oxidation and hydrogen-pickup, and connections to higher...

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Atomistic modeling of unit processes for oxidation and hydrogen-pickup, and

connections to higher length scale models

Mostafa Youssef, Jing Yang, Ming Yang, Bilge Yildiz

Laboratory for Electrochemical Interfaces Department of Nuclear Science and Engineering, Department of Materials Science and

Engineering, Massachusetts Institute of Technology

Collaborators to whom we provide input: Mike Short (MIT); Jaime Marian (UCLA); Dane Morgan, Izabela Szlufarska (UW-Madison)

Update for CASL Leadership Review at MIT, 04.30.2015

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Picture from Phase I

A new framework is to be developed with newly added colleagues (Jaime Marian, UCLA; Donghua Xu, UTK), and without Morgan, Szlufarska and Thornton, in Phase II.

Zr Alloy

Coherent ZrO2 (Barrier Layer) Porous ZrO2

SPP

SPP

SPP

Suboxide ZrO2-x

Planar Compression

Predominantly Tetragonal

Predominantly Monoclinic

Oxygen diffusion

[1] A. T. Motta et al., JAI 5 (2008). [2] A. Yilmazbayhan et al., J. Nucl. Mat. 324, 6 (2004).

Objective: Develop and provide atomistic and quantitative models for ZrO2 as input to continuum level corrosion and hydrogen pickup models

T M H2O

H+

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M. Youssef and B. Yildiz Phys. Rev. B (2012 and 2014) and PCCP (2014)

+ one in review, and one in preparation

Kröger-Vink Diagram for tetragonal ZrO2

Density Functional Theory

Statistical Thermodynamics

Dilute Charged Defect Equilibria in a Metal Oxide

Oxygen Self-diffusion in ZrO2

Tetragonal-Monoclinic transition

Hydrogen solubility

Interplay between stress and H

Corrosion of zirconium alloys

H-pickup of Zirconium alloys

σ σ

Contributions in phase I

Equilibria of point defects

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Oxygen Self-diffusion in ZrO2

Corrosion of zirconium alloys

DO(T,PO2) = Defect Concentration x Mobility





Connecting our work to others

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x δ

ZrO2+x Zr ZrOδ -0.05<x<0.00 oxide

0.0<δ<1 metal

Van der Wen UMich

Yildiz MIT

1- Combine Density Functional Theory (DFT) calculations with statistical mechanics modeling to compute temperature and composition dependent oxygen diffusivity: D (T,x)

D(T,x) MAMBA/

BDM Short MIT

Peregrine Montgomery

ANATECH

2- Feed MAMBA/BDM and Peregrine with the calculated diffusivities.

Oxygen diffusion (T, PO2) = concentration x migration Provides input for the oxidation model, HOGNOSE (Short)

Migration barriers (eV) calculated using CI-NEB method

Random Walk Diffusion Theory

log PO2 (atm)

Kröger-Vink diagram

M. Youssef and B. Yildiz Phys. Rev. B (2012 and 2014)

Oxygen diffusion coefficient (T, PO2)

Validating the overall oxygen self-diffusivity

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Experiments: Park and Olander, J. Electrochem. Soc. (1991)

Impurities explain the small difference from the experimental data.

M. Youssef and B. Yildiz Phys. Rev. B (2012 and 2014)

Equilibria of point defects

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Hydrogen solubility

H-pickup of Zirconium alloys





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Coherent ZrO2 (Barrier Layer) Porous ZrO2

SPP

SPP

SPP

Sub-oxide ZrO2-x

Planar Compression

[1] A. Yilmazbayhan et al., J. Nucl. Mater. 324, 6 (2004). [2] A. Couet et al., J. Nucl. Mater. 452, 614 (2014).

Hydrogen pickup through barrier Zr-oxide

H+

H ingress - Detrimental Fe, Cr, Ni, Sn, Nb …

H

H

~20 µm

Zirconium alloy degradation in nuclear reactors

The key point we build in this topic: The ‘valley’ of hydrogen absorption on the electron chemical potential space of the Zr-oxide M. Youssef and B. Yildiz (in review, 2015) •We uncovered the electron

chemical potential (or, equivalently the Fermi level, EF) as the descriptor of the absorption of hydrogen into ZrO2.

•Higher EF accelerates H-reduction and H2 gas evolution at the surface. Good!

•Provides a physics-based guide for Zr-alloy design to minimize H-pick-up. •Provides H-solubility values for the hydrogen-pick-up models.

The volcano of H-pickup into Zr alloys

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B. Cox, M. J. Davies, A. D. Dent, The Oxidation and Corrosion of Zirconium alloys, Part X., Hydrogen Absorption during Oxidation in Steam and Aqueous Solutions, HARWELL, AERE-M621 (1960).

Explaining this volcano may facilitate faster design of Zr alloys

T = 573 – 773 K 1-5 % alloying

Range of pure Zr

• No physical explanation for this intriguing behavior, since 1960s.

• It takes 40 years to design and qualify alloys for nuclear reactors.

Simplified picture for H-pickup

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H solubility in the oxide

H+ Reduction / H2 Evolution

Transition Metal

Design Explanation

e-

M. Youssef and B. Yildiz, in review (2014)

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The volcano of hydrogen solubility in ZrO2

T= 600 K

•iH ///

ZrH

•iH ///

ZrH

Valley of hydrogen solubility on the µe space

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•iH ///

ZrH

Kinetic acceleration of H+ reduction and H2 evolution

Thermodynamic minimization of H solubility

e-


3d transition metals on the valley to design alloys

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•iH ///

ZrH


Thermodynamic minimization of H solubility

e-


Niobium on the valley to design Zr alloys

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•iH ///

ZrH


e-

Nb defects in ZrO2: U. Ootganbatar, M. Youssef,

W. Ma and B. Yildiz, J. Phys. Chem. C (2014)

µe ↑ e- conductivity ↑ H+ reduction ↑

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Conduction

)exp(TkEn

B

CBMec

−∝∝

µσ

*A. Couet et al., J. Nuc. Mater. 451,1, (2014) Nb increases µe 104 times faster e conduction improved H resistance(*)

⇒ ⇒

Unexplored elements on the valley to design alloys

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•iH ///

ZrH


e-

Comparison of cost and availability

20 http://www.infomine.com/investment/ , https://www.metal-pages.com/metalprices/ , http://www.chemicool.com/

Cost Availability

http://www.infomine.com/investment/

https://www.metal-pages.com/metalprices/

http://www.chemicool.com/

Conclusion 1 The volcano of H solubility in ZrO2 provides an explanation for the volcano of H-pickup in Zr.

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H solubility in ZrO2 H pickup in Zr

n-type doping is a viable design strategy for H-resistant Zr alloys. - Gain at least a decade from the design timeline

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Conclusion 2

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Plans for Phase II: Corrosion and H-pickup processes in ZrO2, investigated at the atomistic level, as input to mesoscale models: - Effect of stress and extended defects

(including precipitate phase boundaries; grain boundaries) on O-diffusion and H-pickup and diffusion.

- Fracture criteria for ZrO2 based on stress, phases, and Li content

- Surface reactions at water/ZrO2 interface (source term for corrosion and H-pickup)

- Guided by experiments of Was (UM). - Provide quantitative input to the

continuum level H-pick up models (used to be of Morgan & Szlufarska at UW-Madison) and mesoscale oxidation / corrosion model of M. Short at MIT, and Jaime Marian at UCLA.

Surface Reactions H & O-incorporation,

H+ reduction O- and H-transport,

H-solubility

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Dominant Hydrogen Diffusion Path and Barriers (this is leveraged by a student (Ming Yang) on fellowship, and not by CASL funds)

CRYSTAL STRUCTURE-MONOCLINIC ZRO2

Zr O4 H O3 O3

O3

O4

Hopping 1 in O3

Inner sub plane Eforward=0.47 eV Ebackward=0.42 eV

Inner sub plane Eforward=0.27 eV Ebackward=0.22 eV

Inter sub plane Eforward=0.47 eV Ebackward=0.42 eV

Hopping 2 in O3 Rotating in O3

Hopping 1 and Rotating are the two rate-limiting-step (0.47 eV), while hopping 2 is relatively easier (0.27 eV).

Hydrogen attached with O4 plane is 0.5 eV higher than hydrogen attached with O3 plane. Hydrogen will diffuse in the O3 plane for the most of time.

Any diffusion path can be constructed from the three elementary step.

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Modeling the interfaces between ZrO2 and oxidized Intermetallic Precipitates as a path for oxygen and hydrogen ingress

Zr(Cr,Fe)2 precipitates incorporated into the oxide layer on Zircaloy-4

D. PBcheur, F. Lefebvre, A.T. Motta, C. Lemaignan, J.F. Wadier, J. Nucl. Mater., 1992, 189, 318 Y. Hatano and M. Sugisaki, Journal of Nuclear Science and Technology, 1997, 34 (3), 264-268

Schematic diagram of oxide film of Zr(Cr,Fe)2 precipitate with Cr2O3 layer at the top surface

• Corrosion rate depends on the nature of the protective oxide formed • Secondary phase particles formed in zirconium oxide layer • Study oxide interfaces to understand the defect distribution in protection layer

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Defect Equilibria at Oxide Interfaces: DFT + Continuum Model

ZrO2 Cr2O3

• Defect formation energy in bulk/across interface is calculated from DFT • Bulk defect concentration profile is used as boundary condition for continuum model

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Continuous model:

Flow chart for solving defect concentrations across the interface under different temperature and oxygen partial pressure

2ε ρ∇ Φ = −∑Poisson’s Equation

Drift-diffusion Equation .

2 2

2 2[ (1 ) (1 2 ) ] 0D DD D

BD

Dqd c dcd dc c cdx dx

ek dx dxT

Φ Φ+ − + − =

.2 2, , ,

,2 2( ) 0e h e h e he h

B

d c q e dc d dcdx k T dx dx dx

Φ Φ+ + =

Equilibrium Condition

0dxρ =∫

Defect Equilibria at Oxide Interfaces: DFT + Continuum Model

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Yue Fan, Sidney Yip and Bilge Yildiz Department of Nuclear Science and Engineering, Massachusetts Institute of Technology

Collaborators: Yuri Osetskiy, Stas Goulubov, Roger Stoller (ORNL) & Blas Uberuaga, Art Voter, Carlos Tome (LANL)

Update for CASL Leadership Review at MIT, 04.30.2015

Dislocation Interactions in Zr for Clad Creep, Growth and Plasticity

The team, topics and methods in PCI-CLAD (vision until 2013)

• TAD method

• Cluster mobility vs size

• Point defect absorption by dislocations

LANL

• ABC method

• interaction between mobile dislocation and obstacles (voids, loops, SIA clusters)

MIT

• Dimer+KMC method

• Cluster mobility vs size

• Dislocation bias on different types of defects

ORNL

benchmark different methods on a unit process

a< >

c< >

VPSC

growth RDT

Climb vs. glide

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Point defects anisotropic diffusion in Zr

benchmark with new methods in MPO Vacancy and SIA migration

Contributions till 2013

Moving dislocation interaction sessile cluster important unit process for creep/growth strain rate effects on mechanisms low rate: SIA absorption high rate: defects recovered

Yield strength of structural materials flow stress upturn at high strain rate strain-rate sensitivity important

input to VPSC creep model

Constitutive relations as interface to VPSC of LANL

Publications: creep; corrosion/hydrogen 1. “Autonomous basin climbing method with

sampling of multiple transition pathways: application to anisotropic diffusion of point defects in HCP Zr”, in Journal of Physics: Condensed Matter, 2014.

2. “Mapping Strain-rate Dependent Dislocation-Defect Interactions by Atomistic Simulations in Zirconium”, in Proceedings of the National Academy of Sciences, 2013.

3. “Onset mechanism of strain rate induced flow stress up-turn”, in Physical Review Letters, 2012.

4. “Mechanism of Incipient Void Swelling in bcc-Fe: Atomistic Simulations at Experimental Time Scales”, in Physical Review Letters, 2011.

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1. “Hydrogen Defects in Tetragonal ZrO2 Studied Using Density Functional Theory”, in Physical Chemistry Chemical Physics, 2014.

2. “Predicting Self-Diffusion in Metal Oxides from First Principles: The Case of Oxygen in Tetragonal ZrO2”, in Physical Review B, 2013.

3. “High Surface Reactivity and Water Adsorption on NiFe2O4 (111) Surfaces”, in Journal of Physical Chemistry-C, 2013.

4. “Intrinsic Point Defect Equilibria in Tetragonal ZrO2 - Density Functional Theory Analysis with Finite Temperature Effects”, in Physical Review B, 2013.

5. “First-Principles Assessment of the Reactions of Boric Acid on NiO (001) and ZrO2 (-111) Surfaces” (a CRUD material), in Journal of Physical Chemistry-C, 2012.

6. “Doping on the Valley of Hydrogen Solubility: A Route to Design Hydrogen Resistant Zirconium Alloys”, under review, 2015.

7. “Tetragonal-to-monoclinic transition mediated by oxygen vacancies in zirconia” in preparation, 2015.

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Back-up slides next….

Framework to predict the equilibria in ZrO2 co-doped with a metal and hydrogen

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∑∑ =−+d q

cvq npdq 0][

Charge Neutrality Condition

Point Defects Free Holes Free Electrons

0 K formation energies using Density Functional Theory (PBE functional)

Finite-T excitation using Density Functional Theory (phonons using harmonic approximation )

Apply charge neutrality and construct Kröger-Vink diagram

[2] A. Van de Walle, G. Ceder, Rev. Mod. Phys. (2002) [3] N. Ashcroft, N. Mermin, solid state physics, (1976)

[1] Vienna Ab initio Simulation Package (VASP) [4] F. Kröger, H. Vink, Sol. Stat. Phys., (1956)

HYDROGEN

Native

Transition Metal

[5] M. Youssef, B. Yildiz, Phys. Rev. B, (2012)

Defect equilibria in co-doped monoclinic ZrO2

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Extract µe for H+ reduction/evolution

Extract the solubility of H

e-

Zinc + Hydrogen in ZrO2 at 600 K

BAD!

GOOD!

oxidation and hydrogen-pickup, and connections to higher...

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