Next Article in Journal
Comparison of Sublimation 3D Scanning Sprays in Terms of Their Effect on the Resulting 3D Scan, Thickness, and Sublimation Time
Previous Article in Journal
Synergistic Reinforcement of Si3N4 Based Ceramics Fabricated via Multiphase Strengthening under Low Temperature and Short Holding Time
 
 
Search for Articles:
Title / Keyword
Author / Affiliation / Email
Journal
Article Type
 
 
Advanced Search
 
Section
Special Issue
Volume
Issue
Number
Page
 
Journals
Materials
Volume 16
Issue 18
10.3390/ma16186164
materials-logo
Submit to this Journal Review for this Journal Propose a Special Issue
► Article Menu

Article Menu

share Share announcement Help format_quote Cite question_answer Discuss in SciProfiles thumb_up
...
Endorse textsms
...
Comment
first_page
settings
Order Article Reprints
Font Type:
Arial Georgia Verdana
Font Size:
Aa Aa Aa
Line Spacing:
Column Width:
Background:
Communication

Decreasing Hydrogen Content within Zirconium Using Au and Pd Nanoparticles as Sacrificial Agents under Pressurized Water at High Temperature

by
Yeon Ju Lee
†,
Juhee Ha
†,
Su Ji Choi
,
Hyeok Il Kim
,
Sumin Ryu
,
Youngsoo Kim
* and
Young-Sang Youn
*
Department of Chemistry, Yeungnam University, Daehak-ro 280, Gyeongsan 38541, Gyeongbuk, Republic of Korea
*
Authors to whom correspondence should be addressed.
†
These authors contributed equally to this work.
Materials 2023, 16(18), 6164; https://doi.org/10.3390/ma16186164
Submission received: 10 August 2023 / Revised: 31 August 2023 / Accepted: 8 September 2023 / Published: 11 September 2023
(This article belongs to the Special Issue Corrosion of Metallic Alloys: Advances and Discoveries)
Browse Figures
Versions Notes

Abstract

:
Decreasing hydride-induced embrittlement of zirconium-based cladding is a significant challenge for the successful dry storage of spent nuclear fuel. Herein, to radically minimize hydride-induced embrittlement, we used nanoparticles as sacrificial agents with a greater affinity than zirconium for hydrogen. Corrosion experiments in the presence of gold (Au) and palladium (Pd) nanoparticles under simulated pressurized water reactor (PWR) conditions revealed that the hydrogen content of the zirconium samples was remarkably reduced, with a maximum decrease efficiency of 53.9% using 65 nm Au and 53.8% using 50 nm Pd nanoparticles. This approach provides an effective strategy for preventing hydride-induced embrittlement of zirconium-based cladding.

1. Introduction

Zirconium-based alloys consisting of 95% or more zirconium are typically used as nuclear fuel cladding materials in pressurized water reactors (PWRs) owing to their superior mechanical properties, corrosion resistance, chemical stability, heat transfer, and thermal absorption neutron cross-section compared to other alloys [1,2,3,4,5,6,7,8]. During reactor operation, the cladding is constantly in contact with the primary circuit water to transfer the thermal energy produced by the nuclear fuel to the water for the generation of electrical energy [9]. The corrosion reaction with the primary water produces hydrogen [10,11,12,13,14,15], which accumulates in the cladding owing to the high hydrogen affinity of zirconium [16]. Consequently, hydrogen ingress into the cladding is inevitable during reactor service [17,18,19]. When the hydrogen concentration exceeds the terminal solid solubility (TSS) limit for precipitation, the hydrogen absorbed in the cladding agglomerates as hydrides in the zirconium matrix [5,12,20,21]. These hydrides preferentially orient along the circumferential direction rather than the radial direction in cylindrical cladding during normal operation [5,11]. Although hydrides embedded along the circumferential orientation reduce the cladding ductility, the cladding can endure deformation by the circumferential hydrides [5,22]. However, when the spent nuclear fuel is withdrawn from the spent fuel pool for dry storage after a certain period, the hydrides reorient from the circumferential direction to the radial direction because the applied tensile hoop stress on the cladding exceeds the threshold stress under dry storage conditions [11,23,24,25,26]. Radial hydrides severely embrittle cladding, not only deteriorating the mechanical properties such as ductility and fracture toughness [5,10,11,22,27,28,29], but also increasing the ductile–brittle transition temperature (DBTT) [22,29]. Therefore, preventing the reorientation of hydrides into the radial direction in the cladding is crucial for maintaining cladding integrity during the dry storage of spent nuclear fuel [12,19,26,30,31].
One way to reduce radial hydride formation in zirconium-based cladding under PWR conditions is to utilize sacrificial materials capable of capturing hydrogen near the cladding. Several studies have examined the efficacy of metal nanoparticles, including Au, Pd, and Pd-containing alloy nanoparticles, for hydrogen capture or dissociation in non-nuclear-related applications [32,33,34,35]. Although Au nanoparticles do not directly absorb hydrogen molecules, the strong catalytic activity on the nanoparticle surface contributes to the dissociation of the adsorbed hydrogen molecules into atomic hydrogen, which exhibits a strong affinity for the Au surface [35,36,37]. In contrast, Pd and Pd-containing alloy nanoparticles are known for their ability to absorb and convert hydrogen into a Pd-hydride form [33,34,38]. Single crystal α-phase Pd nanoparticles can absorb hydrogen under moderate temperature and pressure conditions. As the amount of hydrogen absorbed by the Pd nanoparticles increases, the lattice distance between the Pd atoms expands, resulting in the formation of β-phase Pd nanoparticles known as Pd-hydrides [33,34,39]. Therefore, both Au and Pd nanoparticles are promising materials for capturing hydrogen, albeit via different mechanisms.
This study is the first to utilize Au and Pd nanoparticles as sacrificial agents to preferentially capture hydrogen and reduce the hydrogen absorption of zirconium-based cladding under simulated PWR conditions, which consequently minimizes the hydride-induced embrittlement of the cladding. The core concept of the proposed strategy is schematically illustrated in Figure 1. In the absence of nanoparticles, the zirconium-based cladding is highly vulnerable to corrosion owing to the high absorption of hydrogen on its surface and throughout its bulk under PWR conditions. However, in the presence of nanoparticles, the hydrogen produced by the reaction between the cladding and water is distributed between the cladding and nanoparticles under PWR conditions, thereby decreasing hydride formation on the cladding. The hydrogen content of the zirconium after corrosion experiments using Au or Pd nanoparticles under simulated PWR conditions was significantly reduced compared to that without nanoparticles, indicating that the hydrogen produced on the zirconium surface was efficiently captured by the Au and Pd nanoparticles dispersed in the water. These findings suggest that hydrogen is preferentially absorbed on the Au and Pd nanoparticles over the zirconium. Therefore, a significant reduction in radial-hydride-driven embrittlement due to hydride reorientation in the cladding during the dry storage of spent nuclear fuel can potentially be achieved by dispersing Au and Pd nanoparticles in the coolant.

2. Materials and Methods

Zirconium pellets with a diameter of 10 mm and a thickness of 1 mm were prepared by mechanically pressing zirconium powder (99.5% purity, Se-Jong Materials Co., Ltd., Incheon, Republic of Korea) at 20.7 MPa. The fabricated zirconium pellet was heated at 850°C for a week under an argon (99.999% purity) atmosphere in a quartz tube furnace (LF-GT530, LK Lab Korea, Namyangju-si, Republic of Korea). After heating, the zirconium pellets were polished with 3000 grit SiC paper, resulting in a mean density of 4519 kg/m3. The hydrogen content of the as-prepared zirconium pellet was 13 μg/g, which was similar to the values reported in the literature for zirconium-based cladding [2,18].
The Au and Pd nanoparticles were prepared via colloidal synthesis. Two different synthesis methods were used to prepare the spherical Au nanoparticles. Small spherical Au nanoparticles (13 and 25 nm) were synthesized using the Frens method by adjusting the HAuCl4/citrate/AgNO3 ratio to an appropriate value [40]. Large Au nanoparticles (65 and 109 nm) were prepared using the seed-growth method [41,42]. For the synthesis of Pd nanoparticles, the nucleation and growth method was used to synthesize 12 nm Pd nanoparticles [43], whereas the ethanol reduction method was used to synthesize 50 and 108 nm Pd nanoparticles [44]. The synthetic procedures for all the metal nanoparticles are described in detail in the Supplementary Materials.
The corrosion tests of the zirconium pellets were conducted in 350 mL of deionized water (New P.NIX Power water purification system, Daihan Scientific, Wonju, Republic of Korea) with/without nanoparticles. The pressure and temperature were maintained at 15.5 ± 0.5 MPa and 315°C, respectively, for 24 h under continuous stirring at 200 rpm in a 700 mL stirred autoclave system (Ilshin Autoclave, Daejeon, Republic of Korea). An appropriate amount of nitrogen gas (99.999% purity) was injected into the system before the temperature was increased to attain the target pressure at 315°C. The scheme in Figure 2 shows a zirconium pellet mounted on a sample holder for the corrosion experiments. An 8 mm diameter area on both sides of the zirconium pellet was exposed to the deionized water during the corrosion tests.
X-ray diffraction (XRD) data were obtained in the range of 20–80° with a scanning step of 0.02° for 0.6 s using a MiniFlex600 system (Rigaku, Japan) with Cu Kα radiation operated at 15 mA and 40 kV. Raman spectra were acquired over the range of 130–800 cm−1 using an NS240 Raman spectrometer (Nanoscope Systems, Daejeon, Republic of Korea) with a continuous-wave diode-pumped laser at a wavelength of 532 nm and an exposure time of 30 s. Transmission electron microscopy (TEM) images were acquired using an H-7600 system (Hitachi, Tokyo, Japan) at an accelerating voltage of 120 kV. The optical properties of the metal nanoparticles were characterized using a UV-1800 spectrophotometer (Shimadzu, Kyoto, Japan) in a scan range of 300–800 nm. The hydrogen content within the zirconium pellet was determined using a hydrogen analyzer (RH-404, LECO Corporation, St. Joseph, MI, USA) with a sensitivity of ±5 μg/g [26].

3. Results

The XRD pattern of a zirconium pellet before the corrosion experiment is shown in Figure S1. At room temperature and atmospheric pressure, zirconium exhibits a hexagonal crystal structure [2,6], and the diffraction patterns associated with hexagonal Zr can be clearly observed in Figure S1.
For the corrosion test of the zirconium pellets, the size of the Au and Pd nanoparticles was varied. Au nanoparticles with four different diameters and Pd nanoparticles with three different diameters were examined. Figure 3 shows the TEM images of the various synthesized Au and Pd nanoparticles. The nanoparticle diameters were determined by randomly selecting nanoparticles from different regions of the TEM grid. The mean diameters of the Au nanoparticles (Figure 3a–c and Figure S2) were 13 ± 1.9 nm, 25 ± 3.1 nm, 65 ± 8.7 nm, and 109 ± 11.8 nm, respectively, and those of the Pd nanoparticles (Figure 3e–g) were 12 ± 2.2 nm, 50 ± 12.0 nm, and 108 ± 16.6 nm, respectively.
Figure 4 shows the XRD and Raman data of the zirconium specimens after the corrosion experiments with/without various sizes of synthesized Au and Pd nanoparticles. Diffraction peaks corresponding to a monoclinic ZrO2 crystal structure were observed in all pellets, regardless of the nanoparticles used (Figure 4a) [45,46]. This monoclinic ZrO2 crystal structure was also confirmed by the Raman profiles (Figure 4b) [45,47]. Zirconium is known to absorb hydrogen while being oxidized to ZrO2 by the corrosion reaction with the primary water during reactor operation [21,26,48]. Therefore, the ZrO2 observed in all the pellets arose from the reaction of zirconium with water under PWR conditions.
The hydrogen content of the zirconium pellets was determined after the corrosion tests with/without various sizes of synthesized Au and Pd nanoparticles (Figure 5). In the absence of nanoparticles, the hydrogen content of the zirconium after the corrosion test was 7201 μg/g, which was significantly higher than the 13 μg/g value observed before the corrosion test. This indicated that a significant amount of the hydrogen produced under the simulated PWR conditions had accumulated in the zirconium. In the presence of nanoparticles, the hydrogen content of the zirconium samples was remarkably reduced by an average of 4048 μg/g, an average decrease efficiency of 43.8%, regardless of the type and size of the nanoparticles, owing to the excellent hydrogen absorption abilities of the Au and Pd nanoparticles [32,33,34,35,36,37,38]. The hydrogen capture ability of nanoparticles typically increases with decreasing nanoparticle size, regardless of the type of nanoparticle [35,49,50,51]. However, in this study, the midsized Au and Pd nanoparticles resulted in a greater decrease in the hydrogen content of the zirconium specimens, with values of 3883 μg/g using the 65 nm Au and 3875 μg/g using the 50 nm Pd nanoparticles (a decrease efficiency of 53.9 and 53.8%, respectively), than that observed for the 13 nm Au, 25 nm Au, and 12 nm Pd nanoparticles. In addition, when larger 109 nm Au and 108 nm Pd nanoparticles were used, the effect of the nanoparticles on the reduction in the hydrogen concentration within the zirconium pellets declined. In general, metal nanoparticles primarily capture hydrogen through surface sorption, and the nanoparticle’s surface plays a crucial role in this process. Notably, all the nanoparticles used in our experiments were exposed to high temperature and pressure. During corrosion tests conducted under PWR conditions, nanoparticles can potentially destabilize, rendering them susceptible to destruction or agglomeration. Consequently, the actual size of the metal nanoparticles during the reaction under PWR conditions may differ from the original size determined from the TEM images. Smaller nanoparticles in the range of 12–25 nm can succumb to the prolonged high-temperature and -pressure conditions encountered in PWR systems. In contrast, the midsized nanoparticles used in our experiments (65 nm for Au and 50 nm for Pd) maintained their particulate structure under the PWR conditions for a longer period than the smaller particles, which enabled them to capture more hydrogen. In addition, particles larger than 100 nm exhibited a slightly lower hydrogen capture capacity owing to the size effect. As a result, nanoparticles larger than the threshold size exhibited the same trend as those reported in the literature, namely the hydrogen capture ability increased as the particle size decreased [35,49,50,51]. Combining our experimental findings with those in the literature, we concluded that the optimal hydrogen capture performance is achieved using 65 nm Au or 50 nm Pd nanoparticles under the simulated PWR conditions. This observation aligns with trends previously reported in the literature and can explain the volcano-like trend in the decrease efficiency (Figure 5).
In addition, we monitored the UV–vis absorption spectra of the nanoparticle-containing water before and after the reaction to compare their optical properties (Figure S3). The absorption spectra of the recovered water after the reaction exhibited no noticeable peaks for any of the nanoparticle sizes. Instead, small and broad absorption features were observed across the entire wavelength range. When Au and Pd nanoparticles undergo significant aggregation, their behavior resembles that of bulk materials. Consequently, the nanoparticles lose their unique nanoscale optical properties, resulting in the disappearance of absorption features in the visible-light region. The data in Figure 5 and Figure S3 suggest that the nanoparticles were unable to maintain an intact structural framework under the PWR conditions and were prone to significant aggregation. Consequently, we postulated that the process by which hydrogen was captured on the nanoparticles was highly active during the initial phase of the reaction. However, as the reaction time increases, the hydrogen capture ability of the nanoparticles may degrade owing to structural deformation.

4. Conclusions

We investigated the decrease in hydrogen content within zirconium using Au and Pd nanoparticles as sacrificial agents under simulated PWR conditions. The composition of all the zirconium pellets was changed from hexagonal Zr metal to monoclinic ZrO2 after the corrosion experiments owing to their reaction with water in which the zirconium absorbed hydrogen while being oxidized. After the corrosion experiments in the presence of Au or Pd nanoparticles, the hydrogen content of the zirconium samples decreased significantly. In particular, the 65 nm Au and 50 nm Pd nanoparticles resulted in the lowest hydrogen contents among the zirconium samples, with contents of 3318 and 3326 μg/g and a corresponding decrease efficiency of 53.9 and 53.8%, respectively. Our discovery of the successful application of Au and Pd nanoparticles as sacrificial agents for preferential entrapment of hydrogen over zirconium is unprecedented in the field of nuclear materials and can be utilized as a strategy to significantly minimize the hydride-induced embrittlement of zirconium-based cladding.

Supplementary Materials

The following supporting information can be downloaded at: https://www.mdpi.com/article/10.3390/ma16186164/s1, Detailed synthetic procedures; Figure S1: XRD spectrum of a zirconium pellet obtained before the corrosion test.; Figure S2: Representative TEM images of Au and Pd nanoparticles.; Figure S3: UV–vis absorption spectra for 109 nm Au and 108 nm Pd nanoparticles before and after the corrosion test.

Author Contributions

Conceptualization, Y.K. and Y.-S.Y.; validation, Y.K. and Y.-S.Y.; formal analysis, Y.J.L., J.H., S.J.C., H.I.K. and S.R.; investigation, Y.J.L., J.H., S.J.C., H.I.K. and S.R.; resources, Y.K. and Y.-S.Y.; writing—original draft preparation, Y.K. and Y.-S.Y.; writing—review and editing, Y.K. and Y.-S.Y.; visualization, Y.J.L. and J.H.; supervision, Y.K. and Y.-S.Y. All authors have read and agreed to the published version of the manuscript.

Funding

This research was supported by the National Research Foundation of Korea (NRF) funded by the Korean government (Grant No. 2022M2D2A1A02059163).

Data Availability Statement

Not applicable.

Conflicts of Interest

The authors declare no conflict of interest.

References

  1. Min, S.-J.; Won, J.-J.; Kim, K.-T. Terminal cool-down temperature-dependent hydride reorientations in Zr–Nb Alloy claddings under dry storage conditions. J. Nucl. Mater. 2014, 448, 172–183. [Google Scholar] [CrossRef]
  2. Youn, Y.-S.; Park, J.; Lim, S.H. Stable lattice thermal expansion of ZIRLO™: High-temperature X-ray diffraction results. J. Nucl. Mater. 2019, 523, 66–70. [Google Scholar] [CrossRef]
  3. Kim, S.-S.; Lim, S.; Ahn, D.-H.; Lee, G.-G.; Chang, K. Effect of Inhomogeneous Nucleation of Hydride at α/β Phase Boundary on Microstructure Evolution of Zr–2.5 wt% Nb Pressure Tube. Met. Mater. Int. 2019, 25, 838–845. [Google Scholar] [CrossRef]
  4. Park, S.; Kim, K.-j.; Lee, J.; Kim, J.-Y.; Lee, D.W.; Lim, S.H.; Youn, Y.-S. Synchrotron-based high-resolution photoemission spectroscopy study of ZIRLO cladding with H2O adsorption: Coverage and temperature dependence. Sci. Rep. 2020, 10, 6650. [Google Scholar] [CrossRef]
  5. Kim, J.-S.; Kim, T.-H.; Kim, K.-m.; Kim, Y.-S. Terminal solid solubility of hydrogen of optimized-Zirlo and its effects on hydride reorientation mechanisms under dry storage conditions. Nucl. Eng. Technol. 2020, 52, 1742–1748. [Google Scholar] [CrossRef]
  6. Ha, J.M.; Park, S.; Kwon, E.; Lee, D.W.; Kwon, T.H.; Nam, J.-W.; Lee, J.; Kim, J.-Y.; Lee, H.; Lim, S.H.; et al. Effects of minor alloying elements added in simulated cladding on lattice thermal expansion. J. Nucl. Mater. 2021, 557, 153240. [Google Scholar] [CrossRef]
  7. Topping, M.; Long, F.; Cherubin, I.; Badr, N.N.; Cui, J.; Park, J.S.; Daymond, M.R. Investigating the stability of reoriented hydrides and their reprecipitation using in-situ heating experiments. J. Nucl. Mater. 2022, 564, 153670. [Google Scholar] [CrossRef]
  8. Kim, S.; Kang, J.-H.; Lee, Y. Suppressed hydride precipitation in the welding zone of a zirconium-based alloy cladding tube. J. Nucl. Mater. 2023, 580, 154406. [Google Scholar] [CrossRef]
  9. Stojilovic, N.; Ramsier, R.D. Oxidation of Zircaloy-4 by H2O followed by molecular desorption. Appl. Surf. Sci. 2006, 252, 5839–5845. [Google Scholar] [CrossRef]
  10. Hong, S.I.; Lee, K.W. Stress-induced reorientation of hydrides and mechanical properties of Zircaloy-4 cladding tubes. J. Nucl. Mater. 2005, 340, 203–208. [Google Scholar] [CrossRef]
  11. Colas, K.B.; Motta, A.T.; Daymond, M.R.; Almer, J.D. Effect of thermo-mechanical cycling on zirconium hydride reorientation studied in situ with synchrotron X-ray diffraction. J. Nucl. Mater. 2013, 440, 586–595. [Google Scholar] [CrossRef]
  12. Lee, H.; Kim, K.-m.; Kim, J.-S.; Kim, Y.-S. Effects of hydride precipitation on the mechanical property of cold worked zirconium alloys in fully recrystallized condition. Nucl. Eng. Technol. 2020, 52, 352–359. [Google Scholar] [CrossRef]
  13. Barashev, A.V.; Zhao, Q.; Wang, Q.; Yan, Q.; Gao, F. Cluster dynamics simulation of Zr hydrides formation on grain boundaries in Zr. J. Nucl. Mater. 2022, 561, 153521. [Google Scholar] [CrossRef]
  14. Auzoux, Q.; Bouffioux, P.; Machiels, A.; Yagnik, S.; Bourdiliau, B.; Mallet, C.; Mozzani, N.; Colas, K. Hydride reorientation and its impact on mechanical properties of high burn-up and unirradiated cold-worked stress-relieved Zircaloy-4 and ZirloTM fuel cladding. J. Nucl. Mater. 2022, 568, 153893. [Google Scholar] [CrossRef]
  15. Kim, D.; Woo, D.; Lee, Y. Radial hydride fraction with various rod internal pressures and hydrogen contents for Zr-Nb alloy cladding tube. J. Nucl. Mater. 2022, 572, 154036. [Google Scholar] [CrossRef]
  16. Zanellato, O.; Preuss, M.; Buffiere, J.Y.; Ribeiro, F.; Steuwer, A.; Desquines, J.; Andrieux, J.; Krebs, B. Synchrotron diffraction study of dissolution and precipitation kinetics of hydrides in Zircaloy-4. J. Nucl. Mater. 2012, 420, 537–547. [Google Scholar] [CrossRef]
  17. Raynaud, P.A.; Koss, D.A.; Motta, A.T. Crack growth in the through-thickness direction of hydrided thin-wall Zircaloy sheet. J. Nucl. Mater. 2012, 420, 69–82. [Google Scholar] [CrossRef]
  18. Tupin, M.; Martin, F.; Bisor, C.; Verlet, R.; Bossis, P.; Chene, J.; Jomard, F.; Berger, P.; Pascal, S.; Nuns, N. Hydrogen diffusion process in the oxides formed on zirconium alloys during corrosion in pressurized water reactor conditions. Corros. Sci. 2017, 116, 1–13. [Google Scholar] [CrossRef]
  19. Qin, W.; Liang, J.L.; Cheng, Z.Q.; Shi, M.H.; Gu, D.; Li, T.L.; Zhu, W.L.; Szpunar, J.A. Threshold stress of hydride reorientation in zirconium alloy nuclear fuel cladding tubes: A theoretical determination. J. Nucl. Mater. 2022, 563, 153659. [Google Scholar] [CrossRef]
  20. Courty, O.F.; Motta, A.T.; Piotrowski, C.J.; Almer, J.D. Hydride precipitation kinetics in Zircaloy-4 studied using synchrotron X-ray diffraction. J. Nucl. Mater. 2015, 461, 180–185. [Google Scholar] [CrossRef]
  21. Motta, A.T.; Capolungo, L.; Chen, L.-Q.; Cinbiz, M.N.; Daymond, M.R.; Koss, D.A.; Lacroix, E.; Pastore, G.; Simon, P.-C.A.; Tonks, M.R.; et al. Hydrogen in zirconium alloys: A review. J. Nucl. Mater. 2019, 518, 440–460. [Google Scholar] [CrossRef]
  22. Billone, M.C.; Burtseva, T.A.; Einziger, R.E. Ductile-to-brittle transition temperature for high-burnup cladding alloys exposed to simulated drying-storage conditions. J. Nucl. Mater. 2013, 433, 431–448. [Google Scholar] [CrossRef]
  23. Chu, H.C.; Wu, S.K.; Kuo, R.C. Hydride reorientation in Zircaloy-4 cladding. J. Nucl. Mater. 2008, 373, 319–327. [Google Scholar] [CrossRef]
  24. Won, J.-J.; Kim, M.-S.; Kim, K.-T. Heat-up and cool-down temperature-dependent hydride reorientation behaviors in zirconium alloy cladding tubes. Nucl. Eng. Technol. 2014, 46, 681–688. [Google Scholar] [CrossRef]
  25. Cha, H.-J.; Jang, K.-N.; An, J.-H.; Kim, K.-T. The effect of hydrogen and oxygen contents on hydride reorientations of zirconium alloy cladding tubes. Nucl. Eng. Technol. 2015, 47, 746–755. [Google Scholar] [CrossRef]
  26. Lee, J.-M.; Kim, H.-A.; Kook, D.-H.; Kim, Y.-S. A study on the effects of hydrogen content and peak temperature on threshold stress for hydride reorientation in Zircaloy-4 cladding. J. Nucl. Mater. 2018, 509, 285–294. [Google Scholar] [CrossRef]
  27. Singh, R.N.; Kishore, R.; Singh, S.S.; Sinha, T.K.; Kashyap, B.P. Stress-reorientation of hydrides and hydride embrittlement of Zr–2.5 wt% Nb pressure tube alloy. J. Nucl. Mater. 2004, 325, 26–33. [Google Scholar] [CrossRef]
  28. Daum, R.S.; Majumdar, S.; Liu, Y.; Billone, M.C. Radial-hydride Embrittlement of High-burnup Zircaloy-4 Fuel Cladding. J. Nucl. Sci. Technol. 2006, 43, 1054–1067. [Google Scholar] [CrossRef]
  29. Kim, J.-S.; Kim, T.-H.; Kook, D.-H.; Kim, Y.-S. Effects of hydride morphology on the embrittlement of Zircaloy-4 cladding. J. Nucl. Mater. 2015, 456, 235–245. [Google Scholar] [CrossRef]
  30. Valance, S.; Bertsch, J. Hydrides reorientation investigation of high burn-up PWR fuel cladding. J. Nucl. Mater. 2015, 464, 371–381. [Google Scholar] [CrossRef]
  31. Woo, D.; Lee, Y. Understanding the mechanical integrity of Zircaloy cladding with various radial and circumferential hydride morphologies via image analysis. J. Nucl. Mater. 2023, 584, 154560. [Google Scholar] [CrossRef]
  32. Zlotea, C.; Oumellal, Y.; Provost, K.; Ghimbeu, C.M. Experimental Challenges in Studying Hydrogen Absorption in Ultrasmall Metal Nanoparticles. Front. Energy Res. 2016, 4, 24. [Google Scholar] [CrossRef]
  33. Narayan, T.C.; Hayee, F.; Baldi, A.; Leen Koh, A.; Sinclair, R.; Dionne, J.A. Direct visualization of hydrogen absorption dynamics in individual palladium nanoparticles. Nat. Commun. 2017, 8, 14020. [Google Scholar] [CrossRef]
  34. Namba, K.; Ogura, S.; Ohno, S.; Di, W.; Kato, K.; Wilde, M.; Pletikosić, I.; Pervan, P.; Milun, M.; Fukutani, K. Acceleration of hydrogen absorption by palladium through surface alloying with gold. Proc. Natl. Acad. Sci. USA 2018, 115, 7896–7900. [Google Scholar] [CrossRef] [PubMed]
  35. Gatin, A.; Grishin, M.; Dokhlikova, N.; Ozerin, S.; Sarvadii, S.; Kharitonov, V.; Shub, B. Effect of Size on Hydrogen Adsorption on the Surface of Deposited Gold Nanoparticles. Nanomaterials 2019, 9, 344. [Google Scholar] [CrossRef] [PubMed]
  36. Manzoli, M.; Chiorino, A.; Vindigni, F.; Boccuzzi, F. Hydrogen interaction with gold nanoparticles and clusters supported on different oxides: A FTIR study. Catal. Today 2012, 181, 62–67. [Google Scholar] [CrossRef]
  37. Watkins, W.L.; Borensztein, Y. Mechanism of hydrogen adsorption on gold nanoparticles and charge transfer probed by anisotropic surface plasmon resonance. Phys. Chem. Chem. Phys. 2017, 19, 27397–27405. [Google Scholar] [CrossRef] [PubMed]
  38. Kobayashi, H.; Yamauchi, M.; Ikeda, R.; Yamamoto, T.; Matsumura, S.; Kitagawa, H. Double enhancement of hydrogen storage capacity of Pd nanoparticles by 20 at% replacement with Ir; systematic control of hydrogen storage in Pd–M nanoparticles (M = Ir, Pt, Au). Chem. Sci. 2018, 9, 5536–5540. [Google Scholar] [CrossRef]
  39. Dekura, S.; Kobayashi, H.; Kusada, K.; Kitagawa, H. Hydrogen in Palladium and Storage Properties of Related Nanomaterials: Size, Shape, Alloying, and Metal-Organic Framework Coating Effects. ChemPhysChem 2019, 20, 1158–1176. [Google Scholar] [CrossRef] [PubMed]
  40. Xia, H.; Xiahou, Y.; Zhang, P.; Ding, W.; Wang, D. Revitalizing the Frens Method to Synthesize Uniform, Quasi-Spherical Gold Nanoparticles with Deliberately Regulated Sizes from 2 to 330 nm. Langmuir 2016, 32, 5870–5880. [Google Scholar] [CrossRef]
  41. Zheng, Y.; Zhong, X.; Li, Z.; Xia, Y. Successive, Seed-Mediated Growth for the Synthesis of Single-Crystal Gold Nanospheres with Uniform Diameters Controlled in the Range of 5–150 nm. Part. Part. Syst. Charact. 2014, 31, 266–273. [Google Scholar] [CrossRef]
  42. Khlebtsov, B.N.; Tumskiy, R.S.; Burov, A.M.; Pylaev, T.E.; Khlebtsov, N.G. Quantifying the Numbers of Gold Nanoparticles in the Test Zone of Lateral Flow Immunoassay Strips. ACS Appl. Nano Mater. 2019, 2, 5020–5028. [Google Scholar] [CrossRef]
  43. Wang, Y.; Biby, A.; Xi, Z.; Liu, B.; Rao, Q.; Xia, X. One-Pot Synthesis of Single-Crystal Palladium Nanoparticles with Controllable Sizes for Applications in Catalysis and Biomedicine. ACS Appl. Nano Mater. 2019, 2, 4605–4612. [Google Scholar] [CrossRef]
  44. Wang, L.-m.; He, S.; Cui, Z.-m.; Guo, L. One-step synthesis of monodisperse palladium nanosphere and their catalytic activity for Suzuki coupling reactions. Inorg. Chem. Commun. 2011, 14, 1574–1578. [Google Scholar] [CrossRef]
  45. Baylon, R.A.L.; Sun, J.; Kovarik, L.; Engelhard, M.; Li, H.; Winkelman, A.D.; Wang, Y. Structural identification of ZnxZryOz catalysts for Cascade aldolization and self-deoxygenation reactions. Appl. Catal. B 2018, 234, 337–346. [Google Scholar] [CrossRef]
  46. Nelson, A.E.; Schulz, K.H. Surface chemistry and microstructural analysis of CexZr1−xO2−y model catalyst surfaces. Appl. Surf. Sci. 2003, 210, 206–221. [Google Scholar] [CrossRef]
  47. Lokesha, H.S.; Nagabhushana, K.R.; Singh, F.; Tatumi, S.H.; Prinsloo, A.R.E.; Sheppard, C.J. Unraveling the Charge State of Oxygen Vacancies in Monoclinic ZrO2 and Spectroscopic Properties of ZrO2:Sm3+ Phosphor. J. Phys. Chem. C 2021, 125, 27106–27117. [Google Scholar] [CrossRef]
  48. Yan, Y.; Qian, S.; Garrison, B.; Smith, T.; Kim, P. Nondestructive hydrogen analysis of steam-oxidized Zircaloy-4 by wide-angle neutron scattering. J. Nucl. Mater. 2018, 502, 191–200. [Google Scholar] [CrossRef]
  49. Yamauchi, M.; Ikeda, R.; Kitagawa, H.; Takata, M. Nanosize Effects on Hydrogen Storage in Palladium. J. Phys. Chem. C 2008, 112, 3294–3299. [Google Scholar] [CrossRef]
  50. Kobayashi, H.; Yamauchi, M.; Ikeda, R.; Kitagawa, H. Atomic-level Pd–Au alloying and controllable hydrogen-absorption properties in size-controlled nanoparticles synthesized by hydrogenreduction. Chem. Commun. 2009, 32, 4806–4808. [Google Scholar] [CrossRef]
  51. Bond, G.C. Hydrogenation by gold catalysts: An unexpected discovery and a current assessment. Gold Bull. 2016, 49, 53–61. [Google Scholar] [CrossRef]
Materials 16 06164 g001
Figure 1. Schematic of the influence of metal nanoparticles on hydride formation on zirconium-based cladding under PWR conditions.
Figure 1. Schematic of the influence of metal nanoparticles on hydride formation on zirconium-based cladding under PWR conditions.
Materials 16 06164 g001
Materials 16 06164 g002
Figure 2. Schematic of the front and diagonal views of a zirconium pellet mounted on the sample holder for corrosion experiments; 8 mm diameter zones on both sides of the pellet were in contact with water during the corrosion test.
Figure 2. Schematic of the front and diagonal views of a zirconium pellet mounted on the sample holder for corrosion experiments; 8 mm diameter zones on both sides of the pellet were in contact with water during the corrosion test.
Materials 16 06164 g002
Materials 16 06164 g003
Figure 3. Representative TEM images of (a–c) Au and (e–g) Pd nanoparticles. Histograms of the (d) Au and (h) Pd nanoparticle size distribution; SD and N denote the standard deviation and number of particles counted, respectively.
Figure 3. Representative TEM images of (a–c) Au and (e–g) Pd nanoparticles. Histograms of the (d) Au and (h) Pd nanoparticle size distribution; SD and N denote the standard deviation and number of particles counted, respectively.
Materials 16 06164 g003
Materials 16 06164 g004
Figure 4. (a) XRD and (b) Raman data of the zirconium pellets after the corrosion tests. Bottom panel in (a): Diffraction pattern of monoclinic ZrO2 (PDF#65-1022) obtained from the PDF-2 database.
Figure 4. (a) XRD and (b) Raman data of the zirconium pellets after the corrosion tests. Bottom panel in (a): Diffraction pattern of monoclinic ZrO2 (PDF#65-1022) obtained from the PDF-2 database.
Materials 16 06164 g004
Materials 16 06164 g005
Figure 5. Hydrogen content within the zirconium pellets and the corresponding decrease efficiency after the corrosion experiments with/without various sizes of the synthesized Au and Pd nanoparticles.
Figure 5. Hydrogen content within the zirconium pellets and the corresponding decrease efficiency after the corrosion experiments with/without various sizes of the synthesized Au and Pd nanoparticles.
Materials 16 06164 g005
Disclaimer/Publisher’s Note: The statements, opinions and data contained in all publications are solely those of the individual author(s) and contributor(s) and not of MDPI and/or the editor(s). MDPI and/or the editor(s) disclaim responsibility for any injury to people or property resulting from any ideas, methods, instructions or products referred to in the content.

Share and Cite

MDPI and ACS Style

Lee, Y.J.; Ha, J.; Choi, S.J.; Kim, H.I.; Ryu, S.; Kim, Y.; Youn, Y.-S. Decreasing Hydrogen Content within Zirconium Using Au and Pd Nanoparticles as Sacrificial Agents under Pressurized Water at High Temperature. Materials 2023, 16, 6164. https://doi.org/10.3390/ma16186164

AMA Style

Lee YJ, Ha J, Choi SJ, Kim HI, Ryu S, Kim Y, Youn Y-S. Decreasing Hydrogen Content within Zirconium Using Au and Pd Nanoparticles as Sacrificial Agents under Pressurized Water at High Temperature. Materials. 2023; 16(18):6164. https://doi.org/10.3390/ma16186164

Chicago/Turabian Style

Lee, Yeon Ju, Juhee Ha, Su Ji Choi, Hyeok Il Kim, Sumin Ryu, Youngsoo Kim, and Young-Sang Youn. 2023. "Decreasing Hydrogen Content within Zirconium Using Au and Pd Nanoparticles as Sacrificial Agents under Pressurized Water at High Temperature" Materials 16, no. 18: 6164. https://doi.org/10.3390/ma16186164

Note that from the first issue of 2016, this journal uses article numbers instead of page numbers. See further details here.

Article Metrics

Back to TopTop