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C-84 - Reactors-Special Features
of Aircraft Reactors -

AEC RESEARCH AND DEVELOPMENT REPORT
M=3679 (23rd ed.)

APPROVED FOR PUBLIC RELEASE &
Name/Title: Leesa Laymance, ORNLTIO
Date: December 21, 2015

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ORNL~-2840

C=84 — Reactors—Special Features
of Aircraft Reactors
M=3679 (23rd ed.)

This document consists of }?gfiages.
Copy £ of 228 copies. Series A.

Contract No. W=7405=eng=26

ATRCRAFT NUCLEAR PROPULSION PROJECT
SEMIANNUAL PROGRESS REPORT

for Period Ending October 31, 1959

Date Issued

DEC £ 91359

OAK RIDGE NATIONAL LABORATORY
Oak Ridge, Tennessee
operated by
UNION CARBIDE CORPORATION

for the
U. S. ATOMIC ENERGY COMMLSSION

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B p———

Aging of Columbium=Zirconium Alloy Specimens ..cieeseencssss 47
Effects of Thermal-Stress Cycling on Structural Materials .. 50
ENEINERBING LMD HEAT 'TRANSEFER STUDIHS . asscstscwmabbovasss L
Molten Lithium Heat Transfer ....... paAAl DD AL AE aEEma -t 88 R . )
Thermal Properties of Columbium=Zirconium ALlOYS cevreees 5 s o
Dynamic Seal Research (.vsvvesescvcsas & e ex Bt B AN Gk 62
CHREMECS RESHIRCE ; s6 e svonemni@ 885 » o o i arprarons oG B - grear TR § . 64
Preparation of Berylllium Oxide ...veveescsee T o T 64
Beryllium Oxide Calecining Studies ...... v 36 DIREEGE DGRl St E 65
Sthdice of the Sintewability OFf Bl cewes snassoen s T T 68

Effects of Process Variables on Density ..... o adase b 69

Vacuum Sintering ..... spongd haae I I 70

gbmger of Blabter#z .oaset ot sens inbad i § 585k bas i Al . i g s
BeO—Cal Phase Studies ..iceveesteseann 5 Euai g 4@ ey A 5 & e
Analyses of Beryllium Oxide ..... Snssemensandalid h @ ¥ & R RERTSp——— "V
FRRMAETTON TEEETE .« x 05 m 6 «onveod 8 g 0 ase o ke W A B R s Fyqe 79
Irradiation of Moderator Materials in the ETR ......ccv0es . 7S
Creep and Stress Rupture Tests Under Irradiation ...sesseuss o
ADVANCED POWER PLANT STUDIES ....... iganslo D P LR HEGGHIOINE GD@ 4 87
Space Power Units .vevvenese sad el 4 bk ska kel @ DDA Q Gemimarad b 5 87
Vortiex Remchelr Expermenti® uoeess s i bommw T ymy LR AL, &7

PART 2. SHIEIDING

SHIEILDING THEORY ... 5 S e @D @ @ Sees—— T e I %
Monte Carlo Calculations of Response Function of Gamma-

Ray Scintillation Detectors eesveesaees e 00 i GEEE P EENES BT O 97
Monte Carlo Calculations of Dose Rates Inside a

Cylindrical Crew Compartment ....... b B btirsornd BAGDEE 66 awEDD i 104
A Monte Carlo Code for the Calculation of Deep

Penetrations of Gamma Rays ..vcvvverecenans PR, —— 105
Prediction of Thermal=Neutron Fluxes in the Bulk

Shielding Facility From Lid Tank Shielding Facility Data .. 106
LID TANK SHIEIDING FACTILITY .eeveccevnes PR PR TG 109
Effective Neutron Removal Cross Section for Zirconium ...... 109
Experimental Flux Depression and Other Corrections for

Gold Folls Exposed in Water ..c.se.. & 1 o o @ 2 Sanhas § prommie 111

BULE. SHEREDRHE HADTLITY canwsootaab wo b BT BERELY 38 0na b ba iS=2
S‘tainleSS Ste@l-UOQ ReaCtOI‘ (BSR"‘II) 5 %0 ¢ 0 QA BTSS0I PGS SRR 112
Dewign CHEISED § o fdee o oimesssa sl L A T R R 112
Critica—l Experiments e 4 8 8 P9 S B ® & 8 52 8% 5 &0 & B " O 0SS PO PN B S Y E s ll3
Recent Reactivity Calculations ...... R BTOES S 40§ S bk . 114
SPEBT-I TeStS " 8 0 8 B 8 S S S S0 TS SN G T OO O N b s 0 8 8 P E 115
The Model IV Gamma~Ray Spectrometer ..... chasvannne dasosvess . A3

Investigation of the Nonproportionality of Response of a
Sodium Iodide (Thallium~Activated) Scintillation Crystal

-to Galmn-a- Rays .......... ® % ¢ &5 " % " 88 a0 ® 8 5 9 0 B " B S 5SS B O 9 B R D B O PP llr7
Energy Spectra of Gamma Rays Associated with the Thermal

FiSSion OfU235 S & 9 & 8 9 0 " 6 ¢ 9 PP S ST B ® % 5 2 8 ¢ 8 8 8 & S F O S B B S B S = 119
Correction Factors for Foil-Activation Measurements of

Neutron Fluxes in Water and Graphite ...... BE © 5 T 5T T Egaks s 123
TOWE:R SHEIDING FACILITY « & 9 &« 8 P8 B0 * 8 9 9 v 95 0 & 0 4 00 8 BT P e SO ® & 8 3 129
Pulse-Height Spectra of Thermal~Neutron Capture Gamms

Rays in Various Materials .....ceceeess AR DB S PEE - AP 129
TSR~1II1 Experimental Shielding Program ....... v @ B asfat e d 136

Bea DiffrewenifiEl Bxpenimenis we:seb sosmendad tsssbbhice. L36
Skield Meekup EXperimerilos ou. oo 8% & 8§50 mmmeneiand buo & b b mne s ane 132

TOWER. S}HEIDINGREACTOR II " 688 6 00 RS2 B S EE OGP S OSSP S R s B 146

wsECH BR vii
AP PROJECT SEMIANNUAL PROGRESS REPORT

SUMMARY

Part 1. Materials Research and Engineering

1 Materisls Preparation and Fabrication Research

A correlation was found between hardness and oxygen content of co-
lumbium. The data demonstrated that increased hardness is a good 1Indi-
cation of increased oxygen content of columbium which does not contain
other comtaminants. When specimens with various oxygen contents were
heat treated together in a dynamic vacuum their various degrees of hard-
ness were retained. When heat treated together in a sealed evacuated
capsule they attained a uniform, intermediate hardness, probably as a
result of equalization of thelr oxygen content,.

The rate of oxygen absorption by columbium at pressures ranging
from 3 X 10=° to 5 X 10™% mm Hg and temperatures of 850, 1000, and 1200°C
were determined. At low oxygen pressures, the absorption resulted in
internal oxidation. A slight increase in the reactlon rate was observed
when the solubility limit of oxygen in columbium was approached. At the
higher pressures, visible oxide films caused the reaction rate to change
from linear to parabolic. The rate of contamination of columbium by air
at an equivalent oxygen pressure was lower by an order of magnitude than
that with pure oxygen, indicating that nitrogen msy significantly affect
the contamination.

Numerous columbium alloys were screened from the standpoint of
melting, fabricabllity, and compatibility with lithium at 1500°F. Based
upon the results, future alloy composition investigations will be con-
cerned with the columbium-molybdenum and columbium-zirconium binary and
columbium-molybdenum-zirconium ternary alloys, with the possible addition
of a scavenging element for initial oxygen removal.

Studies of a Cbo1% Zr alloy have indicated that the alloy responds
to aging heat treatments. In the experiments conducted to date, aging

viii

PE—

at 1500 and 1700°F has resulted in increased tensile strength and de-
creased ductility. The decreased ductility was particularly evident in
high-temperature tensile tests. Overaging phenomens were observed during
700°F heat treatments but not during 1500°F treatments for periods up to
750 hr. The increase in hardness of the alloy due to aging was in general
agreement with the tensile data.

Attempts to remove oxygen from yttrium by zone melting and solid-
state electrolysis were unsuccessful. These purification methods did,
however, remove fluorides. Operation of the yttrium metal pilot plant

and related work on yttrium were discontinued in May 1959.

2. Materials Compatibility Studies

The tensile strength and ductility of columbium containing small
amounts of oxygen were little effected by exposure of the metal to lithium
for 100 hr at 1500°F. The exposure to lithium caused the predicted
several mils of subsurface attack. When the oxygen concentration of the
columbium specimen exceeded 1100 ppm, however, marked losses of strength
and ductility accompanied the deep grain-boundary attack by lithium.

Weld-specimens of columbium and a Cb—1% Zr alloy were prepared with
the welding current varied from 125 to 55 amp, and the specimens were
then exposed to lithium at 1500°F for 100 hr. Postexposure bend duc-
tility, hardness, and corrosion resistance examinations indicated that
these properties of the welds were not affected by varying the welding
current. All the columbium welds were attacked by the lithium, but none
of the Cb-1% Zr alloy welds were attacked. The columbium welds were
ductile after the exposure to lithium, while, in contrast, the Cb—1% Zr
alloy welds had impaired room-temperature bend ductility.

Tests were run to determine the effect of the lithium-removal pro-
cedure on the hydrogen content of the tube walls of experimental loops
fabricated of columbium and a columbium-zirconium alloy in which lithium
had been circulated. OSpecimens treated for lithium removal 1in water and
in 10, 30, 50, and 100% alcohol were found to have increased a maximum

of only 60 ppm in hydrogen content.

s = & L
Carbon and nitrogen have been observed to transfer from type 316
stainless steel to columbium in a three-component system consisting of
columbium, sodium, and type 316 stainless steel when held at 1700°F for
1000 hr. The carbon and nitrogen formed brittle layers of CbC and CbsN
on the columbium. These layers cracked on bending, but the cracks did
not propagate through the base metal. When the temperature was decreased
to 1600°F, the total thickness of the layers decreased from 0.8 to 0.5
mil. The type 316 stainless steel specimens were unaffected when the
ratio of the stainless steel surface area to columbium surface area was
large (10:1), but, when this ratio was small (0.1:1), columbium trans-
ferred to the stainless steel surface and formed films containing Cb,
CbN, CbC, and CbsCs. When a Cb—1% Zr alloy was substituted for columbium
in the three-component system, similar results were observed.

The tensile strengths at 1700°F of Cb—1% Zr alloy specimens that
had been tested for 500 hr in a sodium—type 316 stainless steel system
at 1700°F were higher than the tensile strengths of specimens heated in
argon for the same time at the same temperature. The elongation observed
for both sets of specimens was extremely small and indicative of an age-
hardening effect.

The effect of prior heat {treatment on the corrosion resistance of
oxygen-contaminated Cb—1% Zr alloy was studied. When tested in an un~
homogeneized condition, the alloy was attacked by lithium at 1500°F when
the oxygen concentration of the allcy was as low as 900 ppm. After
having been heat treated in vacuum for 2 hr at 1300°C, no attack was
cbserved, even when the alloy contained 2300 ppm oxygen. Weld specimens
were not as sensitive to prior heat treatment as the bare material, and,
at oxygen concentrations in excess of 900 ppm, the amount of corrosion
in the weld material increased with increased oxygen concentration of
the alloy.

Screening tests have been run of various columbium alloys in static
lithium. Binary alloys of columbium with minor additions (0.5 to 5 wt
%) of cerium, lanthanum, hafnium, thorium, or Misch Metal showed no cor-

rosion when subjected to lithium at 1500°F for 100 hr. Ternary columbium
(e

alloys containing rhenium as a strengthening element likewise showed
no corrosion. Alloys in this category were Cb~Zr-Re and Cb-La-Re.

In screening tests of brazing alloys, zirconlum-base alloys showed
mass transfer of zirconium to the walls of the columbium test container
during corrosion tests in static lithium at 1700°F for 500 hr. Several
titanium-base alloys contalning iron and molybdenum cracked badly during
similar tests in a titanium container. A 70% Ti~14% Fe—10% V alloy did
not crack and showed no evidence of corrosion.

In a search for electrical-~insulating materials for use in molten
lithium systems, specimens of high-quality, hot-pressed BeO were ex@osed
to lithium at 1500 and 1700°F in tests of 100 and 500 hr duration. The
BeO specimens showed only limited corrosion resistance but were superior

to materials tested previously.

3. Welding and Brazing Studies

Fusion welding studies have been conducted on columbium and columbium-
zirconium alloys with the use of the inert-gas-shielded, tungsten-arc
process, Welds made on unalloyed columbium were found to exhibit ductile
behavior in room-temperature bend tests both before and after vacuum aging
at 1500°F for 100 hr. Negligible ductility was observed in room-
temperature and 400°F bend tests on aged samples of columbium~-zirconium
alloy welds. BSome of the alloy welds were ductile prior to aging and
some were not.

A welding procedure has been developed for welding l/fi-in.-thick
unalloyed columbium plate which incorporates fusing the root of a
beveled Joint with the inert-gas shielded, tungsten-~arc process and com-
pleting the weld with the inert-gas-shielded, metal-arc process.

A tube-to-tube sheet Jjoint has been designed for fabricating a
stainless steel-clad columbium radilator for transferring heat from liquid

metal to air. Materials are being prepared for feasibility studies.

4,  Mechanilcal Properties Investigations

Studies are being conducted to determine the effects of various

gaseous enviromments on the mechanical properties of columbium and

ouus 7 TR "
columbium-zirconium alloys at elevated temperatures. Creep tests have
been run in argon, nitrogen, hydrogen, and In environments containing
small amounts of water vapor and oxygen. The creep rate is lowered by
the presence of nitrogen compared with the creep rate in pure argon.
Thin nitride films are formed 1n nitrogen which are quite brittle and
may be a problem in fabrication. Although hydrogen and water wvapor do
not decrease the high-temperature creep ductility, they do cause con-
siderable loss in room~temperature ductility.

Reproducibility experiments were performed with the high-frequency
pulse-pump system in conclusion of the experimental study of the effect
on Inconel of thermsl-stress cycling in a fused-salt environment. Re-
sults of two out of three duplicate tests agreed reasonably well, and
in view of the sensitivity of the data to small variations in thermal.
stress amplitude, it 1s concluded that the results are within limits ex-
pected for repetitive fatigue-type measurements. Maximum thermal stresses
on the inside wall fibers have been recalculated using a more exact
equation which gives stress values 40 to 60% greater than those previ-
ously calculated. The data so corrected appear to fall in line with re-

sults of mechanical stress-cycling fatigue studies for low stress levels.

5. Heat Transfer Studies and Seal Development

Preliminary data on heat-transfer coefficients with molten lithium
flowing turbulently through a heated tube at approximately 700°F were
obtained. The data indicate reasonable agreement with the theoretical
and emplricel equations describing liquid metal heat transfer.

Measurements of the thermal conductivity of columbium-zirconium
alloys (1% Zr, nominal) up to 1000°F have been made with the use of =
longitudinal, comparison type of apparatus. The thermal conductivity of
the alloy lies between two recent sets of measurements for pure columbium,
but the precision of the measurements is not adequate to determine the
effects of composltlon varilations or ingot fabrication techniques.

Developmental work on a precision seal tester for use in dynamic

seal research was continued. DProposals for fabrication of precision

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minor cracks. A second test that will provide a longer exposure to

radiation and a greater number of thermal cycles is in progress.
Additional data were obtained on the reduction in time to rupture

of Inconel irradiated in the ORR. GSimilar experiments were performed on

type 304 stainless steel, and some evidence of in~pile shortening of time

to rupture was detectable. With INCR-8 no effect was apparent. An appa~

ratus is being developed for determining the effect of neutron irradi-

ation on the creep and stress rupture properties of columbium alloys.

8. Advanced Power Plant Studies

Design studies of reactor—turbine generator systems for auxiliary
power units in satellites have continued. Radiator studies have been
expanded to encompass manifold designs and meteorite protection. Calcu-
lations were done on the characteristics of epithermal Pbolling potassium
reactors, and a design study was made of a power unit utilizing a
potassium~-vapor cycle. Design work was started on equipment for studying
burnout heat fluxes in a boiling-potassium system.

Experiments on the effect of near-~laminar injection of gas into a
vortex tube away from the boundary layer have shown that no appreciable
increase in vortex strength occurs, as compared with turbulent injection.
However, it was possible in the laminar case to utilize uniform wall
bleed to reduce the exit mass flow by as much as a factor of 4 without
serious loss in local vorticity. Experiments indicated that at conditions
of practical interest the tangential Reynolds number mey be as high as
10° times the critical value, making it doubtful that conventional lami-

narization techniques will be campletely effective.

Part 2. Shielding

9. Shielding Theory

A Monte Carlo code which can be used for IBM-704 calculations of
the gamma~ray response functions of sodium icdide and xylene scintillation
detectors has been completed, and several cases have been run. For these

calculations the detector geometry can be either a right cylinder with

= W
conical end or a complete right cylinder; the source is restricted to a
monoenergetic source of arbitrarily chosen energy in the range from 0,005
to 10.0 Mev. The treatment of the primary incident radiation takes into
account Compton scattering, pair production, and the photoelectric effect;
however, secondary Bremsstrahlung and annihilation radiation will not be
considered until later. The particular Monte Carlo method uged is de-
signed for minimum statistical error in the so-called "Compton tail" of
the spectrum. The results of one calculation with this code are in
agreement with the results of calculations by Berger and Doggett and by
Miller et al.; however, as was expected because of the neglect of second-
ary radiation, all three cases give photofractions higher than those ob-
tained experimentally. Other calculations with this code have included
investigations of the effect of crystal size and the effect of including
exial wells of various depths in the crystal.

The Monte Carlo code for calculations of fast-neutron dose rates
inside a cylindrical crew compartment was completed, and preliminary
calculations have been made. The code, called the ABCD Code (for Air-
Borne Crew Dose), is designed to use as input the results from the Convair
D~35 Code, which computes the neutron flux distribution in air from a
unit point, monodirectional source. Preliminary calculations have been
made for a shield simulating the cylindrical crew compartment used at
the Tower Shielding Facility. Qualitative agreement between the calcu-~
lated results and experimental results is good.

The so-called "conditional" Monte Carlo technique was investigated
for possible application in a computing machine code to calculate deep
penetrations of gamma rays, but the results of test cases flucturated
badly about those of a moments-method calculation. It appears that more
mathematical work will have to be done on the problem.

The calculation to predict the thermal-neutron fluxes near the Bulk
Shielding Reactor on the basis of Lid Tank Shielding Facility data has
been reviewed, and the agreement between the predicted and meassured fluxes
is better than was previously reported. The predicted flux is now a

factor of 1.19 higher than the measured flux at a distance of 40 cm, and

& -
the predicted and measured fluxes are essentially in agreement at dis-

tances beyond 95 cn.

10. Lid Tank Shielding Facility

The effective removal cross section of zirconium has been determined
to be 2.36 £ 0.12 barns on the basis of thermal-neutron flux measurements
made beyond two slabs of zirconium (1.8 wt % hafnium), each 54 X 49 X 2
in. A mass attenuation coefficient (ZR/p) based upon the removal cross
section and a measured density of 6.54 g/cm3 s (.56 £ 008 ] % ilg=~
em?/g.

11. Bulk Shielding Facility

The fabrication of all components of the stainless steel-UO, core
(BSR-II) for the Bulk Shielding Facility has been completed, and initial
critical tests have been performed in the Pool Critical Assembly. The
critical mass of the initial loading was about 5.84 kg of U23%, Machine
calculations have been completed to determine the reactivity worth of
the control rods, the effect of the stainless steel near the core, and
the worth of the reactivity insertion device to be used in the tests at
the SPERT--I Facility of the National Reactor Testing Station. The core
and auxiliary equipment have now been assembled at the SPERT-I Facility,
where static tests preliminary to dynamic excursion tests have begun.

A1l components for the Model IV gamm-ray spectrometer have been
assembled with the exception of mounting the crystal housing on the
positioner. Testing of the housing for voids incurred during pouring
and solidification of the lead-lithium alloy is almost complete, and no
voids have been discovered. In the study to select a crystal for the
spectrometer, a recently developed "composite" sodium iodide (thallium-
activated) crystal, made by optically coupling two shorter crystals to-
gether, has been tested. Although the composite crystal has not been
completely evaluated, there was no evidence of the double peaks which
were characteristic of the conically ended crystal previocusly tested.
The experimental responses of the crystal are in good agreement with
responses calculated by the recently developed Monte Carlo code (see
Chap. 9).

xvi

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with published data.

Concurrent with the construction of the Tower Shielding Reactor II
(see Chap. 13) other equipment has been fabricated for use in the shield-
ing program at the Tower Shielding Facility. A TSR-II beam shield and a
detector collimator shield have been constructed for use in the "beam
differential" experiments. The TSR-II beam shield consists of a lead-
water shield containing a collimator opening through which a beam of
radiation from the TSR-I1I can he emitted. The detector collimator shield
is also a lead~water shield pierced by two collimator openings, either of
which can be used. With these two shields the radiation received at the
detector can be studied both as a function of the angle at which the
reactor beam is emitted and as a function of the angle at which the radi-
ation reaches the detector. For a second series of experiments, the
TSR-1II will be encased in a specigl uranium—lithium hydride shield de-~
signed by Pratt & Whitney Aircraft. The uranium is included as a shadow
shield which is removable. This shield has also been fabricated and will
be used in conjunction with the compartmentalized cylindrical crew shield

used in earlier experiments at the Tower Shielding Facility.

13. Tower Shielding Reactor II

As a result of the discovery that the water-reflected fuel annulus
of the TSR-II was subcritical, the spherical Internal reflector region
was redesigned to include a considerable amount of aluminum which would
increase the reactivity of the reactor. Part of this aluminum is in the
form of a spherical aluminum shell within which the control rods move.
The shell serves to restrict the water flow in this region sufficiently
to preclude the formation of dangerous alr voids. When the redesigned
control system was fabricated, a second set of critical experiments was

performed with the full-core geometry. In these experiments it was

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Y-28954

ONE INCH

Fig. 4.4. Photograph of Columbium Specimen 180 which Was Tested in
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Fig. 4.5. Photomicrograph of Section of Gage Length of Columbium
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of test was 52.7 hr. Etchant: HyO0-HF-HNO3—H,50,. 250X.

strengthening from a precipitate formed during the homogenelzation, an
isothermal dilatometry test was made. This technique has been used
with success on other alloys to detect second-phase formation. However,
the success of this technique depends upon a volume change caused by
the formation of the precipitate.

A rod, 1/4 in. in diameter and 2 in. long, was machined from
stock heving a nominal zirconium content of 1%. The dilatometer used
has an optical measuring system with a sensitivity of 5 X 1o=° in./in.
The specimen was homogeneized at 2900°F and annealed in the dilatometer
under vacuum at 1700°F for 265 hr. The maximum change in length which

was measured in the specimen was 0.0002 in. or 0.01%. This test points

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AT BATTELLE MEMORIAL INSTITUTE
403 { L
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Fig. 4.6. Comparison of Thermal Stress-Cycling and Mechanical

NUMBER OF CYCLES TQ FAILURE AT 4400°F

Stress-Cycling Fatigue Data for Inconel.

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PHOTO 34742

HEAT
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UNCLASSIFIED
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ture Profile Obtained in Study of Thermal

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Columbium-Zirconium Alloy Specimens.

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PHOTO 3498%

T
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2 8 9 10 il 12 13 19 20 21 22
OXIDE NUMBER

SURFACE AREA {m24)
W
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Fig. 6.1. Variations in Surface Area of
BeO Powders Obtained by Calcining Different
Batches of Beryllium Oxalate under the same
Conditions.

UNCLASSIFIED
PHOTO 34957
TEMPERATURE (°C)

200 400 600 800

| |

100

DIFFERENTIAL THERMAL ANALYSIS

s

WEIGHT CHANGE

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BeCpO4 HyO—e~BeO —-.__._"_'T.__ e g —
~400
o} 15 30 45 60 75 90
TIME (min)

Fig. 6.2. Differential Thermal Analysis and
Weight Change Data for the Calcining of BeC,0,4-3H,0
in the Preparation of BeO.
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YE 6141

Fig. 6.5. BeO Powder made by Calcining BeSO,4-XH,0. 22,700X.

UNCLASSIFIED
YE 6305

Fig. 6.6. Brush Beryllium Company's Special
High-Purity BeO Powder. 22,700X.

72
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UNCLASSIFIED
PHOTO 34980
100 4 . = — = — =

1
® OXIDE 18 PRESSED AT 20,000 psi 4
A OXIDE 18 PRESSED AT 10,000 psi
a0 | ¢ OXIDE 14 PRESSED AT 20,000 psi
m  OXIDE {4 PRESSED AT 10,000 psi
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R.T. 1000 1200 1400 1650 1650
{UNFIRED) TEMPERATURE {°C) i-hr SOAK

Fig. 6.7. Effect of Sintering Stages of Beryllium
Oxide on Densification.

the densities for the poorly sinterable pellets (oxide 14) come closer
together but are still influenced by the forming pressure.

After holding the oxides at temperature for 1 hr, the highly sinter=
able oxide had almost attained its maximum density as it reached 1650°C,
whereas the density of the poorly sinterable powder was increased con-
siderably during the soak period. It maybe seen, however, that the final
density of oxide 14 is still influenced by the forming pressure. This
information is preliminary and must be enlarged upon by further heat-
treatment experiments before conclusions or generalizations can be

made.

Th
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= BERYLLIUM OXIDE
= BERYLLIUM OXIDE

2 CALCIUM OXIDE

/A

Fig. 6.8.
1500°C. (a) Mixture
1500°C. (b) Mixture
1500°C. (c¢) Mixture
1500°C. (d) Mixture
from 1500°C.

8

34 30

of 65 mole
of 55 mole
of 60 mole
of 60 mole

26 22

% Be0O-35 mole
% BeO—45 mole
% BeO—40 mole
% BeO—40 mole

18 14 10

Phases Appearing in BeO—Ca0 Mixtures Heated to

% Ca0 quenched from
% Ca0 quenched from
% Ca0 gquenched from
% Ca0 slowly cooled
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UNCLASSIFIED
PHOTO 47864

‘
e - -
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Assembled Tube Burst Experiment for Irradiation in the ORR.

At the extreme left is the top plate of the exposure can. The capillary
pressure tubes from the specimens can be seen emerging from the furnaces.
The specimen ends at the bottom of the photograph face the pool-side face
of the reactor core when installed in the irradiation facility.

82

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RUPTURE TIME (hr)

Fig. 7.2. ©Stress vs Time to Rupture of Inconel
(Heat No. 1) Tested in Air at 1500°F at the MIR and

ORR and Out-of-pile.
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RMG 2715

Fig. 7.3. Transverse Sectlon in the Fracture Region of an Inconel
Tube~Burst Specimen Tested at 1500°F in Air at the MIR. The stress was
5000 psi and the time to rupture was 94 hr. (100X)

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Fig. 7.4. Transverse Section in the Fracture Region of an Inconel
Tube~-Burst Specimen Tested at 1500°F in Air at the MIR. The stress was
5000 psi and the time to rupture was 94 hr. (250X) Note the scalloped
edges of many of the grains along the major separations. Also note the
series of voids in the grain boundary above and to left of center prior
to separation.

84
UNCLASSIFIED

Fig. 7.5. Transverse Section in the Fracture Region of an Inconel Tube-
Burst Specimen Tested at 1500°F in Air Out-of-Pile.

The stress was 4000 psi
and the time to rupture was 800 hr. (100X).

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RMG 2718

Fig. 7.6.

Burst Specimen Tested at 1500°F in Air Out-of~Pile.
and the time to rupture was 800 hr. (250X)

exhibited more ductility at the grain boundaries than the specimen shown in
Fig. 8.5.

Transverse Section in the Fraction Region of an Inconel Tube-

The stress was 4000 psi
Note that this control specimen

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Fig. 8.1. Boundary-lLayer Injection Slit
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Fig. 8.6.

Variation of Ratio of

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Fig. 9.1. Absorption of 0.5-, 1.0-, and 2.0-Mev Gamma Rays in

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Fig. 9.2. Absorption of 2-Mev Gamma

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Fig. 9.3. Absorption of 2-Mev
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EXTERNAL DISTRIBUTION

AiResearch Manufacturing Company

Air Force Ballistic Missile Division
AFFR, Boeing, Seattle

AFPR, Boeing, Wichita

AFPR, Douglas, Long Beach

AFPR, Douglas, Santa Monica

AFPR, Lockheed, Marietta

AFPR, North American, Downey

Air Force Special Weapons Center

Air Research and Development Command (RDZN)
Air Technical Intelligence Center

ANP Project Office, Convair, Fort Worth
Albuquerque Operations Office

Argonne National Laboratory

Armed Forces Special Weapons Project, Washington

Army Ballistic Missile Agency

Army Rocket and Guided Missile Agency
Assistant Secretary of the Air Force, R&D
Atomic Energy Commission, Washington
Atomies International

Battelle Memorial Institute

Bettis Plant (WAPD)

Brookhaven National Laboratory

Bureau of Aeronautics

Bureau of Aeronautics General Representative
BAR, Aerojet~General, Azusa

BAR, Chance Vought, Dallas

BAR, Convair, San Diego

BAR, Grummsn Aircraft, Bethpage

BAR, Martin, Baltimore

Bureau of Yards and Docks

Chicago Operations Office

Chicago Patent Group

Director of Naval Intelligence

duPont Company, Aiken

Engineer Research and Development Laboratories
General Electric Company (ANPD)

General Electric Company, Richland
General Nuclear Engineering Corporation
Hartford Aircraft Reactors Area Office
Idaho Test Division (LARQO)

2t )

W

154~155. Knolls Atomic Power Laboratory
156. Lockland Aircraft Reactors Operations Office
157. Los Alamos Scientific Laboratory
158. Marquardt Aircraft Company
159, Martin Company
160. National Aeronautics and Space Administration, Cleveland
16l. National Aeronautics and Space Administration, Washington
162. National Bureau of Standards
163. Naval Air Development Center
164. Naval Air Material Center
165. Naval Air Turbine Test Station
166. Naval Research Laboratory
167. New York Operations Office
168. Nuclear Metals, Inc.
169. Oak Ridge Operations Office
170. Office of Naval Research
171. Office of the Chief of Naval Operations
172. Patent Branch, Washington
173-174. Phillips Petroleum Company (NRTS)
175=178. Pratt & Whitney Aircraft Division
179. Sandia Corporation
180~181l. School of Aviation Medicine
182. Sylvania-~Corning Nuclear Corporation
183. Technical Research Group
184. Thompson Products, Inc.
185. USAF Headquarters
186. USAF Project RAND
187. U. S. Naval Postgraduate School
188. U, S. Naval Radiological Defense Laboratory
189-190. University of California, Livermore
191-202. Wright Air Development Center
203=227. Technical Information Service Extension
228. Division of Research and Development, AEC, ORO

153
ORNL-528
ORNL=629
ORNL-768
ORNL-858
ORNL-919
ANP-60
ANP-65
ORNL-1154
ORNL~1170
ORNL-1227
ORNL-129
ORNL-1375
ORNT.~1439
ORNL-1515
ORNL~1556
ORNT.~1609
ORNL~-1649
ORNL~1692
ORNL-~1729
ORNL~1771
ORNL-1816
ORNL-1864
ORNL~1896
ORNL-1947
ORNIL,-2012
ORNL~-2061
ORNL~-2106
ORNL-2157
ORNL-2221
ORNL-2274
ORNL~2340
ORNI-2387
ORNL-2440
ORNL~2517
ORNL~-2599
ORNL~-2711

e~

Reports previously issued

Period
Period
== e ]
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period
Period

in this series are as follows:

Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending
Ending

November 30, 1949
February 28, 1950
May 31, 1950
August 31, 1950
Deecenber 10, 1950
M&rel 10, 1950
Juwe 10, 1951
September 10, 1951
Decenber L@, 195l
March 10, 1952
Jime 10, 1952
September 10, 1952
December 10, 1952
Marek 18, 1853
June 10, 1953
September 10, 1953
December 10, 1953
March 10, 1954
June 10, 1954
September 10, 1954
December 10, 1954
March 10, 1955
June 10, 1955
September 10, 1955
December 10, 1955
March 10, 1956
June 10, 1956
September 10, 1956
December 31, 1956
March 31, 1957
June 30, 1957
September 30, 1957
Degenber 31, 1395%7
March 31, 1958
September 30, 1958
March 31, 1959
155
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