deformation mechanisms in an advanced disc ni-base superalloy · 2015-02-24 · advanced disc...
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![Page 1: Deformation Mechanisms in an Advanced Disc Ni-base Superalloy · 2015-02-24 · Advanced Disc Ni-base Superalloys E. Knoche¹, B.M.B. Grant¹, M. Daymond², J. Quinta da Fonseca¹,](https://reader030.vdocuments.mx/reader030/viewer/2022040103/5e981af08e9c1a74f2275e60/html5/thumbnails/1.jpg)
Deformation Mechanisms in
Advanced Disc Ni-base
Superalloys
E. Knoche¹, B.M.B. Grant¹, M. Daymond²,
J. Quinta da Fonseca¹, M. Preuss¹
¹University of Manchester, School of Materials, UK
²Dept. of Mechanical and Materials Engineering, Kingston, Ontario, Canada
Acknowledgements: EPSRC/DSTL for providing funding (EP/E020933/1), beam line
scientists at ISIS, Rolls-Royce plc. for providing material
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Material studied RR1000• Polycrystalline nickel based
superalloy for turbine disk
application
• Good creep and fatigue properties
even at elevated temperatures www.firthrixson.com/page.asp?ID=277
• Main strengthening by ordered g’precipitates (close to 50 vol.%)
multimodal size distribution
gNi3Al (L12)
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Objectives
• Microstructure - deformation mechanism relationship poorly
understood
• classical precipitation strengthening mechanisms fail to
provide a full mechanistic understanding
R.C. Reed, The Superalloys - Fundamentals and Applications. 2006, Cambridge University Press.
W. Huether, Zeitschrift fuer Metallkunde, 1978, 69(10), 628-634.
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Methodology
• Deformation mechanisms in polycrystalline nickel-
base Superalloys (RR1000) with high vol.% of g’
studied using simplified model microstructures with unimodal g’ size distribution
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Generating the model microstructures
Coarse g (230 nm)
Medium g (130 nm)
Fine g (90 nm)
-0.1°C/min
20°C
Time
1050°C
800°C
925°C
1h
-1°C/min
Tem
pera
ture
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Tensile tests Yield strength decreases with increasing particle size at all three
test temperatures
20°C
500°C
750°C
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In situ loading
• (100) and (110)
superlattice peaks
required (position and
width) to fit γ+γ’ (200)
and (220) reflections
• we measure the
elastic strain
response of grain
families
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In-situ neutron diffraction
• Elastic lattice strain response of the matrix and precipitate
phase almost identical even in the regime of plastic
deformation
Deformation of g is not possible without deformation of g’
{100/200}
{110/220}
Fine g
tested at 20°C
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In-situ neutron diffraction
• Elastic lattice strain
response identical at
first for g and g
• After certain level of
plastic strain: load
transfer from g to g
• g takes up more
plastic strain than g
Coarse g
Medium g20°C tests
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Load transferTendency for load transfer increases with increasing particle size
and test temperature
a)
c)
b)
Typical error
a)
c)
b)
Typical
error
a)
b)
c)
Typical
error
Coarse gMedium gFine g
20°C
500°C
750°C
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Post-mortem SEM (20°C test)
• Shearing dominates
all three deformed
microstructures
Shearing Shearing
Shearing
Fine g
Medium g
Coarse g
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Localised deformation
• Very fine shear lines in
coarse g microstructure,
but not in fine or medium
g
Deformation less
localisedFine g
Medium g
Coarse g
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TEM results for 500°C tests
Fine g’ RR1000
500°CStrongly coupled dislocations
Shear lines
Results suggest shearing by strongly coupled dislocations as
main deformation mechanism good agreement with
neutron/modelling results suggesting joint deformation of g and g’
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Medium g’ RR1000 500°C
Shear
lines
Bowing of
dislocationsIncreased dislocation
density around precipitates
Neutron/modelling results: g-g’ load
transfer after initial joint deformation
TEM/SEM: shearing
dislocation pile up on
precipitate boundaries
bowing of dislocations
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Coarse g tested at 500°C
• Features comparable to medium
RR1000, but more pronounced
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750°C tests
Fine g
Medium g
Coarse g
Stacking faults in all three microstructures
Extending through both phases in fine g
Mainly restricted to g in medium and coarse
Also increasing pile up of dislocations on
precipitate boundary with increasing particle size
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Conclusions
• Load transfer changes with temperature, level of
plastic strain and gparticle size change in
micromechanisms of deformation
• For fine g:g cannot deform without g post-
mortem microstructures testify uniform
deformation of matrix and precipitates
• For coarser g: deformation of g becomes harder
to deform after initial level of plastic strain load
transfer and less localised deformation
g can deform without g to some extent visible
in TEM images as pile up of dislocations around g
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Thank you