ORNL-4191 - the Molten Salt Energy Technologies Web Site
ORNL-4191 - the Molten Salt Energy Technologies Web Site ORNL-4191 - the Molten Salt Energy Technologies Web Site
0.250in. It 4 0.250in. I- ORNL-DWG 67-14844 Fig. 18.17. Geometry of Diffusion Specimen. (at 1110"F, AFo for TiF, is -90 kcal per gramatom of F and AFOfor CrF, is -77 kcal per gramatom of F). Since protective films do not seem to form in fluoride systems, we would assume that both the chromium and the titanium will be removed as rapidly as these elements can diffuse. Our previous studies indicate that the corrosion rate of the standard alloy is acceptable, and the question of paramount importance is whether the addition of titanium will accelerate the corrosion rate. To answer this question we are measuring the rate of titanium diffusion in modified Hastelloy N. The following techniqueg is being used. Diffusion samples, 0.625-in.-diam cylinders (Fig. 18.17), were machined from small commercial heats of modified Hastelloy N (heat 66-548). They were heat treated 1 hr at 2400°F to establish a stable grain size and impurity distribution. The radioactive 44Ti isotope was deposited on the polished face of the sample using a micropipet. The isotope was supplied in an HF-HC1 acid solution; therefore, additions of NH40H were made after depositing the isotope to neutralize the solution. The sample was then heated in vacuum for 0.5 hr at 932°F to decompose the mixture to leave a thin layer of 44Ti. Each sample was given a diffusion anneal for appropriate times in flowing argon at precisely controlled temperatures. Sections were then taken on a lathe at 0,001-in. increments, and the activity of the turnings was measured using a single-channel gamma spectrometer with an NaI(T1) scintillation crystal detector. At lower diffusion anneal temperatures, a hand-grinding technique 'A. Glassner, The Thermodynamic Properties of the Oxides, Fluorides, and Chlorides to 250@K, ANL-5750. 'J. F. Murdock, Diffusion of Titanium-44 and Vana- dium-48 in Titanium, ORNL-3616 (June 1964). 232 10.' 5 TEMPERATURE 1250 1200 1150 It00 1000 Fig. 18.18. Hastelloy N. ORNL-DWG 67.11845 Diffusivity of Titanium in Modified was used to obtain smaller increments since the penetration distances were less. From a plot of the specific activity of each section against the square of the distance from the original interface, a value of titanium diffusivity was obtained for the diffusion anneal temperature of that specimen. To date we have determined the diffusivity of titanium at five temperatures from 2282 to 1922°F. The results of these measurements are shown in Fig. 18.18. Although the temperature range over which we have data is considerably higher than the proposed reactor operating temperature, we can compare the rates of titanium diffusion with that of chromium to get some ideas of the relative mobilities of the two constituents. At 2012°F the diffusion rate of chromium in an Ni-20% Cr alloy is reported to be approximately 8 x 10- l1 cm2/sec. lo From our data at 2012°F the diffusivity of titanium in modified Hastelloy N is 3.9 x lo-' cm '/set, which is a factor of 2 lower than for chromium at this temperature. Thus on a very rough basis there does not appear to be too much difference in the rate of diffusivity of these constituents at these higher temperatures. However, we cannot conclude at this lop. L. Gruzin and G. B. Federov, Dokl. Akad. Nauk SSSR 105, 264-67 (1955).
time what the effective diffusivities of titanium will be in the alloy at 1100 to 1400°F, because at these lower temperatures short-circuit diffusion paths become an important factor in the materia1 transport. Since we currently have no estimate of this latter contribution to the net diffusivity for titanium, we must extend our diffusion measure- ments to lower temperatures before concluding what the expected behavior would be under reactor operating condil ions. 18.8. HASTELLOY N-TELLURIUM COMPATIBILITY C. E. Sessions The compatibility of IJastelloy N with fission products in the MSRE is of concern, since the strength and ductility of the structural material could be reduced after prolonged exposure at ele- vated temperatures. Consideration as to which of the products imight be detrimental to the strength of the alloy revealed that tellurium was a poten- tially troublesome element. Tellurium is in the same periodic series as sulfur, a known detrimental element in nickel-base alloys. 'Yo evaluate the possible effects of tellurium on Hastelloy N, several tensile samples were vapor plated with tellurium and then heat treated in quartz capsules to allow interdiffusion of the tel- lurium with the alloy. Also, several samples were 233 vapor coated with tellurium and then coated with an outer layer of pure nickel in order to reduce the vaporization of the tellurium during subsequent heat treatments. After heat treatment of the coated samples, the specimens were tensile tested at either room tem- perature or 1200°F using a strain rate of 0 05 min-'. Table 18.4 lists the test conditions and results for 12 samples of Ilastelloy N. No effect of the tellurium coating on the ductility of Hastel- loy N was found at either test temperature. At 1200"F, the ductility following the various treat- ments ranged from 20 to 34% elongation, which is within the range normally obtained in the ab- sence of tellurium. At room temperature the duc- tility was in the range 52 to 57%, which again is normal. Metallographic examination of the specimens was made after testing to evaluate the interaction of tellurium with Hastelloy N. A representative area on the shoulder of one sample is shown in Fig. 18 19. Irregular surface protuberances are evident in a localized region of the edge of the tIastelloy N. 'The gray phase around the protu- berances is tellurium metal that remained on the sample after mechanical testing in air at room temperature. The roughness of the Hastelloy N specimens resulted from corrosive interaction of the vapor or liquid tellurium during the heat treat- ment. At higher magnifications it is evident that a slight amount of grain-boundary penetration of the tellurium into the Hastelloy N had taken place. Table 18.4. Tensile Properties of Tellurium-Hastelloy N Compatibility Studies" Maximum Sample Coating Anne a ling Technique Temperature (OF) Tellurium in 2012 24 7 5 capsule with 2012 24 1200 spec iinen 2012 150 75 Anne a ling Test Yield T ota 1 Time Tempera turf Strength Elongation (hr) (OF) (psi) (%) 2012 150 1200 Vapor coated with 1652 100 75 tellurium and 1652 100 1200 nickel Vapor coated with 1472 100 75 tellurium 1472 100 1200 -~ aTested at a strain rate of 0.05 minC1 49,100 31,300 49,800 37,000 53,2 00 36,700 52,800 40.500 57 22 57 20 52 27 54 34
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0.250in. It<br />
4 0.250in. I-<br />
<strong>ORNL</strong>-DWG 67-14844<br />
Fig. 18.17. Geometry of Diffusion Specimen.<br />
(at 1110"F, AFo for TiF, is -90 kcal per gramatom<br />
of F and AFOfor CrF, is -77 kcal per gramatom<br />
of F). Since protective films do not seem<br />
to form in fluoride systems, we would assume that<br />
both <strong>the</strong> chromium and <strong>the</strong> titanium will be removed<br />
as rapidly as <strong>the</strong>se elements can diffuse.<br />
Our previous studies indicate that <strong>the</strong> corrosion<br />
rate of <strong>the</strong> standard alloy is acceptable, and <strong>the</strong><br />
question of paramount importance is whe<strong>the</strong>r <strong>the</strong><br />
addition of titanium will accelerate <strong>the</strong> corrosion<br />
rate.<br />
To answer this question we are measuring <strong>the</strong><br />
rate of titanium diffusion in modified Hastelloy N.<br />
The following techniqueg is being used. Diffusion<br />
samples, 0.625-in.-diam cylinders (Fig.<br />
18.17), were machined from small commercial heats<br />
of modified Hastelloy N (heat 66-548). They were<br />
heat treated 1 hr at 2400°F to establish a stable<br />
grain size and impurity distribution. The radioactive<br />
44Ti isotope was deposited on <strong>the</strong> polished<br />
face of <strong>the</strong> sample using a micropipet. The isotope<br />
was supplied in an HF-HC1 acid solution;<br />
<strong>the</strong>refore, additions of NH40H were made after<br />
depositing <strong>the</strong> isotope to neutralize <strong>the</strong> solution.<br />
The sample was <strong>the</strong>n heated in vacuum for 0.5<br />
hr at 932°F to decompose <strong>the</strong> mixture to leave<br />
a thin layer of 44Ti.<br />
Each sample was given a diffusion anneal for<br />
appropriate times in flowing argon at precisely<br />
controlled temperatures. Sections were <strong>the</strong>n<br />
taken on a la<strong>the</strong> at 0,001-in. increments, and <strong>the</strong><br />
activity of <strong>the</strong> turnings was measured using a<br />
single-channel gamma spectrometer with an NaI(T1)<br />
scintillation crystal detector. At lower diffusion<br />
anneal temperatures, a hand-grinding technique<br />
'A. Glassner, The Thermodynamic Properties of <strong>the</strong><br />
Oxides, Fluorides, and Chlorides to 250@K, ANL-5750.<br />
'J. F. Murdock, Diffusion of Titanium-44 and Vana-<br />
dium-48 in Titanium, <strong>ORNL</strong>-3616 (June 1964).<br />
232<br />
10.'<br />
5<br />
TEMPERATURE<br />
1250 1200 1150 It00 1000<br />
Fig. 18.18.<br />
Hastelloy N.<br />
<strong>ORNL</strong>-DWG 67.11845<br />
Diffusivity of Titanium in Modified<br />
was used to obtain smaller increments since <strong>the</strong><br />
penetration distances were less. From a plot of<br />
<strong>the</strong> specific activity of each section against <strong>the</strong><br />
square of <strong>the</strong> distance from <strong>the</strong> original interface,<br />
a value of titanium diffusivity was obtained for<br />
<strong>the</strong> diffusion anneal temperature of that specimen.<br />
To date we have determined <strong>the</strong> diffusivity of<br />
titanium at five temperatures from 2282 to 1922°F.<br />
The results of <strong>the</strong>se measurements are shown in<br />
Fig. 18.18. Although <strong>the</strong> temperature range over<br />
which we have data is considerably higher than<br />
<strong>the</strong> proposed reactor operating temperature, we<br />
can compare <strong>the</strong> rates of titanium diffusion with<br />
that of chromium to get some ideas of <strong>the</strong> relative<br />
mobilities of <strong>the</strong> two constituents. At<br />
2012°F <strong>the</strong> diffusion rate of chromium in an Ni-20%<br />
Cr alloy is reported to be approximately 8 x 10- l1<br />
cm2/sec. lo From our data at 2012°F <strong>the</strong> diffusivity<br />
of titanium in modified Hastelloy N is 3.9 x<br />
lo-' cm '/set, which is a factor of 2 lower than<br />
for chromium at this temperature.<br />
Thus on a very rough basis <strong>the</strong>re does not appear<br />
to be too much difference in <strong>the</strong> rate of diffusivity<br />
of <strong>the</strong>se constituents at <strong>the</strong>se higher temperatures.<br />
However, we cannot conclude at this<br />
lop. L. Gruzin and G. B. Federov, Dokl. Akad. Nauk<br />
SSSR 105, 264-67 (1955).