Introduction

Black glasses are ceramic materials where some part of O2− ions are exchanged for C4− ones. Therefore, these materials feature both SiO2 and SiC bonds. This leads to the strengthening of glass structure and enhancement of its properties, i.e., chemical, thermal, and oxidation resistance [1,2,3,4]. Two main concepts of silicon oxycarbide structures exist. First one states that free carbon phase is distributed inside SiO2 glassy matrix, while the second one states that amorphous silica is closed inside graphite/graphene network [5, 6]. In our previous work, we tried to describe the formation of free carbon phase in silicon oxycarbide glasses pyrolized at temperature ranging from 200 to 800 °C [7]. Many routs can be employed to achieve black glasses [7,8,9,10]. Depending on desired outcome—final product properties, a variety of preceramic materials with different function groups can be used—like methyl, ethyl, and vinyl [11,12,13,14]. Changing the precursor can lead to formation of different black glasses, e.g., materials with or without free carbon phase [5, 7, 15, 35]. From the variety of possible applications, at least few should be mentioned, i.e., anodes for Li-ion batteries [16], material for artificial heart valves [17], and protective coatings [4]. Most of the research focuses on two temperature ranges used to obtain SiOC glasses—below 400 °C for low-k thin layers and above 1000 °C, where phase separations occurs [4, 10]. In our work we focus on obtaining fully amorphous silicon oxycarbide materials that can be obtained below 1000 °C.

Aim of this work is to track, with the usage of TG and MIR studies, the formation of black glasses obtained from methyl terminated ladder-like silsesquioxanes of different Si/O/C ratios.

Experimental

The MTES–CH3Si(OCH3)3 (T units) and DMDES–((CH3)2Si(OC2H5)2) (D units) were used as a silsesquioxane precursors [11, 22, 23]. Three mixtures of T/D = 1/1, 2/1, and 4/1 were synthesized according to the procedure described in our previous papers [7, 18, 35]. To obtain glassy SiCxOy, dried samples (xerogels) were subsequently heat-treated in a tube furnace at 200, 400, 600, 800, and 1000 °C temperature ranges under flowing argon atmosphere. To ensure oxygen-free environment, titanium shavings were used inside the furnace during pyrolysis process.

The middle infrared spectroscopy (MIR) studies were carried out to determine the structure of obtained materials. Standard KBr pallet method was used, and 128 scans were accumulated with resolution of 4 cm−1 in the range of 4000–400 cm−1 using Bruker VERTEX 70v spectrometer.

Thermogravimetric (TG) analysis was performed by the use of a Hi-Res TGA 2950 thermogravimetric analyzer (TA Instruments) in argon atmosphere (heating rate 5 K min−1, resolution 3, sensitivity 3).

SEM with EDX studies were carried out using FEI Europe Company Nova Nano SEM 200 with EDAX EDX attachment.

X-ray powder diffraction measurements were done using Philips PANalytical X’Pert PRO MPD diffractometer. Cu Kα1 line was used as radiation source and monochromatized by Ge (111) monochromator. Standard Bragg–Brentano geometry with Θ–2 Θ setup was applied.

Results and discussion

Total mass loss, which can be determined as finished at about 1000 °C for all tested samples, is setting out as expected by the authors. With increase in number of D units within set mixtures, the thermogravimetric curve changes as well (Fig. 1). The least mass loss is observed for the least amount of D units, mix T/D = 4/1, while the most is registered for T/D = 1/1 mix (Table 1).

Fig. 1
figure 1

Thermogravimetric and first derivative (dTG) curves of analyzed T/D mixtures

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Table 1 Mass loss during pyrolysis of T/D mixtures
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Most likely this is because that with increase in the number of D groups that are responsible for terminating ladder-like silsesquioxanes, obtained structures are getting shorter—lesser degree of condensation [19]. XRD studies seem to confirm this assumption. It is typical to receive two amorphous “halo” on diffraction patterns of ladder-like silsesquioxane samples (Fig. 2) [7, 8, 18]. Their presence, along with the conducted MIR studies (Figs. 4–6, samples A0, B0, C0), indicates well-defined ladder structure [20, 38]. Silsesquioxane ladders, with their limited degree of order, especially with the chain-to-chain (intramolecular chain) distance give intensive reflection visible in the XRD pattern at approx. 10° 2Θ (Fig. 2). Second halo, the broad one, can be attributed to intermolecular distance (intermolecular chain-to-chain thickness), or it can be the distance between the ladder structures [20, 38, 39]. In the case of xerogel T/D = 1/1, first halo (approx. 10°) is poorly visible and has completely different shape and intensity from the rest of xerogels. This probably is due to the weaker ordering structure of this xerogel—the silsesquioxane ladders are shorter and disordered.

Fig. 2
figure 2

XRD patterns of obtained T/D mixtures

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The first mass loss in the TG curve (Fig. 1) is observed at a temperature of approx. 200 °C. With the decrease in the content of D units in the material, stronger shift toward higher temperatures are being observed (approx. 235 °C for T/D = 4/1). It can be attributed to the release of cyclic D-oligomers that formed during the synthesis of ladder-like silsesquioxanes as a by-product. In addition, a mass loss associated with the release of residual solvent and EtOH/H2O from ongoing polycondensation reaction should be observed at this temperature [11, 14, 21, 44]. High impact on loss of mass in this area is the number of D groups in the starting xerogel—it increases with the quantity (Fig. 1). Two less significant mass losses are observed for T/D = 2/1 sample at approx. 330 and 410 °C. Minor mass loss at approx. 300 °C (290 °C for 1/1, 340 °C for 2/1 and 350 °C for 4/1) most likely corresponds to elimination of branched T/D-oligomers formed during the synthesis [19, 21, 22]. Next loss is registered at 410 and 440 °C for 2/1 and 1/1 mix accordingly. It is responsible for the release of cyclic D-oligomers [19, 22,23,24,25]. Two high peaks on dTG curve for T/D = 2/1 sample at approx. 580 °C can be linked with the process of depolymerization of short D chains [22], but authors think that its evenly possible for the sample to pop out of the platinum crucible during thermal analysis. It must be noted that crucibles were not sealed during the analysis process. It seems highly plausible because samples fired in temperatures exceeding 500 °C are characterized by drastically increased volume compared to starting xerogel volume (especially for T/D = 2/1 mixture). It was observed for both partially fragmented and bulk samples. This implies rapid release of high amount of gases. It is peculiar in a way that we have not observed such extreme effect in the case of other T/D mixtures. It can probably be attributed to the evolution of H2 and CH4 from the starting polymer—glass transition process [11, 19, 26]. Mass loss at approx. 600–700 °C can be assigned to further evolution of D units and gases originating from redistribution reaction of Si–O/Si–C bondings [19, 21,22,23,24,25, 44]. Release of T units (oligomers), which based on TG and dTG curves is rising along the decrease in terminal D groups, should still be present in this temperature range [22, 23]. At approx. 1000 °C, no more mass loss is being observed.

SEM with EDX confirmed presence of Si, C, and O atoms in tested samples (Fig. 3). Chemical formulas were calculated for all the T/D mixtures at room temperature (xerogel) and after pyrolysis at 800 and 1000 °C (Table 2). During the heating process amount of carbon is decreasing more rapidly the more D unites are introduced into xerogel. T/D = 2/1 sample burned at 1000 °C is the closest to the stoichiometric composition. This confirms TG observations concerning the behavior of D terminal units.

Fig. 3
figure 3

SEM images and EDX spectra of T/D = 1/1, A T/D = 2/1, B and T/D = 4/1, C samples—a xerogel, samples pyrolyzed at b 800 °C and c 1000 °C

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Table 2 Chemical formula of tested T/D mixtures after curing and pyrolysis in 800 and 1000 °C
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Structural studies in the middle infrared range (MIR) were conducted for all the T/D mixtures (Figs. 4–6). For the purpose of infrared studies, samples were named accordingly to notation: T/D = 1/1(A), 2/1(B) and 4/1(C)—xerogel (A, B, C)0, 200 °C (A, B, C)1, 400 °C (A, B, C)2, 600 °C (A, B, C)3, 800 °C (A, B, C)4, 1000 °C (A, B, C)5 (Figs. 4–6). All three xerogels have very similar spectra. Bands responsible for CH vibrations are very well visible on the xerogel spectra—Si–(CH3)x bending vibrations are visible at 750–860 cm−1 range, and the Si–CH3 and Si–C2H5 stretching vibrations are visible at 1273 cm−1 (vs) and 1413 cm−1(va) along with stretching vibrations of C–H groups at 2971 (va) and 2913 cm−1(va) [7,8,9, 18, 20, 28, 29, 33, 34, 43, 45]. For A0 sample also 2800 cm−1 (vs) C–H band is visible [7, 28, 30]. The Si–OH stretching bands at 3600–3800 cm−1 along with approx. 900 cm−1 bending vibration is visible, and therefore it can be concluded that the polycondensation process is not finished and the material will undergo further changes more easily during pyrolysis [7, 8, 18]. At approx. 1000–1200 cm−1 two bands are visible. The first one can be attributed to va vibrations of Si–O–Si (bridging) vibrations of ladder-like structure, while the other at around 1100 cm−1 is responsible for cage-like vibrations in ring-like structures of Si–O–Si ladder [7, 28, 30, 32, 34, 36, 37]. The vs vibration of Si–O–Si bridges is visible in the range of approx. 550 cm−1 [7, 8]. The Si–C3 vibration from the Si–CH3 molecules can be observed at 700 cm−1 [21, 27, 30]. Based on the XRD analysis (Fig. 2), MIR studies, and theoretical calculations [40], it can be stated that obtained xerogels contain ladder-like silsesquioxane structures. As the temperature rises, materials start to undergo a series of changes. First one, at 200 °C, is attributed to ongoing polycondensation reaction and release of water during this process, which can be seen as a broad band at approx. 3400 cm−1 on the A1 and C1 spectra (not visible for B1 sample). In addition the CH groups are becoming more intense and can suggest that more D-oligomers are being formed during this step. Samples burned at 400 °C (A, B, C2) exhibit gradual loss of all types of CH bands. Also water and OH bands are less visible. It is also worth to mention that during this step intensity of Si–O–Si band at 1100 cm−1 decreases, while the 440 cm−1 (Si–O bending mode) is starting to be more visible [18]. This confirms that during this step T/D-oligomers and D-oligomers, which are not involved into creation of glass structure, are being evaporated from the tested samples [19, 21]. Similar situation is being observed for the samples fired at 600 °C. Broadening of the Si–O–Si range and constant loss of intensity of 1100 cm−1 band indicates that the polymer to glass transition start to take place [7, 19, 21]. Additional OH groups that appear for A3 and B3 sample suggest that not all of volatile moistures are removed from the material and that the reorganization of the structure is still ongoing. Our previous studies showed that after pyrolysis at 800 °C obtained materials are black glasses [7, 8, 35] and look very similar. All three spectra contain a large band at 3410 and 1630 cm−1 which is attributed to the water present in the samples. If we compare these bands to 1040 cm−1 one, it is clearly visible that this ratio is lowest for A4 and highest for B4 sample. This is probably due to the high porosity of those samples (Fig. 7) and lack of hydrophobic CH3 groups (Figs. 4–6). Literature data state that a band at 1900 cm−1 can be a combinational band or a residual bonding of –C≡C– specimen [41, 42]. Bands at 2050 and 2230 cm−1 can be attributed to the Si–H stretching vibrations (SiCSi–H and O3Si–H groups) [30, 31, 34]. A, B, C5 samples (fired at 1000 °C) are much alike. Main band region at around 1040 cm−1 assigned to Si–O–Si asymmetric stretching vibrations (bridges) is a bit sharper compared to samples burned at 800 °C. Small bands at 3410 and 1630 cm−1 remain but their presence can be attributed to both humidity in KBr and/or remnants of porosity and its absorbed water.

Fig. 4
figure 4

MIR spectra of T/D = 1/1 samples A0–xerogel, A1–A5 pyrolized at 200, 400, 600 and 1000 °C

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Fig. 5
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MIR spectra of T/D = 2/1 samples B0–xerogel, B1–B5 pyrolized at 200, 400, 600 and 1000 °C

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Fig. 6
figure 6

MIR spectra of T/D = 4/1 samples C0–xerogel, C1–C5 pyrolized at 200, 400, 600 and 1000 °C

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Fig. 7
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SEM image of bulk T/D = 1/1 sample after pyrolysis in 800 °C (A4 sample)

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Conclusions

The aim of this work was to describe thermal evolution of different T/D mixtures. Spectra recorded using MIR spectroscopy match the changes in TG curves for the tested samples. With the increase in amount of D units introduced into xerogel structure dTG peaks shift to lower temperatures. This effect, the temperature shift of the decomposition of ladder-like structure, is also observed on the MIR spectra of all the mixtures. Furthermore, each T/D mixture has its own dominant mechanism responsible for the mass loss. As it was described, despite the differences in TG curves and MIR spectra during heating process, final material—black glass—was achieved at 800 °C for all the tested mixtures.