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Capillary origami uses surface tension to fold an initially flat elastic plate around a liquid droplet. The fold trades a reduction in surface energy for an increase in bending energy; the initial outline helps select the resulting enclosure.^[ref]

In the 2007 experiments of Charlotte Py and collaborators, 40–80 micrometre polydimethylsiloxane sheets rested on a water-repellent support. A water droplet reached the sheet's corners; time-lapse images followed its evaporation. Squares changed from four-corner bending to a tubular shape; triangles formed a tetrahedron. Smaller or thicker sheets could bend and then reopen without enclosing the droplet.^[ref]

The elastocapillary length makes the thickness dependence quantitative. For fixed Young's modulus, Poisson's ratio and surface tension, the bending stiffness obeys $B\propto h^3$ and ${\ell }_{\mathrm{ec}}\propto h^{3/2}$. Halving thickness therefore reduces ${\ell }_{\mathrm{ec}}$ by $2^{3/2}$, about $2.83$. At the same lateral size $L$, the sheet elastocapillary energy ratio $\eta =\gamma L^2/B$ increases eightfold. This calculation explains why making the sheet thinner can enable wrapping even without changing its outline.

The sheet elastocapillary energy ratio compares available energy scales; it does not determine a unique final shape. The contact angle, initial liquid volume and outline also matter. A cut chosen to permit several panels to meet is a mechanical design choice, while the surface tension supplies the driving force. Predicting the complete folding path requires more than the scalar energy comparison. The same group reported cross-shaped templates forming a cube and flower-shaped templates forming nearly spherical enclosures.^[ref]

Charlotte Py has investigated elasto-capillarity, including how surface tension deforms an elastic sheet. She is the first author of the 2007 study introducing capillary origami: spontaneous wrapping of a liquid droplet by a flexible sheet.^[ref]

The experiment used thin polydimethylsiloxane sheets cut into different shapes. As water evaporated, surface tension progressively curved the sheet around the diminishing droplet. Square and triangular cuts followed different folding sequences, while sufficiently small or stiff sheets reopened rather than completely enclosing the liquid. This connected an accessible observation with a competition between surface energy and elastic bending.^[ref]

A complementary loop experiment measured the elastocapillary length: a wetting meniscus held a long strip in a loop whose shape could be compared with an elastic calculation. The resulting length scale helped organize the threshold for enclosure across sheet thicknesses and geometries.^[ref]

An elastic sheet is a body whose thickness $h$ is small relative to its lateral dimensions and which responds elastically to deformation. Its geometry separates in-plane stretching from out-of-plane bending. A thin elastic plate is a useful model when the assumptions of linear elasticity and small through-thickness strain apply.

The different thickness dependences explain much of a sheet's behaviour. For uniform uniaxial loading with free lateral contraction, Hooke's law gives $\sigma =E\epsilon$. Multiplying by thickness gives the tensile force per unit width $N=Eh\epsilon$: the uniaxial sheet stretching stiffness is $Eh$. For a homogeneous, isotropic thin elastic plate, its bending stiffness iswhere $E$ is Young's modulus and $\nu$ is Poisson's ratio.^[ref]

For an original scaling example, halve $h$ while keeping material and lateral dimensions fixed. The uniaxial tensile stiffness halves, but the bending stiffness falls to one eighth. Thin sheets can therefore become much easier to bend without becoming equally easy to stretch. In simple bending to radius $R$, a layer a distance $z$ from the middle surface has strain approximately $z/R$; choosing $h=0.1\mathrm{mm}$ and $R=10\mathrm{mm}$ gives outer-layer strain about $0.005$, or $0.5\%$.

The 2007 capillary origami study made this competition observable by placing a water droplet on cut polydimethylsiloxane sheets and following their folding during evaporation. Whether a sheet enclosed the drop depended on size, thickness and outline.^[ref] The sheet elastocapillary energy ratio compares the resulting capillary and bending energy scales.

Elastocapillarity is the coupling between surface tension and elastic deformation. Changing an interface can reduce surface energy while bending a compliant solid increases bending energy. Thin structures can deform strongly when the available capillary energy competes with their elastic resistance.

For an isotropic thin elastic plate, its bending stiffness iswhere $E$ is Young's modulus, $h$ the thickness and $\nu$ Poisson's ratio. A sheet bent over a size $L$ has curvature of order $1/L$. Its bending energy scales as $B(1/L^2)L^2\sim B$, while the capillary energy scale is $\gamma L^2$, where $\gamma$ is surface tension. Balancing these scales gives the elastocapillary lengthHere $B$ has units of energy and $\gamma$ energy per area, so the ratio has units of length squared. At fixed material properties, ${\ell }_{\mathrm{ec}}\propto h^{3/2}$; doubling thickness multiplies this length by $2\sqrt{2}$. Geometry and contact angle enter the more detailed wrapping criterion.^[ref]

The 2007 capillary origami experiments of Charlotte Py and collaborators provide a direct demonstration. They cut polydimethylsiloxane membranes, 40–80 micrometres thick, into planar shapes, placed them on a water-repellent support, added a water droplet and recorded the deformation during evaporation. Suitable triangular sheets folded around the shrinking drop into a tetrahedral enclosure. Smaller or stiffer sheets failed to close completely. The observations connected a controlled material thickness and initial shape to the competition between surface energy and bending energy.^[ref]

For a thin elastic plate interacting with a liquid interface, the elastocapillary length isHere $B$ is the plate's bending stiffness, $\gamma$ the surface tension, $E$ Young's modulus, $h$ the thickness and $\nu$ Poisson's ratio. In this plate convention $B$ has units $\mathrm{N}\mathrm{m}$, while $\gamma$ has units $N/m$; their ratio has units of length squared. The quantity is different from the gravity-dependent capillary length.

To see the balance, bend a portion of sheet of lateral size $L$ through an angle of order one. Its curvature is of order $1/L$, so its bending energy scales as $B(1/L{)}^2{L}^2\sim B$. The competing surface energy scale is $\gamma L^2$. Their dimensionless quantity is the sheet elastocapillary energy ratioLarge $\eta$ means that the capillary energy scale is large relative to the bending energy scale. This dimensional analysis does not make $L={\ell }_{\mathrm{ec}}$ a universal threshold for complete closure in capillary origami.^[ref]

For chosen illustrative values $B=10^{-9}\mathrm{N}\mathrm{m}$ and $\gamma =0.05N/m$, the elastocapillary length is $\sqrt{2\times 10^{-8}}\mathrm{m}\simeq 141\mu \mathrm{m}$. A lateral size of $0.1\mathrm{mm}$ gives $\eta =0.5$, whereas $1\mathrm{mm}$ gives $\eta =50$. These are calculations with assumed parameters, not measurements of a particular material.

Two ways of changing size give opposite trends. Keep Young's modulus, Poisson's ratio and surface tension fixed, and let $s=L/L_0$ be a lateral scale factor. At fixed thickness, $B$ stays fixed and $\eta /{\eta }_0=s^2$. If all sheet dimensions shrink in the same proportion, then $h/h_0=s$, $B/B_0=s^3$ and $\eta /{\eta }_0=s^{-1}$. Halving lateral size alone decreases the sheet elastocapillary energy ratio fourfold; halving lateral size and thickness together doubles it. The phrase "smaller sheets" therefore needs a specified thickness rule.

The length can also be calibrated directly: the 2007 study fitted an elastic-loop model to a long polydimethylsiloxane strip held by an ethanol meniscus. For their complete-wetting configuration, loop width was $0.89{\ell }_{\mathrm{ec}}$. The coefficient belongs to that model and geometry.^[ref]

Use a freely rotating chain: fixed bond length $b$, fixed angle $\vartheta$ between forward bond vectors, and independently random torsion angles. Then $⟨{\hat{t}}_0\cdot {\hat{t}}_n⟩=(\cos \vartheta {)}^n=e^{-nb/{\ell }_p}$, giving the orientational persistence length of a freely rotating chainThe equivalent long-chain Kuhn length divided by two, $b(1+\cos \vartheta )/[2(1-\cos \vartheta )]\simeq 3.48\mathrm{nm}$, is nearly equal here but is a distinct discrete-chain convention. A chemical internal bond angle is supplementary to the forward-vector angle used above.

Synthetic examples are relatively stiff poly(p-phenylene terephthalamide) and flexible polydimethylsiloxane. Light scattering and viscometry established rodlike solution conformations for the former; single-chain mechanical measurements support the latter's flexibility. Persistence is solvent- and model-dependent, so no universal numerical value is inferred for either example.^[ref][ref]

Entropic elasticity. A rubber contains flexible polymer strands tied into a network by cross-links. Stretching biases the strands toward relatively extended configurations, reducing their configurational entropy. The restoring entropic force follows from the increase in Helmholtz free energy $F=U-TS$. For a Gaussian strand with $N_s$ statistical steps of length $b$, its deformation-dependent free energy is approximately $3k_{B}T{R}^2/(2N_s{b}^2)$. Its stiffness therefore increases with absolute temperature, even if the underlying bond stiffness changes little.

In the ideal affine-network model of rubber elasticity, the shear modulus iswhere ${\nu }_s$ is the number density of elastically active network strands. Thus heating increases the modulus approximately in proportion to $T$, provided the network density and rubbery state remain approximately unchanged. Thermal expansion, changing relaxation times or damage can modify that simple trend.

Examples are lightly crosslinked natural rubber, based on cis-rich polyisoprene, and crosslinked polydimethylsiloxane. The crosslinks prevent the long-time macroscopic flow of an unconnected chain solution.

Density estimate and the unspecified modulus convention. With room temperature $T\simeq 298\mathrm{K}$, the Boltzmann constant gives $k_{B}T\simeq 4.11\times 10^{-21}\mathrm{J}$. If the stated modulus is $G=2\times 10^5\mathrm{Pa}$, thenThe molar value counts moles of active strands. If “modulus” instead means Young's modulus $E$, a nearly incompressible isotropic rubber has $E\simeq 3G$, and the inferred value isThus the robust order-of-magnitude estimate is $10^{25}{\mathrm{m}}^{-3}$. The cross-link density inferred from rubber elasticity is usually an effective strand density; the actual junction density is ${\nu }_j=2{\nu }_s/f$ for junction functionality $f$ in an ideal network without inactive loops or dangling ends. For four-functional junctions this would be half the strand density. The paper supplies neither modulus type nor junction functionality, so a unique chemical junction count cannot be extracted.

single-molecule force spectroscopy measures force and extension of an individual tether while controlling position or load. In an atomic-force arrangement, a synthetic chain connects a cantilever probe to a translated substrate. For the cantilever compliance correction, a deflection sensor gives $d$, a calibrated spring constant gives $F=k_{c}d$, and substrate displacement $Z$ gives chain extension $x=Z-d$ after geometric offsets are removed. Additional linkers and instrument compliance must be included if appreciable. Thermal deflection calibration uses $k_c⟨d^2⟩=k_{B}T$ only after isolating the cantilever's calibrated thermal contribution.

An optical-tweezers implementation detects a tethered bead's displacement from a calibrated trap centre, with $F=k_{\mathrm{trap}}\Delta x$ in the harmonic regime. Detector calibration, drag and trap linearity determine the usable force and frequency range. These instruments measure individual force–extension curves and distributions; averaging many curves can hide multiple tether populations.

For a synthetic freely jointed chain with Kuhn length $b$,A strongly stretched worm-like chain instead has $1-x/L\simeq \sqrt{k_{B}T/(4F{\ell }_p)}$ before backbone stretching becomes important. Fits can estimate contour and persistence lengths only in their appropriate regimes. Hysteresis and pulling-rate dependence test whether an apparent mechanical transition is quasistatic or activated.

Control single versus multiple attachments, subtract nonspecific adhesion, vary pulling speed, calibrate temperature and stiffness, and correct drift. A rupture peak is not a universal bond strength independent of loading history. A primary nonbiological example measured individual polydimethylsiloxane chains by atomic-force methods; its flexibility interpretation combines those measurements with molecular calculations.^[ref]

An experimental physicist who coauthored evidence for the polymer brush regime in grafted chains. The collaboration used small-angle neutron scattering on polydimethylsiloxane attached by one end to silicon dioxide. Layer thickness changed with grafting density and solvent quality, showing how neighboring chains force one another to stretch away from a surface.^[ref]

A silicone is a polymeric material with a silicon-oxygen backbone bearing organic substituents, commonly methyl groups. Polydimethylsiloxane is a familiar example.

Backbone flexibility, side groups, chain length, and crosslinking determine whether the material behaves as a fluid, gel, or elastic solid. Silicone is a polymer family and should be distinguished from elemental silicon and inorganic silicon dioxide.

Song Lu coauthored research on polydimethylsiloxane.^[ref]

A flexible silicone polymer that can form an elastomer when lightly crosslinked. The network's recoverable deformation provides an example of rubber elasticity.

ACS Materials Letters 4, 329–335.

Publisher: doi.org/10.1021/acsmaterialslett.1c00655

The primary-paper abstract describes single-chain atomic-force measurements and calculations supporting the flexibility of polydimethylsiloxane. It is a modern material-property reference, not a source supplied with the historical exam.