Calcium orthophosphates (CaPs) are important in geology, biomineralization, animal metabolism and biomedicine, and constitute a structurally and chemically diverse class of minerals. In the case of dicalcium phosphates, ever since brushite (CaHPO4·2H2O, dicalcium phosphate dihydrate, DCPD) and monetite (CaHPO4, dicalcium phosphate, DCP) were first described in 19th century, the form with intermediary chemical formula CaHPO4·H2O (dicalcium phosphate monohydrate, DCPM) has remained elusive. Here, we report the synthesis and crystal structure determination of DCPM. This form of CaP is found to crystallize from amorphous calcium hydrogen phosphate (ACHP) in water-poor environments. The crystal structure of DCPM is determined to show a layered structure with a monoclinic symmetry. DCPM is metastable in water, but can be stabilized by organics, and has a higher alkalinity than DCP and DCPD. This study serves as an inspiration for the future exploration of DCPM’s potential role in biomineralization, or biomedical applications.
Calcium orthophosphates (CaPs) are common and important in geological and biological systems1, constituting a family of compounds with varying Ca/P atomic ratios and structural water contents. Important members are hydroxyapatite (Ca10(PO4)6(OH)2)2, octacalcium phosphate (Ca8H2(PO4)6·5H2O)3, brushite (CaHPO4·2H2O)4, monetite (CaHPO4)5, and tricalcium phosphate (Ca3(PO4)2)6,7. Amorphous calcium phosphates (ACPs) have different chemical formulae, and can be the precursors of various crystalline CaPs8,9,10,11,12,13, including hydroxyapatite, in vivo14,15,16,17,18,19,20. However, the role of ACPs in biomineralization has been debated21,22,23,24,25. CaPs are involved in hard tissue formation and the metabolism of humans and animals, whereas they can also form pathologically13,26.
Due to their chemical composition being similar to that of hard tissues, high biocompatibility and bioactivity, synthetic CaPs have been extensively studied for uses in biomedicine, for example, as coatings of metallic implants and synthetic substitutes for bone repair27. Since X-ray crystallography was developed in the early 20th century28,29, the structures of all known CaPs were resolved in the course of that century, while some CaPs were discovered for the first time even earlier7. Despite their structural and chemical variability, however, no further crystalline form of CaP has been found lately. Until now, two different forms of crystalline CaPs with a Ca/P atomic ratio of 1:1 have been documented: CaHPO4·2H2O (brushite; dicalcium phosphate dihydrate, DCPD) and CaHPO4 (monetite; dicalcium phosphate, DCP), both playing important roles in geology4,5 and biology30,31. In DCPD, structural water molecules link layers composed of CaHPO4 via hydrogen bonds, whereas DCP is anhydrous and the structure is not layered32,33 (see below). These differences give rise to rather distinct chemical and physical properties for the two forms34,35. DCP and DCPD are both useful in biomedical applications, especially for the curing of calcium phosphate cements in clinical orthopedics. However, DCPD seems to provide generally better performance in real uses, as it exists in the majority of setting products36,37.
Metastable CaPs with structural water are thus promising for advancing biomedical applications. In this work, we introduce another crystalline form of CaP: dicalcium phosphate monohydrate (DCPM, CaHPO4·H2O). Due to its layered nature and structural water content, advantageous properties for applications within the biomedical field are anticipated. Also, it might play an important role as an intermediate in CaP biomineralization.
Preparation and characterization of DCPM
Amorphous calcium hydrogen phosphate (ACHP), with a Ca/P atomic ratio of 1.038, which is identical to that of DCPM, was used as a precursor for the crystallization of DCPM (see Methods section for details). The amorphous character of its precursor was confirmed by X-ray powder diffraction (XRPD), transmission electron microscopy (TEM), and electron diffraction (ED) (Supplementary Fig. 1). In water-poor environments, that is, mixtures of methanol and water, or in humid air, ACHP transforms into DCPM (see Methods section for details). Large crystals of DCPM, sufficient for single-crystal X-ray diffraction (SCXRD, see Fig. 1b and Supplementary Fig. 2 for typical morphologies), could unfortunately not be obtained. However, ED provides a tool to overcome this issue, as the strong interactions between electrons and matter allow diffraction data to be obtained from crystals that are much smaller than in the case of X-rays. Indeed, recently, single-crystal electron diffraction (SCED) methods have proven to be invaluable for the structure determination of sub-micrometer-sized crystals for a wide range of compounds39,40,41,42,43,44,45,46. Three-dimensional SCED data were collected for DCPM by continuously rotating a crystal in the electron beam of a transmission electron microscope while collecting a series of selected-area electron-diffraction patterns, the so-called continuous Rotation Electron Diffraction technique (cRED), Fig. 1. This procedure was aided by sequential defocusing of the intermediate lens of the TEM in order to confirm the position of the crystal in the beam47. The reconstructed three-dimensional reciprocal lattice was successfully indexed using a monoclinic unit cell (space group P21/c, Fig. 1, Supplementary Figs. 3 and 4, and Supplementary Comment Section). Ab-initio structure determination revealed a layered structure with one unique calcium and one phosphate ion in the asymmetric unit constituting DCPM, while the location of the hydrogen atom on the phosphate could not be determined from this data alone. In addition, one water molecule per calcium and phosphate ion was found, consistent with its chemical formula, which was further confirmed by thermogravimetric analysis (TGA) (Supplementary Fig. 5). Although the SCED data contained diffuse scattered lines, indicating layered disorder (see Fig. 1d and Supplementary Fig. 6), least-squares refinement converged with a residual of 0.260 (see Supplementary Table 1 for details). So as to improve the confidence in the structural model of DCPM obtained by SCED further, and to show that it is representative for the bulk of our sample, Rietveld refinement of XRPD data converged with a Rwp of 6.67% (Supplementary Fig. 7, Supplementary Table 2). This yielded a monoclinic unit cell for DCPM with a = 8.0063(4) Å, b = 6.7954(5) Å, c = 7.7904(5) Å, α = γ = 90°, β = 91.548(4)°. Due to uncertainties in unit cell parameters as determined from ED data, all refinements were performed using the unit cell from XRPD data. The structure of DCPM refined against cRED and XRPD data shows only minor changes with an average difference in atomic positions of 0.16 Å and maximum difference of 0.25 Å. The coordination environment around Ca and P is the same for the structures after the two refinements, see Supplementary Figs. 8 and 9.
In order to further define the structural characteristics of DCPM, first principles quantum mechanical calculations were performed (see Methods section for full details). Hydrogen atoms were inserted into the structure for a variety of different initial positions for both the HPO42− ions and water, followed by geometry optimization and annealing via molecular dynamics. A consistent picture emerges in which two chains of hydrogen bonded HPO42− anions run parallel to the b axis, with the OH groups pointing in opposite directions in each chain. Attempts to transfer the proton along the chain (i.e., from OH…O to O…HO) led to spontaneous return of the hydrogen to its initial site, indicating a strong preference for the original order. Water coordinates to one calcium ion via oxygen and is simultaneously able to hydrogen bond to two different anions. All hydrogen positions are commensurate with the space group without the need for partial occupancy or disorder (see Supplementary Fig. 8).
The unit cell parameters of DCPM differ from those of DCPD (monoclinic; a = 5.812 Å, b = 15.180 Å, c = 6.239 Å, α = γ = 90°, β = 116.42°) and DCP (triclinic; a = 6.910 Å, b = 6.627 Å, c = 6.998 Å, α = 96.34°, β = 103.82°, γ = 88.33°). Consistently, also the atomic structures of CaHPO4·xH2O, with x = 0, 1, and 2 for DCP, DCPM, and DCPD, respectively, differ significantly (Fig. 2). Although both DCPM and DCPD contain water molecules located between the layers, the atomic arrangements within each layer of the two structures are different. The structural differences of the three CaPs were further confirmed by XRPD patterns and infrared (IR) spectra (Fig. 3). Regarding the vibrational modes of the HPO42− ion (Fig. 3b) in the three forms, the ν6, and ν6’ bands share similar wavenumbers (~1126 cm−1 and ~1060 cm−1, respectively), while those of ν2, ν3, and ν4 bands differ (DCPM: 1001 cm−1 for ν2; 901 and 887 cm−1 for ν3; 551 and 533 cm−1 for ν4); the split ν3 band in the spectrum of DCPM also contrasts DCPD and DCP. Lastly, the H1–H4 bands, which can be assigned to two crystallographically distinct waters in DCPD, are not seen in the spectrum of DCPM. The pattern of the OH stretching modes is further supported by quantum mechanical calculations, which yield two groups of four IR-active modes each for DCPD in the ranges 3477–3429 and 3253–3146 cm−1, whereas DCPM only has a single group of four active modes between 3402 and 3364 cm−1 consistent with the experimental spectra (Fig. 3b). A structural comparison of DCPM with other CaPs is summarized in Supplementary Table 3.
DCPM was previously neither observed during the dehydration of DCPD49,50 nor the hydration of DCP in H2O51,52. We also failed to obtain DCPM from other amorphous calcium phosphates (with Ca/P atomic ratios higher than 1.0). This indicates that ACHP is an essential precursor for the crystallization of DCPM. Although prepared by ACHP transforming in mixtures of methanol and water, DCPM is an intermediate phase between ACHP and DCP. As shown in Supplementary Fig. 10, DCPM can be formed as early as 2 min, and kept for 7 h. But after 24 h, while minor fractions of DCPM can still be detected by IR spectroscopy and XRPD, the majority phase became DCP.
Crystals of DCPM also formed via crystallization of ACHP in humid air (humidity 95%, 25 °C) during the transformation of ACHP to DCPD (as opposed to DCP that formed in mixed solvent as discussed above). Under these conditions, DCPM was the majority phase of the transformation of ACHP after 4 h (whereas two reflections were indicative of a DCPD impurity). ED of the as-obtained samples confirmed that the structure was identical to those prepared by the mixed water/methanol approach (Supplementary Fig. 11). This identity was evident by comparing the corresponding XRPD patterns and IR spectra of the DCPM from the distinct preparations (Supplementary Figs. 12 and 13). However, DCPM that crystallized from methanol/water mixtures exhibited a higher crystallinity as the broad feature of ACHP in the XRPD pattern was significantly reduced (Supplementary Fig. 12). After treating ACHP for 12 h in humid air, DCPD formed (alongside impurities of OCP, Fig. 4a). That the crystallization of ACHP in humid air progressed via DCPM to DCPD after 4 h and 12 h was corroborated by IR spectroscopy (Fig. 4b). TEM analysis (Fig. 4c) revealed corresponding morphological changes, where the spherical aggregates of the precursor ACHP yielded platelet-like DCPM without obvious elongations after 4 h, alongside some un-crystallized ACHP nanoparticles. After 12 h (Fig. 4c), typical elongated platelets of DCPD with well-defined edges had formed. H2O is required for the crystallization of DCPM from ACHP, as the amorphous precursor did indeed not crystallize in dry air (humidity < 5%, Methods section) for at least 1 month. The presence of too much water will lead to crystallization yielding other phases such as DCPD38.
Properties of DCPM
In water, DCPM was stable for at least 0.5 h, but transformed into poorly crystallized HAP within 1 h (Fig. 5a), which is the main biomineral component of human bones and teeth. In contrast, DCP and DCPD did not transform within 2 h (Supplementary Fig. 14), although they will ultimately yield more stable CaPs52. Organics, such as citrate salts, which are abundant in vivo and biocompatible53 can effectively stabilize DCPM for at least 2 h (Fig. 5a); polyelectrolytes such as sodium polyacrylate (NaPAA) can stabilize it for even longer times, i.e., at least 13 h (Fig. 5a). Notably, upon initial dissolution, the pH of the DCPM solution can reach a value of 8.2 before DCPM transforms (Fig. 5b), which is the highest of the three forms (DCP, DCPM, and DCPD). The comparably high pH in relation to the aqueous chemistry of the different protonation states of the phosphate anions upon HPO42− dissolution indicated that DCPM has the highest solubility among the three CaPs. Support for this comes from theoretical calculations (see Supplementary Table 4), which indicate that formation of DCPM from monetite is as endergonic as formation of brushite, though the latter has twice as much water. A brief comparison of DCPM with other CaPs in terms of chemical properties is compiled in Supplementary Table 5. It is also interesting that DCPM exhibited a significantly higher adsorption capacity for some organic molecules compared to DCP and DCPD, e.g., methyl blue, congo red, doxorubicin hydrochloride (anti-cancer drug), and ibuprofen (analgesic drug) (Supplementary Table S6). This higher adsorption capacity, in combination with the biocompatibility shown in Supplementary Fig. 15, points toward a significant potential use of DCPM for improving drug delivery carriers or pollution treatment materials. In their totality, in any case, these properties highlight that DCPM is a material that may significantly improve or extend current in vivo applications of CaPs.
In conclusion, the CaP family has been expanded by DCPM, exhibiting a unique crystallographic structure. Considering the important biological role of CaPs and their wide use in biomedicine, it seems highly promising to study and explore the potential use of DCPM in biomedical applications. Last, but not least, it should be carefully investigated to confirm whether or not DCPM occurs (transiently) in geological or biological natural contexts, e.g., biomineralization.
DCPM was obtained either via transformation of ACHP in mixed solvents of methanol and deionized water or in humid air.
Na3PO4·12H2O and Na2HPO4 were purchased from Sigma-Aldrich; methanol, ethanol, DCPD and CaCl2 were purchased from Sinopharm Chemical Reagent Co.; sodium polyacrylate (NaPAA, 50% solution, Mw 3000–5000) was purchased from Aladdin Reagent. All chemicals were used as received without further purification. All of the chemicals were of analytical grade. DCP was prepared by heating DCPD at 195 °C for 1 h and was confirmed by XRPD. Deionized water was used in all experiments.
Preparation of ACHP
At ambient temperature (ca. 25 °C), Na2HPO4 (0.95 mmol) and Na3PO4·12H2O (0.05 mmol) was dissolved in 3 mL deionized water, then quickly added into 2 mL CaCl2 (1.67 mmol) aqueous solution under vigorous stirring. Immediately, the white product of ACHP was formed in the solvent. After 3 s, 80 mL methanol was added to quench the reaction. Then, ACHP was separated from the solvent by centrifugation, washed with methanol 3 times, and dried in a vacuum desiccator. The ACHP obtained has a Ca/P atomic ratio of 1.02, formula CaHPO4·H2O, confirmed by inductively-coupled plasma optical emmission spectroscopy (ICP-OES) and TGA. Its amorphous character was confirmed by XRPD and ED (Supplementary Fig. 1).
Preparation of DCPM in a water-methanol mixed solvent
Typically, the ACHP obtained as described above was quenched in 32.5 mL methanol (not 80 mL), and kept in the solvent (that is, 32.5 mL methanol + 5.0 mL water) which was placed in an oscillating incubator (XZQ-X160, Suzhou Peiying) at constant temperature (90 rpm, 25 °C) for 20 min. Afterwards, the resulting product was centrifuged and washed with ethanol 3 times, and dried in a vacuum desiccator to obtain DCPM. To prevent its transformation, DCPM can be stored in dry (humidity < 5%) or cold (<−20 °C) environments.
Preparation of DCPM in humid air
Following the procedure for ACHP preparation, the dried ACHP was incubated for a specified period of time (as indicated below) at 25 °C and 95% humidity with air blowing in a temperature humidity chamber (HWS-080, Shanghai Jinghong). During the first 4 h, the ACHP was stirred with a glass stick for 10 s after every 20 min to ensure that the ACHP contacted the humid air more uniformly.
The stability of ACHP in dried air
Five gram CaCl2 powder was sealed in a beaker to create a dried air atmosphere (humidity < 5%), alongside a powder of ACHP (0.050 g) that was kept for 1 month. After the ACHP was again taken out, XRPD patterns showed no apparent reflections indicative of crystallization.
Transformation of DCPM in water
10.0 mg freshly prepared DCPM was placed in a centrifuge tube containing 20 mL deionized water (25 °C). Afterwards, it was kept in an oscillating incubator (XZQ-X160, Suzhou Peiying) for specified times at constant temperature (150 rpm, 25 °C). Then the samples were isolated by centrifugation, washed with ethanol 3 times, and dried in a vacuum desiccator.
In order to study the ability of citrate salts stabilizing DCPM, 15.0 mg trisodium citrate dihydrate was dissolved in water before adding DCPM, while the other conditions remained unchanged.
In order to study the ability of NaPAA towards stabilizing DCPM, 23 mg NaPAA was dissolved in water before adding DCPM (pH adjusted to 7.0 using 1:10 hydrochloric acid), while the other conditions described above remained unchanged.
So as to investigate the pH changes during DCPM transformation in water, 10.0 mg freshly prepared DCPM was dispersed in 20 mL deionized water. Under vigorous stirring and maintaining the temperature at 25 °C, a pH meter (A 600, Asone) was used for real-time monitoring of the pH development in the solution.
DCP and DCPD were used as the controls with the same experimental conditions as DCPM.
Adsorption capacity of DCPM for organics
Methyl blue, congo red, doxorubicin hydrochloride (anti-cancer drug) and ibuprofen (analgesic drug) were used to study the adsorption capacities of DCPM. Briefly, at 25 °C, 10.0 mg DCPM was dispersed in water, methanol or ethanol with 2.0 mg mL−1 organics (doxorubicin 1.0 mg mL−1), and then placed in an oscillating incubator at constant temperature (150 rpm, 25 °C). The incubation was performed for 30 min (aqueous solution) or 2 h (methanol or ethanol solution) so as to adsorb organics on DCPM without phase transformation. Afterwards, the samples were isolated by centrifugation. The concentration of the organic molecules in the supernatant was measured with a UV-Vis spectrophotometer (UV2300II, Techcomp). As the detection of ibuprofen in ethanol solution is problematic, 1 mL of the supernatant was dried in vacuum, then re-dissolved in the same volume of hexane for the UV-vis measurement. The wavelengths for the determination of the concentrations of methyl blue in water, methyl blue in methanol, congo red, doxorubicin hydrochloride and ibuprofen were 596 nm, 591 nm, 501 nm, 495 nm, and 220 nm, respectively. DCP and DCPD were used as the controls with the same experimental procedure.
Sprague-Dawley (SD) rat bone marrow mesenchymal stem cells (rBMSCs) were kindly provided by Stem Cell Bank, Chinese Academy of Sciences, catalog number: SCSP-402. Samples of DCP, DCPM and DCPD dispersed in ethanol were added into 24-well plates. After drying and sterilizing by UV, rBMSCs in 1 mL culture medium was added for co-incubation (0.5 × 105 cells/well) at 37 °C. After a certain time, the culture medium was removed, and 1 mL fresh medium containing 10% Cell Counting Kit-8 (CCK-8; Dojindo) solution was added to each well. After further incubating for 2 h, 100 µL solution from each well was transferred to a 96-well plate. The absorbance of the sample was measured with a microplate reader (BioRad 680, USA) at 450 nm to determine the cell viability. The cell incubated without samples was used as the control.
TEM micrographs were obtained on a Zeiss Libra 120 operated at 120 kV. Samples were dispersed in ethanol, then a drop of the dispersion was added onto a carbon-coated Cu grid. The TEM analyses were performed immediately after drying.
X-ray powder diffraction
The XRPD patterns were recorded using an X-ray diffractometer (Bruker D8 ADVANCE) in reflectance Bragg-Brentano geometry employing Ni filtered Cu Kα line focused radiation (λ = 1.54178 Å) at 3000 W (40 kV, 40 mA) power. Each sample was measured with a 2θ rate of 10°/min for normal characterization, and 1°/min for refinement. The Rietveld refinement was performed using the software Topas version 5. The refinement was performed using isotropic atomic displacement parameters, a pseudo-Voigt peak shape function, a fourth order spherical harmonic correction to take into account preferred orientation, and seven parameters to fit the background. No restraints on the geometry of the structure were used. Details of the structure after Rietveld refinement are available from the Cambridge Crystallographic Data Center with deposition code CCDC 1961467.
Fourier transform IR spectroscopy was performed on a PerkinElmer spectrum 100 Spectrophotometer. Before measurements, thin KBr disks with a diameter of 1.0 cm were prepared by pressing KBr powder by applying a pressure of 10 MPa. The samples were dispersed in ethanol, then dropped on the KBr disks. After the ethanol was dried, the samples were adsorbed on individual KBr disks. The disks were then used for the measurements. In order to achieve a sufficient signal-to-noise ratio, 16 scans were accumulated for each spectrum.
TGA measurements were performed using a thermal analyzer instrument (NETZSCH STA 449 F3 Jupiter®) in a nitrogen atmosphere. The heating rate was 10 °C min−1. 10–15 mg of powdered samples were placed in a crucible for measurements, whereas an empty one served as reference.
The elemental composition of the ACPs was determined using an ICP-OES (Horiba, JY2000-2). The samples were dissolved in 1% HNO3 solution for measurements. 5 solutions, containing a different concentration of Ca and P in each one, were prepared for the setup calibration.
Continuous rotation electron diffraction
The sample was crushed in an agate mortar, dispersed in absolute ethanol and ultrasonicated for 5 s. Then, a droplet of the suspension was transferred onto a copper grid covered by a holey carbon film. The grid was mounted to a single-tilt cryo-transfer tomography holder, Gatan Type 914, operated at liquid nitrogen cooling at ~−176 °C. The data were collected using a JEOL JEM-2100 TEM operated at an accelerating voltage of 200 kV. The cRED data were collected by continuously tilting the goniometer with a tilt speed of 1.12°/s. During tilt the crystal was tracked by sequential defocusing of the intermediate lens using the software Instamatic47. The diffraction patterns were collected using the high-speed hybrid detection camera Timepix Quad (ASI). The datasets were processed using X-ray Detector Software (XDS) in order to extract intensities for structure solution and refinement. The reconstructed reciprocal lattice could be indexed by a monoclinic unit cell and systematic extinctions indicated that the space group was P21/c, see Supplementary Fig. 4. The structure of DCPM was solved using the software SHELXT54 and the subsequent least-squares refinement was performed in SHELXL-9755 using atomic scattering factors for electrons extracted from SIR201456. The structure solution directly identified 7 peaks identified as 1 Ca, 1 P, and 5 O. The least squares refinement converged without the use of any restraints and with reasonable isotropic atomic displacement parameters to an R1 residual of 0.260, using 29 refinement parameters. No restraints on the geometry of the structure were used during the refinement. Details regarding the cRED data collection, as well as the refinement, can be found in Supplementary Table S1. Details of the structure after refinement against cRED data are available from the Cambridge Crystallographic Data Center with deposition code CCDC 1961466. cRED data were also collected from the sample of DCPM prepared in humid air. Structure solution resulted in the same structure as for the sample prepared by mixed solvent and the refinement converged with an R1 residual of 0.256.
First principles calculations
All quantum mechanical calculations have been performed within the framework of Kohn-Sham density functional theory using one of two different methods:
Geometry optimizations and phonon calculations were conducted using the planewave pseudopotential method as implemented within the code CASTEP version 18.157. On-the-fly generated ultrasoft pseudopotentials were used with a small core for Ca and a planewave cutoff of 1000 eV for a high level of convergence (dEtot/dlog(Ecut) < 0.001 eV per atom). Reciprocal space was sampled with a Monkhorst-Pack mesh with a spacing of 0.02 Å−1. The PBE exchange-correlation functional58 was used with Grimme’s D2 dispersion corrections59. All geometries were optimized with a fully variable unit cell to an energy tolerance of 10−5 eV, a force tolerance of 0.02 eV/Å and a stress tolerance of 0.1 GPa. Phonon calculations were performed at the gamma point only using finite differences, from which the zero point energy and thermal corrections were estimated at 298.15 K. All phases were confirmed to have no imaginary modes at the zone center. Calculations on monetite, brushite and DCPM all used unit cells containing four formula units and so any systematic error due to the use of only the gamma point phonons will be largely canceled. In order to estimate the thermodynamics of water incorporation into the phases, calculations were also performed for a proton-ordered structure of ice-Ih at the same level of theory. Here the computed hypothetical free energy of ice at standard conditions was corrected using the experimental free energy of fusion under the same conditions to estimate the corresponding thermodynamics of liquid water.
Ab initio molecular dynamics was also performed for DCPM in order to explore the stability of the initial hydrogen position choices after geometry optimization. Here the Gaussian-augmented planewave method was used as implemented in the Quickstep60 module of CP2K61. In order to also verify that the computed behavior of DCPM was not especially sensitive to the choice of functional, these calculations were performed using BLYP62,63 with D3 dispersion corrections64. The Goedecker-Teter-Hutter pseudopotentials65 and basis sets of TZVP quality were used, except for Ca which used a DZVP basis. A planewave basis with a cutoff of 300 Ry was used for the electron density. Molecular dynamics was performed using a 2 × 2 × 2 supercell of DCPM containing 362 atoms in the NPT ensemble, again with a fully flexible unit cell. A slightly elevated temperature of 330 K was used to enhance the rate of exploration of configuration space, with the use of a canonical sampling velocity rescaling thermostat and barostat66, both with time constants of 50 fs, and a time step of 0.5 fs. Hydrogen was also assigned a mass of 2 amu (i.e., deuterated). A total of 34 ps of MD was run during which no proton transfer events or significant changes in the orientation of water molecules beyond libration were observed. Quenching of structures harvested from the dynamics resulted in the same structure as obtained initially by geometry optimization.
Force field calculations
As a further test of the validity of the DCPM structure, calculations were also performed using the GULP code67 and a recently fitted force field that was designed to reproduce the properties of aqueous calcium phosphate systems during crystallization68. Again the DCPM structure was optimized and a full phonon analysis performed across the Brillouin zone that revealed no instability within the initial space group.
Further information on research design is available in the Nature Research Reporting Summary linked to this article.
Rietveld refinement and cRED data are available from the Cambridge Crystallographic Data Center with deposition code CCDC 1961467 and CCDC 1961466, respectively. The source data underlying Figs. 1b, 3a-b, 4a-c, 4c, 5a-b and Supplementary Figs. 1, 2, 4, 5a, b, 7, 10a, b, 12, 13, 14, 15, and Supplementary Table 6 are provided as a Source Data file. Data is also available from the corresponding author upon reasonable request.
Dorozhkin, S. V. & Epple, M. Biological and medical significance of calcium phosphates. Angew. Chem. Int. Ed. 41, 3130–3146 (2002).
Mehmel, M. On the structure of apatite. Z. Kristallogr. 75, 323–331 (1930).
Brown, W. E., Lehr, J. R., Smith, J. P. & Frazier, A. W. Crystallography of octacalcium phosphate. J. Am. Chem. Soc. 79, 5318–5319 (1957).
Moore, G. E. On brushite, a new mineral occurring in phosphatic guano. Am. J. Sci. Ser. 2 39, 43–44 (1865).
Shepard, C. U. On two new minerals, monetite and monite, with a notice of pyroclasite. Am. J. Sci. Ser. 3 23, 400–405 (1882).
Muhlenberg, W. F. Address in Hygiene, Transactions of the Medical Society of the State of Pennsylvania, at Its Thirty-third Annual Session, Held at Titusville, May 10, 11 and 12. Vol. XIV, 81–102 (Times printing house, Philadelphia, 1832).
Dorozhkin, S. V. A detailed history of calcium orthophosphates from 1770s till 1950. Mater. Sci. Eng. C. 33, 3085–3110 (2013).
Lotsari, A., Rajasekharan, A. K., Halvarsson, M. & Andersson, M. Transformation of amorphous calcium phosphate to bone-like apatite. Nat. Comm. 9, 4170 (2018).
Zyman, Z. et al. Thermally induced crystallization and phase evolution in powders derived from amorphous calcium phosphate precipitates with a Ca/P ratio of 1:1. J. Cryst. Growth 450, 190–196 (2016).
Tung, M. S. & Brown, W. E. An intermediate state in hydrolysis of amorphous calcium-phosphate. Calcif. Tissue Int. 35, 783–790 (1983).
Maciejewski, M., Brunner, T. J., Loher, S. F., Stark, W. J. & Baiker, A. Phase transitions in amorphous calcium phosphates with different Ca/P ratios. Thermochim. Acta 468, 75–80 (2008).
Pan, H. H., Liu, X. Y., Tang, R. K. & Xu, H. Y. Mystery of the transformation from amorphous calcium phosphate to hydroxyapatite. Chem. Commun. 46, 7415–7420 (2010).
Combes, C. & Rey, C. Amorphous calcium phosphates: synthesis, properties and uses in biomaterials. Acta Biomater. 6, 3362–3378 (2010).
La Fontaine, A. et al. Atomic-scale compositional mapping reveals Mg-rich amorphous calcium phosphate in human dental enamel. Sci. Adv. 2, e1601145 (2016).
Akiva, A. et al. Mineral formation in the larval Zebrafish tail bone occurs via an acidic disordered calcium phosphate phase. J. Am. Chem. Soc. 138, 14481–14487 (2016).
Tertuliano, O. A. & Greer, J. R. The nanocomposite nature of bone drives its strength and damage resistance. Nat. Mater. 15, 1195–1202 (2016).
Lowenstam, H. A. & Weiner, S. Transformation of amorphous calcium-phosphate to crystalline dahllite in the radular teeth of chitons. Science 227, 51–53 (1985).
Zhao, J., Liu, Y., Sun, W. B. & Yang, X. B. First detection, characterization, and application of amorphous calcium phosphate in dentistry. J. Dent. Sci. 7, 316–323 (2012).
Mahamid, J. et al. Mapping amorphous calcium phosphate transformation into crystalline mineral from the cell to the bone in zebrafish fin rays. Proc. Natl Acad. Sci. USA 107, 6316–6321 (2010).
Gordon, L. M., Cohen, M. J., MacRenaris, K. W., Pasteris, J. D. & Seda, T. Amorphous intergranular phases control the properties of rodent tooth enamel. Science 347, 746–750 (2015).
Grynpas, M. D. & Omelon, S. Transient precursor strategy or very small biological apatite crystals? Bone 41, 162–164 (2007).
Gower, L. B. Biomimetic model systems for investigating the amorphous precursor pathway and its role in biomineralization. Chem. Rev. 108, 4551–4627 (2008).
De Yoreo, J. J. et al. Crystallization by particle attachment in synthetic, biogenic, and geologic environments. Science 349, aaa6760 (2015).
Olszta, M. J. et al. Bone structure and formation: a new perspective. Mater. Sci. Eng. R. Rep. 58, 77–116 (2007).
Glimcher, M. J., Bonar, L. C., Grynpas, M. D., Landis, W. J. & Roufosse, A. H. Recent studies of Bone-mineral-is the amorphous calcium-phosphate theory valid. J. Cryst. Growth 53, 100–119 (1981).
LeGeros, R. Z. Calcium phosphate-based osteoinductive materials. Chem. Rev. 108, 4742–4753 (2008).
Habraken, W., Habibovic, P., Epple, M. & Bohner, M. Calcium phosphates in biomedical applications: materials for the future? Mater. Today 19, 69–87 (2016).
Bragg, W. L. The structure of some crystals as indicated by their diffraction of x-rays. Proc. R. Soc. Lond. 89, 248–277 (1913).
Friedrich, W., Knipping, P. & Laue, M. Interferenzerscheinungen bei Röntgenstrahlen. Ann. Phys. 346, 971–988 (1913).
Kerr, A. & Laing, M. Mineralogical studies of human urinary calculi from natal. Environ. Geochem. Health 14, 19–25 (1992).
Mansfield, C. F. & Griffith, D. P. Descriptive human pathological mineralogy. Am. Mineral. 61, 1031–1034 (1976).
Schofield, P. F., Knight, K. S., van der Houwen, J. A. M. & Valsami-Jones, E. The role of hydrogen bonding in the thermal expansion and dehydration of brushite, di-calcium phosphate dihydrate. Phys. Chem. Miner. 31, 606–624 (2004).
Tortet, L., Gavarri, J. R., Nihoul, G. & Dianoux, A. J. Study of protonic mobility in CaHPO4·2H2O (brushite) and CaHPO4 (monetite) by infrared spectroscopy and neutron scattering. J. Solid State Chem. 132, 6–16 (1997).
Wang, L. J. & Nancollas, G. H. Calcium orthophosphates: crystallization and dissolution. Chem. Rev. 108, 4628–4669 (2008).
Dorozhkin, S. V. Calcium orthophosphates in nature, biology and medicine. Materials 2, 399–498 (2009).
O’Neill, R. et al. Critical review: injectability of calcium phosphate pastes and cements. Acta Biomater. 50, 1–19 (2017).
Tamimi, F., Sheikh, Z. & Barralet, J. Dicalcium phosphate cements: brushite and monetite. Acta Biomater. 8, 474–487 (2012).
Lu, B. Q. et al. Short-range structure of amorphous calcium hydrogen phosphate. Cryst. Growth Des. 19, 3030–3038 (2019).
Kolb, U., Gorelik, T., C.Kübel, C., Otten, M. T. & Hubert, D. Towards automated diffraction tomography: part I-data acquisition. Ultramicroscopy 107, 507–513 (2007).
Zhang, D. L., Oleynikov, P., Hovmöller, S. & Zou, X. D. Collecting 3D electron diffraction data by the rotation method. Z. Kristallogr. Cryst. Mater. 225, 94–102 (2010).
Wan, W., Sun, J. L., Su, J., Hovmöller, S. & Zou, X. D. Three-dimensional rotation electron diffraction: software RED for automated data collection and data processing. J. Appl. Crystallogr. 46, 1863–1873 (2013).
Shi, D., Nannenga, B. L., Iadanza, M. G. & Gonen, T. Three-dimensional electron crystallography of protein microcrystals. Elife 2, e01345 (2013).
Nannenga, B. L., Shi, D., Leslie, A. G. W. & Gonen, T. High-resolution structure determination by continuous-rotation data collection in microED. Nat. Methods 11, 927–930 (2014).
Willhammar, T., Yun, Y. F. & Zou, X. D. Structural determination of ordered porous solids by electron crystallography. Adv. Funct. Mater. 24, 182–199 (2014).
Palatinus, L. et al. Hydrogen positions in single nanocrystals revealed by electron diffraction. Science 355, 166–169 (2017).
Xu, H. Y. et al. A rare lysozyme crystal form solved using highly redundant multiple electron diffraction datasets from micron-sized crystals. Structure 26, 667–675 (2018).
Cichocka, M. O., Ångström, J., Wang, B., Zou, X. D. & Smeets, S. High-throughput continuous rotation electron diffraction data acquisition via software automation. J. Appl. Crystallogr. 51, 1652–1661 (2018).
Bailey, R. T. & Holt, C. in Calcified Tissue. In Chapter: Fourier transform infrared spectroscopy and characterisation of biological calcium phosphates (Hukins, D. W. L. ed.) 93–120 (The Macmillan Press Ltd, 1989).
Dosen, A. & Giese, R. F. Thermal decomposition of brushite, CaHPO4·2H2O to monetite CaHPO4 and the formation of an amorphous phase. Am. Mineral. 96, 368–373 (2011).
Frost, R. L. & Palmer, S. J. Thermal stability of the ‘cave’ mineral brushite CaHPO4·2H2O-Mechanism of formation and decomposition. Thermochim. Acta 521, 14–17 (2011).
Lebugle, A., Sallek, B. & Tai, A. T. Surface modification of monetite in water at 37 degrees C: characterisation by XPS. J. Mater. Chem. 9, 2511–2515 (1999).
Duff, E. J. Orthophosphates. Part III. The hydrolysis of secondary calcium orthophosphates. J. Chem. Soc. A 917–921 (1971).
Hu, Y. Y., Rawal, A. & Schmidt-Rohr, K. Strongly bound citrate stabilizes the apatite nanocrystals in bone. Proc. Natl Acad. Sci. USA 107, 22425–22429 (2010).
Sheldrick, G. SHELXT-Integrated space-group and crystal-structure determination. Acta Crystallogr. Sect. A 71, 3–8 (2015).
Sheldrick, G. A short history of SHELX. Acta Crystallogr. Sect. A 64, 112–122 (2008).
Burla, M. C. et al. Crystal structure determination and refinement viaSIR2014. J. Appl. Crystallogr. 48, 306–309 (2015).
Clark, S. J. et al. First principles methods using CASTEP. Z. Für Krist. Cryst. Mater. 220, 567–570 (2005).
Perdew, J. P., Burke, K. & Ernzerhof, M. Generalized gradient approximation made simple. Phys. Rev. Lett. 77, 3865–3868 (1996).
Grimme, S. Semiempirical GGA‐type density functional constructed with a long‐range dispersion correction. J. Comput. Chem. 27, 1787–1799 (2006).
VandeVondele, J. et al. Quickstep: fast and accurate density functional calculations using a mixed Gaussian and plane waves approach. Comput. Phys. Commun. 167, 103–128 (2005).
Hutter, J., Iannuzzi, M., Schiffmann, F. & VandeVondele, J. cp2k: atomistic simulations of condensed matter systems. Wiley Interdiscip. Rev. Comput. Mol. Sci. 4, 15–25 (2014).
Becke, A. D. Density-functional thermochemistry 1. The effect of the exchange-only gradient correction. J. Chem. Phys. 96, 2155–2160 (1992).
Lee, C. T., Yang, W. T. & Parr, R. G. Development of the Colle-Salvetti correlation-energy formula into a functional of the electron-density. Phys. Rev. B 37, 785–789 (1988).
Grimme, S., Antony, J., Ehrlich, S. & Krieg, H. A consistent and accurate ab initio parametrization of density functional dispersion correction (DFT-D) for the 94 elements H-Pu. J. Chem. Phys. 132, 154104 (2010).
Goedecker, S., Teter, M. & Hutter, J. Separable dual-space Gaussian pseudopotentials. Phys. Rev. B 54, 1703–1710 (1996).
Bussi, G., Donadio, D. & Parrinello, M. Canonical sampling through velocity rescaling. J. Chem. Phys. 126, 014101 (2007).
Gale, J. D. & Rohl, A. L. The General Utility Lattice Program (GULP). Mol. Simul. 29, 291–341 (2003).
Demichelis, R. et al. Simulation of calcium phosphate species in aqueous solution: force field derivation. J. Phys. Chem. B 122, 1471–1483 (2018).
B.Q.L. acknowledges financial support by the CSC-DAAD postdoc program for a postdoctoral stay at the University of Konstanz, and characterization help from Shengtong Sun and Min Ju. D.G. was a Research Fellow of the Zukunftskolleg of the University of Konstanz, and partly supported by the DFG-funded SFB 1214 of the University of Konstanz during this work. T.W. acknowledges a grant from the Swedish research council (VR, 2014-06948). J.D.G. acknowledges the support of the Australian Research Council through grant FL180100087, as well as the provision of computing resources by the Pawsey Supercomputing Centre and National Computational Infrastructure. We also acknowledge financial support from the Knut and Alice Wallenberg Foundation through the project grant 3DEM-NATUR (no. 2012.0112).
The authors declare no competing interests.
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Lu, BQ., Willhammar, T., Sun, BB. et al. Introducing the crystalline phase of dicalcium phosphate monohydrate. Nat Commun 11, 1546 (2020). https://doi.org/10.1038/s41467-020-15333-6