[논문]Radiation damage in helium ion-irradiated reduced activation ferritic/martensitic steel

Xia, L.D.; Liu, W.B.; Liu, H.P.; Zhang, J.H.; Chen, H.; Yang, Z.G.; Zhang, C.

doi:10.1016/j.net.2017.10.012

Radiation damage in helium ion-irradiated reduced activation ferritic/martensitic steel 원문보기 논문타임라인

Nuclear engineering and technology : an international journal of the Korean Nuclear Society, v.50 no.1, 2018년, pp.132 - 139

Xia, L.D. (Key Laboratory of Advanced Materials of Ministry of Education, School of Materials Science and Engineering, Tsinghua University) , Liu, W.B. (Key Laboratory of Advanced Materials of Ministry of Education, School of Materials Science and Engineering, Tsinghua University) , Liu, H.P. (Institute of Modern Physics, Chinese Academy of Sciences) , Zhang, J.H. (Department of Nuclear Science and Technology, Xi'an Jiaotong University) , Chen, H. (Key Laboratory of Advanced Materials of Ministry of Education, School of Materials Science and Engineering, Tsinghua University) , Yang, Z.G. (Key Laboratory of Advanced Materials of Ministry of Education, School of Materials Science and Engineering, Tsinghua University) , Zhang, C. (Key Laboratory of Advanced Materials of Ministry of Education, School of Materials Science and Engineering, Tsinghua University)

Abstract ▼ AI-Helper

Nanocrystalline reduced activation ferritic/martensitic (RAFM) steel samples were prepared using surface mechanical attrition treatment (SMAT). Un-SMATed and SMATed reduced activation ferritic/martensitic samples were irradiated by helium ions at $200^{\circ}C$ and $350^{\circ}C$ with 2 dpa and 8 dpa, respectively, to investigate the effects of grain boundaries (GBs) and temperature on the formation of He bubbles during irradiation. Experimental results show that He bubbles are preferentially trapped at GBs in all the irradiated samples. Bubble denuded zones are clearly observed near the GBs at $350^{\circ}C$, whereas the bubble denuded zones are not obvious in the samples irradiated at $200^{\circ}C$. The average bubble size increases and the bubble density decreases with an increasing irradiation temperature from $200^{\circ}C$ to $350^{\circ}C$. Both the average size and density of the bubbles increase with an increasing irradiation dose from 2 dpa to 8 dpa. Bubbles with smaller size and lower density were observed in the SMATed samples but not in the un-SMATed samples irradiated in the same conditions, which indicate that GBs play an important role during irradiation, and sink strength increases as grain size decreases.

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제안 방법

Heat treatment included austenitizing at 1253 K for 45 minutes, followed by water quenching and then tempering at 1033 K for 90 minutes. SMAT, an effective approach to prepare bulk NC materials, was used in this investigation. The plate sample (Φ50.
We systematically analyzed bubble morphologies in helium ioneirradiated NC RAFM steel and coarse-grained RAFM steel to investigate the effects of GBs and temperature on the formation of bubbles during irradiation. The experimental results were as follows:
X-ray diffraction (XRD) analysis of the surface layer was carried out using a Rigaku SmartLab X-ray diffractometer with Cu K_a radiation. A step length of 0.

대상 데이터

The authors are grateful to the National Laboratory of Heavy-ion Accelerators in Lanzhou for providing the experiment platform. The authors are indebted to Dr Z.
The material used in our investigation was RAFM steel with the following chemical composition (in wt%): 0.10% C, 1.50% W, 0.29% V, 0.55% Mn, 0.09% Ta, 8.60% Cr, and balanced Fe. Heat treatment included austenitizing at 1253 K for 45 minutes, followed by water quenching and then tempering at 1033 K for 90 minutes.
The plate sample (Φ50.0 4.0 mm in size) of the tempered steel was submitted to SMAT, with the setup illustrated in Lu's work [21].

성능/효과

2) The average bubble diameters of un-SMATed samples irradiated with 2 dpa at 200°C and 350°C were ~1.2 nm and ~2.3 nm, and the bubble densities were ~ 1:1 1025 =m3 and ~ 1:51024 =m3, respectively.
3) The average bubble diameters of un-SMATed and SMATed samples irradiated with 2 dpa at 350°C were 2.3 nm and 1.9 nm, and the densities were ~ 1:5 1024 =m3 and ~ 0:7 1024 =m3, respectively.
After irradiation, at 200C, the lattice parameters of the SMATed and un-SMATed samples were 2.878 Å and 2.876 Å; at 350C, the lattice parameters were 2.877 Å and 2.874 Å, which corresponded to ~0.28%, ~0.21%, ~0.24%, and ~0.14% of lattice expansion, respectively.
It is generally accepted that radiation-induced defects tend to migrate to the interfacial regions such as GBs [18]. As shown in the analysis of the SMATed and un-SMATed RAFM samples, before SMAT, the average size of martensite lathes was 370 nm, and after SMAT, the average grain size was 130 nm, which means the SMATed steel contained much larger volume fractions of interface regions than the un-SMATed steel. This led to a smaller lattice expansion in the SMATed samples for the reason that their interfaces absorbed more He from inside of the grains.
The decrease in bubble density and bubble size was due to grain size. The TEM result shows that the grain size of the SMATed samples was 130 nm, and the size of the martensitic lath in the un-SMATed samples was 370 nm. Singh suggested that the grain size effect on radiation damage is primarily due to the depletion of bubbles from the grain interior and their migration to the GBs [17,18].
We counted the amount of bubbles in a certain region to get the bubble density. The measured results may not be so accurate because some bubbles were not very distinct in the micrographs because the TEM results were not precise enough, but the results certainly showed the general trend. The un-SMATed samples irradiated at 200°C with 2 dpa and 8 dpa levels of damage had bubble densities of ~ 1:1 10²⁵ =m3 and ~ 1:6 10²⁵ =m³, respectively.

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