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Ongoing Materials Degradation Work within the Primary Systems Corrosion Research Program and the other EPRI “Issue Programs”
John HicklingTechnical Fellow – Materials IssuesTechnology Group – Nuclear Sector
NRC Research PMDM MeetingCharleston, SC; May 11, 2006
2© 2006 Electric Power Research Institute, Inc. All rights reserved.
EPRI Primary Systems Corrosion Research (PSCR) Program: Overview
• Goal: To improve the useful life of BWR and PWR primary system components through a better understanding of crack initiation and early crack propagation processes leading to SCC and IASCC degradation of materials
• Corrosion Research addresses Barrier 1.1 in the Material Degradation & Aging Action Plan:– Limited fundamental understanding of environment related
degradation phenomena
– Lack of mechanistically based predictive models
– Need for new, more corrosion resistant materials
• Planning of current and future projects draws heavily on the information gained during establishment of the MDM
3© 2006 Electric Power Research Institute, Inc. All rights reserved.
CRCRProgramProgram
CHEMISTRY
International SCCInitiation Program
(PEACE)
Cooperative IASCCResearch (CIR)
UCB “in-situ”Autoclave Work
SGMPMRP
Corrosion Research Roadmap
MEOG/MTAG Materials Initiative
(DM/IMT)
MaterialsInformation Portal
Mechanistic “Gap” Studies
BOP Corrosion
BWRVIP
4© 2006 Electric Power Research Institute, Inc. All rights reserved.
Key Corrosion Research Projects: Scope
1. Cooperative IASCC Research (CIR) Program
Objectives • Develop a mechanistic understanding of key parameters (material,
fluence, temperature, chemistry and stress) that control IASCC initiation and growth
• Formulate predictive models for IASCC based on a mechanistic understanding
• Identify suitable countermeasures for IASCC
International collaborative research program managed by EPRI and co-sponsored by organizations from U.S., Sweden, France, Belgium, Spain, Japan, Germany, Finland, Norway and Czech Republic
• Members include utilities, regulators, vendors and research organizations
5© 2006 Electric Power Research Institute, Inc. All rights reserved.
Key Corrosion Research Projects: Scope (cont’d)
2. Participation in an International Program on Life Time Prediction of EAC (work at FRI, Tohoku University, Japan) with following goal:
– Develop predictive models based on better mechanistic understanding of EAC of stainless steels and Ni alloys in BWR and PWR environments
– This program is co-sponsored by Japanese government, utilities, vendors and several international organizations
– Allows significant leveraging of EPRI resources
3. EPRI-managed program at UC Berkeley on:
– In-situ characterization of surface films on SS and Alloy 600 in LWR environments and their role in SCC
– Development of thin film SCC initiation sensors
6© 2006 Electric Power Research Institute, Inc. All rights reserved.
• Development of Understanding of the Interaction between Localized Deformation in Materials and EAC
– Recent findings for several alloys suggest that the tendency to undergo localized deformation is a key element in determining EAC susceptibility
– A coordinated effort across a range of material/environment systems may offer a more proactive approach to managing long-term degradation
• Development of Additional Understanding on Initiation of EAC and the Growth of “Short Cracks”
– Component behavior in the field is often governed as much or more by this phase of degradation than by the behavior of long (deep) cracks as usually studied in the laboratory
– Improved understanding in this area is key to developing successful EAC mitigation techniques
Corrosion Research: Additional Work funded by the U.S. Materials Management Initiative
7© 2006 Electric Power Research Institute, Inc. All rights reserved.
Objectives of new PSCR Project on the Interaction between Localized Deformation in Materials and EAC
• EAC has been studied for 30 years → improving and optimizing of practices in nuclear power plants (repair, replacement of components or materials) → considerably reduced the susceptibility of LWR to EAC.
• 4 Objectives :
• To identify possible strain localization mechanisms in Nuclear Materials
• To review different types of EAC – strain localization interactions in LWR water environments
• To focus on key-gaps and to identify the main issues
• To propose recommendations
8© 2006 Electric Power Research Institute, Inc. All rights reserved.
Localization of plastic flow in nuclear materials
1. Origin of strain localization• Strain localization results from a complex competition between
material hardening versus softening, geometry and loading conditions.
Non homogeneous loading(crack, notch…)
Non homogeneous response(heterogeneous material,
plastic instabilities…)
Strain localization• Intensity• Length scale• Stationary / propagative• Transient regime / persistent
9© 2006 Electric Power Research Institute, Inc. All rights reserved.
2. Four main types of plastic instability in nuclear environment (Estrin-Kubin classification)
Spatial material heterogeneity (type O)Strain softening (type h) : “the more you strain the easier you strain”Strain rate softening (type S) : “the quicker you strain the easier you strain”Fatigue localization (type F)
Localization of plastic flow in nuclear materials Homogeneous loading →Heterogeneous response
10© 2006 Electric Power Research Institute, Inc. All rights reserved.
Spatial material heterogeneity (type O) : GBS plastic instability
304L Stainless steel
CERT (5.10-8 s-1)
PWR environment (360°C) 600 Ni base alloy
CERT (5.10-8 s-1)
PWR environment (360°C)
11© 2006 Electric Power Research Institute, Inc. All rights reserved.
Strain softening (type h) : Lüders (plastic instability)
Mild steel
Tensile test in air (25°C)
S. Graff, Material Science and Engineering A, Vol. 387-389, 2004
El.
Load
Lüdersband
Unyieldedmetal
12© 2006 Electric Power Research Institute, Inc. All rights reserved.
Strain rate softening (type S) : PLC in 718 alloy tested in air
718L Ni base alloy
Tensile test (5.10-5 s-1) in air
L. Fournier, Materials Science & Engineering A269 (1999) 111-119
Tensile test in air at 500°C Tensile test in air at 470°C
13© 2006 Electric Power Research Institute, Inc. All rights reserved.
Fatigue localization = type F plastic instability
PSB in pure copper
Fatigue straining (∆ε)
Localization in PSB
Crack nucleation + damage percolation
Number of cycle to fracture
14© 2006 Electric Power Research Institute, Inc. All rights reserved.
EAC & GBS (type O) alloy 600 tested in PWR environment
Time to failure vs. Intergranular viscosity ηAlloys 600 and 690 RUBs specimens tested in primary environment at 360 °CFrom J.D. Mithieux ph-D (EDF)
CGR vs. Intergranular viscosity ηAlloys 600 and 690 CERTs (5.10-8 s-1) in primary environment at 360 °CFrom J.D. Mithieux ph-D (EDF)
Time to initiation of SCC Crack growth rate of SCC
GBS GBS
15© 2006 Electric Power Research Institute, Inc. All rights reserved.
0
20
40
60
80
100
120
140
160
0 0,1 0,2 0,3 0,4
γ
Cra
ck d
epth
(µm
)
β = −1
β = 0
β = +1
IGSCC
0
200
400
600
800
1000
1200
0 0,1 0,2 0,3 0,4γ
Cra
ck d
epth
(µm
)
β=−1β=0
β=+1
TGSCC
EAC & substructure instabilities (type h) in 304L tested in PWR environment
45°
135°
90°
β = +1
β = −1
β = 0
γ = tan αα
τ
τ
16© 2006 Electric Power Research Institute, Inc. All rights reserved.
Fe-δ
Localized strain around δ-ferrite
σ
IGSCC for a complex strain path
TEM observation
SEM observation
500 nm
17© 2006 Electric Power Research Institute, Inc. All rights reserved.
IGSCC for a complex strain path
→ Strain localization/incompatibilities promote IGSCC
Initiation of cavities at the grain boundary
Grain boundary
σ
18© 2006 Electric Power Research Institute, Inc. All rights reserved.
200 nm
Area under residualstresses
Twin boundary
DFZ
Pile up of dislocations / micro crack
Transgranular crack-tip observation
100 nm
19© 2006 Electric Power Research Institute, Inc. All rights reserved.
EAC & Strain localization (type S) in 304L/316L tested in PWR environment
1E-121E-111E-101E-091E-081E-071E-061E-051E-041E-031E-021E-01
0 200 400 600 800 1000
Temperarure (°C)
Cre
ep ra
te (1
/s)
50 MPa - 316LN (Usami)
100 MPa - 316LN (Usami)
200 MPa - 316LN (Usami)
250-400 MPa - 304L (EDF-MMC)
170 MPa - 304 (Frost)
340 MPa - 304 (Frost)
PLC
Observed by Ehrnsten in 316LN (dε/dt=5.10-5 s−1) with an increasing
effect of pre-strain hardening
Time
Tensile load at 360°C
Initiation & propagation
of SCC
No initationof SCC
20© 2006 Electric Power Research Institute, Inc. All rights reserved.
EAC & fatigue instability (type F)Fatigue straining (∆ε)
Localization in PSB
Crack nucleation + damage percolation
Decrease of number of cycle to fracture
21© 2006 Electric Power Research Institute, Inc. All rights reserved.
Type of
instabilities Physical cause
Governing parameters
microstructure,loading Example in nuclear materials
Type O : macrosopic
heterogeneity
Heterogeneity at the mesoscopic or
macroscopic level Castings, weldings
Scale and connectivity of the soft and hard zones, contrast
between the zones Direction of loading with
respect to the heterogeneities
- PWR primary coolant pipes : Thermally aged cast stainless steels → Hardened ferrite in austenite → mechanical embrittlement +,sensitivity to IASCC - welds - “ghost lines”
Type O : intragranular heterogeneity
Interaction of the GB with chemical species, vacancies
Width of the PFZ, state of precipitation at the GB,
direction of loading with respect to the grain
morphological texture Width of the precipitated free
zone and depleted zone.
- Chemical heterogeneities due to grain boundary precipitation or segregation (chromium carbides in 600 alloys and stainless steels in BWR → sensitised stainless steels) - Chemical heterogeneity due to in service (irradiation or thermal ageing) induced segregation at grain bondary (thermal ageing : pressurizer : temper reversible embrittlement ; irradiation : stainless steels internals)
Type O : Grain
boundary slidings
Stress gradients incompatibilities
Grain size, state of precipitation at the GB
-Nickel base components in PWR primary circuit components : Influence of grain boundaries sliding on Alloy 600 SCC
Strain localization in nuclear materials : type O instabilities
Example of spatial material heterogeneities…
22© 2006 Electric Power Research Institute, Inc. All rights reserved.
Type of
instabilities Physical cause
Governing parameters
microstructure,loading Example in nuclear materials
Type h : Dislocation
burst
Unpinning from obstacles or brutal multiplication of
mobile dislocations
Solid solution composition, Prior Static ageing, state of
recristallisation, Temperature, strain rate
- Corrosion -fatigue of LAS components (static strain ageing),
Type h : Obstacle
destruction
Destruction of chemical order or localised obstacles by the motion of
dislocations
Strengthening effect of the chemical order, density and size of precipitates, density and size of irradiation loops
- Channelling in irradiated stainless steels (internals) - Possible Short and Long range ordering in 690 located in “hot” parts of Inconel components, irradiation (supports M) - Precipitation in alloys 718 and X-750 - Demixtion of ferrite in duplex stainless steels
Type h: substructure instability
Destabilisation of a well developed
substructure by a change path
State of organisation of the substructure prior to the strain
path change Severity of the change
Cold worked stainless steels under complex mechanical loadings
Strain localization in nuclear materials : type h instabilities
Example of strain softening…
23© 2006 Electric Power Research Institute, Inc. All rights reserved.
Type of
instabilities Physical cause
Governing parameters
microstructure,loading Example in nuclear materials
Type S : PLC
instability
Dynamical strain ageing due to the
interaction of dislocations with
mobile solute atoms
Solid solution composition, Strain rate and temperature,
strain threshold
- PWSCC of alloys 718 and X-750 - LAS - Austenitic stainless steels
Strain localization in nuclear materials : type S instabilities
Example of strain rate softening…
24© 2006 Electric Power Research Institute, Inc. All rights reserved.
Type of
instabilities Physical cause
Governing parameters
microstructure,loading Example in nuclear materials
Type F : fatigue
Local softening partial plastic reversibility
Strain amplitude, temperature, possible precipitation.
Stainless steels fatigue Fatigue corrosion of LAS
Strain localization in nuclear materials : type F instabilities
Example of fatigue instabilities …
25© 2006 Electric Power Research Institute, Inc. All rights reserved.
Key gaps : Ni base alloys in PWRs
1. Effect of strain localization (due to strain hardening mode) on the time to initiation and on the CGR ?Time to initiation obtained on alloy 600 exposed to hydrogenatedprimary PWR environment at 325°C → deleterious effect of the complex strain path in RUBs
2. Effect of strain localization on the diffusion of oxygen at grain boundaries (IO model) ?
3. Possible strain localization in HAZ ?
964No initiation after 3840 h586Cylindrical
2142
Predicted tinitiation (h)
2143480RUB
Measured tinitiation (h)σ325°C (MPa)Type of specimen
26© 2006 Electric Power Research Institute, Inc. All rights reserved.
Key gaps : austenitic stainless steels in PWRs
1. Effect of strain localization due to complex strain hardening on the time to initiation and on the CGR ?
→ Complex strain hardening promotes IGSCC
2. Effect of strain localization due to cyclic loadings (Persistent Slip Bands, Shear Bands) on the time to initiation ?
→ No initiation under pure static loading
3. Effect of the interaction between (C + N) and plasticity on the initiation of IGSCC ? on the CGR ?
→ low strain rates promote IGSCC while high strain rates promote TGSCC
4. Physical mechanism ?
→ strain localization seems to be a necessary condition for SCC
27© 2006 Electric Power Research Institute, Inc. All rights reserved.
Recommendations : strategy
1. Two main directions of advance :Comprehension of the local coupling between strain localization with :
Oxidation at the surface or at the crack tipTransport of species (H, vacancies, O)Fracture
Modeling of initiation and propagationQuantitative predictionBased on physical mechanisms (oxidation, transport, fracture, mechanical
behavior)
2. Three main tasks :Choice/development of tools of investigation
SEM, TEM, specific tests, numerical simulationQuantification of strain localization effect on EAC
Empirical modeling, then physical modeling of oxidation, transport and fractureEvaluation of possible EAC-strain localization synergy in components
Selection of critical components (fabrication, in service loading), criteria for survey (ti, CGR), mitigation
28© 2006 Electric Power Research Institute, Inc. All rights reserved.
Recommendations : quantification of interactions between EAC and plastic flow instabilities
Modeling of SCC
Range of T-dε/dt promoting the GBS. Correlation with initiation of SCC.
Range of T-dε/dt promoting interactions between solute atoms and mobile dislocations (reducing intragranular creep). Correlation with initiation of SCC.
Evolution of the surface reactivity during the incubation period as a function of pre-strain hardening.
Rate of appearance of PSBs and shear bands at the surface. Correlation with initiation of SCC.
Austenitic stainless steels
Modeling of IGSCC
Strain softening effect (due to complex strain paths) on the CGR. 2006-2007
Strain localization in HAZ and correlation with the crack propagation. 2006-2007
Strain localization in HAZ and correlation with initiation sites. 2007
Strain softening effect (due to complex strain paths) on time to initiation. 2006-2007
Wrought Ni base alloy
Modeling of IGSCC
Rate of appearance of PSBs and shear bands at the crack-tip. Correlation with CGR of IGSCC.
Strain localization in welds and correlation with the crack growth path.
Rate of appearance of PSBs and shear bands at the surface. Correlation with time to initiation of IGSCC.
Strain localization in welds and correlation with initiation sites.
Weld Ni base metal
5
4
3
2
1
Task order
29© 2006 Electric Power Research Institute, Inc. All rights reserved.
CONCLUSION : “Products” for Utilities
Examples of « end products » for Utilities :
1. Strain localization maps vs. EAC
2. Local fracture criteria for EAC
Temperature
Stra
inra
te
DSAPLC
SRO
GBS
IGSCC
Strain localization maps vs. EAC for a couple material/environment
Local fracture criteriafor IGSCC
Strain map (from Zinkle)
30© 2006 Electric Power Research Institute, Inc. All rights reserved.
• Materials aging due to SCC is the greatest single challenge facing the LWR nuclear industry
• Research into EAC (SCC and corrosion fatigue) mechanisms, mitigation and key factors affectinginitiation and propagation of cracks are important for long-term asset management
• Initiation and short crack growth can dominatecomponent life
• The EPRI Primary Systems Corrosion Research program has used MEOG/MTAG funding in 2005 to develop a review of knowledge “gaps” in this area
New PSCR Project on Initiation and Short Crack Growth: Introduction
31© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Objectives of Review
• Summarize the current knowledge of crack initiation and short crack growth in nickel base alloys, stainless steelsand carbon/low alloy steels in typical PWR and BWR environments
• Identify key gaps in the knowledge base • Recommend experimental work to fill these gaps that
will likely contribute to improved management or mitigation of EAC in PWRs and BWRs
• EPRI report # 1011788 (prepared by Framatome-ANP and GE-GRC) was issued in December 2005
• Question and answer session (telecon) was held on 12/05/05 with the principal investigators (Scott/Andresen)
32© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Stages in the Development of SCC
33© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Report Structure
• Introduction, objectives, definition of terms - P. Scott and P. Andresen
• Surface oxidation, and crack initiation in deaerated hightemperature water – P. Combrade
• Passive layer formation, breakdown and crack initiation in oxygenated conditions – P. Andresen and Y. Kim
• Field experience of crack initiation and growth in austenitic SSand C&LAS, together with associated laboratory testing – R. Kilian and A. Roth
• Quantifying crack initiation and short crack growth – P. Andresen• Multiple crack initiation and coalescence – P. Scott• Conclusions and recommendations – P. Scott and P. Andresen
34© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Definitions
Proposed Working Terminology for Crack Initiation
Metallurgically small cracks, which are cracks smaller than one grain diameter, or some other metallurgical feature.
Phenomenology – Metallurgy
Mechanically small cracks, which are shallow surface cracks growing under plane stress conditions, or where linear elastic fracture mechanics cannot be applied with confidence and certainty.
Phenomenology – Mechanics
Chemically short cracks, in which a mature, long crack chemistrytypical of deeper cracks has not formed.
Phenomenology – Environment
Detectability that is likely to be achievable in in-situ autoclave investigations in the laboratory, e.g., ≈ 50 µm crack depth.
Practical Definition
Formation of a physically distinct geometry that will tend to grow in preference to its surroundings as a sharp crack.
Scientific Definition
35© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Implications
36© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Dynamic Effects during Static Loading
Crack tip
Stra
in
Crack tip
Stra
in
Area where redistribution of strain induces slip offsets at the crack tip
Crack Tip Plastic Strain304 Stainless at 288oC
0.00
0.05
0.10
0.15
0.20
0 10 20 30 40 50
Distance from crack tip (µm)
Cra
ck T
ip P
last
ic S
trai
n
K = 25 MPa√mn = 3.43
E = 172 GPacgr = 1.4x10-7 mm/sec
σYS = 161 MPa
σYS = 550 MPa
Crack tip
Crack Tip Plastic Strain304 Stainless at 288oC
0.00
0.05
0.10
0.15
0.20
0 10 20 30 40 50
Distance from crack tip (µm)
Cra
ck T
ip P
last
ic S
trai
n
K = 25 MPa√mn = 3.43
E = 172 GPacgr = 1.4x10-7 mm/sec
σYS = 161 MPa
σYS = 550 MPa
Crack tip
At constant load, crack tip strain rate occurs due to strain redistribution as the crack grows.↑ yield strength ↑ dε/da
Crack Tip Strain Rate from Redistribution
37© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: General Conclusions
• Oxide film structure– multi-layered structures on all materials in both PWR
and BWR environments– inner layer provides protection against EAC – formation of outer layers depends on cation concentration in water
(may prevent access of Zn, e.g.)• Crack initiation processes
– IG oxide penetrations observed in Alloy 600 in PWR primary water but not• in C&LAS or SS in this medium• in any of these materials in BWR environments (as far as known)
– pitting and dissolution of sulfide inclusions important for C&LAS
38© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: : Oxide Films on Ni-based Alloys in PWRs
39© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: : Oxygen Penetration in Grain Boundaries
SIMS image of ions 16O- at different depths under the oxide layera - 4 µm, b - 1.9 µm, c - 1.1 µm, d - 0.7 µm, e - 0.5 µm, f - 0.3 µm
After Delabrouille
20 % Cr model alloy oxidized 1000 hrs at 360° C in simulated primary coolant.
40© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: : Oxide Films on SS in BWRs
Steel Barrier layer Inner layer Outer layer Deposited layer
(Fe1-xNix)(Cr1-yFey)2O4 (NixFe1-x)(Fe1-yCry)2O4 NiFe2O4
VM´´´Vm VM
´´´
VO••
VO••
Mi•• Mi
••
Maqy+
Maqx+
Maqx+
Vm
Steel Barrier layer Inner layer Outer layer Deposited layer
(Fe1-xNix)(Cr1-yFey)2O4 (NixFe1-x)(Fe1-yCry)2O4 NiFe2O4
VM´´´Vm VM
´´´
VO••
VO••
Mi•• Mi
••
Maqy+
Maqx+
Maqx+
Vm
Steel Barrier layer Inner layer Outer layer Deposited layer
(Fe1-xNix)(Cr1-yFey)2O4 (NixFe1-x)(Fe1-yCry)2O4 NiFe2O4
VM´´´Vm VM
´´´
VO••
VO••
Mi•• Mi
••
Maqy+
Maqx+
Maqx+
Vm
41© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: : Role of Pitting for LAS
Pre-pitting and fatigue in air (top) vs. active pitting during fatigue (bottom) Disproportionate effect of early cycles
under “bad” water chemistry
42© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: General Conclusions (con.)
• Fabrication factors affecting probability of crack initiation:– surface chemical inhomogeneities from oxidation, chemical etching,
pre-segregation…– surface mechanical inhomogeneities, including cold work, handling
damage, casting defects/porosity, welding folds and trapped slag…– material inhomogeneities from microstructure (e.g., grain size,
compositional banding…)– inhomogeneities from local stresses and strains, including those
from grain boundary (GB) orientation (e.g., GB mis-orientation energy…)
– regions of material that undergo accelerated aging during plant operation (e.g., more prone to sensitize, exhibit IG attack/oxidation…)
– complex interactions of the above
43© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Field Experience with Pre-existing Defects
Defects formed in service
Pits as crack initiationside
Manufacturing flaws: cold work > SCC Manufacturing flaws:
root notch > SCC
44© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: General Conclusions (con.)
• Other factors affecting crack initiation/ short crack growth:– when KI<KISCC it cannot be assumed that SCC will not initiate (or that
short cracks will not propagate)– multiple SCC initiation is a common observation in engineering
components– short cracks may grow rapidly initially, slow down exponentially, and
exhibit long periods of dormancy until coalescence with newlyinitiated cracks nearby reactivates growth• ratio of growth of short cracks in depth and at the surface is contrary to
expectations from LEFM analyses– study of databases of generic SCC operating experience can yield
useful practical information for improving fabrication and operating conditions so as to reduce the risk of crack initiation
45© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Crack Dormancy/Coalesence
46© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Crack Dormancy/Coalesence
Dormancy and/or coalescence of multiple cracks (left: PWSCC “craze” cracking in a RPV head penetration; right: in a SG tube roll transition) is a key issue that can best
be described using Weibull statistics and modeled using Monte Carlo methods
47© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Fabrication Effects
48© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Field and Lab Experience for SS in BWRs
• The primary objective is to avoid crack initiation and subsequent crack growth by the application of proper, qualified fabrication processes
• Need to rule out detrimental effects such as– sensitization due to grain boundary chromium depletion– weld imperfections (e.g., root notches, shrinkage defects, mismatch,
misalignment, excessive penetration lack of fusion, slag inclusions)– surface cold work exceeding the critical hardness– excessive residual stresses in the component
• dK/da shown in laboratory testing to have a major influence on growth rates (and thought to represent component behavior)
49© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Role of Stress Intensity Control
50© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: General Recommendations
• Ensure that experiments undertaken to study EAC initiation are carried out under optimal test conditions (& yield statistically valid data)
• Measure the properties of oxide films that impact the rate determining processes that lead to a failure to protect the underlying metal from crack initiation (also relevant to the issue of activation of corrosion products in LWR coolant circuits)
• Identify and, if possible, quantify and model the kinetics of the damage processes that occur in LWR structural materials prior to detectable crack initiation
51© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: General Recommendations (con.)
• Document and further evaluate field experience of SCC in LWRs to identify critical fabrication, environmental and operational factors influencing crack initiation in service
• Devise suitable in-situ test and service crack initiation monitoring equipment
• Improve or develop robust predictive models for generic SCC phenomena, including situations where multiple crack initiation and coalescence occurs (e.g. by applying techniques evolved in the high-pressure, gas transmission pipeline industry)
52© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Specific Recommendations (1)
• Experimental requirements– Use adequate numbers of samples for statistical significance– Tapered specimens are suitable for studying multiple initiation,
coalescence and growth (in combination with conventionalmicroscopy and layer grinding)
– Test designs should avoid complications of stress relaxation associated with fixed-deformation testing
– Good control of specimen surface finish and simulated reactorquality water is essential
– On-line DCPD is well adapted to measure short crack growth rates in appropriately designed specimens - electrochemical noise alsouseful
– ATEM could be usefully deployed to help identify the factors involvedin transitions from incipient crack damage to short crack growth and finally to LEFM controlled growth
53© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Specific Recommendations (2)
• Surface oxide properties:
– Determine the composition, crystallography, microstructure and semi-conducting properties of material/environment combinationssubject to generic SCC (as a necessary precursor for establishingrate determining processes and predictive models)
– Establish the influence of temperature on oxidation rate, cation release rate and damage to the underlying metal
54© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Specific Recommendations (3)
• Damage processes prior to initiation
– For Ni-base alloys in PWR primary conditions:• determine the mechanism, kinetics and temperature dependence of GB
oxidation embrittlement• evaluate local stresses due to oxide growth and selective
oxidation/dissolution• determine the stress/strain conditions necessary for developing the first
microcrack from an oxidized grain boundary
– For stainless steels in PWR primary conditions :• examine cold worked and sensitized stainless steels for the existence of
similar damage processes
55© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Specific Recommendations (4)
• Damage processes prior to initiation
– For austenitic alloys in BWR conditions:• establish the cause and statistics behind crack initiation in uncreviced,
unsensitized SS and Ni alloys in relevant (good) water chemistries• study the films on stressed and unstressed specimens to identify
whether precursor phenomena can be identified in the oxide film or underlying metal
• quantify the benefit of improved alloys and weld metals, such as Alloy 690 and its weld metals, on crack initiation as a function of stress and water purity
• determine how memory effects from periods of "bad" water chemistry can accelerate crack initiation and short crack development in cold worked and sensitized austenitic materials during long periods of acceptable water chemistry
56© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Specific Recommendations (5)
• Damage processes prior to initiation
– For C&LAS in both PWR and BWR media:
• determine critical flaw sizes and shapes for SICC or CF as a function of potential and Cl- and SO4
– concentration
• determine the role of thick, porous oxide deposits on local water chemistry and decoupling from bulk environment
57© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Specific Recommendations (6)
• Analysis of operating experience
– Invest in building databases of generic SCC problems and theiranalysis (e.g., by neural network methods)
– Characterize crevice conditions with respect to stress/strainconcentrations and critical hardness
– Characterize typical industrial surface finishes with high resolutiontechniques prior to HT water exposure and then the characteristicsof oxide layers that form in HT water (especially those associatedwith crack initiation)
58© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Specific Recommendations (7)
• Multiple crack initiation and coalescence– Test tapered specimens of materials subject to generic SCC in
LWRs in order to determine crack initiation density as a function of stress and time (and analyze whether the crack density is sufficientto give rise to coalescence)
– Determine pit birth, growth and death statistics in those systemswhere this process occurs and risk of crack initiation from pits
– Examine LEFM solutions for multiple cracks (developed for fatigue crack growth evaluations) for their applicability to SCC growthmodeling
– Assess importance of dK/da on propagation rates– Establish a theoretical basis for crack dormancy– Develop a Monte Carlo model of multiple crack initiation,
coalescence and growth
59© 2006 Electric Power Research Institute, Inc. All rights reserved.
PSCR “Gap” Project on Initiation and Short Crack Growth: Suggested Priority Areas
1. Determine frequency of multiple initiation as a function of stress and time and determine whether the crack density in typicalmaterial/environment combinations with known SCC susceptibility issufficient to lead to coalescence
2. Determine the effect of dK/da load control on the growth rate of short cracks
3. Create/expand systematic databases of SCC field failures and analyze them so as to determine critical fabrication parametersassociated with SCC initiation
4. Determine kinetics of IG oxidation in Alloy 600 and similar alloys and depth/strain combinations required to initiate a crack – thendemonstrate that Alloys 690/152/52 and SS are not susceptible to the same mechanism
60© 2006 Electric Power Research Institute, Inc. All rights reserved.
BWR Vessel Internals Program (BWRVIP)Example #1 of Proactive Materials Research
• International workshop held in 2003 identified a key issue• Evaluate and quantify the effects of high radiation levels on
behavior of stainless steel components with regard to– Crack growth through IASCC– Fracture toughness
• BWRVIP Inspection and Evaluation Guidelines for internals require supporting data on irradiated stainless steels
• Data in hand show significant degradation due to irradiation– Irradiation at intermediate fluence accelerates SCC growth rate in
stainless steels by a factor of 5 or more– Some data indicate HWC is less effective at fluences approaching
1x1022 n/cm2
• There are data gaps, especially at end of license fluences
61© 2006 Electric Power Research Institute, Inc. All rights reserved.
BWRVIP ProgramExample #1 (con.)
• BWRVIP issued a Request for Proposals (RFP) in early 2004• GE and Studsvik selected as primary contractors to conduct testing
– GE Team• GE Vallecitos – crack growth testing• Battelle – material characterization• University of Michigan – post test SEM
– Studsvik Team• Studsvik – fracture toughness and crack growth testing• Nippon Fuels – fracture toughness testing• Both organizations to conduct post test characterization for materials
tested at their respective facilities• Scope includes 22 fracture toughness and 13 CGR tests (NWC / HWC)• Final report will include a critical assessment of existing BWRVIP
correlations and flaw evaluation methodologies
62© 2006 Electric Power Research Institute, Inc. All rights reserved.
BWRVIP ProgramExample #2 of Proactive Materials Research
• Assess potential advanced mitigation technologies– Demonstration of On-line Noble Metal Chemical Application (NMCA)– Development of Zirconia coatings
• The conventional NMCA process is applied during an outage and requires two days of critical path time– New cracks formed during off-hydrogen periods may continue to
grow
• On-line NMCA process was developed by GE to reduce critical path time required for the conventional NMCA process and deposit noble metal on new crack surfaces which may be created during off-hydrogen periods
• On-line NMCA technology will be demonstrated at an international BWR-4 in mid-2005 (including fuel surveillance)
63© 2006 Electric Power Research Institute, Inc. All rights reserved.
BWRVIP ProgramExample #2 (con.)
• Current mitigation technologies (HWC and NMCA) are not effective in mitigating cracking in components above the reactor core
• Prior work shows that zirconia coatings have the potential to mitigate cracking even in the absence of hydrogen
• Lab studies have demonstrated that adherent zirconiacoatings can be deposited from solution on pre-oxidized surfaces of stainless steel and Alloy 600
• Objective of present studies is to develop an in-situ process for the deposition of zirconia coatings on internals
• Future work will assess effectiveness in mitigating crack growth through IGSCC
64© 2006 Electric Power Research Institute, Inc. All rights reserved.
Materials Reliability Program (MRP)Example #1 of Proactive Materials Research
• PWSCC of Ni-base alloys is an area of great current concern. In addition to responding immediate issues, the MRP Alloy 600 program is conducting longer-term studies on:– Mechanical and chemical mitigation approaches to preventing
crack initiation and slowing or stopping crack growth– Microstructural features affecting material susceptibility (including
detailed characterization of field cracks, HAZ testing, etc.)– Additional effects (fabrication defects, surface condition, grain
orientation, etc.) involved in cracking of the weld metals– Possible involvement of low-temperature crack propagation– Resistance to cracking of replacement materials (A 690/152/52)
• Goal is to improve both understanding and predictability
65© 2006 Electric Power Research Institute, Inc. All rights reserved.
MRP ProgramExample #2 of Proactive Materials Research
• The Reactor Internals Group has program elements proactively addressing aging in several areas:
Screening, Categorization and Ranking of PWR Internals Components (includes consideration of individual and combined degradation mechanisms)Functionality Evaluations of PWR Internals Components (includes development of irradiated materials behavior models)Controlled Irradiation Experiment and Hot Cell Test addressing void swelling and IASCCInspection / Repair / Replacement / Mitigation Strategies
• Overall objective is to demonstrate that components can perform their required functions under aging/degraded conditions and are flaw and degradation tolerant.
66© 2006 Electric Power Research Institute, Inc. All rights reserved.
MRP ProgramReactor Internals Aging Management Flow Chart
Options for Aging Management of PWRReactor Vessel Internals, and the
Associated Gaps and Needs
Use Inspections and Flaw Evaluationsfor Aging Management of PWR
Internals
ObtainNew Data
Document TechnicalBasis
Issue PWR InternalsInspection Guidelines
BOR DataSONGS DataBolts Samples
Perform FunctionalityAnalyses
ScreenComponents
Evaluate LeadComponents
WOG AnalysesBWOG Analyses
Gather EnvironmentalInformation and Materials Data
67© 2006 Electric Power Research Institute, Inc. All rights reserved.
Irradiation Assisted Stress Corrosion
Cracking
Stress Corrosion Cracking
Irradiation Enhanced Stress
Relaxation
CASS Thermal Aging + Irradiation
Embrittlement
Irradiation Embrittlement
Irradiation Induced Void Swelling
Baffle-BoltsWelds
Thermal Shield & Core Barrel
Bolts
Bolted Joints
CASS Components
(Synergistic Effect)
Internals Components
(Increased Strength & Loss of Ductility)
Baffle-Former Plates and Bolts
(High Fluence and Temp. Regions)
Dimensional Changes and Functionality
Stress and Deflection
Due to LOCA and
SSE
UT Inspection EVT-1 or EVT-3 Inspection
1. Scope2. Preventive Actions3. Parameters Monitored4. Detection of Aging
Effects5. Monitoring and
Trending
Meet Current License Basis
IASCC SCC SR CASS TA/IE IE VS
6. Acceptance Criteria7. Corrective Action8. Confirmation Process9. Administrative
Controls10.Operation Experience
??
Meet Current License BasisMeet Current License Basis
Use Data, Generic Analyses and Models to Screen and Select Most-Affected Internals Components
Use Plant-Specific Analyses to Determine Critical Locations, Critical Crack Sizes and Flaw Tolerance for Actual Stresses, Fluences and Temperatures
MRP Program: Reactor Internals Issues for License Renewal
•Scope * Acceptance Criteria•Preventive Actions * Corrective Action •Parameters Monitored * Confirmation Process•Detection of Aging * Administrative
Effects Controls•Monitoring and * Operation ExperienceTrending
68© 2006 Electric Power Research Institute, Inc. All rights reserved.
Steam Generator Management Program (SGMP)Example of Proactive Materials Research
• Original SG tubes were made with alloy 600 MA– Problematic with little hope for long service life– Challenge is to manage the problem until the scheduled replacement
• Some newer and replacement SG used alloy 600TT– Initially believed to be corrosion resistant, but growing evidence is
proving otherwise – In addition to chemistry control, the challenge is to detect and repair
flaws early to avoid potential unscheduled shut downs• New replacement SGs are made with alloy 690TT tubes– Proven to have corrosion-resistant superior to that of alloy 600TT and
so far has shown no service-induced degradation– Challenge is to be proactive and prevent the onset of potential problems
such as the effect of secondary side lead on 690 TT