Chinese Journal of Polar Since  2018, Vol. 31 Issue (2): 191-196

The article information

Bang-zheng Wei, Yu Wang, Meng Liu, Chen-xi Xu, Ji-gui Cheng
魏邦争, 王语, 刘梦, 徐晨曦, 程继贵
Effects of Praseodymium Doping on Conductivity and Oxygen Permeability of Cobalt-Free Perovskite-Type Oxide BaFeO3-δ
Chinese Journal of Polar Since, 2018, 31(2): 191-196
化学物理学报, 2018, 31(2): 191-196

Article history

Received on: August 29, 2017
Accepted on: February 2, 2018
Effects of Praseodymium Doping on Conductivity and Oxygen Permeability of Cobalt-Free Perovskite-Type Oxide BaFeO3-δ
Bang-zheng Weia,b, Yu Wanga, Meng Liua, Chen-xi Xua,b, Ji-gui Chenga,b     
Dated: Received on August 29, 2017; Accepted on February 2, 2018
a. School of Materials Science and Engineering, Hefei University of Technology, Hefei 230009, China;
b. Key Laboratory of Advanced Functional Materials and Devices of Anhui Province, Hefei 230009, China
*Author to whom correspondence should be addressed. Ji-gui Cheng,
Abstract: Among the perovskite-type oxides with symmetrical structure applied in oxygen permeable membranes, cubic phase structure is the most favorable for oxygen permeation.In order to stabilize the cubic perovskite structure of BaFeO3-δ material at room temperature, iron was partially substituted by praseodymium.BaFe1-yPryO3-δ powders were synthesized by a solid state reaction method, and sintered samples were prepared from the synthesized BaFe1-yPryO3-δ powders.X-ray diffraction results reveal that the BaFe1-yPryO3-δ samples remain cubic structure at praseodymium substitution amount of y=0.05, 0.075, 0.1.Scanning electron microscope observation indicates that the sintered samples contain only a small amount of enclosed pores and the grain size of BaFe1-yPryO3-δ increase monotonically with the increase of the praseodymium doping amount, praseodymium doping promotes the grain size growth.Tests of electrical conductivity and oxygen permeation flux show that praseodymium doping improves the conduction properties of BaFe1-yPryO3-δ and BaFe0.9Pr0.1O3-δ composition has an electrical conductivity of 6.5 S/cm and an oxygen permeation of 1.112 mL/(cm2·min) at 900 ℃, respectively.High temperature XRD investigation shows that the crystal structure of BaFe0.975Pr0.025O3-δ membrane completely transform to cubic phase at 700 ℃.The present test results have shown that partially substitution of Fe by praseodymium in BaFeO3 can stabilize the cubic structure and improve the properties.
Key words: BaFe1-yPryO3-δ     Praseodymium doping     Cubic perovskite     Oxygen permeability    

Fossil energy is still the major energy sources in current industrial production, such as coal, oil and natural gas, etc., and enhancing its utilization efficiency and reducing emissions of polluted gases have become one of the most imperative requirements in energy and environment areas. Using oxygen enriched air or pure oxygen instead of air as oxidizer combustion is one of the effective ways to meet the needs. However, the traditional oxygen production processes, such as cryogenic separation and pressure swing adsorption have some disadvantages, including high production cost and low purity of resultant [1, 2]. As a new oxygen production technology, separating oxygen from air by ceramic membranes has shown to be a promising process due to the advantages of without additional circuitry required and high oxygen selectivity of about 100% [3, 4].

Perovskite-type (ABO$_3$) materials with mixed ionic and electronic conductivity (MIEC) have attracted enormous attentions in oxygen permeable membranes [5, 6, 7]. Since the reports of the high oxygen permeability of La$_{1-x}$Sr$_x$Co$_{1-y}$Fe$_y$O$_{3-\delta}$ by Teraoka et al. [8], many cobalt-based perovskite-type oxygen permeable membranes have been developed, e.g. SrCo$_{0.8}$Fe$_{0.2}$O$_{3-\delta}$ [9, 10], Ba$_{0.5}$Sr$_{0.5}$Co$_{0.8}$Fe$_{0.2}$O$_{3-\delta}$ [11, 12], SrCo$_x$ Nb$_{1-x}$O$_{3-\delta}$ [13, 14], BaCo$_{0.7}$Fe$_{0.3-x}$Nb$_x$O$_{3-\delta}$ [15, 16], 60wt%Ce$_{0.9}$Gd$_{0.1}$O$_{2-\delta}$-40wt%Ba$_{0.5}$Sr$_{0.5}$Co$_{0.8}$Fe$_{0.2}$ O$_{3-\delta}$ [17]. However, cobalt-based perovskite-type oxides may be not favorable for practical uses because of their relatively low stability under harsh conditions due to the evaporation and reduction of cobalt [18, 19]. To overcome this drawback, some cobalt-free perovskite-type materials have been developed to use as oxygen permeable membranes. Benefiting from the less flexible redox behavior of iron, Fe replacing Co as B-site ions in the ABO$_3$ perovskite-type materials has been investigated. Among the ferrum-based perovskite-type materials, BaFeO$_{3-\delta}$ has high oxygen permeability because Ba can expand the lattice free volume and lower the average metal-oxygen bond energy in the lattices [20]. Nevertheless, Ba has a large ionic radius, which results in a phase transition of the BaFeO$_{3-\delta}$ materials as temperature decreases [21]. At high temperature, the crystal structure of BaFeO$_{3-\delta}$ materials is cubic phase, however, at low temperature, which probably transforms to hexagonal, tetragonal, triclinic, etc. [22]. Cubic phase provides a large channel for oxygen ions transmission in their interior due to the relatively open space, moreover, the equivalent positions of which are the most, that conducive to the migration of oxygen ions. Thus, in the same material system, the cubic perovskite structure has the highest oxygen permeation flux. Ramadass introduced the concept of tolerance factor ($F_{\rm{t}}$) to characterize the stability of cubic perovskite structure [23]:

$ F_{\rm{t}}= \frac{{\left( {r_{\rm{A}} + r_{\rm{O}}} \right)}}{{\sqrt 2 \left( {r_{\rm{B}} + r_{\rm{O}}} \right)}} $ (1)

Where $r_{\rm{A}}$, $r_{\rm{B}}$ and $r_{\rm{O}}$ are radii of A, B site ions and oxygen ion, respectively. It is usually considered that the material can keep the ideal cubic structure when 0.95 < $t$ < 1.04 [24], and the $t$ of BaFeO$_{3-\delta}$ is calculated to be 1.066, which is beyond the established range.

Previously, several reports have shown that it is feasible to stabilize the phase of BaFeO$_{3-\delta}$ with cubic perovskite structure at low temperature by partial substitution of A or B site ions, such as these in Ba$_{0.95}$La$_{0.05}$FeO$_{3-\delta}$ [25], Gd$_{0.33}$Ba$_{0.67}$FeO$_{3-\delta}$ [26], BaFe$_{1-y}$Ta$_y$O$_{3-\delta}$ [27], BaNb$_y$Fe$_{1-y}$O$_{3-\delta}$ [28] and BaFe$_{1-y}$Cu$_y$O$_{3-\delta}$ materials [29]. The ionic radii of Pr$^{3+}$ and Pr$^{4+}$ were 0.99 and 0.85 Å, respectively, which are slightly larger than that of Fe$^{3+}$ (0.55 Å) and Fe$^{4+}$ (0.585 Å) of B-site ions, meanwhile, much smaller than that of Ba$^{2+}$ (1.61 Å). Therefore, in this paper, Pr$^{n+}$ were selected as the doping ions to partial substitute Fe$^{m+}$ in BaFeO$_3$ materials, and the influences of partial substitution on the crystal structure, microstructure, electrical conductivity and oxygen permeability of BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ have been systematically investigated.

Ⅱ. EXPERIMENTS A. Samples preparation

BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$($y$=0, 0.025, 0.05, 0.075, 0.1) powders were synthesized by the solid state reaction method in which BaCO$_3$, Fe$_2$O$_3$, Pr$_6$O$_{11}$ powders were weighed according to stoichiometric ratio, after ball-milling with zirconia media in absolute alcohol for 20 h, the dried powder mixes were pressed into block, calcined at 1100 ℃ for 5 h in air, and then ball-milled for 10 h to obtain BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ powders. In order to characterize the electrical conductivities, oxygen permeation fluxes and some other performance of the prepared materials, the synthesized powders were pressed into green bars and disks under a pressure of 150 MPa, respectively, and subsequently sintering in air at 1300 ℃ for 5 h. The surface of the sintered samples were then polished with an emery paper (80) to adjust the dimensions of sintered bars with of 4 mm$\times$5 mm$\times$10 mm and thickness of disks with 1.0 mm.

B. Characterizations

Relative densities of the sintered samples were measured using the Archimedes' method. The crystal structures of the BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ powders at room temperature were characterized by X-ray diffraction (XRD D/MAX2500V) using CuK$\alpha$ radiation, with diffraction angles of 10$^\circ$$\leq$2$\theta$$\leq$80$^\circ$ at an interval of 0.02$^\circ$. The crystal structures of BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$ membrane were characterized by a high-temperature X-ray diffraction (HT-XRD), the temperature was slowly increased from room temperature to 100, 200, 300, 400, 500, 600, 700, 800, 900 ℃ and maintained constant at each designated temperature for 30 min before measurements were taken. The elemental compositions of BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$ powders was analyzed by energy dispersive spectrometer (EDS). The surface and cross section morphologies of BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$ and BaFe$_{0.925}$Pr$_{0.075}$O$_{3-\delta}$ disks were examined by scanning electron microscope (SEM, JSM-6490LV).

C. Electrical conductivity measurements

The electrical conductivities of the BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ bars were measured using a four-probe DC method between 300 and 900 ℃ at an interval of 50 ℃. Silver paste and silver wire were used as current collector and current wire, respectively. A constant current was applied to the two current wires, and the voltage response $\sigma$ on the two voltage wires was recorded by Digital Multimeter (U3606A), the electrical conductivity σ was calculated according to Eq.(2).

$ \sigma = \frac{L}{{RS}} $ (2)

Where $L$ is the length of the two voltage contacts, $R$ and $S$ are the resistance and cross-sectional area of BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ bars, respectively.

D. Test of oxygen permeability

The oxygen permeation flux of BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ membranes were tested using a homemade apparatus, described in our previous work [30]. The membranes were sealed onto an Al$_2$O$_3$ tube using a commercial ceramic sealant (Yihui, Hongkong). Within test temperature range of 600$-$950 ℃, the feed side of membranes was exposed to atmospheric air, whilst a 100 mL/min flow of helium was fed with the permeating side to provide the oxygen partial pressure. Flow flux of the helium was controlled by a mass flow controller (D08-1F). The content of O$_2$ and N$_2$ in the permeation gas were analyzed by the gas chromatography, where N$_2$ is the leak gas. The effect of leakages can be estimated using Eq.(3) to calculate the oxygen permeation flux:

$ J_{{\rm{O}}_2} = \left[{C_{\rm{O}}-C_{\rm{N}} \times \frac{{0.21}}{{0.79}} \times {{\left(\frac{{28}}{{32}}\right)}^{1/2}}} \right] \times \frac{f}{S} $ (3)

Where $C_{\rm{O}}$ and $C_{\rm{N}}$ are the measured gas phase concentrations of oxygen and nitrogen in the sweeping gas, $f$ is the flow flux of the exit gas on the sweep side, and $S$ is the effective oxygen permeable area of the oxygen permeable membranes.


FIG. 1 shows X-ray diffraction patterns of the BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ powders with different praseodymium doping amount at room temperature. The main peaks were shifted to lower angles with the increasing of the substitution amount ($y$) in BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$, indicating that the lattice constant increases as doping more praseodymium into the B-site. Moreover, no crystalline phase of praseodymium oxide was detected from the XRD patterns, suggesting that the praseodymium were successfully doped into the oxide lattice of BaFeO$_{3-\delta}$. Table Ⅰ lists structural parameters of BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ powders at room temperature. It is shown that the crystal structure of the parent BaFeO$_{3-\delta}$ is hexagonal, which is consistent with other reports [26, 28]. When the substitution amount $y$=0.025, BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$ failed to stabilize the cubic structure but formed a triclinic phase together with the cubic phase [31]. In contrast, cubic structure forms at a substitution amount of $y$=0.05, 0.075, 0.1. The tolerance factor of the BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ materials decreases from 1.066 ($y$=0) to 1.045 ($y$=0.1) with the increase of the substitution amount ($y$). The results show that doping Pr$^{n+}$ is beneficial to stabilize the cubic perovskite structure of BaFeO$_{3-\delta}$ oxygen permeable membranes at room temperature.

FIG. 1 X-ray diffraction patterns of the BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ powders at room temperature.
Table Ⅰ Structural parameters of BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ powders at room temperature.

FIG. 2 shows point scanning analysis patterns of BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$ powders, only Ba, Fe, Pr, O were detected. Table Ⅱ lists the theoretical and trial percentage of elements of BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$ powders, respectively. The results show that the powders synthesized by the solid state reaction method have good composition stability.

FIG. 2 SEM photograph (left) and EDS spectrum (right) of the BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$ powders.
Table Ⅱ Atomic percentage of elements in BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$.

FIG. 3 shows SEM photographs of the surface and cross section of un-doped BaFeO$_{3-\delta}$, BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$ and BaFe$_{0.925}$Pr$_{0.075}$O$_{3-\delta}$ materials. The surface of all membranes are dense with clear grain boundaries, the cross section contains a small amount of closed pores. The compact structure ensures the purity of separated oxygen. The grain size of BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ increase monotonically with the increase of the praseodymium doping amount, the detail of grain size effects on the oxygen permeability has not been understood well. However, there are different opinions on whether the increase of grain size is beneficial to the improvement of oxygen permeability [32].

FIG. 3 SEM photographs of the surface (top) and cross section (bottom) of membranes. (a, d) BaFeO$_{3-\delta}$, (b, e) BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$, (c, f) BaFe$_{0.925}$Pr$_{0.075}$O$_{3-\delta}$.
B. Conductivity properties

FIG. 4 shows electrical conductivities of BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ bars at temperature intervals from 300 ℃ to 900 ℃. Below 750 ℃, the electrical conductivity of parent BaFeO$_{3-\delta}$ is low, and then increases sharply, implying that there probably exists a phase transition around the temperature. With a small amount of praseodymium doping ($y$=0.025), the temperature of obvious increase of the electrical conductivity for BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$ advances to 600 ℃. Due to the cubic structure that is beneficial to the carrier transmission forms with a larger praseodymium doping amount ($y$=0.05, 0.075, 0.1), the specimen bars also have high electrical conductivity at low temperature. Moreover, under all test temperature, the electrical conductivity increases with the increase of doping amount, and maximum electrical conductivity reaches 6.5 S/cm for BaFe$_{0.9}$Pr$_{0.1}$O$_{3-\delta}$ at 900 ℃. The electrical conductivity in the perovskite oxides is generally created by electron hopping along the B-site lattice cations and oxygen ion through strongly overlapping B$-$O$-$B bonds with a mechanism known as the Zerner double exchange:

$ \begin{array}{l} {{\rm{B}}^{n + }}-{{\rm{O}}^{2-}}-{{\rm{B}}^{(n + 1) + }} \to {{\rm{B}}^{(n + 1) + }} - {{\rm{O}}^ - } - {{\rm{B}}^{(n + 1) + }}\\ \;\;\;\;\;\;\;\;\;\;\;\;\;\;\;\;\;\;\;\;\;\;\;\;\;\; \to {{\rm{B}}^{(n + 1) + }} - {{\rm{O}}^{2 - }} - {{\rm{B}}^{n + }} \end{array} $
FIG. 4 Electrical conductivity of BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ between 300 and 900 ℃.

The stabilization of cubic lattice structure of BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ is strengthened with the increase of the praseodymium doping amount. The cubic perovskite phase can maximize the overlapping of the electron clouds between O$_2$ and Fe$^{m+}$ ions, thus facilitate the electron conduction [28]. Pr$^{n+}$ has a variable valence state, which lets it participate in the Zerner double exchange. It should be noted that, at temperature above 550 ℃, the electrical conductivity of the materials decreases with the increase of temperature. That may be ascribed that the BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ materials are p-type electronic conductors, and the conductivity increases with increasing temperature. However, more oxygen vacancies will be formed inside the materials at higher temperature, but the formation of an oxygen vacancy consumes 2 times electron hole, thus reducing the electrical conductivity [33].

C. Oxygen permeability

FIG. 5 shows oxygen permeation fluxes of the BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ materials as a function of temperature. With praseodymium doping in B-site, the oxygen permeation fluxes of all membranes were higher than that of the parent BaFeO$_{3-\delta}$, particularly at lower temperature around 600$-$750 ℃. In addition, the oxygen permeation fluxes increase with the increase of praseodymium doping amount, and the maximum oxygen permeation flux reaches 1.112 mL/(cm$^2\cdot$min) for BaFe$_{0.9}$Pr$_{0.1}$O$_{3-\delta}$ composition at 900 ℃, which is consistent with the increase of conductivity. However, at temperature below 650 ℃, the oxygen permeation flux of BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$ materials is low, and above 650 ℃, it increases sharply, implying there probably exists a phase transition around the temperature. To elucidate the reason for this, the crystal structure of BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$ membrane with the change of temperature was characterized by high temperature X-ray diffraction (HT-XRD).

FIG. 5 Oxygen permeation fluxes of BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ membranes.

FIG. 6 shows HT-XRD patterns of BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$ membrane at different temperature. The membrane is triclinic phase at 100 ℃, which is the same as that measured at room temperature. With the increase of temperature, the crystal structure of the membrane gradually changes into cubic phase, and completely transforms into a cubic phase above 700 ℃. This phase transformation explains the reason that the oxygen permeation flux of BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$ shows a sharp increase near 700 ℃.

FIG. 6 HT-XRD patterns of BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$ membrane.

BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ ($y$=0, 0.025, 0.05, 0.075, 0.1) powders were synthesized by a solid state reaction method. The BaFeO$_{3-\delta}$ and BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$ samples have hexagonal and triclinic crystal structure at room temperature, respectively, while others have cubic crystal structure, which proves that doping of praseodymium is beneficial to the stabilization of the cubic phase structure. The sintered BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ samples have dense microstructure and praseodymium doping promotes the grain growth. Electrical conductivity and oxygen permeation flux of BaFe$_{1-y}$Pr$_y$O$_{3-\delta}$ samples increase with the increase of the praseodymium doping amount, which reach 6.5 S/cm and 1.112 mL/(cm$^2\cdot$min) for BaFe$_{0.9}$Pr$_{0.1}$O$_{3-\delta}$ composition at 900 ℃, respectively. The test results of high temperature XRD show that the crystal structure of BaFe$_{0.975}$Pr$_{0.025}$O$_{3-\delta}$ gradually transforms from triclinic to cubic at temperature around 700 ℃, which results in a sharp increase in oxygen permeation flux of the materials near around this temperature.


This work was supported by the National Natural Science Foundation of China (No.216060647) and the Industry-University-Research Project of Aviation Industry Corporation of China (No.cxy2012HFGD025).

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魏邦争a,b, 王语a, 刘梦a, 徐晨曦a,b, 程继贵a,b     
a. 合肥工业大学材料科学与工程学院, 合肥 230009;
b. 安徽省先进功能材料与器件重点实验室, 合肥 230009
摘要: 本文尝试通过镨部分取代铁来改善无钴型钙钛矿材料BaFeO3-δ在室温下的结构稳定性,考察镨掺杂对材料导电及透氧性能的影响,获得新型的高性能无钴透氧膜材料.实验中通过固相反应法合成了BaFe3-yPryO3-δy=0、0.025、0.05、0.075、0.1)复合粉末,并由此制得烧结体样品.XRD测试结果表明,BaFe3-yPryO3-δ材料在镨掺杂量为(y=0.05、0.075、0.1)时仍然保持立方相,这表明掺杂Prn+有利于材料立方相结构的稳定.SEM观测表明,烧结样品中仅含有少量闭孔,说明Prn+的掺杂促进了烧结致密化.电导率和透氧率测试结果表明,900℃时,BaFe0.9Pr0.1O3-δ的电导率和透氧率分别为6.5 L/cm和1.112 mL/(cm2·min),镨掺杂可以改善BaFe1-yPryO3-δ材料的传导性能.高温XRD结果表明,BaFe0.975Pr0.025O3-δ的晶体结构在700℃完全转变为立方相.BaFeO3中Prn+对Fem+的部分取代可以稳定立方相结构,提高BaFe1-yPryO3-δ的导电性和透氧率.
关键词: BaFe1-yPryO3-δ     镨掺杂     立方钙钛矿     透氧率