Application of Neutron Characterization Techniques to Metallic Structural Materials
WANG Yanxu1, GONG Wu2, SU Yuhua2, LI Bing1()
1 Shenyang National Laboratory for Materials Science, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China 2 Japan Proton Accelerator Research Complex Center, Japan Atomic Energy Agency, Tokai, Ibaraki 319-1195, Japan
Cite this article:
WANG Yanxu, GONG Wu, SU Yuhua, LI Bing. Application of Neutron Characterization Techniques to Metallic Structural Materials. Acta Metall Sin, 2024, 60(8): 1001-1016.
The correlation between the atomic structure, microstructure, and macroscopic properties of structural materials remains a core issue in materials research. In recent years, substantial progress has been achieved in constructing accelerator-based neutron sources and related experimental techniques, offering a robust platform for an in-depth understanding of the aforementioned correlation under real-time and in situ conditions. This article reviews the latest advancements in the application of major neutron characterization techniques, including neutron diffraction, Bragg-edge imaging, small-angle neutron scattering, pair distribution function analysis, and quasi-elastic/inelastic neutron scattering, in structural materials. Furthermore, it particularly highlights the origins and evolution of internal stresses during the phase transformations of steels, deformation mechanisms in light metals such as magnesium alloys, and microstructure and residual stress analyses using Bragg-edge imaging. Finally, a brief outlook on future development trends is provided.
Fund: National Natural Science Foundation of China(52201029);CSNS Consortium on High-Performance Materials of Chinese Academy of Sciences(JZHKYPT-2021-01)
Corresponding Authors:
LI Bing, professor, Tel: (024)23975272, E-mail: bingli@imr.ac.cn
Fig.1 Evolution of reactor and spallation neutron sources around the world[3] (CP1—Chicago Pile 1, CP2—Chicago Pile 2, X10—X-10 Graphite Reactor, NRX—National Research Experimental, MTR—Materials Testing Reactor, NRU—National Research Universal, HFBR—High Flux Beam Reactor, HFIR—High Flux Isotope Reactor, ILL—Institut Laue-Langevin, ZING-P—Spallation Pulsed Neutron Source Prototype, KENS—KEK Neutron Scattering Research Facility, IPNS—Intense Pulsed Neutron Source, LUJAN—Lujan Center at Los Alamos National Laboratory, ISIS—ISIS Neutron and Muon Source, FRM-Ⅱ—The Research Neutron Source Heinz Maier Leibnitz, OPAL—Open Pool Australian Lightwater Reactor, CARR—China Advanced Research Reactor, SNS-FTS—Spallation Neutron Source-First Target Station, JSNS—Japan Spallation Neutron Source, CSNS—Chinese Spallation Neutron Source, ESS—European Spallation Source, SNS-STS—Spallation Neutron Source-Second Target Station)
Fig.2 Schematics of scattering with scattering vector Q (a), small-angle scattering signal and diffraction spectrum (b), and the time-of-flight diffraction geometry used in the pulsed spallation sources (Scattering vectors Q1 and Q2 are observed by the two detector banks) (c)
Fig.3 Schematic of Bragg-edge (a) and diffraction and transmission spectra of bcc iron (b) (θ—Bragg angle, dhkl —lattice spacing of (hkl) plane, λ—wavelength)
Table 1 Neutron instruments for engineering materials[4,12-22]
Fig.5 Martensite transformation behaviors for a medium-carbon low-alloyed steel during quenching[34] (a) change in lattice parameter for austenite (Dashed lines are the martensite transfor-mation start temperatures) (b) change in lattice parameter for martensite
Fig.6 Schematic of the parent {100} grain (left) with associated twin {0002}grain (right) in respect to the loading axis (Q|| and Q⊥ are the detector banks along the axial and radial directions, respectively) (a)[60] and changes of the macroscopic strain and diffraction profiles along the axial direction during cycle compression-tension deformation of magnesium alloy showing the twinning and detwinning behavior directly (d-spacing—lattice spacing) (b)[73]
Fig.7 Two-dimensional map of the volume fraction of the martensite phase in a metastable austenitic alloy after sub-zero treatment at various temperatures (1 ch = 0.8 mm. The color code represents the martensite volume fraction)[14]
Fig.8 Residual lattice strains obtained via Bragg-edge imaging[115] (a) a 2D map of residual lattice strain (ε110) (b) distributions on the compressive side of the teeth root in the axial direction (RM, RL, and RR represent the right side of the tooth on the middle, the left, and the right sides, respectively)
Fig.9 TEM image, small angle neutron scattering (SANS) profiles, and atom probe tomographic (APT) reconstruction of the differently heat-treated Inconel718 alloys[128] (dΣ / dΩ—absolute macroscopic scattering cross sections)
Fig.10 Inelastic neutron scattering in CrMnFeCoNi alloy[141] (The dynamic structural factor, denoted as S(Q, E),is produced as a function of Q and energy transfer E. T—temperature) (a, b) S(Q, E) contour plots of CrMnFeCoNi at 6 and 300 K (c) S(Q, E) contour plot of Ni at 300 K (d) sliced spectra at 6 Å-1 ≤ |Q| ≤ 10 Å-1
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