Journal of Solid State Physics

Volume 2014 (2014), Article ID 716032, 7 pages

http://dx.doi.org/10.1155/2014/716032

Research Article

Investigation of Structural Formation of Starting Composition 2245 in the Bi-Pb-Sr-Ca-Cu-O System Superconductors

Ashoka Nukkanahalli Venkataswamy,¹ George Thomas Chirayil,¹ and Srinivasan Kannaiyan²

¹Department of Physics, Christ University, Bangalore 560 029, India

²Department of Physics, Government First Grade College, K R Puram, Bangalore 560 036, India

Received 5 June 2014; Revised 7 August 2014; Accepted 8 August 2014; Published 15 September 2014

Academic Editor: Veer P. S. Awana

Copyright © 2014 Ashoka Nukkanahalli Venkataswamy et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

Abstract.

Structural formation of Bi1.65Pb0.35Sr₂Ca₄Cu₅Oy (2245 phase) superconducting compound was investigated by preparing the sample in a new matrix route. The phases formed at different intervals of heat treatment are monitored by X-ray diffraction studies. Bi-2212 phase was found to be the predominant phase till 20 hours of sintering at 850°C after which Bi-2223 phase was found to be the major phase. Traces of Ca₂PbO₄ were also noticed along with 2212 and 2223 phases. For the first time, the highest onset of 127 K with maximum superconducting volume fraction was observed for the sample sintered at 850°C for 30 hours in this preparation. Further sintering is found to deteriorate the onset value of the sample. There was no signature of the formation of 2234 or 2245 phase in this synthesis.

1. Introduction

The bismuth system superconductors are generally represented by the formula Bi₂Sr₂Can −1CunO2n+4 with critical temperature () values around 10 K, 80 K, and 110 K for , and 3, respectively [1, 2]. Among the above, member, namely, Bi₂Sr₂Ca₁Cu₂O₈ (2212), is found to be the most stable one. Preparation of member, Bi₂Sr₂Ca₂Cu₃O₁₀ (2223), as a single phase is extremely difficult because of the intergrowth of low 2212 phase with 2223 phase. Many research groups have tried to synthesize 2223 compound as a single phase [3–8]. The addition of lead to the superconducting Bi-Sr-Ca-Cu-O compounds leading to the formation of 2223 phase has been reported by Wang et al. [5]. Shi et al. [6] have tried to synthesize 2223 phase by heating an off stoichiometric starting composition with excess Ca and Cu. Sastry et al. [7] have tried the matrix method to obtain a single phase 2223 compound with a   120 K. Though there were many attempts made to synthesize (2234) and (2245) members [9, 10], no conclusive evidence is available on the structure and   values of the above phases. In this paper we report the results of our attempt to synthesize the 2245 phase by solid state reaction method.

2. Materials and Methods

The sample Bi1.65Pb0.35Sr₂Ca₄Cu₅Oy was prepared by solid state reaction method as the combinations of two matrices M₁ and M₂ (M₁ = Bi1.65Pb0.35Sr₂Cu₃Ox and M₂ = 2Ca₂CuO₃). High purity (99.9%) Bi₂O₃, PbO, SrCO₃, CaCO₃, and CuO powders were used as starting materials. The powders with the molar ratio of [Bi] : [Pb] : [Sr] : [Cu] = 1.65 : 0.35 : 2 : 3 (matrix M₁) and [Ca] : [Cu] = 4 : 2 (matrix M₂) were separately prepared by thoroughly mixing the components for about an hour using an agate mortar and pestle. The final mixtures in powder form were kept in two alumina crucibles and calcined at 810°C for 16 hours in a tubular furnace. The calcined powders were reground and pressed into pellets of about 10 mm in diameter and 2 to 3 mm in thickness under a pressure of 5 tons/cm². These pellets of matrices M₁ and M₂ were sintered at 835°C for 40 hours with two intermediate grindings and pelletisation and then furnace cooled to room temperature. One pellet of each sample was used for experimental measurements such as X-ray diffraction (XRD), SEM, and EDAX.

The two matrix samples M₁ and M₂ were mixed stoichiometrically into M₁₂ sample of composition Bi1.65Pb0.35Sr₂Ca₄Cu₅Oy. The samples were well ground and mixed thoroughly into a fine powder. It is pressed into pellets of 10 mm diameter and 2 to 3 mm thick. These pellets were kept in a crucible and pulled along the axis of the tubular furnace at the rate of 1 cm per minute. The constant temperature region of the furnace was maintained at 900°C and it took about 40 minutes to pull the samples from one end to the other end of the furnace. The temperature profile along the axis of the tubular furnace is shown in Figure 1. Though a slight melting was observed on the surface of the pellets, all the pellets could be separated. These pellets were further sintered in air at 850°C for varying durations of 5 hours, 10 hours, and 15 hours, removing one pellet at the end of each interval after furnace cooling. The remaining pellets were ground, repelletised, and sintered at 850°C and one pellet each was removed as before at the end of total of 20 hours, 25 hours, 30 hours, and 40 hours, respectively. The removed pellets were labelled as M₁₂ (A, B, C, D, E, F, and G), respectively. For comparison, one more sample of the same composition was prepared by the usual solid state reaction route in which all the constituent compounds are mixed initially and calcined at 810°C for 20 hours, followed by sintering at 835°C for 45 hours with one intermediate grinding and pelletisation. This sample is labelled as P 2245.

Figure 1: Temperature profile of the tubular furnace.

One part of each pellet was cut, powdered, and used for X-ray diffraction, scanning electron microscopy (SEM), and energy dispersive X-ray analysis (EDAX) measurements. Another piece of the pellet was used for measurement. The of the sample was determined by self-inductance method. A Colpitts oscillator and a frequency counter along with a liquid nitrogen cryostat were used for the purpose. The temperature of the sample was recorded using a calibrated chromel-alumel thermocouple with an accuracy of ±1°C. The of the samples were also confirmed by resistance measurement using the conventional four-probe method.

3. Results and Discussion

The X-ray diffraction patterns of the matrices M₁ and M₂ are shown in Figure 2. The XRD of matrix M₁ indicates almost a single phase compound and is indexed in an orthorhombic cell with cell parameters  Å,  Å, and  Å. The XRD pattern is similar to the one obtained by Sinclair et al. [11]. Two peaks of unreacted CuO were also identified in the XRD pattern of M₁. All the peaks in the XRD pattern of matrix M₂ (except one small peak at due to CuO) were indexed in an orthorhombic cell with cell parameters  Å,  Å, and  Å. This pattern is similar to that of pure Ca₂CuO₃ compound identified with the ICDD XRD file (34-0282) as reported by Breuer et al. [12].

Figure 2: X-ray diffractogram of matrices M₁ and M₂.

The XRD pattern of samples M₁₂ (A, B, C, and D) is indicated in Figure 3. The XRD pattern shows that majority of the peaks belong to 2212 phase (marked as L). Three peaks of Ca₂PbO₄ at 2θ = 17.62°, 31.06°, and 32.08° have also been identified in B, C, and D patterns. It can be noted that peaks due to 2223 phase (marked as H) gradually develop as the duration of heat treatment is increased. The analysis of XRD pattern of the samples M₁₂ (E, F, and G) (Figure 4) has shown an increase in cell parameter values and has been indexed in a tetragonal structure with  Å and  Å. These peaks are due to the 2223 phase which has formed when the duration of heat treatment exceeded 20 hours at 850°C. Figure 5 shows the XRD pattern of the sample P2245. Except for three peaks at 2θ = 17.62°, 31.06°, and 32.08° of Ca₂PbO₄ all peaks are identified with that of 2223 phase. The lattice parameters of all the samples calculated from XRD data are given in Table 1.

Table 1: Heating profile and results of X-ray diffraction analysis of samples.

Sample name
History of heat treatment

Å

Å

Å
Cell volume

(10⁻³⁰) m³
Grain size

(in nm)

Temperature (°C)
Duration (hours)

M₁
835
42
5.387
5.301
24.574
701.747
40.116

M₂
835
42
12.247
3.780
3.259
150.871
74.570

M₁₂ A
850
5
5.393
5.421
30.788
900.200
61.139

M₁₂ B
850
10
5.389
5.395
30.767
894.580
75.690

M₁₂ C
850
15
5.392
5.365
30.874
893.198
61.137

M₁₂ D
850
20
5.401
5.391
30.775
896.255
72.250

M₁₂ E
850
25
5.404
5.396
37.253
1086.570
63.580

M₁₂ F
850
30
5.398
5.402
37.220
1085.335
58.870

M₁₂ G
850
40
5.390
5.415
37.216
1086.217
44.170

P 2245
835
45
5.423
5.407
37.003
1085.008
68.814

Figure 3: X-ray diffractogram of samples M₁₂ (A, B, C, and D).

Figure 4: X-ray diffractogram of samples M₁₂ (D, E, F, and G).

Figure 5: X-ray diffractogram of sample P 2245.

The scanning electron microscope (SEM) images and superimposed EDAX spectra of samples M₁ and M₂ are represented in Figure 6. The EDAX spectra are in conformity with the atomic weight percentage of constituent elements as per the stoichiometry. As evident, SEM images reveal a granular and porous surface. The average grain size is calculated from XRD data using Scherrer formula, , where is the grain size, is the wavelength of the X-rays, is the Bragg angle, and is the full width at half maximum (FWHM). SEM images of samples M₁₂ (E, F, and G) and P 2245 are indicated in Figure 7. The variation of average grain size with duration of heating is shown in Figure 8. The mean value of grain size is found to be about 60 nm.

Figure 6: SEM and EDAX images of the samples M₁ and M₂.

Figure 7: SEM images of the samples M₁₂ (E, F, and G) and P 2245.

Figure 8: Grain size versus duration of heating.

The normalised frequency (, where is room temperature frequency) of Colpitts oscillator versus temperature plots of the samples after different durations of heat treatment is represented in Figure 9. The normalised resistance (, where is the resistance at room temperature) versus temperature graph of selected samples is shown in Figure 10. Table 2 shows the values and identified phases in the prepared samples. The superconducting signature is observed in the sample only after 15 hours of sintering at 850°C. The volume fraction of the superconducting phase gradually increases with increase in the duration of heat treatment which is evident from the steeper transitions (Figure 9, M₁₂ C and D). The major phase present in the sample after 20 hours of heating is 2212 phase. The sample heated for 25 hours at 850°C shows a two-step transition, one around 125 K (2223 phase) and another at around 105 K (2212 phase). The corresponding XRD pattern (Figure 4, M₁₂E) confirms this observation. The maximum value of onset (127 K) was observed for the sample heated for 30 hours (Figure 9, M₁₂F). The sample heated for 40 hours shows the onset at 125 K but the volume fraction of the superconducting phase has decreased drastically which is evident from the relatively smaller change in frequency. The XRD pattern of this sample (Figure 4, M₁₂G) also shows two peaks at 2θ = 27.8° and 28.1°, respectively, which are identified with that of Bi₂O₃. Therefore, it is inferred that prolonged heating up to 40 hours has resulted in some Bi₂O₃ coming out of the structure and hence the decrease in volume fraction of the superconducting phase. The   values measured by four-probe method also shows similar values which are tabulated in Table 2.

Table 2: values and identified phases in the samples.

Sample
Sintering at 850°C

        (hours)
        Phases identified

            from XRD
Colpitts oscillator
Four-probe

onset (K)
(K)
onset (K)
zero (K)

M₁₂ A
5
2212, 2223, Ca₂PbO₄

M₁₂ B
10
2212,2223, Ca₂PbO₄

M₁₂ C
15
2212, 2223, Ca₂PbO₄
110
—
—
—

M₁₂ D
20
2212, 2223, Ca₂PbO₄
120
—
—
—

M₁₂ E
25
2223, 2212, Ca₂PbO₄
124
107
125, 111
95

M₁₂ F
30
2223, 2212, Ca₂PbO₄
127
110
127, 115
105

M₁₂ G
40
2223, 2212, Ca₂PbO₄, Bi₂O₃
122
100
121
105

P 2245
45
2223, 2212
119
100
120
100

Figure 9: Normalised frequencies versus temperature curves of samples.

Figure 10: Normalised resistance versus temperature curves of the selected samples.

The   value of cuprate superconductors is known to vary with oxygen stoichiometry and is found to be a maximum for an optimum value of oxygen content. This can be manifested in terms of partial change of the valence state of copper from Cu²⁺ to Cu³⁺ in the Bi system superconductors [13–16].

4. Conclusions

We synthesised Bi1.65Pb0.35Sr₂Ca₄Cu₅Oy superconductor by the matrix method with a new sintering cycle. The sample was initially heated at a comparatively high temperature of 900°C for a short duration followed by sintering at 850°C for different durations. The formation of the different phases as a function of duration of heat treatment was monitored. The X-ray diffraction analysis of the prepared samples revealed the presence of predominantly 2212 phase when sintered at 850°C for 20 hours. Further sintering at the same temperature for 25 hours, 30 hours, and 40 hours, respectively, resulted in the formation of the 2223 phase as the major component. But after 40 hours of sintering, Bi₂O₃ was noticed to be coming out of the structure. The highest onset value (127 K) with maximum superconducting volume fraction was found for the sample sintered at 850°C for 30 hours. The presence of Ca₂PbO₄ is noticed in all samples which are preheated at 900°C. No traces of 2234 or 2245 phase were noticed under the above preparation conditions.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

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