HRTEM study on the ordered phases in Hg3In2Te6 crystals grown by Bridgman method

Luo, Lin; Wang, Jie; Xu, Yadong; He, Yihui; Xu, Lingyan; Fu, Li

doi:10.1039/c3ce42598c

Cited by 5 publications

(5 citation statements)

References 40 publications

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“…3c, which is indicative of SRO formed during the fatigue deformation at 400 °C. The same forbidden diffraction spot has been mentioned in many researches [22][23][24][25][26] and the first time that definitive evidence proposed to be caused by SRO is in the research of Alloy 600 by the combination analysis of electron diffraction pattern and neutron diffraction [27]. In Fig.…”

Section: Dislocation Structuresupporting

confidence: 65%

Fatigue Damage Mechanism of AL6XN Austenitic Stainless Steel at High Temperatures

Hong

Gao²,

Li³

et al. 2020

Acta Metall. Sin. (Engl. Lett.)

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By the combination of transmission electron microscope, neutron diffraction and small-angle neutron scattering methods, mechanical fatigue behavior of AL6XN austenitic stainless steel was investigated in the temperature range of 400-600 °C. At 400 °C, in addition to the occurrence of dynamic strain aging, the formation of short-range order was evidenced from the forbidden electron diffraction spot of 1/3 {422} in face-centered cubic (fcc) structure viewed down [111] zone axis, which facilitate the planar slip mode of dislocation and result in the work hardening during the fatigue deformation. The fatigue damage is mainly dominated by the accumulation of planar slip band and the interaction among various slip systems. With increasing temperature, precipitates of chi phase, Laves phase and sigma phase were formed during the fatigue tests at 500 and 600 °C. An increase in precipitation content at 600 °C has also been confirmed by both scanning electron microscope and small-angle neutron scattering analysis. The dislocation pileup originating from the uncoordinated deformation between precipitate and austenitic matrix is an important fatigue damage leading to crack. The continuous cycle softening behavior was also observed on the fatigue curve at 600 °C, which is considered to be caused by dynamic recovery.

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Section: Dislocation Structuresupporting

confidence: 65%

Fatigue Damage Mechanism of AL6XN Austenitic Stainless Steel at High Temperatures

Hong

Gao²,

Li³

et al. 2020

Acta Metall. Sin. (Engl. Lett.)

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“…Although the diffuse 1/3 {422} forbidden reflections had been observed in 310 SS cathodically charged with hydrogen during deformation at RT [16], the bright 1/3 {422} reflections as shown in Figure 4 seem to be first observed. Moreover, the same 1/3 {422} forbidden reflections were noted in aged metals [17,18], Hg 3 In 2 Te 6 crystals grown by the Bridgeman method [19], an austenitic Fe-Mn-Al alloy after tensile deformation at 77 K [20] and in Alloy 600 after stress corrosion cracking (SCC) tests in 360 • C water [3]. The bright 1/3 {422} reflections as shown in Figure 4a appeared in the last three cases (i.e., Hg 3 In 2 Te 6 crystals grown by the Bridgeman method [19], an austenitic Fe-Mn-Al alloy after tensile deformation at 77 K [20] and in Alloy 600 after SCC tests in 360 • C water [3]).…”

Section: Formation Of Short-range Order In 316 Ss Due To Hydrogen-enhsupporting

confidence: 61%

“…Moreover, the same 1/3 {422} forbidden reflections were noted in aged metals [17,18], Hg 3 In 2 Te 6 crystals grown by the Bridgeman method [19], an austenitic Fe-Mn-Al alloy after tensile deformation at 77 K [20] and in Alloy 600 after stress corrosion cracking (SCC) tests in 360 • C water [3]. The bright 1/3 {422} reflections as shown in Figure 4a appeared in the last three cases (i.e., Hg 3 In 2 Te 6 crystals grown by the Bridgeman method [19], an austenitic Fe-Mn-Al alloy after tensile deformation at 77 K [20] and in Alloy 600 after SCC tests in 360 • C water [3]). Moreover, when the [111] diffraction pattern was tilted around the [110] axis until the [112] was obtained, the bright 1 2 {311} reflections were observed as shown in Figure 4b, which had also been observed in aged metals [18,21] and Hg 3 In 2 Te 6 crystals [19].…”

Section: Formation Of Short-range Order In 316 Ss Due To Hydrogen-enhsupporting

confidence: 61%

“…The bright 1/3 {422} reflections as shown in Figure 4a appeared in the last three cases (i.e., Hg 3 In 2 Te 6 crystals grown by the Bridgeman method [19], an austenitic Fe-Mn-Al alloy after tensile deformation at 77 K [20] and in Alloy 600 after SCC tests in 360 • C water [3]). Moreover, when the [111] diffraction pattern was tilted around the [110] axis until the [112] was obtained, the bright 1 2 {311} reflections were observed as shown in Figure 4b, which had also been observed in aged metals [18,21] and Hg 3 In 2 Te 6 crystals [19]. By observing that the lattice spacing of the 1/3 {422} forbidden reflections determined by electron diffraction was around 0.21 nm for Alloy 600, which agreed perfectly with that determined by neutron diffraction, we have already confirmed that the 1/3 {422} and 1/2 {311} forbidden reflections formed in Alloy 600 correspond to SRO.…”

Section: Formation Of Short-range Order In 316 Ss Due To Hydrogen-enhmentioning

confidence: 96%

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The Role of Hydrogen in Hydrogen Embrittlement of Metals: The Case of Stainless Steel

Kim

Choe

2019

Metals

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Hydrogen embrittlement (HE) of metals has remained a mystery in materials science for more than a century. To try to clarify this mystery, tensile tests were conducted at room temperature (RT) on a 316 stainless steel (SS) in air and hydrogen of 70 MPa. With an aim to directly observe the effect of hydrogen on ordering of 316 SS during deformation, electron diffraction patterns and images were obtained from thin foils made by a focused ion beam from the fracture surfaces of the tensile specimens. To prove lattice contraction by ordering, a 40% CW 316 SS specimen was thermally aged at 400 °C to incur ordering and its lattice contraction by ordering was determined using neutron diffraction by measuring its lattice parameters before and after aging. We demonstrate that atomic ordering is promoted by hydrogen, leading to formation of short-range order and a high number of planar dislocations in the 316 SS, and causing its anisotropic lattice contraction. Hence, hydrogen embrittlement of metals is controlled by hydrogen-enhanced ordering during RT deformation in hydrogen. Hydrogen-enhanced ordering will cause the ordered metals to be more resistant to HE than the disordered ones, which is evidenced by the previous observations where furnace-cooled metals with order are more resistant to HE than water-quenched or cold worked metals with disorder. This finding strongly supports our proposal that strain-induced martensite is a disordered phase.

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“…This may be due to the fact that XRD detects changes that show more than 5% range of variation, however, our final dopant concentration is lesser than 5%. [ 67 ] Hence, it is not possible to detect and analyze the interaction at CsI and perovskite interface from XRD analysis. To analyze the CsPbI 3 formation, PbI 2 was coated on 10 wt% CsI–SnO x films.…”

Section: Resultsmentioning

confidence: 99%

Cesium Iodide Incorporation in Tin Oxide Electron Transport Layer for Defect Passivation and Efficiency Enhancement in Double Cation Absorber‐Based Planar Perovskite Solar Cells

et al. 2021

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Fermi level tuning and defect passivation at the electron selective layer (ESL)/perovskite interface has a strong effect on the perovskite solar cell (PSC) device performance. Two strategies are commonly used for passivation, 1) bulk passivation—by adding dopants in the ESL and 2) surface passivation—to suppress the interface dangling bonds using ligands. Herein, a novel dual passivation (bulk and surface) strategy is presented by incorporating a simple molecule cesium iodide (CsI) in the SnO x ESL. Passivation effects using different CsI dopant concentrations (0–10 wt%) in SnO x solution were studied and its beneficial role of defect passivation is discussed in detail. A systematic study revealed that the addition of CsI in the SnO x ESL not only significantly influences the open‐circuit voltage (V oc) and fill factor (FF), but also suppresses the recombination at the interface due to its improved built in surface potential. Lower trap‐filled limit voltage (V TFL), trap density (n t), and diode ideality factor (n id) are observed for the CsI incorporated SnO x ESL as compared with the bare SnO x layer which leads to a power conversion efficiency improvement from 14.3% to 15.4%.

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HRTEM study on the ordered phases in Hg₃In₂Te₆ crystals grown by Bridgman method

Abstract: The formation and evolution of two Hg3In2Te6 phases with ordered vacancies during the disorder–order transformation process was studied.

Cited by 5 publications

References 40 publications

Fatigue Damage Mechanism of AL6XN Austenitic Stainless Steel at High Temperatures

Fatigue Damage Mechanism of AL6XN Austenitic Stainless Steel at High Temperatures

The Role of Hydrogen in Hydrogen Embrittlement of Metals: The Case of Stainless Steel

Cesium Iodide Incorporation in Tin Oxide Electron Transport Layer for Defect Passivation and Efficiency Enhancement in Double Cation Absorber‐Based Planar Perovskite Solar Cells

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