[보고서]원전 구조재료의 수소취성 평가/예측 및 관리 기술개발

보고서 정보

주관연구기관

한국원자력연구원
Korea Atomic Energy Research Institute

보고서유형

최종보고서

발행국가

대한민국

언어

한국어

발행년월

2011-09

과제시작연도

2010

주관부처

지식경제부
Ministry of Knowledge Economy

등록번호

TRKO201300024534

과제고유번호

1345139160

사업명

원자력기술개발사업

DB 구축일자

2013-09-14

키워드

수소화물지연파괴.입계응력부식균열.동적변형시효.delayed hydride cracking.intergranular stress corrosion cracking.dynamic strain aging.

표 (a) Nucleation of hydrides at a crack, (b) growth of hydrides and (c) growth of a crack by the cracking of hydrides grown to the critical length.
표 Temperature dependence of the crack growth rate in (a) unirradiated and (b) irradiated CANDU　Zr-2.5Nb tubes.
표 Steep rise of the threshold stress intensity factor or KIH above 300oC.
표 Neutron fluence dependence of (a) the tensile strengths and (b) the crack growth rate of a Zr-2.5Nb tube that were determined at 240oC after neutron irradiation at low temperatures ranging from 240 to below 285oC.
표 (a) Microstructures of the Zr-2.5Nb with different heat treatments and (b) their DHC velocity with temperature.
표 Yield stress dependence of DHC velocity at 250oC for the Zr-2.5Nb tubes with continuous and discontinuous β-Zr phase before and after the normalization by DH.
표 Crack growth rate of Zr-2.5Nb tube with (a) the total hydrogen concentration and (b) the extent of hydrogen supersaturation.
표 Difference the TSSP and the TSSD for Zr-2.5Nb tubes at constant temperatures.
표 Loading curves of 1 cycle/min with the load ration R changing from 0.13 to 0.68.
표 Crack growth rate at 250oC of the Zr-2.5Nb tubes with the load ratio changing from 0.13 to 0.68 that were determined
$Striations with the load ratio, R on the fracture surfaces of the heat-treated Zr-2.5Nb tubes after DHC tests at 250oC: (a) R=0.32, (b) R=0.51, (c) R=0.68, and (d) R=1.0.$ 표 Striations with the load ratio, R on the fracture surfaces of the heat-treated Zr-2.5Nb tubes after DHC tests at 250oC: (a) R=0.32, (b) R=0.51, (c) R=0.68, and (d) R=1.0.
표 %Nb in the β-Zr at the inlet, middle and outlet regions of the Zr-2.5Nb tube irradiated for 10 years in Wolsong 1.
표 the distribution of the β-Zr phase in Zr-2.5Nb tubes with the location: (a) fully discontinuous β-Zr phase due to thermal decomposition and (b) fully continuous β-Zr phase.
표 Crack growth rate of the Zr-2.5Nb tubes with the distance from the inlet.
표 The ratio of axial and radial DHC velocity of the Zr-2.5Nb tubes with annealing time at 400oC both of which were determined over a temperature range of 120 to 240oC.
표 Neutron fluence dependence of DHC Velocity at the inlet and the outlet regions of the Zr-2.5Nb tube.
표 (a) Direct pole figures of a CAND Zr-2.5Nb tube with the most basal poles oriented toward the tangential direction, (b) a diagram showing the angle between the loading axis and the basal poles and (c) the tensile specimens taken from the the tangential direction (TD) and from the longitudinal direction (LD).
표 Twinning is working when the angle between direction of stres and the basalpole is zero but slip is working when the angle between them is equal to 90oC.
표 Stress-strain behaviors of the TD and LD specimens taken from the Zr-2.5Nb tube at room temperature.
표 Textuers of the TD specimens before and after the tensile tests that were conducted at temperatures ranging from 27oC to 403oC.
표 Textures of the LD specimens before and after the tensile tests that were conducted at temperatures ranging from 27oC to 403oC.
표 Tensile and yield strengths of the TD (Tangential direction) and LD　(Longitudinal direction) specimens taken from the Zr-2.5Nb tube.
표 Density of twinning for the TD specimens with tensile test temperature.
표 The extent of strain hardening and uniform elongation of the Zr-2.5Nb LD specimen with tensile testing temperature.
표 The formation of cellular dislocations in a Zr-2.5Nb pressure tube and Zircaloy-4, that were given tensile tests at 350 and 300oC, respectively.
표 Strain hardening of a Zr-2.5Nb tube with direction: the LD specimens showed a constant SH over a temperature range below 250oC but decreased linearly with temperature.
표 Intergranular cracking in a 304 stainless steel tube and a Alloy 600 tube exposed to primary water in PWRs.
표 Serrations in (a) Alloy 600 and (b) 316L stainless steel during tensile deformation.
표 Tensile specimen with a cold pressed hump.
표 (a) Crack propagation along a grain boundary assisted by slip bands. Crack growth tests in PWR environment (360oC, pH320oC=7.2), CT specimen (40% cold rolled 304L, Kmax=40 MPam1/2, R=0.7, 1834h) and (b) Planar slip at a grain boundary in Alloy 600.
표 IGSCC initiation sites lined with slip bands intersecting the grain boundary. CERTs (5x10-8/s) in nominal hydrogenated primary PWR environment at 360oC.
표 Evolution of the stress amplitude with the number of cycles for solution annealing (SA) at 930oC and SA+aged 50h at 670oC A-286 austenitic stainless steel fatigued at RT and R=-1for 0.2% plastic strain control.
표 Planar dislocations in aged A286 austenitic stainless steel after fatigue deformation to over 100 cycles at RT with R=-1.
표 Absence of γ΄ precipitates in the slip bands in aged A286 stainless steel after fatigue deformation to over 100 cycles at RT with R=-1.
표 CERT test results on pre-fatigued A286 steels
표 (a) Limited IG crack propagation in aged A286 steel pre-fatigued to 8 cycles at RT and (b) extensive IG cracking in aged A286 steel pre-fatigued to 200 cycles at RT, both of which were exposed to CERT tests at 360oC.
표 Oxide examinations on 304L stainless steel exposed to CERT in PWR environment (360oC, pH320oC=7.2, strain rate=5x10-8/s, 17000h) (From Couvant)
표 Oxide examination (EDS). CT specimen in PWR environment (304L, 360oC, pH320oC=7.2, K=40MPam1/2, R=0.7, 1834h) (from Ref. 1)
표 Tensile properties of a 316L stainless steel with 0.01 to 0.15 wt.% of nitrogen with temperature: (a) the yield stress and (b) the tensile stress.
표 Tensile elongations of 316L stainless steel containing N with temperature showing a tensile elongation minimum at 400oC.
표 Stain hardening of 316L stainless steel containing 0.01 wt.% N with the strain rate, showing the negative strain rate sensitivity of strain hardening.
표 Strain hardening of 316L stainless steel with 0.01 wt.% N after normalization by the yield stress.
표 Temperature dependence of serrated flow in 316L stainless steel with 0.01 wt.% N after tensile deformation at 2x10-3/s.
표 Lattice contraction of Alloy B (Ni-31Cr-2Fe) on aging at 475oC (From Marucco).
표 Increased hardness of Ni3Fe on aging at 480oC with time and the amount of pre-deformation (From Kornilov).
표 A change of the lattice spacing in a 40% cold worked 316L stainless steel with aging time at 400oC.
표 Creep rate in austenitic stainless steel
표 (a) Yield behavior and (b) work hardening (WH) of disordered Ni3Fe with aging time at 490oC showing that the aging time to induce a yield drop corresponds to the onset of an increase of work hardening.
표 Dislocation structures in a 316L stainless steel containing hydrogen with tensile testing temperature: (a) before tensile tests (b) and (c) after tensile tests at 200oC and 400oC, respectively.
표 Chemical composition of type 316L stainless steel (wt%)
표 Compact tension specimen used for fatigue crack growth rate tests.
표 Comparison of crack lengths measured by DCPD and an optical microscope.
표 Fatigue crack growth rate of 316L stainless steel with the degree of cold work and hydrogen concentration.
표 Effect of hydrogen on fatigue crack growth rate of a 316L stainless steel.
표 Effect of temperature on fatigue crack growth rate of a 316L stainless steel.
표 Parameters of Paris
표 Heat treatment conditions applied to a solution-annealed 316L stainless steel.
표 Diagram of the U-bending machine used for making U-bend specimens.
표 Test apparatus for stress corrosion cracking of 316L stainless steel in MgCl2 solutions.
표 TEM micrographs of a 316L stainless steel used in this work: (a) solution-annealing and water-quenching, (b) 20% cold-working.
표 Microstructural evolution of 20% cold-worked 316L austenitic stainless steel annealed at (a) 600℃, (b) 650℃ and (c) 700℃.
표 Chemical composition of grain boundary precipitates formed after aging at 600oC for 59h
표 Chemical composition of grain boundary precipitates formed after aging at 650oC for 24h
표 Chemical composition of grain boundary precipitates formed after aging at 700oC for 165h
표 Formation of precipitates on aging of 316L stainless steel: Laves phase formed at (a) the grain boundary after ageing at 600oC for 150h, (b) on the planar dislocations after aging at 650oC for 165 h, (c) large sigma phase and smaller laves phase inside a grain on aging at 600oC 741h.
표 Chemical compositions of precipitates formed in the grains after aging at 600oC for 150h.
표 Chemical compositions of the yeta and sigma precipitates formed in the grains after aging at 600oC for 741h.
표 Distribution of Cr concentration across the grain boundary in a 20%CW 316L stainless steel after aging at 600oC for (a) 24h and (b) 59h.
표 Distribution of Cr concentration across the grain boundary in a 20%CW 316L stainless steel after aging at 650oC for (a) 24h and (b) 59h.
표 Distribution of Cr concentration across the grain boundary in a 20%CW 316L stainless steel after aging at 600oC for (a) 24h and (b) 59h.
표 The number of cracked U-bend specimens when heat-treated 316L stainless steels at 600 to 700oC were exposed to boiling MgCl2 solutions of 155oC.
표 SCC susceptibility of the as-cold worked and heat treated 316L stainless steel upon exposure to boiling MgCl2 solution at 155oC.
표 Crack growth pattern of the heat-treated 316L stainless steel at 600oC for (a) 2h, (b) 24h and (c) 59h.
표 Crack growth pattern of the heat-treated 316L stainless steel at 650oC for (a) 2h, (b) 24h and (c) 59h.
표 Crack growth pattern of the heat-treated 316L stainless steel at 700oC for (a) 2h, (b) 24h, (c) 59h and (d) 165h.
표 Crack growth pattern of the as-cold worked 316L stainless steel upon exposure in boiling MgCl2 solution at 155oC for xxh.
표 Fracture pattern of a heat-treated 316L stainless steel at 700oC for 2h upon exposure to MgCl2 solution at 155oC, revealing that a crack grew transgranularly at the stage of crack initiation.
표 Percent IGSCC of irradiated 304 or 316 type stainless steels to 2x1021 n/cm2 or 3 dpa as function of the Bulk Cr content when exposed to SSRTs in high purity water of 289oC with 8 ppm DO.
표 Stress-strain curves of irradiated SA 304 STS to 50 dpa at 370oC when exposed to SSRTs of 5x10-7/s in either air or water with 0.01-8 ppm DO.
표 Intergranular and transgranular cracking in water with (a) 0.01 ppm and (b) 8 ppm, respectively, when irradiated SA 304 steels to 50 dpa were tensile tested at 2.5x10-7/s and 289oC.
$Planar dislocations called dislocation channeling at the fracture tip of the specimen tested in air: (a) BF and (b) DF.$ 표 Planar dislocations called dislocation channeling at the fracture tip of the specimen tested in air: (a) BF and (b) DF.
$Planar dislocations at the fracture tip of the specimen tested in water with 0.01 ppm DO: (a) BF, (b) SADP showing unidentified precipitates, (c) dislocation channel cleared of precipitates and (d) DB showing short line dislocations are decorated with precipitates.$ 표 Planar dislocations at the fracture tip of the specimen tested in water with 0.01 ppm DO: (a) BF, (b) SADP showing unidentified precipitates, (c) dislocation channel cleared of precipitates and (d) DB showing short line dislocations are decorated with precipitates.
표 Strain rate dependence of IG cracking rate of irradiated 10% CW 304 SS to ~7 dpa in Point Peach 1 PWR upon tensile testing at 315oC in Ar.
표 Stress-strain curves of CW 316 stainless steels irradiated to 53 dpa during slow and conventional tensile tests at 593K along with those during SSRTs in water environments.
표 Slow tensile tests in Ar gas at an extension rate of 6.7x10-8/s.
표 Fracture surface of the 53 dpa specimen after SSRT in Ar at 593K.
$Side views of fracture surface in PWR irradiated CW 316 stainless steels after SSRT tests in 593K simulated PWR primary water: (a) 53 dpa/2.8 ppm DH/81%IG, (b) 35 dpa/0 ppm DH/16%IG and (c) 53 dpa/0.02 ppm DO/91%IG.$ 표 Side views of fracture surface in PWR irradiated CW 316 stainless steels after SSRT tests in 593K simulated PWR primary water: (a) 53 dpa/2.8 ppm DH/81%IG, (b) 35 dpa/0 ppm DH/16%IG and (c) 53 dpa/0.02 ppm DO/91%IG.
$Hydrogen concentration in fracture section and grip section of the 53 dpa specimens after SSRT tests in different water conditions.$ 표 Hydrogen concentration in fracture section and grip section of the 53 dpa specimens after SSRT tests in different water conditions.
표 Apparent CGR in SSRT tests versus estimated corrosion potential in commercial 304 and 316 stainless steels irradiated irradiated in LWRs.
표 Stress-strain curves of Alloy 600 with test environments upon exposure to slow tensile tests at 2x10-7/s.
표 Fracture surfaces of Alloy 600 with test environments: (a) air, room temperature, (b) deaerated water, 250oC (c) air saturated water, 360oC (d) deaerated water, 360oC.
표 Percent intergranular cracking of Ni-XCr-9Fe when slow tensile tests were conducted at 3x10-7/s and 360oC in Ar or in primary water, showing that IG cracking occurred even in Ar and was enhanced in primary water.
표 Diagram explaining oxidation behavior of Alloy 600 at the grain boundary and the surface during exposure to high temperature water of 360oC.
표 Microstructure of (a) oxide-metal interface in the oxidized grain boundary of Alloy 600: (b) enlarged microstructure with TEM and (c) a diagram explaining the oxidation behavior of Alloy 600.
표 Standard free energy of formation of oxides with temperature.
표 STEM/EDS maps of crack tip #1 in Alloy 600 nozzle showing ~1wt.% S to the end of oxide and Ni enrichment in metal ahead of a crack tip.
표 Alloy composition (wt.%) and heat treatments used.
표 Surface composition of coupons with PPR varying from 0.09 to 0.5 that was determined by XPS after exposure at 400oC[25].
표 Summary of uniform surface film and intergranular (IG) oxides observed in corrosion coupons after testing at 400oC
표 ATEM analysis of the crack tip in MA Alloy 600 steam generator tube
표 Oxide formed near triple point in a steam generator tube20).
표 Effect of hydrogen on the yield and tensile strengths of the Zr-2.5Nb tube.
표 Chemcial composition of 316L stainless steel of plate and rod shapes.
표 Diagram of tensile specimens of plate and rod shapes.
표 수소장입 장비의 개략도
표 봉상 및 판상시편의 수소장입 실험 조건
표 봉상 및 판상시편의 구리도금 실험 조건
표 로크웰 경도기 및 비커스 경도기의 측정 조건.
표 수소장입 후 균질화 열처리가 진행 된 시편의 수소함량 측정
표 수소 유무에 따른 600oC 균질화 열처리된 316L 스테인리스강의 상온 응력-변형 곡선.
표 변형속도에 따른 316L 스테인리스강의 상온 항복강도.
표 변형속도에 따른 316L 스테인리스강의 상온 인장강도.
표 변형속도에 따른 316L 스테인리스강의 상온 연신율.
표 (a) 수소장입후의 균질화 열처리를 진행 한 봉상시편의 미세조직, (b) 수소장입후의 균질화 열처리를 진행 하지 않은 봉상시편의 미세조직.
표 2×10-3/s 변형속도로 인장시험 된 봉상 시편의 파면 SEM 이미지. (a) 수소장입과균질화 열처리 모두 진행하지 않은 시편, (b) 수소장입 후 균질화 열처리 진행하지 않은 시편, (c) 수소장입 하지 않고 균질화 열처리만 진행한 시편, (d) 수소장입 후 균질화 열처리를 진행한 시편.
표 인장시험 전에 측정 한 봉상 316L 시편의 로크웰 경도.
표 인장시험 전에 측정 한 봉상 316L 시편의 경도.
표 2×10-3/s 변형속도로 인장시험 후 측정 한 봉상 316L 시편의 경도.
표 세 가지의 strain rate에서 냉간 가공율 0%, 20%, 40%의 시편을 각각 수소가 장입 된 시편과 수소가 장입 되지 않은 판상 316L 시편의 항복강도 값.
표 세 가지의 strain rate에서 냉간 가공율 0%, 20%, 40%의 시편을 각각 수소가 장입 된 시편과 수소가 장입 되지 않은 판상 316L 시편의 인장강도 값.
표 세 가지의 strain rate에서 냉간 가공율 0%, 20%, 40%의 시편을 각각 수소가 장입 된 시편과 수소가 장입 되지 않은 시편의 연신율 값.
표 (a) 수소 장입 전 • 후의 판상시편의 비커스 경도값, (b) 수소 장입된 시편과 장입되지 않은 판상 시편을 2×10-3 /s의 변형속도로 인장시험 진행 한 후 측정 한 비커스 경도
표 30분의 대기시간 동안 온도에 따른 수소 확산 거리 계산 결과.
표 봉상 316L 시편의 온도 변화에 따른 항복강도 값의 변화.
표 온도 변화에 따른 봉상 316L 시편의 인장강도 값의 변화.
표 봉상시편의 온도 변화에 따른 연신율 값의 변화.
표 모든 변형속도에서 온도 변화에 따른 항복강도 값의 변화.
표 모든 변형속도에서 온도 변화에 따른 인장강도 값의 변화.
표 모든 변형속도에서 온도 변화에 따른 연신율 값의 변화.
표 일정한 온도에서의 온도 변화에 따른 인장강도 값의 변화.
표 온도 변화에 따른 변형속도 감수성의 변화.
표 온도의 변화에 따른 strain hardening stress 값의 변화.
표 온도 변화에 따른 임계 변형량의 변화.
표 변형속도에 따른 임계 변형량의 변화.
표 수소가 장입된 시편을 상온에서 600 ℃의 온도구간에서 인장 시험을 진행한 시편의 EBSD 분석결과.
표 상온-600 ℃ 온도 구간에서 인장 시험 된 시편에 대해 EBSD로 측정한 쌍정 입계량.
표 모든 변형속도에서 온도 변화에 따른 판상시편의 항복강도 값의 변화.
표 모든 변형속도에서 온도 변화에 따른 판상시편의 인장강도 값의 변화.
표 모든 변형속도에서 온도 변화에 따른 판상시편의 연신율 값의 변화.

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