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Thermophysical Properties of Bi-based High-Tc Superconductors

Written By

Asghari Maqsood and M. Anis-ur-Rehman

Submitted: October 10th, 2010 Published: June 27th, 2011

DOI: 10.5772/16359

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1. Introduction

Since the discovery of 90 K superconductivity in the Ba-Y-Cu oxide system (Wu,, 1987) a number of studies have been published. A true superconductor not only shows zero resistance but also excludes a magnetic field completely (the Meissner effect). A visual demonstration of the Meissner effect was carried out by placing a small magnet on a pellet of Dy1Ba2Cu3O7-x and cooling the system to liquid-nitrogen temperature. The levitation of the magnet due to ejection of magnetic lines of flux from the superconductor is shown in Figure 1 (Maqsood,, 1989 ).

Dissipation phenomena in high temperature superconductors are governed by the microstructure that develops during the preparation process. Therefore, detailed investigations of the electrical and thermal transport and ac magnetic susceptibilities in

Figure 1.

The Dy1Ba2Cu307-x specimen, showing the Meissner effect at liquid-nitrogen temperature.

superconductors prepared either in the form of single crystals, thin films or polycrystalline are important for understanding superconductivity as well as for practical applications (Rehman & Maqsood, 2005).

Among high-Tcsuperconductors, (Bi, Pb)-2223 appears to be the most promising candidate for the application of power transmission cables at liquid nitrogen temperature. Unlike other high-Tc superconductors (HTS), such as YBa2Cu3O7-δ(Y-123), it is still a problem to control and increase its critical temperature and current density. The Bi based superconductors offer potential advantages in comparison to the Y-based superconductors. The studies of transport properties, such as electrical resistivity, thermoelectric power (S) and thermal conductivity, are important for exploring the conduction mechanisms. The transport properties are very sensitive to the sample preparation methods.

The BISCCO samples substituted with Fe, Cr, Co, Gd, Er, Nd, Sm, Ag, V, Ga, Zn, Cd, etc. have been widely prepared using conventional solid state reaction and glass–ceramics techniques (Aksan & Yakyncy, 2004; Chatterjee, 1998; Cloots,, 1994; Coskun, 2005; Dorbolo, 1999; Ekicibil,, 2004, 2005; Mandal,, 1992; Munakata,, 1992; Nanda,, 1995; Ozhanli,, 2002; Rao, 1990; Sera, 1992; Varoy, 1992). Investigation of thermal conductivity, λ(T), also gives important information about the scattering mechanism of charge carriers, electron–phonon interaction and other physical properties, such as carrier density and phonon mean free path (Aksan, 1999; Houssa & Ausloos, 1996; Knizek, 1998; Natividad, 2002; Uher, 1994; Yankyncy 1997). In the last decade, many investigations have been made on λ(T)of high-Tcmaterials (Aksan, 1999; Castellazzi, et. al. 1997; Houssa, 1996; Hui, 1999; Knizek, 1998; Natividad, 2002; Uher, 1994; Yankyncy 1997; Wermbter, 1991) and almost similar results are reported. In general, for λ(T)investigation of high-Tcmaterials, three important approaches can be considered to the total λ(T)calculations: (i) phonon contribution; (ii) electron contribution; and (iii) both electron and phonon contributions. Many research groups have investigated these valuable approaches for high-Tcmaterials and results are published (Castellazzi,, 1997; Peacor,, 1991; Tewordt & Wolkhausen, 1989,1990; Wermbter,, 1996; Yu, 1992). However, there exists a difficulty in the λ(T)properties of the high-Tcmaterials. In particular, compared with conventional metallic structures, the high-Tcsuperconductors show unusual behavior just below their Tc. At that point, thermal conductivity rises and reaches to the maximum and then drops sharply. The explanation of the rapid rise and the maximum point seen in a wide range just below Tc, is summed up through two main points (Uher,, 1994). Firstly, decrease on the scattering mechanism, because of the superconducting state (T < Tc (R = 0), and secondly, an increase in the electron mean free path due to decrease in the phonon scattering. In many investigations, the maximal value was also found to depend on the preparation method and chemical composition (Cohn, 1992; Jezowski, 1987; Morelli, 1987; Peacor, 1991; Uher 1992; ). However, it is important to see the effect of the quasi-particle contribution on the rapid rise of λ(T)below the Tc, as explained by many groups (Castellazzi, 1997; Yu, 1992). There exist some other models that have been widely accepted for materials in solid state. Particularly,for the graded materials, effective medium approximation (EMA) (Hirai, 1996; Hui, 1999) and another model developed for the conventional low-Tc superconductors by Bardeen et al (Bardeen,, 1959) that describes the phonon thermal conductivity in the superconducting state. This model then was generalized by Tewordt and Wolkhausen in order to describe the phonon thermal conductivity of high-Tcsuperconductors in a wide range of temperatures (Tewordt & Wolkhuasen, 1989). However, still many efforts have to be made both experimentally and theoretically to understand the λ(T)mechanism of high-Tcmaterials.

Thermoelectric power being sensitive to the energy dependence of the electron lifetime and the density of states near the Fermi level energy, provides valuable information regarding many fundamental aspects of charge carrier transport in the materials. The thermoelectric power (S)of high-temperature superconductors has been widely studied and reported a positive ‘S’, while Khim et al. (Khim et. al. 1987) and others have reported a negative ‘S’for the same compositions. Later studies proved that the sign of the thermoelectric power is sensitive to the oxygen content present in the compound (Lee, et. al. 1988). This behavior was also observed in other materials like Cheverly phase compounds as was seen by Vasudeva Rao et al. (Rao, 1984). In the BISCCO compounds, the TEP studies earlier reported on the (2201), (2212) and (2223) phases. Sera et al. (Sera et. al. 1992) have studied the S behavior of La doped (2201) cuprates. The ‘S’behavior of the Bi2Sr2Ca1−xYxCu2Oycompounds was investigated as a function of temperature (Mandal, 1992; Munakata, 1992; Varoy, et. al. 1992) and it was found that with increasing temperature ‘S’increases, exhibits a maximum value and decreases thereafter. From the ‘S’data they concluded that the substitution of Y for Ca decreases the hole concentration from the optimum value. Varoy et. al. have found a systematic fall to more negative values of thermoelectric power as holes are added with the introduction of more lead or oxygen into BISCCO compounds. In this chapter, we report the structural, electrical, magnetic and thermal transport properties of vanadium-substituted BISCCO (2223) systems.


2. Experimental details

In the Bi-based high-Tc superconductors the Bi-2223 phase is stable within a narrow temperature range and exhibits phase equilibria with only a few of the compounds existing in the system. Precise control over the processing parameters is required to obtain the phase-pure material (Rehman & Maqsood, 2005). Bismuth-based superconducting powder with chemical formula Bi1.3V0.3Pb0.4Sr2Ca2Cu3Oδwas prepared by the solid state reaction method. The starting powders corresponding to stoichiometric quantities of high purity (99.9%) Bi2O3, PbO, SrCO3, CaCO3, V2O5, CuO were weighed on digital balance within 1 mg accuracy. The powders were mixed and ground in an agate mortar and pestle for 2 h and then the mixed powders were calcined in air at 8100C for 24 h. The porcelain crucibles were used for calcinations and sintering. The porcelain crucibles have a melting point of 14000C, are not contaminated with the materials being used and are economical. The aim of the calcination was to eliminate the carbonates and to produce an oxide with a nominal composition Bi1.3V0.3Pb0.4Sr2Ca2Cu3Oδ. The polyvinyl alcohol (PVA) was used as a binder for pellet formation. A pressure of 50 kN was applied to all the pellets by ahydraulic press. The pellets with nominal composition Bi1.3V0.3Pb0.4Sr2Ca2Cu3Oδwere finally sintered in air at 840 ±50C for 216 h in three steps (first step 96 h, second step 72 h and the third 48 h) and gradually cooled down to room temperature. Phase purity and lattice parameters were determined by X-ray diffraction (XRD). XRD data were taken using CuKα (1.5406 Å) radiation. Grain size was analyzed from scanning electron microscopic (SEM) image taken on the surface on several cross-sectional cuts. No appreciable variations of size and aspect ratio of grains were observed for the different zones. DC electrical resistivity was used to characterize superconducting properties of the samples using standard four-probe DC technique, in the temperature range from 77 to 300 K. The critical current density of the sample was measured by the four-probe method in such away that the current may pass through the bulk of the specimen. For the calculation of Jc the following equation is used

Jc= Ic/ A = Ic/ (WT)E1

where A is the area of cross section, W is the width, Icis the critical current and T is the thickness of the sample. Considerable care was taken to ensure that results were not affected by heating at the current contacts. The mutual inductance bridge method was used for AC magnetic susceptibility measurements. For these measurements, a very low AC field (0.5 Oe) was applied parallel to the axis of the rectangular bar-shaped specimen. The temperature range was again 77–300 K. The thermal conductivity as a function of temperature was measured using the advantageous transient plane source techniques (ATPS). The detail of the ATPS technique is described in (Rehman & Maqsood, 2005; Gusstafsson, 1991; Rehman, 2009) at length. Two identical sizes of the sample (diameter 25 mm × thickness 10 mm) were used for measurements. Thermoelectric power S(T)was obtained by taking the ratio of the voltage difference to the temperature gradient as

S =ΔV / ΔTE2

where ΔV is the voltage arising (in the absence of an applied field) across the sample with a temperature difference of ΔT between its ends, given by the relation

S = E / ΔTE3

where E is the electric field in the sample. The detail of the apparatus used is already published (Rehman & Maqsood, 2005).


3. Results and discussion

X-ray diffraction (XRD) pattern of the sample with nominal composition Bi1.3V0.3Pb0.4Sr2Ca2Cu3Oδafter the final sintering of 216 h is shown in Figure 2. XRD pattern was taken using CuKα radiation (λ = 1.5046 Å) and measurements were taken at room temperature. All the peaks in the XRD pattern are indexed. XRD pattern showed peaks belonging to the high-Tc(2223) phase as a major component along with peaks due to the low-Tc(2212) phase. The dominant is the high-Tc(2223) phase having orthorhombic structure with lattice constants: a = 5.417(6) Å, b = 5.392(7) Å and c = 37.164(3) Å. The SEM result of the sample is shown in Figure 3.

It is clear from the figure that the superconducting grains are connected with each other, but with the unfilled spaces between them. This type of granular morphology has been rarely discovered in conventional high temperature crystalline superconducting samples. Furthermore, the average grain size was calculated at different spots of the sample and found to lie between 3 and 4 μm. The electrical property of the sample was examined by DC electrical resistivity measurements. The DC electrical resistivity as a function of temperature is also shown in Figure 4, after the final sintering step of 216 h. The DC electrical resistivity measurements show a well defined metallic behavior and the superconducting transitions. The resistivity versus temperature plot shows that the resistivity decreases linearly with temperature in the normal state. The onset temperature Tc(onset) and zero resistivity critical temperature Tc (R = 0) were found to be 112 ± 1 K and106 ± 1 K, respectively. The measured

Figure 2.

Indexed X-ray pattern of Bi1.3V0.3Pb0.4Sr2Ca2Cu3Oδ superconductor

Figure 3.

SEM micrograph of the sample with composition Bi1.3V0.3Pb0.4Sr2Ca2Cu3Oδ

Figure 4.

Temperature dependence of DC electrical resistivity of the sample with nominal composition Bi1.3V0.3Pb0.4Sr2Ca2Cu3Oδ after final sintering time of 216 h

Figure 5.

Critical current density of the sample with composition Bi1.3V0.3Pb0.4Sr2Ca2Cu3Oδ at 77 K

mass densityof the sample was 3.58±0.01 g/cm3. The critical current density of the samples was measured at a temperature of 77K in zero magnetic field as shown in Figure 5. It is clear that the value of the critical current density increases as the dopant concentration of vanadium increases, as compared to the undoped samples (Gul et. al., 2005). The increase in the critical current density is due to the fact that the increase in the concentration of vanadium increases the flux pinning, and strong coupling between the grain results in high values of critical current density (Jc).

The measurement of the real part χ/of the AC magnetic susceptibility on the sample Bi1.3V0.3Pb0.4Sr2Ca2Cu3Oδis clearly showing that there are two phases. The curve of Figure 6displays a two-step process which reflects the flux penetration between and into the grains, as temperature decreases.

Figure 6.

Temperature dependence of the real part of AC susceptibility of the samplewith composition Bi1.3V0.3Pb0.4Sr2Ca2Cu3Oδ

The diamagnetic transition in χ/ seems to occur in the first phase with onset temperature Tc(onset) around 113 ± 1 K. Another drop in diamagnetic signal is observed around 106 ± 1 K. This second phase has comparatively slow transition and it reflects the presence of low-Tc (2212) component, which is also confirmed by X-ray analysis. It is well known that the demagnetizing correction would cause χ/ =−1 for a sufficiently low temperature. It is evident from Figure 2that X-ray diffraction measurement supports the observation of AC magnetic susceptibility. When the sample is at a temperature just below Tc(R = 0), the superconducting grains shield the applied magnetic field. As the temperature decreases further, the inter-granular component χ/ appears and rapidly grows proportionally to the quality of interconnectivity of the grains, and volume fraction of the sample is expected to be shielded by the super current circulates in the samples, and hence the curve of χ/ versus temperature saturates. Thermal conductivity measurement as a function of temperature ranging from 77 to 300 K is done using advantageous transient plane source (ATPS) technique. Thermal conductivity results are shown in Figure 7.

Figure 7.

Thermal conductivity (λ) as a function of temperature along with electron (λe) andphonon (λph) contributions

This plot shows that there is a change in thermal conductivity at 105±1 K corresponding to Tc (R = 0). There is an increase in slope close to Tc (R = 0), which is in good agreement with the literature (Aliev, 1992; Dey, 1991; Jezowski, 1992) and also agrees with the DC electrical resistivity and AC magnetic susceptibility measurements. In superconducting state theelectrons, which become Cooper pairs, no longer are allowed to exchange energy with phonon; therefore, the lattice conduction rises as more and more Cooper pairs are formed. To find the electron–phonon scattering time (τeph), the relation reported by Hook and Hall (Hook & Hall, 1991) is used as

/ρeph= ne2τeph/ meE4

where n, e and meare the number density, charge and mass of the electron, respectively, ρephbeing the resistivity at a particular temperature. This gave τeph= 2 × 10−15 s at 118 K, the temperature above which the resistivity is linear with temperature. Also, the phonon-limited mobility can be calculated using the relation (Hook & Hall, 1991)

μeph= eτeph/ meE5

The calculated value of the phonon-limited mobility is 3 × 10−4 C-S-Kg−1. To estimate the size of the electron–phonon coupling constant, the lowest order variational solution of the Bloch–Boltzmann transport equation (Pinksi, 1981) is

ħ / τeph=2πdephkBTE6

here deph is the electron–phonon coupling constant which is 6. These results are in good agreement with the results reported by other authors (Heremans, 1988; Suleiman, 1993). The heat flux in solids consists of two contributions: energy transport associated with the flow of the charge carriers that are referred to as the electronic thermal conductivity, and thermal energy carried by lattice vibrations that is known as the lattice or phonon thermal conductivity. As is well known, the thermal conductivity (λ)of metals is given by these two contributions:

λ = λe+λphE7

here λeis the thermal conductivity due to electrons and λphis the thermal conductivity due to phonons. In simple metals, the separation of the two components of the thermal conductivity is made by use of the Wiedemann–Franz (WF) law (Ziman, 1963),

λenρ / T= (1/ 3)π2(k2B/ e2) = 2.45×108W.Ω.K2E8

where, λenis the electronic thermal conductivity in the normal state, ρ is the electrical resistivity, kBis the Boltzmann constant. In ordinary metals, the WF law fails at intermediate temperatures where the electrical resistivity ρ deviates from the T linear dependence. The electrical resistivity of oxide superconductors shows the characteristic T linear dependence over quite a wide temperature range, as can be seen in Figure 4. Accordingly, the WF law is expected to hold over the entire temperature range above Tc (R = 0)for the oxide superconductors and to result in constant and small λen, making a marked contrast to ordinary metals. Below Tc (R = 0)the charge carriers that have condensed in the ground state do not contribute to the heat conduction, and the electronic component λesis expected to decrease with lowering temperature. Among several theories (Bardeen, 1962; Tewordt, 1963) that treat λes, we refer to revised Kadanoff’s formulation adapted by Ikebe et al. (Ikebe, 1994) to observe the linear dependence of ρ,

here, a represents the ratio of the T -linear electrical resistance at Tc(R = 0)to the residual resistance, β = 1/kBT, and Δis the BCS energy gap in the Buckingham (Bardeen, 1957; Buckingham, 1956) form,

Δ= 3.2kBTc(1 T / Tc)1/2E9

The electronic and phonon contribution to thermal conductivity is estimated by (7), (8) in normal and superconducting state, respectively, as is shown in Figure 7, along with λ. The thermoelectric power is used as a medium to investigate the physical properties, in particular the properties thatcan be correlated with the transport mechanism that occurs in these superconductors. Thermoelectric power is a sensitive property in high-temperature superconductors, particularlyto determine the sign of the charge carriers. The apparatus for the measurement of thermoelectricpower was being assembled. In the aim to test the apparatus, it was calibrated with copper. Figure 8 shows that the behavior of the thermoelectric power of copper is almost linear with temperature. The magnitude of thermoelectric power of copper is approximately what one expects in noble metals such as silver and gold.

The thermoelectric power of these metals is positive except at very low temperatures. The positive sign of these metals is due to that of the Fermi surfaces touching the Brillouin zone boundaries. The Fermi surface areas could decrease with an increase of the electron energy (Barnard, 1972). Thermoelectric power (thermopower or Seebeck coefficient) determines the interaction between electrical and thermal currents in a conductor. The phonon–phonon

Figure 8.

Absolute thermoelectric power of copper as a function of temperature

Figure 9.

Thermoelectric power of the sample with composition Bi1.3Pb0.4V0.3Sr2Ca2Cu3Oδ

interaction is dominant at higher temperature, arises from anharmonicity in potential and this increase with temperature. At low temperature phonon–phonon interaction is less important. The precise form of the curve at very low temperatures is uncertain because the thermopower increases rapidly associated with the metal impurities, notably iron. Thus minute quantities of iron were the cause of this increase in thermopower even in the ultra-pure copper at very low temperature (Gul, et. al., 2005). Thermoelectric power of the superconducting sample measured in the temperature range 85–300 K is shown in Figure 9.

From the figure, it is clear that thermoelectric power increases with decreasing temperature and drops rapidly to zero at superconducting transition phase. From transition to room temperature, thermoelectric power is closely linear with temperature and its profile is similar to that of other high-Tc superconductors (Mitra & Trefny, 1988). The critical temperature in thermoelectric power is observed at 116 ± 1 K, after that thermoelectric power begins to decrease and becomes almost zero at 88 ± 1 K. The critical temperature Tcalready determined from electrical resistivity was 106±1 K. To explain these results, we assume that two kinds of carriers existed simultaneously in our sample: electrons and holes. The values of thermoelectric power in our sample are very small so we can say that a very week Seebeck coefficient shows that the behavior of the sample is typically metallic. In any superconductor, two types of contributions are important: one from phonons and the other from electrons. But contribution due to phonons is not important above the liquid nitrogen temperature (Yan,, 1988).

It is also noted that the onset temperature drops of thermoelectric power are higher than those of the resistance drops. A possible explanation might be as follows. Since these materials are granular, one expects high electrical resistance between grains. On the other hand, the temperature drops between grains are expected to be small and, consequently, the granular nature would have less effect on thermoelectric power than the electrical resistivity (Lim, et,al. 1989). Polycrystalline HTSCS are generally viewed as an agglomeration of grains compacted together. On deoxygenation, the surface of the grains loses more and more oxygen than the grain itself. For T <Tc (R = 0), the grains become good superconductors where they are coupled together by weak links formed within the intergranular region. The weak links behave as superconducting region with very small critical current. These links become weaker and weaker with increasing deoxygenation. In such a situation, a very small current used in the critical resistivity measurement can exceed the Jc of the weak links, resulting in the breakdown of the percolation chain. Consequently, the resistance can persist. The temperature Tc (R = 0)Sis lower than the Tc (R = 0)of the bulk material as long as Jc of the weak links is smaller than the transport current density. However, contrary to the resistivity measurement, the thermopower experiment is performed in the absence of any current. Hence the percolation chain of the superconducting grains can persist up to temperatures higher than Tc (R = 0) RESeven in the presence of a small temperature gradient. This shifts Tc (R = 0)S to relatively higher temperatures (Dey, et. al., 1998).


4. Conclusions

A superconducting sample with nominal composition Bi1.3V0.3Pb0.4Sr2Ca2Cu3Oδwas prepared by the solid state reaction method. By resistivity measurement, Tc (R = 0)RESobtained for this composition was 106± 1 K. Thermal conductivity variation with temperature showed initially a slight decrease and then a pronounced increase around Tc (R = 0). Although the expected theoretical trend is similar, the peak near T/2 was not observed due to temperature limitations of the temperature controller. A similar behavior is observed in all hole-type CuO2 plane superconductors and in all their structural forms. This effect is due to phonon or quasiparticle scattering. The Wiedemann–Franz law is applied to predict the magnitude of electron and phonon contributions to the total thermal conductivity of the samples, whereas Tc(onset) observed was at 112 ± 1 K. Thermoelectric power of the sample was positive in the temperature range 85– 300 K. The behavior of thermoelectric power in this superconducting sample was approximately linear with temperature as observed in other Bismuth-based high-Tcsuperconductors. The transition temperature of this superconductor Tc (R = 0)S was measured to be 116 ± 1 K, whereas the transition temperature of this sample measured with resistivity, Tc (R = 0)RES, method was 106±1 K. The difference between Tc (R = 0)RES and Tc (R = 0)Sis 10 K. This difference increases as more and more oxygen is being taken out of the compound by deoxygenation.



The authors would like to acknowledge the Higher Education Commission (HEC) Islamabad, Pakistan for the financial support. Mr. A. Abdullah is acknowledged for useful support in preparation of the manuscript.


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Written By

Asghari Maqsood and M. Anis-ur-Rehman

Submitted: October 10th, 2010 Published: June 27th, 2011