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Colin Judge: Testing structural materials in Idaho’s newest hot cell facility
Idaho National Laboratory’s newest facility—the Sample Preparation Laboratory (SPL)—sits across the road from the Hot Fuel Examination Facility (HFEF), which started operating in 1975. SPL will host the first new hot cells at INL’s Materials and Fuels Complex (MFC) in 50 years, giving INL researchers and partners new flexibility to test the structural properties of irradiated materials fresh from the Advanced Test Reactor (ATR) or from a partner’s facility.
Materials meant to withstand extreme conditions in fission or fusion power plants must be tested under similar conditions and pushed past their breaking points so performance and limitations can be understood and improved. Once irradiated, materials samples can be cut down to size in SPL and packaged for testing in other facilities at INL or other national laboratories, commercial labs, or universities. But they can also be subjected to extreme thermal or corrosive conditions and mechanical testing right in SPL, explains Colin Judge, who, as INL’s division director for nuclear materials performance, oversees SPL and other facilities at the MFC.
SPL won’t go “hot” until January 2026, but Judge spoke with NN staff writer Susan Gallier about its capabilities as his team was moving instruments into the new facility.
Jin-Li Cao, Wei Xiao, Qi Cao, Bing-Ling He
Fusion Science and Technology | Volume 74 | Number 3 | October 2018 | Pages 177-185
Technical Paper | doi.org/10.1080/15361055.2017.1416245
Articles are hosted by Taylor and Francis Online.
Experiments observed preferential He bubble formation in carbide precipitates M23C6 during low-temperature He irradiation in ferritic-martensitic steels. However, the process and mechanism of He trapping in M23C6 present a challenge to measure. Using density functional theory, we have systematically investigated He distribution, migration, and accumulation in Cr23C6. The formation energies of interstitial and substitutional He in Cr23C6 are 3.50 and 3.16 eV, respectively, remarkably lower than those in Fe matrix. The higher solubility of He in Cr23C6 makes it an He-trapping center in martensitic steels. On the other hand, the migration barrier of interstitial He in Cr23C6 is 2.58 eV, about 2.52 eV higher than that in bulk Fe. Furthermore, we only find a very weak attraction potency for substitutional-interstitial He pair, 0.25 eV, and even no binding trend for interstitial-interstitial or substitutional-substitutional He pairs, which suggests that it is more difficult for He atoms to move and less powerful driving force to accumulate in Cr23C6 than those in Fe matrix. Our results indicate that the trapping effect results from a lower charge density zone in Cr23C6, and predict that the small and dense Cr23C6 particles may hinder bubble growth at the initial stage, which can improve the resistance to irradiation void swelling.
