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
19.1. BRAZING OF GRAPHITE TO HASTELLOY N W. J. Werner ra phite-to- Studies were continued to develop methods for brazing large graphite pipes to Hastelloy N. At the present time, three different joint designs are being tested for circumventing the differential thermal expansion problem associated with joining the two materials. Concurrently, two different brasing techniques are under development for joining graphite to graphite and to Hastelloy N. In addition to wettability and flowability of the brazing alloy on graphite, the brazing technique development takes under consideration the application-oriented problems of service temperature, joint strength, compatibility with the reactor environment, and braze stability under irradiation in neutron fluxes Joint Design The first joint design, which has been reported previously,' is based on the incorporation of a transition material between the graphite and Hastelloy N that has an expansion coefficient between those of the two materials. Molybdenum and tungsten are two applicable materials, and, in addition, they possess adequate compatibility with the reactor system. The transition joint design is illustrated in Fig. 19.1. The design incorporates a IOo tapered edge to reduce shear stresses arising from thermal expansion differences. The second design is the same as the first except that the transition portion of the joint is deleted and the graphite is joined directly to the Hastelloy 'MSH Program Serniann. Progr. Rept. Feb. 28, 1966, ORNL-2936, p. 140. 236 Fig. 19.1. Transition Joint Design with 10-deg Tapered Edges to Reduce Sheor Stresses. right the materials are grophite, molybdenum, and tiastelloy N. r- . ,~ . From left to . ,.-, GRAPYITE COO0 CLEARGhZE HASTELLO'I lil ORNL-OWG 61-11846 Fig. 19.2. Schematic lllustrution of a Direct Hustelloy N -t o-Gro ph i te Joint. N. This joint is, of course, more desirable from the standpoint of simplicity. In addition, the graph- ite is in compression, which is highly desirable for a hrittle material. The amount of compressive strain induced in a 31/2-in.-OD by 1/2-in.-wall graphite tube using this design is approximately 1%, which is postulated to be an acceptable compressive strain for high-density, low-permeability graphite.
The third design, which is also a direct graphite- to-Hastelloy N joint, is shown schematically in Fig. 19.2. Once again we have the graphite in compression; however, in this case allowance is made for keeping the joint in compression even if the graphite should shrink under irradiation. Firozing Development We are continuing work on the development of alloys suitable for joining graphite to graphite and to structural materials. We are currently looking at several alloys based on the corrosion-resistant Cu-Ni, Ni-Pd, Cu-Pd, and Ni-Nb binary systems. Quaternary compositions were prepared containing a carbide-forming element plus a meltingpoint de- pressant. Preliminary discrimination between the various alloys was obtained through wettability tests on high-density graphite. Poor flowability was obtained with the Ni-Nb and Cu-Pd alloys. In the Pd-Ni system, the carbide-forming elements and tnelting-point depressant were added to the 70-30, 60-40, and SO-SO binary alloys. In the Cu-Ni sys- tem, the carbide-forming elements and melting-point depressant were added to the 80-20 and 70-30 binary alloys. Most of the alloys seemed to wet graphite well at temperatures ranging from 2102 to 2192°F. Concurrent with the brazing development work, we are investigating the radiation stability of the brazing alloys. We are currently irradiating four batches of IJastelloy N Miller-Peaslee braze speci- mens in the OKR. The specimens will receive a dose (thermal) of approximately 2 r: 10 neutrons/cm2 at 1400OF. 19.2. COMPATISILITY OF GRAPHITE- MOLYBDENUM BRAZED JOINTS WITH MOLTEN FLUORIDE SALTS W. H. Cook The salt-corrosion studies of joints of grade CGB graphite brazed to molybdenum with 60 Pd-35 Ni-5 Cr (wt %) have continued. The specimens are ex- posed to static L,iF-BeF,-ZrF4-ThF4-UF4 (70- 23.6-5-1-0.4 mole %) at 1300'F in HasteIIoy N. We 237 have reported previously2P3 that there was no visible attack on the braze after a 5000-hr exposure, but there was a coating of palladium on the braze and some Ct3C2 on the graphite. A 10,000-hr test has now been concluded with similar results. All salt-corrosion tests of this series were sealed at room temperature with a pressure of approximately 4 x lowfi torr by TIG welding. A thermal control for the 10,000-hr salt test was made in which the test cotnponents and test history were the same except that no salt was present. The results are shown in the microstructures of the two joints in Fig. 19.36 and c. The diffusion of the palladium out of the brazing alloy to form a nearly pure palladium coating on the surfaces of the braze occurred both in the control (the one exposed to a vacuum) and the one exposed to the salt. The coating formed in the vacuum may be more uniform. Formation of the coating in the vacuum eliminates the salt as an agent in its formation. The more probable explanation is that the palladium is diffusing to the surface of the braze metal. 'The thickness of the coating appeared to be a function of time in the 5000-hr test, but this time dependence does not seem to continue for as long as 10,000 hr. There is some possibility that the palladium coating may help prevent corrosion of the brazing alloy by decreasing or preventing exposure of the alloy to the salt. The chemical analyses of the salts remained essentially unchanged, as shown in Table 19.1., with the exception that the chromium content of the salt in the 10,000-hr test rose sharply relative to the others. This is higher than one would expect with Hastelloy N in these types of tests. This particular test series for this brazing alloy will he terminated by a 20,000-hr test which is in progress. Another corrosion test of this brazing alloy in a similar joint configuration is being made in the MSRE core surveillance assembly, where the joint is being exposed to radiation and flowing fuel salt. Other potential brazing alloys will be subjected to similar tests as they are developed. The most promising alloys will be more rigorously tested in dynamic salts and irradiation fields. 'W. H. Cook, MSR Program Semiann. Pro@. Rept. Aug. 31, 1966, ORNL-4037, pp, 115-17. 3W. EI. Cook, MSR Program Serniann. Progr. Rept. Feh. 28, 1967, ORNL-4419, pp. 111-15.
- Page 196 and 197: 186 Fig. 15.6. Inner Surfoce of Col
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19.1. BRAZING OF GRAPHITE TO<br />
HASTELLOY N<br />
W. J. Werner<br />
ra phite-to-<br />
Studies were continued to develop methods for<br />
brazing large graphite pipes to Hastelloy N. At <strong>the</strong><br />
present time, three different joint designs are being<br />
tested for circumventing <strong>the</strong> differential <strong>the</strong>rmal expansion<br />
problem associated with joining <strong>the</strong> two materials.<br />
Concurrently, two different brasing techniques<br />
are under development for joining graphite to<br />
graphite and to Hastelloy N. In addition to wettability<br />
and flowability of <strong>the</strong> brazing alloy on graphite,<br />
<strong>the</strong> brazing technique development takes under<br />
consideration <strong>the</strong> application-oriented problems of<br />
service temperature, joint strength, compatibility<br />
with <strong>the</strong> reactor environment, and braze stability<br />
under irradiation in neutron fluxes<br />
Joint Design<br />
The first joint design, which has been reported<br />
previously,' is based on <strong>the</strong> incorporation of a<br />
transition material between <strong>the</strong> graphite and<br />
Hastelloy N that has an expansion coefficient between<br />
those of <strong>the</strong> two materials. Molybdenum and<br />
tungsten are two applicable materials, and, in addition,<br />
<strong>the</strong>y possess adequate compatibility with<br />
<strong>the</strong> reactor system. The transition joint design is<br />
illustrated in Fig. 19.1. The design incorporates<br />
a IOo tapered edge to reduce shear stresses arising<br />
from <strong>the</strong>rmal expansion differences.<br />
The second design is <strong>the</strong> same as <strong>the</strong> first except<br />
that <strong>the</strong> transition portion of <strong>the</strong> joint is deleted<br />
and <strong>the</strong> graphite is joined directly to <strong>the</strong> Hastelloy<br />
'MSH Program Serniann. Progr. Rept. Feb. 28, 1966,<br />
<strong>ORNL</strong>-2936, p. 140.<br />
236<br />
Fig. 19.1. Transition Joint Design with 10-deg<br />
Tapered Edges to Reduce Sheor Stresses.<br />
right <strong>the</strong> materials are grophite, molybdenum, and<br />
tiastelloy N.<br />
r-<br />
. ,~ .<br />
From left to<br />
. ,.-,<br />
GRAPYITE COO0 CLEARGhZE<br />
HASTELLO'I lil<br />
<strong>ORNL</strong>-OWG 61-11846<br />
Fig. 19.2. Schematic lllustrution of a Direct Hustelloy<br />
N -t o-Gro ph i te Joint.<br />
N. This joint is, of course, more desirable from<br />
<strong>the</strong> standpoint of simplicity. In addition, <strong>the</strong> graph-<br />
ite is in compression, which is highly desirable for<br />
a hrittle material. The amount of compressive strain<br />
induced in a 31/2-in.-OD by 1/2-in.-wall graphite tube<br />
using this design is approximately 1%, which is<br />
postulated to be an acceptable compressive strain<br />
for high-density, low-permeability graphite.