Introduction
Several industries such as paper and pulp manufacturing units, petroleum refineries, and mining produce acidic wastewater rich in sulfate content. The wastewater generated by such activities seeps through open-pit walls leading to contamination of groundwater. Although sulfate is a non-toxic ion, when present in high concentrations, it corrodes the water transport system (Moosa et al. Reference Moosa, Nemati and Harrison2005). Large sulfate concentrations in drinking water result in a noticeable taste and can lead to illness like diarrhea (Fawell et al. Reference Fawell, Ohanian, Giddings, Toft, Magara and Jackson2004). Removal of sulfate ions from industrial wastewater is essential for recycling water in industry. The anaerobic treatment of sulfate-rich wastewater involves reduction of sulfate to H2S by sulfate reducing bacteria (SRB) (Pol et al. Reference Pol, Lens, Stams and Lettinga1998). H2S is a toxic gas making sulfate removal an acute industrial problem.
An alternative approach to sulfate removal is sorption using a sorbent with a large surface area, anion exchange capacity, and thermodynamic stability. Layered double hydroxides (LDHs) are proven materials for their capacity to sorb as well as to intercalate inorganic and organic anions. LDHs have been used for the removal of toxic anionic species such as CrO4 2−, AsO3 3−/AsO4 3−, and SeO3 2− (Rhee et al. Reference Rhee, Kang, Kim and Moon1997; You et al. Reference You, Zhao and Vance2001; Yang et al. Reference Yang, Shahrivari, Liu, Sahimi and Tsotsis2005; Prasanna et al. Reference Prasanna, Rao and Kamath2006; Prasanna and Kamath Reference Prasanna and Kamath2008). The LDHs belong to two different families: II-III LDHs and I-III LDH based on the charge of the cations. The better known II-III LDHs derived from the mineral brucite, Mg(OH)2, consist of positively charged metal hydroxide layers having the composition [M x (II)M′1–x (III)(OH)2] x+ with anions and water molecules [(A n–) x/n ·yH2O] intercalated in the interlayer region (Cavani et al. Reference Cavani, Trifirò and Vaccari1991). The I-III LDH is derived from Al(OH)3. Al(OH)3 is composed of charge-neutral layers with the composition [Al2/3□1/3(OH)2] (□: cation vacancy). Imbibition of Li+ ions into the cation vacancies of the Al(OH)3 layers results in positively charged layers of composition [Al2/3Li1/3(OH)2]1/3+. Anions and water molecules [(A n– )1/3n ·yH2O] are intercalated in the interlayer region for charge neutrality and stability (Serna et al. Reference Serna, Rendon and Iglesias1982). The LDH containing Li and Al is the only system reported in this family and is abbreviated herein as [Li-Al-X] (X = NO3 −, CO3 2−, Cl−, or Br−). The [Li-Al-X] LDHs are unique in exhibiting shape selective anion intercalation (Fogg et al. Reference Fogg, Green, Harvey and O'Hare1999). Structure refinement of LDHs containing different anions is a first step towards understanding the mechanism of sorption reactions employed for environmental amelioration.
A survey of the reported structures of [Li-Al] LDHs indicates that they all contain the same iono-covalently bonded metal hydroxide layer (layer group
) (Britto and Kamath Reference Britto and Kamath2011). The reported structures differ from one another in (i) the manner in which the metal hydroxide layers are stacked, and/or (ii) the packing of atoms in the interlayer region. The stacking of the metal hydroxide layers could be orthogonal, leading to polytypes of hexagonal and rhombohedral symmetries (Fogg et al. Reference Fogg, Freij and Parkinson2002). The stacking of metal hydroxide layers could be non-orthogonal leading to polytypes of monoclinic symmetry (Britto and Kamath Reference Britto and Kamath2009). The intercalated Cl− ions exhibit positional disorder in the interlayer region (Besserguenev et al. Reference Besserguenev, Fogg, Francis, Price, O'Hare, Isupov and Tolochko1997). The position of the Br− ion depends on the degree of hydration, and is influenced by the ambient relative humidity (Nagendran and Kamath Reference Nagendran and Kamath2013). Intercalated OH− ions induce disorder in the stacking of the metal hydroxide layers (Thiel et al. Reference Thiel, Chiang and Poeppelmeier1993). Stacking disorders arise due to the random intergrowth of different polytypes (Britto and Kamath Reference Britto and Kamath2012), and manifest themselves in the broadening of reflections arising from select crystal planes (Britto et al. Reference Britto, Thomas, Kamath and Kannan2008). The packing of polyatomic oxoanions is further complicated by changes in the orientation of the anions at different degrees of hydration. The intercalated NO3
− ion not only changes its orientation but also generates an incommensurate phase upon hydration (Nagendran et al. Reference Nagendran, Periyasamy and Kamath2016, Reference Nagendran, Periyasamy and Kamath2018).
Intercalation of the sulfate ion in [Li-Al] LDH is interesting for many reasons:
(1) The sulfate ion has a large hydration enthalpy (Smith Reference Smith1977) and has the capacity to extend its hydration in the interlayer region to a higher degree than the nitrate ion.
(2) The free SO4 2− ion is of T d symmetry, and can potentially intercalate with any one of its axes of rotation – C 4, C 3, or C 2 – parallel to the stacking direction.
The main objective of this work was to obtain structure models that best describe the packing of sulfate ions and intercalated water molecules in the interlayer region of [Li-Al] LDHs. One of the cardinal features of clay-like materials is their ability to swell by taking in water molecules from their surroundings. A secondary objective was to investigate if [Li-Al-SO4] LDH exhibits a reversible expansion of the interlayer region as a function of the ambient relative humidity, and thereby establish the crystal chemistry underlying the swelling phenomenon.
Experimental Section
Bayerite-Al(OH)3 (60.2% Al2O3 content) was synthesized as described elsewhere by precipitation by the addition of NH3 to AlCl3 (Merck Life Science Pvt. Ltd., Mumbai, India) solution (Poeppelmeier and Hwu Reference Poeppelmeier and Hwu1987). Gibbsite-Al(OH)3 (64.1% Al2O3 content) was provided by the Jawaharlal Nehru Aluminium Research Development and Design Centre (Nagpur, India). The [Li-Al-SO4] LDHs were prepared by suspending ~0.5 g of bayerite or gibbsite in a Teflon-lined autoclave containing ~2 M Li2SO4 (10 mL) solution (>99%, SISCO Research Laboratories Pvt. Ltd., Mumbai, India) followed by hydrothermal treatment at 180°C for 24 h. The resulting precipitate was thereafter centrifuged, washed 3–4 times with Type II water (specific resistance 15 MΩ cm, Millipore Academic water purification system, Molsheim, France), and dried in an air oven at 65°C. The samples were stored in air-tight screw cap bottles without desiccation.
The Li+ contents were estimated by flame photometry (Elico, Hyderabad, India), SO4 2− contents by ion chromatography (Metrohm Model 861 Advanced Compact Ion Chromatograph fitted with a Metrosep SUP 5150 column, Herisau, Switzerland), Al3+ contents by gravimetry, and intercalated H2O contents by thermogravimetry (Mettler Toledo, TG/SDTA Model 851e system, Schwerzenbach, Switzerland; 30–900°C, heating rate 5°C/min, flowing air) in g-[Li-Al-SO4] and b-[Li-Al-SO4] LDHs (g: gibbsite-derived; b: bayerite-derived).
A Bruker D8 Advance diffractometer (Karlsruhe, Germany) (Cu Kα radiation, λ = 1.5418 Å) operating in reflection geometry mode was used to characterize the samples. In situ X-ray powder diffraction (XRPD) measurements at different temperatures (30–120°C) and relative humidity (RH) values (60–90%) were performed using an Anton Paar CHC plus humidity chamber (Graz, Austria) as an attachment. The XRPD patterns were recorded over the 5–100°2θ range with a step size of 0.02°2θ (counting time 10 s step−1). The XRPD patterns were indexed, and the lattice parameters refined using the APPLEMAN code built into the PROSZKI suite (Łasocha and Lewinski Reference Łasocha and Lewinski1994). The DIFFaX code (Treacy et al. Reference Treacy, Newsam and Deem1991, Reference Treacy, Deem and Newsam2005) was used to simulate the XRPD patterns to identify the relationship between the successive layers in the LDH. Within the DIFFaX formalism, a single metal hydroxide layer extracted from the published structure of g-[Li-Al-Cl] LDH was identified as a structural synthon, and used for all the simulations. All the symmetry-related atoms corresponding to the metal hydroxide layer within the unit mesh were explicitly used as input. The metal hydroxide layers were stacked one above another by using different stacking vectors. The Laue symmetry was declared UNKNOWN to enable code DIFFaX to compute the Laue symmetry. The DIFFaX code computes the diffraction intensity for an infinite stacking by integrating the intensity emerging from each layer. A Lorentzian profile function with FWHM = 0.2°2θ was used to broaden the Bragg reflections in the simulated XRPD patterns. The XRPD patterns simulated using different stacking vectors were compared with the experimental XRPD patterns to identify the corresponding polytypes. Once the polytype was identified, the structure and orientation of metal hydroxide layers were used as a partial structure model for refinement. The position and orientation of the intercalated sulfate ions was determined using code FOX (Favre-Nicolin and Černý 2002) in the absence of prior knowledge of the interlayer structure. The SO4 2− ions and water molecules were inserted into the interlayer region and allowed to translate and rotate randomly. After each step, the XRPD pattern was computed and compared with the observed pattern. A Monte Carlo approach was employed for structure optimization using R wp (wp: weighted profile) and R p (p: profile) (Larson and Von Dreele Reference Larson and Von Dreele2004) as the cost functions. This process amounts to structure optimization in direct space and yields an approximate structure model. The model was exported to the GSAS code (Soediono Reference Soediono1989) to complete the structure refinement in reciprocal space in the conventional manner.
Results and Discussion
Two polymorphic modifications of Al(OH)3, namely bayerite (Rothbauer et al. Reference Rothbauer, Zlgan and O'daniel1967) and gibbsite (Megaw Reference Megaw1934), are well known, and are used as precursors for the synthesis of I-III LDHs. Both gibbsite and bayerite crystallize in monoclinic symmetry and contain the same metal hydroxide layer, which is designated by the symbol Ρ. Bayerite is obtained by stacking the layers in the sequence ···ΡΡΡ···. Gibbsite is obtained by the stacking sequence ···
···, where
is the mirror image of Ρ. Consequently, gibbsite is a two-layer polytype (space group P121/n1, a = 8.676 Å, b = 5.070 Å, c = 9.721 Å, β = 94.57°) (Saalfeld and Wedde Reference Saalfeld and Wedde1974) and bayerite is a one-layer polytype (P121/a1, a = 5.062 Å, b = 8.671 Å, c = 4.713 Å, β = 90.27°) (Rothbauer et al. Reference Rothbauer, Zlgan and O'daniel1967) (see Supporting Information [SI, Fig. S1], Supplemental Materials Section, deposited with the Editor in Chief and available (Supplementary material)).
Fig. 1 TGA (continuous line) and DTG (dashed line) data of the as-prepared (a) b-[Li-Al-SO4], and (b) g-[Li-Al-SO4] LDHs
Gibbsite-derived g-[Li-Al-X] LDHs (X = Cl, Br, and NO3) have been studied widely and shown to crystallize as two-layer polytypes. Bayerite-derived b-[Li-Al-X] LDHs (X = Cl, Br) are less well known and are shown to crystallize as one-layer polytypes.
Compositional analysis
Hydrothermal treatment of both gibbsite and bayerite in a concentrated aqueous solution of Li2SO4 yielded white powder samples, which were readily soluble in mineral acids. Flame photometry analysis of an acid solution of both samples showed the presence of Li+ (Table 1), indicating the success of the imbibition reaction. SO4 2− content estimated independently by ion chromatography matched stoichiometrically the Li+ ion content in the b-[Li-Al-SO4] LDHs (observed [Li+]/[SO4 2−] = 1.96, ideal value = 2). The Al3+ content obtained gravimetrically yielded a ratio of [Li+]/[Al3+] = 0.47 (ideal value = 0.5). The TGA plot (Fig. 1) showed three distinct mass-loss steps with inflections at 120°C (step I), 250°C (step II), and 340°C (step III). The mass of the residue obtained at 800°C was ~55.7%. As the sulfate ion does not volatilize at this temperature in air, the residue comprised Li2SO4 + 2Al2O3. The mass observed at 250°C (75.3%) corresponds to dehydrated LDH having the formula [Li2Al4(OH)12](SO4), suggesting that step III was due to dehydroxylation. The mass-loss observed in the temperature range 30–250°C (~25%) was due to loss of adsorbed water (step I, 14%, 30–120°C) and intercalated water (step II, 11%, 120–250°C), respectively. A combination of these results yielded an empirical formula for LDH (Table 1) which could be approximated as [Li2Al4(OH)12]SO4·4.44H2O.
Table 1 Results of compositional analysis
*Unreacted Al(OH)3 observed in the experimental pattern of G-II and G-III
Values in the parenthesis were calculated from the approximate composition
A similar approach to arrive at the composition of the g-[Li-Al-SO4] LDH suffered certain limitations primarily due to the presence of small quantities of unreacted gibbsite. The Al3+ content was overestimated. The SO4 2− content was, therefore, taken as the lead indicator of the LDH composition and Al3+ observed in excess over the stoichiometric requirement ([Al3+]/[SO4 2−] = 4) was assigned to the unreacted Al(OH)3. A combination of independent analyses yielded a ratio [Li+]/[SO4 2−] = 1.76 (ideal value = 2) and [Li+]/[Al3+] = 0.44 (ideal value = 0.5) (Table 1). The TGA curve (Fig. 1) showed a three-step mass-loss over the temperature range 30–900°C. The mass of the residue obtained was 55.2% and was due to Li2SO4 + 2.13Al2O3. Assigning the three steps to loss of adsorbed water (14.8%), intercalated water (10.3%), and dehydroxylation (19.1%) yielded an empirical formula [Li0.44Al(OH)3][SO4]0.25·1.23H2O (Table 1). Structure refinement was carried out using the ideal value [Li+]/[Al3+] = 0.5 for the purpose of electroneutrality. The departure of the observed composition from the ideal composition was deemed to be negligible from a powder diffraction point of view.
Structure of the g-[Li-Al-SO4] LDH
The as-prepared LDH (denoted G-I) yielded an XRPD pattern (Fig. S2) with two intense reflections in the low-angle region at 10°2θ (8.84 Å) and 20°2θ (4.44 Å), respectively, followed by numerous weak and broad undulations in the 25–55°2θ region. These features are typical of layered solids with turbostratic disorder. In such crystals, periodicity is observed only along the stacking direction leading to intense and sharp basal reflections. A close look at the first basal reflection (inset in Fig. S2) showed a distinct asymmetry on the high-angle side, along with a split in the second basal reflection, showing that the as-prepared sample comprised LDH motifs with different basal spacings. Basal spacing differences arise due to differences in the degree of hydration. Such materials are prone to undergo temperature- and humidity-driven transitions that result in pure polytypes.
G-I was heated to different temperatures and at 100°C corresponding to the first inflection point in the TGA curve (Fig. 1), a phase G-II with an XRPD pattern comprising sharp and well defined peaks (Fig. S3a) was obtained. The pattern could be indexed to a two-layer cell (polytype 2H) with a = b = 5.0944 Å, c = 17.1592 Å (Table S1). Numerous structure models are available for the 2H polytype in which the metal hydroxide layers follow the ···
··· stacking sequence, typical of the gibbsite precursor. A DIFFaX simulation (Fig. S3b) of the XRPD pattern using the metal hydroxide layers obtained from the structure of the g-[Li-Al-Cl] LDH reported earlier (Nagendran and Kamath Reference Nagendran and Kamath2013) generated all the observed reflections confirming the Ρ···
interlayer relationship. The Ρ···
interlayer relationship generates the space group P63/m in this LDH system. In the absence of a precedent for the structure of the interlayer sulfate in this family of LDHs, metal hydroxide layers were used as a partial structure model, and FOX code was employed to determine the possible positions of the SO4
2− ions and water molecules in the interlayer region. To this end, the SO4
2− ion was introduced as a molecule along with an oxygen atom (Ow1, for intercalated water) into the interlayer. The two species were allowed to translate randomly. The SO4
2− ion was also randomly rotated. During the optimization process, the structure was periodically visualized for any unrealistic variations in the bond length and bond angle values. When the S atom of the SO4
2− was confined to a plane midway between the metal hydroxide layers, a stable structure optimization was obtained (R wp = 0.173; R p = 0.106).
To complete the structure refinement in the reciprocal lattice, the structure model obtained from code FOX was exported into code GSAS. The non-structural parameters were refined initially. Difference Fourier maps were generated to find the positions of additional intercalated water molecules. Successive difference Fourier maps indicated the presence of water molecules at 4e (0, 0, 0.1767) (Ow2), and 2a (0, 0, 0.25) (Ow3) sites. These sites are proximal to the Li+ ion 2b (0, 0, 0) showing a strong interaction of the intercalated water molecules with the Li+ ion in the metal hydroxide layer. The cumulative occupancy of Ow1, Ow2, and Ow3 atoms was found to be 12% lower than the water content expected from the TGA at 100°C. At this stage, the electron density reflected in the difference Fourier plots was fully accounted for. To improve the fit under the second basal reflection, an orientation parameter was introduced along [002] to complete the fit (Fig. 2, Table 2). Water molecule Ow1 occupies a general site 12i (x, y, z), while Ow2 and Ow3 obtained in the later stages of refinement occupy special positions (Table S2), thus infusing confidence in the refinement process.
Fig. 2 Rietveld fit of the in situ XRPD pattern of g-[Li-Al-SO4] (T = 100°C). The excluded region corresponds to the reflection of unreacted gibbsite
Table 2 Results of rietveld refinement of the structures of [Li-Al-SO4] LDHs
The S atom of the intercalated SO4 2− ion occupies a special position of high degeneracy (6h) proximal to the Al3+ ion. The SO4 2− ion is oriented with its two-fold axis parallel to the crystallographic c axis (Fig. 3) (CCDC No. 1852882). If the crystallographic c axis is treated as the principal axis, then the symmetry of the sulfate is reduced to D 2d upon intercalation. In this orientation, only two oxygen atoms (O2 and O3) of the sulfate ion hydrogen bond with the metal hydroxide layer at distances that range from 2.39 to 2.94 Å (Table S3). Oxygen atoms (O2 and O5) of the SO4 2− ion hydrogen bond strongly with the water molecules with O---O bond distances in the range 2.41–2.75 Å. The contact distance between the O atoms of intercalated water molecules and the hydroxyl O (O1) of the metal hydroxide layer is in the range 2.82–3.87 Å, indicative of a much weaker interaction.
Fig. 3 (a) Structure of g-[Li-Al-SO4] (T = 100 °C) viewed along the b axis, and (b) the asymmetric unit
On cooling and rehydration (Relative Humidity 70%), G-II transformed into a new phase G-III with a basal spacing of 10.6 Å (Fig. 4). An expansion of the basal spacing by nearly 2 Å is due to the ingress of water molecules from the vapor phase. The increased basal spacing includes an interlayer region of ~91 Å3 volume equivalent to ~8.3 water molecules. Given that structure refinement of G-II yields approximately three water molecules in the immediate vicinity of the SO4 2− ion, the additional five molecules of H2O in G-III are in the second coordination sphere of the SO4 2− ion. The presence of such a massive amount of water results in turbostratic disorder, and all hkl reflections are obliterated. The XRPD pattern is dominated by 00 l (l = 1, 2, 3, 4) reflections. In the absence of any meaningful structural information, it is instructive to examine the results of molecular dynamics (MD) simulation studies (Chen et al. Reference Chen, Zhu, Lu, Zhu and He2018) on a related cation-ordered system. The water molecules are shown to coordinate with both hydroxyl ions and intercalated sulfate ions in a cooperative manner.
Fig. 4 XRPD pattern of g-[Li-Al-SO4] obtained in situ at RH = 70%. The reflection marked by the asterisk is due to the 002 plane of the unreacted gibbsite. Inset shows the saw-tooth line shape of reflections arising due to turbostratic disorder
In conclusion, the results show that the as-prepared gibbsite-derived LDH exhibits basal-spacing dynamics involving a reversible variation of the basal spacing by nearly 2 Å as a function of the relative humidity. When excess water was removed the LDH adopted the structure of a two-layer hexagonal polytype. On hydration, the ingress of water molecules from the vapor phase introduced turbostratic disorder in the stacking of the metal hydroxide layers.
Structure of the b-[Li-Al-SO4] LDH
The as-prepared LDH derived from bayerite (denoted B-I) yielded an XRPD pattern (Fig. S4a) with basal reflections at 10°2θ (8.85 Å) and 20.24°2θ (4.39 Å). The first basal reflection has a shoulder on the low-angle side suggesting the existence of motifs with different degrees of hydration. As a consequence, the reflections in the mid-2θ region (25–55°2θ) are broad and few in number, indicating disorder. No structural information could be deduced from this pattern. The sample was investigated for temperature- and humidity-induced structural ordering.
When B-I was heated to 120°C, i.e. the first inflection point in the TGA curve (Fig. 1), a new phase (B-II) with basal reflections at 10.3°2θ (8.59 Å) and 20.6°2θ (4.31 Å) was obtained (Fig. S4b). A broad hump was seen on the higher-angle side of the second basal reflection. When B-II was cooled and rehydrated (RH 70%), an expansion of the basal spacing by ~2 Å (phase B-III) was observed (Fig. S4c). In the first instance, the layer-to-layer relationship was determined using DIFFaX simulations. The XRPD pattern of B-II could be simulated by stacking the metal hydroxide layer (Ρ) using the stacking vector (2/3, 0, 1) (Fig. S5). This stacking vector also generated three Bragg reflections on the higher-angle side of the second basal reflection, showing that the hump observed in the 22–25°2θ region is structural in origin. The XRPD pattern of B-II was indexed to a cell of monoclinic symmetry (Table S1, a = 5.0925 Å; b = 8.8211 Å, c = 8.7612 Å, β = 101.2°) corresponding to a one-layer polytype (polytype 1M). Angle β corresponds to the non-orthogonal stacking direction. A satisfactory LeBail fit to the space group C2/m could be secured in keeping with suggestions from earlier work (Nagendran and Kamath Reference Nagendran and Kamath2017). The metal hydroxide layer extracted from the structure of b-[Li-Al-Br] LDH was used as a partial structure model for structure refinement. The positions of the SO4 2− ion and one intercalated water molecule were obtained from the FOX code. The SO4 2− ion was restricted to a plane mid-way in the interlayer region. The resulting structure model was input into the code GSAS and a series of difference Fourier plots was obtained at different stages of the refinement process. Additional water molecules (Ow2, Ow3) were added at 4i (0.1567, 0, 0.4678) and 4h (0, 0.231, 0.5) sites. The position of Ow1 indicated by the FOX code is a general 8j (0.4506, 0.1105, 0.4837) site. Ow2 and Ow3 determined later were found to occupy special positions (Table S2). The occupancies of the Ow1, Ow2, and Ow3 water molecules were both individually and cumulatively refined. The suggested total water content in the interlayer was 11% less than that indicated by TGA data. Nevertheless, the final Rietveld fit (Fig. 5, Table 2) is quite satisfactory. The resulting structure (Fig. 6) showed that the C 3 axis of the intercalated SO4 2− ion is tilted away from the crystallographic c axis (CCDC No. 1852881).
Fig. 5 Rietveld fit of the in situ XRPD pattern of b-[Li-Al-SO4] (T = 120°C)
Fig. 6 (a) Structure of b-[Li-Al-SO4] (T = 120°C) viewed along the b axis, and (b) the asymmetric unit
Phase B-III obtained on cooling and rehydration showed an XRPD pattern with the following characteristics (Fig. S4c): (i) three basal reflections were observed, (ii) a saw-tooth shaped reflection appeared at ~20°2θ, and (iii) reflections in the 35–65°2θ region were considerably broadened. The XRPD pattern simulated using stacking vector (0, 0, 1) (polytype 1H) generated all the reflections observed in the 30–60°2θ region with some mismatch in the intensities and peak shapes between the observed and computed reflections (Fig. 7). The saw-tooth reflection in the observed pattern covered the range of 2θ values wherein the 100 and 110 reflections appear in the 1H polytype. This kind of asymmetric broadening of the hk0 reflections, also called Warren broadening (Warren and Bodenstein Reference Warren and Bodenstein1966), is attributed to turbostratic disorder. The latter is an extreme model of planar faults, wherein the iono-covalently bonded layers are stacked regularly, but are randomly rotated about the stacking direction. A full profile simulation of the observed pattern could not be secured, but critical portions of the profile spanning 18–24°2θ and 38–60°2θ could be simulated (Fig. 8) using a multiplicity of stacking vectors in different proportions: 30% (1/7, 0, 1); 20% (6/7, 0, 1); 30% [(1/7 + 1/3), 2/3, 1], and 20% [(6/7 + 1/3), 2/3, 1]. These stacking vectors were selected on the basis of the structural synthon approach, which is more fully described elsewhere (Britto and Kamath Reference Britto and Kamath2011). According to this approach, stacking vectors of the type (1/n, 0, 1) and (1–1/n, 0, 1) yielded a pair of “enantiomorphic” polytypes of monoclinic symmetry. The stacking vector (1/3, 2/3, 1) generated a crystal of rhombohedral symmetry. A vector sum of the two families of stacking vectors yielded a faulted crystal with random intergrowths of rhombohedral and monoclinic motifs. MD simulation studies of hydrated LDHs also predicted intergrowth of rhombohedral and monoclinic polytypes (Chen et al. Reference Chen, Zhu, Lu, Zhu and He2018), and the observations reported here provide experimental evidence for the simulations.
Fig. 7 (a) XRPD pattern of b-[Li-Al-SO4] obtained in situ (RH = 70%) compared to (b) XRPD pattern simulated for ···ΡΡΡ··· stacking using (0, 0, 1) stacking vector. In the inset, the mid-°2θ region (38–57°2θ) of the observed and the simulated XRPD pattern is expanded to show the mismatch in the positions of reflections. The rectangular box highlights the asymmetric peak shape in the observed XRPD pattern when compared with that simulated
Fig. 8 Simulation of the of the XRPD pattern of b-[Li-Al-SO4] obtained in situ (RH = 70%) by incorporating 30% (1/7, 0, z) + 20% (6/7, 0, z) + 30% [(1/7 + 1/3), 2/3, z] + 20% [(6/7 + 1/3), 2/3, z]. The black trace corresponds to the observed, and the red trace corresponds to that simulated. The first and the second basal reflections are not shown, and the Bragg reflection marked with asterisk corresponds to the third-order basal reflection. The circle and the rectangular box highlight the good match between observed and simulated XRPD patterns in both the low-angle (5–30°2θ) and the mid-°2θ region (38–60°2θ)
To conclude this section, the b-[Li-Al-SO4] LDH precipitated with the sulfate ions in an incomplete hydration sphere. Long-range order was ill defined. On heating, the crystal ordered itself and adopted the structure of a one-layer polytype having monoclinic symmetry. On hydration, an expansion occurred in the interlayer region. The resultant weakening in the layer–interlayer interaction resulted in a crystal replete with stacking disorders, wherein the local symmetry of the faulted regions was either rhombohedral or monoclinic.
The approach adopted in this study has two limitations.
(1) The water content suggested by structure refinement of both G-II and B-II was less than that obtained from TGA data. The inconsistency is due to (i) the propensity of the LDHs to exchange their intercalated water with the ambient humidity, and (ii) the incidence of stacking disorders, which distort the XRPD profile.
(2) The full-profile simulation of the XRPD patterns was not realized as only the metal hydroxide layers were used in all the DIFFaX simulations. The determination of the positions of the intercalated atoms in a faulted structure is beyond the scope of this work.
Conclusions
Lithium sulfate imbibition into both bayerite and gibbsite led to the formation of poorly ordered SO4 2−-intercalated LDHs. Partial dehydration resulted in ordered structures. The gibbsite-derived phase had a structure different from that of the bayerite-derived phase. Structure refinement provided structure models, which showed that the sulfate ions form hydrogen bonds with the intercalated water molecules as well as with the hydroxyl ions. Increased humidity caused the ingress of water molecules from the ambient environment into the interlayer region, and resulted in a reversible expansion of the basal spacing. Expansion of the basal spacing provides the crystal-chemical basis for the swelling of the LDH, and its clay-like character.
Acknowledgments
The authors are grateful to the Department of Science and Technology (DST), Government of India, for financial support. L.P. is a recipient of support under the Women Scientists (WOS-A) Scheme of the DST.
