CN101845573A - Ni-based alloy for a casting part of steam turbine with excellent high temperature strength, castability and weldability - Google Patents
Ni-based alloy for a casting part of steam turbine with excellent high temperature strength, castability and weldability Download PDFInfo
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- CN101845573A CN101845573A CN200910212116A CN200910212116A CN101845573A CN 101845573 A CN101845573 A CN 101845573A CN 200910212116 A CN200910212116 A CN 200910212116A CN 200910212116 A CN200910212116 A CN 200910212116A CN 101845573 A CN101845573 A CN 101845573A
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 111
- 239000000956 alloy Substances 0.000 title claims abstract description 111
- 238000005266 casting Methods 0.000 title claims abstract description 32
- 239000012535 impurity Substances 0.000 claims abstract description 19
- 238000002360 preparation method Methods 0.000 claims description 17
- 239000012071 phase Substances 0.000 description 27
- 239000010955 niobium Substances 0.000 description 21
- 239000010936 titanium Substances 0.000 description 19
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 16
- 239000011651 chromium Substances 0.000 description 15
- 238000000034 method Methods 0.000 description 15
- 239000011572 manganese Substances 0.000 description 13
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 12
- 230000008569 process Effects 0.000 description 12
- 239000000203 mixture Substances 0.000 description 11
- 238000001556 precipitation Methods 0.000 description 11
- 229910052782 aluminium Inorganic materials 0.000 description 10
- 238000004090 dissolution Methods 0.000 description 10
- 238000011156 evaluation Methods 0.000 description 10
- 229910052719 titanium Inorganic materials 0.000 description 9
- 229910052715 tantalum Inorganic materials 0.000 description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 7
- 229910052799 carbon Inorganic materials 0.000 description 7
- 239000010949 copper Substances 0.000 description 7
- 238000003466 welding Methods 0.000 description 7
- 229910052748 manganese Inorganic materials 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- 229910052750 molybdenum Inorganic materials 0.000 description 6
- 229910052758 niobium Inorganic materials 0.000 description 6
- 229910052710 silicon Inorganic materials 0.000 description 6
- 239000006104 solid solution Substances 0.000 description 6
- 239000010959 steel Substances 0.000 description 6
- 239000000126 substance Substances 0.000 description 6
- 229910000831 Steel Inorganic materials 0.000 description 5
- 229910052796 boron Inorganic materials 0.000 description 5
- 229910052804 chromium Inorganic materials 0.000 description 5
- 230000004927 fusion Effects 0.000 description 5
- 230000006698 induction Effects 0.000 description 5
- 229910052742 iron Inorganic materials 0.000 description 5
- 239000010703 silicon Substances 0.000 description 5
- 238000012360 testing method Methods 0.000 description 5
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 4
- 239000010941 cobalt Substances 0.000 description 4
- 229910017052 cobalt Inorganic materials 0.000 description 4
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 4
- 229910052802 copper Inorganic materials 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 229910001026 inconel Inorganic materials 0.000 description 4
- 239000007788 liquid Substances 0.000 description 4
- 238000002844 melting Methods 0.000 description 4
- 230000008018 melting Effects 0.000 description 4
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 3
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 3
- 239000005864 Sulphur Substances 0.000 description 3
- 230000003628 erosive effect Effects 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 description 3
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 2
- 229910001208 Crucible steel Inorganic materials 0.000 description 2
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- 239000004411 aluminium Substances 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 238000009750 centrifugal casting Methods 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 238000005261 decarburization Methods 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000011733 molybdenum Substances 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 2
- 238000000926 separation method Methods 0.000 description 2
- 229910052717 sulfur Inorganic materials 0.000 description 2
- 230000000007 visual effect Effects 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 208000037656 Respiratory Sounds Diseases 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000012141 concentrate Substances 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000004821 distillation Methods 0.000 description 1
- 238000010891 electric arc Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
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- 238000010438 heat treatment Methods 0.000 description 1
- 239000012943 hotmelt Substances 0.000 description 1
- 239000007943 implant Substances 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 229910001063 inconels 617 Inorganic materials 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 239000012466 permeate Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
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- 229910000753 refractory alloy Inorganic materials 0.000 description 1
- 231100000817 safety factor Toxicity 0.000 description 1
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Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Turbine Rotor Nozzle Sealing (AREA)
Abstract
A Ni-based alloy for a casting part of a steam turbine having excellent high temperature strength, castability and weldability includes, in percentage by mass, 0.01 to 0.15 of C, 18 to 28 of Cr, 10 to 15 of Co, 8 to 12 of Mo, 1.5 to 2 of Al, 0.1 to 3 of Ti, 0.001 to 0.006 of B, 0.1 to 0.7 of Ta, and the balance of Ni plus unavoidable impurities.
Description
The cross reference of related application
The application based on and require the rights and interests of the right of priority of the No.2008-328459 of Japanese patent application formerly that submits on December 24th, 2008; By reference its full content is incorporated at this.
Background technology
1. technical field
The present invention relates to prepare the material of the cast component of steam turbine, wherein high-temperature steam flows as working fluid in described steam turbine.Particularly, the present invention relates to have the nickel-base alloy that is used for the steam turbine cast component of excellent high intensity, castability and weldability, the steam turbine shell of steam turbine, the valve housing of steam turbine, the nozzle chest of steam turbine and the pipe of steam turbine, they are to be made by the nickel-base alloy that is used for the steam turbine cast component.
2. description of Related Art
In comprising the thermal power unit of steam turbine, from the viewpoint of global environmental protection, attention concentrates on the technology that suppresses Carbon emission, and the demand that improves generating efficiency is increased.
In order to develop the generating efficiency of steam turbine, used vapor temperature is effective in the raising steam turbine.Using in the thermal power unit of steam turbine in the recent period, vapor temperature is increased to 600 ℃ or higher.In the thermal power unit of use steam turbine in the future, vapor temperature seems and will be increased to 650 ℃ or 700 ℃.
Along with the temperature around mobile steam such as the steam turbine shell of steam turbine, valve housing, nozzle chest, pipes increases, the steam turbine shell, valve housing, nozzle chest, pipe etc. that are exposed to the steam turbine of high-temperature steam can cause wherein big stress.Consider this point, these parts of steam turbine must tolerate such hot conditions and such condition of high ground stress, therefore, and need be by in the pyritous temperature range, having the various materials of superior strength, ductility and flexible in room temperature.
Especially, when vapor temperature surpasses 700 ℃, consider to use nickel-base alloy, because traditional iron does not also have enough hot strengths (referring to document 1).
Because nickel-base alloy has its hot strength and high corrosion resistance, nickel-base alloy will be mainly used in jet engine and gas-turbine.Representative instance as nickel-base alloy is Inconel Alloy 617 (being made by Special Metals Corporation) and Inconel Alloy 706 (being made by Special MetalsCorporation).
For the mechanism of the hot strength of strengthening nickel-base alloy, be by adding Al or Ti to nickel-base alloy, forming such as γ ' phase (Ni at nickel-base alloy parent phase material
3(Al, Ti)) or the γ " precipitated phase of phase.In Inconel Alloy 706, precipitate γ ' phase and γ and " develop hot strength mutually.
On the other hand, in Inconel Alloy 617 or analogue, Co and Mo solid solution in the parent phase of nickel-base alloy (promptly using dissolving to strengthen), thus develop its hot strength.
[document 1] JP-A 07-150277 (KOKAI)
As mentioned above, use though nickel-base alloy is taken into account in the temperature range that surpasses 700 ℃ as the material of the turibine rotor of steam turbine, for nickel-base alloy, hot strength is not enough to use under such hot conditions.In addition, require to improve the hot strength of nickel-base alloy, keep the castability of nickel-base alloy and weldability etc. simultaneously by the improvement of forming etc.
Summary of the invention
Therefore, the purpose of this invention is to provide the nickel-base alloy that is used for the steam turbine cast component with excellent high intensity, castability and weldability, the steam turbine shell of steam turbine, the valve housing of steam turbine, the nozzle chest of steam turbine and the pipe of steam turbine, they are to be made by the nickel-base alloy that is used for the steam turbine cast component.
In order to reach purpose of the present invention, an aspect of of the present present invention relates to the nickel-base alloy that is used for the steam turbine cast component with excellent high intensity, castability and weldability, and in weight %, it contains C:0.01 to 0.15; Cr:18 to 28; Co:10 to 15; Mo:8 to 12; Al:1.5 to 2; Ti:0.1 to 3; B:0.001 to 0.006; Ta:0.1 to 0.7, and the Ni and the unavoidable impurities of surplus.
Another aspect of the present invention relates to the nickel-base alloy that is used for the steam turbine cast component with excellent high intensity, castability and weldability, and in weight %, it comprises C:0.01 to 0.15; Cr:18 to 28; Co:10 to 15; Mo:8 to 12; Al:1.5 to 2; Ti:0.1 to 3; B:0.001 to 0.006; Nb:0.1 to 0.4, and the Ni and the unavoidable impurities of surplus.
Another aspect of the present invention relates to the nickel-base alloy that is used for the steam turbine cast component with excellent high intensity, castability and weldability, and in weight %, it comprises C:0.01 to 0.15; Cr:18 to 28; Co:10 to 15; Mo:8 to 12; Al:1.5 to 2; Ti:0.1 to 3; B:0.001 to 0.006; Ta+2Nb:0.1 to 0.7 (mol ratio of Ta: Nb is 1: 2), and the Ni and the unavoidable impurities of surplus.
The steam turbine shell that relates to steam turbine more on the other hand of the present invention, it comprises at least by the part of above-mentioned any nickel-base alloy by the casting preparation.
The valve housing that relates to steam turbine more on the other hand of the present invention, it comprises at least by the part of above-mentioned any nickel-base alloy by the casting preparation.
The nozzle chest that relates to steam turbine more on the other hand of the present invention, it comprises at least by the part of above-mentioned any nickel-base alloy by the casting preparation.
The pipe that relates to steam turbine more on the other hand of the present invention, it comprises at least by the part of above-mentioned any nickel-base alloy by the casting preparation.
According to the steam turbine shell of the nickel-base alloy that is used for the steam turbine cast component with excellent high intensity, castability and weldability proposed by the invention, steam turbine, the valve housing of steam turbine, the nozzle chest of steam turbine and the pipe (they are to be made by the nickel-base alloy that is used for the steam turbine cast component) of steam turbine, with respect to those of routine, hot strength, castability and weldability in nickel-base alloy of the present invention and these parts can be enhanced.
Embodiment
To describe the present invention in detail below.
The nickel-base alloy that has the steam turbine cast component of excellent high intensity, castability and weldability according to embodiments of the present invention has following composition.Here symbol " % " refers to " weight % ", unless otherwise indicated.
(M1) C:0.01% to 0.15%, Cr:18% to 28%, Co:10% to 15%, Mo:8% to 12%, Al:1.5% to 2%, Ti:0.1% to 3%, B:0.001% to 0.006%, Ta:0.1% to 0.7%, and its remainder is Ni and unavoidable impurities.
(M2) C:0.01% to 0.15%, Cr:18% to 28%, Co:10% to 15%, Mo:8% to 12%, Al:1.5% to 2%, Ti:0.1% to 3%, B:0.001% to 0.006%, Nb:0.1% to 0.4%, and its remainder is Ni and unavoidable impurities.
(M3) C:0.01% to 0.15%, Cr:18% to 28%, Co:10% to 15%, Mo:8% to 12%, Al:1.5% to 2%, Ti:0.1% to 3%, B:0.001% to 0.006%, Ta+2Nb:0.1% to 0.7%, and its remainder is Ni and unavoidable impurities.Here, term " Ta:2Nb " means that the mol ratio of Ta: Nb is 1: 2.
About being numbered (M1) unavoidable impurities to the nickel-base alloy of (M3), the content of expectation Si is set to 0.1% or still less, and the content of Mn is set to 0.1% or still less.As unavoidable impurities, except Si and Mn, can be exemplified as Cu, Fe and S.Nickel-base alloy with above-mentioned composition is preferred for being manufactured on the material of cast component of the steam turbine of 680 ℃ to 750 ℃ temperature ranges operations.As the cast component of steam turbine, can be exemplified as the steam turbine shell of steam turbine, the valve housing of steam turbine, the nozzle chest of steam turbine and the pipe of steam turbine.
Steam turbine shell is interpreted as, and it makes wherein to implant has the turbine rotor of turbine rotor blade to permeate via steam turbine shell, is used for steam is introduced the internal surface of the nozzle placement of steam turbine shell at steam turbine shell, thereby constitutes steam turbine.Valve housing is a valve housing, and described valve starts to control preparing high-temp high pressure steam flow velocity to be supplied to the effect of steam turbine and/or steam off mobile steam valve.As the housing valve, can be exemplified as the valve housing that under the condition of 680-750 ℃ steam flow, adopts.Nozzle chest is an annular distillation flow passage, its be positioned at turbine rotor around, the high temperature and high pressure steam that is used for supplying at steam turbine uses first nozzle and the first turbine rotor blade to introduce in first section of steam turbine.Described pipe is main team pipe or the high-temperature reheat pipe that is used for steam is introduced by boiler high pressureturbine.Steam turbine shell, valve housing, nozzle chest and pipe are configured in these component exposed under the environment of high temperature and high pressure steam.
Nickel-base alloy can be applied to each part of steam turbine cast component or the part of cast component, and the cast component that is arranged in the steam turbine on the high pressureturbine may be configured under the high temperature and high pressure atmosphere.Alternatively, the steam turbine cast component that is arranged in from the high pressureturbine bridging to intermediate pressureturbine part also possible configuration under high temperature and high pressure atmosphere.Be configured in steam turbine cast component under the high temperature and high pressure atmosphere be not limited to above-mentioned give an example which.In present specification, statement " being configured in the cast component of high temperature and high pressure atmosphere tubine " means the cast component configuration of steam turbine and is exposed under the interior temperature atmosphere of 680-750 ℃ of temperature range.
Above-mentioned nickel-base alloy has hot strength, castability and the weldability that is better than conventional nickel-base alloy.Therefore, if steam turbine cast component such as steam turbine shell, valve housing, nozzle chest and pipe can be by nickel-base alloy manufacturings according to embodiments of the present invention, cast component has higher reliability under high-temperature atmosphere so.That is, can be manufactured on steam turbine shell, valve housing, nozzle chest and the pipe that has high reliability under the high-temperature atmosphere separately.
Below, will the reason that limit according to each composition compositional range in the above-mentioned nickel-base alloy of the present invention be described.
(1) C (carbon)
C is as adding solid phase M
23C
6The component of type carbide is useful.Particularly, at the operating period of steam turbine, M
23C
6The precipitation of type carbide is one of the principal element that keeps the creep strength of alloy (being nickel-base alloy) under 650 ℃ or higher high-temperature atmosphere.Alternatively, carbon has the effect of guaranteeing the flowability of molten metal when casting.When the content of C is set to less than 0.01% the time, the physical strength of nickel-base alloy (hereinafter meaning hot strength usually) can be lowered, because the precipitation that carbide can not be enough, and the mobile of nickel-base alloy melts significantly reduces during the casting.On the other hand, when the content of C was set to surpass 0.15%, the component separation trend of nickel-base alloy hot-melt object increased when making bigger nickel-base alloy ingot bar, and embrittlement phase M
6The generation of C type carbide is quickened.Therefore, the content of C is set to 0.01% to 0.15%.
(2) Cr (chromium)
Chromium (Cr) is the important element that strengthens oxidation-resistance, erosion resistance and the physical strength of nickel-base alloy, and as M
23C
6It is necessary for the essentially consist element of type carbide.Especially, under 650 ℃ or higher hot environment, at the operating period of steam turbine M
23C
6The precipitation of type carbide is the one of the chief elements that keeps alloy (being nickel-base alloy) creep strength.Perhaps, Cr has the effect that strengthens the nickel-base alloy oxidation-resistance under the high-temperature steam environment.When Cr content is set to less than 18% the time, the oxidation-resistance of nickel-base alloy can reduce.On the other hand, when Cr content is set to surpass 28%, M
23C
6The precipitation of type carbide is significantly quickened, thereby has increased sedimentary M
23C
6The thickization trend of type carbide.Therefore, the content of Cr is arranged on 18% to 28%.
(3) Co (cobalt)
Cobalt (Co) is advanced the physical strength that strengthens its parent phase in the parent phase of nickel-base alloy by solid solution (solid-solving).Yet, when cobalt contents is set to surpass 15%, produce the intermetallic compound phase (intermetallic compound phase) that reduces the nickel-base alloy physical strength, thereby the physical strength of nickel-base alloy reduces.On the other hand, when cobalt contents less than 10% the time, the workability of nickel-base alloy (castability) reduces, and the physical strength of nickel-base alloy also reduces.Therefore, carbon content is arranged on 10% to 15%.
(4) Mo (molybdenum)
Molybdenum (Mo) is advanced the physical strength that strengthens its parent phase in the parent phase of nickel-base alloy by solid solution.In addition, M
23C
6Part in the component of type carbide replaces with the Mo element, thereby the stability of carbide increases.When Mo content is set to can not show above-mentioned effect/function less than 8% the time.When Mo content was set to surpass 12%, the component separation trend of nickel-base alloy heat fusing thing increased when making the nickel-base alloy than sow, and embrittlement phase M
6The generation of C type carbide is quickened.Therefore, the content of Mo is arranged on 8% to 12%.
(5) Al (aluminium)
Aluminium (Al) and nickel produce γ ' mutually (γ ': Ni
3Al), thus the precipitation by this γ ' phase improves the physical strength of nickel-base alloy.When the content of Al is set to less than 1.5% the time, the physical strength of nickel-base alloy and workability (castability) are not all improved than ordinary steel, and when the content of Al was set to surpass 2%, the physical strength of nickel-base alloy improved, but the castability of nickel-base alloy (workability) reduces.Therefore, the content of Al is arranged on 1.5% to 2%.
(6) Ti (titanium)
In the mode identical with Al, titanium (Ti) and nickel produce γ ' mutually (γ ': Ni
3Ti), thus improve the physical strength of nickel-base alloy.When the content setting of Ti less than 0.1% the time, the hot workability deterioration of nickel-base alloy.And when Ti content was set to surpass 3%, the notch sensitivity of nickel-base alloy increased.Therefore, Ti content is arranged on 0.1% to 3%.
(7) B (boron)
Boron (B) is advanced the physical strength that strengthens its parent phase in the parent phase of nickel-base alloy by solid solution.When the content of B is set to less than 0.001% the time, the physical strength of its parent phase does not strengthen, and when the content of B is set to surpass 0.006%, causes embrittlement of grain boundaries at nickel-base alloy.Therefore, B content is arranged on 0.001% to 0.006%.
(8) Ta (tantalum)
Tantalum (Ta) is stablized γ ' phase (γ ' x phase Ni
3The precipitation strength of (Al, Ti)).When tantalum (Ta) content is set to less than 0.1% the time, than ordinary steel, can not strengthen the stable of precipitation strength, and when Ta content is set to surpass 0.7%, the increase of the production cost of nickel-base alloy makes the economic benefit deterioration.Therefore, Ta content is arranged on 0.1% to 0.7%.
(9) Nb (niobium)
Niobium (Nb) is solid-solubilized in γ ' phase (γ ' phase (Ni
3In (Al, Ti)), so that settling is strengthened.When the content of Nb less than 0.1% the time, compare with ordinary steel, can not strengthen the stable of precipitation strength, and when the content of Nb was set to surpass 0.4%, the physical strength of nickel-base alloy was improved, but workability (castability) reduction.Therefore, the content of Nb is arranged on 0.1% to 0.4%.
Use Ta and Nb, the total content by (Ta+2Nb) expression is set can improve γ ' phase (γ ' phase (Ni in 0.1% to 0.7% scope
3Al, Ti)) precipitation strength.When the total content of (Ta+2Nb) less than 0.1% the time, compares with ordinary steel and can not improve precipitation strength fully, and the total content of working as (Ta+2Nb) is when surpassing 0.7%, the physical strength of nickel-base alloy is improved, but the workability of nickel-base alloy (castability) can reduce.Ta content and Nb content are set at least 0.01% or bigger respectively.
Because the proportion of Nb roughly be Ta proportion half (proportion of Ta: 16.6, the proportion of Nb: 8.57), therefore, than adding Ta, increase total solid solution scale of construction of its parent phase in the parent phase of nickel-base alloy by common adding Ta and Nb.In addition, because Ta is strategic material, therefore, be difficult to stable obtain it.On the other hand, because the deposit of Nb roughly is 100 times of Ta, Nb can stablize supply.The fusing point of Ta is higher than the fusing point (fusing point of Ta: about 3000 ℃, the fusing point of Nb: about 2470 ℃) of Nb, and therefore, γ ' is strengthened mutually under comparatively high temps.In addition, the oxidation-resistance of Ta is better than the oxidation-resistance of Nb.
(10) Si (silicon), Mn (manganese), Cu (copper), Fe (iron) and S (sulphur)
According to nickel-base alloy of the present invention, Si (silicon), Mn (manganese), Cu (copper), Fe (iron) and S (sulphur) are divided into unavoidable impurities.Therefore, preferably making these impurity residue content as far as possible is 0% as far as possible.The residue content of wishing Si (silicon) in these impurity and Mn (manganese) is set to 0.1% or still less respectively.
In plain carbon stool, add Si (silicon) to compensate its relatively poor erosion resistance.Yet,, can fully guarantee the erosion resistance of nickel-base alloy because the Cr content in the described nickel-base alloy is big.Therefore, Si residue content is set to 0.1% or still less in the nickel-base alloy, and preferably is reduced to 0% as far as possible.
In plain carbon stool, Mn and S constitute MnS, thereby suppress the fragility of nickel-base alloy, because S can cause the fragility of plain carbon stool.Yet the content of the S in the described nickel-base alloy is minimum, therefore, must not add Mn in nickel-base alloy.Therefore, Mn residue content is set to 0.1% or still less, and preferably is reduced to 0% as far as possible.
The nickel-base alloy that is used for steam turbine shell, valve housing and nozzle chest according to the cast component of steam turbine of the present invention, can followingly make: at first, make the moiety fusion of nickel-base alloy by vacuum induction melting (VIM), and gained heat fusing thing is injected the casting case to form ingot bar.Then, handle by dissolution process (solution treatment).
In pipe manufacturer according to the nickel-base alloy preparation of the cast component of steam turbine of the present invention, the composition of nickel-base alloy is the fusion by vacuum induction melting (VIM), and gained heat fusing thing is injected in the cylinder casting case under cylinder casting case high-speed rotating conditions.In the case, because the heat fusing thing is derived from the centrifugal force pressurization of cylinder casting case rotation, the gained ingot bar is shaped with predetermined tube shape, handles by dissolution process then.In this way, can make the pipe of steam turbine, this is called centrifugal casting.
Dissolution process was preferably carried out in 1100 ℃ to 1200 ℃ temperature range 4-15 hour.Carry out dissolution process with solid solution γ ' precipitated phase equably.When the temperature of dissolution process was set to be lower than 1100 ℃, the solid dissolving can not be carried out fully.When the temperature of dissolution process was set to be higher than 1200 ℃, the intensity of nickel-base alloy reduced, and this is because the alligatoring of its crystal grain.
As the cast component according to steam turbine of the present invention, housing, valve housing and vapour nozzle chest can followingly be made.At first, the composition according to the nickel-base alloy of the cast component of steam turbine of the present invention is the fusion by vacuum induction melting (VIM).The heat fusing thing that obtains like this is injected in the corresponding casting case, casts under atmosphere then.Resulting ingot bar is handled by dissolution process.
As cast component of the present invention, steam turbine shell, valve housing and nozzle chest can followingly be made: at first, composition according to the nickel-base alloy of the cast component of steam turbine of the present invention is the fusion by electric furnace (EF), and the decarburization by aod process (AOD).The heat fusing thing that obtains like this is injected in the corresponding casting case, casts under atmosphere then.The ingot bar that obtains like this is by dissolution process and processed.
As cast component of the present invention, pipe can followingly be made: at first, at first, be fusion according to the composition of the nickel-base alloy of the cast component of steam turbine of the present invention by vacuum induction melting (VIM) or electric furnace (EF), and the decarburization by aod process (AOD).The heat fusing thing that obtains like this is injected in the cylinder casting case under with the high rotation speed rotating conditions at cylinder casting case.In the case, because the heat fusing thing is derived from the centrifugal force pressurization of cylinder casting case rotation, the gained ingot bar is shaped with predetermined tube shape, handles by dissolution process then.In this way, can make the pipe (centrifugal casting) of steam turbine.
The manufacture method of steam turbine shell, valve housing, nozzle chest and pipe be not limited to above-mentioned these.
The excellent high intensity, castability and the weldability that are used for the nickel-base alloy of steam turbine cast component will hereinafter be described.
(hot strength, castability and weldability evaluation)
Here, description had excellent high intensity, weldability and the castability of nickel-base alloy of steam turbine cast component that the invention described above limits the composition of compositing range.Table 1 has shown that the sample 1 that carries out hot strength, castability and weldability evaluation arrives the chemical constitution of sample 28.Sample 1 belongs to the chemical composition range that the present invention limits to the chemical constitution of sample 6.Sample 7 does not belong to chemical composition range of the present invention to sample 28.Therefore, sample 7 is to the corresponding comparing embodiment of sample 28 difference.The chemical constitution of sample 7 is equivalent to conventional Inconel 617.In the case, except Si (silicon) and Mn (manganese), the nickel-base alloy of each sample also contains Fe (iron), Cu (copper) and S (sulphur) as unavoidable impurities.
By tensile strength test, hot strength has obtained evaluation.In tensile strength test, the nickel-base alloy of 20kg at the vacuum induction melt in furnace, is formed the ingot bar (being that sample 1 is to sample 28) of each sample.As mentioned above, sample 1 has the listed corresponding chemical composition of table 1 to sample 28.Carry out dissolution process 4 hours for ingot bar at 1180 ℃ subsequently, thereby form cast steel.Then, each sample is prepared by cast steel with predetermined size.
Then, on JIS G 0567, each sample is carried out tensile strength experiment (to the high temperature tension test method of steel and refractory alloy) in the temperature of 23 ℃, 700 ℃ and 800 ℃.In the case, the proof stress of measurement 0.2%.The test temperature of 700 ℃ and 800 ℃ is that temperature condition and its safety factors when considering the steam turbine normal running set.The measuring result of 0.2% proof stress sample is one by one listed in the table 2.
In addition, each sample is carried out the castability evaluation.In this was estimated, the ingot bar that relates to sample was two ingot sheets by vertical segmentation.Then, on JIS Z 2343-1, the liquid penetrate examination (PT) (Non-destructive testing--Penetrant testing--Part 1:General principles--Method for liquid penetrant testing andclassification of the penetrant indication) of welded heat affecting zone is carried out on ingot sheet cutting surface.Then, the appearance of visual assessment casting crack.Castability evaluation result sample is one by one listed in the table 2.Here, the situation of no casting crack " is not occurred " representing by term.In the case, because castability is good, the castability evaluation is by symbol " zero " expression.The situation of casting crack is represented by term " appearance ".In the case, because castability is poor, casting evaluation is represented by symbol " * ".
In addition, weldability is by sample evaluation one by one.In the case, when each sample was formed by corresponding ingot bar, it is wide that sample size is set to 60mm, and 150mm is long, and 40mm is thick.Forming width at each sample place is that 10mm and thickness are the groove of 5mm, thereby alongst is extended at the center of its width almost.Then, the electric-arc heating to this groove carries out employing in the TIG welding makes each sample be cut off at the thickness direction of groove, thereby is parallel to width.Then, on JIS Z 2343-1, the cutting surface of each sample is carried out the liquid penetrate examination (PT) (Non-destructive testing--Penetrant testing--Part 1:General principles--Method for liquid penetrant testing and classification of the penetrantindication) of welded heat affecting zone.Then, each sample is carried out the appearance of visual assessment welding crack.The welding evaluation result is listed in the table 2 one by one.Here, the situation of not having the welding crackle is represented by term " appearance ".In the case, because weldability is good, welding is estimated by symbol " zero " expression.The situation of welding crack is represented by term " appearance ".In the case, because weldability is poor, welding evaluation is represented by symbol " * ".
Table 2
Verified, sample 1 has 0.2% higher proof stress, good castability and weldability to sample 6 under each temperature.Sample 1 is considered to because precipitation strength and dissolving are strengthened to the reason that sample 6 has 0.2% higher proof stress respectively.
For example, on the contrary, sample 18 and sample 20 have 0.2% higher proof stress respectively, but have relatively poor castability and weldability.All conventional steel that relate to the comparative example can not represent excellent high-temperature intensity, castability and weldability.
Though described the present invention in detail with reference to above embodiment, the present invention is not limited to above disclosure, does not break away from the scope of the invention and can carry out variations and modifications.
Claims (18)
1. have the nickel-base alloy that is used for the steam turbine cast component of excellent high intensity, castability and weldability, in weight %, it comprises:
C:0.01 to 0.15; Cr:18 to 28; Co:10 to 15; Mo:8 to 12; Al:1.5 to 2; Ti:0.1 to 3; B:0.001 to 0.006; Ta:0.1 to 0.7, and the Ni and the unavoidable impurities of surplus.
2. the nickel-base alloy of claim 1,
The content that wherein is selected from the Si at least of inevitable impurity and Mn is set to 0.1 or still less respectively.
3. have the nickel-base alloy that is used for the steam turbine cast component of excellent high intensity, castability and weldability, in weight %, it comprises:
C:0.01 to 0.15; Cr:18 to 28; Co:10 to 15; Mo:8 to 12; Al:1.5 to 2; Ti:0.1 to 3; B:0.001 to 0.006; Nb:0.1 to 0.4, and the Ni and the unavoidable impurities of surplus.
4. the nickel-base alloy of claim 3,
The content that wherein is selected from the Si at least of inevitable impurity and Mn is set to 0.1 or still less respectively.
5. have the nickel-base alloy that is used for the steam turbine cast component of excellent high intensity, castability and weldability, in weight %, it comprises:
C:0.01 to 0.15; Cr:18 to 28; Co:10 to 15; Mo:8 to 12; Al:1.5 to 2; Ti:0.1 to 3; B:0.001 to 0.006; Ta+2Nb:0.1 to 0.7 (mol ratio of Ta: Nb is 1: 2), and the Ni and the unavoidable impurities of surplus.
6. the nickel-base alloy of claim 5,
The content that wherein is selected from the Si at least of inevitable impurity and Mn is set to 0.1 or still less respectively.
7. the steam turbine shell of steam turbine, it comprises:
Pass through at least a portion of casting preparation by the nickel-base alloy of claim 1.
8. the steam turbine shell of steam turbine, it comprises:
Pass through at least a portion of casting preparation by the nickel-base alloy of claim 3.
9. the steam turbine shell of steam turbine, it comprises:
Pass through at least a portion of casting preparation by the nickel-base alloy of claim 5.
10. the valve housing of steam turbine, it comprises:
Pass through at least a portion of casting preparation by the nickel-base alloy of claim 1.
11. the valve housing of steam turbine, it comprises:
By the nickel-base alloy of claim 3 at least a portion by the valve housing preparation.
12. the valve housing of steam turbine, it comprises:
Pass through at least a portion of casting preparation by the nickel-base alloy of claim 5.
13. the nozzle chest of steam turbine, it comprises:
Pass through at least a portion of casting preparation by the nickel-base alloy of claim 1.
14. the nozzle chest of steam turbine, it comprises:
Pass through at least a portion of casting preparation by the nickel-base alloy of claim 3.
15. the nozzle chest of steam turbine, it comprises:
Pass through at least a portion of casting preparation by the nickel-base alloy of claim 5.
16. the pipe of steam turbine, it comprises:
Pass through at least a portion of casting preparation by the nickel-base alloy of claim 1.
17. the pipe of steam turbine, it comprises:
Pass through at least a portion of casting preparation by the nickel-base alloy of claim 3.
18. the pipe of steam turbine, it comprises:
Pass through at least a portion of casting preparation by the nickel-base alloy of claim 5.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2008328459A JP2010150585A (en) | 2008-12-24 | 2008-12-24 | Ni-based alloy for casting part of steam turbine excellent in high-temperature strength, castability and weldability, turbine casing of steam turbine, valve casing of steam turbine, nozzle box of steam turbine, and pipe of steam turbine |
| JP328459/2008 | 2008-12-24 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN101845573A true CN101845573A (en) | 2010-09-29 |
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ID=42123079
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN200910212116A Pending CN101845573A (en) | 2008-12-24 | 2009-11-10 | Ni-based alloy for a casting part of steam turbine with excellent high temperature strength, castability and weldability |
Country Status (4)
| Country | Link |
|---|---|
| US (1) | US20100158682A1 (en) |
| EP (1) | EP2206795A3 (en) |
| JP (1) | JP2010150585A (en) |
| CN (1) | CN101845573A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102777654A (en) * | 2011-05-12 | 2012-11-14 | 阿尔斯通技术有限公司 | High temperature steam valve |
| WO2014055642A1 (en) * | 2012-10-02 | 2014-04-10 | Nibco Inc. | Lead-free high temperature/pressure piping components and methods of use |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2012255424A (en) * | 2011-06-10 | 2012-12-27 | Toshiba Corp | Ni-BASED ALLOY FOR CASTING USED FOR STEAM TURBINE AND CASTING COMPONENT OF STEAM TURBINE |
| JP5646521B2 (en) * | 2012-02-08 | 2014-12-24 | 株式会社東芝 | Ni-based alloy for steam turbine casting and cast component for steam turbine |
| US20130323522A1 (en) * | 2012-06-05 | 2013-12-05 | General Electric Company | Cast superalloy pressure containment vessel |
| JP6079404B2 (en) * | 2013-04-19 | 2017-02-15 | 大同特殊鋼株式会社 | Method for forging disc-shaped products |
| WO2015052466A1 (en) * | 2013-10-11 | 2015-04-16 | Reaction Engines Limited | Ducts for engines |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5372662A (en) * | 1992-01-16 | 1994-12-13 | Inco Alloys International, Inc. | Nickel-base alloy with superior stress rupture strength and grain size control |
| US6106767A (en) * | 1995-12-21 | 2000-08-22 | Teledyne Industries, Inc. | Stress rupture properties of nickel-chromium-cobalt alloys by adjustment of the levels of phosphorus and boron |
| US20060051234A1 (en) * | 2004-09-03 | 2006-03-09 | Pike Lee M Jr | Ni-Cr-Co alloy for advanced gas turbine engines |
| JP5147037B2 (en) * | 2006-04-14 | 2013-02-20 | 三菱マテリアル株式会社 | Ni-base heat-resistant alloy for gas turbine combustor |
| JP2009084684A (en) * | 2007-09-14 | 2009-04-23 | Toshiba Corp | Nickel-based alloy for turbine rotor of steam turbine, and turbine rotor of steam turbine |
| JP4635065B2 (en) * | 2008-03-17 | 2011-02-16 | 株式会社東芝 | Ni-based alloy for steam turbine turbine rotor and steam turbine turbine rotor |
-
2008
- 2008-12-24 JP JP2008328459A patent/JP2010150585A/en not_active Withdrawn
-
2009
- 2009-10-19 EP EP09013152A patent/EP2206795A3/en not_active Withdrawn
- 2009-11-10 CN CN200910212116A patent/CN101845573A/en active Pending
- 2009-12-08 US US12/633,468 patent/US20100158682A1/en not_active Abandoned
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102777654A (en) * | 2011-05-12 | 2012-11-14 | 阿尔斯通技术有限公司 | High temperature steam valve |
| CN102777654B (en) * | 2011-05-12 | 2014-12-31 | 阿尔斯通技术有限公司 | High temperature steam valve |
| WO2014055642A1 (en) * | 2012-10-02 | 2014-04-10 | Nibco Inc. | Lead-free high temperature/pressure piping components and methods of use |
| US8991787B2 (en) | 2012-10-02 | 2015-03-31 | Nibco Inc. | Lead-free high temperature/pressure piping components and methods of use |
| US9217521B2 (en) | 2012-10-02 | 2015-12-22 | Nibco Inc. | Lead-free high temperature/pressure piping components and methods of use |
| US9441765B2 (en) | 2012-10-02 | 2016-09-13 | Nibco Inc. | Lead-free high temperature/pressure piping components and methods of use |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2010150585A (en) | 2010-07-08 |
| EP2206795A2 (en) | 2010-07-14 |
| EP2206795A3 (en) | 2010-08-04 |
| US20100158682A1 (en) | 2010-06-24 |
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