ML12340A752

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Official Exhibit - NYSR00337-00-BD01 - Hawthorne, Et Al., Influence of Radiation on Material Properties, 13th International Symposium (Part Ii), ASTM 04-956000-35, Pp. 191-206
ML12340A752
Person / Time
Site: Indian Point  Entergy icon.png
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: ML12340A752 (20)
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Text

United States Nuclear Regulatory Commission Official Hearing Exhibit In the Matter of:

Entergy Nuclear Operations, Inc.

(Indian Point Nuclear Generating Units 2 and 3)

ASLBP #: 07-858-03-LR-BD01 Docket #: 05000247 l 05000286 Exhibit #:

Identified:

Admitted:

Withdrawn:

Rejected:

Stricken:

Other:

NYSR00337-00-BD01 10/15/2012 10/15/2012 NYSR00337 Revised: October 1, 2012 EXCERPT c.\\..\\.p.RREGlI(.q" l~';

0 3:

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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. Igata, University of Tokyo, editors ASTM Publication Code Number (PCN) 04-956000-35

~~l~ 1916 Race Street, Philadelphia, PA 19103 OAG 10000608_00001

Library of Congress Catalogil1g-in-Publication Data InHuence of radiation on material properties.

(ASTM special technical publication; 956~/

"ASTM publication code number (PCN) 04*956000*35."

Companion to: Radiation induced changes in microstructure (part {).

Includes bibliographies and index.

1. Materials~Effect of radiation on~ongresses.
r. Gamer, F. A.

II. Henager, C. H.

IlL Igata. N.

(Naohiro), 1926-IV. ASTM Committee E- \\0 on Nuclear Technology and Applications.

V. Radiation Induces changes ill microstructure.

VI. Series.

TA41S.6.J54 1987 620,1'1228 87~26992 ISBN 0*803\\-0963-6 Copyright ti;) by AMERICAN SOCIETY fOR TESTING AND MATERIALS 19R7 Library of Congress Catalog Card Number: 87-26992 NOTE The Socictyis not responsible. as,t body, for the statements and opinions advanced HI this publication.

Prin1{*~j 10 Ann Ath\\)I, Ml fh::{'J;:mVer J !fB7 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 1-10 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. Igata, 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 I), STP 955, and Influence of Radiation on Material Properties: 13th International

'ymposium (Part II), STP 956.

A88IJ61476A OAGI0000608 00003

J. Russell Hawthorne, I Blaine H. Menke, I Nabil G. Awadalla,2 and Kevin R. O'Kul(l~

Experimental.Assessments of Notch Ductility and Tensile Strength of Stainless Steel Weldments After 120°C Neutron Irradiation

REFERENCE:

Hawthom~. JR.. Menke. B. H.. Awadalla, N. G, ~nd O'Kula, K. R.,

o 'Experimental Assessments of Notch I)udility and Tensile Strength of Stainless Steel Weldments After 1.20"(.: Neutron Irradiation," In/114ma' (~IR<ldi(l/ion on Mawriall'mperlies: 13th IllfemariOlwl SI'wl'lH;lIm /purt 11). ItSTM STP 956. F. A. Gamer, C. H. Henag"'. Jr.. "fld N. Igala. Etls.,

Amcric<)1l S<x:icry for Testing and Matcrials, PhIladelphia, 19!i7. pp.

191~2()6.

AIlSTRACT: Th~ Charpy-V K*,.) propertIes oi American Iron,tnd Stccllnstitutc (AISp 300 SniCS

'Iainbs steel plate, weld, and weld hem.. affcttcd zolle (HAZ) materials from cOlllm~rcial pmduUi\\)n w<:ldtn<'nls in 40lHnm*diamclcr pipe ( I.!. 7*mm wall) were investigated in lInirmdiatcd and irradiated

<nd!ti"n~. Wdd and HAZ tensIle rmperti~s w~re,dso ilssc,:;cd in the tw,) conditions. The plates und wddlillcr wirc~ repr,'Scot diftbrcrH Meel melts: the welds were produced using the mulhp[IS, metal inert gas (MIG) process. Weldrncnt properties in two test orientatIons were cvaiuatcd. Specimens were irradiated in a light water cOQ!cdand HR),kratcd reiKtnr tu I x Hl'" nkm', E> OJ MeV.

using a omtrolkd lcmperature assembly. Specimen tests were performed <It 25 and 12S"C.

The radiation* induced reductions in C, encrgyabsorption at 25 Q C were about 42';'(* fllf the weld

<uldthc HAZ materials evaluated. A trcnd of energy increase wllh tempcr,lture was nhserve,l. The

~"n,,)milant dcvati,jfl in yidd strength was ahout 53%. The increase in tensile strength incolltrasl Wi!> only 1 (""';'. The p')Stirratliation yidd strength Pi' tilC ""lal t.;,( ori<'ntution in Ill<.' pipe was less than lilal of the..:ircumfcrelltial Icst nrj(~I)(ation.

Rcsulh for the HAZ indicate that this component may be the weaKest link m the wcldlTlclIl from a tr'Klmc re,istan(eVl~wp()inl.

KEY WOROS: s(ainles~ Sleds. weld dq)()sits. weld heat affectcd wne, radiation cmbri[lknwot.

nuclear irradiation, notch uuutlily, t~nsik strength. fracture n:sistuncc. 12()OC irradiation This study represents one phase of it large investigation into the fracture resistance of austenitic

~tainlcss steel we!drnents, both as-fabricated and after irradiation at 12()°C. The general objective was to explore notch ductHityand tensile strength changes prodUCed by a llllcm:e of-~ I x HV" nicm' *. /:; :> O. I MeV, asa precursor to,( study inVolving much higher tlucm;es at the same nominal tcmperalUre. The wtal inve~tigation is intended 10 develop a broad base of inform uti on on fracture toughness properties as well as notch ductility und tensile properties where research variables are test temperature. loading rate, neutron tluencc, and weldrnent component,tnat is.

base metal versus weld metal versus weld heat~affeeted zone (HAL).

, Rcs~al\\:h metallurgist and SCni()f engineer, respectively, Mat~rjab Engineering AS'K>,*iates. In<:.. 9700-[\\

Manin Luther King, Jr. Highway, Lanham. MD 20706*1837.

, Research staff engineer and research engineer respectively. E. 1. du Pont de Nemours & Co., Savannah River l..alxjriltory, P.O. [1m; A. Aiken. SC 2<)1\\08*001.

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 advanccdreactor concepts. such as breeder and fusion sy~tems 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 irradiationtetnperatures 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 195{)s, Materials The test materials were 1950 vintage. rolled and welded pipe sections having an outer diameter (00) of 406 mtn (l6 in) and a nominal wall thickness of 12.7 mm fO.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 metal 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 (ID) side to aid pre weld fitup.Figure I is an etched Cross section of one typical Weld. The joint was filled from Ihe 00 side using,everal weld passes; a root pass made from the 10 side was evident in most joints as well, The width of the deposit on the on surface was on the order of 1.5 mm (0.6 in.) and was LSmm (0.1 in.) on the IDsurface.. Based on weld bead patterns, the welds were not filled using the same sequence in aflcases, The chemical compositions of the base metals and the weld metals arc given in Table I. Note that the base compositions indicate different steel melts as their source; the weld metal compoSItions likewise infer that the weldfilJers were from different melts. Thus. the materials provide a basis for statistical evaluation of properties of weldments produced in the 1950, time frame Test Specimens Fun size Charpy-V C, specimens (ASTM Type A) and threaded-end tension specimens baving a gage diameter of 5.08 mmand a gage length of 20.3 mm were Ilsed for the notch ductility and strength determinations. respectively, Specimen blanks were cut in two orientations One group of specimens had their long dimension parallel to the original pipe axis and are identified here as "axial (Irientation specimens," The second group had their long dimension perpendicular to the pipe axis and tangential to the 00; these are termed "circumferential (CMFL) specimens." In all cm;es. the notch of the C,specimen was made perpendicular to the pipe ring surfaces (OD and 10).

FIG. J.. *-Elched cross section of Weld 5( 12. 7-mm base plate 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 [D 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.

[t 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 v and tension specimens was performed in the 2-MW Iight-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 +/- lSOC.

Cv HAZ SPECIMENS AXIAL 11.4mm CMFL

r-

~

---4~--==---

REF.

TENSILE HAZ SPECIMEN CMFL

~ ______ ~~~~~~

_. 2.9mm (0.115 in.)

5.0 mm REF

  • FUSION LINE OAGI0000608 00006

<0 Z

"TI r-C m Z

(")

m 0

"TI II 0 );

~

TABLE J~Base metal and weld compositions.

0 Z

Composition, wt%

0 Z

Base Meta)

(Side)

C Mn Si P

S Ni Cr Mo B

Co Ring Cu N°

~

.-1

.+++++++++++++++++++--------------_ **** _------------------------ -------

m BASE MEtAL A

0.079 1.60 0.79 0.031 0.Q11 9.63 18.79 0.41 0.001 0.11 II 0.29 0.047

~

B 0.035 1.56 0.58 0.024 0.016 9.19 18.44 0.25 0.002 0.10 0.24 0.036

-0

Xl A

0.079 1.50 0.34 0.031 0.024 9.65 18.27 0.45 0.002 0.13 2

0.42 0.043 0

-0 B

0052 1.41 0.38 0.031 0.025

&.50 19.40 0.39

<0.001 0.15 0042 0.036 m

Xl A

0.063 1.30 0.31 0.028 0.024 9.38 J859 0.40 0.001 0.12 3

0.38 0.044

-I iii B

O.fJ48 1.33 0.39 0.027 0.025 9.13 18.67 0.36 0.002 0.13 0.39 0.034 (J)

A 0.053 1.81 0.33 0.026 0.017 8.75 1&.97 0.35 0.002 0.11 B

0.083 1.75 074 0.033 0.017 9.60 18.88 0.46 0002 0.13 0

4 G>

0.28 0.033 0.32 0.043 A

004J l.39 0.67 n.026 n.024 9.64 18.88 052 0.002 0.12 B

0.080 1.25 0.32 0.026 0.016 10.00 19.05 0.44 0.001 0.13 0

5 0

0 0.28 0.035 0041 0.043 0

A 0.058 1.44 0.49 0.027 0.017 9.65 lQ.05 0.43 0.001 0.15 B

OJ146 1.46 0.66 0.026 0.024 SA8 18.88 0.22 0.00) 0.13 (j) 6 0

00 0.62 0.044 0.17 0.034 A

0.052 l.30 0.55 0.028 0.016 9.35 18.65 0.38 0.002 0.12 0

7 0

0.26 0.039 13 0.047 1.33 0.34 0.027 0.019 9.15 IS.50 0.21 0.001 O.OS 0

0 0.20 0037 R

A

{lOSS 130 0.40 0.030 0.026 8.72 19.05 0.41 0.002 n.16 0.45 0.U36 u

n (t7Q 1 7C, f\\.in finn n nl~

~ ~n

,r.)*hn.

(I Jii n ()fe, n <;j n 14 011.-11

r I ~~\\

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t'l 2 8 HAWTHORNE ET Al. ON NEUTRON IRRADIATION 195 OAGI0000608 00008

196 INFLUENCE OF RAOIATIONON MATERIAL PROPERTIES

(.... )

BASE METAL (AXIAL. 25*C TESTS)

>: 82'5 I-"

z: ll'..

on 350 27~ t

0. 1

(',0 YIELD

.,

  • TENSILE

,J" Tk2f1~ t**

2?
:~-~

02 4

~;

8 6

roo BASE METAL (CMFL, 25*C TESTS) r/"

~

I, 1

[)

61 oJ

{f.)

3 4

5 RIN(; NUIoISER Ikti) 160 120 ao

-,0 40 FIG. 3-lndividual yield and 'ensile strength delermiFUuions at 25"e for base metals from four pipe ring (axial and circw1iferential test orientations!. Results for 125°C tests of base metals from Ring 3 are ais, shown.

The target fluence was 1 x 1 020 n/em', E > O. I MeV. Actual ftuenees were detennined fwn iron and nickel dosimeter wires placed in the V-notches of theC, specimens and from 238l dosimeter capsules nested among the tension specimen gage sections. The average measurel specimen ftuence was 1.1 x 10m nlcm2* Neutron spectrumcaIcuJations indicate that the ftuence n.lcm2. E > 0.1 MeV. IS 2.91 times the ftuenee, nJcm2, E > I MeV If,2], The exposure equivalelJt in terms of displacements per atom (dpa). was 0.063 dpa (E > 1 MeV).

Results Unirradiated Condition~Tensile Properties The testrnatrix 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 for ttl base metal, the weld, and the weld HAZ materials, respectively.

~ 82p:

WELD METAL (25*C TESTS) c), LJ

'fIE1.D

.,. TENSILE

/8>'15:': MICe;"\\.,

z w

l' "I*e;

  • LIi" 5'5.0 215 i. 1 o

o c

.(1 B

o:~

{C\\II*'!

0'--' --,:,---':6--------'5 8

I T

  • HAZ (25'C TESTS)

SA~,f. Mf:'l':Al l(Mr-t~' *2 e;:

160 120

  • 2S"C I T(S"::

8D 4C

  • 5WE 3'-

iAC-j -"":\\-':£9C-)--3"'le-:--C;::-' ------' 0 R1N<'; NUM!lt><

FIG. 4-lndividual yield and tensile strength determinations at 2S'C for weld deposit.! and weld he, affected zone materials (axial and circum/erential test oriemations). The range of base metal valUes/rom Fi J is indicated/or comparison. Results of one 125"Ctest of the HAZ is aLm sho"m, OAGI0000608 00009

HAWTHORNE ET AL. ON NEUTRON IRRADIATION 197 10{)

l

.' __.... _.. ' __ * ~~~1g j

'.* 1"0'° 01' ~

{E.. OJMal{}

i

i:~-~-'C2~~---:,_':-,---:-!:?e {"Cl TEMPE:RATVRE BASE MnAL (CMfL) 1 (flllb)

~. 4 RING N' (SIDE AI

-', Z40 0, fJ UNjRNAOIATEP.

RING 3 tA!"'1 IRRAOIATEJlI20*C~.. /. fUNG 4!A}ioo.

/<;.>,/..

-J:

/"

/......

.,..../

'"'BASE' AX 1At, TRENO

~~~-~~~~--:'2~5-~'~'C~)~'O TEMPERATURE FIG. :' *.. Charpy-V I1QKh du(tililY 01 base I1Imerials from Ring 3 and RillK 4 in Jlllirr(uliamialld 120°C irradialed,'OIuli/iolls l.iXial (1l1d i'irt*llmprenliliIIe.Vloriemaliol1s) al thr(>e temperatures. Data Irendsfrom the

!efi panel illY' reprodl"'ni ill lil,- righl panel t{) simpllfv daw (*omparisolls.

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 aI'e 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 Dot change appreciably the yield strengths of either the base metals or the HAZ materials. Weld metal tension tests at 125°C were not peIfonned.

UnirmdiatedCondition-Notch Ductility Properties The test data for the unirradiated condition C,. specimens are shown graphically in Figs. 5 through 9 (see open symbols). All Cv specimens were tested on the same (hot eeIl) 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). The increase in energy absorption with temperature is lIot the same for all materials, however. For example, weld 1 showed a much WELO METAL iCMf'U l2RtNC NUMBER

.:.: -,; *~jNIRRAD~A 'T(DI>

j(t1-!l:I1

)AQ wee" l I (O;X\\OLJ :

. !150

<<A5~ 4 <

",",U.O>;:! i II!.XJAU :

FIG. 6~CharpyN notch ductility oj' weld metals from several ringJ in unirradiated and J 2(t'e irradiau:d colldifilms af three temperatures. Uninadiated cOlldition data trends for base metals J and 4 Irom Fig. 6 are given forrej'ereJIce.

OAGI0000608 00010

198 INFLUENCE OF RADIATION ON MATERIAL PROPERTIES jJ)

HAZ (AXIAL) 3.4 RING /lis (SlOE Al 0, '" UNIRRADIATED 300 -

IRRADIAtED 120*C~

SASE 3(A)"

SASE 4(A) 225 -

150 75

  • "';Jx~02:o"h.",l tE ~O.l NeV) 125

(*C!

TEMPERATURE HAZ (CMFLI 3A. 4A,38, 48 RING No/SlOE o

0 A

V UNIRRAOIATED IRRADIATED 120*C*

"AXIAL TREND!

HlIlb) 240

~I~ __

-"_"---~O 15 125 I*C)

TEMPERATURE FIG. 7--*Charpy-Y notch ductility "f HAZ materials/rom Ring., 3 and 4 in unitradiald atld i 20"C Irradiated condiUons (axial and circumferential lest orientaliolls) atthra leTllperatUT<'S. Data trmds for Ih,' base (parem) meWls for tu}{h conditiotJ." iJre also.vhown in the le!i panel.

greater temperature effect than weld 2 (Fig. 6). Also for reasons unclear at this (im..:, the increase in energy absorption with temperature was much greater for the axial orientation than the CMFL Qrientation for some base and HAZ materials. For example, compare the results for HAZ 3(A) and HAZ 4(A) (Fig. 7). Moreover, in.some cases, slich as HAZ 3(A) and HAZ 4(13), the CMFL orientation data for 125 versus 25'C form a wmmon Scatter band.

At 2ST, 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 mosj 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 appears 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 thc Case for tlR~ two weld metals tested <<26 J or 19 ft *lh). Also.

W~LD Mn:-:~I~L) n" (2S.C TESTS) o UN1FlRAOlAT UJ I (tHo)

IRFU.. QIATED 120"'C I c_. lx !c* 2'J r.ft.;I<

16.0

~

I flU. 8-Charpy'Y nouh due/ilir)' (~t' tht' wdddeposits from seven (iiI rings if I un irradiated and 12ITC irradiated (,onditions (a.tial orientation, 25OC.' lesls). The bands at rhe left shm" the rail?," of proper/ie.1 obserl'ed.

OAGI0000608 00011

HAWTHORNEET AL ON NEUTRON IRRADIATION i99 HAZ t~:X!A~J

-,. ~~~~-"""""""-""""

,IG; q --*.(*lrulpy"'i lIo/{'h dnuilify uf ~1'cldh{!uJ-qt/('i"H-'d ~"(Ine !l1(fJFfit't/.\\j{;,m SVI'(-a {'ttl:' rmf1::)n Nt'7rrrL"didtht

,m;: I~Yt(* irradiatvd rOlllhll>UIS ((i.rill! "ricJ1foliof?, }j'(' If'Sho). Tlu:' (ong<' ~4pn:rl("rJicy (}>J'ep,::td/>a: ?wo hd.'i(.:

'i,l)i'CaU"U{'lH!S <tn.' <d:-o s!u.'wn

','\\l,.e the widt~ hlriabiHty ;n el1t~rg} ;)bs\\)rption ti"J! the HAZ, in ihe ax,al odent;)tion (117 J or :';ti i! *'h). with thel,m'e,t HAZ v,t!ue b~~ing just "hghtlyhigh~~r thi:Hl!h,,~ k;wt~t value for the welds

'i.,' HA,l Gm b<.' judged ;.upcriof to ttl",,veld in tim. orientatiou: butbccaus(: of the {e,( orientation i I,.invjty of thc HAZ" [hi;. d,kS nol appciJr t,> hold in each e;Jse for the CMf'L nrienta!ior)

",';1,'(, thili iJw I,)wc<;t lialue of tht HAl:.~{ Bi l5 mu.,:hl<.>wLr th;m Ihe tf<,nd hand t(W the welds_

'jj,:.:<:"onIiiigly. the former could be the: wL;,k iink "hhe wchlm,;n! for rlK C:\\dFL nri<;nt:!lJm..

'U-,'ngth dmmminatiolls f<x the irr;H!iatcd conditi<Jl1 ;m; sLlrnm;lri/~d in T;lbk :2 and ~U:i;.' iliustrated
10.

\\ cry lIttku;)ta,call<.;[ IS observed for <.~;!(h {It Ih<: ~pt'cjmr~ll P{!UP~ eV(,B though the gafe sectj{m~

Tn: ()[Jlposed wholly or partly of w:::ld m<.:wl. All,peelfllen;; exhibtkd il pn)J)<)uneed t'kv;ttiml Yi_~!:f __ !::1.l:,.IA L ORRf,D!ATED I "Q'C)

*1<;

iO~*** rithl<md fci1silc ::"lr<'n.~:lhJ t.. hserh~d yvilh. <u.l~:dwJ(l i, *jn'an~.f(*rl*~Jilid.l rfS1. (:ri/IJUdtiOJJ :1,t:ld ~"p6.*£ml..'ns

,,~'i(/i~'daf 120;Ct.-;, '-/,,'
, }(r:'n':>:{n::, E '.>0.1 /'sI(~V. tJa({-l JreH(! l;~Uhi':;.i~... r ihe u!?h*rodJ~~u*d (XH7dilionf.~()m.

{I <ue s};ov,nJ.f<:"Tn~j;~'N*~N~<:*

OAGI0000608 00012

HAwrHORNE ET AL. ON NEUTRON IRRADIATION 199 IJlr--~~~

(25°C TESTS) ct"(

I f'iH ~g

~.-

oTr~u*

v 4

6 RING NUMBER FIG.9---Charpy-V notch dl/ctmry ojweld heat-ajJecled :one lnalerialJ/rom seven pipHings inunirradialed and I ;WoC irradiated conditions (axial orienlOtion. 25°C tests). The range of proper/ies observed for two base (par<,nt) m<'la/s are a/so shown.

notice the wide variability in energy abSQrption for the HAZs in the axial orientation (117 J or 86 ft* IbL with the lowest HAZ value being just slightly higher than fhe lowest value for the welds, The HAZ can be Judged superior to the weld in this orientation: but because of thc 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.

[rradiation Condition-Tensil,' 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 ~)r partly of weld metal. All specimens exhibited a pronounced elevation I----cc-~---~---. -

I WELD METAL

l iMP"ll (IRRADIATED 120*C) g5"C TESTS I::'

YIELD A:

TENSILE

-+ -.-.-,,;- -

~.~~-

I

~80 FIG. 10-- Yield and tensile strengths observed wilh axial and circlImferenTial test orienTathmwdd specimens irradiated aT !2(f'C 10 -] x lOW nlcm2, E > 0.1 MeV, Vata Trend bandsjor rhe IJnirradil1ledcondilion/rom Fig. 9 are shown.Il)r reference.

OAGI0000608 00013

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.j>..

TAflLE:>. "*{>(>.)"firmdiatiof1 tfllsile pmperti('S d<'l<'l'lIIill(JIh.>>lI' (w<fmeta/.I,[,ecimcn.l'j.

Test Tempcra(Ur~.

Ring Ofi~nlil!iNI "C

Specimen

........... ~----.

Hi;)i 2~

5W23 5W25 tavg) 125 5W24" 6

"xi;,1 25 6W50 6W51 (avgJ 125 IJW52' 7

CMFL 2,':'

7W7 7Wg t~vgJ 125 7W9 X

eMF!.

25

~W~

gW9 (avg) 125 fiW7

.* O. 2% ()i'fs~t. stati<' Icst,.

/'0 In:cre3:ie t")Vt~r ul'tlrriJdjjled condition average.

, RderelKcd W uninadiar.nl ring tWo 5 weld pn'p<,,*tit's(CMFI..L

,! Spl:(:iIHCnbt:(rki:~ {)nt:;.id{~ of (~xt<."nl.;{jIW,:t\\;'f gagt: h:ugrh <'!{ JJ.'+mm.

Yield Stnmglh" MP'l bi 5<<6

><5.0 SCIS St.U 15<12, Ix5.~i

.190 56.6 579 S4.n 576 x3.6 1578)

UD.g)

.lSI}

55.1 646 93.7 638 92.1; 1M2 )

19.3.n 401 5!\\.2 641 9.H) 651 95.0 (646) 194.0; 42fl 62.1 1m.'! t'mt~tll,

~;~ t, 53.7 52.<)

.53.3' MP.

722 71?

(720}

4.50 71B 719 I7IR) 441 739 731 (36)

  • 1.10 732 751 (742) 468 Tensile Strength ksi ItlcT~m~tH, 104.7 lH4.0

~;:~,

(104.4) 16.7 65.2 104.1 104.3 (104.2) 1411 63.9 107.2 106.2 dOO.7) 17.9 h2.4 W6.2 I09J)

'107.6) 194 h7.9 g

Z "f!

[;

m 5 m

o "f!

~

~

~

o z

~

~

m

v
!B 1J
p

~

m

?J rn

(/J

HAWTHORNE ET AL, ON NEUTRON IRRADIATION 201 In yield strength. SpecImens ti'om Rings 5, 6, and 7 described a yield strength elevation by llTaJiation 011 rhe order of 205\\lPa or 53%. For Ring 8. the devation was much greater, 283 MPa or 77(70. Radi,ltion-indllced elevations in tensilc strcngth WtTC much less, being on the order of 90 to 120 MPaor 16%. (For weld metal 7, preirradiation condition properties werc not avaihlhle; properties of weld metalS I same orientationl Were mfcrcnced as an alternative.)

Based on the tensile strength data, the radiation effe(.~t on the CMFL orientation was greater rhan that of the axialoriGntation. Specijkally. tensile strengrh eJevation~ for Welds 7 and 8 were III the rangc of 110 to 125 MPa while those for Welds 5 and 6 wcre in the. range of 90 to 105 MPa. Postirradiation yield strengths for the CMFL orientation wcre much greater than those for Ihe axial orientation in each case (Table 2).

h1r the comp()site (axial orientation) specimens. the point of final specimen separation was not u1Jlsbtcnri(l[ Weld 5 or for Wdd 6 specimens, Onc specimen of each failed at the midpoint of ille gage Icngth, that is. at the weld l'entcf !il1e; the second specimen failed at a point significantly displaced from the weld center line and inferred (,ailure in the HAZ. This behavior incon$istency was not mirrored in the apparent postirradiation strength level, perhaps because the,trengths of

ht weld and the HAZ in the unirradiated (;ontiltiOfl werc about the same hee Fig,}), Further
,'valuation of the rdative load carrying capability Df individual wddment mmlxlIlents was not PQs~ibJe with the particular specimens awilable, Imulialio/l Condirion-"Notch DlIdility Properties lndivid~lal C,. lest determinations,lrc included in Figs. :') through I) as tilled "ymho!s. Table 3

.,mnpares average values for the irradiated versus unirraJiated conditions, Referring first to the 25°C data for the ax ial orientation of the weld deposits, the reductions in

,'ncrgy absorption range from 54 to 67 J for al! hut two of the welds, Welds 5 and 6, Higher Il:ductions were recorded for the.latter in terms of ixllh absolute energy alld percentage reduction.

i'c'reenrage reductions t\\w the bulk of the welds ranged from 41.5 t043,7%. The greatest reduction ill energy, 90 J, was observed for Weld 6, which also had the highest preirradiation energy Ihsorption, The lowest reduction WaS found for Weld 2, which exhihited [he lowest preirradialion

"::'1 value. Except for Weld 6, the :>ptead in abMliutc values for the axial orientation is considered

'plite trnaU: 76 versus 88 J.

1\\1 125"C, postirradiation values tend to be higher than values for the 25°(' tests. paralleling the pn;irradi,llion energy trend with temperature. Reductions in energy ab>orption with irradiation t'pear lobe much higher aI125°C; but, percentage-wise, the reductions are about equal to those II the I.ower tcst temperature. Notice that the increase in energy absorption with temperature again

" "reater fllr WI:IJ I thun Wctd 2. On tile other hand. the difference in encrgy ahsorption between il(: two test temperatures is less Jor the irradiated condition than the unirradiated condition. For

. \\ample, Weld I data trends describe increases of 42 and 87 J (31 and M ft* Ib) for lheilTadiared 11111 unirradiated c()nditl,lI)~, rcspectively.

nleCMFL orientation was evaluated with Weld 8 only. Because of stock limitations, "rcirradiation data could not be dewloped for this weld. However, the CMFL data for this weld

.Iu match the axial orientation data for Weld 6 at both test temperatures.

i\\xial orientation data developed for base metal 3at 2YC indicate a percentage decrease in nlTgy ab~(}rption that b comparable to that described by the weld metals (46':"(, \\iersus 41 to 49%).

! he energy decrease is much greater at 125 QC than at 25°C in terms of percentage reduction or

,I;';olute reduction. For the CMFL orientation, however. the decre<lses ill energy absorption arc

'!'proximatdy the same m both temperaltlres. In fact, (he data suggest a lesser irradiation effect

.!f the Eye condition. An Qrientation depcndenct~ is clearly indicated in this case. for reasons

",,:iear at this lim".

OAGI0000608 00015

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TABLE J~Radi(t(i(Jn-indll('(';l changes in (JIWi1,~t' C, (*7I(*rgl* J./b,mptims of mawri,,!,

~~~~-~- *** ~~~".~~~>

---.~---........ ~

Ring 2

4 5

(,

2 3

Haw.

Ml;"lal

~Sidd A

Prt'itTa<iialion J"

ft* Ib 154 1133

[30 957 l52 112,'.!

In 100.7 159 117.3 185 136.7 241 177.7 158 11(;:7 107 1:)).0 Pm;~irrddia!jHn Decrease J"

Ii. II:>

al aft'lh

~-.-

WELD METAL, 25"C 87 mR 67 49.5 43.7 7(,

51i,0 54

.~9.7 41.5 88 M.7 64 47.6 42,4 78 57,3 59 43.4 43.!

85 62,7 74 546 46.6 95 70})

90 66,7 48.8 Wfo'l.!) Mn,\\L, 1 Z5°C

!29 95.0 112

&1.7 46.5 l)"

73.0 59 43.7 37.5 BASE Ml'TAl.. 25T In HJ.. \\

94 69.7 456

~

Z T!

E m

~

m

~

~

~

(5 z 2

~

~

g

~

"t)

~

'U m

t{

m

~,.....

<", C x:;

,t",

r',~

<:",,1 :-:1'

.-i; -,6 In

("'/

~;

0

~I"'l

~: '" {" 'I:::

X*

'e-

'Y),...

r..: r-..: v-:' -.0

,~,

("'.

(~

t' 1"'"

<r,... "" ""

r:

. ~ 0 r-: -:::; -. C*

,v:

~:..... ::::-

'c:;, -i C

t..:.

or-

~. V'.'

,\\~

Ir,

('1 W

,r,.

,*,t I{',

.,....:: 8 M

-r,

/.,.

(".J -. '2 "" S ;:--

E

~

c;:

.~

i"r'I, 0

if1

~ rr,

C?

~r:

-.c

'r:; ~--

1""1 8 l

..c OG

~. 0 I

~

~ '"

V') 00

...., *r.

(,-,I '-CJ.

<r, r' -~

.)C ""

c:-......,

(",.)

r':~

,....: 0-

~ oc":

-t

,.... 0

>6 ~

..c

04* f-Of;, '-i;,

e-X; s ;;: -

~ r-:-,

C*l

("'*t I/""

tt;...::

'*0 c:

HAWTHORNE ET AL ON NEUTRONIRRAOIAT10N 203 0- Ir,

-,;- ';Q c;:. c-

-C 1"'1

-j" '"

f-..,..

~" ~

'oC: c-

..c 1"'-. Co;

'~.-.

=. -

q. 0".

11;

'-C' -

.;,.z t"i H", ""1'

~,

C e-,

\\(,,:,..c

'...;' c-

"'. V":

.¢><X

~..c

.... : ~

.:00 'x:

,~, :!

X :x 0 r--~

<P,

(".~

W

" v,

~l -

N

~'

c l" ""

~:,~*I

,0
-

,-. ff',

-r-...,.... ;

c-

~.

'XI...::

Co..c OC 0

V'.'

t-f"'-~

.~ -

.c.. ",.

r,).-.r:

r'} "-

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 46.3%) is on the order of that shown by the weld deposits for the axial orientation. but a much greater range in energy reductions is evidcnt: 58 to 105 j. Again the greater reducti()fiS appear associated with the higher preilTadiation values. Significantly, postirradiation values for the HAl'.

are equal to or higher than weld deposit values (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 reductions 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 Ieveb 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'n/<:m'. E > 0.1 MeV. at 427"C {6]. The higher irradiation temperature in this instance would be expected to reduce the fluence effect through a self-annealing of the displacement damage.

The metallurgical cause of the difference in energyahsorption versus test temperature trends for the axial versus CMFL orientation in some cases is not known. Where the two orientations exhibit about the same preirradiationenergy 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 HAZ,) are noted, especially in copper content. Copper is kllown to have a highly detrimental effect on the radiation resistance of low alJoy 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 is small and would not bea factor in their radiation resistances. For the weItls 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,1 dependence of measured irradiation effect oil matedal composition. As illustrated in Fig. 11, however, a relationship of the absolute radiation-induced decrease to the preirradiation energy absorption level is apparent. The percentage decreases in energy absorption in contrast are about equaJ (~42%i tor alI eleven HAZ materials. These observations. in turn, should simplify the estimating of notch ductility change for other. comparable materials.

Fracture toughness detemlinatons, using O.4T"CT specimens and J-integral assessment proce*

dures, are being developed for the materials for the unirradiated condition and will be reported in 1987. Further detail, of the present investigation arc given in Ref 8 Conclusion Primary observations and conclusions drawn from the materials and test conditions of this investigation are as follows:

PreirradiatiOll 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

II Ir I.

I, IS IS

<I d

II o

\\-

'f

  • c c

n c

a y

It n

HAwrHORNE ET Al. ON NEUTRON IRRADIATION 205 136 163 244 (J)

(ft-lbJI::-'--'--'"

80i:~

HAZ l~J) 190

  • AXIAl.

i

  • CM~L f:i°r 1-w 40;'

~ 20 i30 o

I w

u

l i%J r~~

.c ____ :_~

__ ;.. c~~_c~;

    • c~ "'~~--'---! 0 (3 60 a:

50

~.-!..-...;..;....:....;..;..,..~ ~.-.- -

~-,-ft- __ ";2 30 20 10 i

) -~.~

.. ---~... -'--' ~'-'--~'-'-~

100

!20 140 i60 t80

~f-lbJ C, ENERGY AaSQRPT10N AT 25°c (UNIRRAOIATED)

FlG. II-Dependence of mdiation-inducedrt'duClion in C. energy ohxorption on preirradimion C, <'nt'r[!,y level.

  • Tensile strengths of the base 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 wcldstrengths did not exhibit a pronounced sensitivity to test orientation (axial versus circumferential).
  • C,cnergy <lhsorption 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

[he adjoining HAZ or thc C,. energy absorption range for the weld metals.

  • A pronounced difference inC energy absorption was observed between the axial orientati,lQ (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.

HAZ values wcre superior to weld values in thi!; orientation, but HAZ values could be inferior to those of the weldin the CMFL orientation.

Irradiated Condition

  • Yield strength elevations on the order of 53% were found for specimens spanning the weld IUclal (axial orientation); tensile strength elevations by comparison were on the order of 16%.
  • For those tcnsion specimens ibM spanned the weld joint (axial orientation), the number that broke in the weld metal waS about equal to the number that broke in the HAL
  • Yield strength levels in thc CMFL orientation were greater than those for the axial orientation

,titer irradiation.

OAGI0000608 00019

206 INFLUENCE OF RADIATION ON MATERIAL PROPERTIES

  • C, energy absorption reductions by.irradiation were on tbe order of 42% for weld and HAZ materials at 25°C. Absolute energy reductions tcnded to be greater for a test temperature of 125"e.
  • Tbe 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 fluencc condition evaluated.

References

[I] Lippincott, E. P., Buffalo Lighl j.t'ater Reactor Calculation, Hanford Engineering [)evelopmcntLaooratory Richland, WA, 15 Nov. 1911-

[2] Lippincott, E. P., Kellogg, L. S., and McElroy, W. N.. "Evaluation of Neutron Exposure Condition, for tbe Buffalo Rca<.:tor." HEDL-SA-3101. Hanford Engineering Development Laboratory, Richland.

WA, Aug. 1984.

[3} Steele, L E., Hawthorne, J. R.,Serpan, k, C. Z., and Gray.k, R. k, "Notcb Ductility Cnaracteristic, of Irradiated AISI304L 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. 1O-l2.

[4] Sleele, L E., Hawthome. l.R., and Serpan, Jr., C. Z., "Notch Ductility Characleristics of Irradiated AISI 304L and 347 Stainless Steels After a High Neutron Exposure," irradiation Effects on ReactQl Structural Materials, QuarU!rly ProgressRepori, 1 November /965-3/ January 1966, NRL Memorandum Report 1676, Naval Resean::h Laboratory, Washington, DC, 15 Feb. 1966, pp. 23-26.

[5} Joseph, J. W.* Jr., "Slress Relaxation in Stainless Steel During Irradiation," DP-369, E. L du Pont d~

Nemours & Co. Inc., Savannah River Laboratory, Aiken, SC, June 1959.

{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 10. Irradiation Embrittlement, ', Treatise on Materials,'kiet!<<(! and Techn%g".

Vol. 25, Embrittlemenr (If Engineering Alloys, C. L. Briant and S. K. Balle~ii, Eds., Academic Press.

NY, 1983, pp. 462-518.

[8] Hawthorne, J. R.. Menke, B. H., Awadalla, N. G., and O'Kula, K. R.* "Experimental Assessment of Notch Ductility and TenEile Strength of Stainless Steel Weldments After 120"C Neutron Irradiation."

MEA-2133, Materials Engineering Associates, Inc., Lanham, MD,Der: 1995.

OAGI0000608 00020

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