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. 2018 Apr 27;4(4):eaaq1636. doi: 10.1126/sciadv.aaq1636

Readily accessible shape-memory effect in a porous interpenetrated coordination network

Mohana Shivanna 1,*, Qing-Yuan Yang 1,*, Alankriti Bajpai 1, Susan Sen 2, Nobuhiko Hosono 2, Shinpei Kusaka 2, Tony Pham 3, Katherine A Forrest 3, Brian Space 3, Susumu Kitagawa 2,†, Michael J Zaworotko 1,†
PMCID: PMC5922793  PMID: 29719864

An interpenetrated flexible metal-organic material exhibits only the second example of a shape-memory effect in a porous material.

Abstract

Shape-memory effects are quite well-studied in general, but there is only one reported example in the context of porous materials. We report the second example of a porous coordination network that exhibits a sorbate-induced shape-memory effect and the first in which multiple sorbates, N2, CO2 and CO promote this effect. The material, a new threefold interpenetrated pcu network, [Zn2(4,4′-biphenyldicarboxylate)2(1,4-bis(4-pyridyl)benzene)]n (X-pcu-3-Zn-3i), exhibits three distinct phases: the as-synthesized α phase; a denser-activated β phase; and a shape-memory γ phase, which is intermediate in density between the α and β phases. The γ phase is kinetically stable over multiple adsorption/desorption cycles and only reverts to the β phase when heated at >400 K under vacuum. The α phase can be regenerated by soaking the γ phase in N,N′-dimethylformamide. Single-crystal x-ray crystallography studies of all three phases provide insight into the shape-memory phenomenon by revealing the nature of interactions between interpenetrated networks. The β and γ phases were further investigated by in situ coincidence powder x-ray diffraction, and their sorption isotherms were replicated by density functional theory calculations. Analysis of the structural information concerning the three phases of X-pcu-3-Zn-3i enabled us to understand structure-function relationships and propose crystal engineering principles for the design of more examples of shape-memory porous materials.

INTRODUCTION

A shape-memory effect occurs when the morphology of a material changes in response to an external stimulus, and the new morphology is persistent until another stimulus is applied. Shape-memory effects are well-recognized in general (1, 2) but remain rare in the context of porous materials. Metal-organic materials (MOMs) (3, 4), also known as porous coordination polymers (5, 6) or metal-organic frameworks (MOFs) (7, 8), are a subclass of porous materials that are extraordinarily diverse in composition owing to their modularity and amenability to design from first principles (9). There are at least 20,000 porous MOMs, and ca. 150 of these MOMs are known to exhibit structural flexibility, in some cases, extreme structural flexibility (10, 11). Flexibility occurs in response to external stimuli, such as guest incorporation/removal, temperature, pressure, or light (12–16). The origins of flexibility are well-studied and attributed to flexible MOMs (FMOMs) being able to exhibit one or more of the following phenomena: (i) changes in metal-ligand coordination geometry (17, 18); (ii) cleavage and regeneration of coordination bonds (19); and (iii) distortion/contortion of organic linker(s) (20, 21). Dynamic behavior is also known in zeolites, but it tends to be less pronounced (22, 23). The fact that FMOMs can exhibit breathing or swelling suggests that they might be amenable to shape-memory effects (table S1). However, most of the FMOMs reported to date undergo reversible structural changes in response to interfacial sorbate/sorbent interactions, albeit with hysteresis (20, 24, 25). To our knowledge, the only example of an FMOM that exhibits a shape-memory effect, [Cu2(bdc)2(bpy)]n, does not return to its activated form upon MeOH solvation/desolvation. Rather, it reverts to the original phase upon heating at 473 K, and the shape-memory effect is particle size–dependent (26). Therefore, whereas shape-memory effects are well-documented in metal alloys (27, 28), polymers (29, 30), and ceramics (31), it remains a rare and poorly understood phenomenon in crystalline porous materials.

Here, we report the second observation of a shape-memory effect in FMOMs through the study of gas adsorption in an expanded variant of [Cu2(bdc)2(bpy)]n and [Zn2(L1)(L2)2]n (X-pcu-3-Zn-3i), both of which can be regarded as derivatives of DMOF-1 (32, 33) and its analogs (34–37). The shape-memory effect exhibited by X-pcu-3-Zn-3i was recognized by distinctive sorption isotherms characteristic of shape-memory porous materials (Fig. 1) and occurs under the influence of N2, CO2, or CO (Fig. 2). A suite of experiments involving single-crystal x-ray diffraction (XRD), gas sorption, in situ variable temperature/pressure powder XRD (PXRD), and molecular modeling were performed to afford insight into the shape-memory behavior of X-pcu-3-Zn-3i.

Fig. 1. The typical sorption isotherms associated with a shape-memory effect in an FMOM.

Fig. 1

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The first adsorption cycle occurs in step(s), whereas desorption lacks any steps (left). The second and subsequent sorption cycles are examples of type I isotherms (right).

Fig. 2. Structure of X-pcu-3-Zn and its phase changes under external stimuli.

Fig. 2

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A schematic illustration of the shape-memory effect in X-pcu-3-Zn-3i (left). The structure of X-pcu-3-Zn-3i is composed of axially coordinated L1 linkers that cross-link 2D square grids to form a 3D structure (right).

RESULTS AND DISCUSSION

Single crystals of the as-synthesized X-pcu-3-Zn-3i and X-pcu-3-Zn-3i-α were isolated by solvothermal reaction of ligands L1 [1,4-bis(4-pyridyl)benzene] and L2 (4,4′-biphenyldicarboxylic acid) with Zn(NO3)2·6H2O in N,N′-dimethylformamide (DMF) at 120°C for 24 hours. The extended ligand (X ligand) L1 was prepared by following our previously reported procedure (38), whereas L2 was purchased from Sigma-Aldrich and used as received. The crystal structure of X-pcu-3-Zn-3i-α was determined by single-crystal XRD (SCXRD) and exhibits the triclinic space group P-1 (table S2). Dinuclear Zn “paddlewheel” molecular building blocks (MBBs) (3) are linked equatorially by dicarboxylate dianions to form distorted square lattice (sql) networks. The axial sites of the paddlewheel MBBs are coordinated by dipyridyl linkers (L1), which cross-link the sql networks to generate three-dimensional (3D) networks with primitive cubic (pcu) topology (Fig. 2). Three independent pcu networks interpenetrate (fig. S1), yet X-pcu-3-Zn-3i-α still exhibits 46% guest accessible volume occupied by solvent DMF molecules and a density without solvent of 1.046 g/cm3.

Single crystals of X-pcu-3-Zn-3i-β were obtained from as-synthesized crystals of X-pcu-3-Zn-3i-α by heating at 130°C under vacuum for 12 hours. X-pcu-3-Zn-3i-β also exists in the triclinic space group P-1 and its density is 1.333 g/cm3. Comparison of the crystal structures of X-pcu-3-Zn-3i-α and X-pcu-3-Zn-3i-β reveals that the pcu networks in X-pcu-3-Zn-3i-β are distorted, reducing the guest accessible volume from 46 to 15% (Fig. 2). The phase transformation between X-pcu-3-Zn-3i-α and X-pcu-3-Zn-3i-β was also studied by in situ variable temperature PXRD, which revealed that transformation at 120°C is complete within 10 min (figs. S2 and S6). Those phase transformations in FMOMs can occur in single-crystal–to–single-crystal (SC-SC) fashion as has been previously observed for FMOMs (39, 40).

Gas sorption and in situ coincidence PXRD measurements

The gas adsorption performance of X-pcu-3-Zn-3i-β was studied for N2 (77 K), CO (82 K), and CO2 (195 K). Activation was conducted by washing as-synthesized X-pcu-3-Zn-3i-α with DMF followed by heating at 130°C under vacuum for 12 hours. Two distinct steps were observed in the CO2 adsorption isotherm at 195 K (fig. S3): a plateau at 0.2 to 0.3 bar with uptake of 65 g/cm3 followed by a second step leading to uptake of 160 g/cm3 at 1 bar. The desorption isotherm does not match the adsorption isotherm; it exhibits no step and large hysteresis (fig. S3). We attribute the stepped adsorption isotherm to a structural transformation from X-pcu-3-Zn-3i-β to a new phase, X-pcu-3-Zn-3i-γ, as verified by PXRD (fig. S8). Notably, X-pcu-3-Zn-3i-γ does not revert to X-pcu-3-Zn-3i-β under vacuum but, after being subjected to heating at 130°C in vacuo for 2 hours, it once again exhibits the stepped isotherm of X-pcu-3-Zn-3i-β (fig. S4). The structure of X-pcu-3-Zn-3i-γ was determined by SCXRD (monoclinic space group C2/c, density of 1.117 g/cm3; table S2), and the calculated PXRD pattern for X-pcu-3-Zn-3i-γ matches that of the experimental PXRD pattern. X-pcu-3-Zn-3i-γ exhibits 34% guest accessible volume. These results are indicative of a shape-memory effect in X-pcu-3-Zn-3i.

To validate the shape-memory effect in X-pcu-3-Zn-3i, in situ coincidence PXRD was performed using CO2 at 195 K; diffraction patterns were recorded at adsorption/desorption points a to f (Fig. 3). The PXRD pattern at point d (0.9 bar CO2) reveals that transformation from X-pcu-3-Zn-3i-β to X-pcu-3-Zn-3i-γ had been induced by CO2. From point d to f (desorption), there is no change in the PXRD pattern, which corresponds to the calculated PXRD of X-pcu-3-Zn-3i-γ. X-pcu-3-Zn-3i-γ reverts to X-pcu-3-Zn-3i-β after heating at 130°C under vacuum in situ for 2 hours (Fig. 3, left). In situ coincidence PXRD measurements were also performed using N2 (77 K) and CO (82 K); PXRD patterns were recorded at adsorption/desorption points. Sorption isotherms characteristic of the shape-memory effect observed for CO2 at 195 K were obtained but there are multiple steps in both the N2 and CO adsorption isotherms. This is plausible because N2 and CO offer weaker interfacial interactions than CO2, enabling the observation of intermediate phases. For N2 sorption (Fig. 3, middle), there is little uptake at low pressure (0.05 bar, 9 g/cm3); however, at 0.14 bar N2, there is a step (to 90 g/cm3) before a second step occurs at point c. These steps are indicative of a narrow- to large-pore phase transformation involving at least two large-pore phases. The PXRD patterns at points d and e reveal that transformation to X-pcu-3-Zn-3i-γ had been induced by N2. From points e to g (desorption), there is no change in the PXRD pattern, but X-pcu-3-Zn-3i-γ reverts to X-pcu-3-Zn-3i-β after heating at 130°C under vacuum for 2 hours (Fig. 3, middle). In the case of CO sorption (Fig. 3, right), there are also steps at points a, b, and c, which are consistent with narrow- to large-pore phase transformation to X-pcu-3-Zn-3i-γ.

Fig. 3. In situ coincidence PXRD measurements.

Fig. 3

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PXRD patterns for X-pcu-3-Zn-3i are correlated with adsorption and desorption isotherms for CO2 at 195 K (left), N2 at 77 K (middle), and CO at 82 K (right). a.u., arbitrary unit.

Furthermore, 10 consecutive cycles of CO2 sorption at 195 K were performed (Fig. 4, left). The first cycle exhibits a stepped isotherm, whereas subsequent cycles are type I isotherms with uptake of ca. 170 g/cm3 (Fig. 4, left). High-pressure CO2 adsorption at 298 K also reveals a stepped isotherm with gate opening at 15 bar and, once again, the desorption isotherm exhibits no step and a large hysteresis loop (Fig. 4, right). Consecutive cycles measured at other temperatures (298, 288, and 305 K) all exhibit type I isotherms (fig. S5). The PXRD pattern of a sample isolated after these experiments matches the calculated PXRD of X-pcu-3-Zn-3i-γ (fig. S8). X-pcu-3-Zn-3i-γ fails to revert to X-pcu-3-Zn-3i-β upon heating up to 240°C (fig. S10) but reverts to X-pcu-3-Zn-3i-α by soaking in DMF (5 min) but not with methanol, acetonitrile, or dichloromethane (2 days; fig. S9). These results indicate that the new shape-memory phase reported here, X-pcu-3-Zn-3i-γ, can be accessed with multiple sorbates and that it is kinetically stable over a range of temperatures, sorbates, and pressures.

Fig. 4. Low- and high-pressure CO2 sorption on X-pcu-3-Zn.

Fig. 4

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Ten consecutive cycles of CO2 sorption at 195 K (left). First cycle of high-pressure CO2 at 298 K (right).

Modeling studies

The sorption profiles were modeled using the single-crystal structures of X-pcu-3-Zn-3i-β and X-pcu-3-Zn-3i-γ. The simulated CO2 isotherms at 195 K for X-pcu-3-Zn-3i-β and X-pcu-3-Zn-3i-γ are in good agreement with the corresponding experimental isotherm (fig. S15); below 0.3 bar, the experimental isotherm matches the simulated isotherm for X-pcu-3-Zn-3i-β. The uptake from the simulated isotherm of X-pcu-3-Zn-3i-γ is comparable to its experimental uptake (fig. S15).

Structural insight into shape memory

To gain insight into the origins of the shape-memory phenomenon, we analyzed and compared the crystal structures of X-pcu-3-Zn-3i-α, X-pcu-3-Zn-3i-β, and X-pcu-3-Zn-3i-γ. In X-pcu-3-Zn-3i-α, the paddlewheel MBBs are slightly distorted (∠linker-MBB-linker = 70.9° to 109.6°) and L2 linkers align out of plane with respect to each other (fig. S11). There exist π···π [DC···C = 3.547 (5) and 3.518(5) Å] interactions between the interpenetrated networks, but there are no intermolecular interactions between blue and green networks (Fig. 5, left bottom). In X-pcu-3-Zn-3i-β, the paddlewheel MBB is highly distorted (∠linker-MBB-linker = 46.8° to 132.2°) and L2 linkers align out of plane with respect to each other (fig. S12). Being the densest phase, the interpenetrated networks are in close proximity as evidenced C–H···O [DC···O = 3.587(6) Å] and π···π [DC···C = 3.710(6) Å] interactions (Fig. 5, middle bottom). In X-pcu-3-Zn-3i-γ, the paddlewheel MBB is slightly distorted (∠linker-MBB-linker = 61.1° to 117.7°) and L2 linkers align in-plane with respect to each other (fig. S13). The interpenetrated networks exhibit C–H···O interactions [DC···O = 3.289(5) and 3.446(4) Å; Fig. 5, right bottom]. Structural transformation between the three phases can be attributed to sliding of the interpenetrated networks (fig. S1), a previously observed phenomenon (13).

Fig. 5. Structural insights for the three phases.

Fig. 5

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The sql networks of the α, β, and γ forms of X-pcu-3-Zn-3i (top) and how three of these networks (red, green, and blue, respectively) interact through C–H···O (teal) and π···π (yellow) interactions (bottom).

CONCLUSIONS

X-pcu-3-Zn-3i is only the second example of a porous material that exhibits a shape-memory effect and the first in which multiple sorbates induce such an effect. The shape-memory phase (X-pcu-3-Zn-3i-γ) was observed to be accessible under the influence of several stimuli (CO2 at 195 K, N2 at 77 K, CO at 82 K, and high-pressure CO2 at 298 K) and is kinetically stable over a range of pressures, temperature, and sorbates. The following factors would intuitively be expected to facilitate a kinetically stable shape-memory FMOM, and all three are observed for X-pcu-3-Zn-3i: (i) framework flexibility induced by sorbent-sorbate interfacial interactions and extended ligands (X ligands) that can distort more readily than shorter ligands; (ii) interpenetration that enables framework-framework interactions to stabilize less dense variants; and (iii) reduced strain in the MBBs and linkers when in the shape-memory phase. As noted by a reviewer, it is possible that existing FMOMs are as yet unrecognized as shape-memory porous materials. It is a characteristic feature of FMOMs that they exhibit “stepped” or “S-shaped” isotherm profiles, but this does not prove or even suggest a shape-memory effect, which can only be identified by measurement of multiple cycles of adsorption/desorption. We have analyzed the isotherms for all reported FMOMs (ca. 130 materials), and 10 of these materials (table S1) exhibit strong hysteresis that could be consistent with a shape-memory effect. However, we do not know whether any of these materials are recyclable, regardless of whether they exhibit the features listed above to sustain a shape-memory phase. X-pcu-3-Zn-3i is highly modular and amenable to fine-tuning of the ligands and the metal centers. X-pcu-3-Zn-3i is therefore a platform to determine whether the three factors listed above are crystal engineering principles for the design of families of shape-memory porous materials.

MATERIALS AND METHODS

Synthesis of [Zn2(4,4′-biphenyldicarboxylate)2(1,4-bis(4-pyridyl)benzene)]n·6DMF (X-pcu-3-Zn-3i-α)

Commercially available reagents were purchased in high-purity grade and used as received. A mixture of Zn(NO3)2·6H2O (14.8 mg, 0.05 mmol; purchased from Sigma-Aldrich), L1 (7.7 mg, 0.025 mmol; prepared as previously reported), and L2 (12.11 mg, 0.05 mmol; purchased from Sigma-Aldrich) were dissolved in DMF (3 ml) in a 14-ml glass vial. The vial was capped tightly and placed in an oven at 120°C. Colorless block-shaped crystals were isolated after 24 hours. The contents were cooled to room temperature, filtered, and washed with DMF (3 ml × 10 ml) to afford 60% yield of X-pcu-3-Zn-3i-α (based on L1 as the limiting reagent).

Preparation of [Zn2(L2)2(L1)]·DMF (X-pcu-3-Zn-3i-β)

Crystals of the X-pcu-3-Zn-3i-β were prepared by heating X-pcu-3-Zn-3i-α at 130°C under vacuum for 12 hours.

Preparation of [Zn2(L2)2(L1)] (X-pcu-3-Zn-3i-γ)

Shape-memory phase X-pcu-3-Zn-3i-γ was obtained by gas sorption of first cycle at CO2 at 195 K of X-pcu-3-Zn-3i-β phase.

In situ variable temperature PXRD, PXRD and SCXRD experiments

PXRD experiments were conducted using a PANalytical Empyrean diffractometer equipped with a PIXcel3D detector operating in scanning line detector mode with an active length of 4 using 255 channels. The diffractometer was outfitted with an Empyrean Cu LFF (long fine-focus) HR tube (9430 033 7310x), operated at 40 kV and 40 mA and Cu Kα radiation (λα = 1.540598 Å). Incident beam optics included the Fixed Divergence slit with anti-scatter slit PreFIX module, with a 1/8° divergence slit and a 1/4° anti-scatter slit, a 10-mm fixed incident beam mask and a Soller slit (0.04 rad). Divergent beam optics included a P7.5 anti-scatter slit, a Soller slit (0.04 rad), and a Ni β filter. In a typical experiment, data were collected via a continuous scan in the range of 5° to 45° (2θ) with a step size of 0.02° at a scan rate of 0.1° min−1. Raw data were then evaluated using the X’Pert HighScore Plus software v4.1 (PANalytical). In situ variable temperature PXRD was collected under N2 atmosphere by increasing the temperature to 10°C/10 min; water cooling system was adopted to control the temperature. SCXRD data were collected on a Bruker Quest diffractometer equipped with a complementary metal-oxide semiconductor detector and IμS microfocus x-ray source (Cu Kα, λ = 1.5418 Å). Absorption corrections were applied by using the multiscan program SADABS. Structural solution and refinement against Fobs data were carried out using the SHELXL programs.

Coincident PXRD/adsorption measurement

Coincident PXRD/adsorption measurements were measured on a Rigaku SmartLab with Cu Kα radiation (Rigaku) connected to a BELSORP-18PLUS volumetric adsorption equipment (MicrotracBEL Corp.) and synchronized with each other. To control the temperature, the adsorption equipment was connected to a cryostat. We started with the as-synthesized MOM, X-pcu-3-Zn-3i-α, of known weight. The sample was placed on a copper plate and activated under high vacuum (at a pressure around 200 Pa) at 130°C for 12 hours. The weight of the evacuated sample (~70 mg) was determined under inert atmosphere and set on a cryostat system for in situ evacuation under high vacuum (<10 to 2 Pa) at 393 K for 2 hours before the experiments. CO2 adsorption was carried out by setting the temperature of the cryostat at the measurement temperature (195 K) followed by controlled introduction of CO2 gas to the sample cell. The degree of the adsorption was determined by the decrease in the gas introduction pressure at the equilibrium state. The PXRD pattern of the sample containing adsorbate was simultaneously measured at each equilibrium point of the adsorption isotherms.

In situ SC-SC XRD

In situ SC-SC was studied by selecting a single crystal, which was glued to a glass fiber and inserted into a glass capillary with a wall thickness of 0.01 mm and an outer diameter of 0.2 mm. The crystal was maintained at 300 K, and SCXRD data were collected (X-pcu-3-Zn-3i-α). SCXRD data were then collected at 323, 363, and 403 K for approximately 4 hours at each temperature. The unit cell parameters at each temperature were calculated.

Supplementary Material

http://advances.sciencemag.org/cgi/content/full/4/4/eaaq1636/DC1
supp_4_4_eaaq1636__index.html (3.3KB, html)

Acknowledgments

Coincident PXRD/adsorption measurements were performed in Kyoto University. Funding: This work was supported by the Science Foundation Ireland (award 13/RP/B2549). B.S. acknowledges the NSF (award no. CHE-1152362), including support from the Major Research Instrumentation Program (award no. CHE-1531590), the computational resources that were made available by a XSEDE Grant (no. TG-DMR090028), and the use of the services provided by Research Computing at the University of South Florida. N.H. and S. Kitagawa acknowledge the financial support of KAKENHI, Grant-in-Aid for Specially Promoted Research (no. 25000007) from the Japan Society of the Promotion of Science. S. Kusaka and S. Kitagawa thank JST ACCEL, Japan (grant no. JPMJAC1302). Author contributions: M.J.Z. and M.S. conceived the experiments and designed the study. M.S. conducted the material synthesis and measurements. M.S. and Q.-Y.Y. characterized the phases reported herein (SCXRD, PXRD, and low- and high-pressure gas sorption). A.B. developed the synthetic method to prepare L1. S.S., N.H., and S. Kusaka conducted the in situ coincidence PXRD measurements. T.P., K.A.F., and B.S. conducted the modeling experiments. M.J.Z., S. Kitagawa, Q.-Y.Y., A.B., and M.S. wrote the manuscript. All authors contributed to the interpretation of the data and discussion. Competing interests: The authors declare that they have no competing interests. Data materials and availability: All data needed to evaluate the conclusions in the paper are present in the paper and/or the Supplementary Materials. Crystallographic data for this manuscript have been deposited at the Cambridge Crystallographic Data Centre under deposition numbers CCDC 1565491 and 1565493. Additional data related to this paper may be requested from M.J.Z. (Michael.Zaworotko@ul.ie).

SUPPLEMENTARY MATERIALS

Supplementary material for this article is available at http://advances.sciencemag.org/cgi/content/full/4/4/eaaq1636/DC1

fig. S1. Structure of the three phases.

fig. S2. Diffraction pattern and single-crystal images.

fig. S3. Low-pressure gas sorption.

fig. S4. Recyclability of shape-memory phase at 195 K CO2.

fig. S5. High-pressure CO2 sorption.

fig. S6. In situ variable temperature PXRD.

fig. S7. Solvent-induced phase change.

fig. S8. PXRD data for X-pcu-3-Zn-3i-γ obtained from different experiments.

fig. S9. Phase change from γ to α phase.

fig. S10. Variable temperature PXRD of shape-memory phase.

fig. S11. Distortion of paddlewheel MBB and orientation of X-ligands in X-pcu-3-Zn-3i-α.

fig. S12. Distortion of paddlewheel MBB and orientation of X ligands in X-pcu-3-Zn-3i-β.

fig. S13. Distortion of paddlewheel MBB and orientation of X ligands in X-pcu-3-Zn-3i-γ.

fig. S14. Thermogravimetric analysis (TGA) profiles.

fig. S15. Comparison of modeling and experimental isotherm.

fig. S16. Free-energy difference.

fig. S17. Chemically distinct atoms in X-pcu-3-Zn-3i-α.

fig. S18. The chemically distinct atoms in X-pcu-3-Zn-3i-β.

fig. S19. The chemically distinct atoms in X-pcu-3-Zn-3i-γ.

table S1. Examples of previously reported FMOMs with large hysteresis.

table S2. Crystal data and refinement parameters.

table S3. Numerical labeling of atoms corresponds to fig. S17.

table S4. The crystallographic distances (in Å) between various atoms in X-pcu-3-Zn-3i-α.

table S5. The partial charges (in e−) for the chemically distinct atoms in X-pcu-3-Zn-3i-β.

table S6. The crystallographic distances (in Å) between various atoms in X-pcu-3-Zn-3i-β.

table S7. Numerical labeling of atoms corresponds to fig. S18.

table S8. Labels of atoms correspond to fig. S18.

table S9. Calculated energies for three phases.

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Supplementary Materials

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Supplementary material for this article is available at http://advances.sciencemag.org/cgi/content/full/4/4/eaaq1636/DC1

fig. S1. Structure of the three phases.

fig. S2. Diffraction pattern and single-crystal images.

fig. S3. Low-pressure gas sorption.

fig. S4. Recyclability of shape-memory phase at 195 K CO2.

fig. S5. High-pressure CO2 sorption.

fig. S6. In situ variable temperature PXRD.

fig. S7. Solvent-induced phase change.

fig. S8. PXRD data for X-pcu-3-Zn-3i-γ obtained from different experiments.

fig. S9. Phase change from γ to α phase.

fig. S10. Variable temperature PXRD of shape-memory phase.

fig. S11. Distortion of paddlewheel MBB and orientation of X-ligands in X-pcu-3-Zn-3i-α.

fig. S12. Distortion of paddlewheel MBB and orientation of X ligands in X-pcu-3-Zn-3i-β.

fig. S13. Distortion of paddlewheel MBB and orientation of X ligands in X-pcu-3-Zn-3i-γ.

fig. S14. Thermogravimetric analysis (TGA) profiles.

fig. S15. Comparison of modeling and experimental isotherm.

fig. S16. Free-energy difference.

fig. S17. Chemically distinct atoms in X-pcu-3-Zn-3i-α.

fig. S18. The chemically distinct atoms in X-pcu-3-Zn-3i-β.

fig. S19. The chemically distinct atoms in X-pcu-3-Zn-3i-γ.

table S1. Examples of previously reported FMOMs with large hysteresis.

table S2. Crystal data and refinement parameters.

table S3. Numerical labeling of atoms corresponds to fig. S17.

table S4. The crystallographic distances (in Å) between various atoms in X-pcu-3-Zn-3i-α.

table S5. The partial charges (in e−) for the chemically distinct atoms in X-pcu-3-Zn-3i-β.

table S6. The crystallographic distances (in Å) between various atoms in X-pcu-3-Zn-3i-β.

table S7. Numerical labeling of atoms corresponds to fig. S18.

table S8. Labels of atoms correspond to fig. S18.

table S9. Calculated energies for three phases.

References (41–62)

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