Title Author Keyword ::: Volume ::: Vol. 48Vol. 47Vol. 46Vol. 45Vol. 44Vol. 43Vol. 42 ::: Issue ::: No. 4No. 3No. 2No. 1

Evaluation of Kinetic Parameters and Thermal Stability of Melt-Quenched BixSe100−x Alloys (x ≤7.5 at%) by Non-Isothermal Thermogravimetric Analysis

Leibniz Institut für Analytische Wissenschaften–ISAS e.V., Dortmund 44139, Germany, 1Department of Physics, Faculty of Science, The University of Jordan, Amman 11942, Jordan, 2Department of Physics and Basic Sciences, Faculty of Engineering Technology, Al-Balqa Applied University, Amman 11134, Jordan, 3Physics Department, King Fahd University of Petroleum and Minerals, Dhahran 31261, Saudi Arabia
Correspondence to: Jafar MMA-G, Tel: +00962-6-5355000-22042, Fax: +00962-6-5300253, E-mail: mousa_jafar_2030@yahoo.com
Received June 7, 2017; Revised September 1, 2017; Accepted September 1, 2017.
This is an open-access article distributed under the terms of the Creative Commons Attribution Non-Commercial License (http://creativecommons.org/licenses/by-nc/4.0) which permits unrestricted noncommercial use, distribution, and reproduction in any medium, provided the original work is properly cited.
Abstract

Non-isothermal thermogravimetry (TG) measurements on melt-quenched BixSe100x specimens (x=0, 2.5, 7.5 at%) were made at a heating rate β=10°C/min in the range T=35°C~950°C. The as-measured TG curves confirm that BixSe100x samples were thermally stable with minor loss at T?400°C and mass loss starts to decrease up to 600°C, beyond which trivial mass loss was observed. These TG curves were used to estimate molar (Se/Bi)-ratios of BixSe100x samples, which were not in accordance with initial composition. Shaping features of conversion curves α(T)−T of BixSe100−x samples combined with a reliable flow chart were used to reduce kinetic mechanisms that would have caused their thermal mass loss to few nth-order reaction models of the form f[α(T)] [1−α(T)]n (n=1/2, 2/3, and 1). The constructed α(T)−T and (dα(T)/dT)−T curves were analyzed using Coats-Redfern (CR) and Achar-Brindley-Sharp (ABS) kinetic formulas on basis of these model functions, but the linearity of attained plots were good in a limited α(T)−region. The applicability of CR and ABS methods, with model function of kinetic reaction mechanism R0 (n=0), was notable as they gave best linear fits over much broader α(T)-range.

Keywords : Non-isothermal kinetics, Thermogravimetric analysis, Coats-Redfern kinetic model, Achar-Brindley-Sharp kinetic model, Bismuth-selenium alloys
RESULTS

Fig. 1 depicts the temperature dependence of as-measured non-isothermal TG and DTG data scanned at β=10°C/min in the range 35°C~950°C, plotted as Δm% and dΔm%/d[t(min)] against the sample’s temperature T(°C) for the powder samples of melt-quenched BixSe100−x alloys having x=0, 2.5, and 7.5 at%. Several motivating features can be inferred from these measured TG/DTG curves. No sizeable loss of mass of studied BixSe100−x samples with no signs of desorption (drying), mass gain and/or of thermomolecular flow (convection), can be inferred from their as-measured TG curves at temperatures less than T~ 400°C, below which these BixSe100−x alloys are thermally stable. These features signify that their initial powders were free of water and the nitrogen gas flowing in the chamber of the TG instrument was moisture-free (dry), with no substantial traces of oxidizing gas impurities. The onset (initial) temperature Ti of the mass loss shifts slightly with initial sample’s mass that might be related to delay in its thermal decomposition due to temperature gradients across the powder pressed in the pan. At T>400°C, the mass loss starts to decline gradually and then sharply over the temperature window 400°C~600°C, where the DTG curve is seen to slowly ascend till a maximum before it sharply returns to the zero base line.

As T is increased beyond 600°C the mass loss is feeble up to 950°C, with residual mass of BixSe100−x powder may be related to Bi-content used in preparing their melt-quenched BixSe100−x alloys (Ahmad, 2016). This suggests that the observed loss of sample’s mass upon thermal heating up to T~600°C may be due to sample’s decomposition to its individual elements. This TG/DTG behavior can be realized in view of melting and boiling points of Se (Tmelt≈220°C and Tboil≈685°C) and of bismuth (Tmelt≈271°C and Tboil≈1,564°C) at normal atmospheric pressure. Selenium is more volatile than bismuth and has much higher vapor pressure at temperatures above 300°C, so the drastic decline seen in the studied BixSe100−x samples with rising temperature up to 600°C can be assigned to Se-vaporization from alloy. In the temperature range 650°C~720°C, Fig. 1 shows a slender shoulder/peak on the TG/DTG curves of some of the BixSe100−x powder samples studied (Ahmad, 2016). The origin of existence of such meager shoulder on measured TG/DTG curves is not fully understood.

Presuming that the thermally-heated BixSe100−x powder samples actually suffered from decomposition (breaking apart) into their individual Se- and Bi-components via a certain kinetic reaction mechanism upon increasing the sample’s temperature T, one may be able to estimate the chemical composition (stoichiometry) of their as-prepared melt-quenching BixSe100−x alloys from their as-measured Δm%−T(°C) curves. Suppose that the measured percentage of mass loss Δm% of a particular BixSe100−x powder sample down to its shoulder portion at the high-temperature side is totally related to (Δm%)Se and the remainder percentage mass loss is mainly due to the (Δm%)Bi amount. Based on such hypothesis, the stoichiometric (molar) ratios of selenium (MSe=78.96 g/mol) to bismuth (MBi=208.98 g/mol) estimated from the TG curves of studied BixSe100−x powder samples were not comparable to those initially used in the preparation of their original melt-quenched BixSe100−x alloys, like, for instant, the Bi2.5Se97.5 sample. Also, their TG-estimated compositions (Table 1) are not in accord with stoichiometric ratios calculated from spectra acquired by X-ray energy dispersive spectroscopy technique (Ahmad, 2016).

The discrepancy between the (Se-Bi)-ratios estimated from measured TG curves of BixSe100−x samples and those initially mixed to prepare their original melt-quenched BixSe100−x alloys may be partly ascribed to inhomogeneities in melt-quenched ingots, so the small amounts of powders taken form these ingots for TG characterization might not be well representative of their composition. One had to make TG measurements on powder samples from different parts of ingots, a procedure that we have not carried out in this work; however, this inconsistency might be resolved by the use of accurate analytical spectroscopic techniques such as the X-ray photoelectron spectroscopy (van der Heide, 2012) and X-ray fluorescence spectrometry (Jenkins, 1999), which requires sizable amounts of powder to proceed with composition analysis.

DISCUSSION

Using Ti, Tf, S=(TmT1)/(T2Tm),$Δ1/2exp=(T2-T1)$ and $αmexp=α(Tm)$ and designating features of measured TG/DTG curves of a heated sample, the favored kinetic reaction mechanism responsible for its thermal decomposition can then be identified and discriminated with the help of a flow chart (shape method) that signifies the type and range of these parameters for different kinetic models (Dollimore et al., 1992a, 1992b; Gao et al., 1993; Haixiang et al., 2010; Lee & Dollimore, 1998). Indicative values of these parameters that give a glue on the nature of thermal decomposition of melt-quenching BixSe100−x alloys of the present work were determined by closely visual inspection of the α (T)− T in the range 0≤α(T)≤1 and (dα(T)/dT)−T of the curves, constructed, using Eqs. 1 and 2, from their measured non-isothermal TG/DTG curves for β=10°C and depicted in Fig. 2. These conversion curves show that initial temperature Ti at which sample’s decomposition begins is “diffuse” and final temperature Tf after which decomposition ends is “sharp”. Table 2 lists Tm, $αmexp$, T1, T2, $Δ1/2exp$ and S, whose values could help to identify favored kinetic reaction mechanisms giving rise to observed thermal decomposition of such alloys. As shape factor S>1 and DTG curve is asymmetric for the BixSe100−x alloys, we can disregard some kinetic mechanisms on basis of flow charts and shape methods (Haixiang et al., 2010).

Other irrelevant kinetic reaction models might be further separated and discarded by making use of experimentally-deduced values of the TG/DTG shape parameters $Δ1/2exp$ and $αmexp$ and of a reliable flow chart, which is generally based on theoretical values of shape parameters that characterize certain kinetic reaction mechanisms whose kinetic parameters Eα and A span a fairly wide range: (50≤Eα≤350 kJ/mol) and 105A≤1018s−1 (Haixiang et al., 2010). In a full kinetic analysis of TG/DTG data, this procedure of model discrimination can be assisted by the application of a non-linear conventional curve-fitting of the α(T)−T and (dα(T)/dT)−T data to the numerous kinetic reaction models to search for the model that would describe the observed thermal decomposition of the sample (Haixiang et al., 2010); however, this is an ad-hoc and unwieldy procedure that only yields reliable and physically-meaning results when a global (not local) minimum solution of the problem is reached. Yet, fairly accurate values of the shape parameters featuring the TG/DTG curves of a melt-quenching BixSe100−x alloy often aid one to choose the kinetic model(s) that would actually describe its thermal stability and decomposition upon heating, so rendering an all-inclusive analysis of experimental thermoanalytical data more pragmatic, handy and timesaving.

In view of theoretical shape parameters and flow chart of Haixiang et al. (2010) and of estimated parameters (Table 2), which clarify graphical features of α(T)−T and (dα(T)/dT)− T curves of BixSe100−x alloys of present work, only few kinetic reaction mechanisms would embody these conversion curves and the behavior of their measured TG/DTG curves. These include the mechanism R2, described by the model function f[α(T)]=2[1−α (T)]1/2 and parameters ($αmtheor=0.71-0.77$; Δ1/2=14.5−72.7) and the mechanism R3, described by the model function f[α(T)]=3[1−α (T)]2/3 and parameters (Tid, Tfs; $αmtheor=0.58~0.70$; Δ1/2=16.2~80.3). The first-order (n=1) reaction mechanism (F1), described by the model function f[α(T)]=[1−α(T)]1/2 and parameters (Tid, Tfd; $αmtheor=0.58~0.70$) can be discarded on the basis of asymmetry (shape) factor S>1, as was found for our BixSe100−x alloys. The zero-order (n=0) reaction mechanism (R0), described by the model function f[α(T)]=1 was not treated by Shape methods and is not included in the scheme of the currently-used flow charts (Gao et al., 1993; Haixiang et al., 2010; Lee & Dollimore, 1998) and no theoretical shape parameters for the R0 mechanism are yet available, though its model function was used to analyze experimental data of thermally-induced decomposition of some materials (Marini et al., 1979).

To distinguish between above-stated kinetic reaction mechanisms, and identify which one is suitable for describing thermal decomposition of studied BixSe100−x alloys, we shall perform curve-fitting of their α(T)−T and (dα(T)/dT)− T data to model-based differential-form ABS and integralform CR methods on using the nth-order model functions. Quantitative analysis of the α(T)−T(K) and (dα(T)/dT)−T data of BixSe100−x powder samples were also made for kinetic reaction mechanism F1, whose theoretically shape factor is 1 (Haixiang et al., 2010), though it can be discarded by S>1 determined for these samples.

### Quantitative Analysis of Experimental TG/DTG Data

Quantitative analysis of the α(T)−T(K) and (dα(T)/dT)−T(K), constructed from TG/DTG curves of the melt-quenching BixSe100−x samples (x=0, 2.5, and 7.5 at%) obtained for β=10°C/min has been performed on the basis of the model-based differential-form ABS (Eq. (3)) and integral-form CR formulas (Eq. (4)). This analysis was implemented by making use of the nth-order function f[α(T)] [1−α (T)]n and its function g[α(T)] given in Eq. (5), which model the kinetic reaction mechanisms R0 (n=0), R2 (n=1/2), R3 (n=2/3) and F1 (n=1). In TG terminology, the reaction conversion factor α (T) is the fraction of sample decomposed at the temperature T (fractional decomposition), calculated for a specific range, where a kinetic reaction mechanism is operative. Fig. 3 depict the calculated data α(T)−T(K) of our Bi0Se100, Bi2.5Se97.5 and Bi7.5Se92.5 powder samples as plots of ln{g[α(T)]/[T(K)]2}-Vs-[1,000/T(K)] on the basis of the CR-formula expressed in Eq. (3), using the functions g[α (T)] for the model functions f0[α(T)]=1, f1/2[α(T)]=2[1−α(T)]1/2, f2/3[α(T)]=3[1−α(T)]2/3, and f1[α(T)]=[1−α(T)] describing the R0, R2, R3 and F1 kinetic reaction mechanisms, respectively. These plots show that the application of CR method to analyze the non-isothermal α(T)−T(K) data of the studied BixSe100−x samples gives curvilinear trends for the R2-, R3- and F1- model functions over a good part of the α(T)-values of the decomposition process. Yet, analysis of same α(T)−T(K) data on basis of model-based integral-form CR formulation and model function of kinetic reaction mechanism R0 (n=0), for which g[α(T)]=α(T), yields wider linear portions on plots of Fig. 3 with the best linear fits over a quite broad α(T)-range. Table 3 lists the values of activation energy Eα and frequency factor A determined from attained linear fits on Fig. 3.

The R0 kinetic reaction mechanism appears to correspond to a linear variation of α(t) with the time t in the isothermal mode (Marini et al., 1979) and seems to account for the observed thermal decomposition of our BixSe100−x powder samples over fairly wide range of α(T)-values. The curvilinear trend seen on the ln{g[α(T)]/[T(K)]2}-Vs-[1,000/T(K)] plots fitted to the CR formula can be attributed to setting T0, the lower temperature limit of the integral of Eq. (4) to zero, an assumption that is not always adequate. To remove the non-linearity of the plots attained on the basis of the model-based integral form CR kinetic analysis method, T0 should be chosen to be a non-zero finite temperature at which the process of thermal decomposition of a heated sample actually starts (Marini et al., 1979). This amendment and its consequence implications on the analysis of as-measured TG curves of BixSe100−x powder samples will be conducted in a forthcoming article, as a preliminary analysis of the α(T)− T curves on the basis of the modified formulations of RC formula gave remarkable non-linear curve-fits over much broader α(T)-range.

On the other hand, the calculated (dα (T)/dT)−T(K) data of the studied BixSe100−x powder samples were analyzed on the basis of the linear formulation of the model-based differential-form ABS method exemplified in Eq. (3), along with the model function f[α(T)]=γ[1−α(T)]n describing the kinetic reaction mechanisms R0 (n=0; γ=1), R2 (n=1/2; γ=2), R3 (n=2/3; γ=3) and F1 (n=1; γ=1). Fig. 4 depict the resulting representation depicted as plots of ln{[dα(T)/dT]/f[α(T)]}-Vs-[1,000/T(K)] for the respective n values, which exhibit narrow linear portions over a limited range of α(T)-values; however, the much longer linear portion and the best linear fit are noted to be assigned with the kinetic reaction mechanism R0 (n=0) for values of α(T) covering a rather wide range of α(T) (0.02<α(T)<0.8). The values of the activation energy Eα and frequency factor A determined from linear fits on Fig. 4 are also listed in Table 3.

CONCLUSIONS

Detailed non-isothermal TG measurements on small masses (~13 mg) of several melt-quenched BixSe100−x powder samples (x=0, 2.5, and 7.5 at%) were taken at a constant heating rate β=10°C/min in the temperature range 35°C~950°C. The as-measured TG curves illustrate good thermal stability of samples with no loss of their initially-used masses at temperatures less than T≈400°C, above which mass loss starts to greatly decrease up to 600°C. Between 600°C and 950°C, trivial mass loss is observed and the residual mass left behind is related to the Bi-content in the used powder sample. Presuming that a melt-quenching BixSe100−x sample decomposes into its ingredients, the as-measured TG curves were used to estimate its molar (Se/Bi)-ratio; however, these calculations were not in accord with the molar ratios of bismuth and selenium powders mixed together in the preparation of their original BixSe100−x alloys.

The graphical features of the shape of conversion curves of BixSe100−x samples, combined with a flow chart help to reduce the many kinetic reaction mechanisms causing their thermal decomposition to few ones, namely the R2, R3 and F1 kinetic reaction mechanisms, described by the nth-order model function f[α(T)] [1-α (T)]n (n=1/2, 2/3, and 1). To discriminate between these models and elucidate which one is suitable to account for decomposition of BixSe100−x samples, the α(T)−T and (dα(T)/dT)−T data were analyzed by the model-based integral CR and differential ABS kinetic formulas, combined with these model functions, but linearity of plots were only achieved in a limited range of α(T)-values. Yet, it was found that analyzing such conversion curves by the CR and ABS methods using the model function of kinetic reaction mechanism R0 (n=0) (Marini et al., 1979) gave remarkable linear fits over much broader α(T)-range.

Figures
 Fig. 1. The as-measured thermogravimetry (TG) curves and calculated differential thermogravimetric (DTG) curves in the temperature range 35°C~950°C for the melt-quenching BixSe100−x alloys having various Bi-compositions.
 Fig. 2. The α (T)−T(°C) and (dα (T)/dT)−T(°C) curves for the studied melt-quenching BixSe100−x alloys constructed from their experimental thermogravimetry (TG) and differential thermogravimetric (DTG) curves of using and . The inset shows the procedure for selecting some of kinetic model functions responsible for thermal decomposition in the studied samples.
 Fig. 3. The α (T)−T(K) data calculated from the non-isothermal TG data measured at β=10 K/min for the three powder samples Bi0Se100, Bi2.5Se97.5 and Bi7.5Se92.5 (A) n=0, (B) n=1/2, (C) n=2/3, and (D) n=1. This data is plotted on basis of CR method and nth-order model function f [α(T)]=γ[1−α(T)]n as ln{g[α(T)]/[T(K)]2}-Vs-1,000/T(K). The function g[α(T)]{=−ln[1−α(T)]} and g[α(T)]=[1−[1−α(T)]1−n]/(1−n). Solid lines are linear regression fits to linear portions, and dashed curves are guides-to-eye.
 Fig. 4. The (dα(T)/dT)−T(K) data calculated from non-isothermal thermogravimetry (TG) data measured at β=10 K/min for the samples Bi0Se100, Bi2.5Se97.5 and Bi7.5Se92.5. (A) n=0, (B) n=1/2, (C) n=2/3, and (D) n=1. The data is plotted on basis of ABS method and the nth-order model function f[α(T)]=γ[1−α(T)]n as ln{[dα(T)/dT]/f [α(T)]}-Vs-1,000/T(K). The function g[α(T)]=−ln[1−α(T)] and g[α(T)]=[1−[1−α(T)]1−n]/[(1−n)]. Dotted lines are linear regression fits to linear portions, and solid curves are guides-to-eye.
Tables

Atomic (Se/Bi)-ratios for the BixSe100−x samples of various Bi-contents obtained from their as-measured thermogravimetry (TG) curves, compared to those initially used to prepare their original melt-quenching BixSe100−x alloys (Ahmad, 2016)

BixSe100−x sample Atomic (Se/Bi)-ratio

TG-estimated Mixed in original alloy
Bi0Se100 100 100
Bi2.5Se97.5 23.5 39
Bi7.5Se92.5 12.4 12.3
Bi10Se90 9 6.6
Bi20Se80 4 6

Parameters related to characteristic features and asymmetry of α(T)−T(°C) and (dα(T)/dT)−T(°C) curves for melt-quenched BixSe100−x alloys for β=10°C/min

BixSe100−x sample Ti (°C) Tf (°C) Tm (°C) T1 (°C) T2 (°C) $Δ1/2exp$ (°C) S $αmexp$
Bi0Se100 Diffuse Sharp 538 498 541 43 13.3 0.925
Bi2.5Se97.5 Diffuse Sharp 501 492 509 17 1.13 0.777
Bi7.5Se92.5 Diffuse Sharp 499 461 511 50 3.17 0.662

The meanings of these parameters are given in the text.

Parameters of Kinetic reaction mechanisms for functions f [α(T)]=γ[1−α(T)] (n=0, 1/2, 2/3, 1), deduced from best fits of α(T)-T and dα(T)/dt-T conversion curves of studied BixSe100x samples to the ABS and CR kinetic formulas. Best curve fits of the data of undoped selenium sample to ABS formula were made for 0.02<α(T)<0.45

Analysis method Sample Reaction order

Eα (kJ/mol) A (min−1) Eα (kJ/mol) A (min−1) Eα (kJ/mol) A (min−1) Eα (kJ/mol) A (min−1)

n=0 n=1/2 n=2/3 n=1
CR Bi0Se100 97.9 3.5×105 104.6 6.0×105 106.6 5.9×105 107.6 2.2×106
Bi2.5Se97.5 102.2 1.3×106 117.1 9.3×106 121.0 1.3×107 124.2 7.0×107
Bi7.5Se92.5 103.6 1.8×106 110.3 3.3×106 112.3 3.2×106 113.8 1.3×107
ABS Bi0Se100 96.0 3.3×109 100.5 4.0×109 103.2 4.5×109 108.2 3.6×1010
Bi2.5Se97.5 99.7 1.1×1010 108.1 2.9×1010 110.0 2.7×1010 114.1 1.9×1011
Bi7.5Se92.5 97.3 8.1×109 100.7 8.1×109 100.9 5.6×109 103.5 2.9×1010

References
1. Abdel-Rahim, MM, El-Korashy, A, Hafiz, MM, and Mahmoud, AZ (2008). Kinetic study of non-isothermal crystallization of BixSe100x chalcogenide glasses. Physica B. 403, 2956-2962.
2. Abu El-Oyoun, M (2000). Crystallization kinetics of the chalcogenide Bi10Se90 glass. J Phys Chem Sol. 61, 1653-1662.
3. Achar, BNN, Brindley, GW, and Sharp, JH (1966). Kinetics and mechanism of dehydroxylation processes; III, Applications and limitations of dynamic method. Proceedings of International Clay Conference, Jerusalem. 1, 67-73.
4. Ahmad, MJA 2016. Study of structural and optical properties of bismuthdoped selenium films prepared by flash-evaporation method. MSc thesis. The University of Jordan. Jordan.
5. Atmani, H (1988). Glass transition study of BixSe1x materials. Mater Chem Phys. 19, 235-242.
6. Atmani, H (1992). Some aspects of the behavior of Bi in a matrix of Se. Mater Lett. 13, 21-26.
7. Atmani, H, Coquerel, G, and Vautier, C (1989). Crystallization and melting of thin BixSe1x layers. Thin Solid Films. 177, 239-244.
8. Atmani, H, and Vautier, C (1989). Bismuth effects on crystallization of amorphous selenium. Mater Chem Phys. 23, 541-550.
9. Bettsteller, R, Witte, H, Herms, W, and Freistedt, H (1993). Influence of Bismuth Incorporation on the Optical properties of a-Se Films. Solid State Commun. 87, 763-765.
10. Brown, ME (2004). Introduction to Thermal Analysis: Techniques and Applications. London: Kluwer Publishers
11. Chen, Y, Liu, Y, Chu, M, and Wang, (2014). Phase diagrams and thermodynamic descriptions for the Bi-Se and Zn-Se binary systems. J Alloys Comp. 617, 423-428.
12. Coat, AW, and Redfern, JP (1964). Kinetic parameters from thermogravimetric data. Nature. 201, 68-69.
13. Criado, JM, Málek, J, and Ortega, A (1989). Applicability of the Master plots in kinetic analysis of non-isothermal data. Thermochimica Acta. 147, 377-385.
14. Dollimore, D, Evans, T, Lee, Y, Pee, G, and Wilburn, F (1992a). The significance of the onset and final temperatures in the kinetic analysis of TG curves. Thermochimica Acta. 196, 255-265.
15. Dollimore, D, Evans, TA, Lee, YF, and Wilburn, FW (1992b). Correlation between the shape of a TG/DTG curve and the form of the kinetic mechanism which is applying. Thermochimica Acta. 198, 249-257.
16. Flynn, JH, and Wall, LA (1966). A quick, direct method for the determination of activation energy from thermogravimetric data. J Polymer Sci: Part B Polymer Lett. 4, 323-328.
17. Gao, X, Chen, D, and Dollimore, D (1993). The correlation between the value of α at the maximum reaction rate and the reaction mechanisms. A theoretical study. Thermochimica Acta. 223, 75-82.
18. Hafiz, MM, El-Shazly, O, and Kinawy, N (2001). Reversible phase in BixSe100-x chalcogenide thin films for use as optical recording medium. Appl Surf Sci. 171, 231-241.
19. Haixiang, C, Naian, L, and Weitao, Z (2010). Critical study on the identification of reaction mechanism by the shape of TG/DTG curves. Solid State Sci. 12, 455-460.
20. Innami, T, and Adachi, S (1999). Structural and optical properties of photocrystallized Se films. Phys Rev B. 328, 8284-8289.
21. Abdul-Gader, Jafar MM, Saleh, MH, Ahmad, MJA, Bulos, BN, and Al-Daraghmeh, TM (2016). Retrieval of optical constants of undoped amorphous selenium films from an analysis of their normal-incidence transmittance spectra using numeric PUMA method. J Mater Sci: Mater Electron. 27, 3281-3291.
22. Jenkins, R (1999). X-Ray Fluorescence Spectrometry. New York: Wiley & Sons
23. Jones, LF, Dollimore, D, and Nicklin, T (1975). Comparison of experimental kinetic decomposition data with master data using a linear plot method. Thermochimica Acta. 13, 240-245.
24. Kasap, SO, Aiyah, V, and Yannacopoulos, S (1990). Thermal and mechanical properties of amorphous selenium films in the glass transformation region. J Phys D: Appl Phys. 23, 553-556.
25. Kasap, SO, and Rowlands, JA (2000). X-ray photoconductors and stabilized a-Se for direct conversion digital flat-panel X-ray image detectors. J Mater Sci: Mater Electron. 11, 179-198.
26. Keattch, CJ, and Dollimore, D (1975). An Introduction to Thermogravimetry. London: Heyden
27. Kotkata, MF, Abdel-Wahab, FA, and Al-Kotb, MS (2009). Effect of Incontent on the optical properties of a-Se films. Appl Surf Sci. 255, 9071-9077.
28. Lee, YF, and Dollimore, D (1998). The identification of the reaction mechanism in rising temperature kinetic studies based on the shape of the DTG curve. Thermochimica Acta. 323, 75-81.
29. Marini, A, Berbenni, V, and Flor, G (1979). Kinetic parameters from thermogravimetric data. Z Naturforsch. 34a, 661-663.
30. Mehra, RM, Kaur, G, Pundir, A, and Mathur, PC (1993). Study of Se-Te-Sb system for application to reversible optical-data storage. Jpn J Appl Phys. 32, 128-129.
31. Mehta, N (2006). Applications of chalcogenide glasses in electronics and optoelectronics: a review. J Sci Ind Res. 65, 777-786.
32. Moharram, AH, and Abu El-Oyoun, M (2000). Pre-crystallization kinetics of the Bi10Se90 glass. J Phys D: Appl Phys. 33, 700-703.
33. Mott, NF, and Davis, EA (1979). Electronic Processes in Non-Crystalline Materials. Oxford: Oxford University
34. Moukhina, E (2012). Determination of kinetic mechanisms for reactions measured with thermoanalytical instruments. J Therm Anal Calorim. 109, 1203-1214.
35. Okamoto, H (1994). The Bi-Se (Bismuth-Selenium) system. J Phase Equilibria. 15, 195-201.
36. Ozawa, T (1965). A new method of analyzing thermogravimetric data. Bulletin Chem Soc Jpn. 38, 1881-1886.
37. Perez-Maqueda, LA, Ortega, A, and Criado, JM (1996). The use of master plots for discriminating the kinetic model of solid state reactions from a single constant-rate thermal analysis (CRTA) experiment. Thermochimica Acta. 277, 165-173.
38. Ptá?ek, P, Kubátová, D, Havlica, J, Brandštetr, J, Šoukal, F, and Opravil, T (2010). The non-isothermal kinetic analysis of the thermal decomposition of kaolinite by thermogravimetric analysis. Powder Technol. 204, 222-227.
39. Saleh, MH, Ershaidat, NM, Ahmad, MJA, Bulos, BN, and Abdul-Gader, Jafar MM (2017). Evaluation of spectral dispersion of optical constants of a-Se films from their normal-incidence transmittance spectra using Swanepoel algebraic envelope approach. Opt Rev. 24, 260-277.
40. Saxena, M, and Bhatnagar, PK (2003). Crystallization study of Te-Bi-Se glasses. Bull Mater Sci. 26, 547-551.
41. Šesták, J (1984). Thermal Analysis, Part D: Thermophysical Properties of Solids, Their Measurements and Theoretical Thermal Analysis. Amsterdam: Elsevier
42. Sharp, HK, Brindley, GW, and Achar, BNN (1966). Numerical data for some commonly used solid state reaction equations. J Am Ceram Soc. 49, 379-382.
43. Sharp, JH, and Wentworth, SA (1969). Kinetic analysis of thermogravimetric data. Anal Chem. 41, 2060-2062.
44. Tichy, L, Ticha, H, Triska, A, and Nagels, C (1985). Is the n-type conductivity in some Bi-doped chalcogenide glasses controlled by percolation?. Solid State Commun. 53, 399-402.
45. Tonchev, D, and Kasap, SO (2002). Effect of ageing on glass transformation measurements by temperature modulated DSC. Mater Sci Eng A. 328, 62-66.
46. van der Heide, P (2012). X-ray Photoelectron Spectroscopy: An Introduction to Principles and Practices. Hoboken: Wiley

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