Issues for the life prediction of Ceramic Matrix Composite components Jacques Lamon LMT, CNRS/ENS/Paris-Saclay University, France [email protected] C a c h a n
Issues for the life prediction of
Ceramic Matrix Composite
components
Jacques Lamon
LMT, CNRS/ENS/Paris-Saclay University, France
C a c h a n
Summary
• CMCs are of interest to thermostructural applications.
• They were developed initially for military and aerospace applications.
• Effort on CMCs in France started in the seventies
• They have now a high level of technological development.
• The issues have moved from processing methods and basic characteristics to issues relative to resistance to high temperatures and aggressive environments, life of material and components, predictive models and simulation.
• Predictions and control of life are fundamental issues for safe introduction and reliable use of Ceramic Matrix Composites (CMCs) in industrial systems running at high temperature or in aggressive environments.
- Applications
- Some exceptional properties of CMCs: Features of fast fracture Features of delayed fracture at high temperature
- Significance of microstructure/properties relationships
- Multiscale Modeling for lifetime prediction and composite design by tailoring properties to service conditions
Summary
4
Issue : lifetime control and prediction
for long term applications
APPLICATIONS
Ceramic Matrix Composites (CMC) : FIBRES + Interphase + MATRIX
(SiC, C) (SiC, C) (PyC, BN)
High temperature structural applications • Space and Defence • Aeronautical applications • Nuclear reactors
Gas Fast Reactor
Composite Ceramics
Fuel Element Core Lay-out
Core VesselGFR Core Vessel
NUCLEAR POWER PLANTS
Fuel cladding Control rods (SiC/SiC)
CERAMIC MATRIX COMPOSITES
CMC continuous fiber reinforced ceramics display remarkable properties
- resistance to high temperature
- resistance to high temperature fatigue
- versatile stiffness
- damage tolerance
- crack arrest capability
- decreased flaw sensitivity
- quite infinite toughness/notch insensitivity
- reliability
- versatility
400
300
200
100
00.2 0.4 0.6 0.8 1.0
2D-C/C
2D-SiC/SiCcvi
2D-SiC/CAS
2D-SiC/C
STRAIN (%)
STRE
SS (
MPa
)
(after A. G. Evans)
Tensile behavior: influence of Young’s modulus contrast
VERSATILITY of CMCs
macropore
longitudinal tow
transverse tow
layer
0.5mm
2D woven SiC/SiC microstructure
Matrix damage and tensile behavior
Microstructure – damage – behavior relationship
(Guillaumat, Lamon, 1993)
E f .V f
2.E 0
0.0
0.2
0.4
0.6
0.8
1.0
1.2
0.0 0.2 0.4 0.6 0.8 1.0
E
/ E
0
Strain (%)
G D
A
F
DAMAGE: Load transfer from matrix to fibers during
matrix damage in 2D woven SiC/SiC
A: Ni/(PyC20/SiC50)10/SiC
D: Ni/PyC100/SiC
F: Hi-Ni/(PyC20/SiC50)10/SiC
G: Hi-Ni/(PyC100/SiC
RELATIVE YOUNG’S MODULUS
TOP DOWN PROCESS
load
fibre
matrix
matrix crack
load
debonded
zone
fibre/matrix
interfacial shear
bonded
zone
bonded
zone
load
fibre
matrix
matrix crack
load
debonded
zone
fibre/matrix
interfacial shear
bonded
zone
bonded
zone
(Bertrand, Pailler, Lamon, 2001)
Tensile strength of composite
sTS = VL stow
Tensile strength of tow
Predictions for 2D Nicalon / SiC composites
Nt = 500 aC = 0.17 VL 0.2 Rf = 7.5 mm
tow 2
t C f
F=
N 1 Rs
a
Minimum Tow strength
F(N)
Composite strength
sTS (MPa)
ELS 90 245
LLS 70 190
RLLS (br = 0.35) 40 109
RLLS (br = 1) 25 68
Tensile strength: tow – controlled fracture of 2D composite
Strength density functions for SiC fibers (NLM 202), SiC fiber tows,
SiC/SiC (1D) minicomposites and 2D SiC/SiC composites
0
0.002
0.004
0.006
0.008
0.01
0.012
0 500 1000 1500 2000 2500 Stress (MPa)
Density (
1/M
Pa)
Fibers
Tows
Composites (1D)
Composites (2D)
Reliability: Ultimate failure of CMCs:
from single filaments to woven composites
(Calard, Lamon, 2002)
Reliability: Ultimate failure of CMCs:
statistical distributions of failure strengths
limited effects of stress-state s3p / sR 1.15
(Calard, Lamon, 2002)
Ultimate failure of filaments and multifilament tows
Tensile behavior Damage mode Statistical distribution
[Calard, Lamon, 1996]
Flaw-induced stochastic process
Matrix fragmentation in CMCs
[Calard, Lamon, 1998] [Lebrun, Lamon, 1996]
Matrix damage: Fragment dichotomy based model
Strength data have Weibulll distribution
i
i
V
m
Vrup dV
VP
00
1exp1
s
s
Fragment volume (equivalent to length li ) is a statistical variable such as
ii lSV
di
dx
ll
lxP
2)(
ldi ldi ldi ldi
ldi 2li-ldi 2li x
sm
fragment i
0
2li
Stress-state in fragment i
Fibre
(Lissart, Lamon, 1997, 2009, 2010)
Prediction of composite tensile behavior
0
50
100
150
200
250
0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.8
Déformation(%)
Fo
rce
(N)
expérience
simulation
Longueur du minicomposite : 25.04
tau = 84 MPa
Vf = 0.4
Em = 400 GPa
Ef = 300 GPa
mm=5.03
mf=4.2
S0m=5.7 MPa
S0f=6 MPa
Srf=0 MPa
nombre de fibres : 500
rayon des fibres : 7 microns
Tow damage mode
[Pailler, Lamon, 2004]
Matrix damage mode
Resistance to crack propagation
C/C and C/SiC are notch insensitive
SiC/SiC may be notch insensitive
2D woven SiC/SiC fabricated
By polymer conversion process
(Kagawa, Goto (1997))
0
0.2
0.4
0.6
0.8
1
0 0.2 0.4 0.6 0.8 1
sR/sR(a=0)
a/w
without Fatigue
after Fatigue at450°C
0
0.2
0.4
0.6
0.8
1
0 0.2 0.4 0.6 0.8 1
sR/sR(a=0)
a/w
this study
Damage sensitivity
Notch insensitivity: sR = sR (a=0).(1-a/w)
a= diameter of equivalent hole
Residual strength after static fatigue
Post impact tensile strength
w
a s = F/(w-a)b
Resistance to crack propagation
Fracture toughness:
Material property which characterizes
the initiation of fracture from a sharp crack
(obtained by fatigue cracking under plane
Strain conditions)
2D SiC/SiC composites
(Droillard, Lamon, 1996)
Mechanical loads
Matrix cracking
Degradation of interphases High temperature
oxidation
Fiber overloading
Fiber weakening
Temperature
Environment
Delayed failure of fibers
Ultimate failure
degradation
oxidation
Creep T>1200°C
slow crack growth
T<1000°C
Durability
creep of the matrix
T>1200°C
Delayed failure and lifetime at high temperature
Crack healing in 2D woven SiC/SiBC composite
Cyclic fatigue (20 Hz) at 1200°C
Static fatigue at 1200°C (load150 MPa) (Carrere, Lamon, 1999)
Lifetimes in fatigue at high temperature
700°C Minicomposite BN interphase [Morscher 1998] 600°C NLM 207 treated 700°C NLM 202 as-received [Lavaire 1999] 600°C 1D SiC/Si-B-C
100
1000
10 4
10 5
10 6
10 7
100 1000
Life
tim
e
(s)
Stress on fiber (MPa)
600°C NLM 207 treated 600°C 1D SiC/Si-B-C 600°C 2D SiC/Si-B-C
100
1000
10 4
10 5
10 6
100 1000
Life
tim
e (s
)
Stress on fiber (MPa)
Composite 2D 120 MPa
Composite 2D 220 MPa
Static fatigue: slow crack growth in SiC fibers
500°C 900°C 1000°C 1200°C
SiC tows
SiC/SiC composite
Slow crack growth
Growth of oxide layer at fiber surface Protection of fiber by oxide layer and SiC
matrix: slowing down SCG phenomenon
Slow crack growth
Surface oxidation
Creep
Fracture surface of a fiber after static
fatigue on Nicalon tows at 700°C
Fiber
Silica thin layer
flaw
Stress intensity factors estimated from
crack sizes
crack length KI KI/KIC
0.62 0.47 0.23
1.23 0.66 0.33
1.85 0.81 0.40
3.08 1.04 0.52
Penny shaped cracks :
I
aK 2 s
ICK 2MPa m
Static fatigue: slow crack growth in SiC Nicalon tows
(Forio, Lamon. JACS, 2004)
34
Static fatigue of SiC filaments and tows
n ≈ 8.4
A0 = 5,62.1017 Ea = 182 kJ.mol-1
y = 3,15.10 26 x
-7,25
y = 3,29.10 24 x
-7,24
1
10
100
1000
10000
100000
1000000
10000000
100 300 500 700 900 1100 1300 1500 1700 1900
stress ( MPa )
lifet
ime
( s
)
Fils Hi - Nicalon S 600 °C
Fils Hi - Nicalon S 800 °C
Fils Hi - Nicalon S 800 °C
1 mois
1 sem
1 j
1 h
1 min
1000
100
10
1
0,1
0,01
0,001
dd
v (h
) Hi-Nicalon S tows at 600°C and 800°C
n ≈ 7,2 A0 = 7,38.1015 Ea = 178 kJ.mol-1
Hi-Nicalon tows at 500°C and 800°C
(Gauthier, Lamon, J. Am. Ceram. Soc. 2009)
t sn = A0 exp (Ea/RT) t sn = A
1
10
100
1000
10000
100000
1000000
10000000
100 300 500 700 900 1100 1300 1500 1700 1900
applied stress (MPa)
life
tim
e (
s)
tows 500°C
tows 800°C
single fibres 800°C
1000
100
10
1
0,1
0,01
0,001
life
tim
e (
h)
Theory: fiber lifetime distribution
V =da
dt= V *
K I
K IC
æ
è ç
ö
ø ÷
n
t =2K IC
2
V *Y 2s2(n - 2)
sf
s
æ
è ç
ö
ø ÷
n-2
-1é
ë ê ê
ù
û ú ú
P(t,s,v) =1 - exp -v
vo
æ
è ç
ö
ø ÷
s
s0
æ
è ç
ö
ø ÷
m
1 +t
t*
n - 2
2
æ
è ç
ö
ø ÷
m
n-2é
ë
ê ê
ù
û
ú ú
- Subcritical crack growth
- Stress-strength-rupture time relation
- Lifetime distribution
t* =K IC
2
V *s2Y 2
sfj
= s0(-v
0
vLn(1 - P
j))
1
m
(R’Mili, Lamon, 2011, 2012)
Distribution of lifetimes under constant stresses
Hi Nicalon S filaments @800°C in air
(R’Mili, Lamon, 2015)
0
0.1
0.2
0.3
0.4
0.5
0.6
0.7
0.8
0.9
1
1.E-04 1.E-01 1.E+02 1.E+05 1.E+08
Pro
ba
bil
ity
Rupture time (hours)
1100 MPa 700 MPa
400 MPa
Critical fiber
Fibre Fibre
L1 L2
PyC coating t1 t2
Influence of oxidation of PyC interphase in SiC/SiC: size effects
On lifetime of SiC filament (P=0.1) at 500°C under 700MPa
Size dependence of rupture time
P(t,s,v) =1 - exp -v
vo
æ
è ç
ö
ø ÷
s
s0
æ
è ç
ö
ø ÷
m
1 +t
t*
n - 2
2
æ
è ç
ö
ø ÷
m
n-2é
ë
ê ê
ù
û
ú ú
(R’Mili, Lamon, 2011, 2012)
t2
t1
=L
1
L2
æ
èçç
ö
ø÷÷
n-2
m
0,1
1
10
100
1000
10000
100000
1000000
10000000
100000000
0 50 100 150 200 250 300 350 400
Stress on composite (MPa)
Experimental data
Predicted data
t s 2= cste
75%
0%
25%
50%
p 90%
Ru
ptu
re t
ime
(h)
Stress-Probability-Time diagrams for 2D SiC/SiC
(Loseille, Lamon, 2010)
Static fatigue at 500°C
• CMCs are versatile and smart materials
• Significance of microstructure/properties relationships
• Theoretically, composites can be designed with respect to end use applications
• Empirism still prevails
• But, composite design can be based on models
• Multiscale bottom up models are required: damage processes, failure mechanisms at pertinent scales, constituents properties, interface mechanics, and scale to scale changes
• Interface engineering, processing, treatment and new fibres and matrices (?)
ACKNOWLEDGMENTS
• Financial support: CNRS, Snecma, CEA, Conseil Régional d’Aquitaine, European Commission.
• Ph. D. students: S. Bertrand, K. Rugg, L. Guillaumat, N . Godin, P. Forio, S. Pasquier, S. Pompidou, F. Pailler, P. Carrère, C. Droillard, F. Rebillat, V. Calard, C. Sauder, O. Loseille, V. Calard, J. El Yagoubi, M. R’Mili, A. Laforêt