduced (Comparative Example 2), and both are reduced (Comparative Example 3). I can't see it. Further, even if the amount of C is large, if the amounts of Al and Ti are large (Comparative Example 4), no improvement in susceptibility to solidification cracking is observed. On the other hand, in Examples 1 to 6, the maximum crack length and the total crack length can be suppressed sufficiently lower than those in the conventional example, and it is understood that the hot crack sensitivity is reduced. Considering the tensile test, the maximum crack length evaluation, and the total crack length evaluation, it can be seen that Examples 1, 2, and 5 are particularly excellent. Further, in Comparative Examples 1 and 4, both the maximum crack length and the total crack length are inferior to any of the Examples. As is clear from Example 6, Ti and Al
When the amount is small, the high temperature strength is lowered, so that the Ti and Al amounts must be 1.70% or more.
Thus, C is set in the range of more than 0.13% and not more than 0.30%, and Ti is not less than 1.70% and not more than 3.2.
Range of less than 0%, or 1.70% or more of Al and 3.20
By setting the component so that it is in the range of less than%,
It is possible to reduce high temperature cracking susceptibility while ensuring high temperature strength. From these results, C is 0.
About 27%, Al about 2.8 to 3.0%, Ti about 2.
It is understood that the content is preferably about 0%.

[0038]

According to the filler metal for the Ni-base heat-resistant superalloy according to claims 1 to 3, the susceptibility to solidification cracking can be suppressed. Therefore, while suppressing the occurrence of hot cracking, the conventional High-temperature strength is improved compared to other types of materials, the reliability of the welded part is improved, the number of repairs of the welded part can be reduced, and the cost can be reduced.

According to the filler metal for a Ni-base heat-resistant superalloy according to claim 4, grain boundary strengthening can be achieved, high temperature strength can be improved, and a high quality welded portion can be formed.

The filler metal for a Ni-base heat-resistant superalloy according to claim 5 is most suitable for carrying out the invention, and it is possible to form a welded portion having low hot cracking susceptibility and excellent high temperature strength.

According to the fusion welding method for a Ni-base heat-resistant superalloy according to claim 6, as the content of C increases, the solidification cracking susceptibility in the weld zone is suppressed and the content of Ti or Al is reduced. As a result, the hot crack susceptibility of the weld can be reduced. Moreover, the strength of the weld metal can be improved in a high temperature environment, and the characteristics of the base metal can be sufficiently exhibited. Therefore, the reliability of the welded portion is improved, the number of repairs of the welded portion can be reduced, and the cost can be reduced.

[Brief description of drawings]

FIG. 1 is a simplified diagram showing an embodiment of a fusion welding method of the present invention.

FIG. 2 is a plan view showing a test piece for performing a transformer / Valestrain test on a filler metal for a Ni-base heat-resistant superalloy according to the present invention.

FIG. 3 is a simplified diagram showing a test apparatus for performing the transformer / Ballestrain test.

[Explanation of symbols]

1 filler material 4 base material

Front page continuation (51) Int.Cl. ⁷ identification code FI theme code (reference) F02C 7/00 F02C 7/00 D // B23K 103: 08 B23K 103: 08 (72) Inventor Masahiko Toyota Takasago City, Hyogo Prefecture 2-1-1 Niihama, Arai-machi, Takasago Laboratory, Mitsubishi Heavy Industries Ltd. (72) Inventor Masahiko Tsumaka 2-1-1, Niihama, Arai-machi, Takasago, Hyogo Prefecture (72) In-house Takasago Laboratory, Mitsubishi Heavy Industries, Ltd. (72) Koji Takahashi Takasago, Hyogo Prefecture 2-1-1, Niihama, Arai-cho, Mitsubishi Heavy Industries, Ltd. (72) Inventor Koji Tsukimoto 2-1-1, Niihama, Arai-machi, Takasago, Hyogo Prefecture (72) In-house, Takasago, Mitsubishi Heavy Industries (72) Yoshiko Uemura Hyogo 2-1-1 Niihama, Arai-machi, Takasago-shi, Fukushima Mitsubishi Heavy Industries, Ltd. Takasago Plant F-term (reference) 3G002 EA06 4E001 AA03 CB03 EA05

Claims (6)

[Claims] 1. In a weight ratio, at least C is more than 0.13% and 0.30% or less, Cr is 15.7% or more and 16.3% or less, and Co is 8.00% or more. 9.00% or less, Ta is 1.50% or more and 2.00% or less, and at least one of Mo and W is 1.5% or more and 5.
0% or less, Ti content of 3.20% or more and 3.70% or less, and Al content of 1.70% or more and less than 3.20%. Material. 2. In a weight ratio, at least C is more than 0.13% and 0.30% or less, Cr is 15.7% or more and 16.3% or less, and Co is 8.00% or more. 9.00% or less, Ta is 1.50% or more and 2.00% or less, and at least one of Mo and W is 1.5% or more and 5.
0% or less, Ti content of 1.70% or more and less than 3.20%, Al content of 3.20% or more and 3.70% or less. Material. 3. In a weight ratio, at least C is more than 0.13% and 0.30% or less, Cr is 15.7% or more and 16.3% or less, and Co is 8.00% or more. 9.00% or less, Ta is 1.50% or more and 2.00% or less, and at least one of Mo and W is 1.5% or more and 5.
0% or less, Ti containing 1.70% or more and less than 3.20%, Al containing 1.70% or more and less than 3.20%, and a filler metal for Ni-based heat-resistant superalloy. Material. 4. Further, Zr is 0.03% or more and 0.
The filler metal for a Ni-base heat-resistant superalloy according to any one of claims 1 to 3, characterized in that it contains 0.008% or less and B in an amount of 0.007% or more and 0.012% or less. 5. The Ni-based heat-resistant superalloy in a weight ratio,
At least C is 0.09% or more and 0.13% or less, Cr is 15.7% or more and 16.3% or less, Co is 8.00% or more and 9.00% or less, and Ta is 1 0.5% or more and 2.00% or less, Mo and / or W at 1.5% or more and 5.
0% or less, Ti is 3.20% or more and 3.70% or less, Al is 3.20% or more and 3.70% or less, Zr is 0.03% or more and 0.08% or less, B Is contained in an amount of 0.007% or more and 0.012% or less, the filler metal for a Ni-base heat-resistant superalloy according to any one of claims 1 to 4. 6. A filler material (1) containing C in a larger amount than the base material (4) and at least one of Ti and Al in a smaller amount than the base material. A fusion welding method for a Ni-base heat-resistant superalloy.