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Department or office title: change on Slide Master
High resolution characterization of corrosion and hydrogen pickup of Zr-Nb cladding alloys Jing Hu, Brian Setiadinata, Thomas Aarholt, Alistair Garner, Arantxa Vilalta-Clemente, Jonna Partezana, Philipp Frankel, Paul Bagot, Sergio Lozano-Perez, Angus Wilkinson, Michael Preuss, Michael Moody, Chris Grovenor • Department of Materials, University of Oxford, Parks Road, Oxford, UK • School of Materials, University of Manchester, Manchester, UK • Westinghouse Electric Company, 1332 Beulah Road, Pittsburgh, USA
MUZIC-2 (Mechanistic Understanding of Zirconium Corrosion and
Hydrogen Pickup) consortium
Work on oxidation of Zr started in Oxford in 2007 with UK research council funding (MUZIC-1)
• In phase 1 we asked ourselves a set of questions
• Can Atom Probe tomography be applied to studying oxidation mechanisms?
• Can new techniques developed in electron microscopy give new insight?
• Are there completely new experimental approaches that are worth studying?
A brief introduction
500 nm
oxide metal
Local Electrode Atom Probe
Datasets of
100s of
millions of
atoms
First APT analysis of oxidised Zr samples (Dan Hudson) -shows 3D shape of interface as well as identifying a ZrO stoichiometry
Zr (green),
ZrO (blue),
O2 (orange)
3D visualisation by FIB sectioning (Na Ni)
FIB 3D imaging [1]
Several hundred
individual images 20
by 5 microns
combined to make an
image of the cracks
and of the
metal/oxide interface
morphology
[1] Ni ect. Corr Sci (2011)
Interconnected porosity (Na Ni)
50 nm
Use Fresnel Imaging technique in TEM to visualise porosity evolution in Zr oxide
Cartoon of the oxide structure
Pores at the
monoclinic ZrO2 grain
boundaries gradually
reach the metal/oxide
interface
20 nm
Where is the protective oxide?
From these
observations, we
proposed that the
protective oxide
identified by
electrochemical
methods as the
region under the
interconnected
porosity [2]
[2] Na Ni Dphil thesis (2011)
Can correlate specific oxidation
events with local microstructure
NanoSIMS observation of 18O/16O ratio [3]
High
resolution
SEM images
shows a
vertical crack
propagates
far into the
oxide
200 nm
SIMS imaging of 18O spiking
[3] Yardley, Ni ect. JNM (2013)
Phase 2: Ab initio modelling of ZrO phases
Identifies a stable hexagonal ZrO phase [4]
[4]Nicholls et al 2014 Advanced Engineering Materials
Phase 3: new questions
Since 2012 [MUZIC2] we have been asking different questions
• Is the ZrO phase this predicted hexagonal phase (and why do we care about ZrO)?
• What is the role of SPPs?
• Can we directly study H transport mechanisms in the oxide?
• Are there any even newer techniques that will give us new information?
Why study RXA Zr-1.0Nb?
RXA Zr-1.0Nb (Zr-1%Nb-0.01%Sn-0.1%Fe)
• RXA Zr-1.0Nb showed delayed transition than ZIRLO [5]
• Hydrogen pickup fraction (HPUF): 12% RXA Zr-1.0Nb vs 16% ZIRLO [6]
(Zr-1%Nb-1%Sn-0.1%Fe)
Transition
~140 day ~360 day
[5] Wei, J. et. al. (2012). Corrosion Engineering, Science and Technology. [6] Romero, J. et. al (2015). TopFuel 2015
Why study RXA Zr-1.0Nb? – Even better neutron irradiation performance
~ 5.2 μm autoclave
~ 2.2 μm reactor
RXA Zr-1.0Nb in autoclave
RXA Zr-1.0Nb in reactor
Why study annealed Zr-1.0Nb? – Heat treatment can change the corrosion and HPU
Recrystallised
Annealed
• Almost four time corrosion rate after the 720°C heat treatment. [5]
• Hydrogen pickup fraction (HPUF): 12% RXA Zr-1.0Nb vs 9% Annealed Zr-1.0Nb [6]
SPP: β-Nb →β-Zr
[5] Wei, J. et. al. (2012). Corrosion Engineering, Science and Technology. [6] Romero, J. et. al (2015). TopFuel 2015
Recrystallised X2 RXA Zr-1.0Nb in autoclave
RXA Zr-1.0Nb in reactor
Sample Overview
Oxide
Metal
Pt protective layer
120-day H2O Early-trans
225-day (180-day H2O +45-day D2O) Mid-trans
360-day H2O Transition
3-day H2O Early
585-day (540-day H2O +45-day D2O) Post second-trans
540-day In reactor
1 um
Oxide microstructure by TKD
RXA Zr-1.0Nb 360-day transition
• Equiaxed-columnar-equiaxed grain structure • Very organised microstructure [7]
2um Metal
Oxide
[7] Hu, J. Garner, A. et al. Micron 69, 35–42 (2015).
Oxide microstructure by TKD
2um
360-day transition
585-day Post-transition
RXA Zr-1.0Nb neutron irradiated 540-day
• Equiaxed-columnar-equiaxed grain structure • Very organised microstructure • Fewer cracks • Longer columnar grains
Hu, J. et al. Micron 69, 35–42 (2015). Garner, A., Hu, J. et al, Acta Materialia, 99, 2015
RXA Zr-1.0Nb in autoclave
Wider, shorter grains Very few cracks
ASTAR oxide phase analysis
120-day RXA Zr-1.0Nb 46-day annealed Zr-1.0Nb
• More tetragonal phase throughout the oxide ( especially far from crack)
• Non-uniform suboxide distribution, Left-thicker suboxide, right ( 2nd tran)- thinner. [9]
• Mostly monoclinc, 3% tetragonal phase scattered, mostly at M/O
• Saw-tooth suboxide along M/O
[4] Nicholls, R. J. et al. Adv. Eng. Mater. (2014).
[8] B. Puchala and A. Van der Ven (2013)
[9] Hu ect. TopFuel 2015
Hexagonal ZrO phase with P-62m symmetry
lattice parameters a=5.31 Å and c=3.20 Å[4,8,9]
2nd transition cracks
• EELS mapping and TKD tells us that there are 2 kinds of Zr-O regions at the metal/oxide interface:
1) Hexagonal ZrO and 2) oxygen-saturated zirconium metal • Their thicknesses vary enormously with position and stage of
oxidation, but the combined region forms an uniform protective layer
Low loss EELS mapping +MLLS fitting*
*Electron Energy Loss Spectroscopy (EELS) + Multiple Linear Least Squares (MLLS) fitting
RXA Zr-1.0Nb 360-day transition
Zr-O layer across M/O in RXA Zr-1.0Nb
This is not one line profile, this is hundreds of line profile across the mapping area of 10 um width.
• Saw-tooth shape suboxide + oxygen saturated Zr form an uniform protective layer
• Combined layer undergoes cycle growth, drops at transition
Transition
Exposure (days)
Thickness (um)
Correlating Zr-O with instantaneous oxidation rate
ZIRLO
ZIRLO
• SPPs are too far apart to directly influence transport processes
3D FIB
reconstruction
What is the role of SPPs?
• Widely reported that SPPs gradually become amorphous and dissolve in the growing oxide
• This must dope the oxide locally with Fe2+, Cr3+ Nb5+
[10] Anada, H., Herb, B. J., Nomoto, K., Hagi, S., Graham, R. A., Kuroda, T. (1996)
Zirconium in the Nuclear Industry: Eleventh International Symposium, ASTM STP 1295, American Society for Testing Materials p. 74-93.
Page 37
surrounding oxide. It is generally agreed that SPP in the oxide film readily oxidise [70]. This
process is illustrated in Figure 13. Metallic precipitates do not oxidise until they are completely
surrounded by the oxide [115], before this their metallic character is retained within the oxide
[116]. EDX showed that Ni and Cr also diffused away from precipitates in the oxide, although at
a lesser rate than Fe [89]. Anada et al. [117] reported that a transformation from columnar grains
to equiaxed grains was observed predominantly around the oxidised precipitates and that
oxidation of the precipitates was the cause of an accelerated corrosion.
Figure 13: Schematic of the effect of iron diffusion from intermetallics precipitates in the oxide
film on Zircaloy-4 [117].
What is the role of SPPs?
SPP analysis from Atom Probe Tomography
Zr metal
Suboxide 100 nm
Nb Zr
Fe
ZrO
• dislocations at suboxide/metal interface.
decorated with Fe atoms • β-Nb particles: Containing ≈ 85at% Nb and ≈13at% Zr at the core. Fe segregates to interface. This Fe segregation is rapidly lost to the oxide as the SPPs oxidise
Line profile through SPP-metal interface
(Brian Setiadinata)
[9] Hu ect. TopFuel 2015
Beta-Nb (smaller) + Zr-Fe-Nb SPP (larger) Both rather stable in oxide
RXA Zr-1.0Nb in autoclave RXA Zr-1.0Nb in reactor
Beta-Nb + Zr-Fe-Nb SPP Fe dissolves under irradiation Cr dissolves slower j
EDX mapping on SPPs in RXA Zr-1.0Nb
Hu ect. TopFuel 2015
EELS study of SPP oxidation state
EELS study on SPP oxidation state
XANES data also shows a similar trend. SAMAKOTO et al Topfuel (2012)
Gradual oxidation of Nb from 2+ to 5+ from M/O to top surface
Where should we worry about doping?
Protective Oxide
Both Nb and Fe released from the SPPs may contribute to doping the oxide or reducing space charge build up
H+
2H-
3D SIMS profiling of deuterium
Depth profile of top 1.2 um of 1.7 um oxide layer Deuterium segregation to horizontal cracks and to linear features through the oxide thickness?
APT of deuterium at oxide grain boundaries
D+ ions OD+ ions Grain boundary map
Similar observations in: Sundell, G et al (2015) Direct observation of hydrogen and deuterium in oxide grain boundaries in corroded Zirconium alloys. Corrosion Science 90:1-4.
50 nm
Zr 2.5% Nb CANDU sample (provided though MUZIC2 project)
Porosity study: Fresnel imaging
RXA Zr-1.0Nb in
autoclave 225-day
100nm from the metal-
oxide interface:
a) interconnected pores parallel to M/O
b) vertically interconnected pores along the columnar oxide grain boundaries
a) b)
Underfocus:
Overfocus:
Oxide growth direction
[9] Hu ect. TopFuel 2015
Porosity in ex-reactor and autoclave
Oxide growth direction
RXA Zr-1.0Nb in reactor
• Very little porosity in reactor vs in autoclave
Annealed Zr-1.0Nb in autoclave • Lots of interconnected porosity
along grain boundaries vs RXA Zr-1.0Nb in autoclave and in reactor
Conclusions
Equiaxed oxide
Columnar oxide
Suboxide
Metal
RXA Zr-1.0Nb with better oxidation resistance and lower HPU. Compared with ZIRLO and annealed Zr-1.0Nb, it has: • Fewer cracks, more organised and longer
columnar grain structure • Porosity along equiaxed and columnar
GBs. Porosity content is much lower in neutron irradiated RXA Zr-1.0Nb.
• Two types of SPPs, β-Nb and Zr-Nb-Fe and gradual oxidation of Nb from 2+ to 5+ from M/O to top surface.
• Thicker Zr-O region when oxidation rate is slower
• New experimental techniques can help understand the oxidation and HPUF performance of Zr fuel clad alloys.