ML15329A273
| ML15329A273 | |
| Person / Time | |
|---|---|
| Site: | Indian Point  |
| Issue date: | 12/31/2005 |
| From: | Couvant T, Vaillant F, Amzallag C, Boursier J, Champredonde J Govt of France, EDF Generation |
| To: | Atomic Safety and Licensing Board Panel |
| SECY RAS | |
| References | |
| RAS 23735, 50-247-LR, 50-286-LR, ASLBP 07-858-03-LR-BD01 | |
| Download: ML15329A273 (9) | |
Text
INFLUENCE OF A CYCLIC LOADING ON THE INITIATION AND PROPAGATION OF PWSCC IN WELD METAL 182 François Vaillant1, Jean-Marie Boursier1, Thierry Couvant1, Claude Amzallag2, Jacques Champredonde3 1EDF/R&D/MMC, Les Renardires Research Center, 77818 Moret sur Loing, France 2EDF/SEPTEN, 12-14 avenue Dutrievoz, 69628 Villeurbanne Cedex, France 3EDF/CEIDRE, 2 rue Ampre, 93206 - Saint-Denis Cedex 01 Keywords: Stress Corrosion Cracking, weld metal 182, primary water, cyclic loading Abstract PWSCC (Primary Water Stress Corrosion Cracking) of nickel based weld metal 182 is now a major issue in Pressurised Water Reactors, since significant cracking was observed in several welds of the primary circuit in some countries. Many questions arise about the stress (or strain) threshold for initiation and on the crack growth rates of SCC, with significant differences depending on the orientation of the loading axis with regard to the dendrites.
The stress threshold for initiation was determined at the level of 350 MPa with constant load tests on as-welded material. This threshold was not significantly modified by a ripple loading at 360°C. The strain threshold for initiation, determined by interrupted SSRTs for various elongations, was found to range between 1.25 and 1.5%.
Preliminary data of crack growth rates (CGRs) at 325°C provided a dependence on (K-9)0.4 for the average values of the CGRmax.
The strongly oriented microstructure led to faster (x 2 to 3) CGRs in the direction of the dendrites. The influence of a trapezoidal loading (R = 0.7, 2.8 10-4 Hz) on CGRs depended on the orientation : no significant modification was found with respect to a pure static loading in the direction TL perpendicular to the dendrites, but some significant increase (x 5 to 7) could be observed in the direction of the dendrites TS. A stress relief treatment (610°C) could lower the CGRs by a factor 2 to 3.5 with respect to the as-welded condition. The results are discussed with regard to available data from literature and compared to the background on alloy 600 : the chemical composition of the weld metal could lead to some variability (factor 3) in the CGRs (4 welds with significantly different chemical compositions).
Tests are scheduled to account for the influences of temperature and composition of the weld metal on the stress threshold and on the crack velocities.
Introduction PWSCC (Primary Water Stress Corrosion Cracking) of nickel based weld metal 182 is now a major issue in Pressurised Water Reactors, since significant cracking was observed in several welds of the primary circuit in several countries. Despite important R&D efforts to determine the influence of the main parameters which could affect PWSCC of alloy 182, many questions arose about the stress- (and strain-) threshold for initiation and on the crack growth rates of SCC, with significant differences depending on the orientation of the loading axis with regard to the dendrites.
Moreover, because crack growth rates are sometimes extensively determined using periodic unloading reloading procedures, a comparison was proposed for CGRs obtained with this kind of loading with respect CGRs values deduced from a pure static loading, depending on the orientation of specimens.
This contributing paper presents the status of EDF R&D program on the initiation and propagation of SCC in weld metal 182, with a particular emphasize on the influence of the loading mode.
Materials Two welds (D545 and D1054) in alloy 182 were investigated in the as-welded conditions : they were realized by two different manufacturers with SMAW process, using the same batch of electrodes (Soudonel CQ5, diameter 4 mm) to fill a V-shape (10°)
mould (width 50 mm at the bottom, thickness 35 mm, length 350 mm) made of alloy 600. The welding conditions were 110 A, 19 volts, temperature between weld deposition higher than 128°C.
The resulting weld metal consisted in a pile-up of 15 layers with 7 beads.
The chemical compositions and mechanical properties met the RCC-M requirements.
Table I. Chemical composition and mechanical properties of weld metals 182 C
Si Mn Ni Cr Ti Nb + Ta Fe YS20 (MPa)
UTS20 (MPa)
YS350 (MPa)
Requir AWS 5.11-76 d 0.10 d 1 0,6 max 5.0 to 9.5
! 59 13 to 17 d 1
> 1.8 6 to 10 t 250 t 550
> 190 D545 0.029 0.42 7.55 bal.
14.8 0.08 2.13 7.35 395 657 353 D1054 0.026 0.35 6.20 bal 15.0 0.05 2.00 6.90 386 627 347 Proceedings of the 12th International Conference on Environmental Degradation of Materials in Nuclear Power System - Water Reactors -
Edited by T.R. Allen, P.J. King, and L. Nelson TMS (The Minerals, Metals & Materials Society), 2005 557 RIV000140 Submitted: November 9, 2012 United States Nuclear Regulatory Commission Official Hearing Exhibit In the Matter of:
Entergy Nuclear Operations, Inc.
(Indian Point Nuclear Generating Units 2 and 3)
ASLBP #: 07-858-03-LR-BD01 Docket #: 05000247 l 05000286 Exhibit #:
Identified:
Admitted:
Withdrawn:
Rejected:
Stricken:
Other:
RIV000140-00-BD01 11/5/2015 11/5/2015
Experimental procedure Tests and specimens Initiation tests. The tests were mainly performed to determine the stress and strain thresholds for SCC, they included :
x Constant load tests in order to assess a threshold stress on tensile specimens with a diameter of 4 mm and a gauge length of 25 mm. Most of the results obtained on weld D545 were previously reported in [1,2].
x Constant extension rate tests (SSRTs, 5 10-8 s-1) on tensile specimens with a diameter of 4 mm and a gauge length of 85 mm, cut in the weld D1054. They were interrupted after various elongations in order to provide a threshold strain, most suitable for application to components in plants.
x Periodic unloading-reloading at R = 0.9 every hour (frequency 2.8 10-4 Hz), on tensile specimens with a diameter of 4 mm and a gauge length of 25 mm, cut in the weld D545. They have allowed to assess the influence of a ripple load near the stress threshold defined by the previous constant load tests.
Propagation tests. The tests were performed firstly to determine the influence of the main mechanical and metallurgical parameters on the CGRs, secondly to assess any influence of a periodic unloading-reloading procedure (R = 0.7, frequency 2.8 10-4 Hz, hold time 57 min) on the CGRs, with regard to the CGRs measured with a pure static loading. CT specimens from both welds were used, thickness 15 mm, pre-cracked by fatigue in air at Kfmax less than 15 MPam. They were cut in the welds according to the TL orientation (fatigue pre-crack perpendicular to dendrites in a plane containing the axis of the dendrites) and the TS orientation (fatigue pre-crack in the direction of the axis of the dendrites, see Figure 1). They have allowed one to assess the influence of the orientation on the CGRs. The results were compared to previous results obtained both on CT, DCB and WOL specimens [2,5].
Figure 1. Orientation of the CT specimens in the welds Environment and facilities The basic environment contained 1000 ppm B as boric acid and 2 ppm Li as LiOH,H2O, with 30 cc/kg of hydrogen. The control of hydrogen depended on the facility and the temperature.
Initiation tests. They were conducted in static autoclaves at 360°C, as shown in Figure 2 and Figure 3. The SSRT facility was described with details in [3] (Figure 2), deaeration was performed by evaporation of 20% of the water volume at 125°C, then hydrogen was introduced and controlled by a AgPd thimble at 360°C.
Figure 2. Autoclave for SSRTs at 360°C Constant load and ripple load tests were performed in a static autoclave placed in the load line of a creep machine. The load was applied by dead weights to reach the maximum stress level (350 or 380 MPa), a part (10%) of the load was applied by a volume of water admitted in a tank installed on the dead weights, at regular intervals with a constant flow rate in order to reach the desired trapezoidal loading (rising time 90 s, hold time 57 mn).
Figure 3. Facility for SCC tests with constant load or periodic unloading-reloading Propagation tests. They were performed at 325°C in an autoclave equipped with a load line containing 4 CT specimens, mounted on a creep machine in which the load was applied by using dead weights (static loading) or an air-jack (trapezoidal loading, rising time 90 s, hold time 57 mn), Figure 4. The autoclave was constantly fed in primary water with a Cormet loop to ensure the required water chemistry (conductivity and oxygen control) and hydrogen was monitored by an Orbisphere sensor to meet a content of 30 cc/kg.
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Figure 4. Facility for SCC CGRs measurements with constant load or periodic unloading-reloading Evaluation of the crack depth Initiation tests. During the test, a LVDT sensor allowed a record of the elongation of the load line. The crack extension was assessed by examination of fracture surface (optical and/or scanning electron microscope). For unbroken specimen, the examination of the surface was realized optically.
Propagation tests. The true extension of the crack was performed on the fracture surface (optical and/or scanning electron microscope), along the longest crack branch in the case of macrobranching) : it has provided maximum value ('amax), and mean value ('amean) of the crack depth, in the latter case after measurement on 15 equally-distributed points of the crack front.
The crack growth rate (CGRmax or CGRmean) was deduced from the crack depth and from the duration of the test (generally 1300 h to 2000 h).
Results Initiation of SCC Threshold stress Vth. From previous constant load tests performed at 350°C on tensile specimens (EDF and CEA) and capsules (Framatome ANP) [1], it was deduced that for reasonable durations of tests, the stress threshold Vth for PWSCC of alloy 182 was near 350 MPa. Since that time, this assumption was reinforced by a rupture by SCC observed after 23771 h at 350 MPa on weld metal D 545 at 350°C [4]. Assuming an activation energy of 185 kJ/mol, it corresponded to a time for failure next to 13700 h at 360°C, which will be the reference result in the followings.
Strain threshold. In order to improve the use of such data for plant components, the threshold strain was investigated on both welds using interrupted SSRTs (5 10-8 s-1). Preliminary tests on weld metal D545 have demonstrated that no cracking occurred after a (plastic) elongation of 0.9%and a rupture by SCC was noted for an elongation ranging between 3.4% and 4.9%. Complementary data were obtained on weld metal D1054, without any cracking for 1.0 and 1.25% elongation, while a very significant cracking was noted for 1.5% elongation (Figure 5). It meant that the threshold strain ranged between 1.25 and 1.5%, which was roughly consistent with the threshold stress (350 MPa), due to the extremely severe SSRTs. For these reasons, this threshold appeared slightly lower than the value of 2% determined from capsules tests in [1].
Figure 5. SC crack after an interrupted SSRT at 1.5% elongation at 360°C (weld D 1054)
Influence of a ripple loading on Vth. Finally, the influence of a ripple loading (R = 0.9, 2.8 10-4 Hz) on the stress threshold was investigated at 360°C on weld metal D545. At the maximum stress of 380 MPa, a significant crack occurred after 7372 h under a ripple loading but the result on a pure static loading at 380 MPa was not available at that time. At the maximum stress of 350 MPa, a rupture occurred by SCC after 14034 h under a ripple loading (Figure 6). This result was very similar to the reference result obtained with a pure static loading at 350 MPa (13700 h). Despite the limited number of available results, a ripple loading did not seem to induce a significant influence on the stress threshold of alloy 182. A definitive conclusion will be drawn with regard to the influence of a ripple loading at the end of the test at 380 MPa.
Figure 6. Fracture surface of specimen in weld metal D 1054 after a ripple loading at R = 0.9, 2.8 10-4 Hz at 360°C Propagation of SCC Fracture surface examination. Fracture surface of PWSCC on weld metal 182 appeared intergranular / interdendritic. The crack front was uneven and a strong macro-branching at 30-45° was observed for the TL-orientation (Figure 7), while the crack front was most regular and the crack propagated roughly in the plane of 559
the fatigue pre-crack for the TS-orientation (the direction of the axis of the dendrites), Figure 8.
Figure 7. SCC at 325°C : fracture surface in the TL orientation (specimen TL9, D1054 AW, 41.4 MPam, R = 0.7)
Re-assessment of previous results : da/dt versus K. Previous CGR data obtained by EDF, CEA and ETH-Zürich [5] with a static loading were reassessed on weld metal D545, in the TL orientation :
x
different loading modes have been applied (constant load (CT) or constant deflection (WOL or DCB)).
Consequently, the initial K values were re-calculated taking into account the anisothermal stress relaxation between 20°C and 325°C for constant deflection tests, roughly 18%.
Figure 8. SCC at 325°C : fracture surface in the TS orientation (specimen 1471-TS1, D1054 AW, 22.9 MPam, R = 0.7) x
CGRs measured between 310°C and 330°C were considered and re-calculated at 325°C using an activation energy of 130 kJ/mol. This could be a reason for the typical behaviour of the 3 CEA results within a narrow range of K values (2 values at 330°C and one value at 310°C).
The mean curve for the maximum values of CGR of weld D545 as a function of the initial value of K became :
(da/d)max = 0.5114.(K-9)0.42 using K values ranging between 18 and 41 MPam (Figure 9).
This K-dependence was not so far from the law reported in the case of alloy 600, with the exponent between 0.3 and 0.5, see [6].
Significant data are required to better define the curve at low K values.
D545 & D1054 - AW - TL - static 0,01 0,10 1,00 10,00 0
10 20 30 40 50 60 K (MPa.m0.5)
CGRmax325 (E-10 m/s ETH D545 AW TL EDF D545 AW TL CEA D545 AW TL CGRmax325 D545 AW TL EDF D1054 AW TL D545 : CGRmax325 = 0,5114(K-9)^0,42 Figure 9. Mean curve of the max. CGRs as a function of K on alloy 182 (weld D545) in the TL orientation at 325°C The new results obtained in the TL orientation with weld D1054 were in close agreement with these data (Figure 9) and demonstrated a good reproducibility for tests performed at the same K-value. With the available data, the proposed law for PWSCC of 182 was : (da/d)max = D(material).(K-9)0.4.
Influence of the orientation. Though true crack lengths have been considered in the case of macro-branching (TL) or straight propagation in the direction of the axis of dendrites (TS), the present results demonstrated that the orientation induced significant changes in CGRs. The CGRs measured in the TS orientation were generally higher than in the TL orientation : 2 times for D545 with a static loading, 2.5 to 3 times for D1054 with a trapezoidal loading at R = 0.7.
Influence of a trapezoidal loading (R = 0.7). The influence of a trapezoidal loading on the CGRs was examined on both welds in the TL and TS orientations.
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On weld D545, the data from Westinghouse [7] obtained with a trapezoidal loading (R = 0.7) were compared to the above-mentioned reference curve for a static loading, in the TL orientation. It could be concluded that no significant influence of the loading procedure was observed in the TL orientation, while the CGRs obtained with a trapezoidal loading in the TS orientation were 5 to 7 times higher than the reference (TL) curve in static loading (Figure 10).
D545, Static / dynamic 0,01 0,10 1,00 10,00 0
10 20 30 40 K (M Pa.m0.5)
CGRmax325 (E-10 m/s)
West A W TS R = 0.7 West A W TL R = 0.7 CGRmax325 AW TL s tatic CGRmax325 = 0,5114(K-9) ^0,42 Figure 10. CGRs on weld D545 : comparison between static and trapezoidal loadings On weld D1054, the CGRs were also very similar in static and in trapezoidal loading in the TL orientation, slightly higher than for weld D545 (Figure 11). By contrast, CGRs measured under a trapezoidal loading with the TS orientation were 3 to 5 times higher than those deduced from the reference (TL) curve.
Unfortunately, the data for the TS orientation with a pure static loading was not yet available, but it could be expected from the available CGRs on the two (similar) welds that data with a trapezoidal loading from [7] and from the present paper in the TS orientation, would be in good agreement (those from [7]
were the highest). Finally, it seemed that the influence of trapezoidal versus static loading on the SCC CGRs of alloy 182 depended on the orientation : no significant influence in the TL orientation, but a detrimental factor 2 to 7 could be observed with the TS orientation.
0,01 0,1 1
10 0
10 20 30 40 50 60 K (MPa.m0.5)
CGRmax325 (E-10 m/s)
D545 AW TL static D1054 AW TS R 0,7 D1054 AW TL R 0,7 D1054 AW TL static D545-TL D1054-TL D 1054-TS Figure 11. CGRs on weld D1054 : comparison between static and trapezoidal loadings Influence of the stress relief treatment. The CGRs obtained at 325°C with welds D545 under a static loading and D1054 under a trapezoidal loading in the stress-relief condition (610°C-20 h) were 2 times lower than the CGRs measured in the as-welded condition (at the limit of the scatterband for reproducibility but always in the lowest part).
Discussion Some comparisons could be realized with available data in relation to the influence of some major parameters on PWSCC of alloy 182.
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Comparison of da/dt versus K curves between laboratories The K-dependence of CGRs was investigated by several laboratories. The Figure 12 compares the da/dt versus K curves proposed by EPRI and the preliminary reference curve proposed in this paper. It should be remind that EPRI-MRP 115 curve, with assumed KISCC = 0, was obtained as the best fit for a set of international average values from different welds, at 75%
of the cumulative distribution ((da/dt)ave325 = 1.5 10-12.K1.6), with static or trapezoidal loadings. By contrast, the proposed reference curve in this paper has assumed a KISCC value of 9 MPam, and the proposed law ((da/d)max = 0.5114.(K-9)0.42 for welds D545 or D1054) for a pure static loading was rather similar to the law proposed for alloy 600 [6].
0,01 0,1 1
10 0
10 20 30 40 50 60 K (MPa.m0.5)
CGRmax325 (E-10 m/s)
D545 EDF AW TL static D1054 AW TS R 0,7 D1054 AW TL R 0,7 D1054 AW TL static EPRI MRP 115 132 JNES AW TS static Studsvik lab data [8]
Ringhals field data [8]
Ringhals curve TS EDF on D545-TL CGRmax325 = 0,5114(K-9)0,42 D1054-TL D 1054-TS R 0,7 EPRI MRP 115 CGRave325 = 1,5 10-12 K1,6 Rhingals curve :
K < 25 : CGRmax325 = 7,22 10-23 K9,3 K > 25 : CGRmax325 = 6 10-10 Figure 12. Reference curves for weld metal 182 by EPRI, Ringhals and EDF from laboratory. Comparison with JNES results The Ringhals curve in the TS orientation presented a part with a dependence on K9.3 at K lower than 25 MPam, and a plateau regime at 6 10-10 m/s at K values higher than 25.1 MPam, which was consistent with EDF values on weld metal D1054 in the same (TS) orientation and with a trapezoidal loading. The results they obtained in laboratory under a static loading and from the field [8] were in close agreement with the curve suggested by EDF.
Trapezoidal loading versus static loading It should be noted that the data generated in this paper on weld D1054 in the TS orientation with a trapezoidal loading were slightly higher than the EPRI-curve which should account for this kind of loading. The differences in the shape and the level of EPRI and EDF curves could be the consequence of the differences in the loading procedures. It should be noted that Tsutsumi et al [9] did not recommend the use of a trapezoidal loading to measure CGRs on weld metal 132, unless hold times higher than 105 s would be used or unless pre-cracking of the specimen at the beginning of the test.
This kind of conclusion was still brought on alloy 600 in primary water : no change in CGRs was observed on very susceptible heats, while a significant increase of CGRs under a trapezoidal loading with respect to a static loading could be noted for heats with a low susceptibility to SCC [10]. Finally, it was not possible to explain the reason why no similar influence was observed for weld metal 182 in the TL orientation while a significant increase could be noted with a trapezoidal loading in the most sensitive (TS) orientation.
JNES data obtained in the TS orientation at 325°C (calculated from 340°C) under a pure static loading ranged between EPRI and EDF curves, they referred to a law similar to (K-9)1.16, Figure 12, [11].
Influence of the chemical composition of the weld In this paper, two weld metals from the same batch of electrodes and deposited in similar processes by two different manufacturers have provided very similar data, as expected.
However, the scatter on CGR results appeared to be somewhat larger on weld D545 than on weld D1054. This difference could come from laboratory-to-laboratory test procedures, since weld D545 has been tested by 3 different laboratories and weld D1054 by EDF only. On weld D545, the scatter was mainly observed within the K-range of 15-25 MPam, in which the influence of K on CGRs was significant, while EDF has investigated a broader range of K (20-42 MPam) on weld D1054, for which the influence of K was the lowest.
Besides, some CGRs measured at 330°C by CEA on 3 other welds in alloy 182 with C contents ranging from 0.022% to 0.089%, and Si contents from 0.27% to 0.79% were found to be somewhat similar : calculated values of the CGRmax at 325°C were 1.4 to 1.5 10-10 m/s for high or low C low Si weld, 1.8 to 562
2.35 10-10 m/s for the high C high Si weld, and 0.75 to 4.5 10-10 m/s on weld D545 [5].
Finally, weld to weld variability led to a factor 3 on the CGRs for the same TL orientation.
Influence of the stress relief-treatment CGRs measured on weld metal D545 or D1054 in the SR conditions were generally 2 to 3.5 times lower than in the AW conditions in most of the laboratories (EDF, CEA, ETH-Zürich) at 320-330°C, just above the limit for significance according to the reproducibility factor of 2 for this kind of tests. This slight beneficial effect of SR treatment at 610°C could not be explained by any significant change in the microstructure or density of dislocations [12] but could rely on some contribution of residual stresses to the true K level in the case of the AW condition. It should be noted that a significant beneficial effect of SR was noted by [13] at 290°C (factor 3 to 10 in the TL orientation).
For comparison, some significant beneficial influence of the SR treatment was observed on the resistance to the initiation of SCC in the case of highly susceptible materials (high C, high Si), the effect was limited in the case of materials with the lowest susceptibility to SCC [1].
Finally, the root causes of the major beneficial influence of SR treatment in plants rely partly on the reduction in the residual stresses which could reach 50% of the initial stresses and, in the case of initiation, on a possible recristallization of the surface cold worked layer. The intrinsic influence of SR treatment on the initiation of SCC is low on specimens with low C and Si.
Conclusion The initiation and growth of PWSCC of alloy 182 were investigated with regard to the influence of the loading parameters.
The stress threshold for initiation of SCC at 360°C was found close to 350 MPa in constant load tests. With the limited available data, it seemed that a ripple loading did not modify this value. The strain threshold was determined by interrupted SSRTs : SCC occurred for an elongation between 1.25 and 1.5%.
Preliminary data of crack growth rates (CGR) at 325°C provided a dependence on (K-9)0.4 for the average values of the CGRmax.
The strongly oriented microstructure led to faster (x 2 to 3)
CGRs in the direction of the dendrites (TS) than in the perpendicular direction (TL). The influence on the CGRs of a trapezoidal loading (R = 0.7, 2.8 10-4 Hz) with regard to a pure static loading depended on the orientation : no significant modification in the direction perpendicular to the dendrites (TL),
but some significant increase (x 2 to 7) could be observed in the direction of the dendrites (TS). A stress relief treatment (610°C) could lower the CGRs by a factor 2 to 3.5 with respect to the as-welded condition. The chemical composition of the weld metal could lead to some variability in the CGRs (factor 3).
Work is still in progress to assess the influence of temperature and chemical composition of the weld on the stress threshold for the initiation of SCC. For propagation, the influence of low values of K (less than 20 MPam) on the da/dt versus K curve, temperature, stress relief treatment and chemical composition of the weld metal will be investigated.
References 1
C. Amzallag et al, Stress Corrosion Life Assessment of 182 and 82 Welds used in PWR Components (10th International Conference on Environmental Degradation in Nuclear Power Systems - Water Reactors, South Lake Tahoe (NV), august 2001) 2 C. Amzallag et al, Stress Corrosion Life Experience of 182 and 82 welds in French PWRs (Contribution of Materials Investigation to the Resolution of Problems Encountered on Pressurized Water Reactors, Fontevraud V, France, September 2002) 3 Francois Vaillant, Chedly Braham, Jean-Marie Gras,
<< Etude de la corrosion sous contrainte en milieu primaire des alliages X-750 et X-750 modifié 19% de chrome laide de lessai de traction lente. Influence du traitement thermique >>,
(EDF report HT-45/PV D 736A), january 1990)
[4] << La corrosion sous contrainte des alliages de nickel dans leau haute température >>, F. Vaillant et al Editors, Reference book, (EDF report HT-29/04/077/A, 2005)
- 5.
S. Le Hong et al, Measurements of Stress Corrosion Cracking Growth Rates in Weld Alloys 182 in Primary Water of PWR (10th International Conference of Environmental Degradation of Materials in Nuclear Power Systems - Water Reactors, South Lake Tahoe (NV), august 2001) 6 F. VAILLANT et al, Crack Growth Rates in Thick Materials of Alloy 600 and Weld Metals of Alloy 182 in Laboratory Primary Water. Comparison with Field Experience (Contribution of Materials Investigation to the Resolution of Problems Encountered on Pressurized Water
- Reactors, Fontevraud V, France, September 2002, pp 107-116) 7.
John Hickling, << Materials Reliability Program. Crack Growth Rates for Evaluating Primary Water Stress Corrosion Cracking (PWSCC) of Alloy 82, 182 and 132 welds (MRP-115) (EPRI report 1006696, November 2004) 8 A. Jenssen et al, A Swedish Perspective on PWSCC of Alloy 182 (2005 International PWSCC of Alloy 600 Conference and Exhibit Show, Hyatt Regency Tamaya Resort, Santa Ana Pueblo (NM), 7-10 March 2005) 9 K. Tsutsumi et al, SCC Growth Rate of Nickel based Alloy 132 Weld Metal in PWR Primary Water (11th International Conference on Environmental Degradation in Nuclear Power Systems - Water Reactors, Stevenson (WA), august 2003)
- 10. F. Vaillant et al, Influence of a Cyclic Loading on Crack Growth Rates of Alloy 600 in Primary Environment : An Overview (11th International Conference of Environmental Degradation of Materials in Nuclear Power Systems - Water Reactors, Stevenson (WA), august 2003) 11 Y. Yamamoto et al (JNES), Outline of Evaluation Technology for SCC Growth of Ni Base Alloys (NiSCC)
Project in Japan and Current Results in PWR Environment 563
(2005 International PWSCC of Alloy 600 Conference and Exhibit Show, Hyatt Regency Tamaya Resort, Santa Ana Pueblo (NM), 7-10 March 2005) 12 C. Cayron et al, << Etude par microscopie électronique en transmission de la microstructure de différentes nuances dalliages déposés 182 >> (Technical report CEA DTEN N° 127/2001) 13 Ruth Magdowski, Markus O. Speidel, << Stress Corrosion Crack Growth of Various Materials Exposed to Simulated PWR Water>> (Technical report ETH-Zürich, contract ND 3367-RE, april 1997) 564
Session Name: Ni-Based Alloys - I, II Session Day/Time: Thursday 8/18, 8am - noon Influence of a Cyclic Loading on the Initiation and Propagation of PWSCC in Weld Metal 182 Presenter: Thierry Couvant Name of Person Asking Question: John Hickling Affiliation of Person Asking Question: EPRI Question: You mentioned the extensive macrobranching in the T-L samples. Did you find any difference in the extent of this crack branching between specimens under static constant load and those exposed with periodic unloading?
Response: We didnt notice any difference. Additional examinations could be performed to precise this point.
Name of Person Asking Question: Jun Peng Affiliation of Person Asking Question: Babcock & Wilcox Company Question: Whereby do you check the effects of a spike in cyclic loading on da/dt (Crack Growth Rate)?
Response: No we dont.
565