# Size Effect on Failure of Pre-stretched Free-Standing Nanomembranes

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- Received:
- Accepted:

DOI: 10.1007/s11671-010-9625-y

- Cite this article as:
- Long, R., Hui, CY., Cheng, W. et al. Nanoscale Res Lett (2010) 5: 1236. doi:10.1007/s11671-010-9625-y

## Abstract

Free-standing nanomembranes are two-dimensional materials with nanometer thickness but can have macroscopic lateral dimensions. We develop a fracture model to evaluate a pre-stretched free standing circular ultrathin nanomembrane and establish a relation between the energy release rate of a circumferential interface crack and the pre-strain in the membrane. Our results demonstrate that detachment cannot occur when the radius of the membrane is smaller than a critical size. This critical radius is inversely proportional to the Young’s modulus and square of the pre-strain of the membrane.

### Keywords

Free standing membranePre-stretchSize effectEnergy release rate## Introduction

Free-standing ultrathin nanomembranes are a new class of two-dimensional materials that possess nanoscale thickness across macroscopic dimensions. Such nanomembranes are not only ultra-lightweight but also robust and flexible. It has been reported that elastic moduli of ultrathin nanomembranes can be 1–10 GPa with ultimate strengths of up to 100 MPa [1–6]. These striking properties of free-standing nanomembranes have resulted in a broad spectrum of applications in separation, sensing, biomedicine and energy harvesting [7–10].

## Model

*R*. The thin substrate with micro-holes is assumed to be rigid. Let

*h*≪

*R*denote the thickness of the membrane. For a circular membrane without defect, the pre-stretch is equi-biaxial and is spatially uniform. Since the out of plane stresses are identically zero, the membrane deforms under plane stress conditions. With respect to a polar coordinate system (

*r*,

*θ*) with origin at the center of the circular membrane, the non-zero pre-strains in a membrane without defect are where are the axial and hoop strains, respectively. This equi-biaxial stretch state can be achieved mechanically by imposing a radial displacement of on the circumference of the membrane. The strain energy density of the pre-stretched membrane is where

*E*and

*ν*are the Young’s modulus and the Poisson’s ratio of the membrane, respectively. The total elastic strain energy Γ of the membrane without defect is

*W*as the energy required to detach or break a unit area of membrane in the interface region. This region includes the edge of the micro-hole as well as a thin layer of membrane adjacent to it. If adhesive failure occurs,

*W*is identified as adhesion energy per unit area between the membrane and the substrate, while in cohesive failure,

*W*is the facture toughness of the membrane. The energy needed to detach the

*entire*membrane from the edge is 2

*πRhW*. The elastic energy stored in the membrane Γ will not be large enough to detach the entire membrane if

Equation (3) shows why sheets over smaller holes (smaller *R*) is less likely to fail. This conclusion is also valid for non-circular shaped micro-holes; in this case *R* should be replaced by the characteristic length of the micro-hole.

*entire*interface, whereas in reality, only partial detachment is observed (Fig. 1a). We ask a more general question: suppose there is a defect on or near the interface between the membrane and the micro-hole edge, will this defect grow? If the defect grows, elastic energy is released locally to debond or break the membrane and part of the membrane is relaxed. To model this process, we consider an interface crack of length

*a*< 2

*πR*as shown in Fig. 2. The surface of this crack is traction-free whereas the rest of the membrane circumference is subjected to a radial displacement of According to fracture mechanics [13], a necessary condition for the growth of this interface crack is

*G*is the energy release rate of the crack. Energy release rate is the elastic energy per unit film thickness that would be released if the crack were to extend by a unit distance along the interface. In this analysis, deviation of the crack trajectory from the interface (e.g. in cohesive failure) is assumed to be small so that the energy release rate

*G*can be computed by assuming the crack is right on the interface.

*f*is an unknown dimensionless function of

*θ*

_{o}(0 ≤

*θ*

_{o}≤

*π*), the half angle sustained by the interface crack (see Fig. 2). We will call the normalized energy release rate. Its behavior for small cracks (

*θ*

_{o}≪ 1) can be found using a simple argument. In this limit, the crack can be viewed as a straight crack with length

*a*lying on the interface between the lower half plane (circular membrane) and the upper half plane (rigid substrate). The crack is loaded by a hydrostatic tension at infinity. The energy release rate for this geometry is:

*f*(

*θ*

_{o}

*ν*) is a linear function of

*θ*

_{o}for small cracks. Applying the crack growth criterion (4) using (6), we found small defects (

*a*/

*R*≪ 1) with

will not grow.

*f*(

*θ*

_{o}→ 0,

*ν*) → 0

*.*In addition, since the strain energy of the membrane goes to zero as

*a*→ 2

*πR*(or

*θ*

_{o}→

*π*), the energy release rate is expected to vanish in this “long” crack limit. This explains why complete detachment does not occur. The fact that

*f*vanishes at both end points (0 and

*π*) means that

*f*must have an interior maximum

*f*

^{*}> 0 at some

*θ*

_{o}

^{*}∈ (0,

*π*). The existence of this maximum and the crack growth criterion (4) imply that no defect can grow if

where *f*^{*}is a numerical constant which depends only on the Poisson’s ratio of the membrane.

*f*and its maximum

*f*

^{*}are determined numerically using finite element method. Details of the finite element calculation are given in Appendix A. Figure 3 plots the normalized energy release rate

*f*(

*θ*

_{o},

*ν*) against

*θ*

_{o}for

*ν*= 0, 0.1, 1/3, 0.4 and 0.49. The energy release rate increases linearly

*θ*

_{o}for small cracks as predicted by (7), reaches a maximum at

*θ*

_{o}

^{*}and then decreases rapidly to zero. The fact that the energy release rate decreases to zero after implies that the interface crack will always be arrested before it can de-cohere the entire membrane, consistent with experimental observation that the interface crack eventually arrests before the complete detachment of membrane can take place (Fig. 1). According to (8), irrespective of the size of a defect, it cannot grow if . Values of

*f*

^{*}for different Poisson’s ratio

*ν*can be approximated by

*f*

^{*}= 4.26

*ν*

^{2}+ 0.49

*ν*+ 0.92 with

*ν*∈ [0, 0.5]. This result suggests that membrane detachment can be prevented when the membrane radius

*R*is smaller than a critical radius

*R*

_{c}:

*W*and This result is consistent with our preliminary experimental results. In these experiments, the stiffness of the membrane can be tuned by varying the length of the DNA molecules attached to the gold particles [11]. However, more data is needed to confirm this result.

Our experimental observations suggest that *R*_{c} is in the range of 1–4 μm. The Young’s modulus *E* of a typical membrane is reported to be about 6.5 GPa [11]. Assuming *ν* is 1/3, the pre-strain is estimated to be 0.12%. This estimate is based on the initial slope of the force–displacement curve of indentation tests [11], where we have assumed that the force–displacement curve is controlled by the pre-tension for small deflections and approximated the indenter as a point load. There is no direct measurement of *W*. Using the values of *R*_{c}*E* and *v* listed above, *W* is estimated to be 15–50 mJ/m^{2}, which is consistent with the strength of van der Waals interaction [15].

## Conclusion

In summary, a fracture mechanics model is used to explain why small free-standing membranes are more resistant to detachment. We show that detachment can be prevented by making the membrane smaller for a given pre-strain and *W*, which is consistent with our experimental observations. A useful expression for critical radius of the membrane is obtained and may guide future design of free-standing membrane systems.

## Acknowledgments

C.Y. Hui and R. Long are supported by a grant from the Department of Energy (DE-FG02-07ER46463). W. Cheng, M. Campolongo and D. Luo are partially supported by NYSTAR and the NSF CAREER award (grant number: 0547330).

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