## Abstract

The localized loading of an elastic sheet floating on a liquid bath occurs at scales from a frog sitting on a lily pad to a volcano supported by the Earth’s tectonic plates. The load is supported by a combination of the stresses within the sheet (which may include applied tensions from, for example, surface tension) and the hydrostatic pressure in the liquid. At the same time, the sheet deforms, and may wrinkle, because of the load. We study this problem in terms of the (relatively weak) applied tension and the indentation depth. For small indentation depths, we find that the force–indentation curve is linear with a stiffness that we characterize in terms of the applied tension and bending stiffness of the sheet. At larger indentations, the force–indentation curve becomes nonlinear and the sheet is subject to a wrinkling instability. We study this wrinkling instability close to the buckling threshold and calculate both the number of wrinkles at onset and the indentation depth at onset, comparing our theoretical results with experiments. Finally, we contrast our results with those previously reported for very thin, highly bendable membranes.

## 1. Introduction

Poking is a natural way in which to test the material properties of an object, both in everyday life (for example, an under-inflated bicycle tyre) or, more quantitatively, in AFM measurements of graphene [1,2] and biological cells [3]. While in many situations the object being poked is a homogeneous bulk material, in others the object is a composite, consisting, for example, of a bulk material with a thin coating. In such scenarios, poking may provide information about the coating, the substrate that is coated or some combination of the two.

The canonical problem to understand the relative roles of coating and substrate is that of a thin elastic film bonded to a substrate. Perhaps the simplest substrate response is one that provides a restoring force linear in the vertical deflection—a Winkler foundation [4]. Physically, this corresponds to an object floating on the surface of a liquid: the hydrostatic pressure within the liquid provides a restoring force that is precisely linear in the vertical deflection. However, this linear response is also commonly used as a model of an elastic substrate—this model assumes that the substrate consists of an array of linear springs and is therefore also known as the mattress model.

At the same time as being relatively simple to formulate mathematically, this scenario is also of interest at a range of scales: at very large scales, floating ice sheets are often used in cold regions as construction platforms for transport routes, airfields and offshore oil exploration sites. Determining the bearing capacity and failure of ice sheets subject to vertical loads is essential when assessing the operational potential of floating ice sheets [5–8]. This requires knowledge of the bending rigidity of sea ice [9,10], which is usually measured by comparison with theoretical results for the loading of a thin floating plate [11,12]. At still larger scales, the loading of ice sheets by surface melt water has been implicated in the catastrophic collapse of the Larsen B ice sheet in Antarctica [13], while at global scales the gravitational loading of the lithosphere by mountain ranges [14,15] and volcanic sea mounts [16] involve much the same physical ingredients.

At the other end of the length-scale spectrum, the elastic properties of thin biological materials may be characterized by measuring the deflection that results from an applied central point force [17–19]. Similarly, the material properties of ultra-thin polymer films can be determined from the readily observable wrinkle patterns that form when floating films are subject to a localized force either from the capillary pressure of a fluid droplet or an imposed displacement from an indenter [20–22]. In both cases, a vertical deflection pulls material radially inwards and in so doing generates a compressive azimuthal stress in the film that ultimately results in a radial pattern of wrinkles. The properties of these wrinkling patterns at very small scales have been extensively studied both ‘near-threshold’ (close to the onset of instability) [23] and ‘far-from-threshold’ (once the wrinkling pattern is well developed) [21,22,24–26]. The key observation is that in highly flexible films, the stress state is qualitatively changed by wrinkling: wrinkling relaxes the stress in the direction perpendicular to the wrinkles [24,27,28]. This may have important consequences for the mean shape of the wrinkled object, which is, in general, different from what would be observed in the absence of wrinkles [22,29]. Furthermore, this wrinkling can have the surprising consequence that the force–displacement response depends not on the mechanical properties of the film (its modulus and thickness), but rather only its geometry (e.g. radius) and other physics in the system [22,29]. As well as their aesthetic appeal, these wrinkle patterns are of interest as a means of generating surfaces with functional patterned topology [30] that may be useful in applications such as wetting [31] and photonic devices [32].

Although the large and small length-scale problems discussed above contain the same physical ingredients, the former are dominated by bending stresses and gravity, while the latter are dominated by the surface tension of the interface, together with gravity. Indeed, it is this influence of the liquid surface tension that distinguishes large scales from small scales. The two problems may therefore be thought of as two limits of an elastic sheet floating at the surface of a liquid and subject to a tension at its boundary. Here, we study the relative effects of the sheet’s bending stiffness and the applied (interfacial) tension, focusing, in particular, on the transition between regimes in which one dominates the other. However, we shall also see that a key third ingredient is the amount of imposed deformation.

The paper is structured as follows: the detailed mathematical model used to describe this system is discussed in §2. The experimental set-up used to study axisymmetric deformations of the floating sheet is described in §3. In §4, axisymmetric deformations are considered theoretically with the results of numerical and analytical arguments compared with experiments. This section finishes with a discussion of what distinguishes ‘small’ and ‘large’ deflections. The onset of wrinkling is detailed in §5, including a linear stability analysis of the axisymmetric state, a description of the experimental technique employed to identify the onset of wrinkling and comparison between experimental results and the linear stability analysis, before conclusions are presented in §6.

## 2. Theoretical setting

We consider an elastic sheet of thickness *h*, Young’s modulus *E* and Poisson’s ratio *ν*, floating on a fluid of density *ρ*. The sheet is subject to a point-like force *F* at its centre (shown schematically in figure 1) which results in the deformation of the sheet. Provided that deformations occur over a length scale that is large compared to the thickness of the sheet, we may model the resulting elastic deformation using the Föppl–von-Kármán equations, incorporating the hydrostatic pressure exerted by the fluid phase on the elastic sheet. Accordingly, the vertical displacement of the sheet from its neutral floating equilibrium, *ζ*(*r*,*θ*), satisfies the vertical force balance equation [22] B∇4ζ−[ζ,χ]=−ρgζ−F2πδ(r)r,2.1where *B*=*Eh*^{3}/[12(1−*ν*^{2})] is the bending stiffness of the sheet, *g* is the acceleration due to gravity, *δ*(*r*) is the Dirac *δ*-function and the operator [*f*,*g*] is given in polar coordinates by [33]: [f,g]=∂2f∂r2(1r∂g∂r+1r2∂2g∂θ2)+∂2g∂r2(1r∂f∂r+1r2∂2f∂θ2)−2∂∂r(1r∂f∂θ)∂∂r(1r∂g∂θ).2.2In (2.1), the Airy stress function *χ*(*r*,*θ*) is a potential for the in-plane stress and is introduced to ensure that the stress within the solid sheet automatically satisfies the equilibrium equation; this is achieved by setting σθθ=∂2χ∂r2,σrr=1r∂χ∂r+1r2∂2χ∂θ2andσrθ=−∂∂r(1r∂χ∂θ).

A second differential equation arises from the ‘compatibility of strains’, the requirement that the strains associated with the stress of a particular stress function, *χ*(*r*,*θ*), match the geometric strains associated with a particular out-of-plane displacement, *ζ*(*r*,*θ*). This condition may be written as ∇4χ=−12Eh[ζ,ζ],2.3where the product *Eh* is the stretching stiffness of the sheet.

Indentation may be achieved by imposing a given force *F* and measuring the indentation depth *ζ*_{0} that results, or by imposing an indentation depth and measuring the force required to produce this indentation. Both techniques were employed in our experiments, described in §3, and are mathematically equivalent in terms of the model developed here. However, in numerical calculations, it is simpler to prescribe the indentation depth *ζ*(0)=*ζ*_{0} and calculate the force *F* that is required to achieve this level of indentation subsequently. The conditions imposed on *ζ* at the indentation point are therefore the indentation depth, that the sheet does not have a cusp and the requirement of zero horizontal displacement, ζ(0,θ)=−ζ0,∂ζ∂r|(0,θ)=0,up up Go amp; Red M29 amp; Red amp; up M29 Go Go ur(r=0)=0.2.4The last condition on the horizontal displacement at the origin is equivalent to a condition on the hoop strain, limr→0[rϵθθ]=0, which may, using Hooke’s Law, be restated as a condition on the stress distribution at the origin, and hence on the derivatives of the Airy stress function *χ*, namely limr→0 [r∂2χ∂r2−ν∂χ∂r−ν1r∂2χ∂θ2]=0.2.5We also have an arbitrary choice of gauge in *χ* (because it is only the derivatives of *χ* that have physical relevance), and hence we take χ(0,θ)=0.2.6

We consider a sheet where out-of-plane deformation occurs over a distance much smaller than the radial extent of the sheet. The effect of the finite radius of the sheet is known to play an important role in the development of wrinkle patterns in very thin sheets [22]. Here, we use larger sheets for which the effects of finite size are negligible (we shall discuss later what ‘large’ means in this context). We therefore expect that, far from the indenter, the sheet will return to its undeformed, freely floating position, i.e. ζ,∂ζ∂r→0as r→∞.2.7In the far field, we imagine that the sheet is subject to a homogeneous, isotropic tension which, in our experiments, arises from the surface tension of the liquid, *γ*_{lv}; we therefore have *σ*_{rr},*σ*_{θθ}→*γ*_{lv} as r→∞, which requires that χ∼γSeven Women's Handmade Heel Boots Low Up Leather Lace Knee Black Nine The Round Suede Toe Over 1qt1SdRlvr22as r→∞.2.8

### (a) Non-dimensionalization

In this paper, we seek to describe both relatively thick sheets (where we expect the applied, far-field tension due to surface tension to be a perturbative effect) and thinner sheets where this tension is important. We, therefore, choose a non-dimensionalization that does not break down in the limit *γ*_{lv}→0. In particular, we let Z=ζh,R=rℓg,Ψ=χBandF=F(Bh/ℓ2g),2.9where ℓg=(Bρg)1/42.10is the *elasto-gravitational* length scale over which the deformation of the elastic sheet produces a bending stress comparable with the buoyancy force from the fluid.

With this non-dimensionalization, we find that (2.1) becomes ∇4Z−[Z,Ψ]=−Z−F2πδ(R)R,2.11while (2.3) becomes ∇4Ψ=−6(1−ν2)[Z,Z].2.12Equations (2.11)–(2.12) are to be solved subject to the boundary conditions Z(0)=−δ=−ζ0h,Z′(0)=0,limR→0[R∂2Ψ∂R2−ν∂Ψ∂R−ν1R∂2Ψ∂θ2]=0,Ψ(0)=0.2.13Far from the indenter, we also have Z,Z′→0,Ψ→12τR2as R→∞.2.14Here, τ=γlv(ρgB)1/22.15is the dimensionless ‘applied tension’. We note that *τ* is the ratio of the relevant applied stress (surface tension, *γ*_{lv}) to the bending stresses when deformations occur on a length scale ℓ_{g}, i.e. *B*/ℓ^{2}_{g}; hence *τ* may also be thought of as a ‘mechanical bendability’, *ϵ*Subtle Thermoball Green Face Button Smoked Pearl North Shiny Grey up Prior The Season Womens UPqTvxtw^{−1}_{m} in the terminology of Hohlfeld & Davidovitch [34]. In our experiments, *τ* was varied predominantly by changing the thickness of the sheets, but also by changing the interfacial tension, to attain values in the range 10−3≲τ≲30. This range covers a wide range of behaviours and allows us to observe the beginning of the transition to extremely bendable, ultra-thin films with τ≳104 that have been studied previously [22,26].

Another measure of the bendability of a thin elastic sheet exists, besides the mechanical bendability *τ*: as indentation will itself induce a stress within the sheet, there is also a ‘geometrical bendability’ [34]. To determine this geometrical bendability, we note that if an indentation of amplitude *ζ*_{0} decays over a horizontal length scale ℓ_{*}, then the geometry-induced stress is *Eh*(*ζ*_{0}/ℓ_{*})^{2}, while the bending-induced stress is B/ℓ2∗. The geometrical bendability is, therefore, ϵ−1g=Ehζ20B∼(ζ0h)2=δ2.2.16This geometrical bendability is simply the square of the dimensionless indentation depth, *δ*, up to constants whose only dependence on the sheet’s properties is through the Poisson ratio *ν*.

Our problem is therefore governed by two dimensionless parameters: the geometrical and mechanical bendabilities, *ϵ*^{−1}_{g} and *ϵ*^{−1}_{m}, respectively. While one might expect, on counting grounds, there to be another quantity measuring the significance of bending stresses to the stretching stiffness of the sheet, i.e. *q*=(*Bρg*)^{1/2}/(*Eh*), we note that this *q*∝(*h*/ℓ_{g})^{2}, which must be small for our use of the Föppl–von Kármán equations to be appropriate. Nevertheless, this ‘nearly inextensible’ limit is a regular limit [22].

Focusing instead on the two parameters *δ*=*ϵ*^{−1/2}_{g} and *τ*=*ϵ*^{−1}_{m}, we note that the geometrical bendability is independent of the bending stiffness of the sheet, liquid density and applied tension while the mechanical bendability depends on all of these and is, instead, independent of the imposed indentation. We also emphasize that the behaviour of the limits *τ*≪1 and *τ*≫1 is quite different. In the limit *τ*→0, the problem is perfectly regular, but only the parameter *δ* remains. As a result, we expect the behaviour of the sheet to be determined only by the value of *δ*. A consequence of this is that features of the wrinkling instability in the sheet (e.g. the critical indentation depth at which wrinkles appear) must be described by order 1 numbers as *τ*→0: we can immediately see that the dimensionless critical indentation depth *δ*_{c}=*O*(1), so that the dimensional critical indentation depth ζ(c)0∝h, and the number of wrinkles at onset *n*_{onset}=*O*(1) also. By contrast, when *τ*≫1 (*ϵ*^{−1}_{m}≫1), both of the dimensionless parameters *τ* and *δ* will matter; in particular, we should expect to observe a dependence of *δ*_{c} and *n*_{onset} on *τ*. In table 1, we highlight the relevant dimensionless groups (DGs) observed in each of the regimes *τ*≪1 and *τ*≫1, as well as focusing on which features of the problem have been studied previously, are the focus of this work, or remain open problems for future work.

## 3. Experimental measurements of axisymmetric deformation

Initially, a series of experiments were performed on relatively large floating elastic sheets for which the mechanical bendability was small, *τ*≪1. In this series of experiments, detailed in §3a, sheets of varying thickness *h* were indented with a known applied force and the resulting, axisymmetric, profiles of the sheets were measured. A schematic diagram of the experimental apparatus used to measure the elastic response of a floating sheet to a localized load is shown in figure 1*b*. Further experiments were then performed on smaller, thinner sheets of varying bending stiffness *B* to assess the influence of *τ*. In these experiments, described in §3b, the centre of the sheet was indented to a known displacement and the force required to achieve such a deformation was measured. Together, the results from both sets of experiments map the transition from a regime in which bending controls the axisymmetric deformation to one in which the in-plane tension dominates instead. The experimental techniques used to study the wrinkling that occurs for large-amplitude deformation are described separately, in §5b.

### (a) Low mechanical bendability, *τ*≪1

A first series of experiments were performed using a range of circular sheets of polydimethylsiloxane (PDMS) with diameter D≳0.5 m and thickness h≳1.5 mm. These sheets were produced by spreading a commercial silicone elastomer (Sylgard 184, Dow Corning, UK) on a carefully levelled table, and then curing the sample for one week in a temperature-controlled room that maintained the temperature in the range 40–45°C. Young’s modulus and Poisson’s ratio of these sheets were measured by performing compressive tests using an Instron 3345 and were found to be *E*=2.06±0.03 MPa and *ν*=0.50±0.01, respectively. The detailed properties of the PDMS sheets used in these experiments are given in table 2.

For each experiment, an elastic sheet was carefully positioned on top of a layer of water contained within a tank of square cross section and area 50^{2} cm^{2} or 1 m^{2}, depending on the diameter of the sheet in use. The density of PDMS, *ρ*_{PDMS}≈929 kg m^{−3}, is less than that of water at 20°C, *ρ*=998 kg m^{−3}, so that the sheet floats in equilibrium. The edge of the elastic sheet was freely floating (with no normal force or bending moment applied). However, spacers attached to the internal tank walls reduced the size of the tank cross section to that of the sheet diameter at four positions and contacted the sheet to ensure it did not rotate during experiments, while minimizing any effect on the stress within the sheet.

In these experiments, the mechanical bendability was calculated to be τ≲10−2. The relative insignificance of surface tension was confirmed by adding surfactant (washing-up liquid) to the liquid bath. The addition of surfactant reduced the surface tension of the fluid from *γ*_{lv}=72.8 Nm^{−1} to *γ*_{lv}=24.9 Nm^{−1}, as was measured using a Drop Shape Analyser (DSA100, Kruss GmbH, Germany). At the concentrations used, the density of the water remains unaltered. Despite a reduction in surface tension of more than a factor of two, the results obtained here were quantitatively indistinguishable. Further, our surface tension measurements did not change when compared before and after the experiment: any free polymer chains released by the sheets did not modify the surface tension of our (relatively large) bath significantly, as has recently been reported for small droplets [36].

A localized force was applied to the centre of the floating sheet using an indenter of length 300 mm, diameter 6.0±0.05 mm with a hemispherical end cap (making contact with the sheet). The radius of this contacting cap, *r*_{cap}≈3 mm, is significantly smaller than the relevant horizontal length scale (**Red M29 Go amp; up Go amp; amp; up Red up M29 Go** ℓg≳15 mm throughout this series of experiments); we therefore expect the point indenter approximation to be reasonable, as we shall discuss in due course. The indenter was weighted to obtain a given applied force in the range 0.34–20.76 N with an accuracy of ±0.01 N, and was held inside a guiding tube to ensure the application of a central, vertical force.

For a small applied force, and therefore small indentation depth, the vertical deflection of the sheet remained axisymmetric. The magnitude of this axisymmetric deformation was determined by digitally imaging the deflection of a line drawn along the bottom surface of the sheet. The line was approximately 2 mm in width, fluorescent and illuminated using a blue-light LED lamp. The entire sheet was imaged using a Nikon D5000 with a resolution of 4288×2848 pixels which was positioned at 27° to the horizontal and perpendicular to the line. A high-pass filter positioned between the line and imaging camera produced a high-contrast image, enabling the line to be distinguished from other features in the experiment. The deflection of the line was measured with respect to a reference image of the undeflected line. Vertical deflections were resolved to within 100 μm by fitting a Gaussian profile across the line, and processing the differences between images of the deflected line and the reference image [37].

### (b) Moderate mechanical bendability, τ≳10−1

Further experiments were performed on thinner sheets for which the mechanical bendability was no longer small (in particular, τ≳0.1). To obtain significantly thinner sheets of uniform thickness, we used spin coating of two grades of polyvinylsiloxane (PVS) elastomer (Elite Double 8 and 22, Zhermack, Italy). The thickness of the spin-coated sheets was measured prior to experimentation using a microscope (Leica DMIL, Leitz Wetzlar, Germany). Young’s modulus of the cured elastomers were measured by performing tensile tests on a structural testing machine (Instron 3345, Instron, UK) and found to be 200±13 kPa and 801±18 kPa, respectively, with *ν*=0.5 in both cases.^{1} Experiments were also conducted on a Polyimide (PI) sheet of *h*=8.5±2.0 μm, *E*=3.7±0.7 GPa and *ν*=0.34 (supplied by Goodfellow, Cambridge). The material properties of the PVS and PI sheets are detailed in table 2.

Limitations of spin coating meant it was not possible to obtain very large, thin sheets. Here, we used circular sheets of diameter *D*=89±0.5 mm, floating on a layer of water contained within a petri dish of inner diameter *D*=91±0.5 mm.

The petri dish containing water and a floating thin sheet was itself positioned upon a microbalance (Pioneer PA64C Analytic Balance, Ohaus, Switzerland). The centre of the sheets were indented by a needle tip of diameter 0.4 mm attached to a linear actuator (M228, Physik Instrumente, Germany) that was driven by a computer-controlled stepper motor (Mercury Step C663, Physik Instrumente), reported vertical deflections were accurate to 0.1 μm. The applied force was measured by recording the mass reported by the microbalance (accurate to within 0.1 mg).

## 4. Axisymmetric deformations

Having outlined the experimental techniques used for studying axisymmetric deformations, we now return to the theoretical setting discussed in §2, and specialize to the case of axisymmetric deformations, i.e. *Z*(*R*,*θ*)=*Z*(*R*).

### (a) Numerical solution

For axisymmetric deformations, the vertical force balance and compatibility equations, (2.11) and (2.12), become a pair of coupled, nonlinear ordinary differential equations 1RddR{RddR[1RddR(RdZdR)]}−1RddR(dZdRdΨdR)=−Z−F2πδ(R)R4.1and RddR[1RddR(RdΨdR)]=−6(1−ν2)(dZdR)2,4.2subject to force and symmetry boundary conditions on the deflection at the origin, Z(0)=−δ,Z′(0)=limR→0[RΨ″−νΨ′]=Ψ(0)=04.3and far-field conditions Z,Z′→0,Ψ→12τR2(R→∞).4.4

The system of equations (Power Rasolli Closed Purple Back Flower Women's Professional Clogs xYrgaYq6)–(Yellow Cushioning Balance Team Solar Shoe Trail Pigment Royal Running Women's 410v5 New PRdqwtt) can readily be solved numerically using, for example, the Matlab routine `bvp4c`. This numerical solution is computed on a finite domain, [0,*D*/(2ℓ_{g})], where we use *D*/ℓ_{g}=2000 to ensure that the domain is large enough that its finite size is not apparent when comparing with our analytical results (which are calculated with D/ℓg=∞). This yields predictions for the axisymmetric shape *Z*(*R*) and the stresses within the sheet, and may also be used to determine the indentation force F required to produce a given indentation depth *δ*, because the first integral of (4.1) gives F=−2πlimR→0{RddR[1RddR(RdZdR)]}.4.5The force–displacement relationship calculated for *τ*=0 is shown as the solid curve in figure 2*a* along with the results from experiments, obtained for τ≲10−2 and detailed in §3a. In figure 2*b*, the numerically determined force–displacement relationship is shown for a variety of values of *τ* together with experimental results for 10−1≲τ≲30, detailed in §3b. Both the numerical and experimental results reveal the existence of two apparent regimes in the force–displacement law: for ‘small’ displacements, δ≲1, the displacement of the sheet scales linearly with the applied force, while for ‘large’ displacements, δ≳1, the force scales with the square of the imposed displacement. Moreover, the results shown in figure 2*b* also expose a dependence of the force–displacement response on the mechanical bendability *τ* that appears to only be present for ‘small’ displacements. We, therefore, turn to try and understand these relationships analytically and to quantify more precisely what is meant by ‘small’ and ‘large’ displacements.

### (b) Small displacement theory

For small displacements, we expect that the stress within the sheet should remain axisymmetric (independent of *θ*), being close to the unperturbed value set by the far-field tension (or mechanical bendability), and, further, that the vertical displacement will be everywhere small. Following a similar analysis for the indentation of pressurized elastic shells [38], we seek small deviations from this uniform tension state and so let Ψ=τR2/2+∼Ψ and Z=∼Z. Hence (4.1) and (4.2) may be linearized to give ∇4∼Z−τ∇2∼Z+∼Z=−F2πδ(R)R4.6and RddR[1RddR(Rd∼ΨdR)]=0.4.7

The solution of (4.6) can be found by noting that solutions of the Helmholtz equation ∇2∼Z=λ∼Z are also solutions of (4.6) if λ2−τλ+1=04.8and hence that λ=λ±=12(τ±√τ2−4).4.9We, therefore, have that the relevant general solution for small vertical deflections is ∼Z=αK0(λ1/2+R)+βK0(λ1/2−R),4.10where *K*_{0}(*x*) is the modified Bessel function of zeroth order and the constants *α* and *β* need to be chosen to satisfy the boundary conditions as *R*→0. (The boundary conditions as R→∞ have already been satisfied by our choice of the solution of the Helmholtz equation—we have neglected the possibility of any solutions ∝*I*_{0}(*x*), which would diverge as amp; Go amp; M29 Go Red up amp; Red M29 up Go up x→∞.) We find that ∼Z=−2δlog(λ−/λ+)[K0(λ1/2+R)−K0(λ1/2−R)].4.11It is possible to repeat this calculation to account for the effect of a finite-sized indenter, *r*_{in}. We find that the prefactor in (4.11) is correct to *O*(*r*_{in}/ℓ_{g}) and hence the limit of a point indenter, *r*_{in}/ℓ_{g}→0, is regular. (This regularity is a result of the finite bending stiffness of the sheet, and is distinct from the indentation of a membrane, where a logarithmic dependence on the indenter radius was found [39] analytically, although a power-law correction has also been claimed [40].) In the majority of our experiments, rin/ℓg≲0.1≪1 and hence the effect of indenter size may be neglected. Finally, we note that, at this order, the perturbed Airy stress function ∼Ψ=0: from (4.7), ∼Ψ=AR2+BlogR+C, which cannot satisfy the boundary conditions unless *A*=*B*=*C*=0.

To compute the force required to produce the displacement in (4.11), we use (4.5), which gives that F=K1δ,4.12where K1=2π(τ2−4)1/2arctanh[(1−4/τ2)1/2],4.13is the dimensionless ‘stiffness’, or spring constant, of the floating sheet.

It is important to note that the dimensionless stiffness (4.13) is a function solely of *τ*, as defined in (2.15). In figure 3, experimental values of *K*_{1} are shown as a function of *τ* alongside the theoretical result (4.13). (For definiteness, experimental calculations of the spring constant used experimental data with *δ*<1.)

We note that, in the limits of small and large mechanical bendabilities, the dimensionless stiffness takes the values K1∼{8,τ≪12πτlog(4τ),τ≫1.4.14For *τ*≪1, the stiffness of the sheet becomes insensitive to the value of that tension (because the restoring force is provided predominantly by the bending stiffness of the sheet). In dimensional terms, we have that, for *τ*≪1, F≈8Bℓ2gζ0=8(Bρg)1/2ζ0,4.15which is a result derived first by Hertz [35]. For large mechanical bendability, *τ*≫1, however, the stiffness of the sheet is instead dominated by the surface tension of the interface; the corresponding dimensional result is F≈2πγlvlog(4τ)ζ0.4.16In this limit, the bending stiffness of the sheet enters only via a logarithmic correction.

### (c) Large displacement scaling analysis

The theoretical analysis just presented for small displacements relied on the stress state within the sheet remaining close to its pre-indentation levels. However, as the indentation, *ζ*_{0}, increases, the sheet is forced to stretch over a horizontal region of size ℓ_{*} (with ℓ_{*} currently unknown). This stretching induces a strain ∼(*ζ*_{0}/ℓ_{*})^{2} and hence costs an elastic energy ∼Eh(ζ0/ℓ∗*Go Go amp; Red amp; amp; Red up Go up M29 M29 up* )4ℓ2∗=Ehζ40/ℓ2∗. As this elastic energy decreases as the sheet stretches over a greater horizontal distance (the strain is smaller), it is tempting to assume that ℓ_{*}=*R*_{sheet}, the radius of the sheet. However, such a deformation is extremely expensive in terms of the gravitational potential energy of the liquid that is displaced, ∼ρgζ20ℓ2∗. Instead, an indentation-dependent horizontal scale ℓ∗∼(Ehζ20/ρg)1/4 emerges that minimizes the sum of gravitational and elastic energies. Using this estimate of ℓ_{*} in the above energy estimates, we find that the total energy of the system then scales like (Ehρg)1/2ζ30, which must balance the work done in indentation, *Fζ*_{0}. This argument predicts that the indentation force F∼(Ehρg)1/2ζ20, or in dimensionless terms that F∼δ2,4.17with a prefactor that is independent of *τ*. This scaling is consistent with both numerical and experimental results shown in figure 2. However, it seems possible that this scaling might fail with *τ*≫1; for example, the relevant stretching energy might be that in the flat portion of the membrane, r≳ℓ∗, rather than that induced by the out of plane deformation. We shall carefully consider this possibility shortly.

Profiles of the deflection of the PDMS sheets measured as a function of radial position are shown in figure 4 for various ratios of indentation displacement to sheet thickness, *δ*=*ζ*_{0}/*h*. Naturally, an increase in the applied load resulted in greater deformation of the elastic sheet. For the results shown in figure 4*a* the indentation of the sheet is less than the thickness of the sheet, *δ*<1, while in figure 4*b* the indentation is greater than the sheet thickness, *δ*>1 (though in all cases plotted in figure 4, the measured deformation of the sheet remains axisymmetric). For small deformations, the normalized indentation displacement, *ζ*/*ζ*_{0}, is plotted as a function of the radial distance scaled by the elasto-gravity bending length, * Go Go Red M29 up amp; up amp; M29 Go amp; up Red r*/ℓ

_{g}, in figure 4

*a*; we observe good collapse, particularly with the smallest

*δ*≪1. By contrast, for large deformations, shown in 4

*b*, the normalized indentation displacement

*ζ*/

*ζ*

_{0}is plotted as a function of the radial distance

*r*scaled by the horizontal scale that emerges from the large displacement scaling analysis ℓ∗∼(Ehζ20/ρg)1/4—we see that plotting the data in this way provides a better collapse in this regime than would be obtained by using

*r*/ℓ

_{g}(see inset of figure 4

*b*). For both small and large displacements, we see that the vertical deflection of the edge of the sheet is negligible, though this is expected to break down for very large indentations, i.e. once ℓ

_{*}∼

*R*

_{sheet}.

Figure 5*a*–*c* presents numerically determined profiles of the hoop stress, *σ*_{θθ}, within the sheet for *τ*=0.1,1 and 10, and different values of the indentation depth *δ*. These stress profiles show that the stress differs from the applied (interfacial) tension only near the indenter, and also that the indenter’s region of influence grows with increasing indentation depth. The key feature of these plots is, however, that the hoop stress becomes increasingly compressive as *δ* increases—this compression ultimately leads to wrinkling, as we shall see in §5.

The scaling law that led to (4.17) predicts that the stresses within the sheet, *σ*_{ij}∼*δ*. It is, therefore, natural to test this scaling law by rescaling the numerical results of figure 5*a*–*c* using a lateral length scale *δ*^{1/2} and stress scale *δ*. This collapse is shown in figure 5*d* and supports the validity of the scaling argument as already presented. However, two DGs, both *τ* and *δ*, influence the behaviour and hence it seems plausible that some *τ*-dependence may remain. To test this possibility, we use the rescalings suggested by our scaling analysis to rescale the full, axisymmetric dimensionless problem (4.1)–(4.2). In particular, we let ∼R=Rδ1/2,∼Z=Z(R)δand∼Ψ=(Ψ−12τR2)/δ24.18and find that the system of equations (Patricia Women's Pink Green Slippers Chloe CCRwqWngvr)–(4.4) becomes δ−21∼Rdd∼R{∼Rdd∼R[1∼Rdd∼R(∼Rd∼Zd∼R)]}−1∼Rdd∼R[d∼Zd∼R(τδ∼R+dΨdR)]=−∼Z−F2πδ2δ(∼R)∼R4.19and ∼Rdd∼R{1∼Rdd∼R[∼R(τδ∼R+d∼Ψd∼R)Grey Shoe Easy Climacool Boat outdoor Sleek Orange Women's Chalk adidas White Water Terrex Mid xWnz7C0qR0]}=−6(1−ν2)(d∼Zd∼R)2,4.20subject to ∼ZIV Columbia Masochist Mountain Trail Running Montrail Women's Shoe Ancient Dark Fossil Mirage O7npxInr(0)=−1,∼Z′(0)=lim∼R→0[∼R∼Ψ″−amp; up M29 M29 Red amp; up Go amp; Red Go up Go ν∼Ψ′]=∼Ψ(0)=04.21and far-field conditions ∼Z,∼Z′→0and∼Ψ→0(∼R→∞).4.22

This rescaling shows that the effect of the bending stiffness (the first term on the L.H.S. of (4.19)) may be neglected for *δ*≫1, apart from a small boundary layer near the origin. Interestingly, this rescaling also reveals that the effect of the mechanical bendability is perturbative, provided that the indentation depth is sufficiently large that *τ*/*δ*≪1. Therefore, in the limit δ≫max{τ,1}, a universal problem is recovered and the problem, including the force law (4.17), is indeed independent of the mechanical bendability *τ*, even for *τ*≫1.

### (d) Transition from small to large displacements

To understand what is meant by large and small displacements, we now compare the two force laws given by (4.12) and (4.17). We expect that these two forces become of the same order when δ∼K1(τ)4.23and hence that the transition between the linear and quadratic regimes will occur when the dimensionless displacement is comparable to the dimensionless stiffness of the sheet, i.e. *δ*=*O*[*K*_{1}(*τ*)]. As K1(τ)∼max{1,τ/log(τ)}, we note that the criterion (4.23) for the transition between small and large indentation depths is also consistent with the condition δ≫max{τ,1} for which the rescaled problem (4.19)–(4.22) becomes universal.

The analysis of this section has characterized the axisymmetric behaviour of the sheet. As the load, F, or, equivalently, the indentation depth *δ*, increases, the stresses within the sheet are changed from the uniform, homogeneous tension applied by surface tension initially. As might be expected, the application of a load generally stretches the sheet, increasing the magnitude of the stress. However, indentation also acts to pull material within the sheet to a smaller radial coordinate: to fit within this smaller circle, the hoop stress, *σ*_{θθ}, becomes relatively compressive (e.g. figure 5 and stress profiles for the membrane, τ=∞, case [Womens 6M Nubuck Shoes Elsa Shoe Drew 73010 Navy Uxz1qn6w]). The degree of relative compression increases with indentation depth and, at sufficiently large *δ*, the hoop stress becomes absolutely compressive, *σ*_{θθ}<0. Very thin membranes (*τ*≫1) offer very little resistance to bending [22], and so this compression signals the onset of wrinkling. However, to determine this onset of wrinkling for finite mechanical bendability requires more detailed consideration, and it is to this that we now turn.

## 5. Large-amplitude deformation: the onset of wrinkling

In the limit of infinite mechanical bendability, τ=∞, it was shown previously [22] that the hoop stress first becomes compressive when ζ0=ζ(c)0≈11.75ℓc(γlvEh)1/2,5.1which in the non-dimensionalization used here reads δc=ζ(c)0h≈11.75[12(1−ν2)]1/2τ.5.2It was also shown experimentally that very thin membranes do indeed wrinkle at this indentation depth, to within experimental resolution.

However, sheets of finite mechanical bendability are of most interest here and do, by definition, have a finite resistance to bending. As such, they may accommodate some compressive stresses before buckling. We, therefore, expect that there will be a *τ*-dependent critical indentation depth *δ*_{c}(*τ*) at which a wrinkled solution first exists. Determining this critical indentation depth should also reveal the properties of the wrinkle pattern at onset. We, therefore, focus on the behaviour of the system close to the threshold of wrinkling: this is a ‘near-threshold’ analysis, rather than the ‘far-from-threshold’ analysis in which the stress field is fundamentally changed to relax compression [22Jouston Tommy Women's Navy Hilfiger Oxford xHr5fEw6qr,24].

### (a) Linear stability analysis

We seek a solution of (2.11) and (2.12) that is a small perturbation of the axisymmetric solution found in §4. We, therefore, let
*Ψ*→*Ψ*_{(0)} and *Z*→*Z*_{(0)}, i.e.
**up up amp; Go Red Red Go M29 amp; Go up M29 amp;** (
*f*′ denotes differentiation with respect to *R* and the operator

Equations (5.3) and (5.4) are to be solved subject to the boundary conditions that the perturbation to the displacement and its slope must vanish both at the indenter and as
*Ψ*_{(1)}(0)=0.

The problem (5.3)–(5.8) is a quadratic eigenvalue problem for *n*^{2} [41]. We solve this problem numerically by first solving the axisymmetric problem via relaxation (using `bvp4c` in Matlab). With this solution, we then discretize the resulting linear equations for *Ψ*_{(1)} and *Z*_{(1)} using centred finite differences and solve the resulting quadratic eigenvalue problem by restricting *n* to be an integer and determining the smallest value of *δ* for which the linear system has vanishing determinant. This gives a range of critical indentation depths *δ*_{c}(*n*), which can then be minimized to give the smallest value of *δ* at which wrinkles may occur, as well as the corresponding number of wrinkles at the onset of wrinkling, *n*_{onset}. The results of this numerical analysis, together with the results from experiments focused on the onset and form of wrinkling, are detailed below.

### (b) Experimental investigations of the onset of wrinkling

To explore the onset of wrinkling, further experiments were performed on the elastic sheets described in §3. An image of the relatively large-amplitude wrinkles observed with a thick PDMS sheet, for *δ*≫*δ*_{c}, is shown in figure 6. The key parameters of interest here, however, are those determined by our near-threshold analysis, namely the critical indentation depth at which wrinkling first occurs, *δ*_{c}, and the number of wrinkles present at the onset of wrinkling, *n*_{onset}. (We do not investigate how the wrinkle patterns evolve beyond onset, which has been studied in detail for sheets with *τ*≫1 [26].) The physical properties of the sheets used in these experiments are summarized in table 3.

As before, relatively thick PDMS sheets and thin PVS sheets (material properties as detailed in table 3) were floated on water and indented until the wrinkles became visible so that the number of wrinkles could be counted by eye. Additional experiments were performed on a PI sheet (detailed in §3b) and a polycarbonate (PC) sheet of *h*=2.2 μm and *E*=2.73 GPa and *ν*=0.37 (supplied by Goodfellow, Cambridge). The experiments performed on the PI and PC sheets were performed with the sheets floating on water (*γ*_{lv}=72.81±0.12 dyn cm^{−1}) and also on a well-mixed solution of water and washing-up liquid (*γ*_{lv}=24.85±0.12 dyn cm^{−1}, measured as described previously). The variation in the sheet thickness and material, as well as of the liquid–vapour surface tension *γ*_{lv} permitted the variation of *τ*: here we report experiments with

### (c) Linear stability and experimental results

The key quantities of interest are the critical depth, *δ*_{c}, at which wrinkling begins and *n*_{onset}, the number of wrinkles observed at this onset. Figure 7*a*,*b*, therefore, shows how *n*_{onset} and *δ*_{c}, respectively, vary with the dimensionless mechanical bendability *τ*. The experimental observations of both the number of wrinkles at onset and the critical indentation depth broadly agree with the results of the linear stability analysis. In particular, both theory and experiment illustrate that the number of wrinkles and onset indentation are approximately constant for small mechanical bendability, *τ*≪1. This is as should be expected: recall that the limit *τ*=0 is regular and so, for *τ*≪1, the problem is governed by the indentation depth *δ* alone (or equivalently, the geometrical bendability *ϵ*^{−1}_{g}=*δ*^{2}). This implies that the wrinkling instability must occur at some critical value *δ*_{c}, independently of *τ*. This critical value *δ*_{c} must therefore be some *O*(1) constant for *τ*≪1 (in agreement with the numerical and experimental results).

In the limit of large mechanical bendability, *τ*≫1, we find that the numerical results for the indentation depth at onset, *δ*_{c}, are consistent with previous results for
*b* for comparison. In this limit, our numerical results for the wrinkle number suggest
*n*_{onset}∼*τ*^{1/2}. We emphasize that this apparent scaling law is simply the transition between different scaling laws (*n*_{onset}=*O*(1) at *τ*≪1 and *n*_{onset}∼*τ*^{2/3} at *τ*≫1) and should not be relied on. This is similar to the behaviour observed in a related, near-threshold, buckling problem [42]. Finally, we note that as *δ*_{c}/*τ*∼*τ*^{−1/3}→0 as
*τ*≫1: such sheets will wrinkle before they reach the limit *δ*/*τ*≫1 for which the axisymmetric state becomes universal and the length scale ℓ_{*}∝*δ*^{1/2} emerges (figure 5*d*). Whether similar scalings persist far from threshold remains to be seen.

For many applications, it may also be interesting to understand how the indentation depth required for wrinkling varies with sheet thickness as the other, material, properties of the system are maintained. In particular, with fixed *E*, *ρg* and *γ*_{lv}, the dimensional indentation depth at the onset of wrinkling has a minimum as the sheet thickness *h* varies. To see this, consider first a scaling point of view: one expects
*τ*≪1, while previous work [22] showed that
*τ*≫1 (see equation (5.1), for example). These qualitatively different scalings of
*h*, combined with the monotonic decrease of *τ* with *h* (*τ*∝*h*^{−3/2} from (2.15)) lead us to expect that
*τ* alone:
*b*) with the minimum located at *δ*_{c}/*τ*^{2/3}≈12.6 and *τ*^{−2/3}≈0.27 for *ν*=0.5. Our experiments were not able to reproduce this minimum cleanly but, when combined with previously published experimental data [22], do show a clear minimum.

The appearance of a minimum in the indentation depth required for wrinkling is surprising at first, but may be understood qualitatively by recalling that wrinkling requires both a sufficient level of compression and a sufficiently low bending rigidity. Thin sheets have a high mechanical bendability (*τ*≫1) and so the precise value of their bending rigidity is irrelevant. Instead, the threshold for wrinkling is governed by the compression level: wrinkling occurs when the azimuthal compression induced by indentation overcomes the applied (interfacial) tension. As a result, when the tensile load is reduced (e.g. by using a thicker, but still ‘thin’, sheet), a lower compression level is needed to induce wrinkling. At the other end of the spectrum, thick sheets have a low mechanical bendability (*τ*≪1) and hence can withstand large compressive forces before buckling through wrinkling. As a result, the threshold for wrinkling of such sheets is governed by the bending rigidity: the thinner a ‘thick’ sheet is, the lower is the compression level required for wrinkling. Between these two extremes, the indentation depth required for wrinkling is minimized.

## 6. Discussion and conclusion

In this paper, we have investigated the response of a floating, elastic sheet to an applied, localized load focusing on the limit of low-to-moderate mechanical bendability,
*Fζ*_{0}, giving a linear force–displacement relation. For large indentation depths, the deflection of the elastic object occurs over the horizontal length scale
*ζ*_{0} (though we emphasize that the development of wrinkling far beyond threshold may return the system to a linear force law [22]).

We began this study by posing the question of which material we feel when we poke a sheet that coats a liquid layer. We can now answer this question, assuming our poking is limited to small vertical displacements, by examining the small indentation spring stiffness
**amp; amp; Go up Go up Red M29 amp; M29 Go Red up** ρ
*τ*≪1), the linear stiffness is a mixture of that due to the substrate and that due to the sheet itself. This observation can be rationalized by the fact that the limit of zero mechanical bendability, *τ*=0 is regular, and determined entirely between the balance between the bending stiffness of the sheet and the hydrostatic pressure within the liquid. However, for sheets with high mechanical bendability (*τ*≫1) this stiffness is instead dominated by the surface tension of the interface with the mechanical properties of the sheet entering only via a logarithmic correction. In the analogous case of a Winkler foundation—an elastic composite comprising a thin sheet bonded to a substrate that provides a linear restoring force—we anticipate that a similar result will hold: for relatively unbendable sheets the stiffness will result from a combination of the sheet and the substrate, while for highly bendable sheets the stiffness will be dominated by any boundary tension existing in the sheet prior to indentation.

Larger indentations cause a significant perturbation to the stress (compared with the stress prior to indentation). This is the origin of the emergent length scale ℓ_{*}, and the transition between the small-displacement and large-displacement force laws. However, another consequence of the change in the stress is that the hoop stress becomes compressive: material is pulled to a radial position at which its natural length is too great. If this compression becomes large enough, the sheet relieves this frustration by buckling out of the plane, with radial wrinkles forming. We have analysed the onset of this wrinkling instability as a function of the mechanical bendability *τ* determining both the critical indentation depth required to bring about wrinkling, and the number of wrinkles observed at onset. Our results for the critical indentation required to generate wrinkling in the high mechanical bendability, *τ*≫1, limit agree with those determined from membrane theory and verified experimentally previously [22]. Our results for the number of wrinkles at onset in this regime suggest that *n*_{onset}∼*τ*^{2/3} for highly bendable sheets. Our study of the onset of wrinkling at low and moderate mechanical bendabilities,
*O*(1) quantities as *τ*→0, and are confirmed by our own experiments.

We note in closing that our analysis of the onset of wrinkling assumed that wrinkling occurs with a single wavenumber. In the case of well-developed wrinkling (far from threshold) with high bendability, it has recently been observed that the wrinkle number may, in fact, evolve with both indentation depth and radial position [26]. More detailed analysis of this problem beyond onset is needed to understand whether this spatial variation is also observed at low and moderate mechanical bendabilities—the parameter regime highlighted as ‘open’ in table 1. Nevertheless, our study of the small-indentation behaviour up to and including the threshold of instability extends our understanding of deformation in such scenarios. In particular, our exploration of the role of the dimensionless parameters *τ* and *δ* in this problem allows the behaviour of a wide range of systems from the nano-indentation of ultra-thin films to the geological context of the loading of ice sheets and tectonic plates to be studied within a single framework.

## Data accessibility

All data accompanying this publication are available as the electronic supplementary material.

## Author contributions

F.B., D.V. and J.A.N. designed the research; F.B., D.V., R.W.S. and J.A.N. performed the research, co-wrote the paper and gave their final approval for publication.

## Competing interests

We declare that we have no competing interests.

## Funding statement

The research leading to these results has received funding from the European Research Council under the European Union’s Horizon 2020 Programme/ERC Grant Agreement no. 637334 (D.V.). J.A.N. is supported by a Royal Society University Research Fellowship.

## Acknowledgements

We are grateful to Benny Davidovitch for discussions on this work.

## Footnotes

Electronic supplementary material is available online at https://dx.doi.org/10.6084/m9.figshare.c.3900355.

↵1 In tables 2 and 3, PVS

_{8}and PVS_{22}correspond to elastomers Elite Double 8 and 22, which had measured moduli*E*=200 kPa and*E*=801 kPa, respectively.

- Received May 13, 2017.
- Accepted September 8, 2017.

- © 2017 The Authors.

Published by the Royal Society under the terms of the Creative Commons Attribution License http://creativecommons.org/licenses/by/4.0/, which permits unrestricted use, provided the original author and source are credited.