ML20147B573
| ML20147B573 | |
| Person / Time | |
|---|---|
| Site: | Point Beach, 05000000 |
| Issue date: | 06/10/1975 |
| From: | Farmelo D, Lowry L, Perrin J Battelle Memorial Institute, COLUMBUS LABORATORIES |
| To: | |
| Shared Package | |
| ML20147B514 | List: |
| References | |
| FOIA-88-45 NUDOCS 8803020125 | |
| Download: ML20147B573 (99) | |
Text
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FINAL REPORT l
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1 POINT BEACH NUCLEAR PLANT UNIT NO. 2 i
PRESSURE VESSEL SURVEILLANCE PROGUd4:
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EVALUATION OF CAPSULE V j
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WISCONSIN ELIC7RIC POWER COMPANY j
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June 10, 1975 i
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J. S. Perrin, D. R. Famelo, L. M. Lowry f
j R. O. Wooton, and R. S. Denning l
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BATTELLE I
i Columbus Laboratories t
1 505 King Avenue j
Columbus, Ohio 43201 i
8803020125 880226 I
CONNOR ee-45 PDR 4
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TABLE OF CONTENTS i
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.Page
SUMMARY
........................... 1 INTROC UC TION........................ 2 CAPSULE RECOVERY AND DISASSD4BLY,
5 S AMPLE PREPARATION.......
8 Pre ssure Vess el Material................ 8 t
Correlation Monitor Material.............. 8 EXPERIMENTAL PROCEDURES.......
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Dosimeter and Thermal Monitor Examination....... 9 Tensile Properties......
........11 Charpy Impact Properties...
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RESULTS AND DISCUSSION...
17 Dosimeter and Thernal Monitor Examination......
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j Tensile Prcperties......
........27 Charpy Impact Properties....
........37 CONCLUSIONS...........
......... $6 i
REFERENCES......................... $7 1
APPENDIX A i
PRESSURE VISSEL MATIRIAL....
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APPEKDIX B
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4 ASIM CORRELATION MONITOR MATERIAL.
......... B - 1.
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.I APPENDIX C DOSIMETER COUNTING DATA...
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APPENDIX D i
DOSIMETER AND CAPSULE EXAMINATION.
........D-1 APPENDIX E i
INSIRUMDITII) Cit \\RPY PROPERTIIS,.
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i APPENDIX F a
WOL FRACTURE TOUCHNESS PROPERTIES.
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POINT BEACH NUCLEM PIANT UNIT NO. 2 PRESSURE VESSEL SURVEILIANCE PROGRAM:
EVALUATION OF CAPSULE V e
by J. S. Perrin, D. R. Farmelo, L. M. Lowry, R. O. Wooton, and R. S. Denning s
SUMMARY
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The irradiation conditions and the irradiation induced changes in
' mechanical properties of the Point Beach Unit No. 2 reactor pressure vessel
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have been determined from evaluation of specimens contained in Capsule V.
j This capsule contained base metal, weld metal, and heat-affected-zone metal i
specimens. The capsule was removed af ter 1.52 equivalent full-power years of operation. The irradiation temperature did not exceed 590 F, and the
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capsule received a fluence of 4.74 x 10 nyt (>l MeV).
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The measured changes in the 30 f t-1b and 50 f t-lb Charpy Lapact transition temperature for the three reactor materials were consistent with j
those observed for other programs involving similar materials and irradiation conditions. Of particular interest is the upper shelf energy level drop l
from a preirradiatten value of approximately 65 f t-lb to an irradiated value l
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of 42 f t-lb.
A trend band for the change in the 30 f t-lb and 50 f t-lb
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transition temperature with increasing exposure to fast neutrons was determined from the results of this program and those of other programs. The tensile specimen examination showed that, in general, the yield and uitbnate tensile strengths of the materials examined increased and that the reduction in area and the total elongation decreased.
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i INTRODUCTION r
This report presents the results of the examination of Capsule V, the first capsule of the continuing surveillance progras for monitoring the effects of neutron irradiation on the A508 Grade B Point Beach Unit No. 2 reactor pressure-vessel material under actual operating conditions.
This report contains experimental procedures, results, and discussion relating to the investigation.
Radiation damage studies initiated during the early days of l
nuclear power-reactor development revealed the deleterious effects of high energy neutrons upon the notch ductility of reactor vessel steels. The effect was characterized by a rapid rise in the transition temperature with increasing neutron exposure.
In addition, the tensile properties show a significant increase in yield strength and tensile strength, accompanied by a
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a loss of uniform elongation and reduction of area with increasing neutron j
exposure.
Sufficient data on the effects of radiation on the mechanical 1
properties of reactor pressure-vessel steel are now available to indicate t
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the type and relative magnitude of property changes to be encountered during the expected lifetitae of the reactor structure. This information is an integral part of the design basis for a nuclear reactor. During the reactor l
life the operating limitation curves (i.e., pressure and temperature) will be periodically adjusted to incorporate the projected changes in mechanical properties.
j To further ensure the continued safe operations of the plant, a reactor-vessel radiation-surveillance program is being conducted. The I
primary purpose of this program is to evaluate the specific changes in the j
mechanical properties of the pressure-vessel materials under the actual service conditions (neutron fluence, time, and temperature) of the reactor
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plant. It is known that the magnitude and relationships of the property changes are functions of the specific material composition and metallurgical 1
2 condition; the amount, rate, and energy spectrum of the radiation; and d
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O the exposure temperature The surveillance program is designed to provide information for determining whether the reactor pressure-vessel operating limitations are indeed conservative, as is expected, i
The surveillance program for the reactor was designed and recom:nended by the Westinghouse Electric Corporation and is based on AS1H E 185, "Surveillance Tests on Structural Mat erials in Nuclear Reactors"( ).
The details of this program and the preirradiation mechanical properties of the materials are presented in Reference (9). Prior to start-i up, six capsules containing tensile, Charpy V-notch, and WOL fracture-mechanics specimens of the pressure-vessel materials were installed in the a
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reactor.
The capsules were located between the thermal shield and the 4
vessel wall. In addition to these mechanical-property test specimens, the
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capsules contain thermal-monitor and neutron-fluence specimens for evaluation of the specific temperature and radiation exposure conditions of the specimens.
1 The particular exposure condition variables evaluated are the total integrated fast fluence of the capsule and the maximum tenperature encountered by the specimens during the exposure period.
The temperature history of the surveillance capsule is f airly representative of that encountered by the l
pressure-vessel wall. However, the capsule is a finite distance from the reactor pressure-vessel wall, and therefore the capsule receives an accelerated fluence as compared to the vessel wall.
The most essential mechanical properties evaluated by the test spect= ens in the surveillance capsule are the ductile-to-brittle fracture 1
transition temperature av d the conventional tensile-strength and ductility values. In this contex,, essential refers to those requirements of the l
current methods for establishing pressure-temperature operating limitations of the reactor pressure vessel. An essential requirement of the mechanical t
j property acasurements is that they be made on representative material.
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- References at end of text.
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i For this surveillance program, the capsules contain test specimens of the A508 Class 2 reactor-vessel steel from two 6-1/2 in, thick shell l
plates f rom the vessel intermediate and lower shell courses, and also representative weld metal and heat-affected sone (HAZ) metal. The thermal t
l history of the material used to f abricate test specimens is as identical l
as possible to that received by the reactor pressure vessel during 2
f abr!.e s tion.
The surveillance capsule being examined contained not only I
charpy specimens machined from pressure vessel metal used in the reactor l
under examination, but also ASIM correlation monitor Charpy specimens, j
These specimens are in numerous commercial power reactor surveillance capsules. By comparing the results of the correlation monitor specimens from numerous surveillance programs, further knowledge should be gained concerning the effect of dif fering nuclear irradiation conditions (neutron spectrum and flux intensity) on the radiation response of reference correlation monitor steels.(5) l q
The main text of the report contains the results of the thermal monitor and neutron dosimeter examination, the Charpy impact specimen j
j examination, and the tensile specimen examination. The WOL specimen exami-
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nation is presented in an appendix to the report.
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CAPSULE RECOVERY AND DISASSEMBLY I
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Batte11e's Columbus Laboratories (BCL) personnel vent to the Point 4
Beach Nuclear Plant Unit No. 2 to pick up the surveillance capsule assembly.
l They brought a pool-side jib crane, a specialized underwater cutting tool, and a shipping cask. The cutting head of the underwater cutting tool is a mild steel casting. The head had been sand blasted, copper plated, and then nickel plated to prevent it f rom rusting and thereby contaminating the pool water. To further avoid contamination, pool water was used in the line leading f rom the nump intensifier unit to the cutting head.
The capsule asselmbly had an overall length of approximately 130 inches.
Point Beach personnel removed the capsule assembly from the pressure vessel and 1
transferred it underwater in a canal to the spent fuel pool.
The upper lid and lower drain lid were removed from the shipping cask. Using an overhead crane, j
the cask was then raised f rom the receiving area, moved to a position over the spent fuel pool, and lowered into the pool so that the bottom end of the cask was resting on the floor of the pool.
The Point Beach handling tool attached to the bridge crane was then used to position the square capsule, with the attached
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round lead tube, at the bottom of the shipping cask. Westinghouse drawing i
number 686J468 showed the internal eask cavity to be approximately 95 inches deep and the upper lid depth to be 8 inches.
L The cutting tool was lowered into the pool using a stainless steel l
cable attached to the pool-side jib crane. The cutter was guided into position using the stainless steel pipe line leading to the cutting head. The capsule j
was raised about 35 inches and binoculars were used to determine the position l
of the cutting head. The first sectioning cut was then made. After 1
cutting, it was determined that the capsule had been cut on the square a
i capsule section. A second cut was made separating the lead tube. into two
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sections. These two sections were placed into the cask along side the i
lower capsule section.
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The cask was raised from the pool and its exterior was. thoroughly rinsed with water. The water inside the cask was allowed to drain into the pool. The overhead crane was then used to lower the cask to the decontamination area. The cask was decontaminated to the level of removable i
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contamination required for shipping, 2200 disintegrations /100 cm / min Sy and l
220 disintegrations /100 cm / min c.
The cask was then shipped to the BCL
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Hot Laboratory Facility by commercial carrier.
1 Upon arrival at BCL, the cask was placed in a hot cell. The threc 4
capsule and lead tube sections were then removed from the cask. The capsule j
sections were examined and measurements indicated the first cut had been made j
at about 54 in, from the capsule bottom in the region of a WOL specimen.
l Visual examination showed the capsule to be a dark gray color with the identification mark "V" stamped on the lower end of the capsule.
i The specimens were removed from the capsule and inventoried.
The appearance of the specimens was a dark gray color and it was found that one i
i WOL had been severed during the reactor site cutting operation. The specimen inventory is shown in Table 1, which is in agreement with WCAP 7712('}.
1 Before testing, the mechanical property specimens were cleaned in the 4
following manner:
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- 1. Prevashed in a solution of Radiac and water i
- 2. Ultrasonically cleaned for a minimam of 45 minutes a
l in a solution of detergent and water
- 3. Removed from ultrasonic bath, rinsed with clean water, and then rinsed with reagent grade alcohol.
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l EXPERDIENTAL PROCEDURES I
j This section describes the procedures employed in the testing of
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the impact and tensile specimens. Also included are the procedures used to 1
j examine the dosimeters and thermal monitors. All experimental examinations j
j and evaluations were conducted at satte11e's Columbus Laboratories, j
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i Dosimeter and Thermal Monitor Examination The capsule contained two kinds of low melting-point eutectic
. alloy thernal monitor wires for determination ot' the maximum temperature l
attained by the test specimens during irradiation. One alloy was 2.5%
i As-97.5% Pb with a melting point of 579 F.
The other alloy was 1.75% As-j 0.75% Sn-97.5% Pb with a melting point of 590 F.
These thermal monitor alloys
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were sealed in Pyrex tubes and inserted in spacers in the capsule. During capsule disassembly the thermal monitor wires were removed from the spacers j
and Pyrex tubes. The wires were then visually examined for evidence of f
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melting at a magnification of 4X using a stereomicroscope.
l The capsule contained a total of 22 dosimeters of copper, nickel, f
l cadmium-shielded aluminum. cobalt alloy, unshielded alminum-cobalt alloy, j
neptunium 237 and uranium 238 in three locations. Included are the iron I
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dosimeters, obtained from actual Charpy or tensile test specimens. The i
reactions used for the dosimetry calculations were as follows:
54, g,,p) %,
Iron 7
58 1
Nickel g
) 58,
c 1
63 Copper Cu (n,n) 60Co i
'Co (n,y)
Oco l
238U (n,f) I Cs f
Urani a Nep tuniu:s Np (n,f)
Cs f
Y e
All 22 Josimeter samples were analyzed. The composition of the impurities of the medium surrounding the dosimeter monitor specimens was not stated in i
Reference (9) and is not known.
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4 Af ter removal from the capsule, the individual samples were placed in vials for transfer to the radiochemistry laboratory. Radiation readings at 1 meter and on contact were recorded. The nickel, copper, and cobalt wires were decontaminated by wiping with dilute acid, distilled water, and O
I reagent grade acetone. The iron samples and U and Np capsules were 1
4 wiped with dilute acid and distilled water to remove major contmaination and then cleaned ultrasonically in a solution of Radiac and water.
The copper, nickel, and Al-0.15 Co wires were weighed to *0.0001 g, 4
and the activation product intensities were determined directly by gauna ray spectrometry. For the iron samples drillings were taken through a complete i
cross section near the center of the designated Charpy impact or tensile t
specimen. The drillings were then weighed and mounted on a standard counting ring and ganuma counted.
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3 0 and Np capsules were opened in an alpha radiation contain-ment box by specially prepared tools used to grip the small 1/4 in, diameter x 3/8 in. long cylinders and cut off the tops. The tool used for cutting off j
237 the tops was a modified tubing cutter. The U and Np were present in
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the form of oxide powders. The two samples were poured into small tared I
J primary containment vials and then into clean cared secondary vials for t
weighing to *0.0001 g on an analytical balance. They were dissolved in 85 HNO3 (U 0 ) and @ gSO -0.1M NaBr03 (Np0 ), and diluted to appropriate 38 4
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137 volumes.
Cs analyses were performed in duplicate by pipeting 1 a1 aliquots into plastic vials and counting with a high resolution, lithium drif ted germanium detector. NBS Cs standards in identical form were utilized to obtain the appropriate disintegration rates. Utilizing this 137 method a Cs separation is not necessary since it is resolved from I34 Cs i
and other fission product activities.
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i The remaining activation products were analyzed by gansa-ray i
t spectrometry utilizing a 3 in, diameter x 3 in. long Na1 (71) scintillation I
i crystal detector and model 401D 400 channel analyzer (Technical Measurements Corp) capable of 7 percent resolution FWH (full width half maximura) at the 0.663 MeV Cs-
"Ba gamena ray energy level. The g
Co, and Cs 54 60 13I samples were counted directly against NBS standards. The Co activity was I
obtained frc:a comparison with theoretical efficiency curves prepared from 1
NBS standards.
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11 The procedures used in the evaluation of the dosimetry samples followed the appropriate ASIM recorrnendations(
Tensile Properties The design of the tensile specimens is shown in Figure 1.
The gage section has a nominal 0.250 in, diameter and a nominal 1.000 in. length.
Tensile properties were detemined using a Model IT-D Instron machine. The machine has a 20,000 lb capacity. During tests a crosshead speed of 0.05 in.
per min was used. An elastic strain gage tensile bar built at Battelle.
Columbus and cattbrated against NBS proving rings was used to calibrate the loading system of the Instron over a 0 to 10,000 lb range. The gripping devices used to grip the ends of the tensile specimen are pin-type units made at Battelle-Columbus.
The defomation of the specimen was measured using a Baldwin Series 200 high temperature extensometer. An Instron Model G51-12A strain gage unit is part of the extensometer. The strain gage unit i
senses the differential movenent of two extensometer extension ams attached to the specimen gage length 1 in, apart.
The extension ams are required for j
themal protection of the strain gage unit during the elevated temperature tests. Figure 2 shows the extensometer extension ams and strain gage assenbly used for tensile testing. A tensile specimen is shown at the top of the figure next to the region of the extension ams where '.he specimen is loaded for testing.
The strain gage unit is shown at the bottom of the figure next co the region of the extessometer ams where the unit is attached during testing. The extensonner was calibrated before testing using an Instron Extensometer Calibrator.
The load and elongation were recorded on the recorder unit which is an integral part of the Instron machine. Curves were run in a load-elongation mode until the vicinity of maximum load. The curves were then finished in a load-time mode so that a complete curve would be generated in case of extensometer slippage after the specimen started to neck down locally.
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i P4973 FIGURE 2 EXTENSOMETE ETENSION ARMS AND SIEAIN CAGE ASSDiBLY USED FOR TENSILE TESTING l
14 Elevated temperature tensile tests were conducted using a three-zone split furnace. The irradiated tensile specimens were tested at room temperature, 300 F, and 550 F.
The specimens were held at tempera-ture before testing to stabilize the temperature. Temperature was monitored using a Chromel-Alumel thermocouple in direct contact with the gage section of the specimen.
The load-extension data were recorded on the testing machine strip chart. The yield strength, ultimate tensile strength, and total elongation were determined from these charts. The reduction in area was determined from specimen measurements made using a vernier caliper. The yield strength was determined by drawing a line parallel to the elastic region of the stress-strain curve. The line was drawn offset to the curve at a distance of 0.2% strain.
Charpy Impact Properties The Charpy impact tests were conducted using a 240 f t-lb Satec-Baldwin Model SI-1C impact machine in accordance with ASIM E23-72(1 )
Standard specimens of the desiga shown in Figure 3 were used. The 240 ft-lb range was used for all tests. The velocity of the hammer at impact was 17.0 ft/sec. The impact machine was checked and calibrated by a represen-tative of the manufacturer. The calibration of the machine was then verified specified in ASIH E23-72 using Charpy impact specimens purchased from the at U.S. Army Materials Research Agency.
The results, listed in Table 2, confirmed the machine was calibrated.
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l TABLE 2.
CALIBRATION DATA FOR THE BCL HOT LABORATORY CHARPY IMPACT MACHINE Average Standarp,)
BCL Energy,
- Energy, Variation Croup ft-lb f t-lb Actual Allowed Low Energy 13.3 13.3 0 f t-lb
- 1.0 f t-lb Medium Energy 49.0 50.7
- 3.4%
- 5.0%
High Energy 74.7 77.3
- 3.4%
5.0%
(a) Established by U.S. Army Materials and Mechanics Research Center.
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CHARPY V-NOTCH DiPACT SPECIMEN i
16 The impact machine was inspected each day during use to determine the energy loss due to friction. -nis was done by the following: (a) releasing the pendulum from the 240 f t-lb upright position with no specimen in the machine and determining the indicated energy value is O f t-lb; (b) without resetting the pointer, again releasing the pendulum from the 240 f t-lb upright position and permitting it to swing 11 half cycles. After the pendulum starts its lith cycle, the pointer is moved to between 12 and 24 f t-lbs and it is determined that the indicated value, divided by 11, does not exceed 0.4. percent (9.6 f t-lb) of the 240 f t-lb capacity.
ASE procedures for specimen temperature control were utilized.
The low temperature bath consisted of agitated methyl alcohol cooled with additions of liquid nitrogen. The container was a Dewar flask which contained a grid to keep the specimens at least 1 in, from the bottom.
The height of the bath was enough to keep a minimum of 1 in, of liquid over the specimens. The Charpy specimens were held at temperature for a minimum of at least the ASE recommended time.
The tests above room temperature were conducted in a similar manner except that a metal container with a liquid bath was used. The bath used for temperatures from 70 to 212 F was water, and the bath used for temperatures above 212 F was oil.
The baths were heated to temperature using a hot plate.
The specimens were manually transferred from the temperature bath to the anvil of the impact machine by means of tongs that had also been brought to temperature in the bath.
The specimens were removed from the bath and impacted in less than 5 sec.
ne energy required to break the specimens was recorded and plotted as a function of test temperature as the tes ting proceeded.
Lrteral expansion was determined from measurements made with a lateral expansion gage. Fracture appearance was estimated from observation of the fracture surf ace, and comparing the appearance of the specimen to an ASni f racture appearance chart (1 )
17 RESULTS AND DISCUSSION Dosimeter and Thermal Monitor Examination The capsule contained three 579 F and two 590 F thermal monitors.
The 579 F monitors were located in the top, middle, and bottom regions of the capsule. One 590 F monitor, referred to as the top-middle monitor, was located between the top and middle regions of the capsule. The other 590 F monitor, referred to as the bottom-middle monitor, was located between the bottom and middle regions of the capsule.
Monitors were examined at a magnification of 4X using a stereo-microscope.
The middle 579 F monitor showed no evidence of melting. This monitor had a cross section which was approximately rectangular. The four i
f aces were flat, and the edges were sharp and well defined.
The top 579 F monitor had three faces along the length.
Two were flat, but the third was melted as though some melting may have occurred. Figure 4A shows the two relatively flat surfaces. The bottom 579 F monitor showed obvious melting along the complete length. There were areas along the length which were rounded, and were smooth and shiny. Figure 4B shows the monitor. It was both shorter and larger in diameter as compated to the other two 579 F monitors. The cross section along cost of the length of the top-middle 590 F monitor appears to be rectangular with flat surfaces and sharp edges.
However, at one end there appears to have been a slight amount of melting, which may have occurred when the Pyrex tube was sealed. This monitor was definitely not at or above 590 F along the length bec~ use there is no a
evidence of general melting.
The bottom-middle 590 F monitor appears to have at least partially melted, since there is rounding along one edge of the complete length.
In addition, one end shows some evidence of melting.
1 This monitor is shown in Figure 40.
The slight curve along the complete
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1ength is a result of the monitor being bent slightly on removal from the Fyrex capsule.
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FIGURE 4a.
TOP 579 F THERMAL MONITOR "a
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s FIGURE 4b.
BOTTOM 579 F MONITOR i
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FIGURE 4c.
BOITOM-MIDDLE 590 F MONITOR I
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19 The results of the themal monitor examination indicate some melting of 579 F monitors occurred including general melting of one 579 F monitor. However, there was no general melting of the 590 F monitors.
Therefore the surveillance capsule appears to have been below 590 F during irradiation.
The surveillance capsule was in the reactor for 556 equivalent full power days or 1.52 equivalent full power years, based on a full power output of 1518 Mv(t).I The positions in the reactor of capsule V and the other surveillance progra:n capsules shown in Figure 5.
Capsule V had an exposure lead factor with respect to the inner surface at the pressure vessel wall of 2.5.( 0)
All 12 f ast neutron monitors and 10 themal neutron monitors were counted for gamma ray activity to detemine integrated fast fluence and themal fluence, respectively. The f ast flux monitors are iron, nickel, copper, uranium and neptuniu:, and the results are shown in Table 3.
Fast 18 fluence values (E > 1 MeV) for Ni, Fe, and Cu were 3.80 x 10, 4.74 x 10 8
and 4.76 x 10 n/cm, respectively. Neptuniu:n and uranium values were 1
7.79 x 10 and 8.24 x 1018,jc,2, respectively. Because the iron samples are from actual Charpy or tensile test specimens and the nuclear constants 0
are well established, the average iron fast fluence (E > 1 MeV) of 4.74 x 10 n/cm is considered most represent ative of the five monitors. The copper monitor confirms this value. Nickel dosimetry results are not reliable for long term irradiations due to its relatively short half-life of 71.3 days (Co
).
The Np-237 and U-238 monitors resulted in values 60-70 percent higher than the Fe results. '1hese values tend to run higher than average and it is believed due to uncertainty in cross sections and threshold values in the relatively new procedures. The Np-237 procedure is presently undergoing evaluation by ASIM.
The Point Beach Unit No. 2 Technical Specification indicates that 6
18 0.891 x 10 Mw(t)-days of operation is equivale e to 1.9 x 10 nje, (31 g,y),(21)
Based on the capsule exposura lead factor of 2.5, the fluence of 4.74 x 1018
(>l MeV) for iron dosimete-s is equivalent to a maximum pressure vessel nyt 18 wall exposure of 1.90 x 10 nyt (> 1 MeV). The surveillance capsule was 6
removed af ter 0.844 x 10 Mw(t)-days of operation. The predicted fluence of the surveillance capsule based on the Technical Specification information is therefore only 5 percent greater than the measured fluence.
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I FIGURE 5.
CAPSULE LOCATIONS IN REACTOR Capsule V is at 77*.
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21 TABLE 3.
FAST NEU' IRON DOSIMETRY RESULTS (E>l MeV)
Location Fast Neutron Dosimeter in Capsule Fluence, n/cra Fe Top 4.83 x 10 Fe Mid-Top 4.59 x 1018 Fe Middle 4.46 x 10 Fe Mid-Bottom 18 5.17 x 10 Fe Bottom 4.62 x 10 10 Avg 4.74 x 10 Cu Top 4.76 x 10 8 Cu' Mid-Top 4.48 x 10 Cu Mid-Bottom 4.88 x 10 Cu Bottom 8
_4.94 x 10 10 Avg 4.76 x 10 Ni Middle 3.80 x 10 U
Middle 18 8.24 x 10 Np Middle 18 7.79 x 10 1
22 The thermal neutron fluences for the bare and cadmium covered cobalt dosimeters are shown in Table 4 The true themal fluence was equal to S.60 x 10 n/cm, calculated from nyt
=C true bare
- R R (cadmium ratio) = C l Cd covered = 2.16.
bare Basic counting data from fast and thermal monitors is shown in Appendix C.
Constants used in the calculations are summarized in Table 5 where the effective cross sections, c ' 8re f Prime importance. The neutron flux R
and reaction cross section are defined in terms of the "f ast flux" or neutron flux above 1.0 MeV as
.f c(E)N(E)dE l [ c(E)N(E)dE = I
=Ic (l) f gR
[
N(E)dE where
.0 MeV i = neugron flux at full reactor power, n/cm /sec f=i[
N(E)dE = flux abcve 1.0 MeV i
1.0 MeV U = average reaction cross section above 1.0 MeV R
c(E) = reaction cross section, em, at energy E.
Calculations have been performed to determine the reaction cross sections, a, and the activation correction f actors, C, for five dosimeters placed in R
the reactor. The ANISN computer program was used to calculate the neutron energy spectrum at the dosimeter positions and to perform the integrations indicated in Equation (1). The dosimeter activation at the time of removal from the reactor is then A=nl cg R where t
A = disintegrations /cm'/see n = dosimeter nuclei concentrations, 2 toms /cm.
23-TABLE 4 Ti1ERRAL ICEUTRON DOSDIETRY RESULTS Location l
Dosimeter in Capsule Fluence, n/cm 8
C Top 11.8 x 10 Bare Mid-Top 10.6 x 10 Middle 8.55 x 10 Mid-Bottom 10.4 x 10 Bottom
_10.6 x 10 Avg.
10'.4 x 10 18 Co Top 5.28 x 10 cadmium Covered Mid-Top 4.96 x 10 18 Middle 4.38 x 10 8
Mid-Bottom 4.96 x 10 10 Bottom 4.55 x 10 Avg 4.82 x 10 18 Average True Thernal 5.60 x 10 (1) These values show observed values not corrected for resonance energies.
(2) Corrected by factor @-lyR where R = C Bare! C admium " 2
- 10
- i l
i
- -,. - - - l
24 TABLE 5.
VALUES USED IN DOSIMETRY CALCULATIONS I)
Target o
Threshold Fission Product I Isotope R
Energy Yield Half-Reaction Target
% Abundance barns MeV Life Cu(n,c)60Co 1007. Cu 69.17 0.000608' 5
5.26y Ni(n.p)58Co 100% Ni 67.77 0.105 1.0 71.3d F e(n,p) Mn 96.9% Iron 5.82 0.0785 1.5 314d U(n,f)1 7Cs U0
>99.9 0.345 0.8 6.2 30.0y 33 Np(n,f)1 Cs Np0
>99.9 2.66 0.4 6.0 30.0y 2
59Co(n,Y)60Co Al-0.157. Co 100 37.1 5.26y t
(1) For fast reactions, o is f r neutr ns >l MeV at capsule location.
R L
l
25
- AT)) e-A(T - t))
J C=
E F (1 - e
= activation correction f actor, j=1 th t = the elapsed time at the end of the j time interval, see J = number of time intervals F = fractional power level during a time interval T 3
3 1
A = dosimeter decay constant, see T = length of time the dosimeter is in the reactor, sec.
Figure 6 is a comparison of the ANISN-calculated neutron spectrum with the fission spectrum. It is seen that the ANISN spectrum contains f ar fewer high-energy neutrons than the fission spectrum. At the dosimeter location the ratio of the fast flux above 1.0 MeV to the total flux DF
- = 0.0426 C
This causes the ANISN-calculated values of C I *** " * #
R than the fission-spectrum-averaged cross sections. The activation correction f actors were calculated for Point Beach Unit No. 2 operation through October 31, 1974 The power history was taken from Reference (22). The 0
decay for the Np and U dosimeters was calculated for the fission product Cs-137.
Appendix D contains a letter from Westinghouse to Wisconsin Electric containing dosimeter and capsule information. This information includes dosimeter material purities, capsule location in the reactor, and capsule exposure lead factor.
l l
26 l.0 i
i i
i i i i; i
i l
l i i i, 0.8
~
0.6 0.4 E
FISSION SPECTRUlf l
~
'g 0.2 x
G v*
ANISN SPECTRUM 0.1 g
g, 0.08 m
i-y 0.06 e
di C
0.04 8
=
i 0.02 0.01 I
I
~
II
'1 I
I I
I I I I 0.1 0.2 0.4 0.6 03 1.0 2.0 4.0 6.0 80 to Neutron Energy, MeV FICURE 6.
COMPARISON OF THE NEU7RON FISSION SPEC 7RLM WITH THE ANISN-CALCULATED SPECTRLH AT THE DOSIMETER LOCATION FOR POINT BEACH UNIT No. 2
27 Tensile Properties The irradiated tensile properties are listed in Table 6A for the base and weld metal. The table lists temperature, 0.2 percent offset yield strength, ultimate tensile strength, fracture stress, fracture strength, uniform elongation, total elongation, and reduction in area. The unirradiated tensile properties from Reference (9) are listed in Table 6B for comparison.
Posttest photographs at 4X of the tensile specimens are shown in Figures 7 through 9.
These photographs show the necked down region of the gage length and the fracture. A typical tensile curve showing stress as a function of strain is shown in Figure 10; the particular test shown is for base metal specimen V1 tested at 550 F.
Tensile tests for the irradiated metals were run at room temperature, 300, and 550 F.
The results are shown compared to the unirradiated properties from Reference (9) in Figures 11, 12, and 13, which are plots of ulttmate tensile strength, 0.2 percent offset yield strength, reduction in area, and total elongation. The yield strengths and ultimate tensile strengths increased af ter irradiation for all three metals at the three temperatures except for the two base metals at 300 F.
The reduction in area after irradiation was the same or slightly less than before irradiation for the two base metals, but decreased appreciably af ter irradiation for the weld metal. The total elongation af ter irradiation for the base metal 122W195VA1 decreased slightly at 88 and 550 F, but was unchanged at 300 F.
The total elongation after irradiation for the base metal plate 123V500VA1 and the weld metal decreased at all three test temperatures, with the weld metal showing the greater decreases.
l
TABLE 6A.
POINT BEAC11 UNIT NO. 2 IRRADIATED TENSILE PROPERTIES 0.27.
Offset Ultimate Yield Tensile Fracture Fracture Uniform Total Reduction Temp.,
- Strength, Strength,
- Strength, Stress, Elongation, Elongation, in Area, Material Specimen F
psi psi psi psi 7.
7.
7.
Base E2 88 75,300 97,400 60,410 189,740 9.2 21.5 68.1 (122W195VA1)
Base E3 300 66,400 89,200 56,620 180,520 8.6 20.4 68.6 (122W195VA1)
Base El 550 74,900 100,200 64,290 199,370 8.3 19.6 67.8 g
(122W195VA1)
Base V2 88 67,700 91,200 54,990 191,490 10.5 23.2 71.3 (123V500VA1)
Base V3 300 57,400 80,700 51,120 172,410 10.1 22.3 70.3 (123V500VA1)
Base V1 550 74,100 96,800 61,220 192,310 9.1 20.9 68.1 (123v500VA1)
Wald W2 88 88,600 105,800 78,820 176,710 11.2 21.0 53.4 Wald W3 300 80,200 97,100 77,100 123,200 9.7 17.6 37.4 Wald W1 550 81,200 99,700 82,820 148,900 7.3 16.3 44.4
29 TABLE 6B.
PREIRRADIATION TENSILE PROPERTIES FOR THE POINT BEACH UNIT NO. 2 REACTOR PRESS VESSEL SHELL FORGINGS AND WELD HETAL 0.2%
Ultimate Shell Test Yield Tensile Uniform Total Reduction Forging Temp.
Strength Strength Elong.
Elong.
In Area Material (F)
(psi)
(psi)
(%)
(%)
(%)
123V500VA1 Room 57,050 82,100 17.2 32.0 72.7 Room 53,800 78,400 18.1 31.9 72.3 300 63,450 84,500 13.3 25.5 73.4 300 55,500 78,400 15.1 25.5 68.0 600 44,500 77,300 14.4 27.9 72.3 600 49,700 78,950 16.5 28.5 71.1 122W195VA1 Room 71,100 92,500 14.1 27.5 70.5 Room 70,500 91,450 13.9 26.6 70.5 300 71,500 92,150 10.4 21.6 72.3 300 64,500 85,550 11.0 22.2 69.6 600 64,350 90,650 13.9 27.2 72.3 600 61,600 86,800 14.2 28.1 71.9 Weld Metal Room 71,300 86,150 16.4 27.2 64.1 Room 72,500 87,800 15.9 27.0 64.1 300 66,800 82,000 11.4 22.8 63.1 300 64,600 79,550 13.9 24.0 64.1 600 63,750 85,750 13.7 21.9
- 54. 6 600 62,500 84,000 15.6 23.9 54.6 (a) This tensile data is from Reference (9).
FIGURE 7a.
TENSILE SPIR,IMm E2 TESTED AT 88 F M 7 % sy y,,
sf6lll
- "b
&g-b eum 1
FIGURE 7b.
TENSILE SPECDim E3 TESTED AT 300 F l
1 FIGURE 7c.
TENSILE SPECIMEN El TESTED AT 550 F S
w---
a-
l
.Xrg 1
Wh FIGURE 8a.
TENSILE SPIEIME V2 TESTED AT 88 F 4
' Y&re FIGURE 8b.
T5SILE SPECIMD V3 TESTED AT 300 F FIGURE 8c.
TBSILE SPECIMD1 V1 TESTED AT 550 F
l FIGURE 9a.
TENSILE SPECIMEN
,,'1 TESTED AT 88 F
~
FIGURE 9b.
TENSILE SPEIMEN W3 TESTED AT 300 F l
FIGURE 9c.
TENSILE SPEIMDi W1 TESTED AT 550 F
~. -. - - - - - - - - - - -
-- ~- -
1 34 A
100,000 a
4 b
Ultimate Tensile Strength I
'R 80,000 t
c%
e J
Yi'Id SIa9thi O_
ce$
60,000 -
o,OL nicrodioted',
U A,0- tirodioted l l
I I
I I
I 40,000 80 i
D k
i Reductim in Areal 60'-
wiM 40 E i otal Etongollen.
O 20 b,0-Unisradioted A,e-triodioied i I
I I
I I
i 0
0 10 0 200 300 400 500 600 TEMPERATURE,F.
FIGURE 11, COMPARISON OF LTNIRRADIATED AND IPJtADIATED TENSILE PROPHtTIES FOR POINT BEACH UNIT NO. 2 BASE METAL PLATE 122W195VA1
35 100,000 k
UNimote Tensile Strength 6
- l 80,000 A-g g-i
-g.
Yield Strength o M
60,000 o'
6 6,Olunirredtofw O
40,000, A,9-trrylotW l O
I I
I I
i i
l I
l l
h A
O
=
3 A
Reducl% in Arso 60
$l Uj40 Si e
Tolol Elongotion.
C C
to 6,O-Unitrodioles.
A,0- trrodioted -l l
0 i
I I
I I
O 10 0 200 300 400 500 600 TEMPERATURE, F.
FIGUEE 12 CCt4PARISON OF UNIRRADIATED AND IRRADIATED TENSILE PROPERTIES FOR POINT BEACH U'11T 110. 2 BASE HETAL PLATE 123V500 val
+
i i.
-..,e.
36 120,000 i
i i
i i
i Ultimale Tensile StrengthL 100,000
- m b
A y 80,000 3
H Yield Stre th-O-
60,000 6,O-Unitrodisted A,9-Irrodisted i I
I I
I 40,000 80 d
60 Reduction in Areo-H:
40 -
m.
CL :
E Tolol Elongotion n
g O
i o
20 6,0-Unlirodioted A,$-Irrodioted l
I 0
O 100 200 300 400 500 600 TEMPERATURE,F FIGURE 13, COMPARISON OF UNIRRADIATED AND IRRADIATED TDSILE PROPERTIES FOR POINT BEACH UNIT NO 2 WELD METAL
37 Charpy Impact Properties The impact properties determined.as a function of temperature are listed in Tables 7 through 11.
In addition to the impact energy values, the tables also list the measured values of lateral expansion and the estimated fracture appearance for each specimen. The lateral expansion is a measure of the deformation produced by the striking edge of the impact machine harmner when it impacts the specimen; it is the change in specimen thickness of the section directly adjacent to the notch I
j location. The fracture appearance is a visual estimate of the enount of shear or ductile type of fracture appearing on the specimen fracture surface.
The impact data listed in Tables 7 through 11 are graphically shown in Figures 14 through 18. These figures show the change in impact properties as a function of temperature. The data for the irradiated curves was determined in the present program, and the unirradiated curves are from
'l WCAP 7712(9)
Of particular interest are the temperatures corresponding i
j to the impact energies of 30 and 50 f t-lb.
The energy level of the upper shelf is also of interest.
The curves for the five irradiated metals are well defined with j
little data scatter with only one exception. The exception is the curve for i
the irradiated HAZ metal.
The reason for this is that is is difficult to t
cut specimens out of a heat affected zone in a plate between base metal and weld metal., and be assured that the HAZ specimens 'all have the identical microstructure and thermal history.
The unirradiated impact data for the HAZ metal also showed substantial data scatter.
l l
I t
t i
)
1 1
i i
)
i l
i
38 TABLE 7.
CHARPY V-NOICH IMPACT TEST RESULTS FOR BASE METAL PLATE 122W195VA1 (E SDtIES)
Test Impact Lateral Fracture Temperzture,
- Energy, Expansion, Appearance, SpecLmen F
ft-lb mils Percent Shear E1
-80 3.0 8.0 5
E3
-80 7.5 11.5 2
E8
-45 25.5 25.5 10 E2 0
58.5 46.0 30 E4 0
10.5 18.0 5
E9 0
55.0 47.0 25 E7 74 86.0 66.5 100 Ell 76 76.5 67.0 55 E5 145 141.5 98.5 100 E6 145 133.0 90.0 100 E12 200 136.5 89.5 100 E10 290 135.0 88.0 100 TABLE 8.
CHARPY V-NOICH IMPACT TEST RESULTS FOR BASE METAL PLATE 123V500VA1 (V SERIES)
Test Impact Lateral Fracture Temperature,
- Energy, Expansion, Appearance, Specimen F
ft-lb mils Percent Shear V10
-80 3.5 11.0 0
V3
-80 2.0 6.5 0
V6
-45 50.5 48.0 15 VI
-45 22.0 29.5 5
t V2 0
90.0 80.0 50 Vil 0
94.5 90.5 50 V12 74 114.5 89.5 65 V7 76 108.5 75.5 65 V5 145 186.5 87.5 100 V4 200 216.0 72.5 100 V9 290 165.0 78.5 100 V8 345 198.5 75.5 100 1
i 39 TABLE 9.
CHARPY V-NOTCH IMPACT TEST RESULTS i
FOR WELD HETAL
=
Test Impact Lateral Fracture Temperature,
- Energy, Expansion, Appearance, Specimen F
f t-lb mils Percent Shear W6 76 13.5 15.5 7
W3 145 22.5 26.5 35 WS 145 27.0 31.5 40 i
a W8 200 43.0 46.8 90 I
W1 290 41.5 48.0 100 W7 310 41.0 45.5 100 W2 345 41.5 52.5 100 W4 345 43.5 47.0 100 i
I i
TABLE 10. CHARPY V-NOTCH IMPACT TEST RESULTS FOR I
HEAT AFFECTED ZONE HETAL I
i t
Test Impact Lateral Fracture Temperature,
- Energy, Exp ans ion, Appearance, i
Specimen F
ft-lb mils Percent Shear
\\
H2 0
10.5 14.0 2
H5 0
27.0 31.0 15 118 0
15.0 15.5 2
H1 76 115.0 82.0 90 j
H6 76 152.0 67.5 100 H4 145 177.0 91.5 100 H7 200 102.5 75.5 60 1
H3 290 195.0 91.0 100 I
+
i 1
I d
i i
2
i 40 TABLE 11. CHARPY V-NOICH IMPACT TEST RESULTS FOR AS'Di CORRELATION MONITOR METAL Test Impact Lateral Fracture Temperature,
- Energy, Exp ansion, Appear ance,
Specimen F
ft-lb mils Percent Shear R7 76 9.5 13.5 10 R2 80 7.0 11.0 10 R4 145 39.0 43.5 25 RS 145 31.0 35.5 30 R6 200 55.0 54.5 50 R8 290 81.5 75.5 90 R1 345 96.5 83.5 100 R3 345 90.5 88.0 100 t
i
i 41 160 O, / - -
140-Q
=== Unitradiated
/p
\\J
/
O Irradiated
/
/
120 -
7
/
/
/
100 -
/
e
/
l O
A 80 -
[
e o
o 5
i I
60 -
/
/
/
40 -
j
/
6 i
20 -
/
/
O O
i i
i
-100 0
100 200 300 Tc.p e r a. t u r e, F
j i
FIGL3E IL, CRUtPY D' PACT 0:ERGY VD. SUS TOlPD.ATURE FOR POU;T 3FACH U:4IT 2:0. 2 3.2SE >!ETAL (122il143VA1) i
42 250
===== Unit rad ia ted
@ Irradiated O
200 -
o O
t'
~
I
~s O
y 150 -
/
/
.a
/
0
/
100 -
/
l e
/
/
/
/O 50 -
f II
/
O
/
/
0
-150 100 0
100 200 300 400 Temperature, F FIGURE 15. CHARPY IMPACT DIDICY VERSUS TDiPIRATURE FOR POIllT BEACH UNIT NO, 2 BASE METAL (123V500VA1) l l
i
i j
\\
43 80
. Unitradiated O Irradiated 60 -
p'
/
l a
7
/
=
/
/
A 6
40 -
f
/
/
w
/
/
/
20 -
/
/
/
/
0 i
i i
i
-100 0
100 200 300 400 Temnerature, F FIGURE 16 CHARPY DiPACT ENERGY VERSUS TEMPERAR*RE FOR POINT BEACH UllIT NO. 2 WELD METAL l
9 F
e
44 20e o
aan==== Unitradiated
- O--
Irradiated 150-O 0
1 e
g 100-O E
ta
, = = " " " " " " " "
a#
ew***
/
/
- 50-p i
/
/
/
O p
O O
O I
i i
-100 0
100 200 300 1
Temperature, F FIGURE 17.
CHARPY IMPACT ENERGY VIRSUS TDiPDtAnrRE FOR POINT BEACH l
UNIT NO. 2 HAE METAL i
l 45 150 125 -
p#"~~
====== Un ir r a d ia t ed j # es*
Q Irradiated 100 -
f l
O p
A
/
75 -
9
/
/
E
/
50 -
/
/
/
o
/
O
,/
23 -
/
,,s' 0~
8 3
-50 o
200 300 350 Te=perature, 7 FIGURE 18. CHARPY DiPACT ENEGY VERSUS TDiPGARTRE FOR POINT BEACH UNIT NO. 2 ASDf CORRELATION MONIIOR METAL I
I
46 Figures 19 through 23 show the fracture surfaces of the Charpy specimens. Figure 19, as an example, shows how the fracture surface changes as the test temperature is increased for base metal specimens.
The -80 F specimen (E1) shows an almost flat fracture surf ace, with only 5 percent shear fracture appearance.
This specimen absorbed 8.0 f t-lb of energy during the impact test, a typically low value for the low temperature, brittle region of the Charpy curve. As can be seen in the figure, the amount of lateral expansion is small, and was measured as being only 8.0 mils. As the test temperature is increased, specimens show an increasing amount-of shear fracture appearance. The +290 F specimen (E10) fracture surf ace is typical of the type seen at the higher temperature end of the Charpy transition curve. The fracture surface shows large shear lips with a 100%
shear fracture appearance. The specimen absorbed the relatively large amount of 135.0 f t-lb during impact.
The substantial amount of plastic deformation occurring during this test is reflected in the large value of 88.0 mils lateral expansion.
Table 12 summarizes the unirradiated and irradiated 30 and 50 f t-lb transition temperatures and the upper shelf energy levels for the five metals.
Table 13 lists the 30 f t-lb and 50 f t-lb transition temperature shif ts due to irradiation. The 30 and 50 f t-lb transition temperatures are difficult to determine for the HAZ metal due to the scatter in the data.
The ASTH correlation monitor metal shows a 30 f t-lb shif t of 90 F 4
and a 50 f t-lb shif t of 110 f t-lb.
Irradiation has caused the upper shelf energy to drop from 125 to 95 f t-lb.
For the four reactor vessel metals, the irradiated 30 f t-lb transition temperature ranges from -50 F (base) to 165 F (veld). The HAZ value is a
dif ficult to define due to data scatter, but is below the 165 F weld metal value. The largest shif t due to irradiation is an increase from 0 F to 165 F, a total of 165 F, for the veld metal. The irradiated 50 ft-lb transition temperature ranges from -25 F (base) to an undefined value for the weld metal due to an upper shelf below 50 f t-lb.
The 50 f t-1b HAZ value is difficult to define due to data scatter, but the most conservative curve through the data yields a value below 100 F.
1 l
i
)
i
i l
El E3 E8 E2 E4 E9 I ;;
E w 155 W ? !!iB 4
E7 E11 ES E6 E12 E10 4
l FIGURE 19. C'MRPY DiPACT SPIIIMEN FRACIURE SURFACES FOR POINT BEACH UNIT NO. 2 BASE HETAL PLATE 122W195VA1 V10 V3 V6 V1 V2 Vil 4
l
<(
s
- 2
- + 1915 *iG var 6
i V12 V7 VS V4 V9 V8 1
FIGURE 20. CHARPY IMPACT SPECIMEN FRACTURE SURFACES FOR POINT BEACH UNIT NO. 2 BASE HETAL PIATE 123V500VA1
l i
i
,1
.l l
1 l
W6 W3 W5 W8 1
^
b.
H59e 1
l W1 W7 W2 W4 FIGURE 21, CHARPY MPACT SPECmm FRACTURE SURFACES FOR 1
POINT BEACH UNIT NO, 2 WELD METAL J
l I
H2 H5 H8 H1
.r r
T f
c; a
l
- r..
I
{
1 1
l H6 H4 H7 H3 l
i l
FIGURE 22. CHARPY EPACT SPECmm FRACIURE SURFACES FOR i
POINT BEAC}i UNIT NO. 2 HAZ METAL l
I l
R7 R2 R4 R$
1
^
i
^
J i
l R6 R8 R1 R3 1
1 FIGURE 23. CHARPY IMPACT SPECD4EN FRACTURE SL7 FACES FOR POINT BEACH UNIT No. 2 ASIM CORRELATION l
MONITOR METAL 1
4 t
i 1
I l
50 1
i r
TABLE 12. CHARPY IMPACT PROPERTIES FOR POINT BEACH UNIT NO. 2 I
Transition Temperature. F Upper Shelf, Material Condition 30 f t-lb 50 ft-lb ft-lb Base (122W195VA1)
Unirradiated
-55
-15 145 Base (122W195VA1)
Irradiated
-35 0
135 Base (123V500VA1)
Unirradiated
-80
-60 180 Base (123V500VA1)
Irradiated
-50
-25 190
' Weld Unitradiated 0
60 65 Weld Irradiated 165 42 HAZ Unitradiated (a)
(a)
(a)
HAZ Irradiated (a)
(a)
(a)
ASIM Correlation Unirradiated 45 80 125 ASTM Correlation Irradiated 135 190 95 3,
(a) See text for discussion of HAZ metal.
f j
TABLE 13. COMPARISON OF POINT BEACH ENIT NO. 2
)
30 FT-LB and 50 FT-LB TRANSITION j
TEMPD.ATURE SHIFTS 1
30 f t-lb Transition 50 ft-lb Transition j
Temperature Shift, Temperature Shift, t
Material F
F t
Base (122W195VA1) 20 15 i
Base (123V500VA1) 30 35 Weld 165 HAZ (a)
(a) -
ASTM Correlation 90 110 (a) See text for discussion of HAZ netal.
I 4
4 i
I
9 51 i
One base metal upper shelf dropped from 145 to 135 ft-lb, a change of 10 f t-lb.
The other base metal upper shelf shows an increase from 180 to 190 f t-lb; this apparent increase is probably due to data scatter because upper shelf energy levels normally decrease due to d
irradiation. The weld metal upper shelf dropped from 65 to 42 f t-lb, a change of 23 f t-lb.
The upper shelf change for - the HAZ metal is difficult to determine due to the large amounc of data scatter.
The significant drop in upper shelf energy level for the weld metal from 65 f t-lb to the relatively low value of 42 f t-lb represents a decrease of 23 f t-lb or 35 percent.
Drops of this magnitude have been associated with high residual element levels (
}
The chemical compositions of the base metal and weld metal used for the surveillance capsule specimens is presented in Appendix A of this report. The weld metal copper content is quite high, having a value of 0.25 weight percent. It is this relatively high copper level which is most probably causing the low irradiated upper shelf level of the weld metal.
1 The transition temperature shif ts for the three reactor vessel metals are shown plotted in Figures 24 and 25 as a function of fluence. The
]
two figures are the 30 and 50 f t-lb transition temperature shif t values obtained in the present surveillance program and in other surveillance programs for A302B and A508 pressure vessel steels (24-31)
HAZ values frees t
the present program are not included. Weld metal values from the present progra:s are shown only in Figure 24, since only the 30 f t-lb value is j
defined. The values used to form the trend band are those from programs where i
the irradiation temperature was between 550 and 590 F.
The apparent large scatter in data among the various programs is not unusual. Note that the weld metal values generally determine the upper bound of the trend band, f
t j
It can be seen that the transition temperature shif t values for the base metals of the present program fall within the upper and lower bounds l
determined by metals of the other programs. The weld metal 30 f t-lb value j
for the present program in Figure 24 f alls above the trend band.
s j
i l
I l
l
52 l
I i
il i iiIl l
l I
i 1 l l1l Bose Weld HAZ Point Beach No.1 Q
onnecucut Yankee O
9 300 Big Rock Point V
V V
Yankee Surveillance 6
Yankee Special O
Humbolt Boy C)
Son Onofre
<l 4
4 y
Point Beach No.2 O-E g,
Elk River X
i200 u
E
.a V
x g
6 z
10 0 O
e 4
V y
x D
Trend Bond For 550-590 F
\\x D
x 0
--- I \\
I I II11 I
I i
i i iill 18 i9 10
!0 1020 Neutron Fluence, nyt FIGURE 24 COMPARISON OF 30 FT-LB TRANSITION TDIPEARTE VALUES FROM VARIOUS SURVEILLANCE PROGRAMS FOR A302 CRADE B AND A508 FRESSURE VESSIl STEELS
53 i
i i
i il l
i ii6 ij Base Weld HAZ Point Beach No.1 Q
4 Connecticut Yankaa O
e 9
300 H. 8. R0binson D
Point Beach No. 2 0
u.
~
w 8
E E
U 3200 Ee c.e
. 3 85
+
E I
O#
n 10 0 e
o t
to q
o G
0 O
OO D D
I
' ' ' ' 'I i
0 10 20 10 10'8 10 Neutron Fluence nyt i
r FIGURE 25.
COMPARISON OF 50 FT-LB TRANSITION TDiPERATURE VALUES FRQi VARIOUS SURVEILLANCE PROGRAMS FOR A302 GRAD B AND A508 PRESSURE VESSEL STEELS l
I a
h i
54 The 30 f t-lb transition temperature value for the ASDi correlation monitor material is shown in Figure 26 Also shown in this figure are the 30 f t-lb transition temperature values obtained from other programs using ASTM correlation monitor A302 and A533 pressure vessel steels. The 30 f t-lb transition temperature value determined in the present progra:n for ASTM A533 correlation monitor material is consistent with other values shown.
i i
i i iiiij i
i i
iiiiij Q - Point Beach No.1 o
Connecticut Yankee V - Big Rock Point 300 O - Yankee
< - San Onofre A - Point Beach No.2
',200 55 s,
.a C
$5 z K)0 o
O o
Trend Band for 550-590 F 7
V 0
f I
I IIIll i
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i i l t il 1018 lgl9 1020 Neutron Fluence,nyt FIGURE 26.
COMPARISON OF 30 FT-LB VALUES FROM VARIOUS SURVEILLANCE PROGRAMS FOR ASTM CORRELATION-MONITOR STEELS
f 56 CONCLUSIONS The maximum irradiation temperature of the irradiation surveillance capsule did not exceed 590 F.
The neutron fluence experienced by the capsule was 4.74 x 10 nyt (>l MeV) which was attained af ter 1.52 equivalent full-power years of operation. Based on a capsule lead factor of 2.5, this is equivalent to a maximum fluence of 1.90 x 10 nyt (>l HeV) for the pressure i
vessel af ter 1.52 equivalent full power years. For a pressure vessel life of 40 years operation at an 80 percent load factor (32 equivalent full power years), the maximum fluence experienced by the pressure vessel would therefore i
be predicted to be 4.00 x 10 nyt (>l MeV).
Tensile tests were conducted at 88, 300, and 550 F on base and weld metal. In general, the yield strength and ultimate tensile strength of these metals increased due to irradiation, and the corresponding ductilities (reduction in area and total elongation) decreased.
The Charpy impact behavior was determined for base, weld, and HAZ metal. The lowest upper shelf observed was for the weld metal, which decreased fro:n 65 to 42 f t-lb due to irradiation. The highest 30 f t-lb irradiated transition temperature observed was the 165 F value for the weld metal.
l 4
i i
4 1
4
57 REFERENCES (1) Reuther, T. C., and Zwilsky, K. M., "The Effects of Neutron Irradiation -
on the Toughness and Ductility of Steels", in Procandinen of Toward Tenroved Duetilftv and Touehnama Svenomium, published by Iron and Steel Institute of Japan (October,1971), pp 289-319.
(2)
Steele, L. E.,
"Major Factors Affecting Neutron Irradiation Embrittle-ment of Pressure-Vessel Steels and Weldments", NRL Report 7176 (October 30, 1970).
(3)
Berggren, R. C., "Critical Factors in the Interpretation of Radiation Effects on the Mechanical Properties of Structural Metals", Welding Research Council Bulletin, A2, 1 (1963).
(4) Witt, F.
J., "Heavy-Section Steel Technology Program Semiannual Progress Report for Period Ending February 29, 1972", ORNL Report No. 4816 (Octobe r, 1972).
(5) Hawthorne, J. R., "Radiation Effects Information Generated on the ASTM Reference Correlation-Monitor Steels", American Society for Testing and Materials Data Series Publication DS54 (1974).
(6) Steele, L. E., and Serpan, C. Z., "Neutron Embrittlement of Pressure Vessel Steels - A Brief Review", Analysisof Reactor Vessel Radiation gffects Surveillance Programs, American Society for Testing and Materials Special Technical Publication 481 (1969), pp 47-102 (7)
Integrity of Reactor Vessels for Light-Water Power Reactors Report by the USAEC Advisory Committee on Reactor Safeguards (January,1974),
(8) ASTM Designation E185-66, "Surveillance Tests on Structural Materials in Nuclear Reactors", Book of ASTM Standards, Part 31 (1967), pp 638-642 (9) Yanichko, S. E., and Zula, C. C., "Wisconsin Michigan Power Co. and the Wisconsin Electric Power Co. Point Beach Unit No. 2 Reactor Vessel Radiation Surveillance Program", WCAP 7712 (June,1971).
(10) ASTM Designation E320-69T, "Radiochemical Determination of Cesium-137 in Nuclear Fuel Solutions", Book ofASTM Standards, Part 30 (1970),
pp 1004-1009.
(11) ASTM Designation E261-70, "Measuring Neutron Flux by Radioactivation Techniques", Book of ASTM Standards, Part 30 (1970), pp 762-772.
(12) ASTM Designation E262-70, "Measuring Thermal-Neutron Flux by Radio-actication Techniques", Book of ASTM Standards, Part 30 (1970), pp 773-780.
(13) ASTM Designation E263-70, "Measuring Fast-Neutron Flux by Radioactivation of Iron", Book of ASTM Standards, Part 30 (1970), pp 781-783.
58 (14) ASTM Designation E264-70, "Measuring Fast-Neutrein Flux by Radioactivation of Nickel", Book of ASTM Standards, Part 30 (1970), pp 787-791.
(15) ASTM Designation E343-67T, "Fast-Neutron Flux by Activation of Molybdenum-99 Activity from Uranium-238 Fission", Book of AS1H Standards, Part 30 (1970),
pp 1078-1084 (16) ASTM Designation E393-69T, "Measuring Fast-Neutron Flux for Analysis for Barium-140 Produced by Uranium-238 Fission", Book of ASTM Standards, Part 30 (1970), pp 1174-1180.
(17) ASTM Designation E23, "Notched Bar Impact Tt: sting of Metallic Materials",
Book of ASTM Standards, Part 10 (1974), pp 167-183.
(18) ASTM Designation A370-71, "Mechanical Test'.ng of Steel Products", Book of ASIM Standards, Part 10 (1974), pp 1-52 (19)
Private coemunication from D. Dill of Wis':onsin Electric to J. S. Petrin of BCL (June 13, 1975).
(20)
Private coccunication frce D. Dill of Wisconsin Electric to J. S. Perrin of BCL (May 14, 1975).
(21)
Private co:cunication from D. Dill of Wisconsin Electric to J. S. Perrin of BCL (June 10, 1975).
(22)
Private comunication from J. Each of Wisconsin Electric to J. S. Perrin of BCL (December 6,1974).
(23)
Bush, S. H., "Structural Materials fe,r Nuclear Power Plants". ASTM Gillette Memorial Lecture (1974),
(24)
Serpan, C. Z., Jr., and Watson, H. L., "Mechanical Property and Neutron Spectral Analyses of. tte Big Rock Paint Reactor Pressure Vessel",
Nucl. Eng. Design, 11, 393-415 (1970).
(25)
Serpan, C. Z., Jr., and Hawthorne, J. R., "Yankee Reactor Pressure-Vessel Surveillance: Notch Ductility Performance of Vessel Steel and Maximum Service Fluence Determined from Exposure During Cores II, III, and IV", NRL Report 6616 (Septembar 29, 1967).
(26)
Brandt, F. A., "Humboldt Bay Pove:r Plant Unit No. 3 Reactor Vessel Steel 1
Surveillance Prograd', GECR-5492 (May,1967).
)
(27)
"Analysis of First Surveillance Material Capsule from San Onofre Unit I", Southern California Edison Company (July, 1971).
(28)
Perrin, J. S., Sheckherd, J. W., and Scotti, V. G., "Examination and Evaluation of Capsule F for theConnecticut Yankee Reactor Pressure-Vessel Surveillance Prograd', Final Report to Connecticut Yankee Atomic Power Company (March 30, 1972).
59 (29)
Perrin, J. S., Sheckhard, J. W., Farmelo, D. R., and Lowry, L. M.,
"Point Beach Nuclear Plant Unit No.1 Pressure Vessel Surveillance Program:
Evaluation of Capsule V", Final Report to Wisconsin Electric Power Company (June 15, 1973),
(30)
Ireland, D. R., and Norris, E.
B., "Influence of Neutron Irradiation on the Properties of Steels and Weld Typical of theERR Pressure Vessel Af ter Two Power Years Operation", SvRI-1228-P-9-15 (March,1968).
(31)
Sterne, R.
H., Jr., and Steele, L. E., "Steels for Commercial Nuclear Power Reactor Pressure Vessels", Nucl. Eng. Design, la, 259-307 (1969).
G e
I l
l 1
l l
i APPENDIX A PRF9SURE VESSET MATER T At_.
i
.i I
r i
l i
1 I
i
i APPEND 1X A POINT FACli LNtt NO. 2 PRESStTRE VESSET MATERTAT.(#
For theReactor Vessel Surveillance Program, Combustion Engineering, Inc., supplied Westinghouse sections of A508 Class 2 forgings used in the core region of the Point Beach Unit No. 2 reactor pressure vessel.
The sections of material were removed from the 6-1/2 inch-thick intermediate and lower shell rings (forgings No. 123V500VA1 and 122W195VA1, respectively) of the pressure vessel.
In addition, a weldment made from sections of the two forgings, using veld wire representative of that used in the original fabrication, was also supplied by Combustion tagineering Inc.
The forgings were produced by the Bethlehem Steel Corp. The chemical analysis and heat treatment history of the vessel materia *. follows:
A.1 Chemical Analyses (Percent)
Torging
, Forging Weld Element 123V500VA1 122W195VA1 Matal C
0.20 0.22 0.079 Mn 0.65 0.59 1.40 P
0.009 0.010 0.014 S
0.009 0.008 0.013 Si 0.24 0.23 0.55 Mo 0.59 0.60 0.39 Ni 0.71 0.70 0.59 Cr 0.35 0.33 0.07 V
0.010 0.010
<0.002 Cu 0.088 0.051 0.25 Co 0.004 0.010 0.013 Al
<0.005
<0.005
<0.005 N2 0.004 0.002 0.010 (a)
This Appendix is from Yanichka, S. E., and Zula, G. C., "Wisconsin Michigan Power Co and the Wisconsin Electric Power Co. Point Beach Unit No. 2 Reactor Vessel Radiation Surveillance Prograd', WCAP 7712 (June, 1971).
A-2 A.2 Heat Treatment Intermediate Shell Heated at 1550 F for 9 1/2 hours, water quenched Heat 123V500VA1 Tempered at 1200 F for 12 hours1.388889e-4 days <br />0.00333 hours <br />1.984127e-5 weeks <br />4.566e-6 months <br />, air cooled Stress-relieved at 1125 F for 12 hours1.388889e-4 days <br />0.00333 hours <br />1.984127e-5 weeks <br />4.566e-6 months <br />, furnace cooled Lower Shell Heated at 1550 F for 8 hours9.259259e-5 days <br />0.00222 hours <br />1.322751e-5 weeks <br />3.044e-6 months <br />, water quenched Heat 122W195VA1 Te:pered at 1200 F for 12 hours1.388889e-4 days <br />0.00333 hours <br />1.984127e-5 weeks <br />4.566e-6 months <br />, air cooled Stress-relieved at 1125 F for 12 hours1.388889e-4 days <br />0.00333 hours <br />1.984127e-5 weeks <br />4.566e-6 months <br />, furnace cooled Weldsent Stress-relieved at 1125 F for 11-1/2 hours, furnace cooled.
A.3 Machining Test enterial from each shell forging was heat-treated with the shells. All test specimens were machined from the 1/4 thickness location of the forgings af ter performing a simulated postweld stress-relieving treatment on the test material. The test specimens represent material taken at least one forging thickness (6-1/2 inches) 'from the quenched ends of the
- forging, Specteens were machined from veld and heat-affected zone metal from a stress-relieved veldment which joined sections of the two shell ring m forgings. All heat-affected zone spectmens were obtained from the veld heat-affected zone of forging 122W195VA1.
Charpy V-Notch Iepact Specimens the axis of the notch of the Charpy V-notch impact specimens was machined perpendicular to the major surfaces of the shell ring forging.
The longitudinal axis of the specimen was parallel to the hoop direction of the shell ring forging.
t A-3 Tensile Specimens All Tensile specimens were machined with the longitudinal axis of the specimen parallel to the hoop direction of the shell ring forging.
t Wedge Opening Loading Specimens t
All WOL test specimens were machined with the sinulated crack in t
the specimen perpendicular to the hoop direction and the major surfaces of the shell ring forging. The specimens were fatigue precracked according to ASTM E399-70T.
b E
ii I
?
i i
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1 i
i
APPENDIX B ASTu coverfATTON MONf TOR MMRTAL 1
e l
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i
d l
1 APPEND 1X B
{
Am ennartAttow unwitna watratAt (*)
Correlation monitor material was supplied by the Oak Ridge National j
Laboratory from plate material used in the AEC-sponsored Heavy Section Steel L
Technology (HSST) Program.
This material was obtained from a 12-inch-thick A333 Grade B, Class 1 plate (HSST Plate 02) which was provided to Subcommittee i
II of ASTM Committee E 10 on Radioisotopes and Radiation Effects to serve as i
correlation monitor material in reactor vessel surveillance programs. The j
plate was produced by the Lukens Steel Co. and heat treated by Combustion
)
Engineering, Inc.
The following is a tabulation of the heat treatment history and plate chemistry:
I.
Heat Treatment History 1675 i 25 F - 4 hours4.62963e-5 days <br />0.00111 hours <br />6.613757e-6 weeks <br />1.522e-6 months <br /> - Air-cooled 1600 & 25 F - 4 hours4.62963e-5 days <br />0.00111 hours <br />6.613757e-6 weeks <br />1.522e-6 months <br /> - Water-quenched I
1225 3 25 F - 4 hours4.62963e-5 days <br />0.00111 hours <br />6.613757e-6 weeks <br />1.522e-6 months <br /> - Furnace-cooled t
1150 & 25 F - 40 hours4.62963e-4 days <br />0.0111 hours <br />6.613757e-5 weeks <br />1.522e-5 months <br /> - Furnace-cooled to 600 F i
j Plate Chemistry 1
A M:L.
P 1
11 Ei_
Mst Cu.
i Ladle 0.22 1.45 0.011 0.019 0.22 0.62 0.53 u
1 Check 0.22 1.48 0.012 0.018 0.25 0.68 0.52 0.14 i
j i
u (a) This appendix is from Yanichko, S.
E., and Zula, C.
C., "Wisconsin
)I Michigan Power Co. and the Wisconsin Electric Power Co. Point Beach i
Unit No. 2 Reactor Vessel Radiation Surveillance Progrant', WCAP 7712 (June, 1971).
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APPENDIX D DOST1ETER AND CAPSULE EXAMINATTON e
-,-w,.-
fs s'
Westinghouse Electric Corporatlan.
Powe-Systems nonsereavwm 8cx355 hna@Pmewu15230 May 1, 1975 WES 75-44
/Mr. T. J. Rodgers Wisconsin Electric Power Company 231 West Michigan Street Milwaukee, Wisconsin S3201 ATTENTION:
D. L. DILL
Dear Mr. Rodgers:
SUBJECT:
POINT BEACH UNITS #1 & #2 REACTOR VESSEL SURVEILLANCE CAPSULE INFORMATION
Reference:
PBM-W!iP-1572 (April 8,1975)
We believe the attached information will answer your questions as outlined in the above reference.
Westinghouse will consider the subjects of new heatup and cooldown curves and reactor vessel compliance to 10CFR50 Appendix G for the Point Beach Units as pending action unless othenvise directed.
If you have any questions.on either of these matters, please contact tre.
Sincerely.
W w
J
- 4. S. Taylor, ProjectyEngineer JST/fak (Operating Plants Service Attachment ec:
G. A. Reed J. D. Trotter S. E. Yanichko R. S. Longdon/WEP 1.2 File: WEP 1060
-y-,y.
,y
I
- b MM-SME-1103 i..
,' 4 1 ll},li?.
" ',d7J //[!
WR0 - PWRSD Engineering r:an, Mechanics and Materials Technology 236-4802 n3.,
April 21,1975
_,; JgC vm w, Point Beach Unit No.1 and 2 Reactor Vessel Surveillance C.apsules Ref:
Wisconsin Electric Power Co. Letter PBM-WMP-1572, April 8,1975 ro J. S. Taylor Field Operations, North Region NSO cc:
J. N. Chirigos J. A. Davidson J. H. Phillips T
M. M. Anderson
. S. Longdon The following infomation regarding dosimeters and capsule lead factors for the Point Beach Unit No.1 and 2 reactor vessel surveillance capsules has been prepared in response to the WisconsfiiElectHe Power Company referenced letter.
1.
U-238 and Np-237 Dosimeters Unit No. 1 V
N 238 Dosimeter 38 Purity Np0 237 h esiale U0 2
Purity rduMtu4 ow Block No.
mg
_mg Le r-(wc A P - ?s/ 3.)
35 11.52 99.9 20 99.9 Vv 36 9.68 99.9 20 99.9 R
37 13.21 99.9 20 99.9 7-38 8.82 99.9.
20 99.9 S-39 11.26 99.9 20 99.9 4
40 9.90 99.9 20 99.9 P
,n."'
. Unit No. 2 Awc A P - 99 / 2. )
68 10.96 99.9 20 99.9 Y
69 11.91 99.9 20 99.9 R-70 10.28 99.9 20 99.9 S
71 12.00 99.9 20 99.9 T
72 12.00 99.9 20 99.9 N
73 12.00 99.9 20 99.9 p
The weight of Np02 and U 0s was measured to an accuracy of 0.2%. The 3
neptunium oxide was ordered with a U235 and U238 content of less than 300 ppm and a Pu 239 content of less than 500 ppm.
The uranium oxide was ordered j
with a U235 content of less than 300 ppm.
1%
e M-SME-1103 April 21,1975
)
2 Copper Dosimeters The weight of the copper dosimeters was not determined, a.
b.
The purity of the copper dosimeters was reported as 99.999% by the
- supplier, A chemical analysis performed by the supplier resulted in the detection c.
on no impurities.
3.
Capsdle Lead Factors for Units No.1 and 2 Capsule Capsule Position Identification (degrees)
_ Lead Factors V
77 2.5 R
257 2.5 T
67 1.6 P
247 1.6 S
57 1.4 N
237 1.4
,.f0fw.:4Ac S.EIYanichko Structural Materials Engineering
/lat
i l
l l
l 1
l APPENDIX E INSTRUMENTED CHARPY EXAMINATION i
l 1
\\
APPENDIX E INS 1RUMENTED CHARPY EXAMINATION
SUMMARY
The instrumented Charpy technique was applied to the impact specimen evaluations of the following pressure vessel materials: base metal, veld metal, heat-affected-zone metal, and ASTM correlation monitor metal.
Because of the limited number of specimens and their need in establishing other parameters such as the upper shelf energy and the ductile-brittle transition temperature, there were insufficient data available for a complete
. analysis on these materials. However, load-time traces were obtained which show the change in impact behavior as a function of temperature for each of the materials tested.
INTRODUCTION The radiation embrittlement of an operating nuclear pressure vessel is determined by the accelerated irradiation of the original materials as part of a surveillance program. The lifetime of the pressure vessel will depend on the radiation-induced shift in the ductile-brittle transition temperature as measured by the Charpy V-notch Lmpact test.
The value of Charpy imiact specimens, particularly in present surveillance programs, can be considerably enhanced by tha use of the instrumented Charpy test. The instrumented Charpy test provides a valuable link between the transition-temperature approach and the fracture-mechanics approach to fracture toughness. A knowledge of the effect of radiation on key metallurgical fracture parameters can be used to accurately predict (1) the radiation-induced shift in the ductile-brittle transition temperature, and (2) the radiation-induced change in the dynamic fracture toughness, KId*
The results obtained by applying these techniques to the surveillance program Charpy specimens are presented in this section of the report.
l
E-2 BACKGROUND There are two approaches to determining the effect of radiation on the fracture toughness of pressure-vessel steels: (1) the shift in the ductile-brittle transition temperature, and (2) the change in the fracture toughness (either the static fracture toughness ye or the dynamic fracture toughness kid).
The modern theories of fracture define key metallurgical fracture parameters such as friction stress, grain size, grain-size dependence of the yield stress, and surface energy or plastic work of microcrack propagation.
The effect of radiation on most of these metallurgical fracture parameters has been previously studied, but until recently, the results had not been directly linked with the radiation-induced change in fracture toughness. This recent work established the relationships between the key metallurgical fracture parameters and the transition' temperature and b c(1)
- The instrumented Charpy test is an excellent tool for determination of the effects of radiation on the key metallurgical fracture parameters.
This test provides load-time information in addition to the energy absorbed.
The loads involved during impact are obtained by instrumenting the Charpy striker with strain gages so that the striker or tup is essentially a load cell. The details of this technique have been reported previously.(2,3)
The additional information obtained from the instrumented Charpy GY (P astic yielding across the entire cross l
test is the general yield load, P section of the Charpy specimen), the maximum load, P,,x, the brittle fracture load, P, and the time to brittle fracture (see Figure E-1).
Also, the area F
under the load-time curve corresponds to the total energy absorbed, which is the only data obtained in a normal uninstrumented Charpy test.
The instru-mented test, however, allows separation of the energy absorbed into (1) the energy required to initiate ductile or brittle fracture (premaximum load energy), (2) the energy required for ductile tearing (postmaximum load energy),
and (3) the energy associated with shear lip formation (postbrittle fracture energy), as shown in Figure E-1.
- References at the end of this Appendix, i
~
1
)
E-3 yMaximum load, P' t General yield 4
max i
load, P '
GY M rittle fracture load, PF Po s t'*ma xinrum-los d" j
energy
.3 Post brittle-fracture
, energy PRE"ciaxicru:n-load"energy l
N h
Time to brittle fracture H
Time FIGURE E-1.
AN IDEALIZED LOAD-TIME MISTORY FOR A CHARPY IMPACT TEST l
l l
l 6
i E-4 In a nomal Charpy impact study, the energy absorbed is determined as a function of temperature to obtain the Charpy impact curve and the transition temperature. The instrumented Charpy test also gives the infor-mation shown in Figure E-1 as a function of temperature, as shown by the example in Figure E-2 Various investigators (4-7) have developed theories that permit a detailed analysis of the load-temperature diagram. This diagram can be divided into four regions of fracture behavior, as shown in Figure E-2 In each region different fracture parameters are involved ( ).
Extended discussions of these fracture parameters can be found in the references indicated above.
In general, the key metallurgical fracture parameters for radiation damaFe studies are the cleavage fracture stress, o *, and the yield strength, g
Both of these parameters and the temperature sensitivity of a can be c.
,y y
derived from the results of the instrumented Charpy tests. The determination of the cleavage fracture stress o *, requires an evaluation of P at the f
gy temperature where P is 80 percent of P The yield strength, a, is p
g.
y calculated from the general yield load, P I7)gy, and is related to the uniadal te r > trength, oyg, by the relation c
= 33.3 P yg gy.
This relation is for a standard Charpy V-notch specimen, is dependent on the flank angle of the notch, and assumes Tresca yield criterion.
EXPERIMENTAL PROCEDURES The general procedures for the instrumented Charpy test are the same as those for the conventional impact test, and are described in the main text of this report. The additional data are obtained through a fairly simple electronic configuration, as shown in the schematic diagram of Figure E-3,
E-5 7
a N
- g*g'g P u
%\\
%g P
ex u
F m
j Pp PGY y
E Region 1 Region 2 Region 3 Region 4 Test temperature FIGURE E-2, GRAPHICAL ANALYSIS OF CHARPY IMPACT DATA i
l l
E-6
.A.
? A
. h I
r s.
I kI
/
v Bridge balance Oscilloscope and O
O amplifier Shunt Triggering resistance device Hamer 3
FIGURE E-3.
DIAGRAM OF INSIRUMENTATION ASSOCIATED WITH INSIRUMENTED CHARPY EXAMINATION
E-7 The striker of the Unpact machine is modified to make it a dynamic load sensor. The modification consists of a four-arm resistance strain gage bridge positioned on the striker to detect the compression loading of the striker during the impact loading of the specimen. The compressive elastic strain signal resulting from the striker contacting the specimen is conditioned by a high-gain dynamic amplifier and the output is photographed as it develops on the cathode ray tube of an oscilloscope. A previously established calibration method (9) is used to convert the oscillograph into a time-load record.. The time-load history as a function of test temperature forms the basis for further data analysis. The oscilloscope is triggered by a solid-state device at the correct time to capture the amplifier output signal.
RESULTS AND DISCUSSION The instrumented Charpy tests were conducted following the procedures discussed in the main text of this report. Specimens were tested from four irradiated materials.
These materials were the pressure vessel base metal, weld metal, heat-affected-zone metal, and ASIM correlation monitor metal.
The results of the instrumented Charpy work with the corresponding load-time i
records are given in Tables E-1 through E-5.
The tables list the specimen numbers, test temperature, impact energy, general yield load, and maximum load. Some curves are not shown because they were not obtained on the oscilloscope. It can readily be observed that the features of the load-time or load-deflection traces change as a function of temperature; however, all tests f all into one of the six distinctive notch-bar bending classifications t
shown in Figure E-4 The pertinent data used in the analysis of each record are the general yield load (PGY), maxi u 1 ad (P,, ), and fracture load (P ).
p The impact energy values listed in the tables are those normally obtained from the impact machine dial. These values are in excellent agreement with energy values from the area under the load-time curves, m
3
E-8 TABLE E-1.
INSTROLENTED CHARPY IMPACT DATA FOR BASE-METAL PLATE 122W195VA1 FRQi POINT BF).CH D11T 2 Specinen No.
El 5000 Test Temperature, F
-80 4000 A
,3000 Inpact Energy, ft-lb 8.0 General Yield Load, PGY, Ib 1000 Maximua Load, P
, Ib 3950 0
g y g ag Time, psec Specimen No.
E3 N
4000 Test Temperature, F
-80 A
g
^
Impact Energy, ft-lb 7.5
=
1 General Yield Load, Pgy, Ib g
Maximum Load, P
, Ib 3900 o
Tns, pac Specinen No.
E8 5000 Tes t Tenperature, F
-45
/
Icpact Energy, ft-lb 25.5 A"
~
32000 General Yield Load, PCY, Ib Maximum Load, P,,x, Ib 4350 0 0 M M M em Tne, ysac Specimen No.
E2 5000 m
[j g
Test Tenporature, F 0
Impac t Energy, f t-lb 53.5 3300 General Yield Load, Pgy, ib 1000 tIaximu., toad, P
, 1b 4400 o
2000 3000 4000 5000 n...,,e.
i
E-9 TA3LE E-1 (Continued)
Specimen No.
E4 4000 Test Temperature, F 0
i e
Impact Energy, f t-ib 10.5 32M' General Yic1d Load, Pgy, Ib loco
}taximum Load, P Ib 3700 0
0 1000 2000 3000 4000 5000 Time, psec 5000 Specimen No.
E9
/
4g Test Temperature, F 0
8,3o0c Impac t Energy, f t-lb 55.0
}2000 3300 1000 General Yield Load, Pgy, Ib Maximum Load, P Ib 4450 0 0 1000 2000 3000 4000 5000 D "X,
Time, ysec Specimen No.
E7 5000 Test Temperature, F 74 i
Impact Energy, f t-lb 86.0 3000 General Yield Load, Pgy, Ib
,g 4250 11aximum Load, P
,x, Ib o
g Time, psec 5000 Specimen No.
E11 Tes t Tcnperature, F 76 e 3000 Impact Energy, ft-lb 76.5 j2000 General Yic1d Load, Pgy, Ib 3050 icoo
}la;:inu:2 Load, P,,x, Ib 4050 0 0 1000 2000 3000' 4000 5000 Time,pste l
E-10 TABLE E-1 (Continued)
=
5000 Specimen No.
ES Tes t Temperature, F 145 m.3000 Impact Energy, f t-lb 141.5
]2000
\\
General Yield Load, Pgy, Ib 2MO m
Maximum Load, P
, Ib 4150 0 0 s
so m Tiet, psec Specimen No.
E6 5000 g [A\\
Test Temperature, F 145 e
Impact Energy, f t-lb 133.0
]2000
\\
2950 General Yield Load, Pgy, Ib gooo Maximum Load, Pen, Ib 4100 o
m.,,,..
Specimen No.
E12 Test Temperature, F 200 Impact Energy, f t-lb 136.5 General Yield Load, Pgy, Ib Maximum Load, P,g, Ib Specimen No.
E10 5000 Test Temperature, F 290
[
}2000
\\
Impact nergy, f t-lb 135.0 General Yield Load, Pgy, Ib 2750 g
,gg Maximum Load, Pmax, Ib 3900 N-00 1000 2000 3000 4000 5000 Time, pset
E-11 TABLE E-2 INSTRUMENTED CHARPY DiPACT DATA FOR BASE-METAL PLATE 123V500VA1 FROM POINT BEACH UNIT 2 5000 Specimen No.
V10 4000 Test Temperature, F
-80 e.3000 Impact Energy, f t-lb 3.5
]2000 General Yield Load, Pgy, Ib poco
!!aximum Load, P
, Ib 2900 0 0 1000 2000 3000 4000 5000 Tae,psec 5000 Specimen No.
V3 g
Tes t Temperature, F
-80 e,3 con Impac t Energy, f t-lb 2.0
}2000 '
General Yield Load, Pgy, Ib l000 Flaximum Load, P
, Ib 2500 0 0 K)00 2000 3000 4000 5000 TLme,psec 5000 Specimen No.
V6
[
4000 Test Temperature, F
-45 8,,3000 Impact Energy, f t-lb 50.5 32000 M
E General Yield Load, Pgy, W 4250 0 0 1000 2000 3000 4000 5000 11aximu:2 Load, Pmax, Ib y,, pgee 5U Specimen No.
V1 4000 3000[
Test Temperature, F
-45 m
Impact Energy, f t-lb 22.0 j2000 General Yield Load, Pgy, Ib icon
}!aximura Load, P
, Ib 4250 0
Time, ysoc
<*-m
E-12 TABLE E-2 (Continued)
Specimen No.
V2 Test Temperature, F 0
Impact Energy, f t-lb 90 General Yic1d Load, Fgy, Ib Maximum Load, P
, Ib Specimen No.
Vil Test Temperature, F 0
[
Impact Energy, f t-lb 94.5 General Yield Load, Pgy, Ib 3200 goo Maximum Load, P
, Ib 4350 o
Tm, pec 5000 Specimen No.
V12
[
\\
Test Temperature, F 74 Impact, Energy, f t-lb 114.5
]2000
\\
General Yield Load, Pgy, Ib 2950 gooo 1
4250 o
Maximun Load, P,,, Ib m 3 00 mW Tm, me i
Specimen No.
Y7 Test Tcoperature, F 76 Impac t Incrgy, f t-lb 108.5 General Yield Losd, PGY, Ib l
Haxinu:n Loud, P,,x, Ib
-,-o
E-13 TABLE E-2 (continued)
Specimen No.
V5 5000 Test Temperature, F 145 4000 30 %
Impact Energy, f t-ib 186.5 y
General Yield Load, Pgy, Ib 2550 1000
'\\
Maximum Load, P
, Ib 3800 00 5000 10000 Time, psec 5000 Specimen No.
V4 4000
,-g Test Temperature, F 200 e
/
30 %
Impact Energy, f t-lb 216.0 32000 General Yield Load, P 2400 1000 GY, Maximum Load, P
, Ib 3600 0 0 1000 2000 3000 4000 5000 Time, psec 5000 Specimen No.
V9 Test Temperature, F 290 8
3oon
, K Impact Energy, f t-lb 165.0 32000 General Yield Load, Pgy, Ib 2500 1000
\\k Maximum Load, Pma, Ib 3550 00 5000 m
Time, ysec 5000 Specimen No.
V8 4000 Test Tcaperature, F 345 e
f
\\
Impact Energy, ft-lb 198.5 32000 w
General Yield Load, Pg,, Ib 2300 1000 llaxinica Load, P
,x, Ib 3450 0,
10m n
Time, yuc
E-14 TABLE E-3.
INSIRIAIENTED CHARPY IMPACT DATA FOR WELD METAL FRot! POINT BEACH UNIT 2 5000 Specimen No.
W6 4000 A
Test Temperature, F 76 8 3000 Impact Energy, f t-lb 13.5
}2000 General Yield Load, Pgy, Ib 10M Maximum toad, P
, 1b 3800 0 0 1000 2000 3000 4000 5000 Time, psee Specimen No.
W3 5000 Tes t Temperature, F 145 4000 a
p Impact Energy, f t-lb 22.5
]2@
General Yield Load, PGY, 20 Maximum Load, P
, Ib 3800 o
2000 3000 4000 5000 Time. psec 5000 Specimen No.
WS 4000 Test Temperature, F 145 8,3oon O Impact Energy, f t-lb 27.0 f2000 General Yield Load, Pgy, Ib l000 Maximum Load, P,g, Ib 3850 00 1000 2000 3000 4000 5000 Time, pses i
Specimen No.
W8 Test Temperature, F 200 Impact Energy, f t-lb 43.0 Ocncral Yield Load, PCY, Ib Mai:inus Load, P,,x, Ib 74F
E-15 i
TABLE E-3 (Continued) 5000 Specicen No.
W1 Test Temperature, F 290 3000 Impact Energy, f t-lb 41.5
\\
2000
\\
General Yield Load, Pgy, Ib 3050 000 Maximum Load, P
, Ib 3550 0 0 1000 2000 3000 4000 5000 Twee, psec Specimen No.
W7 Test Temperature, F 310 e.3000 0 Impact Energy, f t-lb 41.0
}2000 General Yield Load, Pgy, Ib 2750 goon 5
Maximum Load, P
,x, Ib 3450 0 0 1000 000 3000 4000 Sc00 Tune, psec 5000 Specimen No.
W2 4g Test Tuperature, F 345 2
A 3ooo Impact Energy, f t-lb 41.5 32000
\\
General Yield Load, Pgy, l'o 2750 1000 Maximun Load, Paax, Ib 3500 0 0 1000 2000 3000 4000 5000 Tlee,psee 5000 Spe:inen No.
W4 4000 O '
Test Tc 1perature, F 345
,.3000 Inpact Energy, ft-lb 43.5 32000
\\
General Yield Load, P 3000 W
GY, 0
Maximum Load, P"", I b 3550 0
1000 2000 3000 4000 5000 Time, puc j
i j
E-16 i
TABLE E-4 INSIRUMENTED CHARPY IMPACT DATA FOR HEAT-AFFIX:TED ZONE METAL FRGi POINT BEACH UNIT 2 Specimen No.
H2 Song Test Temperature, F 0
4000 g
Inpact Energy, f t-lb 10.5
-3000 3
General Yield Load, Pgy, lb a2000 Mexinum Load, P Ib 4000 0
1000 2000 3000 4000 5000 Tlaw, yuc 5000 Specimen No.
HS
- A Tes t Tenperature, F 0
e 3oon Inpact Energy, f t-lb 27.0 32000 General Yield Load, Pgy, Ib 1000 Maxinus Load, P Ib 4400 0
0 m 2000 3000 4000 5000 Tae, yus Specimen No.
H8 4000 g Test Te=perature, F 0
8 3000 Impact Energy, f t-lb 15.0 General Yield Load, Pgy, Ib 3000 Maxinem Load, P,, Ib 4100 0
g g g
' 4g g Tee, pec 5000 Specinen No.
H1 4000 O
/
\\-
a Tes t Temperature, F 76
-3000 7
3 Inpact Energy, f t-lb 115.0 2000
\\
\\
General Yield Load, Pgy, Ib 3100
!!aximum Load, Pman, Ib 4350 0
1000 2000 3000 4000 5000 Time, puc
_ - - -. =.
~
E-17 TABLE E-4 (Continued)
N Specimen No.
H6 I l l
---m 4000
/
N Test Temperature, F 76 e
(
\\
3000 Impact Energy, f t-lb 152.0 32000 General Yield Load, Pgy, D 3200 W
\\ \\-_-
Maximum Load, Pmax, Ib 3450 0 0 1000 2000 3000 4000 5000 Time, pec.
Specimen No.
H4 5000 Tes t Teeperature, F 145
[
ey Impac t Energy, f t-lb 177.0 32000 N
General Yield Load, Pgy, Ib 2950 3
1 jg Maximum Load, Pmax, Ib 3400 o-m i
0 1000 2000 3000 4000 5000 Ties, ysoc 5000 Specinen No.
g m
[
\\
Test Temperature, F 200 8
}3noo Inpact Energy, f t-lb 102.5 2000 N
Ceneral Yield Load, Pgy, Ib 2MO M
N Maximum Load, P,,x, Ib 4050 0 0 1000 2000 300[4000 5000 Tm, psec 5000 Specimen No.
H3 4 00 m
Test Tcnperature, F 290 e 3000 N
I N
Impact Energy, f t-lb 195.0 32000:
w General Yield Load, Pgy, Ib 10 00 A
2800 Hoximum Load, P
,x, Ib 4050 0
n 0
1000 2000 3000 4000 5000 Tirne, psec
=-
i a -
E-18 TABLE E-5.
INSTRUMENTED CHARPY DIPACT DATA FOR ASIM CORRELATION MONITOR MATRIAL FROM POINT BEACH UNIT 2 Specimen No.
R7 5000 Test Temperature, F 76 4#
Impact Energy, f t-lb 9.5 2W General Yield Load, PGY, Ib goon Maximum Load, P, Ib 3300 0 0 m mmem Time, psec 5000 Specimen No.
R2 4000 Test Temperature, F 80 e 5000 f2000 I.npact Energy, f t-lb 7.0 General Yield Load, Pgy, Ib 1000 Maximum Load, P,,x, Ib 3150 0 0 1000 2000 3000 4000 5000 Tkne, psec 5000 Specimen No.
R4 g
a g3ooo [
Tes t Temperature, F 145 Impact Energy, f t-lb 39.0 8,2000 General Yield Load, Pgy, Ib 3200 1000 Maximum Load, P,,x, Ib 4150 0 0 1000 2000 3000 4000 5000 Twe,psec l
5000 Specinen No.
R5 4000 Test Temperature, F 145
-3#
I#
Impact Energy, f t-lb 31.0 General Yield Load, Pgy, Ib 2950 Maximum Load, P
, Ib 4050 0
1000 2000 3000 4003 5000
[
max T**, PS**
E-19 TABLE E-5 (Continued)
Specimen No.
R6 5000 Test Temperature, F 200 4000 Impac t Energy, f t-lb 55.0 R 3000
]2M General Yield Load, Pgy, B 2800 Maximum Load, P
,x, Ib 4050 1000 0 0 1000 2000 3000 4000 5000 Time, psec Specimen No.
R8 Test Temperature, F 290 Impact Energy, f t-lb 81.5 General Yield Load, Pg7, Ib Maximum Load, P
, Ib 5000 Specimen No.
R1 4000 Test Temperature, F 345 a
/3 (
3noo Impact Energy, f t-lb 96.5
]2000 N
General Yield Load, Pgy, Ib 2550 1000
(
Maximum Load, P,,x, Ib 3750 0 0 1000 2000 3000 000 5000 Tee, pses 5000 Specimen No, R3 4g Test Temperature, F 345 e 3000 f A
Impact Energy, ft-lb 90.5
]2000 General Yield Load, Pgy, Ib 2550 1000 Maximum Load, P
,x, Ib 3700 0
n 0
1000 2000 3000 4000 5000 Time, psec
==
E-20 Fracture Load-displacement Raw Remarks type curves data I
7 P
Brittle fracture F
3 Defteetion s
11 8
P Brittle frace re a
gy e
I Deflection
}
P Brittle fracture followed by III gy v
fracture indicative of shear lip formation De flection Stable crack propagation IV t
P followed by' Unstable brittle OY' c
fracture and' fracture P
max indicative of shear lip Deflection V
i P
Stable crack r.'nagattor-j gy' follevea by tiacture p
inote; tve of shear lip max reation Deflection VI m
P Stable crack propagation 2
gy' followed by gross daformation
' max Deflection FIGURE E-4 Tile SIX TYPES OF FPACTURE FOR UOTCHED BAR BENDING i
t I
1 E-21 The Charpy energy curves and the load-temperature information obtained from the instrumented Charpy tests are shown in Figures E-5 through These figures illustrate a unique feature of this type of analysis; E-9.
that is, the determination of a definitive fracture traneition temperature by discrimination between fractures occurring below and above general yield (Pgy).
This transition is a clear indication of the mechanical properties of the material and does not depend on empirical correlations, as the nil-ductility transition temperature (NDIT) determined by the 30 f t-lb fix temperature does.
It is interesting to note that impact fracture at the 30 f t-lb level corresponds to ductile specimen behavior, where considerable work hardening is required to raise the stress at the notch to a value sufficiently above the yield stress for fracture to result.
In general, the curves show both the general yield load and the maximum load initially increasing as temperature is decreased from the upper shelf region of the Charpy impact curve. As temperature is further decreased through the transition temperature region, the maximum load goes through a maximum and drops of f as temperature continues to be decreased.
The general yield load is also quite sensitive with respect to temperature. As the temperature is decreased from the upper shelf region, the general yield load increases substantially.
CONCLUSTONS The instrumented Charpy impact test technique was used to study the impact behavior of pressure-vessel materials.
Because of the limited number of Charpy specimens, it was not possible to do a complete analysis of these materials.
However, it was shown that in all materials the nil-ductility transition te=perature as determined by the 30 ft-lb fix corresponds to specimen behavior where there is some ductile behavior rather than completely brittle behavior. Ihe maximum load was shown to go through a maximum as temperature is lowered from the upper shelf region into the transition temperature region.
In addition, the general yield load was shown to increase as temperature is decreased.
l E-22 4500 i
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l N
PGY 3000
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15 0 6
0 0
u 2500
- 12 5 100 eb 75 f
[
e 50 i
25 0
- 10 0 0
10 0 200 300 400 Temperature, F FIGURE E-5.
Ik"AvriENTED CHARPY LOAD-TDiPDMTURE AND DiPACT DIDtGY-TD4PIRATURE CURVES FOR POINT BEACH UNIT 110. 2 FASE METAL PLATE 122W195VA1 (E SERIES)
E-23 4500
^
i i
i i
O 4000 -
P ox m
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~~~
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a
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200 O
0 0
15 0 2
i 3
4 g
10 0.[
tu O
50 0
I I
i i
0
-100 0
10 0 200 300 400 Temperature, F FIGURE E-6.
INSIRttiENTED CHARPY LOAD-TDiPERATURE,GD IMPACI ENERGY-TDiPERAIURE CURVES FOR POINT EEACH UNIT NO. 2 BASE METAL PLATE 123V500VA1 (V SERIES)
E-24 4500 i
i i
I 4000 O
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l 6
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O O
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2500 40 i-l 30 l
r O
20 E E
ta 10 I
i i
i 0
-10 0 0
10 0 200 300 400 Temperature, F FIGURE E-7.
INSTRLHDiTED CHARPY LOAD-TDiPIRATURE AND DiPACT ENERGY-TDtPIRAIURE CURVES FOR POINT BEACH UNIT NO 2 WELD HETAL
E-25 4500 O
O O
O O
4000 O
e
]3500 g
I O
A 3000 PGY O
o 2500 200 O
/
/
O O
/
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/
/
.c
/
O 100 h i
a n.a
/
/
/
50
/
9l 3't i
i i
0
-10 0 0
100 200 300 400 Temperature, F FIGURE E-8 INSIRUMENTED CIBRPY LOAD-TDiPERATURE AND IMPACT ENERGY-TDiPERATURE CURVES FOR POINT BEACH UNIT NO. 2 HEAT AFFETED ZONE HETAL i
.-