Welded high purity low activation vanadium alloys, such as NIFS-HEATs, have demonstrated good mechanical properties at as-welded condition. In this study, welded NIFS-HEAT-2 were irradiated at a low temperature to investigate the effect of irradiation hardening on impact properties, and to understand the characteristics of radiation defects in welded vanadium alloys.The weld materials were 4 mm-thick plates of NIFS-HEAT-2 (V-4Cr-4Ti) annealed at 1273 K for 2 hr. The samples were made by bead-an-plate welding with a 1.6 kW Y AG laser in a high purity Ar. Input power and welding speed were 290 Jim and 0.33 m I min, respectively. Table I shows concentration of HlCINIO before and after welding. No significant contamination by welding was observed. V -notch impact specimens (1.5 X 1.5 X 20 mm) were machined from the weld metal and the base metal of the welded plate. The notch depth (d) was 0.3 mm. In order to investigate the effect of post weld heat treatment (PWHT), specimens for hardness investigation were prepared and annealed for I hr at 673 K, 873 K and 1223 K. The samples were irradiated in JMTR (Japan Materials Testing Reactor) at 563 K. The neutron f1uence was 4.5 X 10" n m" (0.08 dpa). Figure I shows results of Charpy impact test. Absorbed energy is nonnalized by the function of the specimen size at the V -notch, where specimen width (B) is L5 mm, and ligament (b ~ B -d) is 1.2 mm. Before irradiation, both the base metal (BM) and the weld metal (WM) maintained good ductility at all tested temperatures. Upper shelf energy, Eu, was estimated as 0.4 J m'] After irradiation, upper shelf energy of the base metal and weld metal was around 0.35 J m", which was 10-15 % lower than that before irradiation. In addition, absorbed energy of the weld metal after irradiation showed a remarkable drop at 77 K. Ductile-brittle transition temperature (DBTT) of the weld metal after irradiation was estimated as 113 K, where absorbed energy was expected to be half the upper shelf energy before irradiation. DBTIs determined from the other curves were less than 77 K, Figure 2 shows hardness distribution around the weld bead. From microstructural observations, the width of the weld metal was I mm as indicated in the figure. Base metal regions were determined as 4 mm or farther from the bead center, where the hardness before irradiation was the same as that before welding. Irradiation hardening was estimated as the difference between the average hardness in each region. Irradiation hardening of the weld metal, 64 Hv, was 40 % larger than that ofthe base metal, 46 Hv.The weld metal became brittle at 77 K after irradiation as shown in Fig. I. It is recognized that the large hardening shown in Fig. 2 is responsible for the embrittlement of the weld metal at 77 K. Yield stress is increased due to irradiation hardening, and higher than the stress for cleavage fracture.