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Temperature dependent local atomic displacements in ammonia intercalated iron selenide superconductor

  • Scientific Reports 6, Article number: 27646 (2016)
  • doi:10.1038/srep27646
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Abstract

Recently, ammonia-thermal reaction has been used for molecular intercalation in layered FeSe, resulting a new Lix(NH3)yFe2Se2 superconductor with Tc ~ 45 K. Here, we have used temperature dependent extended x-ray absorption fine structure (EXAFS) to investigate local atomic displacements in single crystals of this new superconductor. Using polarized EXAFS at Fe K-edge we have obtained direct information on the local Fe-Se and Fe-Fe bondlengths and corresponding mean square relative displacements (MSRD). We find that the Se-height in the intercalated system is lower than the one in the binary FeSe, suggesting compressed FeSe4 tetrahedron in the title system. Incidentally, there is hardly any effect of the intercalation on the bondlengths characteristics, revealed by the Einstein temperatures, that are similar to those found in the binary FeSe. Therefore, the molecular intercalation induces an effective compression and decouples the FeSe slabs. Furthermore, the results reveal an anomalous change in the atomic correlations across Tc, appearing as a clear decrease in the MSRD, indicating hardening of the local lattice mode. Similar response of the local lattice has been found in other families of superconductors, e.g., A15-type and cuprates superconductors. This observation suggests that local atomic correlations should have some direct correlation with the superconductivity.

Introduction

Among iron-based layered superconductors, the binary FeSe system with PbO-type structure1 is apparently the simplest system without any spacer layers, that may represent the multiband electronic structure of these materials. The superconducting transition temperature of the binary FeSe is ~8 K and it can be increased by anion substitution in the ternary FeSe1−xTex, showing a maximum Tc of ~15 K. The binary FeSe seems to offer less chemical flexibility than the others because of the lack of any spacers between the active FeSe layers, however, the Tc of FeSe increases sharply to ~37 K2 under the high hydrostatic pressure, a clear hope to manipulate it further. A promising way to increase Tc is the introduction of chemical strain by intercalation of the FeSe layers. Indeed, the binary FeSe was successfully intercalated by alkaline atoms for matching the chemical pressure to the physical pressure, resulting in the discovery of AxFe2−ySe2 (A = K, Cs, Tl) materials with a Tc of ~32 K3,4. The alkaline atom intercalated system is interesting due to its peculiar microstructural properties in which the superconducting quantum state is embedded in a Mott insulating state characterized by a large magnetic moment5, however, its complexity hardly helps to go beyond.

Recently, ammonia-thermal reaction has permitted a simultaneous intercalation of lithium cations, amide anions and ammonia molecules between the FeSe layers, producing Lix(NH3)yFe2Se2 superconductor with Tc depending on the thickness of the intercalated spacer layer (maximum Tc ~ 45 K)6,7,8,9,10,11,12,13. Unlike AxFe2−ySe2 compounds, the new system with molecular spacer layer intercalation is crystallographically homogeneous, however, little is known about its local structure. The physical parameters, which are likely to have major role in the superconducting state, are generally controlled by strain/stress fields due to interlayer interactions. For example, when the binary FeSe is produced as a monolayer grown on SrTiO3 the Tc increases upto ~100 K14. This notable experimental result further confirms that local physics and defect chemistry is playing a central role in the superconducting mechanism. Indeed, iron-based superconductors are multiband systems with the electronic properties highly susceptible to any small disorder15 affecting the local structural parameters16,17, e.g., the bond angle and the anion height from the Fe-Fe layer. In this context it is important to understand what is the response of the local structure to the intercalation of the molecular spacer layer and superconductivity of the intercalated system. In this work, we have addressed some of these issues and studied the local structure of ammonia intercalated Lix(NH3)y Fe2Se2 by means of temperature-dependent x-ray absorption spectroscopy. We have exploited polarization dependence of the absorption cross-section to have direct access to the near-neighbour distances in single crystal samples of Lix(NH3)y Fe2Se2 using extended x-ray absorption fine structure (EXAFS) measurements performed at the Fe K-edge.

Here, the focus is on the in-plane polarized x-ray absorption measurements providing direct access to both Fe-Se and Fe-Fe atomic correlations. Figure 1 shows (k2-weighted) EXAFS oscillations extracted from the in-plane polarized Fe K-edge x-ray absorption spectra measured at several temperatures. The EXAFS oscillations are visible upto high wave vector (k) above the noise level and show clear evolution as a function of temperature. Apart from a thermal damping, the EXAFS oscillations also reveal apparent structural changes (see, e.g., k-range 8–10 Å−1), indicating change in the local structure as a function of temperature. Such changes can be better visualized in the Fourier transform (FT) of EXAFS oscillations, displayed in Fig. 2. The FT magnitudes of EXAFS oscillations provide atomic distribution around the selected atomic site. Therefore, in the Fe K-edge EXAFS the axis origin is placed at the photon-absorbing Fe site while the scatterings with neighbouring atoms appear as peaks in the R-space. The FT are not corrected for the scattering phase-shifts and hence the peaks do not appear at the actual distances from Fe. The double peak structure between 1.5 and 3 Å is due to Fe-Se pair (distance ~2.4 Å) and Fe-Fe pair (distance ~2.7 Å). The peaks appearing at longer distances are due to single scattering contributions of distant shells and multiple scatterings involving different paths, i.e., Fe-Fe (distance ~3.8 Å) and multiple scatterings involving Fe-Se (distance ~4.8 Å), Fe-Fe (distance ~5.3 Å) and Fe-Fe (distance ~5.8 Å). The high quality of EXAFS data can be judged from both EXAFS and FT amplitudes, revealing a systematic temperature evolution.

Figure 1: Temperature evolution of the EXAFS oscillations (k2-weighted) extracted from in-plane polarized Fe K-edge x-ray absorption spectra measured on single crystal sample of Lix(NH3)yFe2Se2 system.
Figure 1

The EXAFS oscillations are shown vertically shifted for a better visualization.

Figure 2: Temperature evolution of Fourier transform (FT) of the EXAFS oscillations measured on Lix(NH3)yFe2Se2 system.
Figure 2

The FTs are performed in the k-range 3–17 Å−1 using a sine-shaped window.

In order to obtain the local structural parameters we have modeled the EXAFS signal using the equation based on single scattering approximation18:

where Ni is the number of neighbouring atoms at a distance Ri, δi is the phase shift, fi(k, Ri) is the back-scattering amplitude, λ is the photoelectron mean free path and is the EXAFS Debye-Waller factor measuring the mean square relative displacements (MSRD) of the photoabsorber-backscatter pairs. The is the so-called passive electrons reduction factor, i.e. EXAFS amplitude reduction factor due to many-body effects related with the losses occurring during the photoelectron propagation in the material (excitations as plasmons, electronhole pairs, etc) and the intrinsic losses due to shake-up and shake-off excitations created by the core-hole in the absorption process. The EXAFS modelling has been carried out by the Artemis package19 that uses the FEFF8 code20 for the phase and amplitude functions. As a starting structure model we have used tetrahedrally coordinated FeSe taken from the known diffraction results6. In the structure, the first coordination shell is composed of 4 Se atoms (at a distance ~2.4 Å) and the second shell is composed of 4 Fe atoms (at a distance ~2.7 Å). The effect of beam polarization (since single crystal samples are used) has been taken into account by introducing an effective number of neighbors considering projections of the bond with respect to polarization vector of the x-ray beam. The is fixed after the analysis of five different EXAFS scans, providing to be 0.5. In the two shells model fits, 5 parameters were floated, i.e., two bond distances (Fe-Se and Fe-Fe), two corresponding σ2 and the photoelectron energy zero (E0). The latter was initially set to 2.5 eV after analyzing different scans at a constant temperature and floated within ±1 eV in subsequent fits to get the best fits at all temperatures. The k-range for the model fits was 3–17 Å−1 while the R-range was 1.5–3.0 Å, providing the number of independent data points21kΔR/π to be ~13. Figure 3 shows examples of the two shells model fits (solid lines) in which 5 parameters were allowed to vary.

Figure 3: Fourier transforms of χ(k) · k2 at two temperatures (empty circles), shown along with the two shells model fits (solid line).
Figure 3

The inset shows the respective back Fourier filtered EXAFS oscillations with model fits (R-interval 1.5–3.0 Å).

Figure 4 shows temperature dependence of the local Fe-Se and Fe-Fe bond distances. While the Fe-Se distance tends to increase with temperature (maximum ΔR ~ 0.005 Å), the Fe-Fe distance remains basically temperature independent. The anion height from the Fe-Fe layer and the associated bond angle have been proposed to be the key parameters for superconductivity in iron-based materials, having a direct relationship with Tc16. The present measurements permit to determine these parameters from the measured bondlengths. Assuming tetrahedral coordination of Se we can determined the Se height (hz) and Se-Fe-Se bond angle (α) using the following relations:

Figure 4: Temperature dependence of the local Fe-Se and Fe-Fe distances obtained from the least-squares fitting of the in-plane polarized Fe K-edge EXAFS oscillations.
Figure 4

Inset shows a sketch of the local coordination environment around Fe atom. The dashed line is a guide to the eyes. The error bars represent uncertainties estimated by analyzing different EXAFS scans and considering correlations between different fit parameters.

Temperature dependence of hz and α are shown in Fig. 5. The two parameters are correlated and they basically describe the same effect of the local bondings. Here, the anion height hz is ~1.46 Å. Incidentally, the hz is found to be ~1.47 Å in FeSe1−xTex with a negligible doping/temperature dependence22,23. Therefore, the intercalation of ammonia seems to induce a compression of hz. Also, the FT peaks (Fig. 2) at longer distances due to Fe-Fe correlations are much stronger in Lix(NH3)yFe2Se2 than in FeSe1−xTex system22,23. This is an indication that the Fe-Fe layer in the ammonia intercalated system should be flatter than the one in the ternary FeSe1−xTex. In addition, a small temperature dependent anomaly in hz and α can be identified, revealing a slight increase in α (decrease of hz) by cooling down across ~200 K and ~50 K. The freezing temperature for ammonia (NH3) is ~195 K and it is possible that the change in the chalcogen height/bond angle at ~200 K to be due to a structural change in the intercalating layer, that may be affecting the local correlations of the active FeSe layer. A recent study has reported an anomaly in the quadrupole splitting ~240 K, measured by Mössbauer spectroscopy, and attributed this to a diffusive motion of Li+-ion within the spacer layers24. Although, the small anomaly in the present work appears at a lower temperature, we can not rule out the small anomaly to be related with the Li+-ion motion, and more work is needed to establish the real cause. On the other hand, the anomaly ~50 K is likely to be related with the superconductivity at which the local Fe-Fe layer is getting thinner and flatter. These small changes can be better seen in the distance-distance correlations given by the σ2, measuring the MSRD.

Figure 5: Temperature evolution of the local hz and α parameters i.e. the Se-height from the Fe-Fe layer and the Se-Fe-Se bond angle, respectively.
Figure 5

These parameters are determined using the measured bond distances. Error bars take account of the correlations beween the RFeSe and RFeFe fit parameters. Cartoons showing definitions of the two parameters are also inserted. The dashed line in the lower panel is a guide to the eyes.

The σ2 is the second moment of the local bondlength distribution function and provides insight to the local bond dynamics. Figure 6 shows temperature dependence of σ2 for the Fe-Se and Fe-Fe distances, obtained from Fe K-edge EXAFS analysis. The temperature dependence of σ2(T) can be described by the Einstein model20,25

Figure 6: EXAFS Debye -Waller factors describing the mean square relative displacements (MSRD) as a function of temperature for the Fe-Se (blue squares) and Fe-Fe bonds (green squares).
Figure 6

The Einstein model (3) fits are shown as grey solid lines.

where kB is the Boltzmann constant, μ is the reduced mass of the considered absorber-backscatterer pair and is a offset related with overall configurational disorder. Here, the σ2(T) for the two bondlengths is well described by the Einstein model down to the transition temperature Tc. However, at T < Tc the σ2 shows a down turn by cooling with a clear deviation from the Einstein-like behavior. Temperature dependent EXAFS permits to determine Einstein temperature ΘE describing the bond stiffness. We have used the data between room temperature and ~50 K to determine ΘE (see, e.g., model fits shown in Fig. 6). The ΘE were found to be 313 ± 10 K and 248 ± 10 K respectively for the Fe-Se and Fe-Fe distances. These values are similar to the known values for the two bonds in the binary FeSe (~318 K and ~268 K22,23,26,27,28). Thus, local bond correlations in Lix(NH3)y Fe2Se2 are very similar to those in binary FeSe while ammonia intercalation seems to be separating the FeSe layers (increase of hz), i.e., decoupling without any appreciable change in the local bond characteristics. It is worth mentioning that, while ΘE for Fe-Se bonds in KxFe2−ySe2 also remains similar to the one in binary FeSe (and hence Lix(NH3)y Fe2Se2), the Fe-Fe bond distance suffers a significant softening due potassium intercalation, with ΘE ~ 200 K26,27.

Another important observation is the abrupt change in the σ2 at T  Tc. Such a change has been already observed in the atomic correlations measured in several superconductors29,30. Here, the change in the σ2 for Fe-Se bond is much smaller than that for the Fe-Fe bond. Earlier EXAFS studies on iron-based systems have pointed out such a change in the Fe-As correlations31, however, it turned out to be very small in the subsequent studies32,33. The presence of this anomaly, indicating a local mode hardening by cooling across Tc, is a clear evidence of some correlation between electron-lattice interactions and superconductivity. The fact that such a local mode hardening below Tc has been observed in different superconductors (e.g., cuprates30, Nb3Ge29 and Fe-based materials), it is likely to be common feature of superconductivity phenomena. It should be mentioned that, for the cuprates the anomaly is associated with Cu-O bond correlations. Iron-based pnictides show anomaly to occur in Fe-Fe correlations while the Fe-As hardly showing such an anomaly34. This may be related with the fact that the electronic states near the Fermi level in iron-based superconductors are mainly driven by Fe 3d orbitals with a limited contribution from the As p orbitals unlike the case of cuprates in which both Cu 3d and O 2p orbitals are strongly contributing. Incidentally, in the present work the anomaly appears not only in Fe-Fe but also the Fe-Se correlations, likely to be due to different anion chemistry in pnictides and chalcogenides. The fact that the anomaly is not always observed in iron-based systems it can be due to differences in their structural topologies and interlayer interactions depending on the kind of spacer layer. For example, REOFeAsO1−xFx (RE = rare-earth) system contains a well ordered REO spacer layer that may screen the anomaly at Tc unlike the systems in which the spacer is not well-defined. The BaFe2As2 is an example of the latter in which the anomalous change at Tc is well evident34. Neverthless, although the anomalous change across Tc suggests involvement of local lattice in the superconductivity, the question remains if this local lattice is directly causing the superconductivity (acting as a glue) or it is a mere consequence of the superconductivity phenomena, i.e., a transition from the incoherent local atomic correlations (in the normal state) to the coherent atomic correlations (in the superconducting state).

In summary, we have studied the local structure of superconducting Lix(NH3)y Fe2Se2 by means of in-plane polarized Fe K-edge EXAFS measurements performed on single crystal samples. We find that the Se-height from the Fe-Fe layer, determined by the direct measurements of Fe-Se and Fe-Fe bondlengths, appears shrinked in the intercalated system with respect to the binary FeSe. In addition to the compressed FeSe4 tetrahedron, the results reveal that the bond length characteristics, measured by the temperature dependence of the mean square relative displacements, hardly show any effect of the molecular layer intercalation. On the other hand, the local structure response to the superconductivity appears as an anomalous change in the MSRD across the superconducting transition temperature Tc, an indication of a sudden change in the atomic correlations in the superconducting phase. It is argued that the higher Tc of the ammonia intercalated system should be related with an effective compression of the FeSe-layers (with flatter Fe-Fe layer) and interlayer decoupling due to a thick spacer layer. Neveretheless, the results underline importance of the local atomic correlations in the superconductivity of these materials.

Methods

Sample synthesis and characterization

Single crystal samples of Lix(NH3)y Fe2Se2 were synthesized using liquid ammonia as a solvent. Several single crystals of FeSe and dopant metal in the appropriate ratio were placed in a glass tube. NH3 gas was condensed in the glass tube by cooling with liquid N2. The glass tube was filled with liquid NH3 (~10 ml) and was sealed. After the intercalation reaction, the liquid NH3 was removed by heating and dynamically pumping the glass tube, finally obtaining metal-doped single crystals. The samples were handled in a glove box (O2 ≤ 0.5 ppm and H2O ≤ 0.5 ppm). The samples were characterized by in-house X-ray diffraction (XRD) from the basal plane of single crystals of parent FeSe and Lix(NH3)y Fe2Se2 using a RIGAKU Ultima IV at room temperature with Co source (λ = 1.79 Å). The structural parameters obtained on the single crystal samples studied in the present work are consistent with those reported for polycrystalline samples6. The c-axis of the intercalated sample was found to be 17.24 Å for I4/mmm structure. The magnetization measurements were carried out using a SQUID magnetometer (MPMS-R2 and MPMS3, Quantum Design Co. Ltd.). The temperature dependent resistivity was measured using a Physical Properties Measurement System (PPMS, Quantum Design Co. Ltd. with magnetic field up to 9 Tesla). The quantitative composition of the samples was determined by analyzing energy dispersive x-ray (EDX) spectra obtained with a VE-9800SP (Keyence Co. Ltd.) equipped with a scanning electron microscope (SEM). The EDX spectra were obtained from the cleaved surfaces of single crystals of Lix(NH3)y Fe2Se2. Li and NH3 concentrations were determined by analyzing inductively coupled plasma (ICP) atomic emission spectroscopy (Vista-pro, Seiko Instruments Co. Ltd.), and found to be x ~ y ~ 0.11 for the samples used in the present study.

X-ray absorption measurements

Single crystal samples were used for the EXAFS measurements. Temperature dependent x-ray absorption measurements were carried out at the CLÆSS beamline of the ALBA synchrotron in Cerdanyola del Valles (Barcelona) where the synchrotron radiation emitted by a multipole wiggler was monochromatized by a Si(111) double crystal monochromator and Rh-coated mirrors were used to reject higher harmonics. Due to the alkali-metal content, the samples are prone to degradation if placed in ambient atmosphere. To avoid degradation, all the preparation procedures were performed in glovebox under Ar atmosphere, samples were then transfered to the measurement stage. The samples were exfoliated for transmission measurements to reach the desired thickness for absorption jump to be ~1 at the Fe K-edge energy (7112 eV). The absorption experiments were carried out in the normal incidence geometry exploiting three ionization chambers mounted in series to measure the energy-dependent absorption coefficient of the sample and a reference Fe-foil at the same time. In the geometry the polarization of the x-ray beam is parallel to the ab-plane of the single crystal samples. Samples were mounted on a cold finger attached to a Helium cryostat and measured in the temperature range of 13–300 K. The sample temperature was maintained within ±0.5 K during each data acquisition. Several scans were collected for any given temperature to ensure reproducibility and improve the signal-to-noise ratio.

Additional Information

How to cite this article: Paris, E. et al. Temperature dependent local atomic displacements in ammonia intercalated iron selenide superconductor. Sci. Rep. 6, 27646; doi: 10.1038/srep27646 (2016).

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Acknowledgements

We thank ALBA staff for the assistance during the measurements. One of us (T.W.) would like to acknowledge hospitality at the Sapienza University of Rome. This research was partially supported by the Program for Promoting the Enhancement of Research University from MEXT and the Program for Advancing Strategic International Networks to Accelerate the Circulation of Talented Researchers from JSPS. The support from the Grant-in-Aid for Scientific Research from the Japan Society for the Promotion of Science coordinated by M. Nohara (26287082 and 15H05886), K. Kudo (25400372 and 15H01047), by T. Kambe (15H03529) is acknowledged. The work is a part of the executive protocol of the general agreement for cooperation between the Sapienza University of Rome and the Okayama University, Japan. The work at Sapienza is partially supported by PRIN2012 (grant number 2012X3YFZ2) of MIUR, Italy.

Author information

Author notes

    • T. Wakita
    • , K. Terashima
    • , K. Kudo
    • , M. Nohara
    •  & T. Yokoya

    Present address: Research Institute for Interdisciplinary Science, Okayama University, Okayama 700-8530, Japan.

Affiliations

  1. Dipartimento di Fisica, Sapienza Universitá di Roma, P. le Aldo Moro 2, 00185 Roma, Italy

    • E. Paris
    •  & N. L. Saini
  2. Center for Life NanoScience@Sapienza, Istituto Italiano di Tecnologia, V. le Regina Elena 291, 00185 Rome, Italy

    • E. Paris
  3. ALBA Synchrotron Light Facility, Carrer de la Llum 2-26, 08290 Cerdanyola del Vallés, Barcelona, Spain

    • L. Simonelli
    • , C. Marini
    •  & W. Olszewski
  4. Research Laboratory for Surface Science, Okayama University, Okayama 700-8530, Japan

    • T. Wakita
    • , K. Terashima
    •  & T. Yokoya
  5. Research Centre of New Functional Materials for Energy Production, Storage and Transport, Okayama University, Okayama 700-8530, Japan

    • T. Wakita
    • , K. Terashima
    • , K. Kudo
    • , M. Nohara
    •  & T. Yokoya
  6. Department of Physics, Okayama University, Kita-ku, Okayama 700-8530, Japan

    • J.-H. Lee
    • , T. Kakuto
    • , N. Nishimoto
    • , T. Kimura
    • , K. Kudo
    • , T. Kambe
    •  & M. Nohara
  7. Faculty of Physics, University of Bialystok, 1L K. Ciokowskiego Str., 15-245 Bialystok, Poland

    • W. Olszewski

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Contributions

N.L.S., T.Y., T. Kambe and M.N. programmed and coordinated the study. J.-H.L., T. Kakuto, N.N., T. Kimura, K.K., T. Kambe and M.N. have synthesized the single crystals used for the study. E.P., L.S., T.W., C.M., W.O. and N.L.S. performed the experiments at the CLAESS beamline of the ALBA synchrotron facility and contributed in the data analysis. N.L.S., T.Y., T. Kambe, T.W. and K.T. were part of the scientific discussions on the analysis and interpretations. E.P. and N.L.S. wrote the preliminary draft of the manuscript that was discussed by all the authors to produce the final draft with key inputs from T. Kambe and T.Y.

Competing interests

The authors declare no competing financial interests.

Corresponding author

Correspondence to N. L. Saini.

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