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ASTM 19th International Symposium on Zirconium in the Nuclear Industry
Ex-situ and in-situ studies of radiation damage
mechanisms in Zr-Nb alloys
Junliang Liu1, Guanze He1, Anne Callow1, Kexue Li1, Sergio Lozano-
Perez1, Angus Wilkinson1, Michael Moody1, Chris Grovenor*1,Jing Hu2,
Mark Kirk2, Meimei Li2, Anamul Haq Mir3, Jonathan Hinks3, Stephen
Donnelly3, Jonna Partezana4 and Heidi Nordin5
1 Department of Materials, Oxford University, Oxford, UK.2 Argonne National Laboratory, Argonne, IL, US3 School of Computing and Engineering, University of Huddersfield, UK4 Westinghouse Electric Company, Pittsburgh, PA, US5 Canadian Nuclear Laboratories, Chalk River, ON, K0J 1J0 Canada
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What are we interested in?The use of advanced analytical techniques to study the response of Zr cladding materials to corrosion and radiation damage
J. Hu et al. Acta Materialia May 2nd 2019 https://doi.org/10.1016/j.actamat.2019.04.055
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Materials
Autoclave corrosion:
Zircaloy-4 and Zr-0.5Nb: 360°C,
18MPa, Pure water
Zr-2.5Nb: 300°C, 10 Mpa, D2O,
PH=10.5(LiOD)3
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Materials
CNL Halden reactor
samples
• In-flux
• Out-of-flux but in-reactor
water chemistry
• Static autoclave with D2O
(pH=10.5, LiOD), and at
300°C and 10 MPa.
• In flux 325 oC samples that
have been extensively
analysed
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20 µm
2 µm
Zr-1Nb sheet
SRA Zr-2.5Nb tube
AD
RD*
TD*
RD
TD
ND
Materials
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Aim of study Material Conditions Sample source
In-situ heavy ion irradiation
1. Irradiation effects in Zr
oxidesRX Zr-0.5Nb
Autoclave
corrosionWestinghouse
and CNL2. Irradiation induced
elemental redistribution
RX Zr-1Nb
RX and SR
Zr-2.5Nb
Metal
Ex-situ characterisation of
in-reactor corroded alloys
3. Microstructure of in-
reactor formed oxideSR Zr-2.5Nb
In-reactor
corrosionCNL
4. Irradiation-induced
elemental redistribution
3D mapping of deuterium
distribution using
NanoSIMS
5. The transportation of
hydrogen/deuterium
through the oxide layer
Ziraloy-4
SR Zr-2.5Nb
Autoclave
and
In-reactor
Corrosion
Westinghouse
and CNL
Experiments undertaken
RX: Recrystallised; SR: Stress Relieved
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Sample exchange
Analysis chamber
Duoplasmatro
n source
Cs+ source
Multicollection chamber
Magnetic
sector
Electron beam Electron
beamIon
beam
Ion beamSEM/FIB/EDX
3D APT
In-situ TEM STEM/EELS/EDX
NanoSIMS 50
Experimental methods
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ExperimentTemperature
(K)Ions
Flux
(ions.cm-2.s-1)
Damage rate
(dpa/s)Facility
In-situ irradiation
in oxides
50 1 MeV Kr++ 8 x 1011 1.5x10-3 IVEM
293 700 keV Kr++ 1-5 x 1012 0.5-2.5x10-3MIAMI2
In-situ irradiation
in SPPs and
metal matrix
50 1 MeV Kr++ 8×1011 1.5x10-3 IVEM
293 1 MeV Kr++ 8×1011 1.5x10-3 IVEM
623 1 MeV Kr++ 8×1011 1.5x10-3 IVEM
873 1 MeV Kr++ 8×1011 1.5x10-3 IVEM
623 350 keV Kr++ 6×1011 1-3x10-3 MIAMI2
In-Reactor 600, 520 Neutrons 4.3-4.7×1013 ~10-7Halden
Reactor
Irradiation Parameters
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In-situ Ion Irradiation of bulk monoclinic-ZrO2 on 0.5 %-Nb (210 days)
Evolution of oxide
structure under in
situ 700 keV Kr++
irradiation at room
temperature
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0 dpa 3 dpa (5.6x1015 ions.cm-2) 10 dpa (1.9x1016 ions.cm-2)
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700 keV Kr++ implantation at 293 K to different damage levels; pre-irradiation, 5.6x1015 ions.cm-2 (3 dpa)
and (c) 1.9x1016 ions.cm-2 (10 dpa)
In-situ Ion Irradiation damage in monoclinic-ZrO2
Simulated patterns Rotationally averaged experimental patterns
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In-situ Ion Irradiation damage in monoclinic-ZrO2
Atomic-resolution HAADF STEM image from an oxide grain post-irradiation, 1.9x1016 ions.cm-2
(10 dpa), with corresponding FFT from the whole region, (b) direct measurement of lattice
parameters based on the HAADF STEM images11
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In-situ Ion Irradiation damage in monoclinic-ZrO2
TKD pattern quality and phase maps
from typical regions of in-situ
irradiated Zr oxide.
(a and d) 0 dpa,
(b and e) 4 dpa, 7.4x1015 ions.cm-2
(c and f) 10 dpa, 1.9x1016 ions.cm-2
0 dpa 4 dpa 10 dpa
monoclinic 97.5% 10.5% 0.4%tetragonal 2.5% 4.1% 4.4%
cubic 0 85.4% 95.2%Horizontal
grain size
(nm) 63±6 66±11 97±24Vertical grain
size (nm) 142±28 76±13 162±49
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In-situ Ion Irradiation damage in ZrO suboxide
In-situ TEM images of
suboxide region and metal
substrate in the Zr-0.5Nb
alloy: (a) pre-irradiation (b)
1014 ions/cm2
Pre-irradiation HAADF
STEM image of the region
followed during in-situ
irradiation and (d) O/Zr
atomic ratio map from EELS
analysis of the pre-irradiation
sample.
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Preferential amorphisation of ZrO suboxide
HRTEM images and
FFTs from the
interface region
(a) pre-irradiation
(b) irradiated at 293
K to 1.9x1016
ions.cm-2
(c) irradiated at 50 K
to 4 x 1015 ions.cm-2
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J Liu et al.Journal of Nuclear Materials 513, 226-231 2019
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RTDFg, 3g
350℃BF
In-situ Ion Irradiation damage in SPPs in metal matrix
Following the same particles during in-situ irradiation
• Morphology of SPPs can easily be obscured by dislocation loops, surface oxide and
bend contours
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In-situ Ion Irradiation damage of β-Nb SPPs in metal matrix
0002 α
ത2110 α
ത2112 α
B= 01ത10 α−Zr
01ത1 β
110 β101 β
B= ത111 β−Nb
(a) pre-irradiation BF (b) post-irradiation BF
(c) pre-irradiation SAD (d) post-irradiation SAD
EDX line-scan profiles of Nb Ka for SPPs
irradiated at 293 K, 623 K, and 873 K with 1
MeV Kr++ to 6.4x1015 ions.cm-2 (15 dpa).
Before and after irradiation by 1 MeV Kr++ to
6.4x1015 ions.cm-2 (15 dpa) at 293 K .
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Size changes in ion-irradiated β-Nb SPPs?
-20%
-10%
0%
10%
20%
30%
40%
50%
0
10
20
30
40
50
60
50 293 623 873
Rela
tive
siz
e c
han
ge
Rad
ius
(nm
)
Irradiation temperatures (K)
β-Nb SPP size after irradiation at different temperatures
before after relative size change
0 20 40 60 80 100 120 140 160 180 200
0
50
100
150
200
250
300
350
Zr Kα1
Nb Kα1
Simulated pre NbZr
Kα
1
Distance (nm)
Post irradiation
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In-situ Ion Irradiation damage in Lave phase SPPs in metal matrix
(c)
SPP
Zr(Nb, Fe)2
α-Zr Matrix
(a) (b)
FFT from SPP
FFT from matrix
HRTEM images and inset FFTs showing the amorphisation of a Laves phase SPP
irradiated at 50 K to 6.8x1015 ions.cm-2 (16 dpa), with EDX line-scans over the
same SPP before and after irradiation18
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How can we study composition changes in the matrix?APT tips irradiated in Huddersfield MIAMI2 with 650 keVKr2+ ionsCNL B166 Zr2.5Nb
TEM Before TEM after 15 dpa
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Metal matrix average Nbcontent of 0.42 at% (cf0.45 at% in un-irradiated material.
No Clusters detected
FeNb
Zr
ZrO2
Sample B166 Zr-2.5%Nb650 keV Kr+ 5 dpa
Zr Nb Fe Cr C O Al
98.5 0.42 0.03 0.01 0.12 0.89 0.01
Kr ion irradiation to 5 dpa
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In flux and out of flux CNL samples have been studied to:
• Compare pore distributions between in flux and out of flux samples
• Analyse differences in oxide grain texture in autoclave and in-reactor samples
• Study the growth of nano-scale b-Nb precipitates during n-irradiation
• Analyse the rate at which Nb is oxidised in the oxide under different conditions
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Does neutron-irradiation
damage create extra porosity
in the ZrO2?
Fresnel contrast (±500 nm) bright
field TEM images from 2000-day
autoclave-corroded samples and
2700-day in-reactor sample (1022
n.cm-2, ~8 dpa).
Grain boundary nano-porosity is
formed in both oxides (yellow
arrows) and but voids in the grain
interior only in the n-irradiated
sample (blue circles).
Autoclave In reactor ~ 8 dpa
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Why are we interested in porosity? Because we can map directly
deuterium distributions in oxides. (See Jones et al this afternoon)
Distribution of 2H- and 18O- in a 61-day
Zircaloy-4 sample showing interconnected
pathways for deuterium.
Distributions of 2H- in a 700-day CNL
Zr-2.5Nb sample
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K. Li et al. Applied Surface Science 464, 311-320 2019
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Comparing pore distribution at different stages of oxidation
Autoclave 0.5%Nb samples after 75 and 165 days See Poster: Couet et al
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Neutron-irradiation damage in ZrO2: grain size and shape
TKD analysis of oxides on CNL Zr-2.5Nb tubes (a) In-flux, 190 days, 7.6x1020 n.cm-2 (2
dpa), (b) Out-of-flux, 185 days, (c) autoclave, 150 days and (d) autoclave, 700 days. 25
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All images taken at withB close to [11-20], g = (0002), 4-5g
Neutron induced nano-Nb precipitates
B70 B7426
B56: 250 oC, in flux, low damageNo detectible nano-Nb
B70: 325 oC, in flux , low damageSmall nano-Nb particles
B74: 325 oC, in flux , high damageLarger nano-Nb particles and numerous hydrides
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Morphology of Irradiation induced nano-precipitates
~ 4.5 nm
~ 2 nm
~ 1.5 nm
B70, In flux 190 days, 325⁰C27
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Material Number density(No./cm^3)
Average long axis (nm)
Average short axis (nm)
Aspect ratio
B70 1.9 dpa 1016 5 ± 1.3 2.4 ± 0.5 2.09
B74 25.2 dpa 5. 1015 8.3 ± 3.7 3 ± 0.9 2.71
Size and shape of nano-precipitates versus damage level
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5 10 15 200
2
4
6
8
10
12
14
16
18
20
22
24
Co
unt
long axis (nm)
B74
B70
1 2 3 4 5 60
2
4
6
8
10
12
14
16
18
Co
unt
short axis (nm)
B74
B70
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B62
B74
B56
B70The same CNL Haldenalloys have been analysed by APT
250 oC 190 days
250 oC 2400 days
325 oC 190 days
325 oC 2750 days
Nb
Residual b-Zr
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B70, APT & TEM results
Nb Fe
Grain boundary
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B74, APT & TEM results
Nb FeLine 1
EDX Nb line profile
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Precipitate number density
Sample
Number Density (No. per cm^3)
By APT By TEM
B70 1.3 x 1017 1016
B74 4.9 x 1016 5.5 x 1015
The factor of ~ 10 between APT and TEM results suggest that the precipitates/clusters inspected by APT and
TEM bright field image are different. Only those large, incoherent precipitates got picked up by the TEM bright
field image, while all the large and small, coherent and incoherent clusters were counted by APT.
4 nm
B74: Nb and Fe do not precipitate together
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Nb enrichment at c loops after 1.9 dpa
B70
EDX analysis of Nb segregation to c loops
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Matrix and cluster compositions from APT
Nb in matrixat %
Fe in matrixat %
Nb in clustersat %
B166 Un-irradiated 0.45 0.07 -
B56 250 oC 190 days 0.31 0.07 77
B62 250 oC 2400 days 0.31 0.06 66
B70 325 oC 190 days 0.27 0.06 76
B74 325 oC 2750 days 0.17 0.04 73
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2100 2200 2300 2400 2500 2600 2700
1000
2000
3000
4000
5000
6000
Nb L2
Nb L3
Zr L2
counts
Energy (eV)
Spectrum 1
Spectrum 2Zr L3
Identifying the oxidation rate of Nb in second phase particles by EELS
Edge shift of a specific edge indicates the change of oxidation state.
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Oxide
Metal
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Does the Nb oxidise at the same rate in different samples?
In particular, does more n-irradiation result in faster oxidation?
0 50 100 150 200
0
1
2
3
4
5
high damage
low damage
no damage
Nb
L3
Ed
ge
Sh
ift (
eV
)
Days in oxide for each individual Nb particles
Oxidation State of Nb in Beita Phase
• Oxidation rate of Nb in oxide: Out of flux > in flux low damage > in flux high damage
• Oxidation of Nb in β-Nb is slower than in β-Zr, so the decomposition of β-Zrresults in slower oxidation of Nb
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Conclusions
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• We have used in situ ion irradiation to study the stability of ZrO2 and metastable ZrO
oxide phases to high damage levels. The susceptibility of both phases to phase
changes has been shown.
• The extraordinary resistance of b-Nb SPPs to radiation damage has been confirmed
• Detailed analysis of the nano-structure of CNL 2.5% Nb samples after n-irradiation has
revealed the details of precipitation and changes in matrix chemistry during reactor
exposure.
• The oxidation rate of Nb (and so doping of the oxide phase) is remarkably slowed
down by n-irradiation.
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Acknowledgements
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• EPSRC grants (EP/K040375/1, EP/N010868/1 and EP/M018237
• access to the Culham Materials Research Facility.
• electron Physical Science Imaging Centre (ePSIC) on the Harwell campus for access
to the JEOL ARM300CF instrument.
• Access to the IVEM facilities at ANL was provided through the NSUF RTE
scheme
• Access to the MIAMI2 facilities was provided through the EPSRC UK National
Ion Beam Centre (http://www.uknibc.co.uk/).