Polymorphism of 2-Adamantanone

Philippe Négrier, M. Barrio, M. Romanini, Josep Lluis Tamarit, Denise

Mondieig, A. I. Krivchikov, L. Kepinski, A. Jezowski, D. Szewczyk

► To cite this version:

Philippe Négrier, M. Barrio, M. Romanini, Josep Lluis Tamarit, Denise Mondieig, et al. Polymorphism of 2-Adamantanone. Crystal Growth & Design, 2014, 14 (5), pp.2626-2632. 10.1021/cg500313m. hal-00999243

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<figure><img src="image_1.png" /></figure>
# Polymorphism of 2-adamantanone

P. Negrier¹, M. Barrio², M. Romanini², J. Ll. Tamarit²,*, D. Mondieig¹, A.I. Krivchikov³, L. Kepinski⁴, A. Jezowski⁴, D. Szewczyk⁴

¹ Univ. Bordeaux, LOMA, UMR 5798, F-33400 Talence, France
CNRS, LOMA, UMR 5798, F-33400 Talence, France.

² Grup de Caracterització de Materials, Department de Física i Enginyeria Nuclear, ETSEIB, Diagonal 647, Universitat Politècnica de Catalunya, 08028 Barcelona, Catalonia (Spain)

³ B. Verkin Institute for Low Temperature Physics and Engineering of NAS Ukraine, 47 Lenin Ave., Kharkov 61103, Ukraine

⁴ Institute of Low Temperature and Structure Research, Polish Academy of Sciences, ul. Okólna 2, 50-422 Wrocław, Poland

* josep.lluis.tamarit@upc.edu

## Abstract

The polymorphism of 2-adamantanone (C₁₀H₁₄O) has been investigated by means of X-ray diffraction and high-pressure thermal analysis. The intricate behavior of the low-temperature crystalline phases has been disentangled. The stable phase has been found to be orthorhombic (Cmc2₁, Z=4), fully ordered, with lattice parameters a=6.8884(18) Å, b= 10.830(3) Å, c=10.658(3) Å, V/Z=198.8(1) Å³. The metastable phase was determined to be monoclinic (P2₁/c, Z=4) with lattice parameters a=6.5920(17) Å, b= 11.118(3) Å, c=12.589(3) Å, β= 118.869(11)°, V/Z=202.0(1) Å³. The pressure-temperature phase diagram irrefutably shows the stability relation between both phases and, accordingly, the long-time unknown polymorphic behavior is now revealed and gives coherent physical explanation of the literature published so far.
# 1. Introduction

In the general context of chemical engineering diamondoid molecules is an attractive class of hydrocarbons fully sp³-hybridized formed by three or more rigidly interlocked cyclohexane rings. They have recently received great interest due to their unique structures and their chemical and physical properties making them promising candidates for building blocks for self-assembled processes in a huge number of applications.¹⁻⁶ The main interest is to build up organic crystals with large and dimensionally fixed and tuned cavities giving rise to porous materials with the desired chemical and physical needs.

The pristine and thus the smallest diamondoid molecule is the adamantane, a rigid molecule with point group symmetry $T_d$ formed by 10 carbon atoms arranged as a single diamond cage surrounded by 16 hydrogen atoms.⁷ Despite the rigid molecular skeleton adamantane exhibits a series of thermally induced solid-solid phase transitions before melting that are known to be the consequence of the ability to gain rotational degrees of freedom in the crystalline state (orientationally disordered, OD, phases) mainly due to the little hindrance for reorientational processes associated to its globular shape.⁸,⁹ The OD phase is characterized by long-range positional order, commonly of high symmetry as cubic or hexagonal, whereas the reorientations of molecules take place among a set of distinguishable number of equilibrium orientations. Such a disorder gives rise to high-vapor pressure and low entropy of fusion, in general less than $2.5R$, $R$ the universal gas constant, which is known as Timmermans’ criterium.¹⁰,¹¹

A set of adamantane derivatives can be obtained substituting one or two hydrogen atoms by an atom (Cl, Br, O, ...) or a group of atoms (CN, OH, $CH_3$, $CH_2OH$, $NH_2$, ...) into a tertiary or secondary carbon, given rise to the 1-X- or 2-X-adamantane compounds, respectively. The former give rise to molecules with $C_{3v}$ point group symmetry and both polymorphic behavior as well as dynamic properties have been extensively studied.¹²⁻¹⁸ As for the latter, with $C_{2v}$ symmetry, the literature studies are scarce and, concerning the polymorphic behavior as a function of temperature and pressure, there are some hints but sometimes contradictory.¹⁹⁻³¹
Among the 2-X-adamantane derivatives, 2-O-adamantane (2-adamantanone, C10H14O, hereinafter called 2O-A) has probably been the most studied in the OD phase. The polymorphic behavior of this compound has been described as follows. The OD room temperature phase melts at 529 K and exhibits a face-centered cubic structure (space group Fm$\overline{3}$ m).16,19,27 On cooling the OD phase it transforms at around 178 K to an “ordered” low-temperature phase, which comes back to the OD phase on heating at ca. 205 K.19,20,30,31 A large number of works has been published concerning the orientational disorder of the OD phase, whereas the low-temperature phase was found to be perfectly ordered through NMR studies.19-31 Nevertheless, recent dielectric spectroscopy analyses and X-ray diffraction have shown that a statistical intrinsic disorder concerning the site occupancy of the oxygen atom along different sites giving rise to large-angle molecular rotations associated to time-average fluctuations of the molecular dipole exist.24 As a consequence of such a disorder the dielectric spectra showed the universal features of glass-like materials in which α- and β-relaxation processes appear. Butler et al.19 submitted the 2O-A to a thermal cycling at normal pressure between 150 and 250 K, i.e., around the low-temperature to OD phase transition. As a result, the transition temperature from the low-temperature to the OD phases shifted from 205 till 221 K (see Table 1), which in fact means that a new low-temperature (stable) phase appeared at the expense of the low-temperature (metastable) phase. The authors discarded the usual explanation related to the increase of crystal defects when thermal cycling and proposed the possibility of appearance of new both low- and high-temperature phases. The difficulty of the conversion from the OD FCC phase to the low-temperature stable phase was highlighted by Bazyleva et al.20 through adiabatic calorimetry. After long time annealing, transition temperature on heating was determined to be 216.4 K, close to that obtained by Butler et al. after temperature cycling around the transition.

**Table 1.** Thermodynamic properties of the transitions between stable (s) and metastable (m) phases for 2-adamantanone.
<table><thead><tr><th rowspan="2">Property</th><th colspan="3">Transition</th></tr><tr><th>O<sup>S</sup> → FCC<sup>S</sup></th><th>M<sup>m</sup> → FCC<sup>S</sup></th><th>FCC<sup>S</sup> → L<sup>S</sup></th></tr></thead><tbody><tr><td>T<sub>c</sub>/K</td><td>203.6±1.0</td><td></td><td>557.4±1.0</td></tr><tr><td></td><td>221<sup>a</sup><br>216.4±0.1<sup>c</sup></td><td>205<sup>a</sup><br>-</td><td>557.5±0.2<sup>c</sup></td></tr><tr><td>ΔH / kJ mol<sup>-1</sup></td><td>7.82±0.57<sup>b</sup></td><td>4.59±0.50</td><td>10.4±1.0</td></tr><tr><td></td><td>7.93<sup>a</sup><br>7.627 ±0.014<sup>c</sup></td><td>3.7<sup>a</sup><br>-</td><td>11.77 ± 0.24<sup>c</sup></td></tr><tr><td>ΔS / J mol<sup>-1</sup> K<sup>-1</sup></td><td>22.4±2.4</td><td></td><td></td></tr><tr><td></td><td>35.9<sup>a</sup><br>29.18±0.07<sup>c</sup></td><td>18.0<sup>a</sup><br>-</td><td>21.1±0.4<sup>c</sup></td></tr><tr><td>Δv<sup>RX</sup> (p=0.1MPa) / cm<sup>3</sup> mol<sup>-1</sup></td><td>6.54±0.33</td><td>3.86±0.58</td><td></td></tr><tr><td>Δv<sup>HP</sup> (p=0.1MPa) / cm<sup>3</sup> mol<sup>-1</sup></td><td>6.09±0.43<sup>d</sup></td><td></td><td></td></tr><tr><td>(dT/dp)<sup>exp</sup> / K MPa<sup>-1</sup></td><td>0.181±0.004</td><td>0.171±0.033<sup>b</sup></td><td></td></tr></tbody></table>

The transition between the low-temperature and OD phase has been also revealed by application of pressure at room temperature. Hara et al.²² found that the OD FCC phase reversibly transforms to a tetragonal ordered structure (a=7.15 Å, c=7.82 Å, V= 399.8 Å³) at 8.0±0.5 kbar at 301 K. It should be noticed that the adscription of the new high-pressure phase to the tetragonal system was performed by assuming the similarities with the high-pressure phase of adamantane³² due to the reduced number (only 3) of Bragg peaks and, according to the lattice volume the tetragonal cell should contain 2 molecules. Shortly after Hara et al.²² measured the relative volume as a function of pressure for 2O-A. It is well-known that increasing pressure (or decreasing temperature) gives rise to large hysteresis (4 kbar for the adamantane according to the authors) and thus transition pressure must be assigned when pressure is slowly decreased in order to attain the equilibrium conditions, the authors assigned the transition pressure to the average of the increasing/decreasing experiments. Nevertheless, by reading directly in the ΔV/V vs. P recorded experimental lines of the published work, a pressure of 4.3 kbar at 273 K can be determined. In addition, the authors gave the volume variation along the coexistence curve for a number of states, displaying that such a variation decreases with increasing pressure. A high-pressure Raman study²³ suggested that normal pressure low-temperature phase at 150 K and high-pressure (higher than 6.9 kbar) room temperature are one and the same. The published work emphasized that, as a result of the Raman spectroscopic

<footnote>a From ref. 19; b Calculated from Clauius-Clapeyron; c From ref. 20;</footnote>

<footnote>d Extrapolated from high-pressure values in ref. 22</footnote>
analysis, the high-pressure lattice should contain at least 4 molecules (and not 2
as inferred from the crystallographic study of Hara et al.²²).

In the present paper, the crystal structures of stable and metastable phases of
2O-A are presented, together with the equilibrium pressure-temperature line for
the coexistence between the stable low-temperature and the OD FCC phases to
verify the stability of the involved phases.

**2. Experimental Section**

2.1. *Materials*. 2-O-adamantane was purchased from Aldrich with purity of 99+% and was used without further purification.

## 2.2 Differential Thermal Calorimetry at normal pressure.
Calorimetric measurements at normal pressure were conducted by means of a Q100 thermal analyzer from TA Instruments. Heating and cooling rates of 2 K min⁻¹ and sample masses around 15 mg gathered in Perkin-Elmer high-pressure stainless steel pans were used to avoid spurious signals as a consequence of the deformation of the pans due to the high vapor pressure of material.

2.3. *High-Pressure Differential Thermal Analysis*. High-pressure calorimetric measurements were performed at a heating rate of 2 K min⁻¹ using an in-house built high-pressure differential thermal analyzer similar to Wu□rflinger's apparatus³³ working in the temperature range from 150 K to 473 K and 0 and 300 MPa. To ascertain that in-pan volumes were free from residual air, specimens were mixed with an inert perfluorinated liquid (Galden, from Bioblock Scientifics, Illkirch, France) as a pressure-transmitting medium, and the mixtures were sealed into cylindrical tin pans. Perfluorinated liquid was chemically inactive for 2O-A as demonstrated by DSC measurements carried out on a Galden+2O-A mixture with the TA Instruments Q100 under ordinary conditions.

2.4 *Scanning Electron Microscopy*. Morphology of grains was followed by means of SEM. A cylindrical sample 5 mm-diameter and 12 mm-length was prepared from raw material (grain size was in range 50 – 200 µm) by press. Morphology was examined before and after first cooling down to 77 K and then heating by FE-SEM by using a FEI Nova NanoSEM 230 microscope at room temperature. SEM images were acquired in the low vacuum mode (60 Pa
$H_2O$) using LVD (low vacuum detector) working in SE (secondary electrons) mode with a 3 kV primary electron beam acceleration voltage.

## 2.5 High-resolution X-ray powder diffraction measurements

High-resolution X-ray diffraction patterns were recorded using a horizontally mounted INEL cylindrical position-sensitive detector (CPS120)³⁴ using Debye-Scherrer geometry (angular step ca. 0.029°-2θ over a 2θ-range from 2 to 120°). The system is equipped with a liquid nitrogen 600 series Cryostream Cooler from Oxford Cryosystems with a temperature accuracy of 0.1 K and similar for fluctuations. X-ray profiles were acquired isothermically (no less than 60 min) upon cooling first then heating back so that the temperature range was scanned at intervals of ca. 20 K and less when the transition was approached.

Monochromatic Cu Kα₁ (λ = 1.5406 Å) radiation powered with 1.0 kW (40 kV and 25 mA) was selected. External calibration using the Na₂Ca₂Al₂F₁₄ cubic phase mixed with Silver Behenate was performed by means of cubic spline fittings.

To prevent patterns from possible effects of preferred orientations, samples were introduced into 0.3-mm diameter Lindemann capillaries which were rotated perpendicular to the X-ray beam direction.

Crystal structures have been resolved by using the modules Powder Indexing for cell searching, the Powder Refinement for full profile determination after pseudo-Voigt fittings³⁵ and the module Powder Solve³⁶ of the Materials Studio application.³⁷ Finally, to optimize the crystal structure with the lowest R<sub>wp</sub>, Rietveld refinement was used.

## 3. Experimental Results and Discussion

A capillary with the as-received sample was cooled down to 90 K and X-ray powder diffraction measurements were conducted from 90 to 400 K. Patterns were collected every 20 K until 190 K and every 5 K around the low-temperature to the OD FCC phase transition, which appeared at 205 K as it is demonstrated by the coexistence of both phases at such temperature (Figure 1). The lattice of the low-temperature phase (at T lower than 205 K) was determined by means of X-Cell software, available in the module Powder Indexing of Materials Studio.
Systematic absences enable to determine the space group, which was compatible with *P*2<sub>1</sub>*c* space group. According to a reasonable density, *Z*=4 was assigned. A rigid body molecule was built up by using the cage body obtained for similar adamantane derivatives.<sup>12</sup>

Pawley refinement was carried out using the initial unit-cell parameters in space group *P*2<sub>1</sub>*c*. The unit-cell parameters, zero-point shift, background, peak profile (pseudo-Voigt) and peak asymmetry parameters were refined (see **Table 2**). The constructed molecule was then placed in a general position within the unit cell and the module *Powder Solve* was used to solve the structure. Multiple refinements were performed with oxygen atoms occupying possible positions according to the molecular structure. Those with low values of the refined occupancy factor were successively discarded and, finally the occupancy factors of the three remaining sites gave rise to values close to 25%, 25% and 50%, these being fixed for the next refinements.

In the final Rietveld refinement, the position and orientation of the molecule was refined with the rigid-body constraint, and with a single overall isotropic displacement parameter. All of the profile parameters referred to above were also refined, and preferred orientation was fitted using the Rietveld-Toraya function.<sup>38,39</sup> An example of the experimental and refined patterns is shown in **Figure 1**.

<figure><img src="image_2.png" /></figure>

**Figure 1.** (a) Experimental X-ray diffraction pattern of the OD FCC phase of 2-adamantanone at 205 K with Bragg reflections as vertical sticks. Bottom pattern: Experimental (red circles) and calculated (black line) X-ray diffraction
patterns along with the difference profile (blue line) and Bragg reflections (vertical sticks) for the final Rietveld refinement of *P2*₁/*c* monoclinic (M̂) phase of 2-adamantanone at 190 K. Bragg reflections of the OD FCC phase can be seen coexisting with those of the monoclinic phase. (b) Experimental (red circles) and calculated (black line) X-ray diffraction patterns along with the difference profile (blue line) and Bragg reflections (vertical sticks) of *Cmc*2*₁* orthorhombic phase of 2-adamantanone (at 190 K). Vertical arrows correspond to the position of the Bragg peaks found by Hara et al.²¹ at room temperature and 10 kbar.

The as-received sample was prepared by pressing the powder for scanning electron microscopy. Grain size of the initial as-received sample was in the range 50 – 200 µm and the surface was found uneven and with very irregular grain boundaries (**Figure 2**, left panel). After one cycle between 77 K and room temperature well defined regions with flat surfaces and sharp edges, characteristics for crystalline materials, appear (see **Figure 2**, central panel). After five thermal cycles (**Figure 2**, right panel), the grain sizes are more uniform and clearly defined, so showing the increase of crystallinity. Such a change of the morphology highlights the changes observed by Butler et al.¹⁹ by temperature cycling.

The same experimental protocol was repeated with a sample into a capillary for X-ray diffraction. After ca. 10 cycles, the low-temperature monoclinic phase did not appear and a new pattern emerged (**Figure 2**, right panel). The procedure to determine the structure was similar to that used for the monoclinic form. Nevertheless, in this case, taking into account Z'=0.5, the molecule was placed on the mirror perpendicular to the X-axis reducing the parameters to be found and so final Rietveld refinement was combined with minimization of the lattice energy. Final results are gathered in **Table 2**.
<figure><img src="image_3.png" /></figure>

**Figure 2.** SEM photographs of 2-adamantanone powdered sample before temperature cycling (left panel, magnification of 500), after one cycle between 77 K (central panel, magnification of 500) and room temperature and after five cycles (right panel, magnification of 2500) showing that grain sizes diminish with temperature cycling.

**Table 2.** Results from the Rietveld refinement of the metastable monoclinic (M<sup>m</sup>) and stable orthorhombic (O<sup>s</sup>) low-temperature phases of 2-adamantanone.

<table><tr><td>Chemical Formula</td><td colspan="2">C<sub>10</sub>H<sub>14</sub>O</td></tr><tr><td>M / g·mol<sup>-1</sup></td><td colspan="2">150.2176</td></tr><tr><td>Phase</td><td>M<sup>m</sup></td><td>O<sup>s</sup></td></tr><tr><td>2θ-Angular Range</td><td>10 - 55°</td><td>15 - 80°</td></tr><tr><td>Space group</td><td>P2<sub>1</sub>/c</td><td>Cmc2<sub>1</sub></td></tr><tr><td>a / Å</td><td>6.5920 ± 0.0017</td><td>6.8884 ± 0.0018</td></tr><tr><td>b / Å</td><td>11.118 ± 0.003</td><td>10.830 ± 0.003</td></tr><tr><td>c / Å</td><td>12.589 ± 0.003</td><td>10.658 ± 0.003</td></tr><tr><td>α / °</td><td>90</td><td>90</td></tr><tr><td>β / °</td><td>118.869 ± 0.011</td><td>90</td></tr><tr><td>γ / °</td><td>90</td><td>90</td></tr><tr><td>V/Z / Å<sup>3</sup></td><td>202.0 ± 0.1</td><td>198.8 ± 0.1</td></tr><tr><td>Z (Z')</td><td>4 (1)</td><td>4 (0.5)</td></tr><tr><td>Temperature</td><td>190 K</td><td>190 K</td></tr><tr><td>D<sub>x</sub> / g·cm<sup>-3</sup></td><td>1.235 ± 0.001</td><td>1.255 ± 0.001</td></tr><tr><td>Radiation type: X-Ray, λ</td><td>λ=1.5406 Å</td><td>λ=1.5406 Å</td></tr><tr><td>2θ-shift (zero correction)</td><td>-0.0030 ± 0.0013</td><td>0.0529 ± 0.0029</td></tr><tr><td>Profile Parameters</td><td></td><td></td></tr><tr><td>Na</td><td>0.513 ± 0.008</td><td>0.233 ± 0.010</td></tr><tr><td>Reliability Parameters</td><td></td><td></td></tr><tr><td>R<sub>wp</sub></td><td>3.70%</td><td>4.22%</td></tr><tr><td>R<sub>p</sub></td><td>2.75%</td><td>3.07%</td></tr><tr><td>Peak width parameters</td><td></td><td></td></tr></table>
<table><tbody><tr><td>U</td><td>0.350 ± 0.089</td><td>0.349 ± 0.050</td></tr><tr><td>V</td><td>0.145 ± 0.040</td><td>0.060 ± 0.024</td></tr><tr><td>W</td><td>0.005 ± 0.004</td><td>0.000 ± 0.003</td></tr><tr><td>Overall isotropic<br>temperature factor, U<br>/ Å<sup>2</sup></td><td>0.0622 ± 0.0013</td><td>0.0196 ± 0.0009</td></tr><tr><td colspan="3">Preferred Orientation<br>(Rietveld-Toraya<br>function)</td></tr><tr><td>a*</td><td>0.268 ± 0.023</td><td>-0.555 ± 0.025</td></tr><tr><td>b*</td><td>-0.003 ± 0.076</td><td>-0.240 ± 0.038</td></tr><tr><td>c*</td><td>0.964 ± 0.006</td><td>-0.796 ± 0.020</td></tr><tr><td>G2</td><td>-2.44 ± 0.26</td><td>-7.16 ± 1.31</td></tr><tr><td>G1</td><td>0.773 ± 0.011</td><td>0.712 ± 0.032</td></tr></tbody></table>

After the determination of low-temperature structures, M<sup>m</sup> and O<sup>s</sup>, lattice parameters were measured as a function of temperature for thermal-expansion and volume change at the transition purposes. The site occupancy of the oxygen atoms remains constant for the whole temperature range. The results are plotted in **Figure 3**. Pattern matching refinement was applied to the patterns collected for the OD FCC phase.

<figure><img src="image_4.png" /></figure>

**Figure 3.** Lattice parameters of the low-temperature phases, stable O<sup>s</sup> (left axes, filled symbols) and metastable M<sup>m</sup> (right axes, empty symbols) as a function of temperature
The so-obtained lattice parameters and unit cell volume were fitted by a
standard least-squares method as a function of temperature and the polynomials
describing such a temperature variation are compiled in **Table 3**. The volume
values at each temperature, depicted in **Figure 4**, were used to calculate the
volume change at the $M^m$ and $O^s$ to OD FCC transitions, 6.54 and 3.86 $cm^3$
$mol^{-1}$, respectively (**Table 1**). The last figure shows up that volume changes as
a function of pressure previously determined from Hara et al.²² perfectly match
the value for the $O^s$ to OD FCC transition at normal pressure determined in this
work, which means that the low-temperature phase obtained by increasing the
pressure must correspond to the stable orthorhombic phase. In addition, volume
changes as a function of pressure for the ordered to OD transition follows the
typical variation for such kind of transitions.⁴⁰⁻⁴³

To check once again the stability of the orthorhombic phase, high-pressure
thermal analyses were performed as a function of pressure. **Figure 5a** shows
the obtained pressure-temperature phase diagram for the low-temperature to
OD FCC phase transition. The diagram evidences that application of pressure
stabilizes the orthorhombic phase because the extrapolation at normal pressure
gives the value of 217 K which nicely agrees with the value obtained by
adiabatic calorimetry²⁰ and that obtained by Butler et al.¹⁹ after temperature
cycling. Moreover, the high-pressure value of Hara et al.²² perfectly matches
the equilibrium line determined in this work. Pressure transition at room
temperature obtained by Harvey et al.²³ by means of Raman spectroscopy
(6.9±0.2) kbar for a decompression measurement is certainly far away from our
results. This transition point cannot be associated to the $M^m$ to OD FCC phase
transition because of two reasons: (i) the same authors established that the
high-pressure obtained phase is the same than that obtained at normal pressure
and low-temperature and, (ii) because the equilibrium coexistence line for the
$M^m$ to OD FCC transition is less steeper (0.171 K $MPa^{-1}$) than that of $O^s$ to OD
FCC (0.184 K $MPa^{-1}$), as it can be calculated by Clausius-Clapeyron with the
experimental enthalpy and volume changes for the $M^m$ to OD FCC transition
(see **Table 1**). This fact implies that equilibrium coexistence $M+FCC$ and
$O+FCC$ lines cross at low-temperature and low-pressure (**Figure 5b**) and,
according to Bakhuis Roozeboom,⁴⁴ the $M^m$ phase behaves monotropically for
the whole temperature and pressure space. Several examples of overall
monotropy can be found in the literature.⁴⁵⁻⁴⁹

As far as the tetragonal lattice found by Hara et al.²¹ at 10 kbar throughout
indexing 3 Bragg peaks, the pattern of the orthorhombic phase (Figure 1b)
clearly shows that those peaks match the most intense peaks of the O⁸ phase.

Another irrefutable experimental proof of the stabilization effect of pressure is
obtained by compression and decompression of the monoclinic metastable
phase at temperatures lower than 200 K and heating up at normal pressure.
Following this detour the temperature of the phase transition is found at 217 K,
which corresponds to the O⁸ to OD FCC transition (instead of 203.6 K of the
M⁶M OD FCC transition temperature).

<figure><img src="image_5.png" /></figure>

**Figure 4.** Molar volume for the orthorhombic stable O<sup>s</sup> (filled circles), monoclinic metastable M<sup>m</sup> (empty circles) and OD face-centered cubic phases as a function of temperature from X-ray measurements. Upper inset shows the volume variation as a function of pressure (half-filled circles) from ref. Hara et al.<sup>22</sup> and the volume change at normal pressure (filled circle) obtained in this work. Empty square represents the value for the OD FCC phase from ref. 27.
<figure><img src="image_6.png" /><figcaption>**Figure 5.** (a) Experimental Pressure-Temperature phase diagram for low-temperature orthorhombic (filled circles) to FCC phase transition. Empty circle at normal pressure corresponds to the monoclinic $M^m$ to FCC phase transition (the equilibrium line is shown in grey). The start at high-pressure corresponds to the value read from the volume change as a function of pressure (figure 2 in ref. 22) for the decompression measurement. (b) Topological Temperature-Pressure phase diagram with triple points 1 (O+FCC+vapor), 2 (M+O+ vapor), 3 (M+FCC+ vapor) and 4 (M+O+FCC) according to Bakhuis Roozeboom.⁴⁴</figcaption></figure>

<table><caption>**Table 3.** Polynomial Equations $P = p_0 + p_1T + p_2T^2$ (T in K and p in Å or in deg for $\beta$ parameter) to which the lattice parameters of the monoclinic ($M^m$), orthorhombic ($O^s$) and OD FCC phases were fitted as a function of temperature; R is the Reliability Factor.</caption><thead><tr><th>Phase</th><th>Temperature Range (K)</th><th>Parameter</th><th>p<sub>0</sub></th><th>p<sub>1</sub>·10<sup>3</sup></th><th>p<sub>2</sub>·10<sup>5</sup></th><th>R·10<sup>8</sup></th></tr></thead><tbody><tr><td rowspan="3">M<sup>m</sup></td><td rowspan="3">90-205</td><td>a/Å</td><td>6.527(2)</td><td>-0.04(3)</td><td>0.20(1)</td><td>4.5</td></tr><tr><td>b/Å</td><td>11.006(19)</td><td>0.23(3)</td><td>0.19(1)</td><td>0.4</td></tr><tr><td>c/Å</td><td>12.456(12)</td><td>0.11(1)</td><td>0.31(6)</td><td>1.7</td></tr><tr><td rowspan="3">O<sup>s</sup></td><td rowspan="3">90-215</td><td>β/°</td><td>118.73(8)</td><td>-0.50(1)</td><td>0.65(4)</td><td>0.3</td></tr><tr><td>a/Å</td><td>6.810(1)</td><td>0.355(8)</td><td>-</td><td>15</td></tr><tr><td>b/Å</td><td>10.690(23)</td><td>0.30(3)</td><td>0.17(9)</td><td>5.6</td></tr><tr><td rowspan="2">FCC</td><td rowspan="2">205-400</td><td>c/Å</td><td>10.537(10)</td><td>0.23(1)</td><td>0.16(4)</td><td>1.3</td></tr><tr><td>a/Å</td><td>9.228(7)</td><td>0.80(5)</td><td>0.06(8)</td><td>0.4</td></tr></tbody></table>

From the lattice parameters as a function of temperature the intermolecular interactions can be enhanced throughout the isobaric thermal-expansion
tensor.<sup>43,50,51</sup> It is a symmetrical second-rank tensor, $dU_{ij}=\alpha_{ij}dT$, with non-zero eigenvalues on the diagonal. A small value of a tensor eigenvalue is commonly referred to as a “hard” direction, because it shows up small deformation $dU$ against temperature variation, $dT$, whereas a large value is referred to as “soft” direction because it indicates a large deformation. For a monoclinic lattice the tensor is completely defined by the principal coefficients, $\alpha_1, \alpha_2$, and $\alpha_3$, and an angle between the direction of one of the principal directions ($\alpha_3$, in the present case) and the crystallographic axis **a**, the $\alpha_2$ eigenvector being coincident with the 2-fold axis **b** of the crystal. For orthorhombic systems, eigenvectors are parallel to the mutually perpendicular crystal axes.

<figure><img src="image_7.png" /></figure>

**Figure 6.** Figures (a) and (b) show the thermal-expansion tensors for orthorhombic and monoclinic phases, respectively, at 190 K. (c) The eigenvalues $\alpha_i$ as a function of temperature for the orthorhombic (full symbols) and monoclinic (empty symbols) and the OD FCC (empty diamonds) phases.

**Figure 6** shows the variation of the eigenvalues as a function of temperature for all the phases involved in 2O-A. The $\alpha_1$ direction in the $M^m$ phase, close to the [100] direction, is the soft direction, while the $\alpha_3$ direction is the hard direction. These eigenvectors $\alpha_1$ and $\alpha_3$ lie on the (0k0) monoclinic crystallographic plane (see **Figure 7**). From **Figure 7a** it can also see that the O atoms are related by a rotation of the molecule around a perpendicular axis to **a**, being such an axis close to the $\alpha_3$ direction (30.3°), the hardest direction.
Both monoclinic and orthorhombic structures can be described by stacking planes along the *c*\* direction (see **Figure 8**) as it is evidenced from the *c* and $c\sin\beta$ lattice values for the orthorhombic and monoclinic structures, respectively (**Figure 3**).

As for the orthorhombic structure, the C=O bonds (the dipolar direction of the molecule) are sited in the (100) crystallographic plane and the smaller O···H intermolecular distances are 2.94 Å, larger than the van der Waals radii (1.52 Å and 1.20 Å for O and H, respectively), making the directions $\alpha_2$ and $\alpha_3$ softer. On the contrary, the hardest direction corresponds to [100] crystallographic direction ($\alpha_1$) despite such a direction does not contain dipole-dipole interactions.

The equivalence of the occupancy factors for O1 and O2 atoms has a counterpart concerning the intermolecular interactions. Figure 7b clearly shows that C···O1 (3.12 Å) and C···O2 (3.26 Å) form an square containing the *a* axis and making almost no difference between both distances, and thus interactions, as a consequence of the equal occupancy factor for both O1 and O2 atoms (0.25). Moreover, the distances O1···O2 within the described square are 2.58 and 2.77 Å, which are certainly shorter than O3···O3 (3.05 Å). Such a steric hindrance can give rise to the higher occupational factor for the O3 site when compared to O1 and O2 sites.

<figure><img src="image_8.png" /></figure>
**Figure 7.** Projection of the monoclinic structure on the (0k0) crystallographic plane together with the eigenvectors $\alpha_1$ and $\alpha_3$ (a) and on the (0kl) plane (b). Dotted lines link the O3···O3 (a) and the O1···O1 and O2···O2 atoms (b).

As for the overall volume expansivity, $\alpha_v = \sum_{i=1}^{3} \alpha_i$ (not shown), the metastable monoclinic $M^m$ phase expands more than the stable orthorhombic $O^s$ stable phase (27.8·10⁻⁵ K⁻¹ and 24.3·10⁻⁵ K⁻¹ at 190 K, respectively) as a consequence of the statistical disorder, a fact which is coherent with the highest packing (lower density) of the most stable phase (see **Table 2**).

<figure><img src="image_9.png" /></figure>

**Figure 8.** (0k0) crystallographic planes for the monoclinic (a) and orthorhombic (b) structures.

**5. Conclusions**

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The stable and metastable low-
temperature phases of 2-adamantanone
have been determined by X-ray powder
diffraction as monoclinic (P2₁/c) and
orthorhombic (Cmc2₁), respectively. For
the former, a statistical disorder
concerning the site occupancy of the
oxygen atom has been demonstrated.

<figure><img src="image_10.png" /></figure>