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Nanoscale Res Lett. 2010; 5(7): 1236–1239.
Published online 2010 May 15. doi:  10.1007/s11671-010-9625-y
PMCID: PMC2893971

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


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 membrane, Pre-stretch, Size effect, Energy release rate


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].

These free-standing nanomembranes are usually subjected to residual tensions induced during formation or by thermal mismatch. As a result, they may detach from the suspending micro-holes and lose their functionality [11,12]. Experiments have demonstrated that smaller free standing membranes are structurally and thermally more stable than larger ones [9,10]. This size dependence is also observed by Cheng et al. [11] who fabricated free standing membranes composed of highly ordered arrays of gold nanoparticles linked by single strand DNA molecules. Briefly, these membranes are formed using the following process: first, droplets of a solution consisting of 13 nm diameter gold nanoparticles capped with 5′-thiolated single strand DNA (ssDNA) is dried on a thin silicon nitrate substrate with micron size holes in it. Satellite micro-droplets were formed and trapped in these microholes due to pinning of contact lines by the hole edges. As solvent evaporated, these pinned satellite micro-droplets thinned and formed monolayer nanoparticle membranes. Pre-tensions were built up on the membranes during this drying stage. It was found that these membranes tended to detach from the edges of larger microholes, but not smaller ones (Fig. (Fig.11).

Figure 1
a A free standing membrane is partially detached from a 7.5 μm × 6.5 μm rectangular hole. b A free standing membrane is fully attached to a circular hole with diameter of 2 μm


We propose a model to understand the size effect on the detachment of membranes due to pre-stretch. Micro-holes used in the experiments are usually rectangular or circular. For simplicity, we assume that the micro-holes are circular with radius R. The thin substrate with micro-holes is assumed to be rigid. Let h [double less-than sign] 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 An external file that holds a picture, illustration, etc.
Object name is 1556-276X-5-1236-i11.gif where An external file that holds a picture, illustration, etc.
Object name is 1556-276X-5-1236-i12.gif are the axial and hoop strains, respectively. This equi-biaxial stretch state can be achieved mechanically by imposing a radial displacement of An external file that holds a picture, illustration, etc.
Object name is 1556-276X-5-1236-i13.gif on the circumference of the membrane. The strain energy density of the pre-stretched membrane is An external file that holds a picture, illustration, etc.
Object name is 1556-276X-5-1236-i14.gif 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

equation image

A simple scaling argument shows why membranes with larger radius are more likely to fail. Specifically, we envision two failure modes: adhesive or cohesive. In adhesive failure, a crack grows along the edge of the micro-hole. In cohesive failure, crack growth occurs inside a region of the membrane that is adjacent to the interface (e.g. see Fig. Fig.1a).1a). To quantify these failures, we define 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 2πRhW. The elastic energy stored in the membrane Γ will not be large enough to detach the entire membrane if

equation image

Using (1), the inequality in (2) can be rewritten as

equation image

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.

The above argument is too simplistic since it assumes that detachment occurs on the entire interface, whereas in reality, only partial detachment is observed (Fig. (Fig.1a).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 < 2πR as shown in Fig. Fig.2.2. The surface of this crack is traction-free whereas the rest of the membrane circumference is subjected to a radial displacement of An external file that holds a picture, illustration, etc.
Object name is 1556-276X-5-1236-i15.gif According to fracture mechanics [13], a necessary condition for the growth of this interface crack is

equation image
Figure 2
Pre-stretched thin membrane with an interface crack of length a. The membrane is subjected to a radial displacement of An external file that holds a picture, illustration, etc.
Object name is 1556-276X-5-1236-i25.gif at its circumference outside the crack

where 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.

Linearity and dimensional argument show that

equation image

where f is an unknown dimensionless function of θo (0 ≤ θoπ), the half angle sustained by the interface crack (see Fig. Fig.2).2). We will call An external file that holds a picture, illustration, etc.
Object name is 1556-276X-5-1236-i16.gif the normalized energy release rate. Its behavior for small cracks (θo[double less-than sign] 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 An external file that holds a picture, illustration, etc.
Object name is 1556-276X-5-1236-i17.gif at infinity. The energy release rate for this geometry is:

equation image

where the dimensionless numerical factor An external file that holds a picture, illustration, etc.
Object name is 1556-276X-5-1236-i18.gif in (6) depends only on the membrane’s Poisson’s ratio, and is an order 1 quantity [14]. Equation (6) shows that f(θoν) is a linear function of θo for small cracks. Applying the crack growth criterion (4) using (6), we found small defects (a/R [double less-than sign] 1) with

equation image

will not grow.

For longer cracks, growth is possible. To study this possibility, we note that (5) and (6) imply that the normalized energy release rate f(θo → 0, ν) → 0. In addition, since the strain energy of the membrane goes to zero as a → 2πR (or θoπ), 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 θo* [set membership] (0, π). The existence of this maximum and the crack growth criterion (4) imply that no defect can grow if

equation image

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

The normalized energy release rate f and its maximum f* are determined numerically using finite element method. Details of the finite element calculation are given in Appendix A. Figure Figure33 plots the normalized energy release rate f(θo, ν) against θo for ν = 0, 0.1, 1/3, 0.4 and 0.49. The energy release rate increases linearly θo for small cracks as predicted by (7), reaches a maximum at θo* and then decreases rapidly to zero. The fact that the energy release rate decreases to zero after An external file that holds a picture, illustration, etc.
Object name is 1556-276X-5-1236-i19.gif 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. (Fig.1).1). According to (8), irrespective of the size of a defect, it cannot grow if An external file that holds a picture, illustration, etc.
Object name is 1556-276X-5-1236-i20.gif. Values of f* for different Poisson’s ratio ν can be approximated by f* = 4.26ν2 + 0.49ν + 0.92 with ν [set membership] [0, 0.5]. This result suggests that membrane detachment can be prevented when the membrane radius R is smaller than a critical radius Rc:

equation image
Figure 3
Normalized energy release rate An external file that holds a picture, illustration, etc.
Object name is 1556-276X-5-1236-i26.gif versus θo = a/2R for Poisson’s ratio ν = 0, 0.1, 1/3, 0.4 and 0.49. The dashed lines show that energy release rate increases linearly with crack length when the crack is small

Equation (9) also implies that stiff membranes are easier to detach than soft membranes for the same W and An external file that holds a picture, illustration, etc.
Object name is 1556-276X-5-1236-i21.gif 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 Rc 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 An external file that holds a picture, illustration, etc.
Object name is 1556-276X-5-1236-i22.gif 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 RcEAn external file that holds a picture, illustration, etc.
Object name is 1556-276X-5-1236-i23.gif and v listed above, W is estimated to be 15–50 mJ/m2, which is consistent with the strength of van der Waals interaction [15].


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.

Appendix A

Numerical calculations were carried out using ABAQUS, a finite element software [16]. Radial displacement of An external file that holds a picture, illustration, etc.
Object name is 1556-276X-5-1236-i24.gif was imposed on the edge of the circular membrane outside the crack while the crack face was left traction free. A typical mesh consisted of approximately 4,000 plane stress four-node quadrilateral elements. Finer mesh was used near the crack tip. The total strain energy of the system Γ can be found for any normalized crack length θo, and the energy release rate can be computed according to

equation image

where Δθo is a small increment in normalized crack length. We started the simulation with a very small crack and gradually increased its length. The calculation is tedious since each crack length increment requires remeshing and change of boundary conditions. This process was automated using a PYTHON script. The energy release rate was also computed using the J-integral option in ABAQUS. We found practically no difference between the two methods.


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).

Open Access

This article is distributed under the terms of the Creative Commons Attribution Noncommercial License which permits any noncommercial use, distribution, and reproduction in any medium, provided the original author(s) and source are credited.


  • Cheng W, Campolongo MJ, Tan SJ, Luo D. Nano Today. 2009. pp. 482–493. COI number [1:CAS:528:DC%2BC3cXkvFGitb0%3D] [Cross Ref]
  • Jiang CY, Rybak BM, Markutsya S, Kladitis PE, Tsukruk VV. Appl Phys Lett. 2005. p. 121912. Bibcode number [2005ApPhL..86l1912J] [Cross Ref]
  • Mueggenburg KE, Lin XM, Goldsmith RH, Jaeger H. Nat Mater. 2007. pp. 656–660. COI number [1:CAS:528:DC%2BD2sXpvFKjsr0%3D]; Bibcode number [2007NatMa...6..656M] [PubMed] [Cross Ref]
  • Markutsya S, Jiang C, Pikus Y, Tsukruk VV. Adv Func Mater. 2005. p. 771. COI number [1:CAS:528:DC%2BD2MXktlSktbw%3D] [Cross Ref]
  • Fery A, Dubreuil F, Möhwald H. New J Phys. 2004. p. 18. [Cross Ref]
  • Vinogradova OI. J Phys Condens Matt. 2004. p. R1105. COI number [1:CAS:528:DC%2BD2cXns1ars78%3D]; Bibcode number [2004JPCM...16R1105V] [Cross Ref]
  • Jiang C, Markutsya S, Pikus Y, Tsukruk VV. Nat Mat. 2004. p. 721. COI number [1:CAS:528:DC%2BD2cXotVSltrc%3D] [PubMed] [Cross Ref]
  • Steele BCH, Heinzel A. Nature. 2001. p. 345. COI number [1:CAS:528:DC%2BD3MXovFGitrs%3D]; Bibcode number [2001Natur.414..345S] [PubMed] [Cross Ref]
  • Baertsch CD, Jensen KF, Hertz JL, Tuller HL, Vengallatore ST, Spearing SM, Schmidt MA. J Mater Res. 2004. p. 2604. COI number [1:CAS:528:DC%2BD2cXns1Sht78%3D]; Bibcode number [2004JMatR..19.2604B] [Cross Ref]
  • Tiefenauer LX, Studer A. Biointerphases. 2008. p. FA74. COI number [1:CAS:528:DC%2BD1cXmvVSrsbs%3D] [PubMed] [Cross Ref]
  • Cheng W, Campolongo MJ, Cha JJ, Tan SJ, Umbach CC, Muller DA, Luo D. Nat Mater. 2009. p. 519. COI number [1:CAS:528:DC%2BD1MXmtFemsLg%3D]; Bibcode number [2009NatMa...8..519C] [PubMed] [Cross Ref]
  • Jin J, Wakayama Y, Peng X, Ichinose I. Nat mater. 2007. p. 686. COI number [1:CAS:528:DC%2BD2sXpvFKjs74%3D]; Bibcode number [2007NatMa...6..686J] [PubMed] [Cross Ref]
  • Anderson TL. Fracture mechanics: fundamentals and applications. 3. CRC Press, Boca Raton; 2005.
  • Rice JR. J Appl Mech. 1988. p. 99. [Cross Ref]
  • Israelachvili J. Intermolecular & surface forces. 2. Academic Press, London ; 1992. [PubMed]
  • ABAQUS Version 6.7 Dassault Systemes Simulia Corp. Providence, RI, USA;

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