ORIG. RUSSIAN: DEVELOPMENT OF HEAT-RESISTANT MG-BE ALLOYS AS A CLADDING MATERIAL FOR FUEL ELEMENTS

• Document Type: CREST
• Collection: General CIA Records
• Document Number (FOIA) /ESDN (CREST): CIA-RDP88-00904R000100100039-8
• Release Decision: RIPPUB
• Original Classification: U
• Document Page Count: 21
• Document Creation Date: December 22, 2016
• Document Release Date: August 12, 2009
• Sequence Number: 39
• Publication Date: May 1, 1964
• Content Type: STUDY

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In this case beryllium can be added into magnesium
at the temperatures near the boiling point of magnesium.
After melting and a subsequent rapid cooling of the alloy
to the temperature of casting, the alloy pouring takes pla-
ce in the air without any protective fluxes. The optimum
technology of the preparation of the alloy in closed cru-
cibles consists in melting of an alloy at 1000-1050?C and
casting it at 720-750?C with minimum time-delay at these
temperatures.
Thus the ingots of 15-20 kg containing 0.09-0.20 %
weight of beryllium can be obtained (M$ -4 alloy) /3/
Mg-Be alloys containing aluminium, calcium, silicon
and thorium as a third component were obtained by means of
this method. Investigations of effectiveness of introducing
beryllium into liquid magnesium from different alloys sho-
wed that the double Si-Be alloy is most acceptible in this
case.
Mg-Si-Be alloys thus obtained have a sufficient homo-
genity of the structure and stable grain-size at high tem-
peratures (Fig.I). Composition and some physical properties
of alloys are given in tables I and II.
The method of powder metallurgy is one of the most eco-
nomical methods of preparing the magnesium alloys with a
higher beryllium content. We have prepared heat-resistant
powder !dg-Be alloys with 2-10% and more percent of Be con-
tent (1Ik alloys) /3, 4/.
Magnesium powder of the 160-50 microns grain-size
with a surface oxidation less than 0.18-20% weight were used
as initial materials. The total content of impurities (wit-
hout oxyden) was not more than 0.2% weight.
The grain size of beryllium powder was-50, microns,
oxidation of the surface was 1.5+2% weight and general pu-
rity was better than 99,5%. The technological scheme common-
ly used consists of subsequent operations of the formation
and dry mixture of the charge, of cold briquetting and hot
extruding of the powder. The porosity of the specimens from
leg-Be alloys obtained by hot extrusion at the optimum condi-
tions is practically zero. Fig. 2 shows some specimens pre-
pared of Mg-Be alloys. The composition and some properties
of the alloys are given in tables I and K.
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Composition
of alloys % Be Si Al Th Fe Mn Ni Cu MgO Ca Zr
weight
pe o a..oy
from
EVE
0.5
-
0.01
- 0.04
-
0.001
0.005 0.2 -
to
0.3
32
ALE-3
0.04
0.5
-
- 0.01
0.001
0.001
0.005
MB--4
0.08-
0.7
-
- 0.01
0?001
0.001
0.005 - -
0.15
Mg-Al-
0.04
-
0.5
- 0.01
0.001
0.001
0.005 -
Flo
Mg-Th-
0.04
-
-
3 0.01
0.001
0.001
0.005 -
Mg-Ca-Zr-Be 0.04
-
-
- 0.01
0.001
0.001
0.005 - 0.5
-
0.5
2. MECHANICAL PROPERTIES OF MR-Be ALLOYS
Some properties of Mg--Si-Be alloys M E -3 9 M E -4 and powder
alloys HUE -2 and HUE -5 are given in table II.
The physical properties of the alloys are almost the same
as the properties of pure magnesium while the mechanical proper-
ties are different.
The mechanical properties of powder Mg-Be alloys in main
part depend upon the quantities of fine-dispersed magnesium oxi-
de on the surface of particles of the magnesium powder. The fine-
dispersed oxide phase in the magnesium matrix results in the
increase of the hardening and strengthness of alloys with the
increase of the testing temperature.
The addition of the fine-dispersed beryllium phase into the
magnesium metal-ceramic alloy results in the alloy additional
strength although it is accompanied by some decrease of plasti-
city of alloys
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The minimum plasticity of alloys at decreased rate of
deformation is observed at 300-350?C (Fig. 3). The plastici-
ty of alloys increases with the increase of the testing tem-
perature, but plasticity of magnesium metal-ceramic that does
not contain beryllium gradually decreases. This is evidently
connected with the increase of the plasticity of a magnesium
matrix which in case of ME alloys consists of a satura-
ted solid solution of beryllium in magnesium.
It is necessary to note that the use of the methods of
the powder metallurgy for preparing um Mg-Be alloys makes it
possible to introduce easily the fine-dispersed magnesium
oxide into the alloys and to improve their strength at the
temperatures much higher the permi ssablE operating temperatu-
res of usual alloys on magnesium base.
3. OXIDATION OF Mg-Be ALLOYS
The results of the tests of powder alloys in the air and
in technical carbon dioxide (0.1-0.2% H20) under pressure of
50 atm. showed that the Mg-Be alloys are corrosion resistant
at the temperature of 5800C for more than 5000 hours if the
beryllium content in alloys is equal to 2% or more (Fig. 4).
The qualitative tests of corrosion-resistance of ME alloys
were performed under these conditions during 12000 hours
(fig. 5).
The electronographic and alectronmicroscopic studies of
the oxide fi lms of MM alloys showed that their structure
and phase composition as well as those in the case of disti-
led alloys depend upon beryllium content in the alloy, ty-
pe of agressive agent, temperature and period of oxidation
/1, 2/. The essential feature of oxide film structure of
ME alloys as well as of oxide films of distilled alloys is
their double-layer structure which is especially distinct
when the alloys are oxidized in the carbon dioxide.
The rate of oxidation of Mg-Si-Be alloys in the air and
in the carbon dioxide (Fig. 4) slightly differs from the rate
of oxidation of double Mg-Be alloys with the same beryllium
content /2/. The alloys containing 0,08-0.15% of beryllium
are not destroyed being tested in the air and in the carbon
dioxide at 52000 for a period of more than 3000 hours. The
resistance of these alloys is higher than that of alloys of
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 SOME PHYSICAL AND MECHANICAL PROPERTIES OF MAGNESIUM AND MAG-
NESIUM- BERYLLIUM ALLOYS
TABLE II
Properties
Alloys
a. sical properties
density t C of
g:r/cm3 multing
at
?20C
ape- Coef-
cific fici-
elec- ent
tri c of li-
con- near
ducti-expan-
vity sion in
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Iii.b.cm
the in-
terval m
ep
of 200
x 106= ~on
I/degr.
m
Mechanical properties
20 0?C 300?C
400? C
I
Magnesium
1.738
650?I
4.70
25.8
18
9
9
34
5.4
2.3
46
1.8
1.4
52
0.8 0.4
60
0.4 -
1
78
-4
1.746
648?2
4.40
23.7
22
15
6
38
8.5
5
29
3.8
1.9
48
2 0.9
64
0.9 -
82
ME -3
1.742
648?2
4.40
23.6
20
13
8
36
7
4
36
2.9
1.7
58
1.3 0.7
69
0.8 -
90
LIME -2
1.741
649?1.5
4.85
23.0
26
19
5.2
40.5
12
7
14
8
4.8
16
5 3
27
2.8
49
LINE -5
1.743
649?1.5
4.90
22.8
24
19
5
40.5
11.5
7.9
12
7.5
5
15
5 3.1
26
3 -
49
Note: The samples tested are prepared hot extruded rods after their thermal treatment were tested.
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500? C
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"magnox" type /5/. The resistance of Mg-Si-Be alloys decrea-
ses under pressure of 50 atm. of the carbon dioxide as com-
pared with the alloy resistance under pressure of I atm. Ne-
vertheless ME -4 alloys are not destroyed under these condi-
tionR for 5000 hours at 520?C or less (Fig. 4). MgO and small
quantities of BeO are detected in oxidized films of y Mg-Si-
-Be alloys by electronographic methods.
The heat-resistance of the alloys that content Si, Al,
Ca, Zr and Th depends first of all upon the beryllium content.
Additions of Si, Al and Zr in quantities that are given in
the Table I have no appeciable effect upon the heat-resistan-
ce of the alloys, but Th addition decreases the heat-resis-
tance of the alloys.
Calcium additions slightly improve the heat-resistance
of alloys in the air but deteriorate the same in carbon dio-
xide.
The protective propertives of beryllium on oxidation
of magnesium-beryllium alloys are dharacterized by predomi-
nant diffusion of beryllium to the surface of oxidation and
formation of BeO layer in the lower layers of oxide films.
This layer is low-permeable for beryllium ions and practically
impermeable for Mg ions. The process of magnesium oxide re-
duction by beryllium plays an essential part in formation of
a sub layer.
The increase of a content of BeO in oxidized films re-
sults in improvement of their strength and cohesion to the
alloys.
Long time heat-resistance of Mg-Be alloys is determined
by beryllium content despite the fact that alloys of small
beryllium content (0.03-0.2%) show a lower rate of oxidation
at the initial oxidation stage than the alloys that have a
larger content of beryllium (Fig. 6). The value of concent-
ration of Be which is necessary to provide a long time heat-
-resistance of alloys substantially depends upon the techno-
logy of the preparing the alloy its structure and a quantity
of other alloying components in it. Thus the heat-resistance
of powder alloys is determined by the dispersion of berylli-
um component, its distribution and is achieved at a conside-
rably higher content of beryllium in an alloy than in alloys
with high dispersed beryllium prepared by a distillation met-
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hod.
Magnesium alloy corrosion resistance in different gases
depends to the great extent upon the humidity of these media.
This report deals with the study of the behaviour of va-
rious Mg-Be alloys at the temperatures of 500-580?C in the
air containing 10% of H2O and in thh carbon dioxide containing
6.5% of H20. Comparing the curves (Fig. in 7, 8) with those
(Fig. 4, 6) as well as with the results given in the work /2/,
one finds that the moisture has no appreciable effect upon the
alloy oxidation rate at the first stage of oxidation. However
destruction of Mg-Be alloys prepared by disstillation with
small amounts of beryllium begins after some time of oxida-
tion while at the same time only porosity and swellings appear
in some places of the alloys with a some higher beryllium
content. The porosity that appear under the same conditions
of oxidation in Mg-Be alloys prepared by powder matallurgy is
much smaller.
The alloys are corrosion-resistant for a long time in
damp gases and in the water vapour at 520?C.
Chemical analysis of samples of the alloys tested previo-
usly in the damp medium showed that the process of hydrogena-
tion of the alloys takes place during oxidation (Table III).
TABIE III
HYDROGEN CONTENT (CM3/100 G OF METAL) IN MAGNESIUM
AND Mg-Be ALLAYS
Magnesium or Mg-Be After oxidation in
alloy Before tbsting the air (10% H20)
for 750 hours, 580?C
Magnesium Mg-I 9 The samples were
destroyed
Distilled magnesium
(druse) 13 -"-
Distilled alloy
(0.27% of Be) 16 86
LIME -5 alloy 20 80
The harmful effect of water vapour upon Mg-Be alloys
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during oxidation in a damp air and carbon dioxide is probably
related to penetration of hydrogen ions formed during the
interaction between the water vapour and Mg and Be into the
lattice of the magnesium oxide and to its diffusion to the oxi-
de-metal boundary and into the metal /6, 8/.
The atomic hydrogen dissolved in an oxide film and in a
metal may reach the equilibrum with molecular hydrogen in po-
res, cracks or in other defects of the oxide film and the me-
tal since the equilibrum pressure of atomic hydrogen at con-
sidered temperatures and the molecular hydrogen pressure of
I atm is equal to 10-12 atm, the pressure of molecular hydro-
gen in this case may reach a high value and destroy the mate-
tial.
A favourable effect of beryllium on magnesium oxidation in
damp gas media is probably related to strengthening of oxide
films and their better cohesion to the metal and the decrease
of hydrogen penetration into them.
Therefore in case of Mg-Be alloys the atomic hydrogen
diffuses into the alloy in considerable quantities without
destroying oxide films and appears in molecular stare on the
defects of an alloy, and this results sometimes in swelling
of the alloy. In case of oxidation of pure magnesium and 1Mg-
Be alloys with a small beryllium content (^' 0.005%), the me-
tal-oxide film boundary or the film itself is the weakest
point of the system. These materials are oxidized with no
formation of protective films. A smaller effect of nydrogen
in powder Mg-Be alloys may be due to strengthening of these
alloys by particles of beryllium MgBe13 intermetallide and
oxide films.
Ignition temperature of pure magnesium in the air is be-
low its melting point and equals to 632-2.5?C ; and in pressu-
rized carbon dioxide it is equal to 6507750?C (Table 1V).
Ignition temperature of Mg-Be alloys both in the air
and the carbon dioxide rises considerably with the increase of
beryllium concentration.
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Alloy
lgnation temperature
Content of
bdtyllium in
air CO
60 atm
alloy (%)
2
-
6 32+2.5
650-750 Y)
0-09-0-15
650-3
720-750
2
66515
770-850x)
5
700?15
-"-
Mg-Be (distill.) 0.5-2 - "- -"-
Pure Mg
Mg-8i-Be
IIMB -2
HUB -5
faces of the materials makes them quite co4ipatible at tempera-
samples (Table Y). Preliminary oxidation of the contact sur-
ted materials and also upon the pressing force between the
Mg-Be alloys, upon oxidation level of contact surface, of tes-
low carbon steels depends upon the method of fabrication of
Mg-Be compatibility with Zr, Zr-Cu alloys, stainless and
of 580-600?C (Table Y).
tanium, carbon and uranium for long periods at the temperature
truction . The Mg-Be alloys are compatible with chromium, ti-
above the temperature of an eutectic formation without des -
2-5% weight the alloys resisted to a considerable overheating
destruction. However if the beryllium content in alloys reached
diate layers of low corrosion-resistance results in the alloy
ratures of 450-500?C since formation of eutectics and interme-
Mg-Be alloys are incompatible with Al,Zn,Cu,Ni at tempe-
MATERIALS
5. COMPATIBILITY OF Mg-Be ALLOYS WITH DIFFERENT
on but the total inflammation does not take place.
rized commercial carbon dioxide results in the alloy destructi-
Temperature at the beginning of intensitive oxidation.
Heating up to high temperature( above 700?) in the pressu-
tore s in the range of 500-550?C C.
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IGNITION TEMPERATURE OF ALLOYS
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Tested toC Time
of Alloys
material of test
test (hrs)
Zr,
Zr-Cu
450 Mg-Be, Mg-Si-Be Diffusion layers Corrosion destruction
up to 400 m in contact place o
t
(0.5-1% Cu) 580 650
1000
Steel
1 x18H9T
Degree of diffusion,
interaction
Note
1450 1650 Mg-Si,-8e, flMB-5 Interaction was not Initial pressing force
observed 15 - 20 kg/amt
520 650 Mg-Si,Be- Mg-Be Diffusion layer Initial pressing force
up to 300 m 15 - 20 k9/ MM
1000 TIME -5
450 1650 Mg-Be,Mg-Si-Be
520
200
Steel 3 580
Diffusion layer
15-20m.
Interaction was not Tablets of Zr-Cu alloy
observed were previously oxidized
Initial pressing force
1 kg/mm2
Diffusion layers Initial pressing force
0.5-1 mm
Interaction was
not observed
Diffusion layers
1 - 2mm
15 - 20 kg/m.m2
Initial2pressing force
1 kg/mm
Initial pressing force 15-20 kg/mm2.
Diffusion of Ni, Fe into Mg alloys
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Tested t"C -mime
material of of test test Alloys
450 1650 Mg-Be , Mg-Si-Be
U 520 1000 Mg-Be
Interaction was
not observed
Poor diffusion
interaction with
Sintering of tablets
Ti and Cr with Mg-Be
alloys takes place
Impoverishment of
Mg-Be h]loy in
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APPLICATION OF Mg-Be ALLOYS FOR COATING OF ROD
FUEL ELEMENTS
Tubes were extruded from ME and UMS alloys and used
afterwards for coating of uranium rods of fuel elements of
the heavy water has reactor (I, 9/. The fuel , elements of
5 mm outer diameter and 4000 mm long were coated with a
layer of Mg-Be alloy that was 0.5 mm thick. Rod fuel elements,
were tested for a long time in the air and in the static
carbon dioxide at the pressure of 50 atm (Table VI , Fig.9).
TABLE VI
Test conditions
Air Iatm. Commercial Carbon dioxide
Coating
material
50 atm. (humidity)
0.1% weight)
520?C
470?R 520?C
550?C
Mg-Si-Be alloy
ME -4
3000 hr''
11000 hrx 5000 hrx
2000 hrxx
Powder alloy HE -2
-
11000 hrx 11000 hrx
7000 hrxC
-"- IIME -5 2000 hrX 11000 hr 11000 hrx 11000 hr'
Tests are continued without coating destruction.
xX Time interval before coating destruction.
is clear from the data given in Table YI that powder
alloy HE -5 is the most corrosion-resistant material com-
pared with all other materials having been tested.
As the experiments showed fuel elements coated with
the alloy endure overheating in the air and also in the car-
bon dioxide without destruction up to the temperature of
650?C.
A decrease of the beryllium content in alloys during
long-time tests is observed due to burning out beryllium
during oxidation of alloys as well as to beryllium diffusion
into uranium and formation of intermetallide compound UBe1-,.
The thickness of the impoverished layer in distilled alloys
which have a high dispersed beryllium component reaches 50p
on the boundary alloy-carbon dioxide and-100 JI,t on the boun-
dary alloy-uranium interface (Fig.10). It was found out after
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testing for 1500 hours at 580?C. The impoverished layer in
both cases equals to 30-40 4/ after testing for 2500 hours
at 520?C.
The decrease of beryllium content is less observed in
powder alloys than in distilled alloys-It is explained first
of all by lower dispersion of beryllium in alloys. Tests of
fuel elements proved that the increase of roughness of the
protective coatings under static conditions in the air and
carbon dioxide at 550?C , after 7000-10000 hours does not
exceed 15-20 micron and is mainly due to corrosion proces-
ses on the coating surface.
Tensile tests of rod fuel elements showed that providing
the maximum cohesion of coating to an uranium core one may
considerably improve the plasticity of thin sheets of magne-
sium-beryllium layer. In this case the permissible elonga-
tion of coating, which is not followed by any breakdown in its
air-tightness, may reach 15-20% (Table YII) even at a low
rate of elongation.
TAKE YII
ULTIMATE DEFORMATION OF IIME -5 ALLOY COATING
Temperature of testing 250?C 30000 400?C 500?C
Ultimate deformation
of lIME -5 alloy 10-12% 16-17% 18-20% 20-25%
coating, 0.5 mm thick
Note: A deformation rate under the test was equal to
7.10-3 mm/min. The thermo-cyclic tests of the fuel
elements were carried out in order to determine the
strength of cohesion of the the coating with uranium,
the plasticity and corrosion resistance of the coating.
The tests were performed at temperatures 50Ju500?C.
It was proved that protective layers of ME -4, IIME -2,
111E -5 alloys stand 600-700 cycles without breakdown
of the hermeticity of the coating and without exfolia-
tion of the coating from the uranium core. The roughness
rises in this case up to 150,170)j and that is explained
primarily by different coefticients of linear expansion
of uranium and magnesium-beryllium alloys.
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340 1 r -
The radiation tests of the fuel elements in the reac-
tor in the pressurized flow of carbon dioxide of 60 atm in
the range of temperatures 150-'5800C and in the integral
neutron f lux of 2.102b n/sq. cm for 6000 hours showed that
the protective coatings fabricated from the developed mag-
nesium-beryllium alloys met the requirements of the coating
material used under these conditions.
No corrosion or mechanical destructions of the fuel
elements were observed,no failure in hermeticity.No changes
were detected in the alloy structure because of irradiation.
CONCLUSION
Heat-resistant Mg--Re alloys containing the amounts of
beryllium exceeding, the limit of solubility of beryllium
are developed. Investigations of the properties of these
alloys as a cladding material for fuel elements (long-time
heat-resistance, mechanical properties, ignition resistance,
compatibility with other materials, leak-tightness of fuel
elements coating under thereto-cyclic and reactor conditions)
were performed.
The Mg-Be alloys be used as a cladding material for
fuel elements of reactors cooled with carbon dioxide at the
coating surface temperature of 520-530?C.
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I. K.A. CI1HeJILHLIICOB, B.Y. I/IBaHOB, B.O. 3eJIeHCICYIg
AOKJIaA Ha 2-9 JKeHeBcico KOH( epeHLU 1 110 MMPH0My
MCH0 L3OBaHK1O aTOMHo 4 axepri i, p/2153 (1958).
2. B.E. 1/IBaHOB, B.O. 3e3IeHCICI4t-I, B.K., XopeHlco, Z.A. IleTenb-
ry3OB, B.B. MaTBLIeHxo, P.O. RojialIeHKO, X.O. KopHM-
eHKO, A.A. KopEoB. Aoi naA Ha KoH1J)epeHW1M rio peaic-
T0 Hb M MaTepMaJlaM, 3aJILii ypr (1962).
3. B.E. (IIBaHOB, B.O. 3eJleHCKLt9, C.14. 'aftep, I1. A. IIeTeJrbry-
30B. ABTOpCICOe CBLIAeTeJIbCTBO N2-K114, (1959), CCCP.
4. B.E. YIBaHoB, B.c. 3eJIeHCKM 1, C.M. (Dal~ep, B.Z. MaKcH-
McHK0, C.M. )K aHoB, B.Z. CaBUeHKO.
Aoit iaA Ha KoH(epeHI.HYI Ho TeXHOJIOPYILI HOBLDC peaK-
TopHUX MaTepMaJloB, IIpara (woAB, 1963 r. ).
5. R. Huddle, J. Laing, A. Jessup, E. Emley.
British patent No. 776649 (1953).
6. S. Gregg, W. Jepson, Journal Inst. Metals, 87,187
(1959)-
7. A. Popple. Journal of Nuclear Mater., v.8 No. 1(1963).
8. R. Huddle. Nuclear Engineering and Science Congress,
Cleveland (1955)-
9. II.1/1. XpMcTeHRO, II.A. IIeTpoB, B.A. MMTporioJIeBCKUH, K.A.CM-
HeJILHYII{oB, B.&. MBaHOB, B.1. 3e3leHcK1I#.
AorJIaA Ha 2-i4 leHeBCKo 1 rcoH(DepeHwmYI no M14PHOMY
McnoJlb3oBaHMjo aTOMHO9 alleprzx p/2053 (1958).
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Fig. I. Structure of hot-pressed rods of :4g-Be alloys:
a) M13 -4 alloy (x200); b) WE -2 alloy (x340).
Fig. 2. Outward view of articles made of Mg-Be alloys.
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100 200 300 400 500 600
MEMnEDArnYDA (?C)
0 - 1IMB -5 (Mg + 0.3% M90 + 5% Be) .
0 - Mg + 0.3i% MgO alloy
tested under low rated of tension (1.6% p/h)
Fig. 3. Relative elongation of the powder magnesium alloys
Fig. 4. Curves of oxidation of magnesium-beryllium alloys
in different gases (A P - increase in weight
mg/sq.cm t - hours).
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-1:8-
Fig. 5. Outward view of the samples after testing in the air
at the temperature of 580?C:
1 - non-alloying magnesium, 0.5 hrs. ;
2 - Mg-Si-Be alloy ( ME-4)9 400 hrs. (beginning of
6.1
decay) ;
3 - distilled Mg-Be alloy; 0.5% Be, 1000 hrs;
4 - LIME -0.5 alloy, 500 hrs. (beginning of decay);
5 - 1M6 -2 alloy, 12000 hrs. (beginning of decay) ;
6 - IIM6 -5 alloy, 12000 hrs.
Fig. 6. Oxidation of Mg-Be alloys in the air:
1-0.16% ; 2-0.98%; 3-2.69% Be.
Approved
 Approved For Release 2009/08/17: CIA-RDP88-00904R000100100039-8
340
6 A
qd r0.6 r
-I 9-
580C
300 400
BPEMQ, 4fCbl
Fig. 7. Oxidation of Mg-Be alloys in damp air.
A - distilled Mg-Be alloys; I - 0.03%; 2 - 0.16%;
3 - 0.27%;
4-0.7%Be
B - IIMB
alloys-, 5 - 2.5% Be; 6 - 5% Be.
Fig. 8. Oxidation of Mg-Be alloys in damp carbon dioxide:
I - 0.03% Be, 2 - 0.16% Be; 3 - 0.7% Be (distilled
alloys) ; 4 - 0.5% Be ; 5 - 1% Be; 6 - 5% Be ( IIMB
alloys).
Approved For Release 2009/08/17: CIA-RDP88-00904R000100100039-8
 Approved For Release 2009/08/17: CIA-RDP88-00904R000100100039-8
-20-
Fig. 9. The view of the surface of the fuel element samples
before and after testing in the carbon dioxide at
50 atm:
1 - coating before testing;
2 - coating of IIME -2 alloy, 550?C 7000 hrs;
3 - coating of IIME -2 alloy, 550?C 7000 hrs;
4 - coating of IIMS -5 alloy,550?C !I000 hrs.
(x2.7).
Fig. 10. Impoverishment in beryllium of the coating made of
distilled Mg-Be alloy, (1.32% Be) of the fuel ele-
ment after testing in C02 at 580?C, 500 hrs.
I - coating - gas limit;
2 - coating- uranium ( x 200 ) limit.
Approved For Release 2009/08/17: CIA-RDP88-00904R000100100039-8