Structure and properties of x SnO–(100 – x) P2O5 glasses

Émilie Bekaert; Lionel Montagne; Laurent Delevoye; Gérard Palavit; Bertrand Revel

doi:10.1016/j.crci.2003.12.012

Structure and properties of x SnO–(100 – x) P₂O₅ glasses

Émilie Bekaert ¹ ; Lionel Montagne ¹ ; Laurent Delevoye ¹ ; Gérard Palavit ¹ ; Bertrand Revel ¹

¹ Laboratoire de cristallochimie et physicochimie du solide, École nationale supérieure de chimie de Lille, BP 108, 59652 Villeneuve-d’Ascq cedex, France

Comptes Rendus. Chimie, Volume 7 (2004) no. 3-4, pp. 377-382.

Résumés

Anglais
Français

x SnO–(100 – x) P₂O₅ glasses (0.30 ≤ x ≤ 0.75) were prepared under argon atmosphere. The Sn²⁺/Sn_total ratio, determined by wet chemical analysis, varies from 90 to 99% depending on glass composition. Glass transition temperatures are very low, and no effect of Sn⁴⁺could be detected. Glass structure was characterised with ³¹P and ¹¹⁹Sn NMR. There is no evidence for a specific Qⁿ site bonded to Sn⁴⁺, but taking into account the amount of Sn⁴⁺ enabled to obtain Qⁿ distribution close to calculated values for binary site distribution. ¹¹⁹Sn NMR spectra were recorded in static conditions. Chemical shift anisotropy (CSA) of glasses were compared to crystalline reference compounds. Tin(II) local environment in glasses is close to a trigonal pyramid, and Sn⁴⁺ NMR parameters are in accordance with a local environment similar to SnP₂O₇. .

Des verres x SnO–(100 – x) P₂O₅ (0,30 ≤ x ≤ 0.75) ont été préparés sous atmosphère d'argon. Le rapport Sn²⁺/Sn_total, mesuré par analyse chimique en solution, varie de 90 à 99%, en fonction de la composition du verre. Les températures de transition vitreuse sont très basses, et aucun effet de Sn⁴⁺ n'a pu être détecté. La structure des verres a été caractérisée par RMN du ³¹P et ¹¹⁹Sn. Il n'y a pas d'évidence pour qu'un site Qⁿ soit spécifiquement lié à Sn⁴⁺, mais la prise en compte de la quantité de Sn⁴⁺ a permis d'obtenir une distribution de sites Qⁿ proche des valeurs calculées pour une distribution binaire. L'anisotropie de déplacement chimique des verres a été comparée à celle de références cristallisées. L'environnement local de Sn(II) dans les verres est proche d'une pyramide trigonale, et les paramètres RMN de Sn⁴⁺ sont en accord avec un environnement local similaire à SnP₂O₇. .

Métadonnées

Reçu le : 2003-05-19
Accepté le : 2003-12-15
Publié le : 2004-03-01

DOI : 10.1016/j.crci.2003.12.012

Keywords: Phosphate glass, Tin–119 NMR, Posphorus-31 NMR
Mots clés : Verre de phosphate, RMN étain–119, RMN phosphore 31

Affiliations des auteurs :

Émilie Bekaert ¹ ; Lionel Montagne ¹ ; Laurent Delevoye ¹ ; Gérard Palavit ¹ ; Bertrand Revel ¹

¹ Laboratoire de cristallochimie et physicochimie du solide, École nationale supérieure de chimie de Lille, BP 108, 59652 Villeneuve-d’Ascq cedex, France

@article{CRCHIM_2004__7_3-4_377_0,
     author = {\'Emilie Bekaert and Lionel Montagne and Laurent Delevoye and G\'erard Palavit and Bertrand Revel},
     title = {Structure and properties of \protect\emph{x} {SnO{\textendash}(100~{\textendash}} \protect\emph{x}) {P\protect\textsubscript{2}O\protect\textsubscript{5}} glasses},
     journal = {Comptes Rendus. Chimie},
     pages = {377--382},
     publisher = {Elsevier},
     volume = {7},
     number = {3-4},
     year = {2004},
     doi = {10.1016/j.crci.2003.12.012},
     language = {en},
}

TY  - JOUR
AU  - Émilie Bekaert
AU  - Lionel Montagne
AU  - Laurent Delevoye
AU  - Gérard Palavit
AU  - Bertrand Revel
TI  - Structure and properties of x SnO–(100 – x) P2O5 glasses
JO  - Comptes Rendus. Chimie
PY  - 2004
SP  - 377
EP  - 382
VL  - 7
IS  - 3-4
PB  - Elsevier
DO  - 10.1016/j.crci.2003.12.012
LA  - en
ID  - CRCHIM_2004__7_3-4_377_0
ER  -

%0 Journal Article
%A Émilie Bekaert
%A Lionel Montagne
%A Laurent Delevoye
%A Gérard Palavit
%A Bertrand Revel
%T Structure and properties of x SnO–(100 – x) P2O5 glasses
%J Comptes Rendus. Chimie
%D 2004
%P 377-382
%V 7
%N 3-4
%I Elsevier
%R 10.1016/j.crci.2003.12.012
%G en
%F CRCHIM_2004__7_3-4_377_0

Émilie Bekaert; Lionel Montagne; Laurent Delevoye; Gérard Palavit; Bertrand Revel. Structure and properties of x SnO–(100 – x) P₂O₅ glasses. Comptes Rendus. Chimie, Volume 7 (2004) no. 3-4, pp. 377-382. doi : 10.1016/j.crci.2003.12.012. https://comptes-rendus.academie-sciences.fr/chimie/articles/10.1016/j.crci.2003.12.012/

Version originale du texte intégral

1 Introduction

During fly ash vitrification processes, heavy metals volatilise and are recovered into chlorinate salts, called secondary ashes [1]. The secondary ashes contain large amounts of chlorinated salts rich in highly soluble and volatile heavy metal chlorides, like lead and cadmium chloride. This is why the treatment of these toxic compounds must involve, in a first step, the conversion of the heavy metals into a thermally stable form [2]. Several processes have been proposed for this conversion. One involves dissolving chlorides in water followed by a precipitate of hydroxides in alkaline medium. The drawback is the handling of brine and energetic cost for eliminating water [3]. Ikeda et al. [4] have studied the thermal conversion reactions of metal chlorides into oxides with boric acid to develop a method for vitrification of radioactive molten salt wastes. But the melting occurred at 1100 °C and volatilisation still occurred at this temperature. We proposed an alternative way using a solid-state conversion of chlorides into phosphates, using ammonium hydrogenphosphate [2]. The reaction leads to the recovery of chlorides as ammonium chloride which sublimates around 300 °C [4], and heavy metals are transformed into non-volatile phosphates that can be vitrified at 900 °C. Tin chlorides are difficult to convert because they are much more volatile than lead and cadmium. Furthermore, Sn²⁺ can oxidise into Sn⁴⁺, which has a low solubility in glasses. It has been reported [5] that stannous chloride (SnCl₂) reacts with ammonium dihydrogenphosphates to form glasses in the SnO–SnCl₂–P₂O₅ system. The conversion of tin chlorides into phosphate using an ammonium phosphate process is efficient [6]. Tin is known to decrease glass transition temperatures of phosphate glasses [7]. However, very little is known about the structure of tin phosphate glasses. Holland et al. reported a NMR study of x SnO–(100 – x) P₂O₅ glasses [8], but did not considered the presence of Sn(IV), since its quantity was expected to be low. Contrary to Holland et al. [8], we paid a special attention to the effect of the redox ratio R = Sn²⁺/Sn_total, on the structure and properties of tin phosphate glasses, because oxidation of Sn²⁺ into Sn⁴⁺ is expected during vitrification of fly ashes. In order to investigate this effect on the structure of phosphate glasses, a series of x SnO–(100 – x) P₂O₅ glasses was synthesised and characterised with ³¹P and ¹¹⁹Sn NMR.

2 Experimental procedures

x SnO–(100 – x) P₂O₅ glasses were prepared from batches of reagent-grade SnO (Aldrich) and (NH₄)₂HPO₄ (Fisher). Each batch was calcined in an alumina crucible at 200 °C to drive off NH₃ and H₂O and was then melted in a carbon crucible at 1000 °C for 2 h under argon.

The glasses were analysed by inductively coupled plasma atomic emission spectrometer (ICP–AES). The [Sn²⁺] concentration was analysed by polarography. The redox R is then calculated as R = Sn²⁺/Sn_total. The redox was also checked with tin Mössbauer on some glass compositions, and found in good agreement with solution measurements.

The glass transition temperature (T_g) was determined using a differential scanning calorimeter. The samples were heated at 5 K min^–1 up to 450 °C. The reported T_g values are reproducible within ±5 K.

The ³¹P MAS-NMR spectra were recorded on a Bruker ASX100 spectrometer operating at 2.34 T, with a 1.5-μs pulse (45°), and a 60-s delay between each accumulation to enable full relaxation. A 7-mm MAS probe was used. The MAS–NMR spectra were decomposed with the DM-FIT software [9]. Gaussian lines were used since ³¹P resonances in glasses are dominated by chemical shift distribution. However, a small Lorentzian contribution (ca 5%) was used to optimise the fits. ³¹P NMR chemical shifts are referenced to an 85% H₃PO₄ solution.

The ¹¹⁹Sn NMR spectra were recorded at 9.4 T on a Bruker AV-400 spectrometer (Larmor frequency 149.1 MHz), with a 2-μs pulse (45°) and a 60-s delay between each accumulation. A 4-mm MAS probe was used, but the spectra were recorded in static condition, since the large CSA of tin, due to its large electronic shielding, cannot be removed by MAS. ¹¹⁹Sn NMR chemical shifts are referenced to liquid Sn(CH₃)₄ (TMT).

3 Results and discussion

Table 1 reports the batch and analysed compositions of x SnO–(100 – x) P₂O₅ glasses. The analysed compositions are very close to the batch ones, meaning that only few losses occurred during melting (excepted for the composition x = 42). In the following text, x always refers to the analysed compositions and to the total Sn content (x = SnO + SnO₂). Table 1 also reports Sn²⁺/Sn_total ratios. Owing to the melting under neutral argon atmosphere, the amount of Sn⁴⁺ is always low. It decreases from 10% for low x values to 1% for the highest Sn content. The solubility of Sn⁴⁺ is known to be very low in glasses [10], but no opacity was detected in the glasses for these Sn⁴⁺ contents.

SnO batch (%mol)	P₂O₅ batch (%mol)	SnO_tot = SnO+SnO₂ (%mol) ± 2	P₂O₅ analysed (%mol) ± 2	Redox Sn²⁺/Sn_tot
75	25	74	26	0.99
72.5	27.5	73	27	0.98
70	30	71	29	0.99
68	32	69	31	0.97
65	35	64	36	0.98
60	40	60	40	0.95
55	45	57	43	0.95
50	50	49	51	0.93
45	55	46	54	0.94
30	70	42	58	0.9

Fig. 1 shows the glass-transition temperatures of x SnO–(100 – x) P₂O₅ glasses. Increasing x does not influence T_g before 60 mol% SnO, and only a small increase in T_g is observed above 60 mol% SnO. This is in accordance with the previously reported effect of SnO on phosphate glass properties [5]. Indeed, tin phosphate glasses are known to exhibit very low T_g values and the reticulating effect on the depolymerised phosphate network is found to be low. This effect is more evident when compared with x ZnO–(100 – x) P₂O₅ and x PbO–(100 – x) P₂O₅ glasses (Fig. 1): for both glass systems, T_g values are much larger (up to 200 K for x ZnO–(100 – x) P₂O₅. Surprisingly, no effect of Sn⁴⁺ is visible on T_g, whereas even small amounts of tetravalent ion like Ti⁴⁺ have a large influence of T_g [11].

Fig. 1
Glass-transition temperatures of RO-phosphate glasses (incertitude is within the size of symbols).

The ³¹P MAS-NMR spectra of x SnO–(100 – x) P₂O₅ glasses are shown in Fig. 2. Broad resonances are observed, in accordance with the chemical shift distribution expected for glasses. However, several resonances, attributed to different Qⁿ sites (n = 3, 2, 1, 0), can be distinguished. The Qⁿ assignment, shown in Fig. 2, is obtained by comparison with spectra of similar glass systems: x ZnO–(100 – x) P₂O₅ [12], x CaO–(100 – x) P₂O₅ [13], and x PbO–(100 – x) P₂O₅ [14]. Q³ sites are located at –43 ppm. Q² and Q¹ sites resonate between –30 and –38 ppm and between –20 and –22 ppm, respectively. The observed shifts with glass composition are attributed to a modification of the bond angle and distance distributions with SnO content in glasses [15]. Indeed, the average chain length decreases when the amount of SnO increases, which influences the bond characteristics. We notice that no specific line can be attributed to Qⁿ sites bonded to Sn⁴⁺. Due to the higher electrostatic field strength of Sn⁴⁺ compared to Sn²⁺ (z/a² = 96 and 38 nm^–2, respectively), Qⁿ sites bonded to Sn⁴⁺ are expected to resonate at higher field than those bonded to Sn²⁺ [11]. This absence of specific resonance may be due either to the small amount of Sn⁴⁺ (signal not detectable), or to an averaged bonding of Qⁿ sites to both Sn²⁺ and Sn⁴⁺ (meaning no specific Qⁿ site for each tin valence). This point will be discussed below.

Fig. 2
(A) ³¹P MAS NMR spectra of x SnO–(100 – x) P₂O₅. (B) Typical fit of ³¹P MAS NMR spectrum of 60 SnO–40 P₂O₅ glass. Continuous line: experimental spectrum, dotted line: calculated spectrum.

The relative amount of Qⁿ sites can be measured by spectral decomposition with Gaussian lines, representative of chemical shift distribution encountered on glass spectra. In a first attempt for quantifying Qⁿ sites, we neglected the contribution of Sn⁴⁺, since its effect is not visible on ³¹P NMR spectra. The fraction of Qⁿ sites was calculated with the assumption of a binary Qⁿ distribution, as generally reported in binary phosphate glasses [11–13].

If only Sn²⁺ is taken into account, the fractions f of the Qⁿ species for ultraphosphate glasses (x < 0.50) is:

{fQ}^{2} = \frac{x}{1 - x}

{fQ}^{3} = \frac{(1 - 2 x)}{1 - x}

The fraction f of the Qⁿ sites for polyphosphate glasses 0.50 ≤ x ≤ 0.67:

{fQ}^{1} = \frac{(2 x - 1)}{1 - x}

{fQ}^{2} = \frac{2 - 3 x}{1 - x}

For glasses with 0.67 ≤ x ≤ 0.75:

{fQ}^{0} = \frac{3 x - 2}{1 - x}

{fQ}^{1} = \frac{(3 - 4 x)}{(1 - x)}

If R = Sn²⁺/Sn_total is taken into account, the total Qⁿ_Sn species for ultraphosphate glasses (x < 0.50) is:

Q_{Sn}^{n} = {fQ}^{3} ({Sn}^{4 +}) + {fQ}^{3} ({Sn}^{2 +}) + {fQ}^{2} ({Sn}^{4 +}) + {fQ}^{2} ({Sn}^{2 +})

The fraction (f) of the Q³ sites for ultraphosphate glasses:

Q_{Sn}^{3} = {fQ}^{3} ({Sn}^{4 +}) + {fQ}^{3} ({Sn}^{2 +})

{fQ}^{3} ({Sn}^{4 +}) = \frac{(1 - 2 (1 - R))}{1 - (1 - R)}

{fQ}^{3} ({Sn}^{2 +}) = \frac{(1 - 2 R)}{1 - R}

The calculation is the same for polyphosphate compositions.

Fig. 3 shows that there is a large discrepancy between calculated and experimental values, meaning that Sn⁴⁺ actually has a large influence on the proportion of Qⁿ distribution. In a second step, the amount of Qⁿ sites bonded to Sn⁴⁺ was included in the Qⁿ site proportion, and the experimental Qⁿ proportions were thus corrected. A further contribution was indeed included in the fits (Fig. 2b), at a chemical shift close to those of Q³ sites (ca. –38 ppm). This small resonance was neglected in the first attempt for quantifying Qⁿ sites, but its presence enables to obtain a better fit, and its small intensity is actually in accordance with the small amount of Sn⁴⁺ in the glasses (Table 1). Fig. 3 shows that the corrected Qⁿ proportions are in very good accordance with the calculated values.

Fig. 3
Qⁿ fractions of x SnO–(100 – x) P₂O₅ glasses versus x (top scale), or versus x′ = SnO + 2 × SnO₂ (bottom scale). Dotted lines: calculated values. Open symbols: experimental values obtained from fitting of NMR spectra, without contribution of Sn⁴⁺. Closed symbols: experimental values obtained from fitting NMR spectra with contribution of Qⁿ sites bonded to Sn⁴⁺(Q(Sn(IV)).

We notice that further information on Qⁿ sites connectivity may have been obtained with double-quantum filtered ³¹P MAS–NMR [12,16], or even better with the recently reported INADEQUATE filter which probes scalar couplings [17]. However, the resolution of Qⁿ sites on our ³¹P MAS–NMR spectra is not enough to obtain separate cross peaks.

Tin NMR spectra are dominated by a very large CSA (Fig. 4), which cannot be removed by magic angle spinning (spectra width is larger than 95 kHz). This behaviour is similar to that observed for ²⁰⁷Pb NMR, although static tin NMR spectra keep a well-defined line shape contrary to ²⁰⁷Pb spectra. The simulation of static spectra enabled to measure the chemical shift anisotropy span (Ω) and to estimate the averaged value of isotropic chemical shift (which takes into account the chemical shift distribution). Unfortunately, there are very few chemical shift data for inorganic tin compounds and even less for tin phosphates. Only three crystalline tin phosphate compounds are known: SnP₂O₇ (Q¹, Sn⁴⁺), Sn₂P₂O₇ (Q¹, Sn²⁺) and Sn₃(PO₄)₂ (Q⁰, Sn²⁺). Curiously, no crystalline tin metaphosphate is known [18]. Moreover, the crystal structure of Sn₂P₂O₇ is not reported. Fig. 5 shows NMR data for these compounds. Some trends can be proposed: by similarity with lead NMR [17] and by examining data in Fig. 5, increasing the covalent character of Sn–O bonds will induce an increase in the CSA span, and a down-field shift of the static line. Fig. 5 illustrates the evolution of CSA span and δ_iso for ¹¹⁹Sn spectra of x SnO–(100 – x) P₂O₅ glasses. The isotropic chemical shifts (δ_iso) reported in Fig. 5 were obtained by recording ¹¹⁹Sn MAS–NMR spectra at a very low field (2.34 T) and a spinning rate of 15 kHz, which enabled to observe isotropic lines resolved from spinning side-bands. They were also estimated by fitting the static spectra recorded at 9.4 T.

Fig. 4
Static ¹¹⁹Sn spectra of x SnO – (100 – x) P₂O₅ glasses.

Fig. 5
Plot of ¹¹⁹Sn NMR data for some crystalline reference compounds and x SnO–(100 – x)P₂O₅ glasses.

When the SnO amount increases in the glass, tin is bonded to less and less polymerised Qⁿ sites (Q² down to Q⁰), meaning that Sn–O bonds become more covalent. This is in accordance with the evolution of CSA span and δ_iso observed in Fig. 5. Moreover, Fig. 5 shows that the spectra of Sn₂P₂O₇ and Sn₃(PO₄)₂ are close to those obtained in glasses, excepted for the lower CSA span of Sn₃(PO₄)₂, due to the absence of distribution. We conclude that in glasses containing a high amount of tin(II), the tin(II) environment should be close to that observed in Sn₃(PO₄)₂, i.e. a trigonal pyramid. The presence of Sn⁴⁺ is detected only on the static tin NMR spectrum of x = 49 glass, probably because of its small amount in the other glasses. Like in silicate and germanate glasses, a narrow resonance near –800 ppm indicates the presence of Sn⁴⁺ with a symmetric environment, generally octahedral in crystalline tin(IV) compounds. We notice that the chemical shift and CSA are close to those obtained in crystalline SnP₂O₇, suggesting that Sn⁴⁺ in the glasses has an octahedral environment similar to that in crystalline SnP₂O₇.

4 Conclusion

Although even small quantities of tetravalent ions have large effects on glass structure and properties, the presence of Sn⁴⁺ in x SnO–(100 – x) P₂O₅ is difficult to detect on ³¹P and ¹¹⁹Sn spectra, as well as on glass transition temperatures. The influence of Sn⁴⁺ becomes visible only for the most oxidised glasses in which the Sn⁴⁺ local environment is close to SnP₂O₇. This suggests that Sn⁴⁺ may segregate as SnP₂O₇ even in non-oxidised tin phosphate glasses.

Acknowledgements

E.B. is grateful to the ADEME for providing a financial support to its thesis work, and A. Kunegel (ADEME, Angers) for its technical support.

Bibliographie

[1] R. Gutmann Glastech. Ber. Glass Sci. Technol., 69 (1996), p. 285

[2] S. Donze; L. Montagne; G. Palavit Chem. Mater., 12 (2000), p. 1921

[3] F. Kraus; R. Meunier Verre, 3 (1997), p. 22

[4] Y. Ikeda; Y. Takashima; H. Kobayashi; H. Igarashi J. Nucl. Technol, 32 (1995), p. 68

[5] Y. Sato; M. Tatsumisago; T. Minami Phys. Chem. Glasses, 38 (1997), p. 285

[6] E. Bekaert, L. Montagne, in preparation.

[7] R. Morena J. Non- Cryst. Solids, 263–264 (2000), p. 382

[8] D. Holland; A.P. Howes; M.E. Smith; A.C. Hannon J. Phys.: Condens. Matter, 14 (2002), p. 13609

[9] D. Massiot; F. Fayon; M. Capron; I. King; S. Le Calvé; B. Alonso; J.O. Durand; B. Bujoli; Z. Gan; G. Hoatson Magn. Res. Chem., 40 (2002), p. 70

[10] R.L. Linnen; M. Pichavant; F. Holtz Geochim. Cosmochim. Acta, 60 (1996), p. 4965

[11] L. Montagne; G. Palavit; A. Shaim; M. Tabirou; P. Hartmann; C. Jaeger J. Non-Cryst. Solids, 293–295 (2001), p. 719

[12] R.K. Brow; D.R. Tallant; S.T. Myers; C.C. Phifer J. Non-Cryst. Solids, 191 (1995), p. 45

[13] R. Witter; P. Hartmann; J. Vogel; C. Jäger Solid-State Nucl. Magn. Reson., 13 (1998), p. 189

[14] F. Fayon, PhD Thesis, University of Orléans, France, 1998.

[15] J.F. Bent; A.C. Hannon; D. Holland; M.M.A. Karim J. Non-Cryst. Solids, 232–234 (1998), p. 300

[16] S. Daviero; L. Montagne; G. Palavit; G. Mairessea; S. Belin; V. Briois J. Phys. Chem. Solids, 64 (2003), p. 253

[17] F. Fayon; G. Le Saout; L. Emsley; D. Massiot Chem. Commun. (Camb.), 3 (2002), p. 1702

[18] A. Durif, Personal communication.

Commentaires - Politique