A New Ni-based Superalloy for Oil and Gas Applications

A NEW NI-BASE SUPERALLOY FOR OIL AND GAS APPLICATIONS

Sarwan Mannan and Shailesh Patel Special Metals Corporations, Huntington, WV 25705-1771

Key words: 945, Chemistry, Corrosion, oil and gas, microstructure

Abstract

A new Ni-base precipitation strengthened alloy has been developed to provide 860 MPa minimum yield strength and an excellent combination of ductility and impact strength. Testing in various corrosive environments has shown that the alloy has excellent stress corrosion and sulfide stress corrosion resistance. A number of commercial heats were melted and processed to establish robust mill processing practice. This paper will talk about the overall alloy development methodology including heat treatment studies to optimize microstructure and target mechanical and corrosion properties to obtain the most cost effective solution to the needs of the oil and gas (O&G) industry.

Introduction As older shallow and less corrosive O&G wells deplete, higher strength and more corrosion resistant materials are needed to enable deeper drilling into more corrosive environments. The commonly used Ni-base superalloys 718 and 925 do not always offer an adequate combination of strength and corrosion resistance hence the need to develop a new alloy. Material selection is especially critical for sour gas wells -- those containing H2S [1,2]. These wells operate at a high temperature of up to 232C and may also contain free sulfur. Additionally, these wells generally contain high levels of chlorides and CO2. Combinations of this type of corrosive media require special care when designing an alloy. Nominal composition of newly developed alloy 945 is Fe-47Ni-20.5Cr-3Mo-2Cu-3Nb-1.5Ti. The relative concentrations of Fe-Ni-Cr-Mo-Cu determine overall corrosion resistance in O&G applications. A minimum of 42Ni is needed for aqueous stress corrosion cracking [3]. Molybdenum is beneficial for pitting corrosion resistant in reducing acids and alkalies [4]. Chromium improves general corrosion resistance and corrosion resistance in oxidizing media [4]. High concentrations of Mo and Cr lead to structural instability [5]. Copper is found to be beneficial for general corrosion in non-oxidizing corrosion environments. A synergistic affect of Cu and Mo is recognized for countering

corrosion in reducing acidic environments which are rich in chlorides [6]. Nb, Ti, and Al are of course added for precipitation strengthening [7]. Data in the literature shows that alloy 925 has superior corrosion resistance to alloy 718 in certain oil patch environments [8]. However, the yield strength capability of alloy 925 is lower than alloy 718 [9]. The aim of the project was to develop a cost effective hybrid of alloys 925 and 718, which has best of both the alloys -- higher strength capability and excellent corrosion resistance.

Laboratory Alloy Development The initial development phase consisted of vacuum induction melting 22Kg lab heats. These heats were homogenized, hot-rolled, and subjected to annealing and aging studies. First phase of evaluation of laboratory heats was done based on microstructure and hardness of annealed plus aged material. The heats that showed potential were tested for tensile, impact, hardness, and microstructure. To begin with, a thermodynamics based software, JMatPro [10], was used to simulate some of the potential chemical compositions. This software predicts variation of strength with chemical composition. However, it does not give any guidance for inter-granular microstructure. Over 100 lab heats were evaluated in this program. Table 1 shows selected lab heats listed to illustrate the observed trends. Effect of Ti Ti in alloy 925 composition was varied from 2.5 to 3.4 wt% as shown in heats S2-A to S2-C in Table 1. An increase in Ti showed a lot of potential to strengthen the alloys. A plot of hardness versus Ti content is shown in Figure 1. The hardness increased rapidly as Ti content was increased. However, increase in Ti also degraded microstructural stability. Cellular inter-granular Eta phase colonies were observed on age hardening, Figure 2. Based on the limited data reported in the literature, any inter-granular second phase precipitation is likely to degrade corrosion resistance in O&G applications [9].

31

Table 1. Chemical compositions of the lab heats

Alloy Fe Ni Cr Mo Cu C Al Nb Ti Alloy 925

Bal 42.3 20.3 3.2 2.0 0.014 0.2 0.3 2.3

Alloy 718

Bal 54 18.5 3.2 - 0.015 0.5 5.0 1.0

S2-A Bal 42.5 20.6 3.4 1.7 0.013 0.4 0.3 2.5 S2-B Bal 42.5 20.8 3.4 2.1 0.015 0.4 0.3 3.0 S2-C Bal 42.8 20.4 3.4 1.8 0.021 0.4 0.3 3.4

S3-A Bal 45.0 20.6 3.2 2.0 0.006 0.6 0.3 2.3 S3-B Bal 48.0 20.5 3.2 2.0 0.005 1.2 0.3 2.3

S4-A Bal 45.5 20.5 3.3 2.0 0.009 1.0 1.0 2.3 S4-B Bal 48.8 20.5 3.3 2.1 0.008 1.0 1.0 2.3

Figure 1. Hardness versus Ti content of S2 series of alloys.

Figure 2. Optical photograph of annealed plus aged S2-C alloy containing 3.4Ti.

Effect of Al Aluminum in the base alloy 925 composition was varied from 0.3 to 1.2 wt% in S3 heats as shown in Table 1. Interestingly, an increase in Al from 0.3 to 0.6 decreased hardness, Figure 3. However, with 1.2Al, the hardness was equivalent to that of 0.3Al. The lower hardness of 1.2Al alloy as compared to 0.6Al alloy in the plot for 24 hours exposure is probably due to over-aging. An increase in Al increases the volume fraction of gamma prime [7], which increases hardness. Further, an increase in Al is also thought to decreases the lattice mismatch / coherency strain [7], which decreases hardness. The observed variations in hardness with Al are combined effects of these two factors. An addition of 1.2Al led to higher inter-granular carbide precipitation, which is detrimental for O&G type aqueous corrosion applications [9]. Based on this data, higher additions than 1.2Al were not studied.

Figure 3. Hardness versus age hardening time at 718C for S3

alloys.

20

25

30

35

5 10 15 20 25Age Hardening Time at 718C

Roc

kwel

l Har

dnes

s, R

c

0.6Al

1.2Al

0.3Al

Age Hardening at 704C for 24h

25

30

35

40

2 2.5 3 3.5Ti Content, wt%

Har

dnes

s, R

c

32

Relationship between Nb and Al Increase in both Al and Nb in alloy 925 increased hardness but marginally decreased yield strength as shown for S4 heats in Table 1 and 2. This is contrary to JMatPro simulations, which suggest an increase in yield strength with this combination of hardeners, Table 2. An increase in hardness but a decrease in yield strength can be misleading because hardness values are typically used as an initial screen during alloys development. Increase in hardness in this set of heats did however increase tensile strength, which is consistent with reported literature, where hardness is correlated to the tensile strength for steel, [11]. These results indicated that increasing Al beyond the levels in alloy 925 would not be beneficial in the new alloy.

Relationship between Nb and Ti Once the behavior and optimum level of Al was determined in the alloy, the synergies between Nb and Ti were studied. JMatPro showed that an increase in Nb together with a decrease in Ti in alloy 925 is required to increase strength, Figure 4. Based on this information, a number of lab heats were prepared to study the Nb / Ti effect. The experimental results on yield strength were consistent with JMatPro simulations. Further, these synergistic variations in Nb and Ti resulted in a microstructure, which was essentially devoid of any inter-granular precipitation. A number of lab heats were evaluated for further processing and properties to optimize the final chemical composition of alloy 945 listed in Table 3.

Table 2. Room temperature yield strength of annealed plus two-step aged S4 heats. YS, UTS, EL, and RA stand for yield strength, tensile strength, elongation, and reduction-of-area respectively.

Alloy Hardness, Rc JMatPro predicted

YS, ksi YS, ksi UTS, ksi % El % RA

925 34 82 118 173 23 27 S4-A 38 96 112 183 25 25 S4-B 38 99 109 180 26 39

Figure 4. JMatPro simulations showing synergistic increase in Nb and decrease in Ti result in increase in Gamma double prime (upper plot) and increase in yield strength (lower plot).

N b / T i C o n t e n t s vs G a m m a D o u b le p r im e o f a F e -N i-C r A l lo y

00 . 5

11 . 5

22 . 5

33 . 5

4

1 2 3 4 5 6

D a ta p o in ts

Nb

and

Ti w

t%

0

1

2

3

4

5

6

Gam

ma

doub

le

prim

e, w

t%N b T i G a m m a d o u b le p r im e

N b / T i C o n t e n t s vs Y ie ld S t re n g t h o f F e -N i-C r A l lo y

00 . 5

11 . 5

22 . 5

33 . 5

4

1 2 3 4 5 6

D a ta p o in t

Nb/

Ti C

onte

nts

9 0

1 0 0

1 1 0

1 2 0

1 3 0

1 4 0

YS, k

si

N b T i Y S

33

Results and Discussion on Mill Scale Heats

Processing An optimized composition of alloy 945 was melted and re-melted in the mill as three commercial heats weighing 22000 to 32,000 kg each. Although a number of variations in electrode / ingots sizes were evaluated, the most common sizes used were 457mm electrode re-melting to 508mm ingot. Melting processes evaluated were vacuum induction melting (VIM) and electric arc furnace (EAF) + argon oxygen decarburization (AOD). The melted electrodes were re-melted using vacuum arc re-melting (VAR) and electroslag re-melting (ESR). The alloy has proved to be process friendly to all the various combinations of primary and secondary melt methods. Figure 5 shows a 508mm VIM +VAR ingot. The ingots produced by various melt methods were rolled or forged to round bars. Figure 6 shows a 229mm diameter forged bar weighing 2300Kg. Hot rolled bars were annealed at 1038C for times according to the section sizes and water quenched. Then, the material was two step aged as follows: 718C/8h, furnace cool at 56C/h to 621C, hold at 621C/8h, air cool.

Figure 5. VIM + VAR ingot of 508mm diameter.

Table 3. Nominal chemical compositions 925, 945, and 718.

Alloy Fe Ni Cr Mo Cu C Al Nb Ti

925 Bal 42.3 20.3 3.2 2.0 0.014 0.2 0.3 2.3

945 Bal 47 20.5 3.3 2.0 0.010 0.2 3.0 1.5

718 Bal 54 18.5 3.2 - 0.015 0.5 5.0 1.0

34

Figure 6. A forged bar of 229mm diameter weighing 2300kg.

Mechanical Properties Rod sizes of diameter ranging from 25mm to 356mm were produced and tested for room temperature tensile, grain size, hardness, and Charpy impact testing. The impact testing was conducted at 23C. Impact tests for rod diameters 76mm or less were conducted in the longitudinal orientation, whereas for over 76mm, the tests were conducted in the transverse orientation.

All the tensile testing was done in the longitudinal orientation. Table 4 shows the mechanical properties. The impact values listed are the averages of 3 tests. Being the first scale up heats for the alloy, multiple testing was conducted at extreme ends of a bar or on different bars produced in a lot to ensure uniformity in the material. The listed multiple values for selected sizes represent data generated in this way. The alloy clearly met the target mechanical properties.

Table 4. Mechanical properties of annealed + aged alloy 945. YS, UTS, EL, and RA stand for yield strength,

tensile strength, elongation, and reduction-of-area respectively.

Rod Size, mm

YS, MPa UTS, MPa % El % RA Impact, Joules

Hardness, Rc Grain Size, ASTM #

25 919.8 939.1

1194.2 1205.2

27.8 26.1

48.0 46.1

103 85

40 40

2 3

51 913.6 942.5

1173.5 1201.8

28.2 25.7

47.6 40.1

95 75

40 40

3 3

89 939.8 934.3

1201.1 1185.9

24.9 25.5

39.5 40.5

77 79

40 43

2 2

114 925.3 929.5

1162.5 1171.5

28.6 26.6

46.7 45.6

84 84

42 39

2.5 2

152 957.0 972.2

1183.9 1213.5

23.7 22.0

35.9 34.6

92 75

40 42

2 2.5

305 981.2 1183.9 26.3 43.6 83 40 2 356 967.4 1167 26.6 30.7 105 39 2

Min Target 862 1034 18 25 54 - ASTM #2 or finer

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Microstructure

An etchant containing one percent bromine in methanol was found to be suitable to reveal the microstructure of alloy 945. An optical photomicrograph revealing single phase, twinned, equi-

axed microstructure is shown in Figure 7. The age hardening treatment precipitates sub-micron Ni3(TiAl)-type gamma prime and Ni3(NbTi)-type gamma double prime phases, which are responsible for the higher strength, Figure 8.

x

Figure 7. Optical photographs of alloy 945, Magnification = 100X.

.05 m

Figure 8. TEM photographs of alloy 945. The left shows gamma prime and gamma double prime distribution and the right shows selected area diffraction pattern of these phases in [001] zone axis.

100 m

36

Corrosion Resistance Stress Corrosion Cracking (SCC): Corrosion testing in MR0175 / ISO 15156-3 [12] NACE (National Association of Corrosion Engineers) level V and level VI was carried out on triplicate C-ring specimens for 90 days on three mill heats at 100% of actual yield strength. Testing was done in accordance with NACE TM0177-2004, method C - C Ring tests. In these tests, stressed C-ring specimens were enclosed in a pressurized autoclave under specified partial pressure of gasses. The specimens were immersed in a solution containing specified chloride content at a fixed temperature. The tests were run for 90 days and the specimens were examined with 20X magnifier for cracking after the test. No cracking was observed, Tables 5 and 6. Specimen dimensions were: 51mm OD, 3.8mm wall-thickness and 24.1mm width. Figure 9 shows a C-ring test specimen.

Table 5. C-ring test results in NACE level V. The environment was 700 kPa H2S, 700 kPa CO2, 91000 mg/l Cl at 150C.

Applied stress was 100% of room temperature yield strength.

Sample Applied Stress, MPa

Results

EX0019PY-12 (1) 920 No failure, 90 days EX0019PY-12 (2) 920 No failure, 90 days EX0019PY-12 (3) 920 No failure, 90 days


EX0021PK-11 (1) 972 No failure, 90 days EX0021PK-11 (2) 972 No failure, 90 days EX0021PK-11 (3) 972 No failure, 90 days

Figure 9. Photograph of a C-ring test specimen.

Table 6. C-ring test results in NACE level VI. The environment

was 3500 kPa H2S, 3500 kPa CO2, 121300 mg/l Cl at 175. Applied stress was 100% of room temperature yield strength.

Sample Applied Stress,

MPa Results

EX0019PY-12 (1) 920 No failure, 90 days



EX0019PY-11 (1) 925 No failure, 90

days EX0019PY-11 (2) 925 No failure, 90

days EX0019PY-11 (3) 925 No failure, 90

days

EX0021PK-11 (1) 972 No failure, 90 days



37

Galvanically induced Hydrogen Stress Cracking (GHSC): To fulfill NACE MR0175 / ISO 15156-3: 2003 acceptance procedure, triplicate samples of three heats of alloy 945 were tested for 30 days with 90 % of the actual yield strength in acidified NACE solution A at 24C. Testing was carried out in accordance with TM0177 - 2004, method A Tensile tests. Samples were nominally of diameter 3.8mm and gauge length 25.4mm. The samples were coupled to carbon steel via the stressing bolts. No failures were detected, Table 7.

Table 7. Test results on triplicate samples for GHSC.

Sample Applied

Stress, MPa Results




Sulfide Stress Cracking (SSC): Sulfide stress corrosion cracking testing was done on triplicate samples of three heats in acidified NACE solution A at 24C for 30 days using method A (tensile test) in accordance with TM0177-2004. The samples were stressed to 90% of the actual yield strength. Samples were nominally of diameter 3.8mm and gauge length 25.4mm. No failures were detected, Table 8.

Table 8. Test results on triplicate samples for SSC.

Sample Applied

Stress, MPa Results




Applications

Mechanical properties and corrosion resistance of alloy 945 shown in the publication makes it suitable for use in O&G applications for hangers, packers, valve stems and tubulars used in wellhead, downhole equipments, christmas tree, and side pocket mandrels. Figure 10 shows wellhead used for above ground pressure control.

Figure 10. Photograph of a wellhead used for above ground pressure control.

Summary and Conclusion

A new alloy named INCOLOY* alloy 945 has been developed for O&G applications using JMatPro simulations and multiple iteration of 22 Kg lab heats. This alloy was scaled up to three 22, 000 to 32,000 Kg mill heats and rolled / forged to 25mm - 356mm diameter rods. Annealed + aged material was tested for mechanical and corrosion properties. The data shows that the material is capable of 860 MPa minimum yield strength with excellent ductility and toughness. The alloy passed complete set of corrosion testing required to qualify for NACE approval as per MR0175 / ISO 15156-3. This included SCC in NACE level VI, GHSC, and SSC corrosion testing.

* INCOLOY is a Trade Mark of Special Metals Corporation

38

References 1. Bruce D. Craig, Selection guidelines for corrosion resistant

alloys in the oil and gas industry, NiDI Technical Series No 10073, pp. 1-8, July 1995.

2. E. L. Hibner and C. S. Tassen, Corrosion Resistant OCTGs and Matching Age-Hardenable Bar Products for a Range of Sour Gas Service Conditions, Corrosion 2001, Paper No 1102, NACE International, Houston, Texas.

3. H. R. Copson, Effect of Composition on Stress Corrosion Cracking of Some Alloys Containing Nickel, published in the, Physical Metallurgy of Stress Corrosion Fatigue, Edited by T. Rhodin, pp. 247-269, Interscience Publishers, NY, 1959.

4. R. C. Scarberry, D. L. Graver, and C. D. Stephens, Alloying for Corrosion Control, Materials Protection, Vol. 6, No. 6, pp. 54-57, 1967.

5. S. T. Wlodek, Long Term Stability of High Temperature Materials, Edited by G. E. Fuchs, K. A. Dannemann, and T. C. Deragon, pp. 1-30, TMS, 1999.

6. J. Montagnon, USA Patent No. 6,004,408, dated Dec 21, 1999.

7. R. F. Decker, Strengthening Mechanisms in Nickel-Base Superalloys, Presented at Steel Strengthening Mechanisms Symposium, Zurich, Switzerland, May 5-6, 1969.

8. R. B. Bhavsar and E. L. Hibner, Evaluation of Corrosion Testing Techniques for Selection of Corrosion Resistant Alloys for Sour Gas Service, Corrosion 1996, Paper No. 59, NACE International, Houston, Texas.

9. S. K Mannan, E. L. Hibner, B. C. Puckett, Physical Metallurgy of Alloys 718, 725, 725HS, and 925 for Service in Aggressive Corrosive Environments, Corrosion 2003, Paper No. 3126, NACE International, Houston, Texas..

10. N. Saunders, Z. Guo, A. P. Miodownik, and J-Ph. Schille, Modeling the Material Properties and Behavior of Ni-and NiFe-Based Superalloys, Superalloys 718, 625, 706 and Derivatives, Edited by E. A. Loria, TMS, 2005.

11. M. C. Meyers and K. K. Chawala, Mechanical Metallurgy ((Prentice-Hall Inc., Englewood Cliffs, New Jersey, 1984), page 602-603.

12. Petroleum and Natural gas industries Materials for use in H2S-containing environments in oil and gas production, International Standard Part 3, NACE MR0175 / ISO 15156-3, first Edition, 2003-12-15.

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WelcomeRelated PublicationsCopyright InformationPrefaceDedicationBest Paper AwardCommittee MembersTable of ContentsSuperalloys 2008Symposium Keynote AddressChallenges for High Temperature Materials in the New Millennium

Latest Advances in Alloy Development INASA and Superalloys: A Customer, a Participant, and a RefereeDevelopment of a New Fatigue and Creep Resistant PM Nickel-Base Superalloy for Disk ApplicationsA New Ni-Base Superalloy for Oil and Gas ApplicationsStructure Control of a New-Type High-Cr Superalloy

Interactive Session A: Alloy DevelopmentDevelopment of Ni-Co-Base Alloys for High-Temperature Disk ApplicationsThe Microstructure and Mechanical Properties of EP741NP Powder Metallurgy Disc MaterialEffects of a Tantalum Addition on the Morphological and Compositional Evolution of a Model Ni-Al-Cr SuperalloyLinking the Properties, Processing and Chemistry of Advanced Single Crystal Ni-Base SuperalloysEffect of Ruthenium on Microstructure and Stress Rupture Properties of a Single Crystal Nickel-Base SuperalloyOptimizing SC Ren N4 Alloy for DS Aft-Stage Bucket Applications in Industrial Gas TurbinesThe Influence of Ruthenium and Rhenium on the Local Properties of the gamma- and gamma'-Phase in Nickel-Base Superalloys and Their Consequences for Alloy BehaviorThe Effects of Heat Treatment and Microstructure Variations on Disk Superalloy Properties at High TemperatureA 5th Generation SC Superalloy with Balanced High Temperature Properties and ProcessabilityP/M Alloy 10 - A 700C Capable Nickel-Based Superalloy for Turbine Disk ApplicationsThe Effect of Composition, Misfit, and Heat Treatment on the Primary Creep Behavior of Single Crystal Nickel Base Superalloys PWA 1480 and PWA 1484Influence of the gamma' Fraction on the gamma/gamma' Topological Inversion during High Temperature Creep of Single Crystal Superalloys

Latest Advances in Alloy Development IIEvaluation of Ruthenium-Bearing Single Crystal Superalloys - A Design of ExperimentsDevelopment of High Temperature Capability P/M Disk SuperalloysDevelopment of a Fabricable Gamma Prime Strengthened SuperalloyElevated Temperature Mechanical Behavior of New Low CTE Superalloys

Latest Advances in Processing INew Boron and Silicon Free Single Crystal-Diffusion Brazing AlloysCreep-Fatigue and Thermo-Mechanical Fatigue of Friction-Welded IN 718/MarM247 Dissimilar JointGas Turbine Blade Made of FG75-Investment Casting Technology for Complex, Hollow, Fibre-Reinforced NiAl-Components

Interactive Session B: Advances in ProcessingA Study of HAZ Microfissuring in a Newly Developed Allvac 718 Plus SuperalloyAdvancement in Fast Epitaxial High Temperature Brazing of Single Crystalline Nickel Based SuperalloysAn Analysis of Solidification Path in the Ni-Base Superalloy, CMSX10KPost-Fabrication Vapor Phase Strengthening of a Nickel-Based Sheet Alloy for Thermostructural PanelsSolute Redistribution during Planar and Dendritic Growth of Directionally Solidified Ni-Base Superalloy CMSX-10The Effects of Withdrawal and Melt Overheating Histories on the Microstructure of a Nickel-Based Single Crystal SuperalloyInfluence of TLP Bonding on Creep Deformation of a Nickel-Base Single Crystal Superalloy at High TemperatureDesign of Solutionizing Heat Treatments for an Experimental Single Crystal SuperalloysEffect of Cooling Rate on Gleeble Hot Ductility of UDIMET Alloy 720 BilletCompetitive Grain Growth in Directional Solidification of a Nickel-Base SuperalloySevere Thermomechanical Processing as an Effective Method for Preparation of Bulk and Sheet Nanostructured Semifinished Products from Nickel Alloys 718 and 718plusInvestigation of the Partition Coefficient in the Ni-Fe-Nb Alloys: A Thermodynamic and Experimental ApproachEffect of Thermal History on the Properties and Microstructure of a Large HIPed PM Superalloy Billet

Latest Advances in Processing IIProcess Development and Microstructure and Mechanical Property Evaluation of a Dual Microstructure Heat Treated Advanced Nickel Disc AlloyA Statistical Analysis of Variations in Hot Tear Performance and Microporosity Formation Versus Composition in Investment Cast FSX-414Grain Selection during Solidification in Spiral Grain Selector

Microdeformation and Macroscopic Properties IDeformation Mechanisms in Ni-Base Disk Superalloys at Higher TemperaturesGrain Boundary and Intragranular Deformations during High Temperature Creep of a PM Nickel-Based SuperalloyGrain Scale Straining Processes during High Temperature Compression of a PM Disk AlloyThe Effect of gamma' Particle Size on the Deformation Mechanism in an Advanced Polycrystalline Nickel-BaseSuperalloy

Interactive Session C: Physical MetallurgySurface Effects on Low Cycle Fatigue Behavior in IN718 AlloyThe Characterisation and Prediction of LCF Behaviour in Nickel Single Crystal Blade AlloysTension/Compression Asymmetry in Yield and Creep Strengths of Ni-Based SuperalloysEffects of Low Angle Boundaries on the Mechanical Properties of Single Crystal Superalloy DD6High Temperature Creep of Directionally Solidified Ni Base Superalloys Containing Local RecrystallizationThe Effect of Thermomechanical Processing on the Microstructure and Creep Behavior of Udimet Alloy 188Failure Analysis of Weld-Repaired B-1900 Turbine Blade ShroudsHigh Temperature Microstructural Degradation of Haynes Alloy 230The Effect of Carbide Morphologies on Elevated Temperature Tensile and Fatigue Behavior of a Modified Single Crystal Ni-Base SuperalloyGamma Prime Morphology and Creep Properties of Nickel Base Superalloys with Platinum Group Metal AdditionsElevated-Temperature Creep-Fatigue Crack-Growth Behavior of Nickel-Based HAYNES R-41, HAYNES 230 and HASTELLOY X AlloysA New Hyperbolic Tangent Modelling Approach for the Creep Behavior of the Single Crystal Nickel-Based Superalloy CMSX4Assessment on the Thermo-Mechanical Fatigue Properties of 98 Ni-Base Single Crystal SuperalloysComparison of Low Cycle (Notch) Fatigue Behaviour at Temperature in Single Crystal Turbine Blade MaterialsFatigue Behavior in Monocrystalline Ni-Based Superalloys for Blade ApplicationsMicrostructural Conditions Contributing to Fatigue Variability in P/M Nickel-Base SuperalloysA TEM Investigation on Precipitation Behavior of AEREX350 SuperalloyElastic Microstrains during Tension and Creep of Superalloys: Results from In Situ Neutron Diffraction

Microdeformation and Macroscopic Properties IIMean vs. Life-Limiting Fatigue Behavior of a Nickel Based SuperalloyAssessment of Lifetime Calculation of Forged IN718 Aerospace Components Based on a Multi-Parametric Microstructural EvaluationEvaluation of the Influence of Grain Structure on the Fatigue Variability of WaspaloyFatigue Crack Initiation in Nickel-Based Superalloy Ren 88 DT at 593C

Coatings and Environmental Effects ISuperalloys for Ultra Supercritical Steam TurbinesOxidation BehaviorEffects of Oxidation and Hot Corrosion in a Nickel Disc AlloyDevelopment of Si-Bearing 4th Generation Ni-Base Single Crystal SuperalloysThe Development and Performance of Novel Pt+Hf-Modified gamma'-Ni3Al+gamma-Ni Bond Coatings for Advanced Thermal Barrier Coatings Systems

Interactive Session D: Coatings, Environmental/Microstructural DegradationThe Performance of Pt-Modified Alumina-Forming Coatings and Model AlloysOxidation of MCrAlY Coatings on Ni-Based SuperalloysOxidation and Coating Evolution in Aluminized Fourth Generation Blade AlloysD5, Formation of gamma'-Ni3Al via the Peritectiod Reaction: gamma; + beta (+ Al2O3) = gamma' (+ Al2O3)Analysis of Surface Chemical Contamination on Ex-Service Industrial Gas Turbine ComponentsLong-Term Cyclic-Oxidation Behavior of Selected High Temperature AlloysHigh Temperature Corrosion Behavior of DS GTD-111 in Oxidizing and Sulfidizing EnvironmentsThe Influence of Hot-Deformation Parameters on the Mechanical Properties and Precipitation Process in Nickel Based SuperalloyCreep Behavior of Thick and Thin Walled Structures of a Single-Crystal Nickel-Base Superalloy at High Temperatures Experimental Method and ResultsMicrostructural Degradation of CMSX-4: Kinetics and Effect on Mechanical PropertiesLong Term Coarsening of Ren 80 Ni-Base SuperalloyTemperature and Dwell Dependence of Fatigue Crack Propagation in Various Heat Treated Turbine Disc Alloys

Coatings and Environmental Effects IIDevelopment of Improved Bond Coat for Enhanced Turbine DurabilityEQ Coating: A New Concept for SRZ-Free Coating SystemsAn Investigation of the Compatibility of Nickel-Based Single Crystal Superalloys with Thermal Barrier Coating SystemsSecondary Reaction Zones in Coated 4th Generation Ni-Based Blade Alloys

High Temperature Behavior IThermal Stability Characterization of Ni-Base ATI 718Plus SuperalloyThe Precipitation and Strengthening Behavior of Ni2(Mo,Cr) in HASTELLOY C-22HS Alloy, a Newly Developed High Molybdenum Ni-Base SuperalloyEffect of Microstructure on Time Dependent Fatigue Crack Growth Behavior in a P/M Turbine Disk Alloy

Interactive Session E: Modelling, Simulation and ValidationPhase-Field Modeling of gamma' Precipitation in Multi-Component Ni-Base SuperalloysEvolution of Size and Morphology of gamma' Precipitates in UDIMET 720 Li during Continuous CoolingQuantitative Characterization of Features Affecting Crack Path in a Directionally Solidified SuperalloyModeling Topologically Close-Packed Phases in Superalloys: Valence-Dependent Bond-Order Potentials Based on Ab-Initio CalculationsMicrostructure Modeling of the Dynamic Recrystallization Kinetics during Turbine Disc Forging of the Nickel Based Superalloy Allvac 718 PlusHigh Temperature Nanoindentation of Ni-Base SuperalloysA New Analytical Method of gamma/gamma' Morphology in Single Crystal Ni-Base Superalloys: For New Orientation of Damage and Remaining Life AssessmentCharacterization of Three-Dimensional Dendritic Structures in Nickel-Base Single Crystals for Investigation of Defect Formation

High Temperature Behavior IIAtom Probe Tomography Analysis of Possible Rhenium Clustering in Nickel-Based SuperalloysDesigning of High-Rhemium Single Cristal Ni-Based Supealloy for Gas Turbine BladesNumerical Modelling of Creep Deformation in a CMSX-4 Single Crystal Superalloy Turbine Blade

Modeling, Simulation and Validation IPrecipitation Model Validation in 3rd Generation Aeroturbine Disc AlloysA Modeling Tool for the Precipitation Simulations of Superalloys during Heat TreatmentsNon-Isothermal Creep Behavior of a Second Generation Ni-Based Single Crystal Superalloy: Experimental Characterization and ModelingDevelopment of a Simulation Approach to Microstructure Evolution during Solidification and Homogenisation Using the Phase Field Method

Modeling, Simulation and Validation IIA Coupled Creep Plasticity Model for Residual Stress Relaxation of a Shot Peened Nickel-Base SuperalloyIntegration of Simulations and Experiments for Modeling Superalloy Grain GrowthPolycrystalline Modelling of Udimet 720 ForgingStudies on Alloying Element Partitioning in DMS4 Nickel Base Superalloy Using Monte Carlo Simulations and 3D Atom Probe

Author IndexSubject IndexAlloys IndexPrintSearchExit

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A New Ni-based Superalloy for Oil and Gas Applications

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