arbon coated alumina with enhanced phase stability at high temperatures

A comparative investigation of the phase stability at high temperatures of nanocrystalline Al2O3 and carboncoated Al2O3@C systems was performed using a set of physicochemical and spectroscopic methods. The obtained data demonstrate that the carbon coating hinders the sintering of the d-Al2O3 phase and its transformation to the a-Al2O3 phase at 1250 C. Without the carbon coating, the d-Al2O3 sinters and becomes completely converted to corundum at noticeably lower temperatures. The stabilization of the nanosized oxide particles in the Al2O3@C system was shown to be the decisive factor preventing their transformation to the a-Al2O3 phase. The thermal stability of the Al2O3@C samples calcined within a range of 1180–1250 C in an argon atmosphere followed by the calcination in air to remove the carbon coating was found to exceed that of pure d-Al2O3. Such samples are characterized by the presence of carbon–alumina interfaces, when carbon is encapsulated in small amounts at the places of contact between the oxide nanoparticles. Such interfaces hinder the sintering of alumina nanoparticles. It is important that the active sites present on the surface of the oxide core in Al2O3@C samples calcined in air are similar to those known for pure alumina. The high concentration of such sites after thermal treatment at elevated temperatures makes this class of materials promising for use as catalysts or catalyst supports capable of operating at high temperatures.


Introduction
Size effects play a dening role in many chemical and phase transformations of oxide materials.For instance, nanocrystalline mesoporous oxides with nanoparticle sizes under 10 nm oen have unusually high reactivity in many chemical reactions.This property leads to their use as efficient catalysts [1][2][3] and destructive sorbents [4][5][6][7][8][9][10] for the neutralization of various toxic compounds.However, the products resulting from their solidstate reactions are usually not nanocrystalline.Solid-state reactions of nanocrystalline oxides even at moderate temperatures are typically accompanied by signicant particle sintering and formation of new phases in the form of much larger particles.The same processes are characteristic of phase transformations taking place with the temperature increase and leading to signicant growth of precursor nanoparticles.
2][13] So, the rutile formation during the temperature growth is related to the growth of TiO 2 nanoparticles due to their sintering.Similar behavior was observed for Al 2 O 3 .g-Al 2 O 3 is the most stable phase at the high specic surface area and the small particle size.5][16][17] Meanwhile, the growth of oxide nanoparticles directly contacting with each other takes place at high temperatures due to the sintering.
We have suggested that such sintering can be slowed down or even completely prevented by eliminating the direct contact between the oxide nanoparticles.This could stabilize the size of the nanoparticles and hinder the formation of the hightemperature phases (rutile and corundum for TiO 2 and Al 2 O 3 , respectively) even at elevated temperatures.The fact that the sintering of alumina particles can be hindered by their coating with carbon is known for a long time.9][20][21][22] At the same time, in a number of recent papers it was shown that the carbon coating can be used for the synthesis of the structured and mesoporous materials based on Al 2 O 3 . 19,23Earlier we have reported that the carbon coating deposited on the surface of the oxide nanoparticles can act as a nanoreactor shell.On the one hand, such coating can be penetrable for the reactant molecules from the gas 7,10,24,25 or liquid 26 phases making it possible to initiate various catalytic or solid-state reactions inside the nanoreactor.Moreover, the carbon coating prevents sintering of nanoparticles inside the shell during the temperature increase and stabilizes their sizes.The anatase phase was shown to be stable for the carbon-coated titania TiO 2 @C with the core-shell structure up to the temperatures as high as 750 C. 25 It is important that the TiO 2 nanoparticles inside the carbon shell practically do not grow in this temperature range.At higher temperatures, the TiO 2 nanoparticles are subjected to reduction by the deposited carbon.
g-Al 2 O 3 is a mesoporous sorbent and a catalyst support widely used in the modern chemical technology.It has high surface area and maintains it at the temperatures as high as 700-800 C. Further temperature increase results in its phase transformations accompanied by the dehydration, the nanoparticle growth and the surface area decrease.Recently reported data indicate that the carbon nanoreactor could be used to stabilize the size of the aluminum oxide nanoparticles and prevent their phase transformations. 25n this study we have analyzed the effect of the carbon coating deposited on the Al 2 O 3 surface on the alumina phase transformations (g / d / a), pore structure and state of active sites on the surface aer the calcination at high temperatures.

Experimental
The g-Al 2 O 3 sample used as a precursor for the synthesis of all other samples was obtained by the calcination of a Condea "Pural SB-1" pseudoboehmite sample in air at 720 C for 6 h.The sample was heated up to the calcination temperature with a ramping rate of 1.5 C min À1 .The specic surface area of the precursor sample was about 210 m 2 g À1 .
To deposit the carbon coating, the g-Al 2 O 3 precursor was mixed with polyvinyl alcohol (PVA) in a 7 : 3 weight ratio.Then, the obtained mixture was heated in a quartz reactor in argon up to 750 C with a ramping rate of 1.5 C min À1 and kept at this temperature for 6 h.
For treatment at higher temperatures, the obtained sample was placed into a graphite crucible that was installed into a corundum tube assembled inside a tubular Starbar TSR heater.Then, the sample was heated in an argon ow with a ramping rate of 3 C min À1 to the desired temperature varied from 960 to 1450 C and kept at this temperature for 6 h.The samples with the carbon coating were labeled as Al 2 O 3 @C-T, where T is the temperature of the nal treatment in argon.
Aer heating in argon at high temperature, some of the carbon-coated samples were subjected to the calcination in air at 700 C (or 1180 C) for 6 h in a muffle furnace to burn off the carbon.Such samples were designated as Al 2 O 3 @C-T 1 -T 2 , where T 1 is the temperature of the heat treatment in argon and T 2 is the temperature of subsequent calcination in air.
In order to elucidate the effect of carbon shell, the reference alumina sample without carbon coating was also subjected to the similar thermal treatment procedures.Such samples were denoted as Al 2 O 3 -T, where T is the thermal treatment temperature.
To control the state of the active sites on the alumina surface, including the samples obtained from the carbon-coated alumina by burning off the carbon, a spin probe method yielding the information on the electron-donor and electronacceptor sites on the alumina surface was used.8][29][30] Prior to adsorption of the probe molecules the samples were dehydrated in air at 500 C for 12 h.The electron-acceptor surface sites were studied using an antracene adsorption from 5 Â 10 À2 M solution in toluene.The electron-donor sites were characterized using adsorption of 1,3,5-trinitrobenzene from 2 Â 10 À2 M solution in toluene.The concentration of the ion-radicals was measured aer maintaining the samples in the mentioned solutions at 80 C for 5 h, thus providing the achievement of their utmost value.
The EPR spectra were recorded using an ERS-221 EPR spectrometer working in the X-band with typical microwave power of 3 mW.The concentrations of the paramagnetic species were determined by a numerical double integration with baseline compensation.A dissolved stable nitroxide radical TEMPO was used for the calibration.
The specic surface areas calculated by the BET method and pore size distributions calculated by the BJH method were obtained from the data of low-temperature argon adsorption using an ASAP-2400 instrument.
The photoluminescence experiments were carried out under the atmospheric conditions at 290 K using a homemade spec-trouorimeter equipped with MDR-12 monochromator (LOMO), an LN/CCD-1100PF/UV (Princeton Instruments) spectroscopic camera and a set of UV-vis laser sources.A 514.5 nm line of Ar ion laser LGN-402 (Russia) was used for the luminescence excitation.A powder sample was placed in a 1 mm deep quartz cell in a front-face conguration.The Al 2 O 3 -1200 sample was used for relative calibration of the PL method in determination of the a-Al 2 O 3 concentration.
UV-vis diffuse reectance spectra were recorded between 200 and 800 nm using a Shimadzu UV-VIS 2501 PC spectrometer with IRS-250A diffusion reection attachment.The UV-vis spectra were transformed into the Kubelka-Munk function , where R is the experimentally measured reectivity coefficient of the samples.
Raman spectra were recorded using a LabRAM HR800 spectrometer from HORIBA Jobin Yvon with a Symphony CCD detector.For spectral excitation the 488 nm line of an Ar ion laser (35LAP431 from Melles Griot, USA) was used.All data were collected using a Raman microscope in backscattering geometry.Spectral resolution was 1 cm À1 .
XRD analysis was performed using a Brucker D8 diffractometer with Co Ka irradiation.The high-resolution transmission electron microscopy (HR TEM) images were obtained using a JEM-2010CX microscope with a 1.4 Å line resolution.

Stabilizing the alumina with the carbon coating
The calcination of the nanocrystalline alumina samples at high temperatures is known to result in their conversion to a corundum phase with signicant loss of the specic surface area and growth of the particle size.So, on the rst stages of the research the effect of the carbon shell on the alumina phase transformations was studied.The carbon coating was found to hinder the sintering process of the Al 2 O 3 nanoparticles without reacting with them within the studied temperature range.
It is well known that an increase of the size of the nanoparticles during the thermal treatment results in the loss of their specic surface area.The values of SSA for the studied samples aer the calcination at high temperatures are shown in Fig. 1.Fast drop of the SSA at the calcination temperatures around 1100 C, when the corundum phase is formed, is evidently seen for pure Al 2 O 3 .At the same time, for the Al 2 O 3 @C samples, relatively high values of SSA are preserved until the calcination temperature of 1380 C.
The pore size distributions for the Al 2 O 3 and Al 2 O 3 @C samples aer different treatments are demonstrated in Fig. 2. The graphs were plotted in accordance with the IUPAC recommendations. 31The initial Al 2 O 3 -720 sample has the SSA close to 200 m 2 g À1 and the mesopore volume equal to 0.55 cm 3 g À1 with a peak on the pore size distribution at about 9 nm (Fig. 2A).Aer the thermal treatment at 1030 C, when the d-Al 2 O 3 phase is formed, the mesopore structure is preserved.The SSA decreases to ca. 100 m 2 g À1 with the pore volume of 0.45 cm 3 g À1 .The maximum on the pore size distribution shis to 11.5 nm.Meanwhile, the conversion of alumina to a-Al 2 O 3 aer the calcination at 1250 C leads to a collapse of the pore structure with the surface area going down to 5 m 2 g À1 and pore volume decreasing to 0.05 cm 3 g À1 .
The pore size distribution for the carbon coated Al 2 O 3 @C-720 looks very similar to that of the Al 2 O 3 -720 precursor before the carbon deposition (Fig. 2B).Aer the thermal treatment of the carbon-coated sample at 1250 C, the mesopore structure is preserved.The properties of this material resemble those of pure alumina calcined at 1030 C. It has the d-Al 2 O 3 phase with the SSA equal to 100 m 2 g À1 , the mesopore volume of 0.27 cm 3 g À1 with a peak on the pore size distribution at 13 nm.Overall, the adsorption data conrm that the carbon coating makes it possible to stabilize the Al 2 O 3 mesopore structure aer the calcination at temperatures as high as 1250 C and extend the temperature range of its existence by about 200 C.
The peculiarities of the phase transformations of pure and carbon-coated alumina samples at 1180, 1250 and 1380 C were studied by means of the X-ray diffraction analysis.The resulted XRD patterns are given in Fig.The effect of the carbon coating on the formation of qand a-Al 2 O 3 phases at the initial stages, when the alumina conversion is very low, was estimated using the photoluminescence spectroscopy.PL spectroscopy is known as a convenient and highly sensitive method of diagnostics for these phases.The appearance of easily identiable R a lines of impurity Cr 3+ ions, which are always present in alumina, was used as an inner probe.The procedure used to determine the concentrations of qand a-Al 2 O 3 phases in such samples is described elsewhere. 32,33he luminescence spectra of the pure alumina and the carbon-coated Al 2 O 3 @C sample calcined in argon at 960 C for 24 h are shown in Fig. 4. To perform the luminescence measurements, the carbon coating was removed by an additional calcination in air at 700 C. Fig. 5 shows the effect of the calcination time on the concentrations of qand a-Al 2 O 3 phases in the samples estimated from the intensity of Cr 3+ R a lines aer excitation of Cr 3+ ions in the 4 A 2 / 4 T 2 band (l ex ¼ 514.5 nm).It is evident that the carbon coating substantially slows down the rates of the qand a-Al 2 O 3 phase's formation at the initial stages, thus hindering ultimately the phase transformation.Note that in this concentration range it is practically impossible to detect the qand a-Al 2 O 3 phases by means of XRD analysis.
The size of the alumina crystallites is stabilized at level of 15-20 nm under such conditions (Fig. 6A).The HR TEM images clearly demonstrate the presence of disordered carbon in the form of the curved graphene packages on the surface of the alumina crystallites and inside the pores within them.The insertion in Fig. 6A presents the two-dimensional Fouriertransform from the selected area.The halo corresponds to the disordered carbon, and the pointed reection conforms to lattice spacing d 013 ¼ 0.455 nm for the d-Al 2 O 3 phase (PDF Data Base, card 46-1131).
As it was shown above by XRD, the transformation of alumina to corundum in the case of the Al 2 O 3 @C sample takes place only during the thermal treatment at 1380 C (Fig. 3).The size of the alumina particles exceeds 100 nm (Fig. 7A), and a monolayer graphene coating is formed on its surface (Fig. 7B).Most likely, at this temperature the carbon species are deformed by redistribution on the Al 2 O 3 surface and leave the surface of the oxide nanoparticles allowing their direct contact and consequent sintering.Finally, the process results in the formation of the corundum phase, which is thermodynamically more stable for the case of large alumina particles.
The presented data demonstrate that in the studied samples the deposited carbon species prevent the sintering of the d-Al 2 O 3 nanoparticles and their conversion to corundum at 1250 C. Without such coating d-Al 2 O 3 undergoes both the sintering and the complete transformation to corundum at substantially lower temperatures.Thereby, it can be concluded that the size stabilization of the Al 2 O 3 nanoparticles in the Al 2 O 3 @C samples is the key factor, which prevents their phase transformation.

Elimination of the carbon coating
In order to characterize the alumina nanoparticles stabilized in the carbon nanoreactor, the carbon was removed by the    5 The dependence of the corundum phase concentration in the Al 2 O 3 and Al 2 O 3 @C samples, and q-phase in the Al 2 O 3 @C sample estimated from the intensities of R a and R q lines of Cr 3+ ions after excitation in 4 A 2 / 4 T 2 bands (l ex ¼ 514.5 nm).For the Al 2 O 3 @C sample, all the data were multiplied by a factor of 10.
calcination in air at 700 C. Fig. 1 also shows the comparison results for the SSA values of the carbon-coated samples before and aer this procedure.As seen, starting from 1200 C carbon has a signicant contribution to the specic surface area of the samples.At temperatures above 1300 C its contribution exceeds that of the Al 2 O 3 phase.Nevertheless, the SSA of the Al 2 O 3 particles measured aer the carbon coating removal by calcination in air at 700 C remains relatively high even for the Al 2 O 3 @C-1300 samples.The calcination procedure eliminates the most of the deposited carbon, thus facilitating toward the preservation of the pore structure due to the carbon coating.Aer the calcination, the SSA remains as high as 72 m 2 g À1 with the pore volume equal to 0.3 cm 3 g À1 and a clear peak on the pore size distribution at 13 (Fig. 2B).According to TEM results, the carbon elimination procedure does not lead to the growth of the oxide nanoparticles (Fig. 6B).This image shows that all carbon accessible to the gas phase burns off during the calcination treatment.However, a minor fraction of carbon remains at the places of contact between the nanoparticles.These carbon species are believed to be responsible for the grey color of the samples and for the stabilization effect observed.
As it was already mentioned, nely dispersed alumina is quite oen used as a catalyst or a catalyst support.Various types of the active sites on its surface might play an important role for such applications.From this point of view, it was important to study the effect of the high temperature calcination on the concentration of active sites present on the surface of the Al 2 O 3 @C samples aer the elimination of the carbon coating.
The electron-acceptor and electron-donor sites related to the strong surface acid and base sites, respectively, were characterized by EPR using appropriate spin probes.The d-Al 2 O 3 sample with SSA about 100 m 2 g À1 prepared by calcination of the initial Al 2 O 3 precursor at 1000 C was used as a reference.
30]32 The electron-acceptor sites on the alumina surface characterized using the aromatic molecules (anthracene) were shown to correlate well with the acidic properties of this material and account for its catalytic activity in ethyl alcohol dehydration to ethylene. 30The electron-donor sites on the surface of alumina and zirconia are responsible for the stabilization of the atomically dispersed forms of deposited noble metals having high activity in a model reaction of CO oxidation and improved stability at elevated temperatures. 27,32,34,35ypical EPR spectra observed aer the anthracene adsorption on the surface electron-acceptor sites are shown in Fig. 8A.The EPR signal of anthracene ionized on the electron-acceptor sites is observed as a singlet line with g ¼ 2.003 and line width about 8G for all studied samples containing such sites.The estimated concentrations of such sites are summarized in Table 1.Almost the same concentrations of the electronacceptor sites were measured for the Al 2 O 3 -1000 and Al 2 O 3 @C-1250-700 samples.Meanwhile, for the Al 2 O 3 -1180 sample, this concentration was below the detection limit.It testies that the surface properties of the alumina particles in the Al 2 O 3 @C sample with respect to the used probe molecule  were not changed signicantly even aer the calcination at 1250 C. At the same time, conversion to the a-Al 2 O 3 phase and accompanying loss of the surface area has resulted in the disappearance of the surface electron-acceptor sites.
Typical EPR spectra observed aer the 1,3,5-trinitrobenzene adsorption on the surface electron-acceptor sites are shown in Fig. 8B.These spectra correspond to TNB radical anions formed on the electron-donor sites of the Al 2 O 3 surface were reported in detail recently. 28,29A typical feature of these spectra is a hyperne splitting on one nitrogen atom with strong anisotropy of the a-tensor.The A zz constant determined from the splitting between the extreme components of the spectra was equal to 31 G for all the samples.
The results observed using this probe molecule are generally similar to the ones obtained by using anthracene, although the types of characterized active sites are entirely different.Hereby, the calcination of the carbon-coated alumina samples in argon at temperatures as high as 1250 C does not result in signicant changes in the concentrations or properties of the electronacceptor or electron-donor sites on the surface of the alumina.The elimination of the carbon coating by the calcination in air leads to the alumina samples with the concentrations of these active sites, which are typical for the conventional d-Al 2 O 3 .
Quite different results were obtained for the Al 2 O 3 @C-1250-1180 sample, which was calcined rst in argon at 1250 C and then in air at 1180 C. As it was already noted, the concentrations of the studied active sites were below the detection limit for Al 2 O 3 -1180 sample without the carbon coating.It is in a good agreement with the data obtained by XRD and textural methods.The sample was completely converted to the a-Al 2 O 3 phase with a major loss of the surface area.Contrary, about 10% of the initial concentration of the active sites was detected on the Al 2 O 3 @C-1250-1180 sample.Thus, the thermal stability of Al 2 O 3 @C-1250 sample with respect to subsequent calcination in air was signicantly higher than that of the pure alumina.Apparently, some carbon is retained in these samples aer the procedure of the carbon coating elimination.These carbon species are presumably located at the places of contact between the crystallites and inaccessible to the air.They accounts for the grey color of these samples and signicantly hinders their sintering at high temperatures.
This grey color appears only for Al 2 O 3 @C-T samples calcined in argon at relatively high temperature T. Calcination of the initial Al 2 O 3 @C-700 sample in air at 700 C results in complete combustion of the carbon deposits yielding a white sample.This observation was conrmed by the lack of additional absorption in the UV-vis and Raman spectra of this sample.9).There are two bands in these spectra.7][38][39] A band at 340-350 nm corresponds to n / p* transition for isolated graphene particles and C-O bonds 40 on Al 2 O 3 reddue to stronger interaction with the support from $300 nm and 330 nm, respectively.The intensities of these lines increase with the growth of the calcination temperature in argon indicating increasing amount of carbon encapsulated during the sintering (Fig. 9).The growth of absorption in the whole spectral region of 450-850 nm can be related to the fact that the size and concentration of the carbon aggregates increase with rising the calcination temperature.
Raman spectroscopy yields averaged information on the state of the carbon shell in Al 2 O 3 @C samples.The Raman spectra of the Al 2 O 3 @C-1230 samples (Fig. 10) show welldeveloped D at 1350 cm À1 , G at 1587 cm À1 , HWHM G -55 cm À1 , D 0 at 1615 cm À1 and 2D peaks near 2700 cm À1 .These data testify towards the formation of 1-3 monolayers of nanocrystalline graphite (nc-G). 41,42According to the three-stage model of Ferrari and Robertson, 42 I D /I G can be used to estimate the sp 2 -bonded cluster size or in-plane correlation length.From the ratio of D and G peak intensities, the in-plane correlation length of nc-G for Al 2 O 3 @C-1230 is presumed to be about L a $20 Å. 42 The presented data are in a good agreement with the data obtained by other authors for nanocrystalline graphite lms on the sapphire substrates prepared by a molecular beam epitaxy, 43 and via CVD on amorphous Al 2 O 3 substrate 40 synthesized within the same temperature range.The Raman spectra of the Al 2 O 3 @C-1230-700 sample, where carbon accessible to the gas phase was burned off by the calcination in air, is shown in Fig. 10.This spectrum is characterized by the lack of 2D peaks and substantially less intense D and G lines in comparison with the carbon-coated sample, and can be attributed to the nc-G particles (Fig. 6B) encapsulated at the places of contact between the alumina nanoparticles (carbon-alumina interfaces), which, as it was mentioned above, account for the grey color of the samples and absorption observed in the DR UV-vis spectra (Fig. 9).

Conclusions
The effect of carbon coating on the stability of the alumina nanoparticles was investigated.The obtained data demonstrate that the deposited carbon prevents the sintering of the d-Al 2 O 3 nanoparticles and their transformation to corundum accompanied by the particle growth and loss of the specic surface area and the pore volume until the temperature of 1250 C. Without the carbon shell, d-Al 2 O 3 is completely converted to the a-Al 2 O 3 phase aer treatment at 1180 C whereas the treatment at 1380 C is required for the same processes to take place in the case of the carbon-coated material.The stabilization of the particle size by the carbon shell in the Al 2 O 3 @C samples is considered as a main factor preventing their phase transformation to corundum.
Further investigation of the thermal stability and properties of the Al 2 O 3 @C samples heated in an argon ow within a temperature range of 1180-1250 C followed by calcination in air to remove the carbon seems to be of considerable interest.Such samples are characterized by an appearance of the carbon-alumina interfaces, which is connected with the presence of the carbon encapsulated in small amounts at the places of contact between the nanoparticles and preventing their sintering.Such carbon-doped samples appear to have signicantly higher stability with respect to the calcination in the oxygencontaining atmosphere at high temperatures if compare with the initial pure alumina.Note that the active sites on the surface of the alumina in the Al 2 O 3 @C samples are similar to those present on the surface of the pristine Al 2 O 3 .These results  suggest that such samples can be used as the catalyst supports or catalysts to be applied at elevated temperatures.
3. Practically complete conversion to a-Al 2 O 3 (corundum) was observed for the pure Al 2 O 3 sample already at 1180 C. At the same time, no noticeable amounts of corundum were formed in the case of the carbon-coated Al 2 O 3 @C sample even at 1250 C. According to the XRD data presented in Fig. 3, only the d-Al 2 O 3 phase was observed there.

Fig. 1 Fig. 2
Fig. 1 Effect of the calcination temperature on the specific surface area of the Al 2 O 3 and Al 2 O 3 @C samples, and the Al 2 O 3 @C samples calcined at 700 C in air.

Fig. 3
Fig. 3 XRD patterns of Al 2 O 3 and Al 2 O 3 @C samples after calcination at 1180 C, 1250 C and 1380 C for 6 h.Al 2 O 3 samples were calcined in air, whereas Al 2 O 3 @C samples were calcined in argon.

Fig. 4
Fig. 4 Luminescence spectra for the Al 2 O 3 and Al 2 O 3 @C samples calcined in argon at 960 C for 24 h.Prior to the luminescence measurements the carbon coating of the Al 2 O 3 @C sample was removed by calcination in air at 700 C for 6 h.

Fig.
Fig.5The dependence of the corundum phase concentration in the Al 2 O 3 and Al 2 O 3 @C samples, and q-phase in the Al 2 O 3 @C sample estimated from the intensities of R a and R q lines of Cr 3+ ions after excitation in 4 A 2 / 4 T 2 bands (l ex ¼ 514.5 nm).For the Al 2 O 3 @C sample, all the data were multiplied by a factor of 10.

Fig. 6
Fig. 6 HR TEM images of the Al 2 O 3 @C sample after the calcination in argon at 1250 C (Al 2 O 3 @C-1250, A) and further calcination in air at 700 C (Al 2 O 3 @C-1250-700, B).Insertion shows the two-dimensional Fourier-transform from the selected area.

Fig. 9
Fig. 9 DR UV-vis spectra of Al 2 O 3 @C-T-700 samples calcined in argon at 1180 C, 1230 C, 1380 C and 1450 C followed by calcination in air at 700 C. The spectrum of the pristine Al 2 O 3 is shown by the dash line.