- About this Journal
- Abstracting and Indexing
- Aims and Scope
- Article Processing Charges
- Articles in Press
- Author Guidelines
- Bibliographic Information
- Citations to this Journal
- Contact Information
- Editorial Board
- Editorial Workflow
- Free eTOC Alerts
- Publication Ethics
- Submit a Manuscript
- Table of Contents
Volume 2012 (2012), Article ID 108781, 8 pages
Thermodynamics and Oxidation Behaviour of Crystalline Silicon Carbide (3C) with Atomic Oxygen and Ozone
Raman Centre for Applied and Interdisciplinary Sciences, 16A Jheel Road, Calcutta 700 075, India
Received 23 September 2012; Accepted 16 October 2012
Academic Editors: Y. Fang, T. M. Inerbaev, and G. Polidori
Copyright © 2012 Chandrika Varadachari 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.
Thermodynamics of oxidation of crystalline silicon carbide (cubic form) by atomic oxygen (O) and ozone (O3) was derived to understand the thermodynamic stability of SiC in the upper atmosphere. Equilibrium constants and equilibrium partial pressures were computed for each of eight possible reactions of SiC with O and O3. Equilibrium activity diagrams were derived, showing the most stable oxidation products of SiC, represented in temperature-oxygen pressure 2D diagrams. Programs were developed in Mathematica. The diagrams provide an understanding of the oxidation routes of SiC under changing levels of O/O3 and temperature, as encountered during reentry of space vehicles. At high levels of the volatiles, CO2, CO, and SiO and temperatures between 1000 and 1500 K, oxidation by atomic oxygen or ozone first produced SiO2 + C followed by SiO2 + CO and finally SiO2 + CO2. When volatiles were at very low pressures, the sequence of oxidation was SiO + CO followed by either SiO2 + CO or SiO + CO2 and finally SiO2 + CO2. Stability of SiC in ozone was much lower than in atomic oxygen. With both oxidants, the oxidation of the Si in SiC occurred prior to the oxidation of C. Implications for mechanisms of thermal protection are discussed.
Silicon carbide is an important material for space applications. It is a particularly useful thermal protection system for very high temperature zones like nose-cones in reentry vehicles. Since temperatures may reach C or higher, oxidation is a major problem and limits the temperatures to which SiC can be used. Several experimental studies on the oxidation of SiC with O2 have been reported. It was observed  that oxidation of SiC between 900–C resulted in a surface layer of SiO2 that formed a protective film. The oxidation of C-SiC heat shield materials under reentry conditions (50–3500 Pa and 1300–C) showed that a protective SiO2 layer was formed , and oxidation was insignificant as long as this silica layer was present. Others  observed etching of the surface and surface segregation of carbon. From photoemission studies on the SiC surface , it was concluded that oxygen is incorporated into the Si surface even at the smallest exposures to O2, but there was no discernible change on the C-terminated surface. Studies have confirmed that the rate controlling process is the diffusion of O2 through the solid SiO2 on the surface . Mogilevsky and Zangvil  modelled the oxidation of SiC-reinforced mullite–zirconia matrix composites and evaluated oxygen permeabilities of the matrix as well as the silica layer. Oxidation kinetics in the temperature range of 1200–1350°C showed  a parabolic behaviour, which indicated a diffusion-controlled mechanism. In high vacuum, the surface composition of SiC (000) changed as a function of temperature due to oxide formation, yielding graphitic surface carbon . Thermodynamic modelling of the reactions of oxygen with SiC has also been reported [3, 9]. Phase diagrams of Si-C-O (oxygen) system are available in the literature [10, 11] as either triangular diagrams (Si-C-O) or biaxial diagrams (T-SiC/SiO2).
Three layers of the atmosphere are involved in the oxidation reactions that occur during re-entry, namely, the troposphere, stratosphere, and mesosphere-lower thermosphere. The troposphere extends to about 18 km at the equator and 8 km at the poles. Tropospheric chemistry would be dominated by oxidation with molecular oxygen whose partial pressures vary from about 0.2 bar to bar at the tropopause [12, 13]. The stratosphere extends from 15–50 km above the Earth. Atmospheric chemistry of the stratosphere is dominated by ozone, with highest concentrations at 15–30 kilometres above the Earth’s surface. Partial pressures of ozone here vary from about bar . The mesosphere is located about 50–85 km above Earth’s surface, and the lower thermosphere is located between 80 and 180 km. Within this layer, temperature decreases with increasing altitude. Two strong photodissociation continua, the Schumann-Runge continuum, and the weaker Herzberg continuum produce atomic oxygen (O) by breakdown of O2 .
To obtain an understanding of the chemical behaviour of SiC in the upper atmosphere, knowledge of the nature of reactions with atomic oxygen and ozone is important. The objective here was a theoretical investigation of the thermodynamics of oxidation of SiC by O and O3. Equilibrium constants were computed for all possible reaction pathways. Equilibrium activity diagrams were derived to show the effects of temperature and pressures of O and O3 on the oxidation of SiC. The resulting diagrams showed the thermodynamically stable oxidation products under variable temperatures and partial pressures of oxidants. Possible pathways of oxidation were proposed. The studies would be useful for modelling chemical transformations of SiC in the stratosphere and mesosphere-lower thermosphere.
2. Theory and Methods
Oxidation of SiC with O/O3 can occur in eight different ways. These reactions are stoichiometrically represented in Table 1.
Standard free energy change of these reactions at temperature , () was obtained from the standard free energy of formation () as: which is related to equilibrium constant as where and are activities of products and reactants, respectively, and the power terms refer to the stoichiometric amounts of the compounds participating in the reaction. Total free energy change under nonstandard conditions was obtained from the relation: Equilibrium activity diagrams were derived from net Gibbs free energy changes (). This allows us to include the effect of variables (such as partial pressures of CO, CO2, and SiO) that have important contributions to oxidation. The dominant reaction will be the one with the most negative total free energy change ().
The process involved (i) computation of free energy changes for all possible reactions in a system, (ii) comparison to obtain the reaction showing greatest reduction in free energy, and (iii) derivation of the limiting conditions for the reaction to have largest free energy reduction compared to all other reactions. Thus, the values of for all equations in Table 1 were derived at small intervals of the variables . These values were compared at each value of the variables, and subsequently boundary conditions were obtained.
Thermodynamic data for the computations were obtained from the literature . Equilibrium activity diagrams showing partial pressure-temperature relations were then computed. For derivation of equilibrium activity diagrams, a program OXID2D was developed in Mathematica (see Supplementary Materials available online at doi:10.542/2012/108781). The main program has 2 subroutines (SubOXID_1 and SubOXID_2), which derive the standard free energy change of the oxidation reaction () and equilibrium ozone (O3) pressures at lower and higher temperatures (flow chart in Figure 1). The first sub-routine (SubOXID_1) is for reactions in the lower temperature range (298.15–1900 K), where SiO2 is in the solid phase; the other sub-routine (SubOXID_2) is for reactions at temperatures above the melting point of SiO2 (2000–3200 K). Inputs required are the gas constant (in kJ/mole) and values of , , and (Figure 1). Other input data are temperatures and the corresponding standard free energy of formation () of all compounds in the reactants and products. Then, for each temperature T, is derived by (1). The list of temperature- is exported for the main program. Additionally, equilibrium ozone (O3) pressures are computed for constant values of , , and and plotted as versus . The subroutines are available as supplementary information.
The main program OXID2D (supplemental file) then derives the equilibrium boundaries from total free energy change of reaction ( ) using (3). To compute the values of , activities of CO2, CO, and SiO have to be defined. Here, these were assigned constant values representing four different conditions, namely, , , , and . The next step of the program (flow diagram in Figure 2) defines minimum and maximum temperatures and ozone (O3) partial pressures () and the respective increment intervals. A list of the variables, T-, is then generated. The data from SubOXID_1 & 2 are imported, and the relation between T- is fitted into a linear regression equation. From this equation, values are derived for every value of temperature increment. Subsequently, using (3), values are computed from the values of using , , and as constants, and as variables, temperature range to 3200 K, ozone levels to −50, and increment intervals of and . Only negative values of are retained. Derived values for all the reactions are combined into separate lists for each T-. In each list, the values are compared, and the reaction showing the most negative value is assigned to that T- as the most favourable (stable) reaction. The reaction is identified and represented by a coloured box at that particular value of T-. The process is repeated over all values of T-, and all points are combined in a single plot. A similar method was earlier used to derive equilibrium diagrams for nonstoichiometric clay minerals in aqueous environments  and also to derive fuzzy phase diagrams representing 464 metastable minerals .
Equilibrium diagrams in the atomic oxygen system were derived with the same program after substituting the values for O and changing the reaction stoichiometries according to those shown in Table 1.
3. Results and Discussion
3.1. Equilibrium Constants and Equilibrium Gas Pressure
Equilibrium constant ()-temperature relationships for 8 types of oxidations of cubic (3C) SiC (Table 1) are presented in Figure 3. values were highly positive and suggested that all oxidations were thermodynamically favourable. The oxidation reaction producing SiO2 + CO2 had highest values of for both the oxidants O and O3. This was followed by SiO2 + CO and then SiO2 + C. At higher temperatures, there was a crossover, with SiO + CO2 having higher than SiO2 + C. In general, reactions producing SiO2 or CO2 were energetically more favourable than reactions producing SiO or CO. The value of reduced sharply with temperature for all reactions except (6) and (8).
Equilibrium constants for reactions with O3 were generally smaller than with O. Thus, at 1000 K, log values for the formation of SiO2 + CO2 from O and O3 were 94.6 and 70.2, respectively; at 2000 K, these values were 36.2 and 33.2. Oxidation to SiO + CO2 at 1000 K showed a similar trend with equilibrium constants of 56.3 and 38.0 for reactions with O and O3, respectively.
Equilibrium partial pressures of O and O3 for oxidation of SiC (under standard pressures of CO2, CO and SiO) are presented in Table 2. Oxidation was thermodynamically favourable at 1000 K with levels as low as −29; reactions forming SiO2 occurred at lower O pressures than those forming SiO. At 3000 K, equilibrium levels were about −6 for SiO formation, and unlike trends at 1000 K, SiO2 was formed at higher O levels compared to SiO. Oxidations with O3 (Table 2) followed a similar trend. However, equilibrium activities for oxidation with ozone were substantially lower than for atomic oxygen.
Partial pressures of the volatiles, CO2, CO, and SiO had a significant impact in lowering the pressures of O/O3 at which oxidation began. Reactions forming SiO (Figure 4) were particularly affected by increasing levels of the volatiles, as observed by the steep slopes. Oxidation to SiO2 was comparatively less affected by the levels of volatile products. This was true for both oxidants, O and O3. Reactivity of SiC towards ozone was particularly remarkable. Even in the presence of substantial levels of the oxidation inhibitors, oxidation to SiO could occur at O3 pressures as low as atm, which is about 1017 times lower than the level of atomic oxygen required for the same oxidation.
3.2. Oxidation Equilibrium Diagrams
Reaction equilibrium diagrams of thermodynamically stable products formed, when SiC (cubic) was exposed to various O pressures at different temperatures and different levels of CO2, CO, and SiO, are presented in Figures 5(a)–5(d). Figure 5(a) shows the nature of products under standard (unit) pressures of gaseous products CO2, CO, and SiO. At temperatures below 1500 K, as O pressure increased, SiO2 and C were the first reaction products. On further increase in O pressure, SiO2 and CO2 were formed (at −18). At temperatures above 1500 K, the initial products were SiO2 + CO followed by SiO2 + CO2 at higher O pressures. In the region beyond ~2300 K, oxidation proceeded from SiO + CO to SiO2 + CO and then to SiO2 + CO2. Significantly, the sequence of oxidation also suggested that oxidation of the Si in SiC occurred prior to the oxidation of C.
As levels of CO, CO2, and SiO were reduced to atm (Figure 5(b)), the stability zone of SiC was reduced from an upper limit of to . Above temperatures of ~1800 K, SiO was the first oxidation product. Further oxidation produced either SiO2 + CO or SiO + CO2 depending on whether temperature was above or below 2350 K. Temperature for formation of SiO was greatly lowered as levels of CO, CO2, and SiO were further reduced (Figures 5(c) and 5(d)). Thus, SiO was formed at ~1100 K when pressures of CO, CO2, and SiO were at atm (Figure 5(d)); equilibrium pressure for stability of SiC also dropped sharply to about atm.
Briefly, at lower temperatures and higher levels of volatiles (Figures 5(a) and 5(b)), oxidation with atomic oxygen first produced SiO2 + C followed by SiO2 + CO2. Increasing temperature and reducing pressures of volatiles (Figures 5(c) and 5(d)) resulted in the oxidation sequence SiO + CO then SiO + CO2 and finally SiO2 + CO2. Lower temperatures favoured the formation of SiO2 (passive oxidation), whereas SiO was formed at higher temperatures (active oxidation).
Stability of SiC in ozone was severely reduced compared to atomic oxygen. Even at of −3, SiC oxidised to SiO and CO at atm O3 and at 1600 K (Figure 6(b)). There was no observable stability field of SiC (down to ) when pressures of volatiles were very low ( atm, Figure 6(d)). Oxidation products were similar to those observed with molecular and atomic oxygen. However, the stability field of SiO2 + CO increased significantly. At lower temperatures, oxidation proceeded with the formation of SiO2 + CO followed by SiO2 + CO2. At higher temperatures, SiO + CO formed first; this oxidised to SiO + CO2 and finally to SiO2 + CO2.
With regard to reactions at the surface of reentry vehicles, the diagrams suggest that at the initial phase (in the upper mesosphere, where temperatures fall as low as 200 K, and the main oxidant is atomic oxygen) oxidation would mainly produce SiO2 and CO2. On entry into the stratosphere, under the conditions of temperature and ozone pressures encountered, SiO2 and CO2 would form. Since tropospheric oxygen levels are in the range of 0.2 bar to bar at the tropopause , the implications are that SiO2 and CO2 would be the major oxidation products (provided CO/CO2 levels are high, as in the presence of ablatives). The initial formation of SiO2 would result in a protective layer that would retard diffusion and further oxidation of SiC. Although in the absence of CO/CO2 producing ablatives the oxidation product would be SiO, the initial coating of SiO2 would protect the bulk SiC from complete oxidation. Such a protective mechanism would be effective only below the melting point of SiO2, that is, 1996 K. Above this temperature, complete oxidation can occur (since wind speeds would be sufficient to blow away the liquid SiO2 coating).
Experimental data on the oxidation of silicon carbide with ozone showed that oxidation rates in ozone-containing atmosphere were much higher than those in a pure oxygen atmosphere . In other experimental observations on oxidations with molecular oxygen, SiO2 has been observed to form a protective film on the surface of SiC between 900 and C ; this has been verified under reentry conditions . Protective action reduces when SiO2 begins to bubble at 3500 Pa and C . Cracks form and become oxidation channels leading to rapid weight loss . The oxidation behavior of the SiC indicated a two-step parabolic oxidation kinetics with formation of crystalline SiO2 film. Diffusion of oxygen through the SiO2 film becomes the rate-controlling step of reaction . Charpentier et al.  observed with massive -SiC samples that the transition between passive and active oxidation occurred at 1300 K for an oxygen partial pressure of 0.2 Pa and at 1600 K for 100 Pa. Our observation that the Si in SiC is more readily oxidized than the C is also corroborated by experimental studies  which show that even very small exposures to oxygen lead to an oxygenated Si terminated surface but without any change in the C-terminated surface.
Thermodynamics of oxidation reactions of SiC were studied by constructing a reaction equilibrium diagram of SiC with atomic oxygen and ozone. Equilibrium constant ()-temperature relations were derived for all the eight possible ways in which oxidation could occur. In all reactions, values were observed to be highly positive and to decrease with temperature. The reaction forming SiO2 + CO2 was thermodynamically the most favourable. Partial pressure-temperature relations suggest that equilibrium pressures are extremely low.
Derived oxidation equilibrium diagrams showed the thermodynamically most favoured oxidation products and the sequence of oxidation under various conditions. As SiC was exposed to increasing levels of O or O3, the first products were SiO2 + C, followed by SiO2 + CO/SiO + CO2. High temperature and lower pressures of volatiles (CO, CO2, and SiO) in the zone of oxidation favoured the formation of SiO over SiO2. Moreover, in the SiC crystal, it is the Si atom which is more susceptible to oxidation than the C atom, and it is the Si which is first oxidized forming SiO2.
Oxidation equilibrium diagrams could help to understand reactions during reentry of space vehicles. Since surface heating becomes significant at about 120 km from the Earth’s surface, three layers of the atmosphere are involved, namely, the troposphere, stratosphere, and mesosphere-lower thermosphere. The SiO2 layer (probably formed in the initial phase of re-entry) protects the bulk SiC from further catastrophic oxidation to SiO which could occur at higher temperatures at the later stages. Protective action towards oxidation would be effective till below the melting point of SiO2 (1996 K), where upon SiO2 liquid would be blown off the surface.
Financial support from ER & IPR, DRDO, and Government of India is gratefully acknowledged.
- P. J. Jorgensen, M. E. Wadsworth, and I. B. Cutler, “Oxidation of silicon carbide,” Journal of American Ceramic Society, vol. 42, no. 12, pp. 613–616, 1959.
- M. Auweter-Kurtz, G. Hilfer, H. Habiger, K. Yamawaki, T. Yoshinaka, and H. D. Speckmann, “Investigation of oxidation protected C/C heat shield material in different plasma wind tunnels,” Acta Astronautica, vol. 45, no. 2, pp. 93–108, 1999.
- Y. Song and F. W. Smith, “Effects of low-pressure oxidation on the surface composition of single crystal silicon carbide,” Journal of the American Ceramic Society, vol. 88, no. 7, pp. 1864–1869, 2005.
- C. Virojanadara and L. I. Johansson, “Metastable oxygen adsorption on SiC(0001)-√3 × √3 R30°,” Surface Science, vol. 519, no. 1-2, pp. 73–78, 2002.
- J. A. Costello and R. E. Tressler, “Oxidation kinetics of hot-pressed and sintered α-SiC,” Journal of the American Ceramic Society, vol. 64, no. 6, pp. 327–331, 1981.
- P. Mogilevsky and A. Zangvil, “Modeling of oxidation behavior of SiC-reinforced ceramic matrix composites,” Materials Science and Engineering A, vol. 262, no. 1-2, pp. 16–24, 1999.
- D. M. Liu, “Oxidation of polycrystalline α-silicon carbide ceramic,” Ceramics International, vol. 23, no. 5, pp. 425–436, 1997.
- J. M. Powers and G. A. Somorjai, “The surface oxidation of alpha-silicon carbide by O2 from 300 to 1373 K,” Surface Science, vol. 244, no. 1-2, pp. 39–50, 1991.
- J. Wang, L. Zhang, Q. Zeng, G. L. Vignoles, and A. Guette, “Theoretical investigation for the active-to-passive transition in the oxidation of silicon carbide,” Journal of the American Ceramic Society, vol. 91, no. 5, pp. 1665–1673, 2008.
- A. E. Mc Hale, Ed., Phase Equilibria Diagrams, Phase Diagrams for Ceramists, vol. 10, American Ceramic Society, Westerville, Ohio, USA, 1994.
- J. Weiss, H. L. Lukas, J. Lorenz, G. Petzow, and H. Krieg, “Calculation of heterogeneous phase equilibria in oxide-nitride systems. I. The Quaternary System C Si N O,” Calphad, vol. 5, no. 2, pp. 125–140, 1981.
- J. W. Chamberlain and D. M. Hunten, Theory of Planetary Atmospheres, Academic Press, San Diego, Calif, USA, 1987.
- R. D. Thompson, Atmospheric Processes and Systems, Routledge, London, UK, 1998.
- M. W. Chase Jr., NIST-JANAF Thermochemical Tables, vol. 14 of Journal of Physical and Chemical Reference Data, AIP, New York, NY, USA, 1985.
- C. Varadachari, “Constructing phase diagrams for silicate minerals in equilibrium with an aqueous phase: a theoretical approach,” Soil Science, vol. 153, no. 1, pp. 5–12, 1992.
- C. Varadachari, “Fuzzy phase diagrams of clay minerals,” Clays and Clay Minerals, vol. 54, no. 5, pp. 616–625, 2006.
- T. Narushima, M. Kato, S. Murase, C. Ouchi, and Y. Iguchi, “Oxidation of silicon and silicon carbide in ozone-containing atmospheres at 973 K,” Journal of the American Ceramic Society, vol. 85, no. 8, pp. 2049–2055, 2002.
- T. Narushima, T. Goto, and T. Hirai, “High-temperature passive oxidation of chemically vapor deposited silicon carbide,” Journal of the American Ceramic Society, vol. 72, no. 8, pp. 1386–1390, 1989.
- L. Charpentier, M. Balat-Pichelin, and F. Audubert, “High temperature oxidation of SiC under helium with low-pressure oxygen-Part 1: sintered α-SiC,” Journal of the European Ceramic Society, vol. 30, no. 12, pp. 2653–2660, 2010.