Effect of Multiplicity Fluctuation in Cobalt Ions on Crystal Structure, Magnetic and Electrical Properties of NdCoO3 and SmCoO3

Abstract

The structural, magnetic, electrical, and dilatation properties of the rare-earth NdCoO₃ and SmCoO₃ cobaltites were investigated. Their comparative analysis was carried out and the effect of multiplicity fluctuations on physical properties of the studied cobaltites was considered. Correlations between the spin state change of cobalt ions and the temperature dependence anomalies of the lattice parameters, magnetic susceptibility, volume thermal expansion coefficient, and electrical resistance have been revealed. A comparison of the results with well-studied GdCoO₃ allows one to single out both the general tendencies inherent in all rare-earth cobaltites taking into account the lanthanide contraction and peculiar properties of the samples containing Nd and Sm.

1. Introduction

The unusual temperature dependence of the magnetic susceptibility and transport properties of LaCoO₃ cobalt oxide [1,2,3,4] have led to the active study of RCoO₃ cobaltites (R is a rare-earth element, RE) and their derivatives for half a century. A characteristic property of such compounds is their proximity to the spin crossover or the approximate equality of Hund’s energy_JHand the10Dq crystal field in the CoO₆ octahedral complexes formed in a rhombohedral or rhombical distorted perovskite-like structure [5,6,7]. This leads to multiplicity fluctuations or thermal fluctuations of the spin value (we want to emphasize that the spin value fluctuations considered here should not be understood as spin fluctuations. The latter usually means fluctuations of the spin projection. Many years ago, Vonsovskii introduced a term «multiplicity fluctuations» to discuss a variation of the magnitude of the spin in the d shell [8]) and competition between the low-spin (LS, S = 0, t_2g⁶) and high-spin (HS, S = 2, t_2g⁴e_g²) states of the Co³⁺ ion, with their intensity depending on the RE ionic radius (“lanthanide contraction”) and environmental factors such as temperature or pressure. It is this competition, combined with the original properties of the rare-earths by themselves, that causes the unique physical properties of the rare-earth cobalt oxides.

Usually the spin crossover is related to the different multiplets level crossing, under high pressure in many iron oxides it is rather abrupt at some critical pressure_PC with the width of crossover dependent on temperature, for the Fe_xMg_1-xO measurements at 5K found the width close to zero [9]. Near_PCthe spin gap defined as the HS and LS energy difference may be comparable to the thermal energy_kBTand the spin crossover can be revealed in the temperature dependences of various material properties. It is the case of LaCoO₃ and other cobaltites. Rare-earth cobaltites in contrast to iron oxides turn out to be in the LS- state already atT= 0 and at zero applied pressure; i.e., the spin crossover already occurs in the course of the formation of their structure owing to the «chemical pressure» determining the equilibrium volume of the unit cell.

The crystal field10Dq, in contrast to the intraionic exchange interaction_JH , can vary depending on the interatomic metal-ligand distance. Hydrostatic or chemical pressure and stretching make it possible to influence the strength of the crystal field and, thus, the population of e_g and t_2g orbitals. In [10] authors reported an unambiguous demonstration of dimensionality control of d-orbital occupation with different symmetries (t_2g and e_g) in atomically thin Mott insulator-band insulator oxide superlattices. The heating induced lattice expansion also vary the crystal field value and related smooth spin crossover effects are the subject of our paper.

The most studied cobaltite compound is LaCoO₃ [11,12]. The ground state of cobalt ions is defined as the nonmagnetic LS- state without any doubt. A series of EPR experiments [13] and X-ray spectroscopy data [14] on LaCoO₃ compositions indicate the cobalt ions transition from the low-spin state to the high-spin state with increasing temperature. This confirms the scheme of multi-electron level given in [15], where the ground LS- state is separated by the spin gap_ΔSfrom the HS- state splitted into sublevels with the total effective momentumJ˜ = 1, 2, 3 due to the spin – orbit interaction. This scheme is consistent with the Tanabe - Sugano diagrams for transition metal ions in octahedral complexes developed in perovskite-like materials [16]. The approximate equality of the Curie constant at room temperature to the value given by S = 1 mimics the presence of the intermediate-spin (IS, S=1, t_2g⁵e_g¹) states, but it follows from the smooth temperature dependence of the average magnetic moment of the mixed LS- and HS- states [17]. Multielectron calculations of the LDA+GTB electronic structure and the properties of LaCoO₃ [17] using the term scheme [15] have shown that, due to multiplicity fluctuations, the effective spin is determined by a combination of LS- and HS- states and depends on temperature, therefore it is close to 1 near room temperature and the saturation S = 2 has been reached only at high temperatures up to 1000K.

The properties of other rare-earth cobaltites have been studiedless. However, the similar features both in magnetic susceptibility behaviorχ(T), thermal dilatationα(T), heat capacity_Cp(T), electrical resistanceρ(T) , have been observed for some RCoO₃ compounds similar to the known for LaCoO₃ [18,19,20,21,22,23,24,25]. With increasing the RE atomic number, the unit cell volume decreases, the additional chemical pressure increases, and the spin gap Δ_S increases, stabilizing the LS- state of cobalt ions to higher temperatures [26]. Moreover, the anomalies in the behavior ofχ(T),α(T),_Cp(T), andρ(T)shift to the region of higher temperatures and are smoother, giving a correlation between electromagnetic and thermodynamic properties. It should be noted that in most cases the magnetic transition temperatures of the ReCoO₃ compounds associated with the magnetic moment ordering of 4f- ions are low,_TN ~ 1 K [27]. In the paramagnetic region, large RE moments make the main contribution to the magnetic susceptibility; however, a small Co³⁺ ions contribution can be distinguished only at high temperatures. This is probably the reason that most of the experimental work is devoted to the study of the thermodynamic and transport properties of cobaltites [5,7,28,29]. LaCoO₃ is an exception, when total magnetic susceptibility is due to Co³⁺ ions. The magnetic properties of other rare-earth cobaltites have less been studied [30,31,32,33].

Considering the potential for extensive use of perovskite-like complex cobalt oxides as solid state oxide power sources [34,35,36], oxygen membranes [37], gas sensors [38], etc., a more detailed study of the rare-earth cobaltite properties seems to be appropriate.

In current paper structural, magnetic, electrical, and dilatation properties of the rare-earth cobaltites NdCoO₃ and SmCoO₃ have been studied and their comparative analysis was carried out. The influence of the multiplicity fluctuations of Co³⁺ ions on physical properties of the studied cobaltites is considered within a virtual crystal model. In this model previously proposed in the study of GdCoO₃the average crystal volume at temperatureT is determined by the volume superposition in LS- и HS- states with statistical weights given by the population of LS- and HS- terms [39]. Then, the maximum of anomalous thermal dilatation for GdCoO₃was found at the temperature of about 750 K in [5]. A lower lanthanide compression for Nd³⁺ and Sm³⁺ ions as compared to Gd³⁺can be expected to enhance the effects of multiplicity fluctuations in a more convenient temperature range from 200 to 700 K to measure.

2. Samples and Experimental Methods The rare-earth cobaltites NdCoO₃ and SmCoO₃ were obtained by conventional ceramic processing using a stoichiometric amount of oxides Co₃O₄, 99.7% (metals basis, Sigma-Aldrich, St. Louis, MO, USA), Nd₂O₃ and Sm₂O₃, 99.99% (Rare Metals Plant, Novosibirsk, Russia), which were thoroughly mixed and the resulting mixture was annealed at a temperature of 120ºC for 36 h with intermediate grinding. After annealing, the mixture was ground again, tablets were pressed in bars of 5 mm × 13 mm × 1 mm, which were then annealed in air at a temperature of 1200 °C for 8 h and cooled together with the furnace up to room temperature at 2 °C/min.

Powder X-ray diffraction (PXRD) data were collected on a PANalyticalX’Pert PRO powder diffractometer (Eindhoven, Netherlands) equipped with a solid- state detector using the CoK_α-radiation in the range of 2θ = 20 –130° and within 300 K to 1000 K. The RCoO₃ samples (R = Nd, Sm) were ground in octane in an agate mortar, dried and placed in a flat holder for PXRD measurements in the Bragg-Brentano geometry. X-ray investigations at high temperature were carried out in an Anton Paar HTK 1200N (AntonPaar, Austria) high-temperature chamber with sample rotation and self-adjustment. The samples were preliminarily kept in a high-temperature chamber for 2 h at a temperature of 1000K. The crystal lattice parameters were refined using the derivative difference minimization method (DDM) [40].

Static magnetization measurements in the temperature range from 1.8 to 400 K and magnetic field up to 50 000 Oe were carried out with a MPMS-XL Quantum Design SQUID magnetometer (USA). Thermal expansion was studied in the temperature range 100–700 K with a Netzsch DIL-402C induction dilatometer in dynamic mode with heating and cooling rates of 3 K/min when purged with dry helium (O2 content ≈ 0.05% of the volume). The rod load on the sample is 30 sN. The fused silica standards to calibrate and account for the dilatation of measuring system were used. The temperature dependences of the electrical resistance were obtained with the universal installation—Physical Properties Measurement System (PPMS-9) Quantum Design (USA) at the core facilities center of Lebedev Physical Institute of the Russian Academy of Sciences (Moscow). 3. Results and Discussions 3.1. X-Ray Phase and X-Ray Diffraction Analysis

According to the PXRD analysis, the amount of cobalt oxide impurity in the samples was 1.5% and 2% for SmCoO₃ and NdCoO₃, respectively. Within the whole temperature range studied, the main phases have an orthorhombic perovskite-type structure with the Pbnm- space group. The experimental, calculated, and difference PXRD profiles after the DDM refinement at 300 K and 1000 K are presented in Figure 1.

The room temperature structural characteristics are consistent with other data available [41,42]. The crystal lattice parameters at various temperatures are summarized in Table 1. The deviation of the oxygen nonstoichiometry index from δ = 3, according to thermogravimetric analysis, does not exceed 0.6%.

The temperature dependences of volume expansion coefficient for NdCoO₃, SmCoO₃, and GdCoO₃ arepresented in Figure 2.

The given dependences are characterized by the presence of maxima within 550 K for NdCoO₃ and 650 K for SmCoO₃.

The combined analysis of the specific heat and thermal expansion of rare earth cobalt oxides and their solid solutions demonstrated that their temperature dependence exhibits characteristic anomalies related to the occupation of the high-spin states of cobalt ions and to the additional electron contribution arising at the insulator–metal transition occurring with the growth of the temperature. With the decrease in the radius of the rare earth ion or with the growth of chemical pressure, the spin gap in these compounds grows and is sample dependent, so we observed the shift of the low-temperature feature toward higher temperatures and the gradual merging of the two contributions to the specific heat and thermal expansion [43]. In Figure 2 the high-temperature feature of the thermal expansion of NdCoO₃, SmCoO₃, and GdCoO₃ due to the insulator–metal transition observed for the entire series of rare-earth cobalt oxides with a characteristic transition temperature_TIMincreasing with decreasing ion radius of the rare-earth element is shown._TIM increasing determine the origin of the sample dependence in the volume expansion (Figure 2).

3.2. Magnetic Properties

The temperature dependences of the molar magnetic susceptibilityχ(T)and field dependences of the magnetic momentM(H) of the NdCoO₃ and SmCoO₃ samples are shown in Figure 3. The magnetic moment values of NdCoO₃ are almost fifteen times higher than the similar values for SmCoO₃. The magnetization curves obtained in the FC and ZFC modes do not differ from each other for both samples. In contrast to the behavior of the NdCoO₃ magnetic susceptibility, being reduced progressively with increasing temperature in the entire studied range (Figure 3a), the SmCoO₃ susceptibility is characterized by a plateau in the temperature range 180–270 K. A further temperature raise leads to an increase in the SmCoO₃magnetic susceptibility (Figure 3b) which is caused by the appearance of a contribution from Co³⁺ ions at high temperatures. The temperature dependence of the magnetic susceptibility of RCoO₃ is determined by the magnetization of rare-earth ions and the additional paramagnetic contribution induced by the thermally excited magnetic terms of Co³⁺ ions. The obtained experimental data are in good agreement with similar studies in recently published works [44,45].

The field dependences of magnetization correspond to paramagnetic behavior (Figure 3, insets), while maintaining the linearity in the region of weak fields. The magnetization saturation trends atT= 1.8 K are not observed in the entire field range up to 50 000 Oe for both samples.

The temperature dependences of the inverse molar susceptibility1/χ of the NdCoO₃ samples (Figure 4a, inset) and SmCoO₃ (Figure 4b, inset) are shown in Figure 4. In the entire temperature range under consideration, these dependences do not obey the Curie–Weiss law. Taking into account the linearity of temperature dependence of the reduced magnetic susceptibilityχT in a certain temperature range (Figure 4), it is worth describing the magnetic sample properties in order to divide the temperature range into a low-temperature, high-temperature, and intermediate interval where dependence is linear.

TheχTdependences in the intermediate temperature range were approximated by straight lines with convergence coefficientsRequal to 0.99999 for SmCoO₃ and 0.99913 for NdCoO₃. The linearity of theχTdependence allows one to describe the magnetic susceptibility in the interval as a superposition of two contributions:χ=C/T+_χVV, whereC/Tis the orientation paramagnetic Curie susceptibility of rare-earth ions, and_χVVis the Van Vleck polarization susceptibility. The diamagnetic contribution of the electron shells is sufficiently small, and therefore is ignored.

The temperature ranges, the calculated valuesC,_χVVobtained by experiment and effective magnetic moments_μeffexpfor NdCoO₃ and SmCoO₃ compounds in the intermediate temperature range_Tmin–_Tmax are shown in Table 2. Some theoretical values are also given [46].

The obtained values of C and_μeffexp are a little larger than the similar values obtained in [47] for SmCoO₃ (C= 0.0276 emu·K/(mol·Oe),_μeff = 0.47 µ_B). The effective magnetic moments for both Nd³⁺ and Sm³⁺ are significantly lower than their theoretical values calculated for free ions (Table 2).

The total magnetic susceptibility of NdCoO₃ and SmCoO₃ can be represented as a sum of two independent summands (since the Co ions acquire a magnetic moment only at high temperatures, the exchange interaction of Co-RE can be neglected)

_χSm(Nd)CoO3=_χSm(Nd)+_χCo

where_χSm(Nd)and_χCo are the magnetic susceptibilities of samarium (neodymium) and cobalt ions, respectively. To describe the contribution of cobalt ions to the total magnetization of Sm(Nd)CoO₃, a diagram of the Co³⁺ ion levels in a crystal field taking into account the spin–orbit interaction is shown in Figure 5. The ground term is aA11low-spin singlet, separated from the triplet sublevelJ˜=1of theT25high-spin state by the_ΔSspin gap. At_ΔS=150 K, the position of the terms for LaCoO₃corresponds to [13,23,48]. Lanthanum substitution on another rare-earth ion with a smaller ionic radius leads to a chemical pressure generation that is equivalent to the external pressure. Therefore, the substitution will lead to the additional stabilization of low-spin state or, in other words, to increase the spin gap.

At low temperatures, there are the SmCoO₃ and NdCoO₃ cobalt ions in theA11nonmagnetic low-spin state. With increasing temperature, thermal excitations of the high-spin state with a nonzero magnetic moment (the multiplicity fluctuations) and increase of the magnetization occur. The statistical sum of the Co³⁺ ions per mole of substance can be represented as:

Z=[1+^e−β_ΔS+2^e−β_ΔSch(_{g1 μB}B˜β)+^{e−β(_ΔS+2_λ˜Co)}+2^{e−β(_ΔS+2_λ˜Co)}ch( _{^g′2 μB}B˜β)^{+2e−β(_ΔS+2_λ˜Co)ch( _{g″2 μB}B˜β)]_NA}

where_λ˜Co=185 K [48] is the effective constant of spin–orbit interaction,_NAis the Avogadro number,B˜is the applied external magnetic field,_kBis the Boltzmann constant,β=1/_kBT,_μBis the Bohr magneton, the Landé factors_g1=3.4for the tripletJ˜=1and _^g′2=3.1, _^g″2=1.8for the quintetJ˜=1. With the partition function, the free energyF=−_kBTlnZand magnetizationM=−∂F/∂B˜are found in a standard way. For not too low temperatures and not too strong magnetic fields, the expression for the molar magnetic susceptibility of Co³⁺ ions_χCo=∂M/∂B˜is as follows:

_χCo=_NA2_μB2β[_g12 ^e−β_ΔS+ ^{g′2 e−β(_ΔS+2λ˜)}+ ^{g″2 e−β(_ΔS+2λ˜)}]/[1+3^e−β_ΔS+5^{e−β(_ΔS+2λ˜)}]

In the case when_ΔS>1000K, the spin–orbit interaction can be neglected, the expression (3) takes the form:

_χCo=_NA^g2 _μB2S(S+1)3_kBT_nHS

whereg=2is the Lande spin factor,_nHS=_gHSexp(−_ΔS/_kBT)1+_gHSexp(−_ΔS/_kBT)is the population of the HS- state,_gHS=(2S+1)(2L+1)=15for the high-spin state withS=2,L=1.

The calculation results_χCo for NdCoO₃ and SmCoO₃are given in Figure 6. The following values are used:_gHS=15,_ΔS=2300 K (SmCoO₃) and_ΔS=1600 K (NdCoO₃).

The magnetic susceptibility of Sm³⁺ ions in SmCoO₃can be represented by the formula [49].

_χSm=0.2482xT1.07x+3.67+(21.45x+0.82)^e−7x/2+…3+4^e−7x/2+…

wherex=_λSm/T,_λSmis the spin–orbit coupling constant of the rare-earth Sm³⁺ ion. It is known from spectroscopic data that the nearest excited term ⁶H_7/2 of the Sm³⁺ ion is separated from the main one by the energy intervalΔ=7/2_λSm approximately 1000 cm⁻¹ [49], therefore_λSm≈400 K. Despite the fact that formula (5) was obtained for a free rare-earth ion with no crystalline field, however, it is possible to describe the temperature dependence of the SmCoO₃ magnetic susceptibility as will be seen below.

Within low temperatures, the expression (5) takes a simpler form:

_χSm≈C/T+_χVV

whereCis the effective Curie constant, and_χVVis the Van Vleck susceptibility.

The calculation resultsχTand^χ−1 respectively, for SmCoO₃ (red solid line), using (1), taking into account (4) and (5) are presented in Figure 7a,b. In contrast, in Figure 7, the contribution of only Sm³⁺ions, according to (5) is depicted by the blue dashed line. That can be seen to be in a good agreement with the experiment. The theoretical dependenceχT (Figure 7a) shows a smooth deviation from the linear dependence atT ≈ 125 K (shown by the dashed arrow), below this temperature the expression (6) is valid. Nevertheless, the approximation (6) for SmCoO₃can be seen from Figure 4b to be valid over a wide temperature range up to 250 K(see above). Thus, Co³⁺ magnetic moment is provided above 250K for SmCoO₃ that agrees with Figure 6.

The ground state of free Nd³⁺ ion with the 4f³ electronic configuration is the ⁴I_9/2 multiplet (L = 6, S = 3/2). The nearest excited state ⁴I_11/2 is 1900 cm⁻¹higher in energy. As for the free Sm³⁺ ion, its electronic configuration is 4f⁵, the ground multiplet state is ⁶H_5/2 (L = 5, S = 5/2). The distinctive feature of this ion is the relative proximity to the first excited state ⁶H_7/2. The energy difference of these states for free Sm³⁺ ion is approximately 1000 cm⁻¹ [49].

The magnetic properties for ions essentially depend on their environment, i.e., on the crystal field value and symmetry. Hence, in perovskite-like crystals, such as cobaltites, the rare-earth ion is in a low-symmetrical ligand environment. The field of such symmetry splits the main Sm³⁺ multiplet into three and five Kramers doublets for Nd³⁺, with each of them having a certain magnetic moment. In the general case, such a splitting leads to a decrease or, by contrast, an increase in the magnetic ion moment and, in addition, the influence of the crystal field can be expressed in a significant difference between theg- factor of Kramers doublets and_g0=32−L(L+1)−S(S+1)2J(J+1)for the free ion and their strong anisotropy, which turns to result in magnetic susceptibility anisotropy. For polycrystalline samples, the average magnetic susceptibility can be calculated as⟨χ⟩=(_χ∥+2_χ⊥)/3, where_χ∥and_χ⊥are the susceptibility components in parallel and perpendicular directions to the external applied magnetic field. Therefore, the complex energy level structure of the Sm³⁺ and Nd³⁺ ions in a crystal field of low symmetry leads to the temperature dependence in the low-temperature region (T<_Tmin ) shown in Figure 4.

It has been known that in order to calculate the temperature dependence of magnetization and susceptibility, the positions of the energy levels of the_Ensystem taking into account the external magnetic field have to be realized. Van Fleck (1932) studied the energy contributions in terms ofperturbative approach depending on the effect of the magnetic fieldH:_En=_En(0)+H_En(1)+^H2 _En(2), where_En(0)are the energy system levels without the external magnetic field_H^0|n⟩=_En(0)|n⟩, generally developing the groups of degenerate states;_En(1)=⟨n|_μB(_L^s+_{g0 S^s})|n⟩,_En(2)=∑^n′≠n^{|⟨n|_μB(_L^s+_{g0 S^s})|n′⟩|2}_En−_En′are Zeeman coefficients of the first and second order (thezaxis is directed along the magnetic field). The Hamiltonian_H^0contains inter-electron repulsion, spin–orbit interaction, and crystal field energy.

The temperature dependence equation of magnetic susceptibility, known as the Van Vleck equation [50], has the form:_χVleck=_NA∑n[^(_En(1))2_kBT−2_En(2)]exp(−_En(0)kBT)∑nexp(−_En(0)kBT), where_NAis the Avogadro constant, and_kBis the Boltzmann constant. It is generally accepted that, in commonly usedH≤10kOe fields, the Zeeman interaction energy is usually less than the splitting caused by inter-electron repulsion, crystal field, and spin–orbit interaction; however, in case of rare-earth ions in low-symmetry crystal fields, the multiplet splitting into Kramers sublevels being sufficiently close to each other (see above) seems to be compared with the interaction energy with magnetic field and to be observed by an unusual dependence of paramagnetic Van Vleck susceptibility on the magnetic field value. Thus, to characterize properly the magnetic properties of the rare-earth and transition metal ions in low-symmetry fields, both the low-symmetry part of crystal field and the magnetic field influence have to be similarly considered or, in other words, simultaneously taken into account.

In contrast to SmCoO₃, NdCoO₃ has a linear regionχTand^χ−1 in a more narrow temperature range (see Table 2). Above_Tmax≈ 250 K, the contribution of Co³⁺ ions to the total magnetic susceptibility of the sample becomes detectible for NdCoO₃.

In a low-symmetry crystal field, the main term ⁶H_5/2 of the Sm³⁺ ion splits into three Kramers doublets, and the main term ⁴I_9/2 of the Nd³⁺ ion splits into five ones in a wider energy range [49]. This causes a significant difference in the_Tmin temperature for SmCoO₃ and NdCoO₃ (see Table 2). As otherwise stated, with decreasing temperature for NdCoO₃, crystal field effects are important even at_Tmin≈ 165 K, while for SmCoO₃ only atT<_Tmin≈ 15K.

The origin of Van Vleck paramagnetism is to add the wave functions of thermally unpopulated excited states to the wave functions of ground state. The Van Vleck susceptibility of the free Sm³⁺ (Nd³⁺) ions is due to possible (virtual) quantum transitions between the energetically lowest ⁶H_5/2 (⁴I_9/2) state and the nearest excited ⁶H_7/2 (⁴I_11/2) state. In the crystal field, additional multiplet splitting occurs and, besides the indicated transitions, some possible ones within the same multiplet have to be taken into account. This is the reason for the difference between the Van Vleck susceptibility of SmCoO₃ and NdCoO₃ and that for free ions.

The electronic structure of cobaltites calculated in the framework of the LDA + GTB multi-electron approach [17,39] depends on the_nHSconcentration. Therefore, correlation of the changes in activation energy with changes in thermal expansion and magnetic susceptibility is also due to the contribution of an increasing concentration of high-spin states with temperature rise.

3.3. Thermal Expansion

The experimental temperature dependences of the volume thermal expansion coefficientβ(T) , obtained in the heating and cooling modes are presented in Figure 8. Hysteretic phenomena were not observed. The coefficientβ for NdCoO₃ compound is characterized by the presence of two diffuse anomalies near 400 and 600 K, and for SmCoO₃by one maximum near 650 K (Figure 8a). Deviation from the usual linear contribution due to anharmonicity occurs in the temperature ranges of 250–270 K and 310–330 K for NdCoO₃ and SmCoO₃, observed in the temperature dependences of the deformationΔL/L (Figure 8b). In this case, the temperatures of the first maximum for NdCoO₃ and the maximum for SmCoO₃ correlate with the maxima obtained on the temperature dependences of the thermal expansion during diffraction studies. The anomalous contribution of electronic origin due to multiplicity fluctuations is revealed by the deviations from linear behavior shown in the inset to Figure 8.

In the case of spin crossover materials, a large contribution to the anomaly of thermal expansion is made by the redistribution of the HS/LS statistical weights due to the large difference in their ionic radii [39]; therefore, the unit cell volume as a temperature function can be represented as

V(T)=_VHS(T)_nHS(T)+_VLS(T)_nLS(T)

where,_VHS(T),_VLS(T)is the unit cell volume, respectively, in the phase of the HS- and LS- states,_nHS/LS(T)is the population of HS/LS- states., this turns to be represented as

_VHS(T)=_VHS(0)(1+_βHST)

and

_VLS(T)=_VLS(0)(1+_βLST)

where_βHS/LSis the volumetric thermal expansion coefficient, and_VHS/LS(0)is the unit cell volume whenT = 0, respectively, in the phase of the HS/LS- state. In the case of rare-earth cobalt oxides, the non-magnetic LS- state is the ground state of cobalt ion, and the HS-state is possible with increasing temperature, therefore expression (8) is suggested to be written by the so-called «virtual crystal model», when the ground state of cobalt ions is the artificially created HS-state (hypothetical HS-phase). A similar approach was previously used to describe the thermodynamic and magnetic properties of GdCoO₃ [39], where_VHS/LS(0)was determined by first-principle calculations using the DFT method. Since_nLS(T)=1−_nHS(T), then

V(T)=(_VHS(0)−_VLS(0))_nHS(T)+(_{VHS(0) βHS}−_{VLS(0) βLS})T_nHS(T)+_VLS(0)(1+_βLST)

In expression (10), both the background (regular) contribution, i.e., the second and third summands due to the anharmonicity of lattice vibrations in the phase of mixed LS/HS- and pure LS- states, and the anomalous contribution of thermal expansion, i.e., the first summand arising due to multiplicity fluctuations of cobalt ions can be distinguished. Since the characteristic values are_βHS/LS∼¹⁰⁻⁵1/K, and0≤_nHS/LS(T)<1then atT<1000 K, the first summand makes the largest contribution compared to the second one, therefore, the volumetric thermal expansion coefficient can be represented asβ=1V∂V∂T≈δβ+_βreg, whereδβ=(_VHS(0)−_VLS(0))_VLS(0)∂_nHS(T)∂T. Thus, the anomalous contribution to the volumetric thermal expansion coefficient is proportional to the first-order derivative with respect to the population temperature of the HS- state_nHS and is determined by the magnitude of spin gap. In Figure 9, by comparison, the experimental data of anomalous contribution to thermal expansion and the calculated values∂_nHS/∂Tfor NdCoO₃ and SmCoO₃ at_ΔS=1600 and 2300 K, respectively, are presented.

Figure 8a and Figure 9 illustrate that, in contrast to SmCoO₃, in temperature dependence of the volumetric thermal expansion coefficient of NdCoO₃, two maxima can be clearly distinguished. The first (low-temperature) maximum is associated with fluctuations of the spin multiplicity of cobalt ions, and the second one with the insulator–semimetal transition (crossover) observed for all rare-earth cobalt oxides with increasing temperature and characteristic transition temperature of the rare-earth element. For SmCoO₃, the spin gap obtained above by the magnetic data analysis is large enough, thus both peaks almost coincide. A similar situation is observed for solid solutions of rare-earth cobaltites. Then, in La_1-xGd_xCoO₃, the low-temperature maximum of thermal expansion shifts to the region of higher temperatures with an increase in the gadolinium concentration and gradually coincides with the second maximum [43].

3.4. Transport Properties

The temperature dependences of the electrical resistivityρ(T) for NdCoO₃ and SmCoO₃ samples and the dependence of resistivity logarithm on the reciprocal temperature are shown in Figure 10. Theρ(T)dependences reliably correspond to the semiconductor typedρ(T)/dT<0over the studied 300 to 750 K range. According to thelnρ(1/T)dependences, it is matter of fact that the semiconductor type of conductivity can be described using the currently accepted thermal activation relation of the formρ(T)=_ρ∞exp(_Ea/_kBT), where_Ea is the activation energy [51], and_ρ∞is the constant determined byT→∞. Moreover, for each sample, there is a temperature^T∗when the activation energy changes in the intermediate region and temperature^T∗∗ characterizing the variation from the activation law at high temperatures. The values of the obtained parameters are presented in Table 3.

Accordance with the thermal activation law is depicted by straight lines in the insets to Figure 10.

The temperature deviations from a thermal activation law and the characteristic temperatures of changes in the activation energy correlate with anomalies in the temperature dependences of the volumetric thermal expansion coefficientβ(T)for both samples.

4. Conclusions

The features of thermal expansion, magnetic susceptibility, and transport properties of NdCoO₃ and SmCoO₃ cobaltites being in a good agreement were experimentally demonstrated. Partially, these correlations were previously known, e.g., those of thermal expansion with a spin and electronic transition [5]. The features have been shown theoretically to be associated with a population increase of high-spin states of Co³⁺ ions. A comparison of the results with well- studied GdCoO₃ allows one to identify both general trends inherent in all rare-earth cobaltites based on lanthanide compression and the specific properties of samples containingNd³⁺, Sm³⁺ions formed with strong single-ion anisotropy and crystal field effects at low temperatures.

A quantitative assessment of the contribution from the fluctuations of multiplicity to the magnetic properties of NdCoO₃ and SmCoO₃ samples seems to be a rather difficult task, since in addition to the complex structure of the energy levels of Sm³⁺ and Nd³⁺ ions in a low-symmetry crystal field, it is necessary to take into account the influence of oxygen non-stoichiometry of the samples referred to a number of research works [52,53]. On the one hand, oxygen non-stoichiometry is the main reason for defects in the structure of rare-earth cobaltites leading to the formation of magnetic excitons [54,55]; on the other hand, it can lead to dimer formation [56] and the appearance of Co³⁺ ions in the HS- state even at low temperatures.

Figure 1. Experimental (upper, black), calculated (middle, red) and difference (lower, blue) Powder X-ray diffraction (PXRD) profiles after derivative difference minimization method (DDM) refinement; (a) NdCoO3 at 300 K, (b) SmCoO3 at 300 K, (c) NdCoO3 at 1000 K, and (d) SmCoO3 at 1000 K.

Figure 2. Temperature dependences of volume expansion coefficients for NdCoO3, SmCoO3, and GdCoO3. The data for GdCoO3 are taken from [39].

Figure 3. Temperature dependences of the molar magnetic susceptibility for NdCoO3 (a) and SmCoO3 (b) samples (H= 15 000 Oe). The insets show the magnetization curves atT= 1.8 and 10 K.

Figure 4. Temperature dependences of the reduced magnetic susceptibility χT for NdCoO3 (a) and SmCoO3 (b) samples. The temperature dependences of the inverse magnetic susceptibility (NdCoO3 (a), SmCoO3 (b)) and the χT dependence for SmCoO3 in the low-temperature region (b) are presented in the insets.

Figure 5. A set of low-energy terms for the d6 electronic configuration for Co3+ ion in a crystalline field of octahedral symmetry, taking into account spin-orbit interaction. The degeneracy multiplicity is shown by digits for terms [15].

Figure 6. Temperature dependences of the Co3+ ion magnetic susceptibility for NdCoO3 and SmCoO3 samples.

Figure 7. The calculation results of the temperature dependencesχT(a) andχ-1 (b), respectively, for SmCoO3 (red solid line). By contrast, the contribution of only Sm3+ ions is shown by blue dashed line.

Figure 8. Temperature dependences of the volume thermal expansion coefficientβ, obtained as a result of successive heating-cooling cycles (a) and (ΔL/L ) deformation (b), for NdCoO3 and SmCoO3 samples. The inset shows abnormal contributions to the deformation after subtraction of the standard linear contribution to the lattice expansion.

Figure 9. Anomalous contributions to the volumetric thermal expansion coefficient for NdCoO3 (depicted by blue color) and SmCoO3 (depicted by red color). Solid blue and red lines show the calculated dependences∂nHS/∂T for NdCoO3 and SmCoO3, respectively.

Figure 10. Temperature dependence of electrical resistivity for the NdCoO3 (a) and SmCoO3 (b) samples. The corresponding dependencies of the resistivity logarithm on the reciprocal temperature are illustrated in the insets. Straight lines show accordance with the thermo-activation law (blue-the region of intermediate temperatures, red-high temperatures).

	NdCoO3				SmCoO3
T, K	a, Å	b, Å	c, Å	V, Å3	a, Å	b, Å	c, Å	V, Å3
300	5.3478(1)	5.3324(1)	7.5505(2)	215.32(1)	5.2887(1)	5.3517(3)	7.5031(2)	212.37(1)
400	5.3591(1)	5.3463(2)	7.5677(2)	216.82(1)	5.2961(1)	5.3572(1)	7.5130(2)	213.16(1)
500	5.3733(1)	5.3649(1)	7.5909(3)	218.82(1)	5.3082(1)	5.3726(1)	7.5291(1)	214.72(1)
600	5.3907(2)	5.3888(1)	7.6176(2)	221.29(1)	5.3246(1)	5.3985(1)	7.5521(1)	217.08(1)
700	5.4067(1)	5.4106(1)	7.6427(3)	223.57(1)	5.3423(1)	5.4292(1)	7.5777(1)	219.78(1)
800	5.4208(1)	5.4270(1)	7.6635(1)	225.45(1)	5.3573(1)	5.4519(1)	7.6001(1)	221.98(1)
900	5.4332(1)	5.4404(1)	7.6819(2)	227.07(1)	5.3707(1)	5.4683(1)	7.6197(1)	223.78(1)
1000	5.4451(1)	5.4521(2)	7.6989(3)	228.56(1)	5.3831(1)	5.4816(1)	7.6380(1)	225.38(1)

	Tmin(K)	Tmax(K)	C(emu⋅Kmol⋅Oe)	χVV(emumol⋅Oe)	μeffexp µB	μeffteor µB	μeffteor(VV) µB	R
NdCoO3	165	250	0.956	0.00201	2.77	3.62	3.68	0.99993
SmCoO3	15	270	0.03504	0.00202	0.53	0.84	1.55	0.99999

	T*, K	T<T∗			T>T∗			T**, K
		Ea, eV	ρ∞, mOhm·cm	R	Ea, eV	ρ∞, mOhm·cm	R
NdCoO3	395	0.379 ± 0.001	0.390 ± 0.001	0.99955	0.679 ± 0.001	5.81 × 10−5	0.99991	590
SmCoO3	460	0.394 ± 0.001	0.401 ± 0.001	0.99893	0.739 ± 0.001	6.56 × 10−5	0.99944	650

Author Contributions

The manuscript was written through contributions of all authors. All authors have read and agreed to the published version of the manuscript.

Funding

This work is supported by the Russian Science Foundation grant 18-02-00022.

Conflicts of Interest

The authors declare no conflict of interest.

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