FTP/3-4Ra: Heat-Resistant Ferritic-Martensitic Steel RUSFER-EK- 181 (Fe-12Cr-2W-V-Ta-B) for Fusion Power Reactors V. Chernov, Russia.

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1 IAEA FEC 2010 Korea, Daejeon, October, 2010 FTP/3-4Ra: Heat-Resistant Ferritic-Martensitic Steel RUSFER-EK- 181 (Fe-12Cr-2W-V-Ta-B) for Fusion Power Reactors V. Chernov, Russia. FTP/3-4Rb Low Cycle Fatigue Properties of RAFM Steels after High Dose Neutron Irradiation E. Gaganidze, Germany FTP/3-4Rc RAFM Steel F82H for in-vessel components N. Okubo, Japan 1

2 IAEA FEC 2010 Korea, Daejeon, October, 2010 FTP/3-4Ra: Heat-Resistant Ferritic-Martensitic Steel RUSFER-EK-181 (Fe-2W-V-Ta-B) for Fusion Power Reactors Viacheslav M. Chernov 1, M.V. Leontyeva-Smirnova 1, D.A. Blokhin 1, N.A.Degtyarev 1, A.G.Ioltukhovsky 1, E.M.Mozhanov 1, A.B.Sivak 2, T.M. Bulanova 3, A.E. Fedoseev 3, Z.E. Ostrovsky 3, A.N. Tyumentsev 4, B.K. Kardashev 5, A.I. Blokhin 6, V.A.Romanov 6 1 JSC A.A. Bochvar High-technology Research Institute of Inorganic Materials, Moscow, Russia, 2 RRC Kurchatov Institute, Moscow, Russia, 3 JSC Research Institute of Atomic Reactors, Dimitrovgrad, Russia, 4 Tomsk State University, Tomsk, Russia, 5 Ioffe Institute of RAS, S-Petersburg, Russia, 6 2 Institute of Physics and Power Engineering, Obninsk, Russia

3 THE RF NUCLEAR REACTORS PRESENT & FUTURE, GOALS & REQUIREMENTS - Structural Materials (SMs) Fast Test Reactors: BOR-60, MBIR (2018 ) Power reactors: - Fast (PFBRs): Na-Coolant: BN-600 (60.1 dpa/year-fe, 2020 ), BN-800 (2014 ), BN-1200 (2020 ), BN-K (R&D) Pb-Coolant: Project BREST (R & D). - Fusion: TOKAMAK DEMO FPP ( ), R & D. Requirements for SMs under operation: - PFBRs (Na): Fuel Burning - (12) % ha, dpa - (90) , Temperature (cores) up to 700 (800, SMs expectations) 0 C. - FPPs: MW year/m 2, dpa Temperature (cores) up to 700 (800) 0 C (SMs expectations). Maximum Wide Operation Temperature window Tmax = (Tmax T min) with high energy efficiency via NEW ADVANCED SMs. 3

4 High-performance Structural Materials are the backbone for all Fusion (DEMO-FPPs) and Power Fast Breeder Reactors (PFBR) There are many commonalities in the SMs R&D Issues for PFBR and TOKAMAK-DEMO-FPP reactors. Substantial improvement in the performance of the Fusion SMs can be rapidly achieved with a science- and high-technology-based materials R&D approach using the RF way for the PFBRs (BN-350, BN-600, BN-800, BN- 1200). New SMs are required for further widening of temperature, mechanical and dose application windows to realize the plan for fusion energy in the first half of the 21 st century. The RF Attention is currently focused on the tasks of creating the High-dose and High&Low-Temperature data base for RAFM (12-14% Cr) Steels for PFBRs and FUSION-TOKAMAK-DEMO-FPPs. 4

5 The RF Attention is currently focused on the tasks of (1) attaining economic competitivenes of the PFBRs and Fusion Power Reactors (DEMO-FPP). (2) creating a closed fuel cycle industry (2035), and Fusion Reactors (Hybrid) are very important part of this cycle. (3) creating the high-dose and high-low-temperature data base for SMs for FB and Fusion Power Reactors. 5

6 Neutron Sources (E>0) Нейтронный спектр [ н/(cм 2 *с*mэв)] BN-600 IVV-2M, col 7-8 IFMIF DEMO-RF BOR-60 GDT-NS ITER E n, эв BN-600 Fast Sodium Power Reactor (60 dpa/y (Fe)), IVV-2M Experimental water reactor, IFMIF accelerator neutron source (2025), DEMO-RF Fusion reactor (R&D, Kurchatov Inst.) (15 dpa/y (Fe), BOR-60 experimental sodium fast reactor, GDT-NS plasma neutron source gas dynamical trap (R&D, Budker Inst.), ITER 6

7 THE QUESTIONS ON THE WAY TO THE ADVANCED SMs FOR NUCLEAR POWER Fusion and Fission REACTORS DIFFERENT: - NEUTRON SPECTRA. - NEUTRON FLUXES AND FLUENCES. - DAMAGE RATES. - STRUCTURAL MATERIALS AND NUCLEAR TECHNOLOGIES. - MODELS AND APPROACHES. HOW TO USE THE UP-TO-DATE RADIATION EXPERIMENTAL RESULTS? HOW TO DO THE SCIENCE-BASED RECOMMENDATIONS FOR ADVANCED MATERIALS? WHAT NEUTRON SOURCES ARE NECESSARY TO PROVIDE ADEQUATE SMs DATABASE FOR THE DESIGN OF FUSION POWER REACTORS IN TIME? 7

8 The RF heat resistance RAFM (12-14)%Cr Steels RAFMS RUSFER-EK-181 Fe-12Cr-2W-V-Ta-B Industrial Steel: Any ingots, Any products. Today s recommendations (300) (700) 0 C. + Reduced activation, No swelling (<100 dpa), Ductile, Industry fabrication. - No high dose tests (>100 dpa), Ferromagnetism (TOKAMAK plasma configuration?). Applications: TBM DEMO in ITER, DEMO-FPP (He, Pb-Li). FBRs (Na): BN-600, BN-800, BN-1200, BN-K, FBRs (Pb): BREST. RUSFER-EK-181 Modifications - The R&D Goals: - Precipitation hardening (nano-structured, including ODS) industrial steels. - More Homogeneity, Thermal Stability of Solid Solutions and Strengthening Precipitations and Phases. -! Improving Radiation and Heat Resistances: dpa, T max C. -! Decreasing Effect of the LTRE: T min 250(300) 0 C. - Improving the Low (Reduced) Activation Properties under Long Time Neutron Irradiation (lower concentrations of impurities elements). - Industrial manufacturing & joining (good rolling, welding and tubing) 8

9 Particles proportion RAFMS RUSFER-EK-181: Fe-12Cr-2W-V-Ta-B-C Precipitation hardening - Basic phase particles Size distribution histograms of phases particles after air quenching and tempering (> 5 nm) Carbide phases precipitate during tempering with different compositions and sizes (TEM): M 23 C 6, M 6 C, M 3 C, TaC, VC; Mean particle size is 75.1±7.4 nm Particle size, nm Carbides provide precipitation hardening of the steel and fixation of low- and large-angle boundaries (grain boundary engineering). VC/TaC nanoparticles of 3 5 nm size providing precipitation hardening of the steel after quenching and tempering VC/TaC nanoparticles of 3 5 nm size constitute an appreciable part of the carbide phase. 9

10 RUSFER-EK-181 (TTT) : Long-term strength ( ) Н ап Stress, р яж ение, MPa М П а о C о 700 C Н апряж ение, М П а Stress, MPa 100 о 650 C о 700 C 40 1E E-3 1E-2 Скорость Steady-state установившейся creep ползучести, rate, %/h %/ч Creep-rupture life, h Время до разрушения, ч Steady-state creep rate as function of stress Creep-rupture life as function of stress RESULTS: С, stress 80 MPa, creep-rupture lifetime hrs С, stress 50 MPa, creep-rupture lifetime >5000 hrs. 10

11 RUSFER-EK-181 ( ): Influence of low-temperature neutron irradiation. Impact tests of small CVN-specimens with different Thermal Treatments (TTT Traditional Thermal Treatment), CTT Cyclic Thermal Treatment near critical point Ac1, α γ transitions) 1,3 INitial, 2,4 Irradiated (BOR-60, 15 dpa, C), 5,6 Post Irradiation Annealing (500 0 C, 3 hours). Impact Energy, J 9 5 (PIA-CTT) 1(IN-CTT) 6(PIA-TTT) 3(IN-TTT) 2(IR-CTT) 4(IR-TTT) Test Temperature ( o C ) 11

12 RUSFER-EK-181. Microstructure of the specimens after TTT (upper level) and CTT (lower level) treatments after irradiation (BOR-60, oc, 15 dpa) and post irradiation annealling (550 0C, 3 hours) TTT CTT General character of the structure-phase states. Dislocation substrucrures. 12

13 BN-600 Tests ( ): RUSFER-EK-181 Neutron flux 6.5 x n/cm 2 /s (E>0), 60.1 dpa/year. NEUTRON START April Irradiation Time 560 x 2 = 1120 days. Irradiation Temperature : С ±(15-25) 0 C. Doses: dpa (April days), Results dpa (April days). Results Environment flowing sodium or static argon. Total number of samples of various types is 290 (SSTT). RADIATION PROPERTIES (Data Base): elastic and micro-plastic; mechanical; swelling; creep (pressure tubes); impact ductility; DBTT, crack-resistance; corrosion; structural and phase transformations. Preparations for BN-800 (2014) and IFMIF (2025) Irradiations. 13

14 RAFMS RUSFER-EK-181 (Fe-12Cr-2W-V-Ta-B) FOR NUCLEAR APPLICATIONS (Na, Pb, Pb-Li coolants). Reference : Temperature window: (700) 0 C, Neutron Fluence dpa Advanced : Different Modifications for the PFBRs and DEMO-FPP: Dispersion/Precipitation Hardening (Nano-structured, including ODS): Temperature window: 250(300) C, Neutron Fluence dpa The problems of reactor tests will be decided up to 2015 on the base of the RF fast power reactor BN-600. The RF main focus is to enhance the interaction between the material scientists and the designers. 14

15 Effect of Neutron Irradiation on the T DBTT in Ferritic/Martensitic Steels after S, J. Zincle (2010), Boutard et al., C.R. Physique. 9 (2008) 287 and Klueh & Harries (2001) RUSFER-EK-181, Tdbtt ( ) C, BOR-60, 340 C, 15 dpa EK-181, Initial 0.3 T M 15

16 Effect of Neutron Irradiation on the T DBTT in Ferritic/Martensitic Steels after C.Petersen, et.al. 21th IAEA Fusion Energy Conference, Chengdu, 2006 RUSFER

17 RAFM (8-9%Cr) Steels for Fusion Application TEMPERATURE WINDOW FOR NUCLEAR APPLICATIONS 300(350) C Typical good RAFM Steels: EUROFER97 (Fe-(8-9)Cr-W-V-Ta), F82H-mod. (Fe-(7-8)Cr-W-V) 17

18 23 rd IAEA Fusion Energy Conference Daejeon, Rep. of Korea, October 11-16, 2010 FTP/3-4Rb Low Cycle Fatigue Properties of Reduced Activation Ferritic/Martensitic Steels after High Dose Neutron Irradiation INSTITUT FÜR MATERIALFORSCHUNG II E. Gaganidze, C. Petersen, J. Aktaa KIT, IMF II, Karlsruhe, Germany A. Povstyanko, V. Prokhorov RIAR, Dimitrovgrad, Russia E. Diegele, R. Lässer F4E, Barcelona, Spain KIT Universität des Landes Baden-Württemberg und nationales Forschungszentrum in der Helmholtz-Gemeinschaft

19 DEMO Relevant Structural Materials Characterization Structural materials for in-vessel components of a future fusion reactor will be exposed to high neutron and thermo-mechanical loads. Synergistic effects of displacement damage, helium, etc. to be generated in a fusion reactor will strongly influence structural materials performance. Objective of current work: Investigation of high dose neutron irradiation influence on Low Cycle Fatigue (LCF) Properties of European Reference RAFM Structural Steel for ITER TBM and DEMO Blanket EUROFER97 and Japanese RAFM Steel F82H-mod. by using Small Specimen Testing Technology (SSTT) Irradiation Programmes ARBOR 1 & ARBOR 2 Irradiation facility: Bor 60, SSC RIAR Irradiation condition: up to 70 dpa at C LCF specimens complying SSTT (L=27mm, GL=7.6mm, =2mm) Post Irradiation Examination at SSC RIAR - Isothermal tests with ε tot between % Institut für Materialforschung II

20 LCF Properties EUROFER97 (980C/0.5h + 760C/1.5h) Strain Range ε tot (%) ARBOR (KIT) unirr. 31dpa/330 C 47dpa/330 C 71dpa/330 C SOSIA-02 (NRG) unirr. 2dpa/300 C model unirr. T test = C Number of Cycles to Failure (-) SSTT large Strain Range ε inelastic (%) T test =330 C unirr. 31dpa 47dpa 71dpa Number of Cycles to Failure (-) considerable underestimation of fatigue lifetime in the reference unirradiated state by SSTT SSTT: minor influence of neutron irradiation on fatigue lifetime for ε tot between % description of the unirradiated and part of irradiated data by a common Manson-Coffin relation noticeable reduction of fatigue life for inelastic strain ranges above 0.5% partly due to inelastic deformation already after the first quarter cycle E. Gaganidze Institut für Materialforschung II

21 LCF Properties EUROFER97 HT (1040C/0.5h + 760C/1.5h) Strain Range ε tot (%) T test =330 C unirr. 31dpa 47dpa 71dpa Number of Cycles to Failure (-) Strain Range ε inelastic (%) T test =330 C unirr. 31dpa 47dpa 71dpa Number of Cycles to Failure (-) For adequate total strains nearly no influence of 47dpa irradiation on fatigue lifetime increased lifetime after 71dpa irradiation more pronounced for low ε tot due to hardening For adequate inelastic strains decreased lifetime after 47dpa irradiation in comparison with unirradiated state description of the unirradiated and 71dpa data by a common Manson-Coffin relation E. Gaganidze Institut für Materialforschung II

22 LCF Properties F82H-mod (1040C/38min + 750C/2h) Strain Range ε tot (%) T test =330 C unirr. 31dpa 47dpa Number of Cycles to Failure (-) Strain Range ε inelastic (%) T test =330 C unirr. 31dpa 47dpa Number of Cycles to Failure (-) Fatigue behaviour after 47dpa irradiation increased lifetime in the irradiated state more pronounced for high ε tot 1.0% apparent increase of lifetime below ε tot 0.9% ( ε inelastic 0.43%) due to irradiation hardening unknown reasons (in addition to hardening) for enhanced lifetime for high ε inelastic 0.57% E. Gaganidze Institut für Materialforschung II

23 Conclusions Investigation of isothermal LCF properties of EUROFER97 and F82H-mod after neutron irradiation to 71 dpa at C by using SSTT conservative estimation of fatigue lifetime in the unirradiated state by SSTT no statistical analysis possible due to limited number of irradiated specimens Increase of stress due to irradiation induced hardening may lead to enhanced lifetime as a result of reduction of the inelastic strain range especially at low strain ranges reduced lifetime as a result of accelerated fatigue damage evolution Remarkable changes in fracture surface morphology: appearance of a complex, 3D fracture surfaces, initiation of secondary cracks propagating into axial direction, roughening of morphology with increasing the damage dose shows no clear effect on fatigue lifetime For unambiguous interpretation of irradiation influence: need for further investigation of LCF properties addressing the state of the surface finish quality and its possibly different influence on fatigue lifetime of SSTT specimens in the unirradiated and irradiated conditions Institut für Materialforschung II

24 LCF Properties Fracture Surface Morphology EURFOER97 HT, 71dpa/334 C, Δε tot =0.9 % F82H-mod, 47dpa/337 C, Δε tot =0.9 % complex, 3D fracture surface morphology terrace like pattern due to deflection of fatigue crack emission of the secondary cracks propagating into axial direction (EUROFER97) pronounced roughening of fatigue fracture surface (F82H-mod) no clear effect of changes in fracture surface morphology on fatigue lifetime 24

25 FTP/3-4Rc : RAFMS F82H for in-vessel components F82H Fe-7.7Cr-2W-V N. Okubo, K. Shiba, M. Ando, T. Hirose, H. Tanigawa, E. Wakai, T. Sawai, S. Jitsukawa and R. E. Stoller* Japan Atomic Energy Agency *Oak Ridge National Laboratory 25

26 RAFMS F82H Fracture Toughness the Influence of Several Heat Treatments Irradiation hardening and fracture toughness of the RAFMS F82H after irradiation (20 dpa) at relative low temperatures below 400 o C, were investigated with a focus on changing the fracture toughness transition temperature as a result of several heat treatments. The results revealed that optimization of the heat treatment conditions improved the irradiation response with respect to toughness and ductility. 26

27 Reduction of irradiation hardening by tightening heat treatments IEA Mod1 A Mod1 B Mod1 C Mod1 E Mod1 F Mod1 G Mod1 H Mod3 Heat Treatments Normalizing 1040 o C /40min 1040 o C /0.5h Tempering 750 o C /1h IEA+1100 o C/2h +960 o C/0.5h 740 o C /1h Heat treatmen t1 N/A Heat treatmen t2 N/A 800 o C/0.5h 700 o C/10h 860 o C/0.5h 700 o C/10h 920 o C/0.5h 700 o C/10h N/A N/A 750 o C/1.5h 700 o C/10h 800 o C/0.5h 700 o C/1h 960 o C/0.5h 700 o C/10h N/A N/A 0.2% Proof Stress (MPa) IEA Mod3 Mod1 C B A C,F,H Ref. A,B,G Ref. 300 o C Irrad. RT test Type SSJ3 C,F,H E F Dose (dpa) Fig. Dependence of 0.2% proof stress 27 on irradiation damage G IEA,Mod3 Ref.

28 Improvement of irradiation response of toughness by tightening heat treatment experiments Toughness K Jc (MPa m 1/2 ) Mod1 13dpa IEA 18dpa IEA Ref. Mod1 18dpa 1T-CT specimens Temperature ( o C) Fig. Temperature dependence of fracture toughness of F82H

29 CONCLUSION OUR NEAR FUTURE IS FUSION JOULE-POWER IN ECOLOGICAL CLEAN ENVIRONMENT Thanks for your Attention & Patience 29