Research Article  Open Access
Analysis of the Indentation Size Effect in the Microhardness Measurements in B_{6}O
Abstract
The Vickers microhardness measurements of boron suboxide (B_{6}O) ceramics prepared by uniaxial hotpressing was investigated at indentation test loads in the range from 0.10 to 2.0 kgf. Results from the investigation indicate that the measured microhardness exhibits an indentation load dependence. Based on the results, we present a comprehensive model intercomparison study of indentation size effects (ISEs) in the microhardness measurements of hotpressed B_{6}O discussed using existing models, that is, the classical Meyer's law, Li and Bradt's proportional specimen resistance model (PSR), the modified proportional specimen resistance model (MPSR), and Carpinteri's multifractal scaling law (MFSL). The best correlation between literaturecited loadindependent Vickers microhardness values, the measured values, and applied models was achieved in the case of the MPSR and the MFSL models.
1. Introduction
With hardness values reported to range between 24 GPa and 45 GPa [1, 2], boron suboxide (B_{6}O) is sometimes considered to be the third hardest material after only diamond (from ~70 to ~100 GPa) and cubic boron nitride (~60 GPa) [2]. The boronrich icosahedral ultrahard material belongs to the rhombohedral boron type structure (Rm) [2] which is similar to those of other ultrahard boronrich materials namely boron carbide B_{4}C [3], aluminium magnesium boride AlMgB_{14} [4], and the newly synthesized boron subnitride B_{13}N_{2} [5].
B_{6}O exhibits a rather unusual and wide range of superior properties; among these are high hardness with low density, high mechanical strength, and high chemical inertness [2, 6]. Along with the other boronrich ultrahard materials, the potential applications of B_{6}O have been an object of intense interest in recent years [2]. However, despite the intensive research efforts, the commercial applications are yet to be realized partly because of (a) the low fracture toughness of polycrystalline B_{6}O [7] and considerable practical challenges in the densification of that material [2, 6, 7] by hotpressing, (b) stoichiometric B_{6}O samples that are not easy to synthesize [1, 2], (c) poor crystallinity [1, 7], and hence (d) numerous mechanical properties of the material that are still poorly understood [8]—indentation size effect (ISE) in microhardness measurements is one such property.
Until now, the investigation of the mechanical properties of B_{6}O by indentation has been neglected in favour of the improvement of densification and fracture toughness of the composites [2, 6, 7]. The hardness reported for the material by different workers often remains a topic of debate, with literaturecited values varying from 24 GPa to 45 GPa. To the best of our knowledge, the indentation loadsize dependence in the microhardness of hotpressed B_{6}O is being comprehensively examined for the first time in this paper. The aim of this paper is twofold: (1) to report experimental data on the microhardness of hotpressed B_{6}O determined by Vickers pyramidal indentation and (2) to critically examine the ISE phenomenon by means of a comprehensive intermodel comparison of various approaches and models proposed in the literature. The nature and the origins of ISE are investigated and discussed.
2. Materials and Experimental Method
B_{6}O powder was prepared by the reaction of B and B_{2}O_{3} as detailed by Andrews et al. in [9] thatwere uniaxiallyhotpressed in hBN pots under argon environment at 1800°C and 50 MPa for 20 minutes. The hotpressed compacts were then metallographically prepared using a method prescribed by Machaka et al. in [10]. The density of the hotpressed compacts measured 2.44 g/cm^{3}. The polished samples were analyzed for phase composition using Xray diffraction, with Cu K_{α} radiation. The powder diffraction patterns were collected using the BraggBrentano backscattering geometry over a 10°–90° 2 range, with a 0.02° step size.
The measurements were performed at room temperature by a FutureTech microhardness tester at different applied test load between 0.1 and 2.0 kgf. At least ten hardness measurements were carefully taken for each load at different locations on the middle of each sample, and the average values were taken as the hardness of the sample at that load. The Vickers indentation impressions were observed using optical microscopy.
3. Results
3.1. XRD Measurements
Figure 1 shows the full profile Xray powder diffraction pattern measured on the starting hotpressed B_{6}O samples. The diffraction pattern is characteristic of a nominally pure polycrystalline B_{6}O. All the dominant diffraction peaks can be perfectly indexed to the XRD pattern of B_{6}O (JCPDS File Card no. 31210) reported elsewhere [9]. The lattice parameters, Å and Å, obtained from XRD analysis are in good agreement with the single crystal data [2].
3.2. Microindentation Measurements
To investigate ISE, microindentation measurements were conducted at test load between 0.1 and 2.0 kgf using a Vickers diamond indenter. Apparent Vickers microhardness values were calculated at each load using the conventional approach shown in: where is the average diagonal length of the Vickers indentation impressions and is the indentation test load in kgf. Figure 2 shows the dependenceof the measured Vickers microhardness of hotpressed B_{6}O on the applied indentation load. Each of the plotted data point is an average of at least ten measurements at each applied test load. The insert in Figure 2 depicts an optical micrograph of a typical Vickers indentation impression.
Evidently, the Vickers hardness is a function of the applied load at low applied indentation test load. The existence of ISE makes it unsatisfactory here to quote a single hardness value when Vickers hardness is used for material characterization. By observation, at applied indentation test loads ≳1 kgf, a single loadindependent Vickers hardness value of 30.0 GPa seems to exists. The loadindependent hardness is also sometimes deemed the intrinsic or “true” hardness. The observed value is consistent with literature reported values [1, 2, 11].
3.2.1. Meyer's Law
The classical power law shown in (2a), also known as the Meyer's law, is frequently used to indicate the existence of ISE for ceramic and other materials [12]. is a powerfit constant, and the exponent is the Meyer's index, also known as the sizeeffect index. The Meyer's index is generally used as a measure of ISE: The regression analysis of the experimental data using (2b) is shown in Figure 3. The slope of the linear fit is the Meyer's index, and observed to be . When , the microhardness is expected to be independent of the applied load. However, indicates the existence of an ISE trend, the measured microhardness decreasing with applied load [13, 14].
3.2.2. PSR Model
Several studies [14, 15] agree that the Meyer law is probably insufficient to describe the origin of the ISE, although it is a good indicator of its existence. According to Li and Bradt [14], the applied indentation load is related to the average indent diagonal length through a polynomial relationship (3a): The parameters and are constants for a given material. The parameters are related to the elastic and the plastic deformation properties of the test material, respectively. The parameter is a measure of the surface effects during microhardness indentation which is directly related to the ISE contribution, whilst is directly related to the loadindependent microhardness value as demonstrated in (3b).
From (3a), a plot of against can be constructed to yield a straight line, where bestfit parameters and can easily be obtained by regression analysis. As shown in Figure 4, a plot of against is significantly linear, implying that (3a) gives an indication of the existence of ISE in hotpressed B_{6}O.
As noted previously, the PSR analysis can be extended to determine directly from using (3b). In this study was found to be 26.8 ± 0.3 GPa.
3.2.3. Modified PSR Model
Gong et al. in [16] modified the PSR model to investigate the ISE behaviour in various materials. The resulting MPSR model is defined by (4a):where is a constant related to the residual surface stresses associated with the surface grinding and polishing processes during sample preparation. The parameters and are constants as defined in the PSR model (refer to Section 3.2.2). The values of , , and can be evaluated by plotting the data against . The plot of versus (and polynomial curve fitting thereof according to the MPSR model) is shown in Figure 5.
As is the case for the PSR model, a loadindependent hardness value, , can be determined directly from bestfit value of from Figure 5 using (4b). In this study, was found to be 28.2 ± 0.9 GPa.
The estimated bestfit values of the , , and parameters corresponding values are listed in Table 1. The residual surface stresses contribution to the observed ISE is negligible compared to the contribution of bulk material's plastic deformation characteristics.

The PSR and MPRS parameters estimated by regression analysis are summarized in Table 1. Based on the values and their physical significance according to the energybalance relation [17], we suggest that the residual surface stresses' contribution () to the observed ISE is negligible compared to the contribution of bulk material's indentation elastic recovery () and the indenter/specimen interface friction resistance coupled with elastic resistance of the specimen and the mixed elastic/plastic deformation response of material ().
3.2.4. MFSL Approach
As illustrated in Figure 2, the variation of microhardness with indentation load is a twoparameter problem exhibiting at least two totally different sizedependent regimes: a loaddependent regime and a loadindependent regime. The variation of microhardness with indentation load in other words exhibits selfsimilarity; that is, by observing the property in different scales, a similar, but not exactly the same structure, is obtained—a property of multifractals.
According to Carpinteri and Puzzi in [18], ISE in materials follows the multifractal scaling law shown in (5). However, the indentation size effect property is observed to vanish in the limit of the applied load tending to infinity. From the later, an asymptotic value of hardness which resembles a loadindependent or intrinsic value can be determined as illustrated in Figure 6. In this study, we apply the multifractal scaling law in the analysis of observed indentation size effect in hotpressed B_{6}O. Further indepth discussions on the fractal approach to indentation size effect are refereed to Carpinteri's comprehensive review on the subject [18].
On the basis of this approach, the multifractal scaling law (MFSL) for ISE can be written in the following analytical form: where is the intrinsic hardness in the limit of infinite (a huge) applied load and is the critical material characteristic length which individuates the transition between the two regimes, that is, the fractal one and the nonfractal (Euclidean) one.
In order to study the fractal characteristic of the size effect dependence of microhardness depicted in Figure 2, a  plot of the Vickers microhardness and the indentation diagonal length was constructed based on the multifractal scaling law shown in (5) (and presented as Figure 6). The result shows that as a function of the is approximately linear in two parts of the scale dependence.
In this study, both and were determined simultaneously by means of nonlinear least squares analysis of the experimental data using Mathematica. and were determined to be 28.9 GPa and 1.41 μm, respectively. The fractal dimension in the first region can be depicted as the following equation.
The slope of the bilogarithmic plot shown in Figure 6 represents the fractal dimensional increment , which is a measure of the variable influence of ISE on the measured Vickers hardness. The variation of fractal dimension of multifractality with , as determined from versus , is presented as an insert in Figure 6. Two limiting conditions have to be satisfied: for large indents (Euclidean response) and for small indents (multifractal behaviour). The last situation corresponds to the highest possible indentation size effect in hardness, which is a theoretical upper bound.
According to the insert in Figure 6, tends to zero and coincides with the occurrence in a crossover between fractal and Euclidean behaviour implying the progressive vanishing of fractality in the measured Vickers microhardness with increasing indentation load/size.
4. Summary and Conclusions
Figure 2 shows that the variation of with indicates that the hotpressed B_{6}O ceramic material exhibits ISE. Based on the observation, a comprehensive study of ISE in microhardness measurements of B_{6}O was conducted using a number of existing models, that is, the classical Meyer's law, Li and Bradt's proportional specimen resistance model (PSR), the modified proportional specimen resistance model (MPSR), and Carpinteri's multifractal scaling law (MFSL). A summary of the hardness values calculated is shown in Table 2.

The average loadindependent hardness of hotpressed B_{6}O from this study has been observed to be 28.0±0.3 GPa.
Based on the values of the PSR and MPSR parameters estimated by regression analysis, the origins of ISE in hotpressed B_{6}O can be attributed to either the bulk material's indentation elastic recovery, the indenter/specimen friction resistance coupled with elastic resistance of the specimen, or/and the mixed elastic/plastic deformation response of material. The residual surface stresses' contribution to the observed ISE is observed to be negligible compared to the aforementioned.
The linear relationship of the double logarithm between measure (the microhardness) and scale (the applied load) shows indentation selfsimilarity, both in indentation shape and in the results of hardness. We can conclude this to be fractal behaviour. The load dependence of hardness shows dual fractal behaviour given the two different regions of hardness.
We can conclude and suggest that the variation of fractal dimension of multifractality with is a more resourceful indicator of the existence of ISE than the Meyer's index, for example.
Acknowledgments
The authors gratefully acknowledge the useful contributions of O. T. Johnson and the financial support from the DST/NRF Centre of Excellence in Strong Materials and the University of the Witwatersrand Mellon Award.
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Copyright
Copyright © 2011 Ronald Machaka et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.