Mass transfer modeling for LM blankets

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Mass transfer modeling for

LM blankets

Presented by Sergey Smolentsev (UCLA) with contribution from:

B. Pint (ORNL)

R. Munipalli, M. Pattison, P. Huang (HyPerComp)

M. Abdou, S. Saedi, H. Zhang A. Ying, N. Morley, K. Messadek (UCLA)

S. Malang (Consultant, Germany)

R. Moreau (SIMAP, France)

A. Shishko (Institute of Physics, Latvia)

Fusion Nuclear Science and Technology Annual Meeting

August 2-4, 2010

UCLA

In this presentation:

• Status of R&D on development of MHD/Heat & Mass

Transfer models and computational tools for liquid metal blanket applications

• Examples : corrosion & T transport

OTHER RELATED PRESENTATIONS at THIS MEETING

TITLE Presenter Oral/Poster

Tritium Transport Simulations in LM

Blankets

Modeling Liquid Metal Corrosion

Integrated Modeling of Mass Transport

Phenomena in Fusion Relevant Flows

H. Zhang

UCLA

S. Saedi

UCLA

R. Munipalli

HyPerComp oral poster poster

Mass transfer in the LM flows is one of the key phenomena affecting blanket performance and safety

Traditionally, major considerations associated with the LM flows are the

MHD effects . But there are more….

Tritium permeation is an issue – no solution has ever been proven

Corrosion/deposition severely limits the interfacial temperature and thus represents an obstacle to developing attractive blankets at high temperature operation

Blanket: “Hot” leg. Mass transfer coupled with MHD. Corrosion. T production. T leakage into cooling He. Formation of He bubbles in PbLi and trapping T.

Ancillary system: “Cold” leg. Turbulent flows. Wall deposition and bulk precipitation.

T leakage into environment. T extraction. Cleaning up.

Main objectives of mass transfer modeling

Blanket:

• Revisit maximum PbLi/Fe t (470 

?) and wall thinning (20

 m/year ?)

• Estimate T leakage into cooling He streams in the blanket

Ancillary system:

• Estimate T leakage into environment

• Model T extraction processes

• Model clogging/deposition

• Model clean up processes

Phenomena, design:

• Address “new” phenomena (i.e. He bubble formation in PbLi and trapping T by the bubbles)

• Find new design solutions/modifications

Challenge!

The whole PbLi loop, including the blanket itself and the ancillary equipment, must be modeled as one integrated system

What do we need?

• New phenomenological models for :

interfacial phenomena

- nucleation/crystallization

- particle-particle/wall interaction

- MHD effects on mass transfer

- T transport physics He bubble transport and trapping T by the bubbles is not well understood

• New material databases (He-T-PbLi)

• New mass transfer solvers and their coupling with existing MHD/Heat Transfer codes

What tools do we use?

• HIMAG as a basic

MHD/Heat Transfer solver

• Many UCLA research

MHD, Heat & Mass transfer codes

• CATRIS (in progress) as a basic mass transfer solver

• Many thermohydraulic / mass transport codes

The R&D on the development of new phenomenological models and their integration into numerical codes is underway

CATRIS: MATHEMATICAL MODELS

1. Dilution approximation, C i

< C i0

C i

 t

( V

) C i

 

( D C i i

)

 q i

2. Lagrangian particle tracking, C i

> C i0

 p

V d V p dt

 k

K 

1

F k

3. Multi-fluid model, C i

>> C i0

  i

 t

   i

V i

 j

N 

1

J ij

 

V i i

 t

  k

 i

V i

V i k   k σ i k   i g  j

N 

1

P ij

MODELING EXAMPLES

Example

#1

Riga experiment

#2

Tritium transport

#3

Magnetic trap

#4

Sannier equation

Description

Modeling of “corrosion” experiment in

Riga, Latvia on corrosion of

EUROFER samples in the flowing

PbLi at 550

 in a strong magnetic field

Numerical analysis of tritium transport in the poloidal flows of the DCLL blanket with SiC FCI under DEMO blanket conditions

Modeling of extraction of ferrous material suspended in the flowing liquid in a magnetic trap

Modeling of corrosion of ferritic/martensitic steels in turbulent

PbLi flows to reproduce existing experimental data and to address the effect of a magnetic field

Modeling status

Good match with experimental data on mass loss. Addressing groove patterns needs more sophisticated modeling.

Analysis for the front duct of the

DCLL DEMO OB blanket has been done using a fully developed flow model.

First “demo” results have been obtained using Lagrangian particle tracking model under some assumptions for B~ 0.1 T.

In progress. Computations are performed using the UCLA corrosion code (Smolentsev).

Turbulence in a magnetic field is modeled via “k-eps” model.

Riga experiment 1/11:

setup

Simulation of “CORROSION” EXPERIMENT in Riga

PbLi loop

EUROFER samples

B=0, B=1.7 T

T=550

C

U=2.5 cm/s, U=5 cm/s

Time=2000 hours

Rectangular duct, 2.7x1 cm 2

Courtesy of Dr. Andrej Shishko, Institute of Physics, Latvia

Two 12-cm sections of 10 samples in a row, one section at B=0 and one at

B=1.7 T

Riga experiment 2/11:

results

Mass loss, mg

U o

=2.5 cm/s U o

=5 cm/s

Macrostructure of the washed samples on the Hartmann wall in 3000 hrs at 550

B=0 B=1.7 T

9

10

6

7

8

#

1

2

3

4

5

B=0,T

376

245

303

193

223

257

163

198

B=1.7,T

593

564

481

486

456

440

483

484

B=0,T

437

338

330

283

251

248

-

310

B=1.7,T

743

757

623

605

506

482

-

512

214

205

566

502

321

314

463

474

Mass loss is almost doubled in the presence of B-field

PbLi flow

Courtesy of Dr. Andrej Shishko, Institute of Physics, Latvia

Riga experiment 3/11:

results

~40

 m

FLOW

~ 500

 m

•Wall thinning: 1.5->1.4 mm

•Grooves: 40  m deep

Courtesy of Prof. Rene Moreau (SIMAP, France)

• In addition to wall thinning, periodic grooves aligned with the flow direction have been observed on the Hartmann wall

• Mechanism of groove formation is still not well understood

• A. Shishko (Latvia): higher velocity in the surface cavities causes higher corrosion rate.

The effect may be related to specimen machining

• R. Moreau (France): the grooves are due to instability mechanism associated with induced electric currents crossing the interface

Riga experiment 4/11:

mathematical model

Basic assumptions

• Fully developed, laminar flow

• Only Fe is considered

• Purely dissolution mechanism

• No oxygen passivation layer

• Mass transfer controlled corrosion

• Zero Fe concentration at x=0

Two BC types have been tested

(C

0 is the saturation concentration at given t)

2 z

U U

2

2 y

2

B

0



0

2 z

2

2

B B y

2

 

B

0 0

B

 z

U

 z

1

0 dP dx

0 z

  b : U

0, y

  a : U

0,

1

1

B

 z

B

 y

1 B

 t w w

1 B w t w

0

0

U

C

 x

D (

 2

 x

C

2

2 y

C

2

2 z

C

2

) x

0 : C

0 z

  b : D y

  a : D

C

 z

C

 y

(

0

C )

0

(

0

C )

0 or C

C

0 or C

C

0

Riga experiment 5/11:

material properties *

• Diffusion coefficient Fe-PbLi:

6.4E-09 m 2 /s **

• Saturation conc. C

0

: 6.26 g/m 3 ***

• PbLi viscosity: 1.08E-07 m 2 /s

• PbLi density: 9300 kg/m 3

• PbLi electrical conductivity:

0.7E+06 S/m

• Ha= 0 and 227.3 (1.7 T) ; C w

= 0.78

;

Re= 1157 and 2314

* At 550

C

** Based on equation of Sutherland-Einstein

*** Recommended by Riga people (=0.676 wppm).

100

Solubility of Fe in PbLi

0.1

0.01

10

1

Solubility experiments

Barker et al., 1988

Borgstedt et al., 1991

Grjaznov et al., 1989

Riga group, 2006

0.001

0.0001

1E-005

600 650 700 750 800 850

T, K

C o

: more than THREE order of magnitude difference ???

Riga experiment 6/11:

modeling results

B=1.7 T, Cw=0.78, U=2.5 cm/s

0.05

B=0, U=2.5 cm/s

0.04

B=0, U=2.5 cm/s

0.03

0.02

0.01

B=1.7 T, U=2.5 cm/s

0

-0.005

-0.003

-0.001

0.001

0.003

0.005

Z, m

Riga experiment 7/11:

modeling results

MASS LOSS: comparison with the experiment

BC : D

C

 n

(

0

C )

0

Riga group: C

0

=6.26 g/m 3 , K=4.27E-05 m/s

430

215

BC : C

C

0

Konys: 700

 m/year

500

C, 0.22 m/s, 0T

Grjaznov et al: C

0

=3.25 g/m 3

Riga experiment 8/11:

modeling results

Effect of the velocity and B-field on the wall and bulk concentration

BC : D

C

 n

(

0

C )

0

Riga group: C

0

=6.26 g/m 3 , K=4.27E-05 m/s

Riga experiment 9/11:

modeling results

Effect of the velocity

- no magnetic field

- Hartmann wall

Effect of B-field

-Hartmann wall

Wall effect

- with magnetic field

Riga experiment 10/11:

modeling results

Development length > 10 m (B=1.7 T, U=5 cm/s)

Wall concentration

Bulk concentration

BC : D

C

 n

(

0

C )

0

Riga group: C

0

=6.26 g/m 3 , K=4.27E-05 m/s

Riga experiment 11/11:

conclusions

• Riga experiment on EUROFER-PbLi corrosion has been successfully modeled (not including grooves)

• Higher corrosion rate of EUROFER samples in a presence of a magnetic field can be explained by the steep velocity gradient in the Hartmann layer

• Boundary condition at the solid-liquid interface is still an open issue. Saturation concentration at the wall can be used as a first approximation

• Uncertainty in experimental data on transport properties

( e.g.

saturation concentration) severely limits modeling predictions

• If to extrapolate to LM blanket conditions - the mass transfer development length can be more than 10 m

Tritium transport, 1/6

DCLL Geometry (not to scale)

• DCLL DEMO blanket conditions (outboard)

• Poloidal flow in a front duct with a 5-mm SiC/SiC FCI

• HIMAG is used to simulate

MHD flow, assuming fully developed flow conditions

• CATRIS is used to simulate tritium transport in the multi-material domain, including PbLi flow, SiC

FCI and Fe wall

• Goals : ( 1 ) T permeation into He; ( 2 ) sensitivity study

0.3 m

B z

FCI x y

Outflow

Inflow

RAFS wall 5 mm thick y

SiC wall 5 mm thick z

207 mm

231 mm

2 mm gap

211 mm

•Neutron wall loading (peak): 3.08 MW/m 2

•Surface heating: 0.55 MW/m 2

•PbLi Tin/Tout: 500/700

C

•Flow velocity: 6.5 cm/s

•Magnetic field: 4 T

•Inlet T concentration: 0

•T generation profile:

4.9E-09 Exp(-3y), kg/m 3 -s

Tritium transport, 2/6

Pb17Li

Physical properties

RAFS SiC FCI

Solubility mol/m 3 /Pa 0.5

[1,2,3]

0.0005

0.1

D m 2 /s

1.0 × 10 -9

7.0 × 10 -9

Solubility mol/m 3 /Pa 0.5

[4]

0.0025

D m 2 /s

Solubility mol/m 3 /Pa 0.5

1.5

× 10 -8 0.117

D m 2 /s

σ

S/m

[5,6]

5.0

× 10 -16 5

500

Low

High

1.

Mas de les Valls, E., Sedano, L.A., Batet, L., Ricapito, I., Aiello, A., Gastaldi, O., Gabriel, F. (2008) Lead-lithium eutectic material database for nuclear fusion technology . J. Nuc. Mat. 376 , 353-357.

2.

Reiter, F. (1991) Solubility and diffusivity of hydrogen isotopes in liquid Pb-Li.

Fusion Eng. and Design. 14, 207-211.

3.

Aiello, A., Ciampichetti, A., Benamati, G. (2006) Determination of hydrogen solubility in lead lithium using sole device.

Fusion Eng. and Design. 81, 639-644.

4.

Aiello, A., Ciampichetti, A., Benamati, G. (2003) Hydrogen permeability and embrittlement in Eurofer 97 martensitic steel . ENEA Report SM-A-R-001.

5.

Causey, R.A., Wampler, W.R. (1995) The use of silicon carbide as a tritium permeation barrier. J. Nuc. Mat. 220-222 ,

823-826.

6.

Causey, R.A., Karnesky, R.A., San Marchi, C. (2009) Tritium barriers and tritium diffusion in fusion reactors . http://arc.nucapt.northwestern.edu/refbase/files/Causey-2009_10704.pdf

There is a considerable degree of uncertainty in the physical properties, particularly for the solubility of T. That is why sensitivity study is needed.

Tritium transport, 3/6

The electrical conductivity of FCI may have a strong effect on the T transport via changes in the velocity, especially in the 2-mm gap

Side-wall jets in the bulk

Hartmann-wall gap flows

=100 S/m, Ha =15,900

Side-wall gap flow s

Tritium transport, 4/6

T concentration (10 -6 kg/m 3 ) for cases with low (0.001 mol/m 3 /Pa 0.5

) and high (0.05 mol/m 3 /Pa 0.5

) solubility of T in PbLi

X=0.5 m

Low solubility

X=0.5 m

High solubility

X=1.5 m X=1.5 m

Tritium transport, 5/6

Fluxes of tritium through the steel. S= 0.001 mol/m 3 /Pa 0.5

, units are 10 -9 kg/m 2 /s

More T permeation occurs from the

Hartmann gap, where velocity is low

Total tritium loss in the front duct

# D S σ T leak

10 -9 m 2 s -1 %

8

9

10

5

6

7

3

4

1

2

2.54

2.54

2.54

2.54

2.54

2.54

1

2.54

7

2.54

mol m -3 Pa -

1/2

Ω -1 m -1

0.01

0.01

0.01

0.0005

0.001

0.005

0.05

0.1

0.01

0.01

5

50

500

5

5

5

5

5

5

5

1.99

1.65

0.60

0.35

0.36

0.06

1.30

1.40

1.35

2.08

Total T leakage < 2%

Tritium transport, 6/6

• Due to very low diffusion coefficient of T in SiC, FCI can be considered as a T permeation barrier

• All tritium generated in the bulk flow remains there.

Tritium permeation occurs mostly from the gaps, especially from the Hartmann gap, where velocity is very low

• Electrical conductivity of the FCI has indirect effect on T transport via changes in the velocity profile: higher

smaller leakage

• Total T leakage into He can be estimated as 2% of all tritium generated in the blanket (not taking into account pressure equalization openings and 3D flow effects)

• More accurate databases for physical properties are needed

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