Synthesis and Characterization of Superconducting Ca₁-xNaxFFeAs.

A representative of the fluoride-containing iron pnictide high-temperature superconductors, namely CaFFeAs, was doped with sodium up to the composition Ca0.86Na0.14FFeAs for the first time. Single crystals with an edge length in the range of 0.1 - 2.0 mm were obtained via solid-state and flux syntheses, respectively. The composition of the crystals was verified by means of single crystal X-ray diffractometry and energy dispersive X-ray spectroscopy (EDX). Measurements of the electrical resistivity, as well as the magnetization on a crystal of Ca0.89Na0.11FFeAs both show a transition to the superconducting state on cooling to 34.5 K. Investigations of the upper critical fields reveal an anisotropy ratio of about five. The lattice parameters and molar volumes increase with rising sodium content. This effect is clearly observable for the c-axis and the volume, whereas the increase of the a-axis is rather minor.

Introduction

With the detection of superconductivity in iron pnictides in 2008 [1,2], a new class of high-temperature superconductors [3] was found 22 years after the discovery of this phenomenon in oxocuprates [4]. The so-called 1111 phases can be derived from LaOFeAs [5,6] with a tetragonal ZrSiCuAs-type structure, in which isotypical cationic [LaO]+ and anionic [FeAs]− layers alternate. An isotypic class is the series, AeFFeAs (Ae = Ca, Sr, Eu) [7-9], which results from the exchange of oxygen by fluorine and lanthanum by divalent alkaline-earth metals or europium, respectively. Meanwhile, several structurally related types of such iron pnictides became known [10]. Analogous to the oxocuprates, the superconductivity occurs in two-dimensional antiferromagnetically ordered layers, based on iron-centered edge-linked pnictogen tetrahedra. Within the 1111 compounds, superconductivity is only observed if a partial reduction (electron doping) or oxidation (hole doping) in the [FeAs]− layers occurs [11]. Critical temperatures between T = 26 and 43 K for LaO1−FFeAs [2,12] and 55 to 58 K for SmO1−FFeAs [13,14] were achievable for fluoride-doped samples, whereas the strontium substituted oxide La1–SrOFeAs [15] exhibits a transition temperature of T = 25 K.

Up to now, only electron-doped derivatives of the fluorine containing the 1111 compound CaFFeAs, like CaFFe1−CoAs [7] and Ca1−FFeAs (Ln = Pr, Nd) [16], are reported to superconduct. After the discovery of superconductivity in 1111 phases, hole doping on LaOFeAs with Ca2+ was already investigated without the detection of any superconducting phases [2]; the reason why electron doping was claimed as a critical factor for the generation of superconductivity in this system at that time. However, this view was disproven by hole-doped La1−SrOFeAs with T = 25 K for x = 0.13 three months later [15].

Results and Discussion

In the present work, we show that it is possible to attain high-temperature superconductivity on alkaline metal-doping of a fluorine containing the 1111 phase for the first time. CaFFeAs [7] was doped with sodium, resulting in the solid-solution series, Ca1−NaFFeAs (x = 0 – 0.14), prepared via a solid-state reaction method. Ca1−NaFFeAs consists of small platelet-like crystal aggregates (Figure 1) sufficient in size and quality for single crystal X-ray analysis (about 0.1 × 0.1 mm2). Larger single crystals with a composition of Ca0.89Na0.11FFeAs and a size up to 2 × 2 mm2 were grown in a flux of sodium chloride for physical measurements.

Figure 1.

Crystal aggregates of Ca1−NaFFeAs viewed via an optical (left) and an electron microscope (right). The inset shows a Laue-image of a representative single crystal.

Crystal Structure and Crystallographic Data of Ca1−xNaxFFeAs

The 1111 phase CaFFeAs [7] crystallizes in the tetragonal ZrCuSiAs-type structure, representing a filled PbFCl variant, in the space group P4/nmm with Z = 2. The structure consists of alternating isotypic cationic [FCa4/4]+ and anionic [FeAs4/4]− layers of edge-connected tetrahedra (Figure 2).

Figure 2.

Crystal structure of Ca1−NaFFeAs. (a) The view along [010]; (b) a three-dimensional picture and (c) top view of a [FeAs4/4]− layer along [001].

Sodium partly substitutes calcium in Ca1−NaFFeAs on the 2c position. From the four crystallographically independent atoms, iron and fluorine are both tetrahedrally coordinated, whereas arsenic and calcium are surrounded in the form of square antiprisms built from four counter ions of each kind (Figure 3).

Figure 3.

Coordination polyhedra around the four crystallographically independent atoms in Ca1−NaFFeAs.

Crystallographic data for selected representatives of the substitution series Ca1−NaFFeAs are listed in Table 1. More detailed crystallographic information can be found in the supplementary part (Tables S1–S4).

Table 1.

Crystallographic data for selected crystals of Ca1−NaFFeAs.

x in Ca1−xNaxFFeAs		0	0.03	0.08	0.14
Crystal system		tetragonal
Space group		P4/nmm (Z = 2)
Lattice parameters	a/pmc/pmc/a	387.57(9)858.4(2)2.215	387.57(2)859.48(5)2.218	387.65(2)859.89(6)2.218	387.68(3)859.87(9)2.218
Vm/cm3·mol−1		38.83	38.87	38.91	38.91
Dx/g·cm−3		4.89	4.87	4.84	4.82
Diffractometer		Nonius KappaCCD (Bruker AXS, Karlsruhe, Germany)
Radiation		Mo-Kα (λ = 71.07 pm)
Collected reflections		1589	2278	3232	1622
Unique reflections		118	145	211	118
Rint, Rσ		0.083, 0.028	0.060, 0.018	0.068, 0.021	0.104, 0.039
R1, wR2		0.076, 0.157	0.018, 0.044	0.022, 0.053	0.026, 0.058
GooF		1.178	1.168	1.166	1.165
Solution and refinement		Program package SHELX-97 [17,18]

Phase Analysis of Ca1−xNaxFFeAs and Discussion

Powder X-ray diffractometry verifies the presence of the target compound in each sample of the series. For x ≥ 0.1, however, an increasingly larger portion of secondary phases arises (Figure 4).

Figure 4.

X-ray powder diffraction patterns (Mo-Kα1 radiation) of the doping series with the target composition Ca1−NaFFeAs (x = 0 – 0.2).

Energy dispersive X-ray spectroscopy (EDX) measurements confirm a certain amount of dopants in the target compounds. The crystals of Ca1−NaFFeAs exhibit compositions in a rather narrow range from Ca0.99Na0.01FFeAs to Ca0.86Na0.14FFeAs, depending on the sodium concentration used in the synthesis. Single crystals of the series Ca1−NaFFeAs can be structurally refined with the compositions from the EDX analyses (Table 1). Figure 5 shows the development of the lattice parameters, a and c, as well as the molar volume, V, of Ca1−NaFFeAs for x = 0, 0.03, 0.08 and 0.14 as a function of the sodium content. The ionic radii with a coordination number of eight are 112 and 118 pm for Ca2+ and Na+, respectively [19]. The expected increase of the lattice parameters and volume for a rising sodium content is only slightly realized for the a-axes, while the increase in the c-axes and, subsequently, the volumes are more visible. For the compound Ca0.86Na0.14FFeAs with the highest degree of substitution, the a-axis increases by 0.02% and the c-axis by 0.17%, as compared to the unsubstituted compound. An almost unchanged a-axis has been observed previously in the case of hole-doped La0.87Sr0.13OFeAs [15], whereas the unit-cell size even decreases with increasing sodium content in the case of Ca1−NaFe2As2 [20]. The observed increase of the c-axis for Ca1−NaFFeAs lies in the similar range as in La0.87Sr0.13OFeAs (0.34%). The rather small rise of the c-axis length, as well as the molar volume may indicate a slight overestimation of the sodium content, particularly for the crystal with highest degree of substitution (x = 0.14).

Figure 5.

Lattice parameters and molar volumes of Ca1−NaFFeAs phases versus the sodium doping grade x (from energy dispersive X-ray spectroscopy (EDX)).

A closer look at the equivalent isotropic displacement parameters (see the Supplementary Information, Table S2) shows that the ones for the Ca/Na position remain nearly constant for x > 0. The parameters of the other atoms increase with rising sodium content. This effect could be explained with an incremental static displacement of the F, Fe and As atoms for an increasing Na level via the statistical occupation of the 2c position (Ca/Na). The atomic coordinates of the Ca1−NaFFeAs crystals do not indicate a significant change with rising substitution grade. This is the reason for the virtually unmodified distances, e.g., d(Ca/Na–F) = 233 – 234 pm, d(Ca/Na–As) = 316 – 317 pm, d(Fe–As) = 240 pm and d(Fe–Fe) = 274 pm, and angles, e.g., ∢(As–Fe–As′) = 107.7° – 108.8° and 110.3° – 103.4°, within the series (see Table S4 of the Supplementary Information for details). Therefore, it seems that the variation of the electron count of iron via doping is exclusively responsible for the appearance of superconductivity in this system.

Magnetization and Resistivity Measurements on Ca1−xNaxFFeAs

Magnetization measurements on Ca1−NaFFeAs-containing powder samples indicate the occurrence of superconductivity. In the range of nominal composition of x = 0.1 – 0.2, a transition temperature to superconductivity of 34 K was observed, regardless of the doping level (Figure 6).

Figure 6.

Magnetic susceptibility of polycrystalline Ca0.9Na0.1FFeAs-containing powder samples in a magnetic field of 100 Oe with a close-up of the transition region.

The superconducting volume fraction in the samples with x = 0.1 and 0.2 can be given by about 10% and 24%, respectively. However, highly substituted Ca1−NaFe2As2 detected as a side phase in all samples was previously reported to exhibit superconductivity with a nearly identical T up to 34 K [20]. For this reason, the superconducting transition observed in the powder samples cannot be ascribed definitively to the target phase. However, it seems that it is at least contributing to the content of the superconducting material, because of the observation that in samples with a higher sodium amount of x = 0.3, where an excess of the side phases according to Figure 4 is present and the target phase becomes the minority component, the superconducting volume fraction decreases considerably. Already known hole-doped oxide compounds of the 1111 class show lower transition temperatures (for example, La0.87Sr0.13OFeAs: T = 25.6 K [15] and Pr0.75Sr0.25OFeAs: T = 16.3 K [21]).

To investigate the characteristics of phase pure sodium-doped 1111, phase resistivity, as well as directional physical measurements of the magnetic susceptibility have been performed on a larger single crystal of Ca0.89Na0.11FFeAs grown in NaCl flux (Figure 7). Single crystal XRD results in a sodium doping grade of 11(3)% and the following parameters: tetragonal, P4/nmm, Z = 2, a = 387.8(1) pm, c = 859.9(2) pm, R1 = 0.034, wR2 = 0.079, GooF = 1.027. The critical temperature apparent at about 34.5 K in both measurements shows that Na-doped CaFFeAs with a sodium content of 11% incidentally exhibits almost the same T as Ca1−NaFe2As2 (x ≈ 0.66) [20].

Figure 7.

Temperature dependence of the zero-field cooled (ZFC) and field cooled (FC) DC magnetic susceptibility (μ0H = 100 Oe) (a) and DC resistivity (b) of an oriented single crystal of Ca0.89Na0.11FFeAs. (The insets are showing close-ups of the transition regions.)

The anisotropic properties of Ca0.89Na0.11FFeAs are available from the temperature dependence of the upper critical fields, which is shown in Figure 8. The anisotropy factor γ = H2(0)/H2(0) can be calculated from the estimated orbital critical fields, H2(0) and H2(0), at 0 K, derived from the Werthamer-Helfand-Hohenberg formula [22], which uses the slope of the H2 curves at T. In the case of Ca0.89Na0.11FFeAs single crystals, this leads to H2(0) = 75.6 T and H2(0) = 370.7 T, which results in γ ≈ 5. The received value for the anisotropy factor is in accordance with the literature data for 1111 compounds [23,24]. In contrast 122 phases exhibit smaller values of about two [25,26]. More details on the superconducting properties of Ca1−NaFFeAs (x = 0.11) will be discussed in a forthcoming publication [27].

Figure 8.

H–T phase diagram of Ca0.89Na0.11FFeAs single crystals. (H2 and H2: upper critical fields perpendicular and parallel to the ab plane, respectively.)

Experimental Section

The approaches to synthesize Ca1−NaFFeAs were performed via classical solid-state reactions at 1000 °C for 24 h, according to the following equation (x = 0 – 0.2).

The precursors were ground to fine powders and pressed to pellets prior to reaction. Previously, CaAs was synthesized by the reaction of calcium pieces with arsenic powder at 900 °C for 10 h in evacuated silica ampoules. All preparation procedures were carried out in an argon-filled glove box (O2, H2O < 1 ppm). Small black crystals with a disc-like shape of the target compound were obtained. Single crystals with a size of up to 2 × 2 mm2 were available via flux growth in sodium chloride. For this purpose, the educts (CaF2, NaF, CaAs, Fe and As), according to Equation (1), are heated with NaCl in an Al2O3 crucible at 950 °C for 6 h, held at an intermediate temperature of 850 °C for the same duration and, subsequently, cooled to ambient temperature in a period of 24 h (cooling rate: 34.6 °C·h−1). These crystals could be separated from the flux manually.

X-ray diffractometry has been performed with the use of Mo-Kα radiation (λ = 71.07 pm) on a Nonius KappaCCD (Bruker AXS, Karlsruhe, Germany) and a STOE STADI P (Stoe & Cie, Darmstadt, Germany) with a DECTRIS MYTHEN 1K detector for the single-crystal and the powder X-ray measurements, respectively. The single crystals were sealed in glass capillaries, and the powder samples were measured in transmission geometry as thin films on an amorphous adhesive foil. Energy dispersive X-ray spectroscopy (EDX) was carried out via a Thermo Scientific NORAN System 7 X-ray Microanalysis System (Thermo Fisher Scientific, Waltham, MA, USA) with a UltraDry detector. DC-magnetization measurements of oriented single crystals were performed using a Quantum Design MPMS SQUID magnetometer (Quantum Design, San Diego, CA, USA) in the temperature range 5–50 K. H2 values were determined from DC magnetization in different magnetic fields for field-cooled (FC) and zero-field-cooled (ZFC) measurements in the reversible regime. The electrical resistivity was measured by a standard four-probe DC-method in the temperature range 5 K < T < 300 K.

Conclusions

The results presented here show that it is possible to substitute the fluorine-containing 1111 class of iron pnictides at the alkaline-earth metal position with sodium and to obtain Ca1−NaFFeAs phases. Crystals of Ca0.89Na0.11FFeAs exhibit superconductivity at 34.5 K, which is intermediate between the observed temperatures for the electron-doped compounds Ca1−CoFFeAs [7] with T = 22 K for x = 0.1 and Ca1−NdFFeAs [16] with T = 56 K for x = 0.6. An estimation of the orbital critical fields, H2(0) and H2(0), for Ca0.89Na0.11FFeAs single crystals results in values of 75.6 and 370.7 T, respectively, which yields an anisotropy ratio of γ ≈ 5. This outcome could lead to the discovery of further compounds that are substituted with less valence electron containing elements, which have been very rare, so far. Promising candidates for this purpose could be SrFFeAs and EuFFeAs, with possible substitutes, like sodium and potassium, from an ionic radii point of view. It seems that the variation of the electron count of iron via doping is exclusively responsible for the appearance of superconductivity within this system, because there is no significant change in the interatomic distances and angles with increasing sodium content.