- Nano Express
- Open Access
Water-Vapor Sorption Processes in Nanoporous MgO-Al2O3 Ceramics: the PAL Spectroscopy Study
© Klym et al. 2016
- Received: 30 November 2015
- Accepted: 1 March 2016
- Published: 9 March 2016
The water-vapor sorption processes in nanoporous MgO-Al2O3 ceramics are studied with positron annihilation lifetime (PAL) spectroscopy employing positron trapping and positronium (Ps)-decaying modes. It is demonstrated that the longest-lived components in the four-term reconstructed PAL spectra with characteristic lifetimes near 2 and 60–70 ns can be, respectively, attributed to ortho-positronium (o-Ps) traps in nanopores with 0.3- and 1.5–1.8-nm radii. The first o-Ps decaying process includes “pick-off” annihilation in the “bubbles” of liquid water, while the second is based on o-Ps interaction with physisorbed water molecules at the walls of the pores. In addition, the water vapor modifies structural defects located at the grain boundaries in a vicinity of pores, this process being accompanied by void fragmentation during water adsorption and agglomeration during water desorption after drying.
- Positron annihilation
- Water sorption
Functional MgAl2O4 ceramics (MgO-Al2O3) with a spinel structure are known as excellent porous materials for humidity sensors [1–3]. These ceramics are thermally and chemically stable in comparison with other types of porous media possessing fast response to humidity changes . An actual challenge is related to porous materials with a controllable microstructure, large specific surface area, high open porosity, optimal pore size, and distribution of free-volume entities [5, 6].
The effect of initial surface area of powdered binary oxide ingredients (MgO and Al2O3) on the structure of MgO-Al2O3 ceramics sintered at 1100–1400 °C was studied extensively in [7–10]. It was shown that the formation of this spinel-structured ceramics is substantially intensified with increase in sintering temperature and duration. In addition, the sintering temperature possessed an essential effect on the pore structure and exploitation properties of MgAl2O4 ceramics .
Traditionally, the microstructures of porous ceramics are studied using X-ray (electron, neutron) diffraction, electron microscopy, and different direct porosimetric methods [11–13]. However, the techniques of mercury and/or nitrogen intrusion porosimetry provide reliable information on open pores with radii over 2 nm , whereas physical processes in such ceramics depend on not only large open pores but closed nanopores too .
To gain knowledge about such fine free-volume entities and their effect on MgAl2O4 ceramics, it is reasonable to use the method of positron annihilation lifetime (PAL) spectroscopy, which is an alternative probe of structural characterization allowing the study of both closed and open pores at a nanoscale . Two channels of positron annihilation were shown to be important in case of ceramics: positron trapping and ortho-positronium (o-Ps) decaying [17–19]. The latter process (“pick-off” annihilation) resulting from positronium (Ps) interaction with electron from environment (including annihilation in liquid water) is ended by emission of two γ-quanta . In general, these two channels of positron annihilation are independent. However, if trapping sites will appear in a vicinity of grain boundaries neighboring with free-volume pores, these positron-Ps traps become mutually interconnected resulting in a significant complication of PAL data.
In this work, we use the PAL method developed in positron trapping and o-Ps-decaying modes to characterize MgO-Al2O3 ceramics sintered at 1100–1400 °C in different stages of water-vapor sorption and drying treatment.
The MgO-Al2O3 ceramics were sintered at maximal temperatures (T s) of 1100, 1200, 1300, and 1400 °C for 2 h, as it was described elsewhere [7, 9, 20, 21]. In respect to X-ray diffraction measurements , the ceramics prepared at lower T s = 1100–1200 °C are composed of the main spinel phase and a large amount of additional MgO and Al2O3 phases (up to 12 %), while the ceramics sintered at high T s of 1300 and 1400 °C contain additionally only the MgO phase in the amount of 3.5 and 1.5 %, respectively.
The PAL measurements were performed with the ORTEC instrument (using 22Na source placed between two identical sandwiched samples) [7, 22] at 22 °C and relative humidity RH = 35 % after drying, 7 days of water exposure (water vapor in a desiccator at RH = 100 %), and further final drying in a vacuum at 120 °C for 4 h. Each PAL spectrum was collected within a 6.15-ps channel width to analyze short and intermediate PAL components. To obtain data on longest-lived PAL components, the same ceramics were studied within a channel width of 61.5 ps . The collected spectra were analyzed with LT software . In previous works [8–10], we used three-component fitting procedures under normal statistical treatment of PAL spectra accumulated near one million of elementary positron annihilation events. At high-statistical measurements (more than ten million counts), the best results were obtained with a four-term decomposition procedure. Such approach allows us to study nanopores of different sizes, responsible for o-Ps decaying. Each PAL spectrum was processed multiply owing to slight changes in the number of final channels, annihilation background, and time shift of the 0th channel. In such a manner, we obtained fitting parameters (positron lifetimes τ 1, τ 2, τ 3, τ 4 and corresponding unity-normalized intensities I 1, I 2, I 3, I 4), which correspond to annihilation of positrons in the samples of interest within a quite reliable error bar.
As it was shown earlier [7–10], the positron annihilation in humidity-sensitive MgO-Al2O3 ceramics is revealed through two different channels related to “free” positron trapping (the intermediate component with lifetime τ 2) and o-Ps decaying (two long-lived components with τ 3 and τ 4 lifetimes). The first component with parameters τ 1 and I 1 reflects mainly microstructure specificity of spinel ceramics with character octahedral and tetrahedral vacant cation sites along with input from annihilation of para-Ps atoms. The intermediate lifetime τ 2 is related to the size of free-volume defects near grain boundaries, and I 2 intensity reflects their amount . The third and fourth components (τ 3, I 3) and (τ 4, I 4), respectively, originate from annihilation of o-Ps atoms in intrinsic nanopores of MgO-Al2O3 ceramics [7, 24].
Fitting parameters describing PAL spectra of MgO-Al2O3 ceramics sintered at different T s temperatures reconstructed from a four-term decomposition procedure
τ 1 (±0.002), ns
I 1 (±1), %
τ 2 (±0.005), ns
I 2 (±1), %
τ 3 (±0.002), ns
I 3 (±0.2), %
τ 4 (±0.02), ns
I 4 (±0.1), %
T s = 1100 °C
T s = 1200 °C
T s = 1300 °C
T s = 1400 °C
Positron trapping modes and free-volume nanopore parameters related to o-Ps decaying determined from four-term decomposed PAL spectra of MgO-Al2O3 ceramics sintered at different T s temperatures
Positron trapping modes
τ av, ns
τ b, ns
κ d, ns−1
R 3, nm
~f 3, %
R 4, nm
~f 4, %
T s = 1100 °C
T s = 1200 °C
T s = 1300 °C
T s = 1400 °C
Preferential decreasing of the lifetime τ 2 in water-vapored MgO-Al2O3 ceramics and increasing of their intensity I 2 demonstrates intensification of positron trapping in defects near grain boundaries filled with water. After final drying, the intensities I 2 practically completely return to the initial values (character for initially dried samples), whereas τ 2 lifetimes are larger in ceramics sintered at 1300 and 1400 °C. Thus, the water adsorption processes in MgO-Al2O3 ceramics are accompanied by fragmentation of positron trapping sites near grain boundaries, and, respectively, the water desorption processes are accompanied by agglomeration of free-volume voids.
Water-vapor sorption processes in the studied ceramics result in essential evolution of the third and fourth o-Ps-related components. The intensity I 3 increases in all initially dried samples after water-vapor exposure, thus confirming o-Ps annihilation in water-filled nanopores through a “bubble” mechanism (with corresponding o-Ps lifetime close to 1.8 ns) [27–29]. At the same time, the lifetime τ 3 decreases in more defective ceramics sintered at 1100 and 1200 °C but increases in more perfect ceramics sintered at 1300 and 1400 °C. After final drying, the intensity I 3 for ceramics sintered at 1100 and 1200 °C is not returned to initial values. This confirms the remainder of sorbed water in the nanopores with size near 0.3 nm and slight desorption ability of these MgO-Al2O3 ceramics samples (Fig. 3). In MgO-Al2O3 ceramics sintered at 1300 and 1400 °C, the intensity of the third component returns to initial value, confirming high efficiency of water adsorption-desorption processes.
Another mechanism of water-vapor sorption processes similar to one reported in  is realized in the studied MgO-Al2O3 ceramics through the fourth component of the PAL spectra. Unlike the third component, the intensity I 4 decreases in water-vapor exposure ceramics samples. Since this intensity does not drop to zero being within 0.4–0.9 % domain, it should be assumed that there exists a fraction of closed nanopores where o-Ps are trapped . After final drying (in a vacuum at 120 °C for 4 h) of the ceramics samples previously exposed to water vapor, the initial pore size tends to be restored (Table 2 and Fig. 3). However, it does not recover entirely, suggesting that some fraction of water molecules remain adsorbed. The intensity I 4 does not return to initial value in ceramics sintered at 1100 and 1200 °C with poorly developed open porosity (Table 1). Most probably, physically adsorbed water is not fully eliminated at 120 °C in these ceramics samples. The decreased τ 4 value for ceramics dried after water-vapor exposure can be connected with formation of thin layers of water molecules covering the walls of pores with radii of 1.5–1.8 nm, which are not completely removed after vacuum annealing at 120 °C for 4 h.
The method of PAL spectroscopy in high-measurement statistics is employed to study water-vapor sorption processes in MgO-Al2O3 ceramics sintered at 1100–1400 °C temperatures for 2 h. It is shown that positrons are trapped more strongly in the ceramics obtained at lower T s, which was reflected in the second component of the four-term decomposed PAL spectra. The third and fourth longest-lived components in these spectra are due to annihilation of o-Ps atoms in the nanopores, the corresponding radii being calculated from τ 3 and τ 4 lifetimes using the known Tao-Eldrup model. The final drying in a vacuum at 120 °C for ceramics previously exposed to water vapor does not restore initial pore size, confirming sensitivity of PAL method to the amount of water molecules adsorbed in the nanopores. The Ps annihilation in nanopores with adsorbed water vapor is shown to occur via two mechanisms: (1) o-Ps decaying in nanopores with radius of 0.3 nm including “pick-off” annihilation in the “bubbles” of liquid water and (2) o-Ps trapping in free volume of nanopores (1.5–1.8 nm) with physisorbed water molecules at the pore walls. The water vapor modifies defects in ceramics located near grain boundaries, this process accompanied by void fragmentation at water adsorption with further void agglomeration at water desorption after drying.
H. Klym thanks the Lviv Polytechnic University under Doctoral Program and support via Project DB/KIBER (No 0115U000446).
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- Kulwicki BM (1991) Humidity sensors. J Am Ceram Soc 74(4):697–708View ArticleGoogle Scholar
- Gusmano G, Montesperelli G, Traversa E, Bearzotti A, Petrocco G, D’amico A, Di Natale C (1992) Magnesium aluminium spinel as humidity sensor. Sensors Actuators B Chem 7:460–463View ArticleGoogle Scholar
- Traversa E (1995) Ceramic sensors for humidity detection: the state-of-the-art and future developments. Sensors Actuators B Chem 23(2):135–156View ArticleGoogle Scholar
- Gusmano G, Montesperelli G, Traversa E, Mattogno G (1993) Microstructure and electrical properties of MgAl2O4 thin films for humidity sensing. J Am Ceram Soc 76(3):743–750View ArticleGoogle Scholar
- Kashi MA, Ramazani A, Abbasian H, Khayyatian A (2012) Capacitive humidity sensors based on large diameter porous alumina prepared by high current anodization. Sensors Actuators A 174:69–74View ArticleGoogle Scholar
- Armatas GS, Salmas CE, Louloudi MG, Androutsopoulos P, Pomonis PJ (2003) Relationships among pore size, connectivity, dimensionality of capillary condensation, and pore structure tortuosity of functionalized mesoporous silica. Langmuir 19:3128–3136View ArticleGoogle Scholar
- Klym H, Ingram A, Hadzaman I, Shpotyuk O (2014) Evolution of porous structure and free-volume entities in magnesium aluminate spinel ceramics. Ceram Int 40(6):8561–8567View ArticleGoogle Scholar
- Klym H, Ingram A, Shpotyuk O, Filipecki J, Hadzaman I (2011) Structural studies of spinel manganite ceramics with positron annihilation lifetime spectroscopy. J Phys Conf Ser 289(1):012010View ArticleGoogle Scholar
- Filipecki J, Ingram A, Klym H, Shpotyuk O, Vakiv M (2007) Water-sensitive positron trapping modes in nanoporous magnesium aluminate ceramics. J Phys Conf Ser 79(1):012015View ArticleGoogle Scholar
- Klym H, Ingram A (2007) Unified model of multichannel positron annihilation in nanoporous magnesium aluminate ceramics. J Phys Conf Ser 79(1):012014View ArticleGoogle Scholar
- Karbovnyk I, Lesivtsiv V, Bolesta I, Velgosh S, Rovetsky I, Pankratov V, Balasubramanian C, Popov AI (2013) BiI3 nanoclusters in melt-grown CdI2 crystals studied by optical absorption spectroscopy. Phys B Condens Matter 413:12–14View ArticleGoogle Scholar
- Karbovnyk I, Bolesta I, Rovetski I, Velgosh S, Klym H (2014) Studies of CdI2–Bi3 microstructures with optical methods, atomic force microscopy and positron annihilation spectroscopy. Mater Sci Pol 32(3):391–395View ArticleGoogle Scholar
- Bondarchuk A, Shpotyuk O, Glot A, Klym H (2012) Current saturation in In2O3-SrO ceramics: a role of oxidizing atmosphere. Rev Mex Fis 58:313–316Google Scholar
- Hajnos M, Lipiec J, Świeboda R, Sokołowska Z, Witkowska-Walczak B (2006) Complete characterization of pore size distribution of tilled and orchard soil using water retention curve, mercury porosimetry, nitrogen adsorption, and water desorption methods. Geoderma 135:307–314View ArticleGoogle Scholar
- Golovchak R, Wang S, Jain H, Ingram A (2012) Positron annihilation lifetime spectroscopy of nano/macroporous bioactive glasses. J Mater Res 27(19):2561–2567View ArticleGoogle Scholar
- Kobayashi Y, Ito K, Oka T, Hirata K (2007) Positronium chemistry in porous materials. Radiat Phys Chem 76:224–230View ArticleGoogle Scholar
- Krause-Rehberg R, Leipner HS (1999) Positron annihilation in semiconductors. Defect studies. Springer, Berlin-Heidelberg-New YorkView ArticleGoogle Scholar
- Jean YC, Mallon PE, Schrader DM (2003) Principles and application of positron and positronium chemistry. Word Scientific, SingaporeView ArticleGoogle Scholar
- Mogensen OE (1995) Positron annihilation in chemistry. Springer, BerlinView ArticleGoogle Scholar
- Klym H, Hadzaman I, Shpotyuk O, Fu Q, Luo W, Deng J (2013) Integrated thick-film p-i-p+ structures based on spinel ceramics. Solid State Phenom 200:156–161View ArticleGoogle Scholar
- Hadzaman I, Klym H, Shpotyuk O, Brunner M (2010) Temperature sensitive spinel-type ceramics in thick-film multilayer performance for environment sensors. Acta Phys Pol - Ser A Gen Phys 117(1):234–237View ArticleGoogle Scholar
- Klym H, Ingram A, Shpotyuk O, Calvez L, Petracovschi E, Kulyk B, Serkiz R, Szatanik R (2015) ‘Cold’ crystallization in nanostructurized 80GeSe2-20Ga2Se3 glass. Nanoscale Res Lett 10:49View ArticleGoogle Scholar
- Kansy J (1996) Microcomputer program for analysis of positron annihilation lifetime spectra. Nucl Inst Methods Phys Res A 374:235–244View ArticleGoogle Scholar
- Nambissan PMG, Upadhyay C, Verma HC (2003) Positron lifetime spectroscopic studies of nanocrystalline ZnFe2O4. J Appl Phys 93:6320View ArticleGoogle Scholar
- Tao SJ (1972) Positronium annihilation in molecular substance. J Chem Phys 56(11):5499–5510View ArticleGoogle Scholar
- Eldrup M, Lightbody D, Sherwood JN (1981) The temperature dependence of positron lifetimes in solid pivalic acid. Chem Phys 63:51–58View ArticleGoogle Scholar
- Leifer I, Patro RK (2002) The bubble mechanism for methane transport from the shallow sea bed to the surface: a review and sensitivity study. Cont Shelf Res 22(16):2409–2428View ArticleGoogle Scholar
- Ljunggren S, Eriksson JC (1997) The lifetime of a colloid-sized gas bubble in water and the cause of the hydrophobic attraction. Colloids Surf A Physicochem Eng Asp 129:151–155View ArticleGoogle Scholar
- Grosman A, Ortega C (2005) Nature of capillary condensation and evaporation processes in ordered porous materials. Langmuir 21:10515–10521View ArticleGoogle Scholar
- Dlubek G, Yang Y, Krause-Rehberg R, Beichel W, Bulut S, Pogodina N, Krossing I, Friedrich C (2010) Free volume in imidazolium triflimide ([C3MIM][NTf2]) ionic liquid from positron lifetime: amorphous, crystalline, and liquid states. J Chem Phys 133:124502View ArticleGoogle Scholar