Effects of High Dose Neutron Irradiation on Reduced-activation
Ferritic/Martensitic Steels
T. Hirose
1, Y. Katoh
2, H. Tanigawa
1, K.G. Field
2, H. Sakasegawa
1, B.K. Kim
2, M. Ando
1, D.T. Hoelzer
2, L. Tan
2, L.L. Snead
2, R.E. Stoller
21
Japan Atomic Energy Agency
2
Oak Ridge National Laboratory
This work is part of the U.S. DOE – JAEA collaboration on Fusion Materials.
Research sponsored by the Office of Fusion Energy Sciences, U.S. Department of Energy, and Japan Atomic Energy Agency under contracts DE-AC05-00OR22725 and
NFE-10-02779, respectively, with UT-Battelle, LLC. 1
OUTLINE
1. Background
– Reduced activation ferritic/martenitic steel (RAFM), F82H – Irradiation testing for F82H
2. Experimental
– JAEA-DOE collaborative research
– Non-instrumental capsules, JP-28 & JP-29 – Post-irradiation tensile tests
3. Results
4. Discussion
5. Summary
Reduced-Activation Ferritic/Martensitic (RAFM) Steel
Fe - 8
∼9Cr - 1 ∼ 2W - V,Ta (F82H, JLF-1, EUROFER, CLAM, ARAA etc.)
Fully tempered martensitic steel, based on Mod9Cr (Gr.91: Fe 9Cr-1Mo V, Nb).
Good swelling resistance was demonstrated as the candidate material for FBR fuel cladding material.
Mo replaced with W, Nb replaced with Ta to reduce activation.
8 to 9 Cr was selected due to its minimum ductile-brittle transition temperature (DBTT) shift after irradiation.
Compared to the other candidate fusion blanket structural material, RAFM has sound technological background on its reproducibility and weldability.
A. Kohyama, J. Nucl. Mater. 233-237 (1996) 138
Swelling resistance Reduced activation Post-irradiation DBTT shift
obtained by Charpy impact test
Irradiation tests for F82H
• Post irradiation tensile tests on F82H have been conducted over 20 years under Japan/US collaboration.
• Irradiation hardening is significant at 300 oC, above 400oC small hardening or softening.
• BOR-60 data shows tendency of saturation in hardening beyond 30 dpa at 300 oC.
• Available high-dose data is limited to fast breeding reactor such as FFTF and BOR-60.
• High dose irradiation tests using a mixed spectrum reactor, High Flux Isotope Reactor (HFIR) has been conducted at 300, 400 and 500 oC.
Post irradiation tensile tests on F82H
4
Irradiation test matrix for F82H
*E. Gaganidze, J. Aktaa, Fusion. Eng. Des. 88 (2013) 118– 128.
High dose irradiation tests using HFIR
• The specimen has been prepared from a certain batch of F82H-IEA heat (5,000kg). Same material
• Neutron irradiation has been conducted in the High Flux Isotope Reactor, HFIR at Oak Ridge National Laboratory.
Same reactor
• Common holder design was employed for 6 capsules.
Irradiation data with minimized disturbance.
Capsule Dose (dpa) Temp. (oC) Note
JP-26 9 300/400/500 Hardening level is comparable w/ instrumented capsule JP-27 21 300/400 Hardening is greater than FFTF at 400oC
JP-28 87 300/400/500
The highest dose on RAFM in HFIR
JP-29 87 300/400/500
JP-30 20 300/400/650 RAFM joints (to be tested) JP-31 20 300/400/650 RAFM joints (to be tested)
Specimen positions in JP-28, JP-29
Position Specimen Temp. (oC)
1 Tensile 400
2 Bend-bar 500
3 Tensile 300
4 Compact 300
5 Bend-bar 300
6 Compact 400
7 Tensile 400
8 Compact 400
9 Tensile 500
10 Bend-bar 300
11 Bend-bar 300
12 Bend-bar 300
13 Bend-bar 300
14 TEM 300
Position Specimen Temp. (oC)
1 TEM 400
2 Tensile 400
3 Tensile 500
4 Bend-bar 300
5 Compact 300
6 Bend-bar 300
7 Tensile 300
8 Bend-bar 400
9 Bend-bar 500
10 Tensile 300
11 Bend-bar 300
12 Tensile 300
13 Tensile 300
14 TEM 500
JP-28 JP-29
Horizontal mid-plane
Tensile and toughness
specimen have been positioned to receive
equivalent dose.
JP28 & JP29
• A pair of non-instrumented capsule was prepared for high dose irradiation.
• Specimen from 400 and 500 oC showed rusty surface, it was found at the previous capsules.
300 oC irradiated (JP29 #13) 400 oC irradiated (JP28 #7) 500 oC irradiated (JP28 #9) 7
JP-28 JP29
Start April, 2005 Jan., 2005 Finish July, 2013 July, 2013 Temperature (oC) 300/400/500 300/400/500
Max dose (dpa) 87 87
# of reactor cycles 46 46 Exposure (MWd) 91569 92334
EFPD 1077 1086
Summary of JP-28 & JP-29
Experimental procedure, PIE
• Materials
– F82H IEA: 0.1C -8Cr-2W-0.2V-0.04Ta – F82H mod3: 0.1C -8Cr-2W-0.2V-0.09Ta
– F82H 1.4%Ni: 0.07C-8Cr-2W-0.3V-0.02Ta-1.4Ni
»
Ni58 and Ni60 isotopes were prepared
Alloying effect onlyTransmutation Helium (11appm/dpa )
and alloying effect• Post irradiation tensile tests
– SS-J3 (0.76
Tx 1.25
Wx 5
Lmm
3) sheet tensile specimen with shoulder loading
– Tensile tests were conducted at irradiation temperature in vacuum
– Cross-head speed controlled at 0.2%/s in gauge
RESULTS OF POST IRRADIATION TENSILE
TESTS AT IRRADIATED TEMPERATURE
Tensile properties of F82H (>80dpa)
• All specimen demonstrated hardening.
• Hardening was significant at lower temperature.
• Tensile properties of mod3 (0.1%Ta) is comparable with IEA.
• Ni58 including 900appm He demonstrated significant hardening at 300oC, but drastically decreased with temperature.
Tensile properties of F82H (>80dpa)
• All specimen demonstrated less elongation.
• Although Ni58 steel which includes 900appm of helium demonstrated minimum ductility, Ni60 kept its ductility >10 %.
• The minimum elongation (7.5 %) was found at 300-400 oC, where unirradiated F82H show minimum elongation.
Tirr = Ttest Tirr = Ttest Tirr = Ttest
Dose dependence of Hardening
• >80dpa, all specimen demonstrated hardening even above 400
o
C where softening was observed at the specimen irradiated in the FFTF.
• Hardening at 300
oC demonstrated tendency of saturation.
• Hardening increased with dose above 400
oC (HFIR).
*E. Gaganidze, J. Aktaa, Fusion. Eng. Des. 88 (2013) 118– 128. 12
Helium effects on Hardening
• F82H w/ 1.4%Ni58 steel produced up to 920appm of He.
–
At 300
oC, larger hardening than the others.
• He w/ immobile vacancy enhanced the hardening.
–
At 400
oC, no difference between 240 and 920ppm He.
–
>80 dpa above 400
oC, hardening is smaller than the others.
*E. Gaganidze, J. Aktaa, Fusion. Eng. Des. 88 (2013) 118– 128. 13Dose dependence of Ductility loss
14 TP Reactor Gauge
length
Gauge
width Thick.
RBT JMTR 25 mm φ 4mm
SS-3 HFIR,
JMTR 7.5 mm 1.5 mm 0.75 mm SS-J FFTF 5 mm 1.2 mm 0.25 mm SS-J3 HFIR 5 mm 1.2 mm 0.75 mm
RBT
Gauge cross section
SS-J SS-J3
Dose dependence of Ductility loss
• >80dpa, ductility is below unirradiated level. No saturation was observed.
• Specimens w/ less aspect ratio, SS-3 & SS-J give less ductility.
• The minimum ductility (7.5 %) was found at 300-400 oC, where unirradiated F82H demonstrates the minimum ductility.
• Total elongation around 300-400 oC should be monitored as well as embrittlement at <300 oC. It might limit the use of RAFM.
HFIR vs FFTF (dpa rate)
• No significant difference in damage rate is observed between FFTF and HFIR.
• Difference in damage rate between HFIR and FFTF is within factor of 2.
• Difference between HFIR and FFTF?
* A.M. Ermi, et al., DOE/ER-0313/18 (1995) 27-62. ** J.P. Robertson, et al., DOE/ER-0313/21 (1996) 249-252. 16 dpa dpa
/MWD Irradiation period (h) FFTF/MOTA
2B* 20 4.4E-04 5.2E+03 HFIR JP-27 21.2 9.1E-04 7.5E+03 FFTF/MOTA
2A* 39 5.1E-04 8.1E+03 HFIR
JP-14** 33.9 8.7E-04 - FFTF/MOTA
2A+2B 59 4.0E-04 1.3E+04 JP-28 & 29 87 9.5E-04 2.4E+04
Irradiation parameters
Softening or Hardening above 400 o C
HFIR irradiated materials demonstrated hardening FFTF irradiated materials demonstrated softening
• Softening
– Thermal Aging: Recovery, Segregation (loss of solute)
• Hardening
– Defects induced by irradiation – Irradiation induced segregation – Transmutation (W => Os)
– Lower irradiation temperature
• Increase of heat transfer between specimen and holder, but surface oxide was observed at specimen irradiated at higher temperature
• Decreasing gap between holder and sleeve?
• Post irradiation properties reflects the results of competing processes above.
• Detailed analysis on microstructure and chemical composition including gas element are required.
HFIR vs FFTF
R.E. Stoller, L.R. Greenwood., J. Nucl. Mater. 271-272 (1999) 57-62.
• No significant difference in damage rate is observed between FFTF and HFIR.
• Effects of neutron energy?
dpa dpa
/MWD Irradiation period (h) FFTF/MOTA
2B 20 4.4E-04 5.2E+03
HFIR JP-27 21.2 9.1E-04 7.5E+03 FFTF/MOTA
2A 39 5.1E-04 8.1E+03 HFIR JP-14 33.9 8.7E-04 -
FFTF/MOTA
2A+2B 59 4.0E-04 1.3E+04 JP-28 & 29 87 9.5E-04 2.4E+04
Irradiation parameters
W186
HFIR vs FFTF
R.E. Stoller, L.R. Greenwood., J. Nucl. Mater. 271-272 (1999) 57-62.
• No significant difference in damage rate is observed between FFTF and HFIR.
• Effects of neutron energy?
• Ex) W transmutation to
Os (HFIR) or Re (FFTF)
L.R. Greenwood et al., J. Nucl. Mater. 212-215 (1994) 635-639
dpa dpa
/MWD Irradiation period (h) FFTF/MOTA
2B 20 4.4E-04 5.2E+03
HFIR JP-27 21.2 9.1E-04 7.5E+03 FFTF/MOTA
2A 39 5.1E-04 8.1E+03 HFIR JP-14 33.9 8.7E-04 -
FFTF/MOTA
2A+2B 59 4.0E-04 1.3E+04 JP-28 & 29 87 9.5E-04 2.4E+04
Irradiation parameters
Impact of Re and Os to tensile properties
• Reduction of W seems small impact on tensile properties of martensitic steel.
–
If W in laves phase (reduction of solute W) transmuted to Os, it could raise the strength.
*R.L. Klueh et al. / J. Nucl. Mater. 279 (2000) 91-99. 20
Summary
• Reduced activation ferritic/martensitic steel, F82H were
irradiated up to ~87 dpa at 300, 400 and 500
oC in the HFIR.
Post irradiation tensile tests have been conducted at irradiation temperature.
–
Irradiation hardening & loss of ductility were observed even at 400 and 500
oC
• It is noted specimen irradiated in the FFTF demonstrated softening at the temperature.
• Difference between FFTF and HFIR should be investigated including transmutation effects.
• Lower irradiation temperature due to deformation of capsule material is possible.
–
Hardening was significant in the specimen irradiated at 300
oC.
The increment gradually decreased w/ dose, but the strength was obviously larger than previous works.
–