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MATGEN IV.2 February 2- 8, 2009 Stockholm – Kiruna, Sweden. Corrosion of steels in liquid metals. Concetta Fazio Program Nuclear Safety Research. Outline. Motivation The role of Nuclear Energy in an Energy Mix The Fast Reactor System and its fuel cycle - PowerPoint PPT Presentation
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1 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 20071 | C. Fazio | MATGEN IV.2 | February 2009
KIT - Die Kooperation von
Forschungszentrum Karlsruhe GmbH
und Universität Karlsruhe (TH)
Corrosion of steels in liquid metals
Concetta FazioProgram Nuclear Safety Research
MATGEN IV.2February 2- 8, 2009Stockholm – Kiruna, Sweden
2 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 20072 | C. Fazio | MATGEN IV.2 | February 2009
KIT - Die Kooperation von
Forschungszentrum Karlsruhe GmbH
und Universität Karlsruhe (TH)
Outline• Motivation
– The role of Nuclear Energy in an Energy Mix– The Fast Reactor System and its fuel cycle– Transmutation objectives and Scenarios
• Fast Reactor Systems and the role of liquid metals as coolant– Examples
• Loop type Na cooled FR• Pool Type Pb cooled FR• ADS
• Corrosion of steels in liquid metals– What is corrosion?– Parameters affecting corrosion– Corrosion mechanisms in HLM and Na– Experimental evaluation of corrosion mechanisms and rate– Models– Practical applications
• Summary and Perspectives
3 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 20073 | C. Fazio | MATGEN IV.2 | February 2009
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The role of Nuclear Energy in an Energy Mix
0
5
10
15
20
25
30
1990 2000 2010 2020 2030 2040 2050
Wo
rld
Pri
ma
ry E
ne
rgy
So
urc
es
(Gto
e)
6
6,5
7
7,5
8
8,5
9
Wor
ld P
opul
atio
n (B
illio
ns)
Other Renewable
Biomass
Nuclear
Gas
Oil
Coal
Population
Source IEA : Energy to 2050 -Scenarios for a Sustainable Future
4 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 20074 | C. Fazio | MATGEN IV.2 | February 2009
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- Economic Competitiveness- Safety and Reliability- Environment Protection - Proliferation Resistance
Fast Breeder Reactor
MOX+MA Fuel
Geological Disposal
Low Decontaminated Fuel
Reprocessing
Fuel Fabrication
U/Pu/MA Mixed Product
Fission Product
Spent Fuel
Global Concept of Future FBR CycleGlobal Concept of Future FBR Cycle
Objectives of future implementation of FR in a power park (starting from ~ 2040)
5 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 20075 | C. Fazio | MATGEN IV.2 | February 2009
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Optimal resources utilisation ….
G. Koch, Radiochimica Acta 37 (1984) 205
6 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 20076 | C. Fazio | MATGEN IV.2 | February 2009
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Transmutation Objectives and Scenarios
• Generic objectives of P/T strategies: – reduce the burden on a geological storage in terms of waste mass
minimization, reduction of the heat load and of the source of potential radiotoxicity.
Radiotoxicity of 1 ton Spent FuelSeparation of Pu and MA
1E+02
1E+03
1E+04
1E+05
1E+06
1E+07
1E+08
1E+09
1E+01 1E+02 1E+03 1E+04 1E+05 1E+06 1E+07
Time after Discharge [years]
Ra
dio
tox
icit
y [
Sv
/ t
HM
]
without
99,9%Pu
99,9%Pu,MA
Nat-U
7 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 20077 | C. Fazio | MATGEN IV.2 | February 2009
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Transmutation Objectives and Scenarios
• More specific objectives can be defined according to the specific policy adopted towards nuclear energy and according to specific strategies of reactor development.
• Three categories of specific objectives:– Waste minimization and sustainable development of nuclear energy
and increased proliferation resistance of the fuel cycle. A transition from a LWR fleet to a FR fleet is foreseen.
– Reduction of MA inventory and use of Pu as a resource in LWRs, in the hypothesis of a delayed deployment of fast reactors. Use of dedicated burners (ADS or FR)
– Reduction of TRU inventory as unloaded from LWRs: Management of spent fuel inventories, as a legacy of previous operation of nuclear power plants in ADS.
It is a generally agreed conclusion that fast neutron spectrum systems are more appropriate for transmutation of TRU
8 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 20078 | C. Fazio | MATGEN IV.2 | February 2009
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Transmutation Objectives and Scenarios
DEDICATED FUEL REPROCESSINGAqueous (A) vsPyro (P)
REACTOR TYPE
High CR CRITICAL FR
ADS
RECYCLE MODE
Homogeneous
FUEL (target)MOX
3-5 % b)
REPROCESSING (MA recovery)
Full TRU
Cm Separa-
tion
Umatrix
Inert matrix
MA content ~ 50 % c)
MA/Puseparation
A A or P
?
?
?
CONVERSION RATIO (CR)
High CR Low (or zero) CR
Heterogeneous
Umatrix
Inert matrix
MA/PuSepara
-tion
10-20 % a)
Cm/Am/Puseparation
A or P
?
?
Low CR CRITICAL FR
HomogeneousHomogeneous
Umatrix
Sustainable nuclear energy development
Double strata and TRU legacy inventory reduction
?
?
a) MA/(MA+Matrix) b) MA/(U+TRU) c) MA/TRU
9 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 20079 | C. Fazio | MATGEN IV.2 | February 2009
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Among the 6 preferred Gen IV systems, 3 are FRs
Very High Temperature Reactor
Sodium Fast reactor
Supercritical Water Reactor Molten Salt Reactor
Lead Fast ReactorGas Fast Reactor
10 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200710 | C. Fazio | MATGEN IV.2 | February 2009
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Examples - Loop type Na cooled FR: JSFR
Ref. SMINS, 2007
11 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200711 | C. Fazio | MATGEN IV.2 | February 2009
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Loop type Na cooled FR: JSFR
Operational conditions
K. Mukai, Int. Seminar on coolants and Innovative Reactor Technologies, CEA Cadarache Nov. 2006
Parameters to be considered for material assessment
12 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200712 | C. Fazio | MATGEN IV.2 | February 2009
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Examples - Pool type Pb cooled FR: ELSY
L. Cinotti, Int. Seminar on coolants and Innovative Reactor Technologies, CEA Cadarache Nov. 2006
PumpImpellerAlternative materials for pump impeller under investigationMaxthal, SiSiC, Noriloy
HX - T91 or AISi 316L
Vessel – AISI 316LCladding – T91
13 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200713 | C. Fazio | MATGEN IV.2 | February 2009
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Pool type Pb cooled FR: ELSY
L. Cinotti, Int. Seminar on coolants and Innovative Reactor Technologies, CEA Cadarache Nov. 2006
Operational conditions
Parameters to be considered for material assessment
14 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200714 | C. Fazio | MATGEN IV.2 | February 2009
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ADS
EFIT XT-ADS
15 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200715 | C. Fazio | MATGEN IV.2 | February 2009
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ADS: Operational conditions
XT-ADS (LBE) EFIT (Pb)
Core components: mechanical stresses: e.g. Hoop stress on cladding
T 300 – 500 °C 400 – 530 °C
dpa Up to 160 Up to 100
flow ~ 2m/s ~ 2m/s
Reactor Vessel T 300 – 400 °C 400 – 430 °C
dpa < 0.02 < 0.003
flow ~ 1 m/s ~ 0.1 m/s
stress 50-150 MPa 80-150 MPa
Heat exchanger T 300 – 400 °C 400 – 480 °C
dpa < 0.02 < 0.03
flow ~ 1 m/s ~ 1 m/s
stress ~100 MPa 125-190 MPa
Spallation target T 240 - 340 °C 400 – 480 °C
dpa/yr Up to 40 Up to 30
flow ~ 3 m/s ~ 1.5 m/s
stress ~100 MPa + 40 fatigue cycles/yr n.a.
EFIT Pump: T= 480 °C; dpa < 0.03; flow = 10 m/s (on impeller)
16 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200716 | C. Fazio | MATGEN IV.2 | February 2009
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Liquid Metals
Fast reactors have:- Hard neutron spectrum (i.e. limited neutron thermalisation and
as small neutron capture as possible)- High power density: need for effective coolant with high
thermal exchange capability.
Therefore: liquid metals as coolant. Historically Na and, at a lesser extent, Heavy Liquid Metals (HLM) have been the preferred choices.
17 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200717 | C. Fazio | MATGEN IV.2 | February 2009
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Liquid Metals Properties
Property Unit Na Pb LBE
Atomic Number - 11 82 -
Atomic Mass amu 23 207 -
Melting Temperature °C 98 327 125
Boiling Temperature °C 883 1745 1670
Density at 450°C kg/m3 845 10520 10150
Thermal Conductivity at 450 °C
W/mK 69 17 14
Chemical reactivity - High Moderate as dust Moderate as dust
Toxicity - High High High
18 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200718 | C. Fazio | MATGEN IV.2 | February 2009
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Corrosion of steels in liquid metals
What is Corrosion?Why it is important to study it?
19 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200719 | C. Fazio | MATGEN IV.2 | February 2009
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„The word corrosion denotes the destruction of metal by chemical or electrochemical action; a familiar example is the rusting of iron” U. R. Evans
Pitting Corrosion: Corrosion Pits are the primary source of leaks in water handling systems
Liquid metal corrosionLecor impeller (presented at the ELSY Meeting by ENEA)
Active Corrosion on Carbon Steel Manhole
20 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200720 | C. Fazio | MATGEN IV.2 | February 2009
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Why it is important to study it
- Ensure Integrity of structures- Avoid Plugging of systems with corrosion products - Ensure thermal conductivity of fuel cladding and functional
components
An example for HLM cooled FR:• Stringent safety requirement on the integrity of the cladding
material has been put for design basis operating conditions and design extension conditions.
• For the chosen temperature regime, the selected cladding material should withstand the combined effect of neutron irradiation, corrosion and mechanical stresses in order to comply with the safety requirements.
21 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200721 | C. Fazio | MATGEN IV.2 | February 2009
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Factors affecting liquid metal corrosion
Temperature Temperature gradient (mass transfer) Cyclic temperature fluctuations Surface area to volume ratio Chemical purity of the liquid metal (wetting) Flow velocity (Reynolds number) Surface conditioning (surface films) Number of materials in contact with the same liquid metal
(dissimilar mass transfer) Condition of the container material (carbides or nitrides at the
grain boundary)
22 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200722 | C. Fazio | MATGEN IV.2 | February 2009
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Liquid metal corrosion mechanism
Alloying between liquid and solid metals: for this type of mechanism there must be some solubility of the liquid metal in the solid metal. In some cases the liquid metal dissolves considerably in the solid metal with the formation of an intermetallic compound (e.g. V in Pb at 1000°C).
Scheme of the simple dissolution mechanism
Simple solution attack: Removal of the metal from the surface to saturate the liquid metal.
Concentration gradient mass transfer dissimilar metals, e.g: Mo samples tested in Na contained in a Ni crucible at 1000°C: Ni had transferred through the Na and deposited on the Mo surface to produce Ni-Mo compounds
23 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200723 | C. Fazio | MATGEN IV.2 | February 2009
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Liquid metal corrosion mechanism
Temperature gradient mass transfer: the most damaging type of liquid metal corrosion is temperature gradient mass transfer. The driving force for temperature gradient mass transfer is the difference in solubility of the dissolved metal at the temperature extremes of the heat transfer system. By knowing the solubility limit of the solid in the liquid metal the driving force of these phenomena can be determined
1. Solution2. Diffusion3. Transport of dissolved metal
4. Nucleation5. Transport of crystallites6. Crystal growth and sintering (plug formation)
Pulg in an Inconel-Pb loop
24 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200724 | C. Fazio | MATGEN IV.2 | February 2009
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Part 2: Factors affecting liquid metal corrosion
Temperature Temperature gradient (mass transfer) Cyclic temperature fluctuations Surface area to volume ratio Chemical purity of the liquid metal (wetting) Flow velocity (Reynolds number) Surface conditioning (surface films) Number of materials in contact with the same liquid metal
(dissimilar mass transfer) Condition of the container material (carbides or nitrides at the
grain boundary)
25 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200725 | C. Fazio | MATGEN IV.2 | February 2009
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Liquid metal quality: Sources and type of impurities
• At installation start up and in normal operating conditions
– From Cover gas and adsorbed gases on structures (O2, H2O)
– From neutron reaction and from spallation (e.g. Po, Hg, other activation products)
– Corrosion products from structural material (e.g. Fe, Cr, Ni, etc.)– Intrinsic impurities (Ag, Cu, Sn, etc.)
• Off normal conditions– From Fuel cladding failure (Pu, U, MA, etc.)
– Air entrance (N2, O2, H2O, ..)
– Steam entrance (H2O)
26 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200726 | C. Fazio | MATGEN IV.2 | February 2009
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HLM quality control: the case of Oxygen
Above solubility limit lead and bismuth oxide formation
Solubility of Oxygen in LBE
Solubility of Oxygen in Pb
Oxides floating on the liquid metal
27 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200727 | C. Fazio | MATGEN IV.2 | February 2009
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Na quality control: the case of Oxygen
10
100
1000
10000
250 300 350 400 450 500 550 600 650
Temperature, °C
So
lub
ilit
y, p
pm
28 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200728 | C. Fazio | MATGEN IV.2 | February 2009
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Solubility of metallic elements
1,0E-05
1,0E-04
1,0E-03
1,0E-02
1,0E-01
1,0E+00
1,0E+01
1,0E+02
1,0E+03
1,0E+04
1,0E+05
1,1 1,2 1,3 1,4 1,5 1,6 1,7 1,8
Temperature 1000/T [K]
So
lub
ility
[w
pp
m]
Ni(Pb)
Ni (Pb-Bi)
Cr (Pb)
Cr (Pb-Bi)
Fe(Pb)
Fe(Pb-Bi)
In Na
In HLM
29 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200729 | C. Fazio | MATGEN IV.2 | February 2009
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From liquid metal quality to corrosion
Liquid metal corrosion depends from the solubility of the solid metal in the liquid metal and its solution rate.• Solution rate and extent of solubility are affected by
– formation of surface intermetallic compounds (among the liquid and the solid)
– oxide or nitride films formation (due to the presence of oxygen / nitrogen in the liquid metal)
– Other impurities present in the liquid metal can increase the solution rate
– Temperature gradients and multimetallic systems
30 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200730 | C. Fazio | MATGEN IV.2 | February 2009
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Results from screening experiments: HLM
10000 h
20 m
PbBi
ferriteferritelayerlayer
20 m
PbBi
Case 1) oxygen content in LBE < 10-9 wt.% T=400 °C
Dissolution of solid metal in the liquid metal
Uniform dissolutionTransgranular and intergranular
Leaching of Ni and ferritisation
AISI 316L
T91
Case 2) [O2]LBE > 10-8 wt.% and < 400 °C < T < 550 °C
(PbO)GΔ O2
Impurities in LBE forming simple or complex substances on the
metal surface
Under controlled O2 content
and T: the oxide can be considered as a corrosion protection layer
AISI 316L
2)
1)
Corrosion mechanism in HLM depends from:Temperature – oxygen content in the liquid metal – composition of steel
31 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200731 | C. Fazio | MATGEN IV.2 | February 2009
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Results from experiments: Na
Low Oxygen High Oxygen
Similar mechanism is observed with Cr (Na-Cr-O are more stable than Na-Fe-O)
Formation of ternary oxides increased corrosion rate
In austenitic steels ferritisation can be observed (Ni solubility highest)
32 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200732 | C. Fazio | MATGEN IV.2 | February 2009
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Experimental Programs to address Corrosion mechanism and rate
33 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200733 | C. Fazio | MATGEN IV.2 | February 2009
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Choice and characterisation of reference structural materials: the case of HLM systems• Materials selected
– Ferritic Martensitic steel T91 for the highly loaded parts (e.g. cladding, spallation target)
– Austentic steel AISI 316L for e.g. Vessel
– Fe, Al based corrosion protection barrier
Element Cr Mo Nb N C V
wt. % 8-9,5 0.85-1.05 0.06-0.1 0.03-0.07 0.08-0.12 0.18-0.25
Element Mn P Si Ni Al S
wt. % 0.30-0.60
<0.02 0.2-0.5 <0.4 <0.04 <0.01
T91
Element Cr Mo Nb N C V
wt. % 16-18 2-3 - 0.1 0.03 -
Element Mn P Si Ni Al S
wt. % 2 0.045 0.75 10-14 - 0.03
AISI 316L
34 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200734 | C. Fazio | MATGEN IV.2 | February 2009
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Materials qualification program for HLM systems
0
1
2
3
4
5
450 500 550 600
Temperature [°C]
HLM
flow
[m/s
]
FZK
CEA
NRI
ENEA
CIEMAT FZK/IPPE
100
200
300
400
500
600
0 20 40 60 80 100
BR2/SHFR/SBOR60/S
BR2/DHFR/DPX/D
Irra
dia
tion
Te
mpe
ratu
re (
°C)
Dose (dpa)
Temperature and Dose of Irradiation Experiments
PHENIX
BOR60
BR2
HFR
HFR
BR2
BR2
HFR
SPIRE (red symbols) DEMETRA (green)
Conditions foreseen for ADS Components
Target window
Clad tubesTarget structuresSINQ
SINQ
+ He
(LBE)
(LBE)
Irradiation studiesCorrosion studies
Corrosion / n-irradiation combined effect
35 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200735 | C. Fazio | MATGEN IV.2 | February 2009
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Corrosion studies in HLM
Dissolution (uniform or transgranular) of the steel elements in the liquid metal
Oxidation of the steel surface. The oxide layer can act as a protection barrier against a direct corrosive attack of the liquid metal
HLM oxides precipitates causing hydraulics problems (e.g. plugging)
Ellingham Diagram
For the operating condition of XT-ADS (300 – 400°C) and EFIT (480 – 530 °C) respectively an appropriate oxygen potential can be selected to avoid HLM oxides formation and to promote oxidation of the steel surface.
These are thermo-chemical statements, which enables to identify the corrosion mechanism. However, no information are available on the corrosion rate and the hydraulics effect.
36 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200736 | C. Fazio | MATGEN IV.2 | February 2009
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Corrosion studies: experimental results
Loop Experimental conditions 2.000 h Oxide scale/LM attack
Up to 10.000 h Oxide scale/LM attack
T91 316 T91 316
CORRIDA (FZK)LBE
550°C; 10-6 wt.-%O flow= 2 m/s
Oxide: 20-25 m Oxide : few Oxide: 45 m(data dispersion)
LM attack up to 350 m
CU2 (IPPE/FZK) LBE 550°C; 10-6 wt.-%O flow= 1.3 m/s
Oxide: 39 m _____ 6600 hOxide: 36-45 m (data dispersion)
_____
CHEOPE III (ENEA) Pb
500°C; 10-6wt%; flow = 1 m/s
20 m (non homog.)
Oxide: few 5000/10000 hOxide: 25 m / scale spall off
5000/10000 hOxide: thin/thin and compact
LINCE (CIEMAT) LBE 450 °C; 10-8 wt.-%O (probl. on sensor)
1700 h T91: 4 m (non homog. oxide)
Unaffected Corrosion attack up to 350 m
Corrosion attack up to 200 m
LECOR (ENEA) LBE 450°C;10-10-10-8 wt%
LM attack less evident LM attack
_____ _____
37 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200737 | C. Fazio | MATGEN IV.2 | February 2009
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Corrosion studies: experimental results
CORRIDA FZKOxide: 25 m
550°C; 10-6 wt.-%O flow= 2 m/sNo magnetite detected (higher velocity)
550°C , 10-6 wt.-%O flow= 1.3 m/sOxide thickness: spinel+ internal oxidation = 22 µm Magnetite thickness: 17 µm
CU2 IPPE/FZKOxide: 39 m
Results after 2000h in LBE at 550°C and Pb at 500°C performed with a controlled oxygen potential
500°C , ~10-6 wt.-%O flow ~ 1 m/s1. Lower temperature2. Different oxygen potential3. “low” flow velocity
CHEOPE /ENEAOxide: ~ 20 m
1. Oxide scale is formed by three layers: outer magnetite – intermediate Fe, Cr spinel oxide – inner oxygen diffusion zone
2. However, oxide scale tested in Corrida do not has the outer magnetite layer: Hydraulics effect (see next slide)?
3. After 2000h oxidation rate in Pb at 500°C is lower with respect to LBE at 550°C: temperature effect
38 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200738 | C. Fazio | MATGEN IV.2 | February 2009
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Corrosion studies: experimental results
100mm 50mm 100mm 50mm 50mm 100mm
V=1 м/s V=2 м/s V=3 м/s
АА
Confirmation of hydraulics effects on the oxide scale formation: Experiment performed with different flow velocities
550 °C, 2000 h, ~10-6 wt.% O
At 1m/s outer magnetite scale, at 1,75 m/s small rests are visible, at 3m/s magnetite scale entirely eroded.
FZK-IHM/IPPE collaboration
Fe3O4
V = 1 m/s V = 1,75 m/s V = 3,0 m/s
(Fe, Cr)3O4
Internal oxidation
Fe3O4
(Fe, Cr)3O4
Internal oxidation Internal oxidation
(Fe, Cr)3O4
39 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200739 | C. Fazio | MATGEN IV.2 | February 2009
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Corrosion studies experimental results
10-6 wt.-%O flow= 1 m/s t=2000h 550°C
Pressurised tube in HLM
40 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200740 | C. Fazio | MATGEN IV.2 | February 2009
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Example of application of corrosion results to Design
(D. Struwe, W. Pfrang, IRS/FZK)
Oxide layer thickness should be limited to less than 20-30 m in order to keep margin on the maximum allowable temperature for the T91 steel.
Control of oxidation process in a reactor system might not be applicable
GESA surface alloyed steel can be seen as a solution
Axial profiles of clad inner temperature modified calculation with different additional oxide layers
41 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200741 | C. Fazio | MATGEN IV.2 | February 2009
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Corrosion studies: Fe, Al corrosion protection barrier
600°C
Up to 600°C and 10000 h no corrosion attack and no visible oxidation.
Thin alumina scales protect the surface alloyed steel.
1. LPPS of Fe, Al
FeC
rAlY
coat
ing
FeC
rAlY
coat
ing
FeC
rAlY
coat
ing
FeC
rAlY
coat
ing
2. GESA treatment on the LPPS coating
1. Enhance metallic bonding with substrate
2. Smoother surface3. Reduced Al content
500°C550 °C
3. GESA treated samples tested for 10000 h in flowing LBE at three different temperatures, flow rate 1 m/s and oxygen ptential equivalent to 10-6 wt%
42 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200742 | C. Fazio | MATGEN IV.2 | February 2009
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Corrosion studies: Fe, Al corrosion protection barrier
100mm 50mm 100mm 50mm 50mm 100mm
V=1 м/s V=2 м/s V=3 м/s
АА
Confirmation of hydraulics effects on the Fe, Al GESA treated samples: Experiment performed with different flow velocities
550 °C, 2000 h, ~10-6 wt.% O
Samples with proper LPPS coating and proper GESA treatment: no flow velocity effect on surface appearance, no dissolution attack, no severe oxidation, no erosion.
FZK-IHM/IPPE collaboration
V = 1 m/s V = 1,75 m/s V = 3,0 m/s
43 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200743 | C. Fazio | MATGEN IV.2 | February 2009
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• Oxygen activity: oxidation/dissolution• Time, Temperature• Flow rate: high flow rate erosion of Fe3O4 • Steel composition: high Cr content increased oxidation resistance. • Stresses: hoop stress enhances Fe diffusion
Parameters affecting corrosion of steels and modelling
Effect of temperature, oxygen content and steel composition Effect of flow velocity
44 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200744 | C. Fazio | MATGEN IV.2 | February 2009
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Corrosion modelling: Example Na – steel system
Oxygen content in Na and flow velocity have been identified as the two main variables affecting the corrosion rate. The corrosion mechanism is the dissolution. From experimental results two semi-empirical equations have been determined:
For v ≤ 4m/s - the corrosion rate depends from the velocity
For v ≥ 4m/s – the corrosion rate depends only from the oxygen concentration
45 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200745 | C. Fazio | MATGEN IV.2 | February 2009
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• Structural material corrosion in a closed an-isothermal system as a nuclear reactor, 2 kinds of model are needed:– Mechanistic model: give the structural material life time hox(t) or kp,
hdiss(t), jox, jdiss, using the physical-chemical data characteristic of the mechanism (Dox, DLM, S…)
– Mass transfer model: give the system life time Vcorr/prec(x) (prediction of plugging in the loop), using the output of the mechanistic model (kp, kpr, jox, jdiss…)
• Data needed:– Mechanistic model is based on numerous specific experiments which can
be partly performed in static conditions– Mass transfer model is based on long term experiments in LM closed
loop– To develop these models, need of physical-chemical data as: Dox, DLM,
SLM, kpr, kdiss which are very difficult to obtain and important lack of data to supply the corrosion model
jox oxygen flux in steel; Jdiss Fe flux in steel, hox oxide thickness, hdiss dissolution thickness, D diffusion coefficient, S solubility limit, kox oxidation constant kpr precipitation rate
Corrosion modelling: Example Steel-HLM
46 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200746 | C. Fazio | MATGEN IV.2 | February 2009
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Corrosion modelling
• Example: Pb-Bi eutectic – steel system
47 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200747 | C. Fazio | MATGEN IV.2 | February 2009
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Perspectives
•Advantages of F/M steels with respect to austenitic steel:
• Better thermal properties: 1. higher thermal conductivity 2. lower thermal expansion
(can have impact on the dimensioning, see e.g. Japanese Sodium Fast Reactor, JSFR)
• Lower Swelling
•However, experience on austenitic steels for the nuclear use is available
7
9
11
13
15
17
19
50 100 150 200 250 300 350 400
Temperature, °C
Me
an
Th
erm
al
Ex
pa
ns
ion
, 1
0-6
/K
AISI316L
T91
5
10
15
20
25
30
0 100 200 300 400 500 600
Temperature, °C
Th
erm
al
Co
nd
uc
tiv
ity
(l )
, W
/mK
AISI 316L
T91
Data AISI316L from AAA handbook; Data T91 from RCC-MR
48 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200748 | C. Fazio | MATGEN IV.2 | February 2009
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Perspectives• Advantages of ODS alloys, with respect to F/M steels
• 9% Cr ODS RAFM steel has been developed for future fusion reactors and has shown very promising mechanical properties at high temperature
R. Lindau et al., FZK
…..but what about corrosion resistance of ODS steels?
49 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200749 | C. Fazio | MATGEN IV.2 | February 2009
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Summary
• For the development of nuclear energy, FRs provide solution to the key issues of sustainability and waste minimisation;
• Among the preferred systems of Gen IV three types of FRs and two among them are liquid metal cooled;
• In this respect corrosion issues have to be considered due to safety requirements;
• The corrosion control in HLM is more challenging when compared to Na;
• Current programs allow to consolidate and extend corrosion understanding and modelling;
• In future, new type of steels (e.g. ODS) can provide improved performances. These materials need to be characterised also for their corrosion resistance
50 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200750 | C. Fazio | MATGEN IV.2 | February 2009
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Selected ReferencesNa• H.U. Borgstedt, C.K. Mathews, Applied Chemistry of Alkali Metals, Plenum, New York, 1987.• K. Fink, L. Leibowitz, “Thermodynamic and Transport Properties of Sodium Liquid and
Vapor” ANL/RE-95-2, January 1995 (www.insc.anl.gov)• M. Konomura, M. Ichimiya „Design challenges for sodium cooled fast reactors“ J. Nucl. Mat.
371 (2007) 250–269HLM• “Handbook on Lead-bismuth Eutectic Alloy and Lead Properties, Materials Compatibility,
Thermal-hydraulics and Technologies” issued by the OECD-NEA and available at the following link: http://www.nea.fr/html/science/reports/2007/nea6195-handbook.html
• Nuclear Technology September 2004 – Vol. 147, No3• Several Issues of J. Nucl. Mater (Vol. 296 (2001); Vol. 301 (2002);Vol. 318 (2003); Vol. 335
(2004), etc.)Comparative assessment HLM - Na• „Comparative assessment of thermo-physical and thermohydraulic characteristics of Pb,
LBE and Na coolants for fast reactors“, IAEA TECDOC – 1289, June 2002F/M Steels• High-Chromium Ferritic and Martensitic Steels for Nuclear applications, Ronald L. Klueh and
Donald R. Harries, ASTM, MONO3
51 | Vorname Nachname | Mid-term Review NUKLEAR | February 5-6, 200751 | C. Fazio | MATGEN IV.2 | February 2009
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Thank you for your attention