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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
Comments on Corrosion R&D Needs for DCLL
B.A. Pint and P.F. Tortorelli
Presented by S.J. Zinkle
Oak Ridge National Laboratory
US ITER-TBM Meeting
Idaho Falls, ID
August 10-12, 2005
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
Compatibility in the DCLL system will likely involve multiple materials
• In-vessel TBM – ferritic/martensitic steel, SiC FCI
• External piping– Ni-base superalloy?
• Tritium processing– Refractory alloy??, tritium permeation barrier materials??
• Heat exchanger– Material options??
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
Liquid Metal Compatibility is Controlled by several mechanisms
• Dissolution– Numerous phenomena can affect mass transfer across metal-liquid interface,
J=k (C0-C)
• Laminar vs. turbulent flow (including magnetic field effects)
• Solubility temperature dependence
• Impurity and interstitial transfer– Very important for refractory metals (and BCC metals in general)
• Alloying between the liquid metal and solid– Typically eliminated early on in selection process (showstopper)
• Compound reduction– Often most relevant for ceramics (e.g., SiC insert)
• The last three mechanisms can be roughly evaluated using low-cost capsule experiments; the 1st mechanism requires flowing loop tests
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
There are two major contributors to dissolution mass transfer
• Static isothermal mechanisms – Capsule tests can provide initial data on solubilities (infinite
dilution steady-state approximation)
• Flowing, nonisothermal mechanisms– Rate-controlling steps include surface reaction, liquid-phase
diffusion through boundary layer, and solid state diffusion
J=k (C0-C)
Mass Change
x
T
max
T
min
0
A
s
A
p
A
p
balance points
(+)
(-)
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
Eventually, Compatibility Issues Need To be Examined Under Dynamic, T Conditions
Ji = k(Csol,i – Ci)
Constant driving force for dissolution
Positive results from isothermal capsule experiments may not be reproduced under these conditions
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
Current knowledge of candidate materials for DCLL system is largely limited to static capsule tests
• Substantial experimental database on ferritic steel compatibility with flowing Pb-Li– Comprehensive analysis of existing data is needed
• Database for other materials generally does not include information for nonisothermal flowing systems and effects of magnetic fields
• Very little is known about potential stress corrosion cracking mechanisms
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
Concluding remarks
• Need to establish reference design (materials, operating conditions) asap
• Near-term compatibility R&D activities would focus on analysis of existing compatibility for ferritic/martensitic steel with flowing Pb-Li– Also continue limited number of static capsule tests on candidate
piping materials (possibility to avoid coatings or ceramic inserts)
• Medium-term activities would be centered on flowing loop experiments– Thermal convection loop– Other loops?
• Scoping experiments on stress-corrosion cracking should also be initiated in the near- to medium-term
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
Chemical Analyses of the Pb-Li Revealed Little Reaction With SiC after 1000h
Li(at.%)
Si(ppma)
C(ppma)
O (ppma)N
(ppma)
Start n.d. <40 <170 1270 <40
800˚C
1000h17.5% <30 1850 4090 100
1100°C
1000h16.3% <30 1160 3550 90
1100˚C
2000h16.0% 185 1025 7890 200
No significant mass gains after any capsule test Si detected after 2,000h at 1100°C, still less than Kleykamp PbLi not analyzed yet for 5,000h 800°C or 1,000h 1200°C
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
Specialized Capsule Experiments Have Been Used For SiC Exposures In Pb-17Li
800 and 1000˚C, 1000 h
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
Negligible Change In Specimen Mass Before Or After Cleaning Was Observed
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
Corrosion-Resistant Metallic Coatings for Pb-17Li
• At highest temperatures at and near first wall, SiC flow channel inserts can provide protection
• Ducting behind this more likely to be made of conventional steels
• Pb-17Li is quite corrosive toward certain ferrous and Ni-based alloys at temperatures above 450°C
• One possible solution to ducting protection is corrosion-resistant aluminized coatings on strong conventional alloys: aluminide surface layers should be stable in Pb-17Li (Hubberstey et al., Glasbrenner et al.)
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
Al-Containing (Al2O3-forming) Alloys Showed Significantly Reduced Mass Losses In Pb-17Li
Specimen CapsuleMass Change
(mg/cm2)
316 SS 316 SS -0.7
316 SS Fe -5.7
316 SS Mo -3.8
ODS FeCrAl Mo -0.2
Fe-28Al-2Cr+Zr Mo -0.2
Ni-42.5Al Mo -0.1
Capsule test: 1000 h, 700˚C, Pb-17Li
0.25 m
*no preoxidation of specimens
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
316 SS Results Can Be Understood Based On Fundamental Dissolution Driving Force
• Dissolution continues until saturation is reached
• For specimens of 316 SS, saturation is reached sooner in a 316 SS capsule because both are contributing solute (mainly Ni)
• Fe or Mo capsules are relatively inert
Ji = k(Csol,i – Ci)
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
Surface Morphology Of Exposed Stainless SteelWas Consistent With Dissolution
1 m
316SS in Mo Capsule, 1000 h, 700˚C, Pb-17Li
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
Examination Of Cross Sections ConfirmedSome Dissolution Had Occurred in Stainless Steel
10 m
2 m
1000 h, 700˚C, Pb-17Li
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
Nickel Depletion Was Observed in Stainless SteelC
ou
nts
Energy, ev
Ni
Co
un
ts
Energy, ev
10 m
1000 h, 700˚C, Pb-17Li
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
Aluminide-Formers Showed Little Mass Loss And Tended To From Stable, Protective Al-Rich Layers
2 m
1000 h, 700˚C, Pb-17Li
ODS-FeCrAlin Mo Capsule
Ni-42.5Alin Mo Capsule
2 m
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
Fe
Energy, ev
Qualitative Analysis Indicated These Surface Layer Were Rich in Al and O (Likely Al2O3)
Al
OCo
un
ts
Energy, ev
1000 h, 700˚C, Pb-17LiODS-FeCrAl in Mo Capsule
Surface Layer
Subsurface Alloy
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OAK RIDGE NATIONAL LABORATORYU. S. DEPARTMENT OF ENERGY
Example Cycle Efficiency as a Function of Interface FS/Pb-17Li Temperature
0.36
0.37
0.38
0.39
0.4
0.41
0.42
0.43
0.44
0.45
475 490 510 530 550
Max. Interface FS/LiPb Temperature, o
C
Cycle Efficiency
For a fixed maximum neutron wall loading ~4.7 MW/m2,
-the max. η~38.8%, Tmax,FS<<550oC for an interface FS/LiPb temperature of 475 oC;
-the max. η~41.5%, Tmax,FS<<563oC for an interface FS/LiPb temperature of 510 oC.
TLiPb,out=700oC;Tmax,FW=800 oC
Tave,FW=700 oC; Ppump/Pthermal << 0.05