Abstract
Infinite-layer (IL) nickelates are an emerging class of superconductors, where the Ni1+ valence state in a square planar NiO2 coordination can only be reached via topotactic reduction of the perovskite phase. However, this topotactic soft chemistry with hydrogenous reagents is still at a stage of rapid development, and there are a number of open issues, especially considering the possibility of hydrogen incorporation. Here, we study the time dependence of the topotactic transformation of LaNiO3 to LaNiO2 for powder samples with x-ray diffraction and gas extraction techniques. While the hydrogen content of the powder increases with time, neutron diffraction shows no negative scattering of hydrogen in the LaNiO2 crystal lattice. The extra hydrogen appears to be confined to grain boundaries or secondary-phase precipitates. The average crystal structure, and possibly also the physical properties, of the primary LaNiO2 phase are, therefore, not noticeably affected by hydrogen residues created by the topotactic transformation.
1 Introduction
Superconductivity exists in various hydrogen-containing compounds, highlighted by the recent discoveries of critical temperatures Tc as high as room temperature for hydride compounds formed under extreme pressures [1, 2]. Metal hydroxide–intercalated iron chalcogenides, such as (Li0.8Fe0.2)OHFeSe [3], show coexistence of antiferromagnetic order and superconductivity, a feature known from some high-Tc superconductors [4]. Electron-doped 1111 iron pnictides, such as RFeAsO1−xHx [5, 6], CeFeAsO1−xHx [7], and the pnictogen-free LaFeSiH [8] are a class, where the introduction of charge carriers via doping with hydrogen drives the system from an antiferromagnetically ordered state toward superconductivity. In layered sodium cobalt oxyhydrate, NaxCoO2·H2O [9], superconductivity with a similar hole/electron-doping behavior by chemical substitution is observed as in the cuprate high-Tc superconductors [10].
For IL nickelates, a close relation and possible analogy to cuprate superconductors was suggested already in 1999 [11], and since the first discovery of superconductivity in the IL nickelate (Nd,Sr)NiO2 [12], the observation of superconductivity has been confirmed [13–15] and extended to (Pr,Sr)NiO2 [16], (La,Sr)NiO2 [17], (La,Ca)NiO2 [18], and Nd6Ni5O12 [19]. Furthermore, a recent work reported superconductivity not only for films grown on SrTiO3 substrates but also on LSAT [20], which provides enough evidence to consider thin-film nickelates as a novel class of superconductors. The possible presence of topotactic hydrogen in IL nickelates, which depends on the rare-earth ion and/or epitaxial strain [21, 22], was proposed in theoretical studies [23, 24] and might have substantial influence on the electronic and magnetic properties of the IL nickelates, as LaNiO2H would realize a two-orbital Mott insulator [23]. A hint toward the possibility of hydrogen incorporation was provided by an early study of topotactically reduced NdNiO3 films, which showed an oxyhydride NdNiO3−xHy phase with a defect-fluorite structure in the surface region [25]. Furthermore, topotactic hydrogen can be found in SrTiO3 thin films [26], that is, the material that is commonly used as a substrate and capping layer for IL nickelate films, which again provides a possible route for inclusion of hydrogen in infinite-layer nickelate thin films. While superconductivity has remained elusive in IL nickelates in bulk form, with studies on powder samples reporting insulating behavior [27, 28], a first step toward superconductivity was taken by our recent investigation of (La,Ca)NiO2 single crystals [29], where metallicity was observed.
In this study, we address the issue of possible hydrogen incorporations in IL nickelates by examining bulk LaNiO3−xHy powder samples with a combination of x-ray and neutron diffraction studies, gas extraction, and complementary high-pressure synthesis attempts of LaNiO2H.
2 Methods
LaNiO3 powder samples with grain sizes of 0.5 μm were synthesized via the citrate–nitrate method as described in Ref. [30]. The method is optimal as the relatively small grains enhance the surface to bulk ratio, reducing reduction times. Moreover, higher purity can be reached than by high-pressure powder synthesis. The IL phase LaNiO2 can be obtained solely through topotactic reduction of the perovskite LaNiO3 phase, which is here achieved by using CaH2 as the reducing agent [27, 28]. We reduced 50 mg of LaNiO3 powder wrapped in aluminum foil, spatially separated from 250 mg CaH2 powder at 280°C, as described in detail in Ref. [30], for various times.
We measured the stoichiometry including the hydrogen content with a combination of inductively coupled plasma mass spectroscopy (ICP-OES) and gas extraction; the former with a SPECTRO CIROS CCD and the latter with an Eltra ONH-2000 analyzer. For the determination of oxygen and hydrogen content, the powder samples were placed in a Ni crucible and clipped and heated, where the carrier gas takes the oxygen and hydrogen out of the sample. The oxygen reacts with carbon, and CO2 is detected in an infrared cell, while hydrogen is detected by a thermal conductivity cell. Each measurement is repeated three times and compared to a standard. The quoted error bars provide the statistical error.
Powder x-ray diffraction (PXRD) data were collected using a Rigaku MiniFlex with a Cu Kα tube at room temperature. Neutron diffraction was performed at the high-resolution powder neutron diffractometer HRPT [31] at the Spallation Neutron Source SINQ at the Paul Scherrer Institute in Villigen. For the HRPT experiments, an amount of 340 mg of LaNiO2 was enclosed into a vanadium can with an inner diameter of 6 mm, where the remaining space of the vanadium can was shielded with Cd foil, and the measurement was carried out at 1.5 K in a 4He bath cryostat with a neutron wavelength of 1.15 Å.
3 Results
As a first step, we checked the purity and stoichiometry of our starting material in the perovskite phase. In PXRD, we found no detectable impurities, and ICP combined with measurements of gas extraction indicated a starting stoichiometry of La0.99(1)Ni0.99(1)O2.99(3)H0.005(2). We studied the reduction progress with time in detail by preparation of several ampules and extracting samples after varying reduction times and analyzed all the products with PXRD. We noticed that the progress of the reduction depends on the purity and sample amount and grain size for a given time as the reduction process is surface-dependent. Motivated by these observations, we carried out a standardized reduction on the same batch of perovskite precursors. After 1 day of reduction in the described process (see Section 2) we found a full structural transition to LaNiO2.5 (see Figure 1). Our Rietveld refinement of the LaNiO2.5 crystal structure is in good agreement with previous reports on reduced powder [32–34]. Notably, reduction times of 1 day and longer are in stark contrast to thin-film samples, which can be fully reduced to the IL phase within hours [12–18, 35, 36], presumably due to the enhanced thickness of our grains, with sizes of 0.5 μm as extracted from scanning electron microscopy (SEM) images. The reduction appears to be happening in domains, as we found cluster spin glass behavior in a detailed magnetic characterization [30], and thus after longer reduction times than 1 day, we observe phase mixtures of LaNiO2.5 in P21/n (#14) [33] and LaNiO2 in P4/mmm (#123) [37], with a slowly increasing fraction of the LaNiO2 phase as a function of time (see Figure 2). Extracting the weight percentages from our refinement, we present the reduction progress for the CaH2 reduction in analogy to a thermogravimetry (TG) curve, which is shown in Figure 2. The reduction process follows an exponential decay, which we also observed in thermogravimetry studies in hydrogen gas flow (not shown here). After a reduction time of approximately 316 h, the crystal structure can be refined assuming a single phase of IL LaNiO2 (Figure 2, and Ref. [30]). Notably, while the structural transition does not progress further on an exponential time scale, a small amount of apical oxygen remains in the crystal lattice, as will be revealed by neutron diffraction below. However, for even longer reduction times, the sample begins to decompose, forming Ni and La2O3, which becomes clearly visible in PXRD after 400 h (Figures 1, 2).
FIGURE 1
FIGURE 2
In the inset of Figure 2, we plot the hydrogen content in the resulting powder samples versus reduction time, obtained by a gas extraction method. While the initial perovskite nickelate shows a hydrogen content of 0.005(2) wt%, we find increase of hydrogen with time (opposite to the oxygen content), with 0.065(3) wt% for 24 h, 0.094(3) wt% for 38 h, 0.015(5) wt% for 240 h, and finally 0.169(7) wt% after 320–376 h. Via gas extraction, we find an oxygen content of 14.1(2) wt% after 316 h and 14.0(2) wt% after 320–376 h of reduction, where 14 wt% corresponds to a full reduction to the LaNiO2 IL phase. If we assume that the amount of hydrogen would be incorporated into the average crystal structure, the corresponding effective stoichiometry of the sample investigated with neutrons would be La0.99(1)Ni0.99(1)O2.00(2)H0.39(2), where La and Ni are determined via ICP. However, a first hint that this might not be the case comes from the presence of small amounts of elemental Ni in the PXRD of the 400-h sample (Figure 1), which is known to trap hydrogen [38]. The Rietveld refinement of the neutron diffraction data below also indicates a small amount of Ni. Furthermore, signatures of Ni precipitates (below the detection threshold of our PXRD) were also detected in powders after shorter reduction times since they give rise to ferromagnetic contributions in the magnetic signal [30]. The amount of Ni likely increases with reduction time, which could explain the increasing capability of incorporating hydrogen.
As a next step, we performed high-resolution neutron diffraction experiments on 340 mg of a sample prepared by mixing batches that had been subject to reduction times of 320, 350, and 376 h, respectively which are all in the range just before the start of the clear decay shown in Figure 2. The obtained neutron diffraction pattern can be well refined (see Figure 3) assuming LaNiO2 in the IL P4/mmm structure (see Table 1), with a c-axis parameter of 3.3588(3) Å, which is lower than previously reported values [29, 30, 37], and 1.1(2) wt% of elemental Ni was included as a secondary phase.
FIGURE 3
TABLE 1
| , | |||||
|---|---|---|---|---|---|
| Atom | x | y | Z | Occ | |
| La (1d) | 0.5 | 0.5 | 0.5 | 0.003 6(6) | 1 |
| Ni (1a) | 0 | 0 | 0 | 0.005 7(5) | 1 |
| O (2f) | 0 | 0.5 | 0 | 0.009 8(5) | 1 |
| O (1b) | 0 | 0 | 0.5 | 0.009 8(5) | 0.06(1) |
| Reliability factors | χ2 | RB | Rf | ||
| 1.89 | 3.53 | 2.79 | |||
Refined atomic coordinates of LaNiO2 in tetragonal space group P4/mmm with preferred orientation extracted from powder neutron diffraction data at 1.5 K (Figure 3).
Figure 4 shows a Fourier map of the scattering density resulting from the Rietveld refinement of the neutron data, where the range of the color scheme is chosen to focus on the negative scattering length of hydrogen. While the used reduction temperatures (see Section 2) are too low to enable significant mobility of the La and Ni ions, the purpose of our topotactic treatment is to reduce oxygen, which becomes mobile and is extracted by reaction with hydrogen. We, therefore, focus on the scattering lengths of the two elements O and H. According to the theoretical prediction of Ref. [23], intercalation of H in IL nickelates is most favorable on the vacant apical oxygen sites with Wyckoff position (1b), or on interstitial positions between the rare-earth ions (Wyckoff positions (2e) and (1c)). Another theoretical work [24] predicts that NdNiO2 is unstable, while NdNiO2H is not and also proposes the apical oxygen site with Wyckoff position (1b) for hydrogen. However, as shown in the Fourier maps of Figure 4, we find no significant negative scattering, which would appear as blue in our plots. The slightly negative scattering realized as a ring around a reflex, here in close proximity to La, is an artifact from the Fourier transformation, typically seen around larger ions [39] due to a signal cutoff from a finite q range. This is best seen in the Fourier maps Figures 4E,F. We note that the data can be refined with similar reliability factors as in Table 1 by putting a mixture of O and H on Wyckoff position (1b) and constraining their occupation. As the positive scattering observed at this site could be a mixture of negative scattering of H and positive scattering of O, which effectively clouds the negative scattering. Realized in a substitution series with LaNiO3−xHx, which would yield occupations of O: 0.430(8) and H: 0.570(8) in refinements of our data, but this oxygen content is way higher than what can be found in multiple gas extraction experiments (La0.99(1)Ni0.99(1)O2.00(2)H0.39(2)). Most importantly, the scenario of LaNiO3−xHx would hint toward the possibility to synthesize the phase directly, similar as observed in the iron pnictides. However, such synthesis attempts have been carried out as described below and were not successful. Furthermore, in the case of iron pnictides, hydrogen substitution leads to no structural transitions [5–7], contrasting the evolution of the underlying structural transitions in LaNiO3−x according to the PXRD data (see Figure 1) and literature [37]. Another possibility to refine mixed occupancy is by constraining an equal occupation of O and H as LaNiO2(OH)x, which converges to 0.18(4). However, this would rather suggest an OH molecule with typical distances around 0.84 Å, which would realize negative scattering [39] and, thus, reduces the quality of the fit and shifts the occupation again down to 0.06(1). Thus, we conclude that intercalated hydrogen is unlikely in our LaNiO2+δ powder sample. Nevertheless, we find the presence of a small amount of residual apical oxygen in Wyckoff position (1b), which corresponds to a deviation of δ = 0.06(1) from the ideal stoichiometry.
FIGURE 4
In addition, we attempted direct synthesis approaches of LaNiO3−xHx as, for example, LaNiO2H via a Walker-type high-pressure synthesis in NaCl crucibles. We mixed La2O3 and NiO with NaH or CaH2 and heated it to 650–1000°C under a pressure of 5–7 GPa, but were unable to synthesize any oxyhydride nickelate. Instead, we obtained La(OH)3 and Ni, which is in contrast to related cases, such as SmFeAsO1−xHx [5], BaCrO2H [41], BaScO2H [42], and SrVO2H [43].
4 Conclusion
In summary, we have synthesized high-quality LaNiO2+δ powders and found some density of residual oxygen (δ = 0.06(1)) even at the final stage of the topotactic reaction, just prior to decomposition of our samples. While our gas extraction method reveals partial hydrogen inclusions in the powder samples, high-resolution neutron diffraction refinements show that there is no clear topotactic hydrogen in LaNiO2, and direct attempts to synthesize LaNiO3−xHx were unsuccessful. The hydrogen detected by gas extraction could be trapped in Ni impurities that increase with increasing reduction time and/or ascribed to phenomena at surfaces or grain boundaries, such as water adsorption/intercalation [44] on powder surfaces or partial formation of LaNiO3−xHx on the nanometer scale [25]. Notably, a relatively high density of grain boundaries/crystallographic defects was reported for IL nickelate thin films [45], and also surface effects can play a more decisive role in films. Thus, future studies clarifying the presence and impact of hydrogen in nickelate thin-film samples are highly desirable.
Statements
Data availability statement
The raw data supporting the conclusion of this article will be made available by the authors, without undue reservation.
Author contributions
PP, MI, BK, and MH conceived the project. RO carried out the topotactic reductions. PP and VP conducted the neutron diffraction experiments. SH executed the ICP and gas extraction measurements. PP analyzed the data and prepared the manuscript with input from all authors.
Funding
We acknowledge financial support by the Center for Integrated Quantum Science and Technology (IQST) and the Deutsche Forschungsgemeinschaft (DFG, German Research Foundation): Projektnummer 107745057—TRR 80. The Max Planck Society is acknowledged for funding of the open-access fee.
Acknowledgments
We thank R. Merkle and A. Fuchs for the synthesis of LaNiO3 and H. Hoier for preliminary PXRD characterizations. We acknowledge PXRD measurements by C. Stefani from the X-ray Diffraction Scientific Facility at an early stage of this work. The use of facilities of the Quantum Materials Department of H. Takagi for the attempted high-pressure synthesis of LaNiO2H is gratefully acknowledged.
Conflict of interest
The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.
Publisher’s note
All claims expressed in this article are solely those of the authors and do not necessarily represent those of their affiliated organizations, or those of the publisher, the editors, and the reviewers. Any product that may be evaluated in this article, or claim that may be made by its manufacturer, is not guaranteed or endorsed by the publisher.
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Summary
Keywords
infinite-layer nickelates, topotactic reduction, superconductivity, neutron diffraction, gas extraction, x-ray diffraction, hydrogen
Citation
Puphal P, Pomjakushin V, Ortiz RA, Hammoud S, Isobe M, Keimer B and Hepting M (2022) Investigation of Hydrogen Incorporations in Bulk Infinite-Layer Nickelates. Front. Phys. 10:842578. doi: 10.3389/fphy.2022.842578
Received
23 December 2021
Accepted
01 February 2022
Published
14 March 2022
Volume
10 - 2022
Edited by
Veerpal Singh Awana, National Physical Laboratory (CSIR), India
Reviewed by
Andrés Cano, UPR2940 Institut Neel (NEEL), France
Atsushi Fujimori, Waseda University, Japan
Updates
Copyright
© 2022 Puphal, Pomjakushin, Ortiz, Hammoud, Isobe, Keimer and Hepting.
This is an open-access article distributed under the terms of the Creative Commons Attribution License (CC BY). The use, distribution or reproduction in other forums is permitted, provided the original author(s) and the copyright owner(s) are credited and that the original publication in this journal is cited, in accordance with accepted academic practice. No use, distribution or reproduction is permitted which does not comply with these terms.
*Correspondence: P. Puphal, puphal@fkf.mpg.de
This article was submitted to Condensed Matter Physics, a section of the journal Frontiers in Physics
Disclaimer
All claims expressed in this article are solely those of the authors and do not necessarily represent those of their affiliated organizations, or those of the publisher, the editors and the reviewers. Any product that may be evaluated in this article or claim that may be made by its manufacturer is not guaranteed or endorsed by the publisher.