High-temperature piping product and method for producing same

Abstract

A high-temperature piping product is configured from a plurality of primary pipe members and a welding material. The primary pipe members are each made from an Ni-based forged alloy containing: Ni, Al, and at least one of Mo and W. The total content of the Mo and the W being 3-8 mass %. The Ni-based forged alloy exhibiting a -phase dissolution temperature of from 920 to 970 C., and the phase being precipitated in 30 volume % or more in a temperature range of from 700 to 800 C. The welding material is made from an Ni-based cast alloy having a cast structure formed by welding. The Ni-based cast alloy containing: Ni, Al, and at least one of Mo and W, the total content of the Mo and the W being 9-15 mass %, the Ni-based cast alloy exhibiting a -phase dissolution temperature of from 850 to 900 C.

Claims

1. A high-temperature piping product for flowing a high-temperature fluid, configured from a plurality of primary pipe members and a welding material, wherein the primary pipe members are each made from an Ni-based forged alloy which contains Ni, Al, and at least one of Mo and W, the total content of the Mo and the W being 3 mass % or more and 8 mass % or less, and the Ni-based forged alloy having a phase precipitated therein in 30 volume % or more in which the precipitated phase has a -phase dissolution temperature of from 920 to 970 C. and a precipitation characteristic of 30 volume % or more in a temperature range of from 700 to 800 C., wherein the welding material is made from an Ni-based cast alloy having a cast structure formed by welding, the Ni-based cast alloy containing Ni, Al, and at least one of Mo and W, the total content of the Mo and the W being 9 mass % or more and 15 mass % or less, and the Ni-based cast alloy having another phase precipitated therein in 20 volume % or more in which the another precipitated phase has a -phase dissolution temperature of from 850 to 900 C. and a precipitation characteristic of 20 volume % or more in a temperature range of from 700 and 800 C., and wherein the welding material is buttered to the primary pipe members in portions welded to each other.

2. A boiler for power plants, the boiler comprising the high-temperature piping product according to claim 1.

3. The high-temperature piping product according to claim 1, wherein the Ni-based forged alloy contains: Al of 3.5 mass % or more and 4.5 mass % or less; Cr of 15 mass % or more and 20 mass % or less; Co of 25 mass % or less; C of 0.01 mass % or more and 0.15 mass % or less; at least one of Mo and W in a total content of 3 mass % to 8 mass %; and Ni and unavoidable impurities accounting for the remainder, and wherein the Ni-based cast alloy contains: Al of 3 mass % or more and 3.5 mass % or less; Cr of 15 mass % or more and 20 mass % or less; Co of 25 mass % or less; C of 0.01 mass % or more and 0.15 mass % or less; at least one of Mo and W in a total content of 9 mass % to 15 mass %; and Ni and unavoidable impurities accounting for the remainder.

4. A boiler for power plants, the boiler comprising the high-temperature piping product according to claim 3.

5. A method for producing the high-temperature piping product according to claim 1, the method comprising: a secondary pipe member forming step of welding the primary pipe members to each other with the welding material buttered to welding portions of the primary pipe members and forming secondary pipe members each constructed from the plurality of primary pipe members; and a high-temperature piping product forming step of welding the secondary pipe members to each other with the welding material buttered to welding portions of the secondary pipe members and forming a high-temperature piping product.

6. The method according to claim 5, further comprising a pre-aging heat treatment step of subjecting the secondary pipe members to a heat treatment at a temperature equal to or greater than the -phase dissolution temperature of the Ni-based cast alloy and at a temperature equal to or less than the -phase dissolution temperature of the Ni-based forged alloy to precipitate 5 volume % or more and 15 volume % or less of the phase in the primary pipe members, the pre-aging heat treatment step being performed after the secondary pipe member forming step and before the high-temperature piping product forming step.

7. A method for producing the high-temperature piping product according to claim 3, the method comprising: a secondary pipe member forming step of welding the primary pipe members to each other with the welding material buttered to welding portions of the primary pipe members and forming secondary pipe members each constructed from the plurality of primary pipe members; and a high-temperature piping product forming step of welding the secondary pipe members to each other with the welding material buttered to welding portions of the secondary pipe members and forming a high-temperature piping product.

8. The method according to claim 7, further comprising a pre-aging heat treatment step of subjecting the secondary pipe members to a heat treatment at a temperature equal to or greater than a -phase dissolution temperature of the Ni-based cast alloy and at a temperature equal to or less than a -phase dissolution temperature of the Ni-based forged alloy to precipitate 5 volume % or more and 15 volume % or less of the phase in the primary pipe members, the pre-aging heat treatment step being performed after the secondary pipe member forming step and before the high-temperature piping product forming step.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

(1) FIG. 1 is a schematic view representing an exemplary procedure of producing a high-temperature piping product according to an embodiment of the present invention.

(2) FIG. 2 is a schematic view showing microstructures of weld joints of Samples 1 to 6.

(3) FIG. 3 is a schematic view showing microstructures of weld joints of Samples 7 to 9.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS

(4) An embodiment of the present invention will be described below. However, the present invention is not limited to the specific embodiments described below, but various combinations and modifications are possible without departing from the spirit and scope of the invention.

(5) (High-Temperature Piping Product)

(6) As described above, the high-temperature piping product according to an embodiment of the present invention is a structure formed by welding and assembling relatively short primary pipe members with a welding material. And the Ni-based forged alloy forming the primary pipe member, and the Ni-based cast alloy forming the welding material have different -phase dissolution temperatures (-phase dissolution temperature of the Ni-based forged alloy>-phase dissolution temperature of the Ni-based cast alloy). The welding portions of the primary pipe members represent a weld joint buttered with the welding material.

(7) In order to ensure desirable weldability and desirable tolerable temperature of the 800 C. class (sufficient mechanical strength in this temperature range), the primary pipe member is preferably made from an Ni-based forged alloy that exhibits a phase (Ni.sub.3Al phase) dissolution temperature of from 920 to 970 C., and in which 30 volume % or more and 40 volume % or less (30-40 volume %) of the phase is dispersed and precipitated in a temperature range of from 700 to 800 C. A sufficient tolerable temperature cannot be obtained when the amount of the phase dispersed and precipitated in the 700 to 800 C. temperature range is less than 30 volume %, and the ductility degrades greatly when the amount of the dispersed and precipitated phase is above 40 volume %.

(8) Furthermore, when the -phase dissolution temperature of the Ni-based forged alloy is less than 920 C., it becomes difficult to obtain the high-temperature piping product exhibiting a tolerable temperature of the 800 C. class by means of the producing method according to an embodiment of the present invention (details will be described later). With a -phase dissolution temperature in excess of 970 C., the weldability of the primary pipe member degrades, and the hot workability suffers (the ductility degrades), making it difficult to produce the pipe member itself.

(9) Preferably, the Ni-based forged alloy has a composition containing: Al of 3.5 mass % or more and 4.5 mass % or less (3.5-4.5 mass %); Cr of 15 mass % or more and 20 mass % or less (15-20 mass %); Co of 25 mass % or less; C of 0.01 mass % or more and 0.15 mass % or less (0.01-0.15 mass %); at least one of Mo and W in a total content of 3 mass % to 8 mass %; and Ni and unavoidable impurities accounting for the remainder.

(10) The Mo component and the W component are constituent elements that have strong effects on the precipitation amount and the dissolution temperature of the phase, and on the hot workability of the Ni-based alloy. A sufficient tolerable temperature cannot be obtained when the total content of the Mo component and the W component is less than 3 mass %. Above 8 mass %, the hot workability suffers (the ductility degrades), making it difficult to produce the pipe member itself.

(11) The Al component is an essential component for forming the phase. With an Al component content less than 3.5 mass %, the -phase precipitation amount becomes deficient, and a sufficient tolerable temperature cannot be obtained. Above 4.5 mass %, the hot workability suffers (the ductility degrades), making it difficult to produce the pipe member itself.

(12) The Cr component dissolves in the matrix, and has the effect of improving the oxidation resistance of the Ni-based alloy. This effect is hardly obtained when the content of the Cr component is less than 15 mass %. Above 20 mass %, a harmful phase is prone to precipitate, and the ductility degrades, making it difficult to produce the pipe member itself.

(13) The Co component dissolves in the matrix, and has the effect of improving the high-temperature mechanical strength by formation of a solid solution. However, the Co component is added in preferably 25 mass % or less, because it also acts to stabilize the harmful phase.

(14) The C component has the effect of preventing the excess coarsening of the Ni-based alloy crystal grains through formation of carbides. This effect is hardly obtained when the content of the C component is less than 0.01 mass %. Above 0.15 mass %, the hot workability suffers (the ductility degrades), making it difficult to produce the pipe member itself. For improved weldability, the content of the C component is preferably 0.01 mass % to 0.05 mass %.

(15) On the other hand, the welding material differs from the primary pipe member in that it is used in the state of a solidification structure, and that it is not subjected to plastic forming (for example, not processed into a tubular shape). Preferably, the welding material is made from an Ni-based cast alloy that exhibits a phase (Ni.sub.3Al phase) dissolution temperature of from 850 to 900 C., and in which 20 volume % or more and 30 volume % or less (20-30 volume %) of the phase is dispersed and precipitated in a temperature range of from 700 to 800 C. A sufficient tolerable temperature cannot be obtained when the amount of the phase dispersed and precipitated in the 700 to 800 C. temperature range is less than 20 volume %. Above 30 volume %, weld cracking is prone to occur.

(16) Furthermore, when the -phase dissolution temperature of the Ni-based cast alloy is less than 850 C., it becomes difficult to obtain the high-temperature piping product exhibiting a tolerable temperature of the 800 C. class by means of the producing method according to an embodiment of the present invention (details will be described later). With a -phase dissolution temperature in excess of 900 C., the buttering weldability degrades.

(17) Preferably, the Ni-based cast alloy has a composition that contains: Al of 3 mass % or more and 3.5 mass % or less (3-3.5 mass %); Cr of 15 mass % or more and 20 mass % or less (15-20 mass %); Co of 25 mass % or less; C of 0.01 mass % or more and 0.15 mass % or less (0.01-0.15 mass %); at least one of Mo and W in a total content of 9 mass % to 15 mass %; and Ni and unavoidable impurities accounting for the remainder.

(18) As described above, the Mo component and the W component are constituent elements that have strong effects on the precipitation amount and the dissolution temperature of the phase, and on the hot workability of the Ni-based alloy. However, because the welding material does not require plastic forming, the Mo component and the W component can be added in larger amounts than in the primary pipe member to ensure high mechanical strength at high-temperatures. A sufficient high-temperature mechanical strength cannot be obtained when the total content of the Mo component and the W component is less than 9 mass %. Above 15 mass %, the ductility, and the processibility of a weld wire suffer.

(19) The content of the Al component in the Ni-based cast alloy for the welding material ranges from 3 to 3.5 mass %. The mechanical strength becomes insufficient when the Al component content is below 3 mass %. Above 3.5 mass %, the wire processibility and weldability become insufficient. The Cr component, the Co component, and the C component are same as in the primary pipe member.

(20) Desirably, the Ni-based forged alloy and the Ni-based cast alloy used in the present invention do not contain a Ti (titanium) component, a Ta (tantalum) component, and an Nb (niobium) component. In other words, these components are not intentionally added. When mixed unintentionally, the total content of the Ti component, the Ta component, and the Nb component is preferably 0.5 mass % or less.

(21) Ti, Ta, and Nb have the characteristics of more strongly stabilizing the phase at temperatures of 1,000 C. and higher, compared to Al. However, the effect of stabilizing the phase is weaker than that of Al at operating temperatures (700 to 800 C.). It is difficult to obtain desirable hot workability and desirable weldability of the Ni-based alloy when the phase is stable at temperatures of 1,000 C. and higher. It is therefore more preferable to stabilize the phase with Al alone, without adding Ti, Ta, and Nb, in order to realize good hot workability and weldability at the same time as the mechanical strength at operating temperatures.

(22) (Method for Producing High-Temperature Piping Product)

(23) The method for producing a high-temperature piping product according to an embodiment of the present invention will be described below. First, the primary pipe member of the Ni-based forged alloy, and the welding material of the Ni-based cast alloy are prepared. The primary pipe member is subjected to a heat treatment (solution heat treatment) at a temperature equal to or greater than the -phase dissolution temperature to dissolve the phase in the matrix.

(24) FIG. 1 is a schematic view representing an exemplary procedure of producing the high-temperature piping product according to the embodiment of the present invention. As shown in FIG. 1, the primary pipe members are welded to each other with the welding material buttered to the welding portions of the primary pipe members to form a secondary pipe member constructed from the plurality of primary pipe members (this step is referred to as secondary pipe member forming step).

(25) The secondary pipe member is then subjected to a heat treatment at a temperature equal to or greater than the -phase dissolution temperature of the Ni-based cast alloy of the welding material and a temperature equal to or less than the -phase dissolution temperature of the Ni-based forged alloy of the primary pipe member (specifically, at a temperature of, for example, above 900 C. and below 920 C.) to precipitate 5 volume % or more and 15 volume % or less (for example, 10 volume %) of the phase in the primary pipe members (this step is referred to as pre-aging heat treatment step).

(26) Prior to the pre-aging heat treatment step, the welding material may be buttered to the welding portions of the secondary pipe members (see FIG. 1). Precipitation of the phase in the primary pipe member lowers the weldability of the primary pipe member itself. However, because the aging heat treatment temperature is equal to or greater than the -phase dissolution temperature of the buttered welding material, the phase does not precipitate in the welding material. This provides desirable weldability for the next step.

(27) Thereafter, the welding material is buttered to the welding portions of the secondary pipe members to weld the secondary pipe members to each other and form a high-temperature piping product (this step is referred to as high-temperature piping product forming step). As described above, the welding material may be buttered to the welding portions of the secondary pipe members before or after the pre-aging heat treatment step.

(28) The high-temperature piping product obtained after the high-temperature piping product forming step is directly used for the assembly of the actual product (for example, a boiler for power plants of the 800 C. class). The phase evenly disperses and precipitates in 30 volume % or more in the primary pipe members as a high-temperature fluid of the 800 C. class is flown during the operation of the power plant, and high mechanical strength at high-temperatures can be ensured. In other words, in the producing method according to the embodiment of the present invention, the high-temperature piping product forming step is not followed by the aging heat treatment performed to precipitate 30 volume % or more of the phase in the primary pipe members under the external heat applied to the whole high-temperature piping product.

Examples

(29) The present invention will be described in more detail below by way of Examples. It should be noted, however, that the present invention is not limited by the specific Examples below.

(30) (Preparation of Primary Pipe Member and Welding Material)

(31) Ni-based alloys (Alloys T1 to T5) of the compositions presented in Table 1 were prepared, and specimens of the primary pipe members were produced according to the following procedures. First, an Ni-based alloy ingot was produced by vacuum melting and vacuum arc remelting (double melting process). The Ni-based alloy ingot was subjected to hot forging to produce a billet. Then, hot extrusion and cold working were performed for the billet to produce a primary pipe member (inner diameter of 50 mm; thickness of 8 mm) that simulates a boiler tube for power plants. The resulting primary pipe members (Alloys T1 to T5) were examined with respect to the -phase dissolution temperature, and the -phase precipitation amount in the aging heat treatment (800 C.). The results are presented in Table 1. Alloys T1 and T2 are conventional Ni-based alloys, and Alloys T3 to T5 represent the Ni-based alloys according to the present invention.

(32) TABLE-US-00001 TABLE 1 Compositions of Ni-based alloys for primary pipe member Alloy T1 Alloy T2 Alloy T3 Alloy T4 Alloy T5 Al 1.9 5.4 4.0 4.2 3.7 Cr 23.2 8.3 15 16 17 Co 18.7 9.2 24 15 0 C 0.14 0.08 0.01 0.03 0.05 Mo 0.49 4.0 0.1 W 2.1 9.4 6.0 3.0 8.0 Ti 3.8 0.8 Ta 1.38 3.19 Nb 1.0 -phase 930 C. 940 C. 930 C. 945 C. 915 C. dissolution temperature -phase 20% 18% 33% 35% 30% precipitation amount

(33) Ni-based alloys (Alloys W1 to W5) of the compositions presented in Table 2 were prepared, and specimens of the welding materials were produced according to the following procedures. First, an Ni-based alloy ingot was produced by vacuum melting. The Ni-based alloy ingot was then subjected to hot forging and cold drawing to produce a welding material (a weld wire with an outer diameter of 1 mm). The resulting welding materials (Alloys W1 to W5) were examined with respect to the -phase dissolution temperature, and the -phase precipitation amount in the aging heat treatment (800 C.). The results are presented in Table 2. Alloys W1 and W2 are conventional Ni-based alloys, and Alloys W3 to W5 represent the Ni-based alloys according to the present invention.

(34) TABLE-US-00002 TABLE 2 Compositions of Ni-based alloys for welding material Alloy W1 Alloy W2 Alloy W3 Alloy W4 Alloy W5 Al 1.9 5.4 3.1 3.3 3.5 Cr 23.2 8.3 15 16 17 Co 18.7 9.2 24 15 0 C 0.14 0.08 0.01 0.03 0.05 Mo 0.49 8.0 10 9.0 W 2.1 9.4 6.0 3.0 8.0 Ti 3.8 0.8 Ta 1.38 3.19 Nb 1.0 -phase 930 C. 940 C. 860 C. 870 C. 880 C. dissolution temperature -phase 20% 18% 20% 20% 22% precipitation amount
(Production of Weld Joint, and Testing and Evaluation of Weld Joint) The primary pipe members and the welding materials prepared as above were used in a TIG (tungsten inert gas) welding performed in the combinations and conditions presented in Tables 3 and 4 to produce weld joints (Samples 1 to 9) as the secondary pipe members. The weld joints (Samples 1 to 9) were then subjected to microstructure observation of a sample cross section (including an evaluation of the presence or absence of weld cracking), and a creep test. The microstructure observation was also performed to unwelded samples and to samples taken out in the middle of the creep test (creep test suspended specimens). The creep test was conducted at a temperature of 800 C. under 190 MPa stress. The result of the creep test was used for the evaluation of a creep tolerable temperature according to the Larson-Miller method (Larson-Miller parameter=20). The creep tolerable temperature is the temperature at which the product can withstand a 100-MPa stress for 100,000 hours. The evaluation results for the presence or absence of weld cracking, and the creep tolerable temperature are presented in Tables 3 and 4.

(35) TABLE-US-00003 TABLE 3 Specifications of weld joints of Samples 1 to 6 and testing and evaluation results Sample Sample Sample Sample Sample Sample 1 2 3 4 5 6 Primary pipe Alloy Alloy Alloy Alloy Alloy Alloy member T2 T1 T2 T1 T3 T5 Welding Alloy Alloy Alloy Alloy Alloy Alloy material W2 W1 W2 W2 W5 W3 Buttering material Solution heat 1,160 C. 2 h 1,160 C. 2 h 1,160 C. 2 h treatment Pre-aging heat 800 C. 16 h treatment Weld cracking Present Present Absent Absent Absent Absent Creep tolerable 733 C. 728 C. 742 C. 738 C. 770 C. 772 C. temperature

(36) TABLE-US-00004 TABLE 4 Specifications of weld joints of Samples 7 to 9 and testing and evaluation results Sample 7 Sample 8 Sample 9 Primary pipe member Alloy T3 Alloy T4 Alloy T5 Welding material Alloy W5 Alloy W3 Alloy W4 Buttering material Alloy W5 Alloy W3 Alloy W4 Solution heat treatment 1,160 C. 2 h 1,000 C. 2 h Pre-aging heat treatment 900 C. 16 h Weld cracking Absent Absent Absent Creep tolerable temperature 805 C. 802 C. 800 C.

(37) The results of the microstructure observation are shown in FIGS. 2 and 3. FIG. 2 is a schematic view showing microstructures of weld joints of Samples 1 to 6. FIG. 3 is a schematic view showing microstructures of weld joints of Samples 7 to 9. These results are explained below with reference to Tables 3 and 4, and FIGS. 2 and 3.

(38) The weld joints of Samples 1 and 2 were obtained from the conventional Ni-based alloys after the pre-aging heat treatment (800 C.16 hours) performed before welding. Buttering was not performed. The phase already precipitated in the unwelded samples (labeled as before welding), and the same structure was observed also in samples examined immediately after the welding (labeled as as-welded), and in the creep test suspended specimens (labeled as during creep test). Weld cracking was also observed. The creep tolerable temperature was in the vicinity of 730 C. (Sample 1: 733 C.; Sample 2: 728 C.), unsuited for the high-temperature piping product of the 800 C. class.

(39) The weld joints of Samples 3 and 4 were obtained from the conventional Ni-based alloys without performing the pre-aging heat treatment before welding (only the solution heat treatment was performed). Buttering was not performed. The phase did not precipitate in the unwelded samples (before welding) and in samples examined immediately after the welding (as-welded), whereas -phase precipitation was observed in the creep test suspended specimens (during creep test). There was no weld cracking. The creep tolerable temperature was in the vicinity of 740 C. (Sample 3: 742 C.; Sample 4: 738 C.), unsuited for the high-temperature piping product of the 800 C. class.

(40) The weld joints of Samples 5 and 6 were obtained from the Ni-based alloys according to the present invention without performing the pre-aging heat treatment before welding (only the solution heat treatment was performed). Buttering was not performed. The phase did not precipitate in the unwelded samples (before welding) and in samples examined immediately after the welding (as-welded), whereas coarse -phase precipitation of an abnormal (amoeba-like) shape was observed in the creep test suspended specimens (during creep test). This is considered to be due to the compositions of the Ni-based alloys of the present invention that generate more -phase precipitation than the conventional compositions, causing the phase to precipitate at once at the creep test temperature (corresponds to the actual operating temperature), and resulting in abnormal grain growth. There was no weld cracking. The creep tolerable temperature was in the vicinity of 770 C. (Sample 5: 770 C.; Sample 6: 772 C.), unsuited for the high-temperature piping product of the 800 C. class. This is probably because of the lack of fine phase dispersion and precipitation (the phase underwent abnormal grain growth).

(41) The weld joints of Samples 7 to 9 were obtained from the Ni-based alloys according to the present invention after the pre-aging heat treatment (900 C.16 hours) performed before welding. Buttering was performed. The phase did not precipitate in the primary pipe members and the welding material in samples examined immediately after the buttering (labeled as as-buttered), and about 10-volume % -phase precipitation was observed after the pre-aging heat treatment only in the primary pipe members (labeled as as-pre-aging heat treated). In the creep test suspended specimens (labeled as during creep test), fine phase dispersion and precipitation was observed in 30 volume % or more in the primary pipe members, and in 20 volume % or more in the welding material. There was no weld cracking. The creep tolerable temperature was 800 C. or more (Sample 7: 805 C.; Sample 8: 802 C.; Sample 9: 800 C.), confirming that the products are sufficiently applicable to the high-temperature piping product of the 800 C. class.

(42) As demonstrated above, it was confirmed to provide the high-temperature piping product exhibiting a tolerable temperature of the 800 C. class, and the method for producing such high-temperature piping products. With the high-temperature piping product of the present invention, a boiler for power plants of the 800 C. class can be provided. This greatly contributes to improving the power generating efficiency of power plants.

(43) Although the invention has been described with respect to the specific embodiments for complete and clear disclosure, the appended claims are not to be thus limited but are to be construed as embodying all modifications and alternative constructions that may occur to one skilled in the art which fairly fall within the basic teaching herein set forth.