CN100345990C - Method for developing a nickel-base super alloy - Google Patents
Method for developing a nickel-base super alloy Download PDFInfo
- Publication number
- CN100345990C CN100345990C CNB028222334A CN02822233A CN100345990C CN 100345990 C CN100345990 C CN 100345990C CN B028222334 A CNB028222334 A CN B028222334A CN 02822233 A CN02822233 A CN 02822233A CN 100345990 C CN100345990 C CN 100345990C
- Authority
- CN
- China
- Prior art keywords
- phase
- room temperature
- degraded
- alloy
- parameter
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
Images
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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B11/00—Single-crystal growth by normal freezing or freezing under temperature gradient, e.g. Bridgman-Stockbarger method
-
- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B29/00—Single crystals or homogeneous polycrystalline material with defined structure characterised by the material or by their shape
- C30B29/10—Inorganic compounds or compositions
- C30B29/52—Alloys
Abstract
The invention relates to a method for developing a nickel-base super alloy, consisting of a gamma phase and a gamma' phase, for the production of monocrystalline or specifically solidified substance bodies. The invention is characterized in that the properties of nickel-base super alloys, exhibiting a volume proportion of at least 50 %, are optimized after degradation at room temperature, by selecting the composition of the alloy in such a way that a high as possible positive lattice dislocation (delta) is obtained at room temperature between the gamma phase and the gamma' phase. As a result the apparent limit of elasticity at room temperature after degradation is relatively high and only a small difference of apparent limits of elasticity occurs between the initial state and a degraded state.
Description
Technical field
The present invention relates to a kind of preparation method of nickel base superalloy, this alloy is used to make the material bodies of monocrystalline or directional freeze.
Background technology
Prior art discloses a series of nickel base superalloys that are used to make monocrystalline or unidirectional solidification material body.Such material bodies for example is used to build the power station with high temperature resistant requirement.For example can make and the hot strength maximum of material can improve the inlet temperature of gas turbine thus once more, thereby improve the efficient of gas turbine by means of the monocrystalline component.
Up to now, according to the such alloy of following thinking exploitation:
-raising creep rupture strength
-raising oxidation-resistance and erosion resistance
-raising stops the crack growth performance, particularly anti-LCF (fatigue of Low Cycle Fatigue=when hanging down the load cycle number of times) performance
-improvement castability and heat treatment performance
-reduce cost.
Known nickel base superalloy for example has CMSX-2, CMSX-4, CMSX-10, Rene N5, ReneN6, PWA 1484 and PWA1483 alloy, it is formed for example by G.L.Erickson:Corrosionresistant Single Crystal Superalloys for Industrial Gas Turbine Application, International Gas ﹠amp; Turbine Aeroengine Congress ﹠amp; Exhibition, Orlando, Florida, June 2-June 5,1997 is disclosed.Such alloy is heat-treated after casting process, wherein one first solution annealing step, is dissolved in the inhomogeneous γ ' that separates out of casting process-phase whole or in part.Again under control, separate out in this phase of second heat treatment step.In order to obtain best performance, so separate out thermal treatment, make to form the uniform distribution of γ-phase particle in γ '-mutually.
Known lattice dislocation can play conclusive effect to the creep rupture strength under the high temperature.Many known nickel base superalloys have between γ-matrix and γ '-phase just or negative crystal case mistake.Dislocation when having suppressed γ '-particle slip or cutting by this lattice distortion, thus the short term strength under the high temperature improved.On the one hand, require nickel base superalloy at room temperature to have the negative crystal case mistake of high amplitude (P.Caron:High γ ' solvus new generation nickel-based superalloys for single crystalturbine blade applications.Proceedings of the 9 as far as possible in the document
ThInternational symposium onSuperalloys-SUPERALLOY 2000, p.737-746, Champion, USA, September 17-21,2000), and other nickel base superalloy (referring to for example EP 0 914 483 B1) is regulated (Konzipiert) by correspondingly selecting alloying element, make and do not have lattice dislocation, reason is when having determined at high temperature a kind of big or permanent mechanical stress of long-term existence, by γ-and γ '-phase between lattice dislocation, can produce directed γ '-particle roughening, the degraded that then produces γ '-structure.
Summary of the invention
The present invention attempts to avoid the shortcoming of known prior art.Its task provides a kind of preparation method of the nickel base superalloy based on new simple thinking.
The present invention has finished this task in the following manner, promptly select the component of alloy, make and at room temperature have high as far as possible γ-phase and the positive lattice dislocation δ between γ '-phase, thereby after at room temperature degrading, the performance that makes γ '-phase volume content be at least 50% nickel base superalloy reaches best, wherein δ [%]=2 (a
γ '-a
γ)/(a
γ '+ a
γ), a
γBe the lattice parameter of γ-phase, a
γ 'It is the lattice parameter of γ '-phase.
The invention has the advantages that, utilize present method can develop nickel base superalloy fairly simplely with best degradation property.
Determined already, when having a kind of mechanical stress and a kind of persistent high temperature stress, can cause directed γ '-particle roughening, be called metal block and form (rafting), cause the conversion of microtexture at γ '-when content is high (γ '-volume content be at least 50%), that is to say γ '-be phase-changed into external phase, early stage γ-matrix embeds wherein.Because intermetallic γ '-be tending towards environmental embrittlement mutually, this can cause the especially decline significantly of yield strength of mechanical property at room temperature under certain stress condition.When moist and when keeping tensile stress for a long time, environmental embrittlement appears especially easily.The present invention selects the lattice dislocation δ between high positively charged γ-phase and the γ '-phase, and the reduction of performance shows not too strongly, that is to say, it is very little with respect to the yield strength loss that does not reduce state to reduce the back state.
Advantageously determine γ-phase and γ ' lattice parameter a mutually according to following known formula
γAnd a
γ ':
a
γ[]＝3.524+0,0196Co+0.110Cr+0.478Mo+0.444W+0.441Re
+0.3125Ru+0.179Al+0.422Ti+0.7Ta+0.7Nb，
Wherein the numeral respective element before the symbol of element the relative atom mark of γ-phase and
a
γ′[]＝3.57-0.004Cr+0.208Mo+0.194W+0.262Re+0.1335Ru
+0.258Ti+0.5Ta+0.46Nb，
Wherein the numeral respective element before the symbol of element is at the relative atom mark of γ '-phase.
In order to characterize the enduring quality of nickel base superalloy, introduce a degraded parameter D who determines according to following formula now:
D＝(T-800)t
1/2σ
1/5
T=temperature in the formula, unit is a ° K, and the t=time, unit is hour, and σ is a stress, and unit is MPa.At room temperature determine the yield strength σ of different nickel base superalloy degraded states according to the degraded parameter
0.2, select the alloy of corresponding virgin state and degraded state yield strength difference minimum, just at the highest as far as possible alloy of degraded state yield strength value.
Description of drawings
Embodiments of the invention have been shown in the accompanying drawing.Wherein:
Fig. 1 represents yield strength and γ-mutually and the relation of the lattice dislocation between γ '-phase after different known nickel base superalloys is at room temperature degraded; With
Fig. 2 represents the relation of different known nickel base superalloy yield strengths at room temperature and degraded parameter.
Essential characteristic of the present invention only is described now.Identical element has identical symbol in different accompanying drawings.
Embodiment
Explain the present invention in detail by means of embodiment and attached Fig. 1 and 2 below.
Determined already, when having mechanical stress and persistent high temperature stress, can cause directed γ '-particle roughening, be called metal block and form (solvate), cause the conversion of microtexture at γ '-when content is high (γ '-volume content be at least 50%), that is to say γ '-be phase-changed into external phase, early stage γ-matrix embeds wherein.Because intermetallic γ '-be tending towards environmental embrittlement mutually, this can cause the especially decline significantly of yield strength of mechanical property at room temperature under certain stress condition.Thereby cause performance decrease.When moist and when remaining on tensile stress for a long time, environmental embrittlement appears especially easily.The present invention is chosen in the high positivity lattice dislocation δ between γ-phase and the γ '-phase, and the reduction of performance shows not too strongly, that is to say, it is very little with respect to the yield strength loss that does not reduce state to reduce the back state.
Yield strength σ after the various known nickel base superalloy that Fig. 1 represents to be used to make monocrystalline or unidirectional solidification material is at room temperature degraded
0.2With γ-mutually and the relation of the lattice dislocation δ between γ '-phase.Lattice dislocation δ between γ-phase and γ '-phase can following in known manner calculating:
δ[％]＝2(a
γ′-a
γ)/(a
γ′+a
γ)
A wherein
γBe the lattice parameter of γ-phase, a
γ 'It is the lattice parameter of γ '-phase.
Table 1 has been listed the chemical constitution (% meter by weight) of alloy.
The alloy of being tested γ-phase and the lattice dislocation δ scope between γ '-phase at room temperature is approximately-0.24% to+0.58%..Along with the increase of positive lattice dislocation, the yield strength σ under the room temperature after the degraded
0.2Also rise.In the alloy of test, alloy PW1480 has the highest γ-phase and the positive lattice dislocation δ between γ '-phase, therefore at room temperature has the highest yield strength σ after the degraded
0.2
According to following known (P.Caron:High γ ' solvus new generation nickel-basedsuperalloys for single crystal turbine blade applications.Proceedings of the 9
ThInternational symposium on Superalloys-SUPERALLOY 2000, p.737-746, Champion, USA, September 17-21,2000) formula determine γ-phase and γ ' lattice parameter a mutually
γAnd a
γ ':
a
γ[A]＝3.524+0,0196Co+0.110Cr+0.478Mo+0.444W+0.441Re
+0.3125Ru+0.179Al+0.422Ti+0.7Ta+0.7Nb，
Wherein the numeral respective element before the symbol of element the relative atom mark of γ-phase and
a
γ′[]＝3.57-0.004Cr+0.208Mo+0.194W+0.262Re+0.1335Ru
+0.258Ti+0.5Ta+0.46Nb，
Wherein the numeral respective element before the symbol of element is at the relative atom mark of γ '-phase.Alloying element B, Zr and C act in lattice dislocation not quite, particularly because they exist with very little amount as just trace element.
Now, people can be according to the degradation property optimizing that the invention enables alloy, and way is to make that by changing to form the positive lattice dislocation δ between γ-phase and the γ '-phase is high as far as possible.In order to characterize the enduring quality of nickel base superalloy, introduce a degraded parameter D who determines according to following formula:
D＝(T-800)t
1/2σ
1/5
T=temperature in the formula, unit is a ° K, and the t=time, unit is hour, and σ is a stress, and unit is MPa.
Then, determine the yield strength σ of the state of at room temperature degrading according to described degraded parameter
0.2In Fig. 2, listed this numerical value of table 1 alloy.In order to make optimized performance, the yield strength of the parameter of respectively degrading under the room temperature should be high as far as possible.Alloy PW1480 has satisfied this requirement best, it at room temperature the positive lattice dislocation δ between γ-phase and the γ '-phase be+0.58%.In contrast, the positive lattice dislocation δ between alloy CMSX4 γ-phase and the γ '-phase only is-0.24%, is minimum in data of the present invention, and according to the degraded parameter of minimum about 5000hMPa, its yield strength value is minimum.Therefore, this alloy is owing to its degradation property is not suitable for.
Symbol table
σ
0.2Yield strength
The δ lattice dislocation
a
γThe lattice parameter of γ-phase
a
γ 'The lattice parameter of γ ' phase
The D parameter of degrading
The T temperature
The t time
Table 1
| Alloy | Ni | Co | Cr | Al | Ti | Mo | W | Ya | Nb | Hf | B | Zr | C | Re |
| SXIN738 | Residue | 8.5 | 16 | 3.4 | 3.4 | 1.7 | 2.6 | 1.7 | 0.9 | - | - | - | 0.03 | - |
| SXCM247 | Residue | 9.2 | 8.1 | 5.6 | 0.7 | 0.5 | 9.5 | 3.2 | - | 1.4 | 0.015 | 0.015 | 0.07 | - |
| MC2 | Residue | 5 | 8 | 5.0 | 1.5 | 2 | 8 | 6 | - | - | - | - | - | - |
| CMSX2 | Residue | 5 | 8 | 5.6 | 1.0 | 0.6 | 8 | 6 | - | - | - | - | - | - |
| CMSX4 | Residue | 9 | 6.5 | 5.6 | 1.0 | 0.6 | 6 | 6.5 | - | 0.1 | - | - | - | 3 |
| CMSX6 | Residue | 5 | 10 | 4.8 | 4.7 | 3 | - | 2 | - | 0.1 | - | - | - | - |
| PW1480 | Residue | 5 | 10 | 5.0 | 1.5 | - | 4 | 12 | - | - | - | - | - | - |
| SXN5 | | 8 | 7 | 6.2 | - | 2 | 5 | 7 | - | 0.2 | - | - | - | 3 |
Table 1: the chemical constitution of alloy (weight %)
Claims (3)
1. the preparation method of nickel base superalloy, this alloy is by γ-phase and γ '-constitute mutually, be used to make the material bodies of monocrystalline or directional freeze, it is characterized in that, by selecting the component of alloy, make at room temperature to have high as far as possible γ-phase and the anode lattice dislocation δ between γ '-phase, thereby reach the best after the performance that makes γ '-phase volume content be at least 50% Ni-based super superalloy is at room temperature degraded, wherein
δ[％]＝2(a
γ′-a
γ)/(a
γ′+a
γ)
A wherein
γBe the lattice parameter of γ-phase, a
γ 'It is the lattice parameter of γ '-phase.
2. the described method of claim 1 is characterized in that, determines the lattice parameter a of γ-phase according to following known formula
γWith γ ' lattice parameter a mutually
γ ':
a
γ[]＝3.524+0,0196Co+0.110Cr+0.478Mo+0.444W+0.441Re
+0.3125Ru+0.179Al+0.422Ti+0.7Ta+0.7Nb，
Wherein the numeral respective element before the symbol of element the relative atom mark of γ-phase and
a
γ′[]＝3.57-0.004Cr+0.208Mo+0.194W+0.262Re+0.1335Ru
+0.258Ti+0.5Ta+0.46Nb，
Wherein the numeral respective element before the symbol of element is at the relative atom mark of γ '-phase.
3. the described method of claim 1 is characterized in that, in order to characterize the enduring quality of nickel base superalloy, introduces a degraded parameter D who determines according to following formula:
D＝(T-800)t
1/2σ
1/5
T=temperature in the formula, unit is a ° K, and the t=time, unit is hour, and σ is a stress, and unit is MPa, wherein determines yield strength σ after the degraded at room temperature according to said degraded parameter D
0.2, in order to make optimized performance, this numerical value should be high as far as possible.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CH2059/01 | 2001-11-09 | ||
| CH2059/2001 | 2001-11-09 | ||
| CH20592001 | 2001-11-09 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1585829A CN1585829A (en) | 2005-02-23 |
| CN100345990C true CN100345990C (en) | 2007-10-31 |
Family
ID=4567342
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB028222334A Expired - Fee Related CN100345990C (en) | 2001-11-09 | 2002-11-05 | Method for developing a nickel-base super alloy |
Country Status (4)
| Country | Link |
|---|---|
| US (1) | US20040261921A1 (en) |
| EP (1) | EP1451382A1 (en) |
| CN (1) | CN100345990C (en) |
| WO (1) | WO2003040419A1 (en) |
Families Citing this family (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4449337B2 (en) * | 2003-05-09 | 2010-04-14 | 株式会社日立製作所 | High oxidation resistance Ni-base superalloy castings and gas turbine parts |
| WO2007006681A1 (en) * | 2005-07-12 | 2007-01-18 | Alstom Technology Ltd | Ceramic heat insulating layer |
| CN100430500C (en) * | 2005-11-18 | 2008-11-05 | 中国科学院金属研究所 | Third nickel-base high-temperature single crystal alloy in low cost |
| CN100494467C (en) * | 2006-08-16 | 2009-06-03 | 中国科学院金属研究所 | Directional freezing column crystal or single-crystal nickel-base high-temperature alloy repairing or coating method |
| CN100557092C (en) * | 2007-12-17 | 2009-11-04 | 北京航空航天大学 | Adopt the method for seed crystal method and spiral crystal separation method combined preparation Ni based single-crystal high-temperature alloy |
| US9347124B2 (en) * | 2011-11-07 | 2016-05-24 | Siemens Energy, Inc. | Hold and cool process for superalloy joining |
| GB201400352D0 (en) | 2014-01-09 | 2014-02-26 | Rolls Royce Plc | A nickel based alloy composition |
| EP3042973B1 (en) | 2015-01-07 | 2017-08-16 | Rolls-Royce plc | A nickel alloy |
| US9644504B2 (en) * | 2015-03-17 | 2017-05-09 | Caterpillar Inc. | Single crystal engine valve |
| GB2539957B (en) | 2015-07-03 | 2017-12-27 | Rolls Royce Plc | A nickel-base superalloy |
| CN113308654B (en) * | 2020-02-27 | 2022-04-08 | 南京理工大学 | Nickel-based alloy with nano structure and gamma' phase composite structure and preparation method thereof |
| CN112359303B (en) * | 2020-11-09 | 2021-08-24 | 中南大学 | Data-driven nickel-based superalloy strength evaluation method |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1213009A (en) * | 1997-09-26 | 1999-04-07 | 冶金工业部钢铁研究总院 | Antioxidant nickel-base alloy |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6250435A (en) * | 1985-08-29 | 1987-03-05 | Natsuo Yugawa | Phase stability indicating diagram of alloy |
-
2002
- 2002-11-05 WO PCT/IB2002/004619 patent/WO2003040419A1/en not_active Application Discontinuation
- 2002-11-05 EP EP02779820A patent/EP1451382A1/en not_active Withdrawn
- 2002-11-05 CN CNB028222334A patent/CN100345990C/en not_active Expired - Fee Related
-
2004
- 2004-05-05 US US10/838,353 patent/US20040261921A1/en not_active Abandoned
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1213009A (en) * | 1997-09-26 | 1999-04-07 | 冶金工业部钢铁研究总院 | Antioxidant nickel-base alloy |
Non-Patent Citations (1)
| Title |
|---|
| INFLUENCE OF CONPOSITION ON THE MICROSTRUCTURE ANDMECHANICAL PROPERTIES OF A NICKEL-BASE SUPERALLOY SINGLECRYSTAL M.V.NATHAL ET AL,NASA TECH.MEMO.NAS.TM.83563,E.1942,NAS 1.15:83563 1984 * |
Also Published As
| Publication number | Publication date |
|---|---|
| US20040261921A1 (en) | 2004-12-30 |
| CN1585829A (en) | 2005-02-23 |
| EP1451382A1 (en) | 2004-09-01 |
| WO2003040419A1 (en) | 2003-05-15 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN100345990C (en) | Method for developing a nickel-base super alloy | |
| Sato et al. | A 5th generation SC superalloy with balanced high temperature properties and processability | |
| CN102653832B (en) | Directed nickel-base high temperature alloy | |
| EP2503013B1 (en) | Heat-resistant superalloy | |
| EP2778241B1 (en) | Heat-resistant nickel-based superalloy | |
| CN101680059B (en) | Ni-based single crystal superalloy and turbine vane using the same | |
| JP4833227B2 (en) | High heat resistance, high strength Ir-based alloy and manufacturing method thereof | |
| KR101687320B1 (en) | Ni-BASED SINGLE CRYSTAL SUPERALLOY | |
| RU2518838C2 (en) | MONOCRYSTALLINE Ni-BASED SUPERALLOY AND TURBINE BLADE | |
| EP2420584A1 (en) | Nickel-base single-crystal superalloy and turbine wing using same | |
| JP2018515690A (en) | Nickel base alloy | |
| EP2290115B1 (en) | Process of producing turbine blades | |
| CN112575229A (en) | Long-life high-strength hot-corrosion-resistant nickel-based high-temperature alloy and application thereof | |
| JP4523264B2 (en) | Nickel-base superalloy for manufacturing single crystal parts | |
| JPH11246924A (en) | Ni-base single crystal superalloy, its production, and gas turbine parts | |
| JP2002146460A (en) | Nickel based single crystal superalloy, its production method and gas turbine high temperature parts | |
| CN108866387B (en) | High-strength hot-corrosion-resistant nickel-based high-temperature alloy for gas turbine and preparation process and application thereof | |
| JP5393829B2 (en) | Single crystal nickel-base superalloy with improved creep properties | |
| EP1715068B1 (en) | Nickel-based super-heat-resistant alloy and gas turbine component using same | |
| CN114318194B (en) | Nickel-based casting high-temperature alloy, heat treatment method thereof and alloy casting | |
| JP2000239771A (en) | Ni BASE SUPERALLOY, ITS PRODUCTION AND GAS TURBINE PARTS | |
| CN111041278B (en) | Gamma' phase reinforced Co-Ni-Al-Ta-based high-temperature alloy | |
| JPH11246954A (en) | Manufacture of ni-base unidirectionally solidified alloy | |
| Shigeyama et al. | Morphological Changes in γ’Phase by Creep, Aging and Aging After Creep for Polycrystalline Nickel-Based Superalloy | |
| CN117305658A (en) | Nickel-based powder superalloy and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| C17 | Cessation of patent right | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20071031 Termination date: 20121105 |