Abstract
This chapter explores the basic mechanisms underlying crack propagation in brittle heterogeneous materials and introduces tools that allow for the prediction of their effective failure properties from their microscale features. The second part of this chapter explores two fascinating features of the failure behavior of disordered materials, namely the intermittent dynamics of cracks and the roughening processes leading to the fractal structure of fracture surfaces.
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Notes
- 1.
With some abuse of terminology, we will refer in the following to \(G_\textrm{c}\) as the material toughness that, strictly speaking, corresponds to the fracture energy.
- 2.
The case of cracks that can meander out of the mean fracture plane is discussed in perspectives in Sect. 2.7.
- 3.
The non-local part of the elastic energy release rate can be conveniently written in the Fourier space as \(\delta \tilde{G}(q) = - |q| G(c_0, \delta ) \delta \tilde{c}(q) \).
- 4.
The convergence of this integral is ensured under the condition \(dG_0/dc_0 < 0 \Leftrightarrow \mathcal {L} > 0\). In fact, the limiting case \(dG_0/dc_0 \rightarrow 0 \Leftrightarrow \mathcal {L} \rightarrow +\infty \), admits also a solution as long as these front perturbations are calculated from the reference configuration \(\delta c(0)\). In physical terms, it means that the structural length \(\mathcal {L}\) is much larger than the obstacle width d.
- 5.
The logarithmic evolution of the perturbation obtained for a crack pinned by a single heterogeneity can be inferred more directly by considering the application of a point force on the front that reflects the toughness distribution \(g_\textrm{c} \sim \delta (z)\) where \(\delta \) is the Dirac function. The application of the equilibrium condition Eq. (13) in the limit \(\mathcal {L} \rightarrow 0 \) gives \( \delta \tilde{c} \sim 1/|q|\) that results in the logarithmic behavior \(\delta c(z) \sim \log (|z|)\).
- 6.
The second order term calculated by this procedure takes a more compact form in Fourier space
$$\begin{aligned} \delta \tilde{G}^{(2)} [\delta \tilde{c}](q) = \int \limits _{- \infty }^{+\infty } \mathcal {Q} (q',q-q') \delta \tilde{c}(q') \delta \tilde{c}(q-q')dq' \quad {(18)} \end{aligned}$$where the kernel \(\mathcal {Q}\) follows the form
$$\begin{aligned} \begin{aligned} \mathcal {Q}&(q',\tilde{q}) = \frac{1}{2} \frac{d^2 G_0}{dc^2_0}-\frac{1}{4}\frac{dG_0}{dc_0}[|q'+\tilde{q}|+|q'|+|\tilde{q}|]+ \\&\frac{G_0}{8} \left[ \textrm{sign}(q'\tilde{q})(q'+\tilde{q})^2 + [\textrm{sign}(q')-\textrm{sign}(\tilde{q})] \, |q'+\tilde{q}| (k'- \tilde{q})-(|q'|-|\tilde{q}|)^2 \right] . \end{aligned}\quad {(19)} \end{aligned}$$.
- 7.
- 8.
Note the interesting asymptotic case \(k \rightarrow \infty \) showing a linear behavior (green line in Fig. 8). This case actually corresponds to the behavior of a semi-infinite crack pinned by a sinusoidal distribution of tough obstacles \(g_\textrm{c} = 2 C \cos (k z)\) that can be solved using Eq. (13) for \(C \ll 1\). One obtains sinusoidal front deformations \(\delta a(z) = 2C/k \cos (k z)\) of amplitude \(\Delta a/\lambda = 2C/\pi \), in agreement with the amplitude of the front perturbations of a penny-shape crack in the limit \(\lambda /a \rightarrow 0\) of very small obstacles with respect to the crack radius. As the last result is valid for any contrast, this suggests that it may also apply to the semi-infinite crack for any value of C. Ultimately, this suggests that the stiffening behavior observed in Fig. 6 and the softening behavior observed in Fig. 13 for large contrast vanish when the front deformations are negligible with respect to the structural length \(\mathcal {L}\).
- 9.
Roughly speaking, the determination of the stationnary front configuration solving the equation \(g(a(\theta )) = C g_\textrm{c}(\theta )\) consists in determining the front deformation amplitude \(\Delta a/\lambda (C)\) corresponding to the imposed contrast C (see Fig. 13). However, as the contrast increases, we expect the curves in Fig. 13 to display a vertical asymptote for the critical contrast \(C_c(k)\) shown in Fig. 12. This implies that the problem has no solution for \(C > C_c(k)\), explaining the continously growing petals observed in the fingering regime.
- 10.
The slight decrease of the effective toughness with the contrast in this regime can actually be explained quantitatively using the first order theory of Gao and Rice (1987). It allows to capture that a larger section of the front visits the weaker region of the fracture plane where the crack deforms further, leading to \(\frac{G_\textrm{c}^{\text {eff}}}{\langle G_\textrm{c} \rangle } = 1 - \frac{4}{k-1}C^2 \).
- 11.
b denotes the sample width along the z-axis.
- 12.
Strictly speaking, the effective fracture energy \(G_\textrm{c}^{\text {eff}}\) corresponds to the maximum of the instantaneous fracture energy \(G_\textrm{c}(t)\) while our calculation predicts here that the proportionality constant corresponds to its time-average \(\langle G_\textrm{c}(t) \rangle _t\).
- 13.
The length scale \(l_0 \approx 8~\upmu \text {m}\) involved in the variations of the correlation time \(\delta t^*\) with \(v_m\) is found to be of the order of one tenth of the characteristic size of the heterogeneities.
- 14.
Higher order momentum of the distribution of toughness do not play any role in the collective regime considered subsequently, as illustrated by the study of the effective toughness of disordered solids presented in Sect. 2.5.
- 15.
See Wiese and Le Doussal (2007) for a review of the appropriate analytical methods based on the Functional Renormalization Group theory. Note however that they provide only approximated solutions, strictly valid at the critical dimension \(d_c\), where d is the interface dimension with \(d_c = 2\) while \(d=1\) for crack propagation problems.
- 16.
A fit of the experimental data of Lengliné et al. (2011) with the law \(G_\textrm{c} \sim (1+ v_m/v_c)^{\gamma }\) allows for an estimation of the characteristic velocity \(v_0 \simeq 140~\upmu ~\text {m.s}^{-1}\) over the experimentally investigated range of crack speeds \(0.4~\upmu ~\text {m.s}^{-1} \le v_m \le 40~\upmu ~\text {m.s}^{-1} \), using the fitting parameters \(v_c = 5~\upmu ~\text {m.s}^{-1}\) and \(\gamma \simeq 0.07\).
- 17.
Two important assumptions have been made here. First, the depth of the largest cluster has been approximated by the depth of the total avalanche. According to our numerical observations and the one made in Lawn and Marshall (1998), this looks like a fair assumption that relies on the anisotropic spatial structure of the avalanches that extend along the front direction rather than along the propagation direction. Second, we have assumed that the velocity during the propagation of the crack over \(one cluster \) is set by the velocity \(v_0\), as observed during the depinning from a single obstacle (see Sect. 2.3).
- 18.
Note that we need to assume here that the largest avalanche size \(S^{*}_{av}\) is proportional to the largest cluster size \(S^{*}_d\). This was indeed observed by Laurson et al. (2010) who found \(S_d \sim S_{av} \) for the largest events.
- 19.
The existence of two distinct scaling regimes with exponent \(\eta _d \simeq 2.0\) for brittle failure and \(\eta _d \simeq 2.5\) for quasi-brittle crack growth also invites to discuss Barés et al. (2013)s experimental results presented in Fig. 16c. Here, a scaling law with \(\eta _d \simeq 2.5\) was reported in the depinning regime. Since such scaling actually does survive to upscaling Tallakstad et al. (2011), it is tempting to interpret this observation in terms of microscopic failure mechanism, and conjecture that microcracking does take place at a scale comparable to the grain size \(\xi \simeq 500~\upmu \text {m}\) of the sintered materials used in these experiments.
- 20.
The constant \(\Omega _c\) involved in Eq. (2.8) is chosen such that the average of \(\omega (\vec {x})\) over all \(\vec {x}\) is zero.
- 21.
The actual decomposition of the height variation computed as a scale \(\delta r\) into the sum of height variations computed at a finer scale \(\epsilon = \delta r /n\) where n is an integer writes as \( \delta h (\vec {x},\delta \vec {x}) = h(\vec {x}+\delta \vec {x}) - h(\vec {x}) = \sum _{k=1}^{n} h (\vec {x}+ \frac{k}{n} \delta \vec {x} ) - h(\vec {x} + \frac{k-1}{n} \delta \vec {x}) = \sum _{k=1}^{n} \delta h ( \vec {x} + \frac{k-1}{n} \delta \vec {x}, \frac{\delta \vec {x}}{n})\).
- 22.
Note however that the original idea of Mandelbrot et al. (1984) was to establish a correlation of the material toughness with the \(roughness exponent \), and not with a crossover length scale between two self-affine regimes as discussed here.
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Acknowledgements
The author would like to dedicate this chapter to my younger collaborators, Aditya Vasudevan, Ashwij Mayya, Estelle Berthier, Guillaume de Luca, Julien Chopin, Manish Vasoya, Thiago Grabois and Vincent Démery without who this research would not have been possible. A special thank to Guillaume de Luca who provided a precious help in the editing of this book.
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Ponson, L. (2023). Fracture Mechanics of Heterogeneous Materials: Effective Toughness and Fluctuations. In: Ponson, L. (eds) Mechanics and Physics of Fracture. CISM International Centre for Mechanical Sciences, vol 608. Springer, Cham. https://doi.org/10.1007/978-3-031-18340-9_3
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