Fracture behavior of lithia disilicate- and leucite-based ceramics
Fracture behavior of lithia disilicate- and leucite-based ceramics
Fracture behavior of lithia disilicate- and leucite-based ceramics
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4<br />
9.8 N. The dimensions <strong>of</strong> the indentation diagonals<br />
were measured using an optical microscope with a<br />
filar eyepiece. The hardness ðHÞ values were<br />
calculated by<br />
H ¼½2P sinðu=2ÞŠ=a 2<br />
ð5Þ<br />
where P is the indentation load, u is the angle<br />
between opposite diamond faces (1368), <strong>and</strong> a is the<br />
mean diagonal length <strong>of</strong> the indentation.<br />
Flexural strength <strong>and</strong> K IC data were analyzed<br />
statistically using one-way ANOVA <strong>and</strong> Tukey’s HSD<br />
test. Weibull regression analysis was performed on<br />
the strength data as previously described 12 <strong>and</strong> as<br />
presented in a previous report. 11<br />
Results<br />
The mean values <strong>of</strong> density ðrÞ; elastic modulus ðEÞ;<br />
Poisson’s ratio ðnÞ; <strong>and</strong> Vickers hardness ðHÞ <strong>of</strong> the<br />
<strong>ceramics</strong> used in this study are summarized in<br />
Table 2.<br />
XRD analyses showed that high-exp<strong>and</strong>ing mineral,<br />
<strong>leucite</strong> (K2O·Al2O3·4SiO2), is the crystal phase<br />
in the IPS Empress core ceramic (E1), <strong>and</strong> the<br />
lithium <strong>disilicate</strong> (Li2O·2SiO2) is the crystal phase in<br />
the IPS Empress 2 (E2) <strong>and</strong> Experimental (ES) core<br />
<strong>ceramics</strong>. These crystal phases are shown in Fig. 2.<br />
The length <strong>of</strong> the elongated Li2Si2O5 crystals ranged<br />
from 0.5 to 4 mm for E2 <strong>and</strong> from 0.5 to 2 mm for ES.<br />
XRD analysis <strong>of</strong> the IPS Empress2 GV produced a<br />
typical amorphous glass plot. The absence <strong>of</strong> any<br />
crystal phase was confirmed by FTIR analysis.<br />
Representative photomicrographs <strong>of</strong> the <strong>ceramics</strong><br />
microstructure are presented in Fig. 2. As<br />
expected, there is a positive correlation between<br />
the elastic modulus ðEÞ; hardness ðHÞ; flexure<br />
strength ðsÞ; <strong>and</strong> fracture toughness ðK ICÞ for the<br />
four <strong>ceramics</strong> studied (E1, E2, ES, <strong>and</strong> GV).<br />
One-way ANOVA <strong>and</strong> Tukey’s test subsets<br />
revealed significant statistical differences for the<br />
mean s <strong>and</strong> K IC values between E1 <strong>and</strong> GV <strong>ceramics</strong><br />
ðp , 0:05Þ: The two <strong>lithia</strong> <strong>disilicate</strong>-<strong>based</strong> <strong>ceramics</strong><br />
(E2 <strong>and</strong> ES) showed greater mean s <strong>and</strong> K IC values<br />
Table 2 Mean values <strong>of</strong> density ðrÞ; elastic modulus ðEÞ;<br />
Poisson’s ratio ðnÞ; <strong>and</strong> Vickers hardness ðHÞ <strong>of</strong> Empress<br />
<strong>ceramics</strong>.<br />
Material properties E1 E2 ES GV<br />
Density (r, g/cm 3 ) 2.47 2.51 2.56 2.53<br />
Elastic modulus (E, GPa) 86 96 96 65<br />
Poisson’s ratio ðnÞ 0.27 0.26 0.24 0.23<br />
Vickers hardness (H, GPa) 5.9 6.3 6.3 5.4<br />
ARTICLE IN PRESS<br />
compared with the <strong>leucite</strong>-<strong>based</strong> ceramic (E1) <strong>and</strong><br />
the GV (Table 3) <strong>and</strong> the differences in mean values<br />
were statistically significant ðp # 0:05Þ:<br />
All fractures initiated along the tensile surfaces<br />
between the inner load points. Corner flaws (CF),<br />
either cracks or voids, were identified as the<br />
fracture origin in 20–30% <strong>of</strong> the specimens (Fig. 3,<br />
Table 3).<br />
Discussion<br />
A. Della Bona et al.<br />
Structural failure associated with an applied load<br />
occurs when the induced stress is greater than the<br />
strength <strong>of</strong> the material. The failure location is<br />
dependent on the size <strong>of</strong> the initiating crack <strong>and</strong> the<br />
fracture toughness. 9 Usually, fracture <strong>of</strong> the ceramic<br />
originates from the most severe flaw. The<br />
large number <strong>of</strong> pre-existing ceramic cracks <strong>of</strong><br />
differing sizes, coupled with a low fracture toughness,<br />
limits the strength <strong>of</strong> <strong>ceramics</strong> <strong>and</strong> causes a<br />
large variability in strength <strong>and</strong> the time dependence<br />
<strong>of</strong> strength. The size <strong>and</strong> spatial distribution<br />
<strong>of</strong> flaws justify the necessity <strong>of</strong> a statistical<br />
approach to failure analysis 18 to determine the<br />
reliability <strong>of</strong> <strong>ceramics</strong>. 11,19<br />
Investigations <strong>of</strong> clinically failed all-ceramic<br />
restorations have shown that the fracture origin is<br />
typically located at the inner tensile surface.<br />
20 – 22<br />
However, for strength tests to yield relevant<br />
service information, the test <strong>and</strong> service environments<br />
must be similar <strong>and</strong> the strength-controlling<br />
flaw population must approximate that responsible<br />
for failure in clinical service. 19 The distribution <strong>of</strong><br />
flexural strengths under wet environmental conditions<br />
is a potential indication <strong>of</strong> ceramic performance.<br />
The greater mean s <strong>and</strong> K IC values <strong>of</strong> E2<br />
<strong>and</strong> ES core <strong>ceramics</strong> are indicative <strong>of</strong> potentially<br />
improved structural performance. However, resistance<br />
to stress corrosion processes <strong>and</strong> a small range<br />
<strong>of</strong> strength values are also factors in structural<br />
reliability. Thus, a combination <strong>of</strong> good fracture<br />
toughness, excellent resistance to stress corrosion,<br />
<strong>and</strong> resistance to loading are required for structural<br />
reliability. If one <strong>of</strong> these elements is missing, then<br />
there may be a false sense <strong>of</strong> security in designing<br />
ceramic prostheses made from these materials. For<br />
example, in the case <strong>of</strong> the Group GV, the Weibull<br />
modulus, m; is twice as large as that for each <strong>of</strong> the<br />
other groups <strong>and</strong> the flaw size is smaller than the<br />
flaw sizes <strong>of</strong> the other groups. This appears to be a<br />
positive result. However, because <strong>of</strong> the low value<br />
<strong>of</strong> fracture toughness, the strength is much less<br />
than that <strong>of</strong> the other groups <strong>and</strong> this, most likely,<br />
would not be a reliable material.