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ORNL-4191 - the Molten Salt Energy Technologies Web Site

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RUPTURE TIME (hr)<br />

<strong>ORNL</strong> -DWG 67-7941<br />

Fig. 16.6. Comparutive Rupture Strains for Various Heats of Hastelloy N Irradiated and Tested at 1200'F.<br />

We removed a second set of Hastelloy N speci-<br />

mens in June 1967. The specimens removed from<br />

<strong>the</strong> core had been at temperature for 5500 ht and had<br />

accumulaied a peak <strong>the</strong>rmal dose of approximately<br />

4 i lo2') neutroms/ctn'. The core specimens were<br />

modified alloys containing approximately 0.5% Ti<br />

(heat 31545) and 0.5% Zr (heat 21554). A stringer<br />

of vessel specimens was also removed. These<br />

specimens had been exposed to <strong>the</strong> MSRE cell<br />

environment for about 11,000 hr and had accumulated<br />

a peak <strong>the</strong>rmal dose of about 3 x 10'' neutrons/cm2.<br />

The vessel specimens were made of <strong>the</strong> same heats<br />

used in constructing <strong>the</strong> MSRE.<br />

We have not completed <strong>the</strong> mechanical testing of<br />

<strong>the</strong>se m a t eria Is, but preliminary metallo graphic<br />

studies have been completed The primary concern<br />

with <strong>the</strong> vessel specimen was whe<strong>the</strong>r <strong>the</strong>y were<br />

being nitrided by <strong>the</strong> cell environment. Figure 16.7<br />

shows <strong>the</strong> surface of heat 5085. There is no evi-<br />

dence of^ nitriding, and <strong>the</strong> maximum depth of oxida-<br />

tion is about 0.003 in. The specimen taken from<br />

1 o3<br />

heat 5065 happened to be a weld made in construct-<br />

ing <strong>the</strong> stringer. This specimen is shown in Fig.<br />

16.8. The amount of surface oxidation is greater,<br />

but <strong>the</strong> depth of oxidation is still. small, and <strong>the</strong>re<br />

is no evidence of nitriding.<br />

Heat 21545 contained 0.5% Ti, arid our main con-<br />

cern was whe<strong>the</strong>r <strong>the</strong> alloy would corrode in <strong>the</strong><br />

fused salt environment. Figure 16.9 shows that<br />

<strong>the</strong>re is some slight surface reaction but no ex-<br />

tensive corrosion. Heat 21554 contained 0.5% Zr,<br />

and we were again concerned with <strong>the</strong> corrosion re-<br />

sistance. Figure 16.10 shows <strong>the</strong> surfaces of <strong>the</strong><br />

surveillance specimens of this heat and indicates<br />

<strong>the</strong> lack of significant corrosion.<br />

Thus we are encouraged by <strong>the</strong> observations that<br />

(1) <strong>the</strong> MSRE grades of Hastelloy N are not being<br />

oxidized at a high rate, and <strong>the</strong>re is no evidence of<br />

nitriding in <strong>the</strong> cell environmeni; and (2) <strong>the</strong> small<br />

zirconium and titanium additions that we are making<br />

to Hastelloy N do not appear detrimental.<br />

i<br />

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