ML12275A511
| ML12275A511 | |
| Person / Time | |
|---|---|
| Site: | Indian Point  |
| Issue date: | 10/01/2012 |
| From: | Gamer F, Henager C, Igata N Battelle Memorial Institute, Pacific Northwest National Laboratory, Univ of Tokyo, Westinghouse Hanford Co |
| To: | Atomic Safety and Licensing Board Panel |
| SECY RAS | |
| References | |
| 07-858-03-LR-BD01, RAS 23554, Indian Point 50-247-LR and 50-286-LR | |
| Download: ML12275A511 (20) | |
Text
NYSR00337 Revised: October 1, 2012 EXCERPT INFLUENCE OF RADIATION ON MATERIAL PROPERTIES:
13th INTERNATIONAL SYMPOSIUM (PART II)
A symposium sponsored by ASTM Committee E-10 on Nuclear Technology and Applications Seattle, WA, 23-25 June 1986 ASTM SPECIAL TECHNICAL PUBLICATION 956 F. A. Garner, Westinghouse Hanford Company, C. H. Henager, Jr., Battelle Pacific Northwest Lab-oratory, and N. lgata, University of Tokyo, editors ASTM Publication Code Number (PCN) 04-956000-35
~~1~1916 Race Street, Philadelphia, PA 19103 OAGI0000608 00001
Library of Congress Cataloging-in-Publication Data InHuence of radiation on material properties.
(ASTM special technical publication; 956~/
"ASTM publication code number (PCN) 04-956000-35.,.
CompMion to: Radiation induced changes in microstructure (part !).
Includes bibliographies and index.
l . Materials-Effect of radiation on-Congresses.
- r. Gamer, F. A. II. Henager, C. H. llL lgata, N.
1Naohiro), 1926- IV. ASTM Committee E-10 on Nuclear Technology and Applications.
V. Radiation induce~ changes in microstructure.
VI. Series.
TA4l8.6.J54 1987 62(LI' 1228 87-26992 ISBN 0-8031-0963-6 Copyright ti;) by AMERICAN SOCIETY fOR TESTING AND MATERIALS 19R7 Library of Congress Catalog Card Number: 87-26992 NOTE The Society is not responsible. as a body.
for the statements and opinions advanced HI this publicatinn.
Prm1c*~l 10 Ann Arh\11, Ml fft:c*.;mher J 9"87 OAGI0000608 00002
=oreword Effects of Radiation on Materials: 13th International Symposium was presented at
- eattle, WA, 23-25 June 1986. The symposium was sponsored by ASTM Committee HO on Nuclear Technology and Applications. F. A. Garner, Westinghouse Hanford
~ompany, served as chairman of the symposium; and N.H. Packan, Oak Ridge National
.aboratory, C. H. Henager, Jr., Battelle Pacific Northwest Laboratory, N. lgata, Jniversity of Tokyo, and A. S. Kumar, University of Missouri-Rolla, served as vice-hairmen. There are two resulting special technical publications (STPs) from the ymposium: Radiation Induced Changes in Microstructure: 13th International Symposium Part/), STP 955, and Influence of Radiation on Material Properties: 13th International
'ymposium (Part 1/), STP 956.
A881J61476A OAGI0000608 00003
}. Russell Hawthorne, 1 Blaine H. Menke, 1 Nabil G. Awadalla, 2 and Kevin R. 0' Kula~
Experimental Assessments of Notch Ductility and Tensile Strength of Stainless Steel Wetdments After 120°C Neutron Irradiation
REFERENCE:
flawthom~. J. R .. Menke. 13. H.. Awadalla, N G, and O'Kula, K. R.,
"Experimental Assessments of Notch Oudility and Tensile Stren~th of Stainless Steel Weldmcnts After 110"(.: Neutron Irradiation," JnjluMa <4Radiation on Mar~riall'mperlies: 13th lntemarimwl Srmpo<ium !Purl II). I!STM STP '156. F. A. Oamer. C. H. Hena!'.:r. Jr .. and N. lgata, Eds.,
Amcrica11 So<:icty for Te~ting and Matcri;tls. Phtladdphia, !9!i7. pp. 19!-206.
AUSTR.-\CT: Th~ Charpy- V I(',) pmper!tc' of American !mn and Steel Institute 1A lSI) 300 snies
'tainlc~s steel plate. weld, and weld h.::;n .. affcctcd zone ( HAZJ materials from comm~rcial pmducti\)n wd.lmt*nts in 401Hnm-diwnt!tcr pipe i 12. 7-mm wall) were investigated in unirradiatcd and irradiated
-:nndttion~. Wdd <~nd HAZ tens1Je rroperti~s w~re abo a".:'scd in the !W<l condition~. The p!at.:s and weld Iiiier wire-; represent difkrcnt 'tee] melts: th.: welds were produced usinp. the multtpass metal inert ga; (MIG) proccs>. Weldrncnt propertic~ in two test orienta! ton' we're cvaiuatcd. Specimens were irradiated in a light water cooled and mod.::ratcd reactor to I X 10'" nkm'. E > 0.1 MeV.
usin~: a .:llntrolkd temperature as,cmbly. Spcdm~n tests were performed <tt 25 and 125"C.
The *adimion-induced reductions in (', energy absnrption at 25°C were about 42';f. fm !he weld and the HAZ mat.:rials evaluated. A trcnJ of em,rgy increase with temperature was nhservcd. The
~onc<>lllitant dcvati<m in yidd '>tren~th was ahout 53%. The in.:rca;e in tensile strength in contrast w;b only ll>'..i-. The ptJstinaJiation yidd o.trcngth ,,f t!Je a.qal t.;,t ori<'ntutinn in tlK pipe wa,; less than that of th~ ..:m:umfcrclltial test nri<:~11tation.
Results lor the HAZ indicate that this component may be the w.:ake't link m the wcldmcut fmm a trcll'tttn.~ rcsi~tance VIewpoint.
KEY WOROS: stainles~ srecb. weld dq)()sits. wdd h<:at affected woe, raui~rion cmbrittknwnt.
nudear irradiatJ<)Il, notch duutlity. t~nsik strength, fractur.:: resistance. 120°C irradiation This study represents nne phase of a large investigation into the fracture resistance of austenitic stainless steel we!drnents, both as-fabricated and after irradiation at 120°C. The general objective was to explore nolch ductJlity 3nd tensde strength changes produced by a lluence of -*l x HP' nicm'. 1:; > 0. I MeV, as a precurstlf to a study inV<living much higher tlucm;es at the same nominal temperature. The total investigation is intended to develop a broad base of information
<~n fracture toughness properti{:s as well as notch Juctiiity and tensile properties where research variables are test temperature. loading rate, neutron tluencc, and weidrnent component. that is.
base metal versus weld metal versus weld hcat~affected zone tHAZ).
' Rcs~al\:h metallurgist and scninr engineer, respectively, Materials Engineering Assol*iate~. Inc . 9700-B Martin Luther King, Jr. Highway, Lanham. MD 20706-1837.
' Research staff engineer and research engineer respectively. E. L du Pont de Nemours & Co .. Savannah River Labowtory. P.O. B<Jx A. Aiken. SC 2'lil08-00J.
191 OAGI0000608 00004
192 INFLUENCE OF RADIATION ON MATERIAL PROPERTIES In the literature, a large volume of data exists for stainless steel materials irradiated at high temperature (>37(fC), especially for thin sheet and plate forms The information was developed primarily in support of advanced reactor concepts. such as breeder and fusion systems that would involve high-temperature service. For lower temperature irradiation conditions, data on mechanical properties and propet1y changes wrought by neutron exposure are sparse. A paucity of data is particularly evident for irradiation temperatures less than 200°C. The present study was undertaken to help fill the void in knowledge on the fracture resistance of American Iron and Steel Institute (AlSI) Type 304 weldments for "low-temperature" radiation service applications. Materials of interest were those produced commercially in the early 1950s.
Materials The test materials were 1950 vintage. rolled and welded p1pe sections having an outer diameter
~OD) of 406 mm (16 in.) and a nominal wall thickness of 12.7 mm (0.5 in.). A total of eight pipe sections was evaluated. In this report. the in<lividual materials are referenced to the arbitrarily assigned pipe ring number (I through 8).
Each pipe test section contained a circumferential weld made by the meta! inert gas (MIG) process and one or more longitudinal welds. Only the circumferential welds were evaluated here.
The weld joint was a single Vee; the joint preparation contained a small land on the inner diameter (lD) side to aid prewcld fitup. Figure I is an etched cross section of one typical weld. The joint was filled from the OD side using 'everal weld passes; a root pass made from the ID side was evident in most joints as well. The width of the deposit on the OD surface was on the order of 15 mm (0.6 in.) and was 2.5 mm (0.1 in.) on the ID surface. Based on weld bead patterns. the welds were not filled using the same sequence in all cases.
The chemical compositions of the base metals and the weld metals arc given in Table l. Note that the base compositions indicate different steel melts as their source; the weld metal composition~
likewise infer that the weld fillers were from different melts. Thus. the materials provide a basis for statistical evaluation of properties of weldments produced in the 1950s timeframe
<l Test Specimens Full s.ize Charpy- V C,. specimens (ASTM Type A) and threaded-end tension specimens having a gage diameter of 5.08 mm and a gage length of 20.3 mm were used for the notch ductility and strength determinations. respectively. Specimen blanks were cut in two orientations One group
- d. of specimens had their long dimension parallel to the original pipe axis and are identified here as
axial orientation specimens." The second group had their long dimension perpendicular to the pipe axis and tangential to the OD; these are termed circumferential (CMFL) specimens." In all cm;es. the notch of the C, specimen was made perpendicular to the pipe ring surfaces {OlJ and ID).
FIG. 1***-Elched cross section of Weld 5 ( 12. 7-mm base plotc thickness).
OAGI0000608 00005
HAWrHORNE ET AL. ON NEUTRON IRRADIATION 193 For best control over the location of weld and HAZ specimens in the stock, the blanks were first rough-machined to approximately 11.5 mm square in cross section and then individually etched to reveal the weld fusion lines. For *axial weld specimens, that is, those which spanned the deposit, the specimen midlength was placed on the weld center line. For the CMFL weld specimens, the cross section was centered on the weld nugget. Because of the Vee-shape of the deposit and its limited width on the ID surface, the C specimens of this orientation contained a small triangular volume of HAZ material on the front face and on the rear face of the specimen. This nonweld material is not believed to have influenced the test result.
Figure 2 shows schematically, the placement of the HAZ specimen relative to the weld deposit.
For the CMFL orientation, specimen locations were indexed to the intersection of the adjacent fusion line with the ID surface side of the rough-machined blank. The axial orientation HAZ C, specimens were also indexed in this manner. Although arbitrarily chosen, the reference distance from the fusion line was intended to make the specimen "bracket" the heat-affected zone.
Typically, the C specimens but not the tension HAZ specimens of the CMFL orientation contained a small volume of weld metal in the test section.
It will be noted that the axial orientation "weld" tension specimens, in fact, were composite specimens since the gage length of 20.3-mm spanned not only the weld nugget but also the HAZ on either side. Tests of these specimens would produce failure in the weakest component.
Material Irradiation The irradiation of C, and tension specimens was performed in the 2-MW light-water-cooled and moderated UBR test reactor located in the Buffalo Materials Research Center. The 93 specimens were contained in three, independently temperature-controlled capsules designated A, B, and C, which together formed one irradiation assembly. Thermocouples welded to specimen midsections were used for temperature monitoring and control. The target irradiation temperature was 120°C (248°F). At full reactor power, temperature differences were less than +/-:!SOC.
Cv HAZ SPECIMENS AXIAL CMFL
- FUSION LINE TENSILE HAZ SPECIMEN OAGI0000608 00006
<0 z
'"TI r
c m
z
("')
m 0
'"TI ll 0
- l TABLE 1-Base mera/ and weld compositions. 0 z
0 Composition, wt% z Base Metal ----------------
Ring (Side) c Mn Si p s Ni Cr Mo B Co Cu N* ~
-1 m
ll BASE METAL A 0.079 1.60 0.79 0.031 0.011 9.63 18.79 0.41 () 001 0.11 0.29 0.047 ~
B 0.035 156 0.58 0.024 0.016 9.19 18.44 0.25 0.002 0.10 0.24 0.036 -o ll 2 0.079 1.50 0.34 0.031 0.024 9.65 18.27 0.45 0.002 0.13 0.42 0.043 0 A -o B 0 052 1.41 0.38 0.031 0.025 8.50 19.40 0.39 <0.001 0.15 0.42 0.036 m
- u
-1 3 A 0.063 1.30 0.31 O.o28 0.024 9.38 !859 0.40 0.001 0.12 0.38 0.044 m 0.(J48 1.33 0.39 0.027 0.025 9.13 18.67 (J.36 0.002 0.13 0.39 0.034 (/)
B 0 4 A 0.053 1.81 0.33 0.026 0.017 8.75 18.97 0 . .15 0.002 0.11 0.28 0.033
)> 0.74 0.033 () 017 9.60 18.88 0.46 0002 0.13 0.32 0.043 B 0.083 !.75 G>
0 5 A 004] 1.39 0.67 n.026 n.024 9.64 18.88 052 0.002 n.12 0.28 o.tns 0
0 B 0.080 1.25 0.32 0.026 0.016 10.00 19.05 0.44 0.001 0.13 0.41 0.043 0
(j) 0 6 A 0.058 1.44 0.49 0.027 0.017 9.65 19.05 0.43 0.001 0.15 0.62 0.044 00 B 0.!146 1.46 0.66 0.026 0.024 8.48 18.88 0.22 0.001 0.13 0.17 0.034 I
0 0.12 0 7 A 0.052 !.30 0.55 0.028 0.016 9.35 18.65 0.38 0.002 0.26 OJJ39 0 B (l.(j47 Ln 0.34 0.027 0.019 9.15 18.50 0.21 0.001 0.08 0.20 0 037 0
...... R A {'),()55 I 30 0.40 0.030 0.026 8.72 19.05 0.4:2 0.002 0.16 0.45 0 036 u (\. (tfQ (\ ctil nnn () 111 ~ ~ ~n lr.) hA. () J.-1 n f1n*' n <J () 14 011.-11 l '"
HAWTHORNE ET Al. ON NEUTRON IRRADIATION 195
"' 0~I r
6 l r l rt t-r*,
r I 6
x,.:
0 6
"" c
,::: - c:"'
- - *- ~;
c-;:- .:; f'* -_f) <r, q n
~
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.,, ...r_:,, .c -.o r- ,_
l/'~
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"" *'J' '="
(::\
,...-i r1
- r, :...,., *C* >r, >r, I
('
.c. 1r) l'* ,:::
7 -~ ~ - - C' ct-.
]'*
~
X
- ::; *~*
c.
~
8 "'c , 2 I <_:_!
6
~
c s---' 2 c 0 co c r]
0 c
c<
--:: 2;: "'-r r--
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-* .::; c ::;
- c
- r,
.... tr; ,.., -.o r-- r I
" C'l --r '"* >r, --:- v-,
~
'6., ,,..., s:.
r--
>r,
-;- =~
0 c ~ C) ::0 "'
- -* *::0
- - c; c "';~
~(*
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" ::::: ,.., 3:
-[:. ~ ~ --:- *r. ~-
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~ '.;: ...: -D 3-.:; *.c 3 ~ "?-
.(; ?:::
,, ./.... *C --- ,~
- r.
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~ ~ ~ ?::: ~ 3 3c. *-~
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- C c) ~. <'I c:
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' "" 00 OAG 10000608_ 00008
196 INFLUENCE OF RADIATION ON MATERIAL PROPERTIES
!IAPo) BASE METAL (AXIAL, 25"C TESTS) r-- BASE METAL (CMFL, 25*C TESTS) lkti)
. 160
('I 0 YIELD
- . a TENSILE
>: 82'5 1-
"z:
ll' ti 350 rk2f1~
,J
{**
RM~{j~
- r
- 3. J. rf~
120 BO 2751- :2-5< :.1! ~ 02 ~; 8 ': 1
[)
- j-1 0,; {f_) t
- 40 J 4 6 RIN(; NUiolllER 3 4 5 FIG. 3-/ndividual yield and /ensile strength determimuions at 25"C for base metals from four pipe ring (axial and circwriferential test orientations). Results for J25*c tests of base metals from Ring 3 are a/s.
shown.
The target flue nee was l x 1020 n/crn2 , E > 0. l MeV. Actual ftuences were detennined fron iron and nickel dosimeter wires placed in the V-notches of the Cv specimens and from 238 l dosimeter capsules nested among the tension specimen gage sections. The average measure' specimen ftuence was 1.1 X lOw n!cm 2
- Neutron spectrum calculations indicate that the ftuence n.lcm 2
- E > 0.1 MeV. is 2.91 times the ftuence, n!cm 2 , E > 1 MeV 11 ,2]. The exposure equivalent in terms of displacements per atom (dpa), was 0.063 dpa (E > l MeV).
Results Unirradiated Condition-Tensile Properties The test matrix for tension specimens encompassed two specimen orientations, three temperature; and two loading rates (static and dynamic). Findings from the dynamic tests will be treated in future report. Figures 3 and 4 are plots summarizing the individual strength determinations forth base metal, the weld, and the weld HAZ materials, respectively.
MPo (k.!li)
C),U 'fiELD TENSILE
{25*c TESTS) t60
...<:>>: 82(>
/8>'1~:_: M\=.:-rAt.. SA~*f. Mf:'l'.Al tZO zw v iA>:ll\~i
- * .2 l{.MPt.'
0:
l * *1 *25"'C i T(S":" 8{l
"' 550 Q 0 c
B 0;::
275 1
" I* T C*2 ~;;:*
4C
- AX:Jlo<...* {C'-'I**L! i(M~l-; *SWE:
0 0 6 5 8 3iAI ~(9) 318i' RlNG NUM!lER FIG. 4-lndividual yield and tensile strength determinations at 2S'C for weld deposit.! and weld he<
affected zone materials (axial and circumferential test orientations). The range of base metal values from Fi 3 is indicated for comparison. Results of one 125"C test of the HAZ is also shoHm.
OAGI0000608 00009
HAWTHORNE ET AL. ON NEUTRON IRRADIATION 197 BASE METAL (CMfL)
- 3. 4 RING N* (SIDE AI I (flllb)
.. , 240 o, n UIIURNAOIATED RING 3 (A!"'I IRRAOIATEJ> 12o*c~.. / ff!NG 4 !A}..
/ ~;.~*/ _J:
/
/
,* /
- /~**
RIN<! 3
. . . :RR"D l
.j l r - -- __...-- --*1
- -1*10, **;,,.,
\E'.o*O.tMalv'}
~i '"'BAS£ AXIAL TREND o:____-:c2~c:----:,,':-,---:-,:?t> {"Cl ----f,~-~~~-~,2~5--:,~.c~l~*o TEMPE:RATVRE TEMPERATURE FIG. 5 ----Charpy-V notch ductiliiv ol base mmerials from Ring 3 and RinK 4 in unirradiaml cuJd J20°C irradiated ,*ondirions ltiXial and c*irt'mnj~remial /e.W oriemations) a/ thrN temperatures. Data trends from the
!efi panel are reprod1<ad in th<' righ1 panel ro simpilfv data comparisons.
The data for the base and weld metals do not show a pronounced effect of test orientation. The yield strength levels of the weld and HAZ are about the same but are somewhat higher than the yield strengths of the two base metals evaluated. However, the tensile strengths of the three components were found to be about equal. An increase in test temperature from 25 to 125°C resulted in a lowering of the tensile strengths but did not change appreciably the yield strengths of either the base metals or the HAZ materials. Weld metal tension tests at 125oC were not perfonned.
Unirradiated Condition-Notch Ductility Properties The test data for the unirradiated condition C, specimens arc shown graphically in Figs. 5 through 9 (see open symbols). All C, specimens were tested on the same (hot cell) impact tester.
In general, specimen energy absorption was greater at 125 than at 25°C. suggesting an increase in fracture resistance with temperature (see Figs. 5 to 7 l. The increase in energy absorption with temperature is not the same for all materials, however. For example, we!d 1 showed a much l
~-------~~----------------,
" WELD METAL {AX tAU ' I WELO METAL {CMf'U (.t1-!b1
~: .~* ::~%c~~~~;:r}~
8 : :; RtNC NUMB£:~
.'.()(')
'1
- , til, 4,
- IARADIAT() I:!WC"'
eAst:F
( A;I(!AL) i 1,
.:.:-,;-~)NIRRAD~A Tl [')I> *'""
I wee" t (6XlOLJ i I
,,> .:'25 ,_,., .. /
/
('ASt 4 -':
.1150
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- !30 1\.:..~ee~~- -::.. _.
751
-It *l*li:/O~/cm~
I T{MP£f<.G ~ >JRE FIG. 6-Charpy- V notch ductility of weld metals from several ringJ in unirradiatcd and J2(f'C irradiau:d conditiims at three temperawres. Unirradiated condition data trends{<lf base metals 3 and 4 from Fig. 6 are
!liven for reference.
OAGI0000608 00010
198 INFLUENCE OF RADIATION ON MATERIAL PROPERTIES JJl HAZ (AXIAL} HAZ (CMFL) Hlllbl 3,4 RING NS (SlOE Al 3A. 4A, 38, 48 RING N*ISIOE 240
- o. t1 UNIRRADIATED o o A v UNIRRAOIATED 300 - IRRADIATED 120"C~
- IRRADIATED 120*c*
HAl 3(A)"'
225 - .-- HAZ4(AI"'
-- 4{~ _ . - *-::: .. ......-
~-
__. . ....-~,..,..,.
160 150 15 f
- -tx~o2:0 11 fn,,l I tE~OIMeV)
"AXIAL TREND l 0 _,_ _:_______,__ _ _~---' ' - - - - ' - - --'----'*-____ _ j 0 ze 75 125 (*C! 25 125 !"C)
TEioiPERATUAE TEMPERATURE FIG. 7---Charpy- V notch ductility <Jf HAZ matcrials.fiYJrn Ring.' J and 4 in unirradiat<'d and i 20"C Irradiated conditions (axial and circumferential test onJ?ntations) at thne tenzperatur<'S. Data trmdsfor th,- base (parem) metals for tuHh conditions are also .vhown in th" lefi pand greater temperature effect than weld 2 (Fig. 6). Also for reasons unclear at this time:, the increas;:
in energy ab~orption with temperature wa~ much greater for the axial orientation than the CMFL orientation for some base and H.AZ materials. For example, compare the results for HAZ 3(A) and HAZ 4(A) (Fig. 7). Moreover. in some cases, such as HAZ 3(AI and HAZ 4(13). the CMFL orientation data for 125 versus 25°C form a common scatter band.
At 25'"C. the base material appears to have a higher energy absorption than its adjoining HAZ or the weld metals in general. In tum, the base metal on balance would appear to be the mos1 fracture-resistant component of the test weldments for a given orientation. Weld 6 was found t<'
have a notch ductility comparable to that of the base metal 4 (Side A) (Fig. 8), but this appear~
to be the exception rather than the norm. The axial and CMFL test orientations of the base and the HAZ materials describe a pronounced difference in notch ductility at 25°C <high and low.
respectively). This was not the ca~e for tlw two weld metals tested ( <26 J or 19 ft
- Ib). Also.
w 2<:>
t;LD MET:-:~I~L) (25"C TEST Sl o UNlFIRAOIATE:D
- IRFU.. OIATED i20"C
- Jx IC*2'J r.tt.;1<
(rt-lb)
~
0 15CJ
~
~
8 Q
"'z 1u w
. .J ...
75 r c.
I, I
~
0 * - - - ****** 1. * - - - * - * * - - - - - '
2 5 4
~lNG NUMPf.R F1G. 8-Charpy-V nouh ductility r~( tht* wdd deposits from seven (!ipe rings itl unirradiatd and 12/PC irradiated conditions (a.tial orientation, 250C,_' Iests). The hands at the lej; shm<* the ranRe of proper/i<'.l observed.
OAGI0000608 00011
HAWTI-lORNE ET AL ON NEUTRON IRRADIATION i99 r,;:-.,z
-* ~~~~-
L~.)U;..;._.)
.. : .*. ;.{~ ._. '* .. *-*
, :~ <*
- ,:: !I s ,a " ,o I
... l ........ ~-*-**-------~-
, IG. q ----Clrntpy- V 110/t.'h di~di!ity of ~n*ld h<!uJ-q{f(*-cf('{l ~-f*ne lnf!lvrf.a/.\from .-.,n*( n {/i{'f' rm_!1-: l.n Naftn;dia.tcd
.m,: I ~~0' (' inoJiatvd roJuhll~ms (o.riu! oricnfo1i-on, .?5" C li'.~h}. TJu:* umgc ~:l pn:r*erJic.~* uhJ*ervr'd _t:-n nve htJsc:
';*iii CIU) ~"U<'IHIS <ff<' <d:O.o :JU.'Wn
,,,,t,.c the witk hlriability :n cnt~rg_v ;lbsnrption kn the H.'\Zs in ihe axt<!l orientation ( 117 J or :'-;{)
!I * *b), with the lovn.:,t HAZ va!u.:: b(~ing just -.;ltghtly high(~r th;w til<~ k;weM value for the wclth
'L,* HAZ com b<: jLJdgcd ;.upcrior tu th~* weld in tht;. orientation: but bccaus(: of th<~ k't ori~*ntalion
'1:. iu;;ity o{ !he HAZs, rhi;. d,:x;:; 110! app..::ur t<> !;old in each cas~* for the C\Hl. ,wientati<.lrl
',,*:t,*c* thm i!w J,>wc<;t value of !he H:\Z .<{ Bi is mu..:h l<.>wa th::rl the trend h.tod t<.w the welds.
- '"' .:<:~*onliligly. rh,* l{>rmcr ._.,,uld be the: wu.k !ink ,,f the wehlm,:rll for !IK Cv!Fl. >>ri<:nt.!liurL
.':*(!\:*n:;th dt:tt~rminatinns for the irr;Hhatcd conditi<.'n ;u~; sunnnari;-ed in T:1bk 2 and ~u:;;.~ iliust!akd
- ,t J.. ,~ HL
\ :ry lHtic Jata c.catln ~~ observtd for <.~ach \lf the ~pecimr~n group~ eve-!! ihough !he gare secti{Jn~
- rt: cnmposed wholly or partly (>f w:::ld mc.:l<.ll. All 'PCC!men;; cxhib!tt'<i a pronounced dt~V;Hi<nl Yi.~!:f..!:'!.I.':.I AL
(!RRt,DIATED 120'C)
F.'AAf:.l
!} ------------~:. *. -**-****-******-----------.....1.
>I<; H)---* }'"ithlu::d k.>1silc :*tr~..*ngth!o t.*hso.'TV<'d H::th. <U.w! wuJ,*ir~*an~,f(*ro;Jid.l f('f.:l. (:fi/ 1JUdtion a*t:ld .'fJ<*Om<.n"i
'"~'if..>f.;.*d *:f 120* C f,-;* *-I _.. J(r:* n*cu1:._. E '.> 0.1 .1-:l.cV. Oat<-l Jrenr! i;~~n~.i.:: _(( ...,- ;!w u!drrodi:.U<*d ('-(.*ndifion f.~(>m
<r <~re shov.*n .f<*.-r n~j;~*;*NNY OAGI0000608 00012
HAWrHORNE ET AL. ON NEUTRON IRRADIATION 199
~
I RH ~ D D
o T r~u
- v 8, :i)n
§
'ee
!I
'2 a'
zS*' "*::.~.t ~(H.l \
- .:tX_ A *H>!t!G":: .:
40
~*o
+
4 6 RING NUMBER FIG. 9---Charpy- V notch ductility of weld heat-affected :one materials from seven pipe rings in unirradiated and 120"C irradiated conditions (axial orientation. 25°C tests). The range of properties observed for two base (parent) metals are also shown.
notice the wide variability in energy absorption for the HAZs in the axial orientation (117 J or 86 ft
The HAZ can be Judged superior to the weld in this orientation: but because of the test orientation sensitivity of the HAZs, this does not appear to hold in each case for the CMFL orientation.
Notice that the lowest value of the HAZ 3(B) is much lower than the trend band for the welds, and accordingly, the former could be the weak link of the weldment for the CMFL orientation.
lrradiation Condition-Tl'nsilt* Properties Strength determinations for the irradiated condition are summarized in Table 2 and are illustrated in Fig. 10.
Very little data scatter is observed for each of the specimen groups even though the gage sections were composed wholly or partly of weld metal. All specimens exhibited a pronounced elevation
~-~-~--~---~-- -- -------------------l WELD METAL 1 g5"C TESTS
,::, Y!EUJ I
iMPoll (IRRADIATED 120°C} A TENSILE
~ $<5tLiTSI~==~=
550 - 2 ~80
\YS.)/===== ----
----- ~ 40 I
275. . lJ .. IRRAO ----
i .
- (AXlAU (CMFU I 0~-~-:--*-~---------:----~--'-___]0 5 6 5 7 8 AlNG NUMB£A FIG. I0-- Yield and temile strengths obserl'ed wirh axial and circumferenTial test orifmtation weld specimens irradiated at 12rf'C ro - J x lOw nlcm2 , E > 0./ MeV. Data trend hands for the unirradimed condition from Fig. 9 are shown_/(Jr reference.
- OAGI0000608 00013
~-~-*- ~--~*.-:-'-'-* **.*'-'..0-' -~- ~ .*. *...*. .* .*..*****~****X*~ .. ~ ..... -:-:*'C*.~-::-..*lo..*~-*!o:. ~
-~ob:o***"*...,. ..... _. ., ......... ~"""---------~-*_....-1~* ..... *~~
- -~*~-./'...,.....,__. __ ..,_._....._.._ _____ .......... ~ --~.,..,._,.,._...._~
tv TABLE~~ ~~f>qsrirradiatinn tmsile pmrn:rtif'S J,*tall!itwlimH (w,*ld metal sr*ecimc>tJ'}, 0
............_. .. ~_..__._._. ........_._. ..__ 0 Yield Stnm;?th" Tensile Strength
- -*** *********** z-n Te>t hK'i t'Hlt~tll, r-Ten >pcrawr~, MP>l bi ~;~ !* MP* bi lttcTnn~nt, c
m Ring Ori~n1ati<m ~'C Specimen ~.:f. z
- ~----*--****--**-*************-*** .......................... ************--.-*-*** n m
5 ~Xi<Ji 2~ 5W23 586 x)/J 7'??. 104.7 0 5W25 SCIS 86.7 717 j04.0 -n
- n
{avg~ 1592> iX5,!'5i ~3. 7 (720: (104A) 16,7 :>
125 5W24" ~190 56~6 450 65,2 0 6 axj;,j 15 6W50 579 l:i4.0 71!'5 104,1 ~
6W5l 576 XHl 719 104,3 0
z (avgJ i57XJ 1~3.81 52,<l C71XJ (104,2) 14 g 0 125 IJW52' JW 55.1 441 63,9 z
~
7 CMFL 2.'5 7W7 646 9J.7 739 107_2 7Wx 638 <)2_1; 731 jl){i_2
~
m
~;:~vg.~ ifi42) I'IJ I l 53~3* 1736) jl(){'d) 17<) :n
)>:
L~5 7W9 401 5!\.2 -UO h.'A r-1J X CMFL 25 ~w~ 641 9,) 0 732 W6.2 :n
>IW9 651 <):\_() 751 109J) 0\)
(avg*~ 1646) i94J.Ii !7.,'. (742) '107,6) 19 4 m 125 fiW7 42S 62.1 468 67,9 :n m
(/J
0. 2'1, Offs~L stati<' ICS!>,
~-- lncn:3:,e t")Vt~r ul'tirr::Jdi.at('d condiri\m an~rage.
' Referenced to unirradiarnl ring n<>- 5 weld prnpertie' !CMPLL
,! Spcctmcn hh'fkt~ <Wit::.tdt~ Dl <':\;t<.'n~o.;otw.:h:f ~agt"~ h:nJ;rh <"lf J3.'+ nun.
0
)>
G>
0 0
0 0
(j) 0
,oo 0
0 0_..
HAWTHORNE ET AL. ON NEUTRON IRRADIATION 201 m yield strength. Spenmens ti*om Rings 5, 6, and 7 described a yie-ld strength elevatwn by irraJiation on the order of 205 \1Pa or 53%. For Ring 8. the elevation was much greater_ 283 MPa or 77'7o. Radi<ttion-induced elevations in tensile strength WtTc much less, being on the order of 90 to 120 MPa or l6':7o. (For weld metal 7, preirradiation condition properties were not available; properties of wdd metal 5 Isame orientationl were rdcrenced as .m alternative.)
Based on the tensile strength data, the radiation effect on the CMFL orientation wa~ greater than that of the axial orientation. SpeciHcally. tensile strength elevations for Welds 7 and 8 were 111 the range of 110 to 125 MPa while those for Welds 5 and 6 were in the range of 90 to !05 MPa. Postirradiation yield strengths for the CMFL orientation were much greater than those for the .1xia! orientation in each ca~c (Table :?).
for the composite (axial orientation) ~pccimen~. the point of final specimen separation was not Ulllsistcnt i(Jr Wdu 5 or for Wdd 6 specimens, One specimen of each failed at the midpoint of ihe gage length, that is. at the weld l'enter line; the second >pecimen failed at a point significantly displaced from the weld center line and inferred l'ailure in the HAZ. This behavior incon~istency was not mirrored in the apparent postirradiation strength level, perhaps because the strengths of
,_*v:lluation of the rchuivc load carrying capability nf individual wddment COllljX!llents was not pns~ible with the particular specimens available, lrrudiatiou Condition---Notch Dut'fility Properties lndividual C, test determinations arc included in Figs. 'i through 1) as tilled ,ymbo!s. Table 3
.-omparcs avefagc values for the irradiated versus unirraJiatcd conditions, Referring first to the 25°C data for the axial orientation or the weld deposits, the reductions in
!\*rcenrage reductions t<)r the bulk of the welds ranged lfom 41.5 to 43. 7%. The greatest reduction
"' energy, 'JO J, was observed for Weld 6, which also had the highest preirradiation energy
,thsorption. The lowest reduction was found for Weld 2, which exhibited the lowest prcirradiation
- .::,t value. Except for Weld 6. the spread in abl>oiute values for the axial orientation is considered
- plite ~mall: 76 versus 88 J.
1\t 125"C. postirradiation values tend to be higher than values for the 25cC te~ts. paralleling the p1c:irradiation energy trend with temperature. Reductions in energy ab>orption with irradiation
- ppear to be much higher at !25°C; but, percentage-wise. the reductions are about equal to those 11 the lower test temperature. Notice that the increase in energy absorption with temperature again
',;Heater fnr Weld I than Weld 2. On tl1c other hand. the difference in energy absorption between
'itc two test temperatures is les& for the irradiated condition than the unirradiatcd condition. For
,--,ample, Weld I data trends describe increases of 42 and 87 J 131 and M ft
- lb) for the i!Tadiated 1111! unirradiated condit~tms, respectively.
n1c CMR. oricntat1on wa>. evaluated with Weld 8 only. Because of stock limitations.
, 'rl*irradiation data could not be developed for this weld. Htlwever, the CMfL data for this weld
.1., match the axial orientation data for Weld 6 at both test temperatures.
Axial oricntation data developed for base metal 3 at 2YC indicate a percentage decrease in nngy ab~orption that i~ comparable to that described by the weld metals (46':"(: versus 41 to 49%).
I Itt~ energy decrease i:;. much greater at 125°C than at 25°C in terms of percentage reduction or
,i;*;olute reduction. For the CMFL orientation, however. the decreases in energy absorption are
'!'Proximately the same at both temperamres. In fact. the darn suggest a lc>.ser irradiation effect
- . q* the 12YC condition. An orientation depcndenn~ is clearly indicated in this case. for reasons
"":karat this timt'.
OAGI0000608 00015
~
!'\)
z T!
r cm
~
m 0
T!
~
0
~
0z iAI'lt.J: 3 ~Radiarion-induad changes in m*em.~t* C, l'nNg\* absmptims of rrwwri<>ls 2
- ~*****************
~
Haw. Pr\'irradia!ion Pm~irr<<dia!itJO Decrease Ml?lal *************-***-*************. *****
~
m Ring ~Sidd 1-' ft. lb }" li *lb ~J a.n
- lh % it.
~*
r-WELD Ml'TAL, 25C "t)
!54 1113 g] o.U 67 49.5 43.7 ei"tl 2 [30 95 7 7(, :ili.O 54 .~9.7 41.5 m 3 152 ll2.J 88 64.7 64 47.6 42A ~
m
(/)
0 4 1.<7 !00.7 78 ~7.3 59 43.4 43.!
)>
G> 5 1~9 ll7.3 85 62.7 74 54 6 46.6 0
0 6 18~ 136.7 95 70.0 90 66.7 48.8 0
0 O'l W~o<.D Mfi,\L, 125"C 0
,oo 241 177.7 !29 95.0 112 &1.7 46.5 0 2 158 !H;, 7 ()() 7J.O :;q 43.7 37.5 0
0_.
O'l BA.SI' METAL, 25T 3 A :?07 I)H! 111 SJ ..\ 94 69.7 45 6
HAWTHORNE ET AL ON NEUTRON IRRAOIAT10N 203
- ,.... ..,. - c .... o- o- *r. *...
- ::* -...,. ¢, c*<
.,. C*l..,. ..,. .,....,. "*-i..., .,...:;. .-""'. o:-*-:*t ::;: ""
n
..0
("!
X;
- n '"*
<:""-)
~. ce,
~:~ ('" 1::: ~: ~-~
,., r--: r-..: v-: *.6 .:;, 0:.
l ...* ("""/
,*, v-j ~ 1..0 ry
...c -*::-
CC, r-*
~
-~ 0
~-
~ -:::;
- . ,... -i C*
-=* or. "
- ~
- ~-
CC*
-i c-c-
.~.
~.
C' X *~ 0.0
-~~
,r,
('J w w
.r. ",.,
\{"* ...::
"' <"*I
- 8 C'l
"' *J
""'~ "" s ""c-s ;;:- ..c
~ ..0 - -- '""
<"'l C'
oc
"" ::::E ""':f "".;
<(
- il
,,., 0 V'l c ,_ce, 0.,. 0 c: ""*,,, ""* c.; r-: ~ 0 <r.
- ~ "' .£i *r; rl 8 <.""*)
-~ !'*
"' ::! *:.C <-
8
=. - *-*
~r:
(')
c l
..c OG ~. 0 <"'*I
~
OAGI0000608_00017
204 INFLUENCE OF RADIATION ON MATERIAL PROPERTIES Referring next to the HAZ, the percentage decrease in energy caused by irradiation (36.6 to 4o.3%) is on the order of that shown by the weld deposits for the axial orientation, but a much greater range in energy reductions is evident: 58 to I 05 1. Again the greater reductions appear associated with the higher preirradiation values. Significantly, postirradiation values for the HAZ are equal to or higher than weld deposit value~ (compare Fig. 9 versus Fig. 8). On the other hand, average HAZ energy levels are consistently lower (by 7 to 14 J) than the base metal in the irradiated condition.
Discussion The C.. notch ductility values reported here for the preirradiation and postirradiation conditions of the materials are indicative of high fracture resistance, but the radiation-induced reduction~
themselves were appreciable. Whether or not the materials have strong tendencies toward embrittlement saturation at much higher fluence accumulations is a key question to be addressed by the continuing program. Data suggesting that saturation tendencies may be found for the base metals do exist [3-5]. On the other hand, reductions of notch ductility to low levels by irradiation have been observed for some stainless steel welds. Specifically, C,. notch ductility values of ~ 20 J and dynamic fracture toughness values of ~-60 MPa
- m'*; have been found for AISI Type 308-16 submerged-arc welds after -*1.5 x 102 ' nf('m', E > 0.1 MeV. at 42T'C [6]. The higher irradiation temperature in this instance would be expected to reduce the ftuence effect through a self-annealing of the displacement damage.
The metallurgical cause of the difference in energy absorption versus test temperature trends for the axial versus CMFL orientation in some cases is not known. Where the two orientations exhibit about the same preirradiation energy absorption at 25°C. trend differences would not be expected. Scanning electron microscopy of fracture surfaces is planned to gain insight on the probable cause.
Referring to Table I, dissimilarities in composition among the base materials (and HAZs) are noted, especially in copper content. Copper is known to have a highly detrimental effect on the radiation resistance of low alloy steels (Ref. 7): an influence on radiation resistance has been observed for an exposure temperature of 288"C and temperatures approaching that of this study (120"C). For the weld deposits examined here, the range of copper contents i& small and would not be a factor in their radiation resistance~. For the welds and the base materials, the ranges of phosphorus content also are narrow: although. on balance. the phosphorus content of the base materials is higher than that of the welds. The HAZ data do not provide clear examples of ~l dependence of measured irradiation effect on material composition. As illustrated in Fig. 11, however, a retauonship of the absolute radiation-induced decrease to the preirradiation energy absorption level is apparent. The percentage decreases in energy absorption in contrast are about equal (~42%) tor all eleven HAZ materials. These observations. in tum. should simplify the estimating of notch ductility change for other, comparable materials.
Fracture toughness detem1inatons, using 0.4T-CT specimens and )-integral assessment proce-dures, are being developed for the materials for the unirradiated condition and will be reported in 1987 Further details of the present investigation are given in Ref 8 Conclusion Primary observations and conclusions drawn from the materials and test conditions of this investigation are as follows:
Preirradiation Condition
- Yield strengths of the weld and HAZ materials were about the same but were somewhat higher than the yield strengths of the base metals.
OAGI0000608 00018
HAWTHORNE ET AL. ON NEUTRON IRRADIATION 205 136 163 244 (Jl (ft-lb) ~-,--,--*-
h 80 i,- HAZ l~Jl 1r
- AXIAl.
I. ~
r 4 CMFL
]"o I, f)O
~-
- w 40:-
~ i
!~ r-~- :~
3 IS 20 0
~---!
IS
<I d
______ ___. ;. ________ ;___ ___j 0 1-ll ~ :
0 0
a:
60' 50 1-
- f ~_!.._- --*~ ~*-*-- ~--*---.;2 30
- 20 10 i
') -~*~ ..--.-- .. - ' - - '~*-----*-*___;___]
100 !20 140 i60 !80 ~f-!b)
C, ENERGY A9SORPTION AT 25°C (UNIRRAOIATED)
- c FIG. !!-Dependence of radiation-induced reduction in C. energy lJh.<orptioll on preirradiation C, enerf!.y c level.
n
- Tensile strengths of the ba~c metal and HAZ materials were !ower at 125 than at 25°C; yield strengths were approximately the same (within -- 55 MPa) at the two temperatures.
- The base metal and weld strengths did not exhibit a pronounced sensitivity to test orientation c
(axial versus circumferential).
a
- C, energy absorption tended to be higher at 125°C than 25"C.
- C, energy absorption of the base metal (at 25"C) was higher than the C.. energy absorption of y
tl 1he adjoining HAZ or the C,. energy absorption range for the weld metals.
- A pronounced difference in C energy absorption was observed between the axial oricntati1m (high) and the CMFL orientation (low) of base metal and HAZ materials but not the weld.
- Wide variability in energy absorption ( 117 J) was observed for the HAZ axial orientation.
n HAZ values were superior to weld values in this orientation, but HAZ values could be inferior to
!hose of the weld in the CMFL orientation, Irradiated Condition
- Yield strength elevations on the order of 53% were found for specimens spanning the weld metal (axial orientation); tensile strength elevations by comparison were on the order of 16%.
- For those tension specimens that spanned the weld joint (axial orientation), the number that broke in the weld metal was about equal to the number that broke in the HAZ.
- Yield strength levels in the CMFL orientation were greater than those for the axial orientation alter irradiation.
OAGI0000608 00019
206 INFLUENCE OF RADIATION ON MATERIAL PROPERTIES
- C, energy absorption reductions by irradiation were on the order of 42% for weld and HAZ materials at 25°C. Absolute energy reductions tended to be greater for a test temperature of !25cc.
- The magnitude of radiation-induced decrease in energy absorption appears related to the preirradiation energy level but not to composition.
- Postirradiation C,. and yield strength values are indicative of good fracture resistance for the fluence condition evaluated.
References
[I] Lippincott, E. P., Buffalo Lighl Vlater Reactor Calculation, Hanford Engineering Development Laboratory.
Richland, WA, 15 Nov. 1977.
[2] Lippincott, E. P., Kellogg. L. S., and McElroy, W. N .. "Evaluation of Neutron Exposure Condition' for the Buffalo Reactor," HEDL-SA-3101, Hanford Engineering* Development Laboratory. Richland.
WA, Aug. 1984.
[3] Steele, L E., Hawthorne, J. R., Serpan, Jr., C. Z., and Gray. Jr., R. A., "Notch Ductility Characteristic' of Irradiated AISI 304L and 347 Stainless Steels," Irradiation Effects on Reactor Structural Materials, Quarterly Progress Report, I August-31 October 1966. NRL Memorandum Report 1731, Naval Research Laboratory, Washington, DC, 15 Nov. 1%6, pp. 10-12.
[4] Steele, L. E., Hawthorne, J. R., and Serpan, Jr., C. Z., "Notch Ductility Characteristics of Irradiated AIS! 304L and 347 Stainless Steels After a High Neutron Exposure, irradiation Effects on Reactor Structural Materials, QuarU!rly Progress Report, 1 November !965-31 January 1966, NRL Memorandum Report 1676, Naval Resean::h Laboratory, Washington. DC, 15 Feb. 1966, pp. 23-26.
[5) Joseph, J. W., Jr., "Stress Relaxation in Stainless Steel During Irradiation," DP-369, E. I. duPont d~
Nemours & Co. Inc., Savannah River Laboratory, Aiken, SC, June l959.
{6] Hawthorne, J. R., "Fatigue and Fracture Resistance of Stainless Steel Weld Deposit> After Elevated-Temperature Irradiation,'* NRL Report 8451, Naval Research Laboratory, Washington, DC, 18 Nov.
1980.
[7) Hawthorne, J. R. , *'Chapter I0. lrradiation Embrittlement, Treatise oil Materials Science and Technolog.
Vol. 25, Embrittlemenr af Engineering Alloys, C. L. Briant and S. K. Bane~ji, Eds., Academic Press.
NY, !983, pp. 462-518.
[8] Hawthorne, J. R .. Menke, B. H., Awadalla, N. G., and O'Kula. K. R., Experimental Assessment of Notch Ductility and Ten~i!e Strength of Stainless Steel Weldments After 120"C Neutron Irradiation."
MEA-2133, Materials Engineering Associates, Inc., Lanham, MD, Dec. 19!.\5.
OAGI0000608 00020