Water sorption and mechanical properties of dental composites C.Bastioli and G. IstmdoG. Donegani,
Roman0
Novara,
&a/y
C. Migliwesi Department
of Engineering,
(Received
8 November
The physical scanning tests.
University
1988:
properties
calorimetry,
disappeared linking
sorption
scanning
indicated
Italy
1989;
accepted
dental
and desorption
calorimetry
20
February
composites
in water,
of the material
1989)
were
measurements
curves of samples
that the small residual monomer
after immersion
reaction
Trento,
14 February
of four commercial water
The differential
ageing in water
of Trento,
revised
investigated and flexural
as prepared
reactivity,
monomer
desorption.
differential properties
and after different
present
which probably acts as a plasticizer
and the residual
through mechanical
times
of
in the as prepared samples,
and facilitates Consistently,
a further crosswater
causes
the
embrittlement of the material, as detected from the flexural mechanical properties. Water sorption and desorption kinetics were measured at different temperatures, the water diffusion coefficients were calculated
and the activation
energies
fracture surfaces and the decrease filler/matrix adhesion. Keywords:
Dental
Bis-phenolglycidyl have gained materials
composites,
methacrylate
increasingly
in dentistry’.
mechanical
(bis-GMA)
larger Many
of the diffusion
properties,
as restorative
of the commercial
of various
impart
types,
high long-term
ization shrinkage3, molecules4
geometry dimensional
reduced
stability’,
finishing
and
chosen
to
low polymer-
release of low molecular
and good surface
weight
to the
high viscosity
dimethacrylate,
methyl
the same
improve
resins’. resin
time
However, and
favour
increase
release
themselves
composites,
about
(MMA),
30%
degree
the water
of
low
included.
In
by weight
fillers of different
monomer
etc., which
the final conversion
diluents the
basic
uptake
molecular most
type, geometry,
at
of the of the weight
commercial
of diluents
are
used.
size and content
ventional
main classes ones, which
silica and silicates ___--___ Correspondence 1990
Butterworth
of dental
contain
composites
70-85%
having a dimension
are: (1) con-
by weight
of about 20 pm, and
and lower mechanical In this
by weight
(< 1 pm).
properties,
the latter shows
properties,
i.e.
high polymerization
properties
paper,
the
properties
compared
effect and
composites
and desorption
MATERIALS
high
shrinkage
with conventional
diffusion
of water
the
were
type
studied
coefficients
sorption
on the
of fracture and water
of four sorption
determined.
AND METHODS
Materials In Table 7, the compositions are reported thin
with
contain
bis-GMA
the class of poly(ethylene The nature, content, of the
inorganic
of the tested dental composites
commercial
layer chromatography
sedigraph 12/90/0302
finishing
size
behaviour-dependent
fillers
means of emission
Ltd. 0142-96
up to 50%
composites.
of quartz,
to Dr C Mlgliaresl. Et Co (Publishers)
of the
of a good
containing
water sorption (about 2 wt%*)
materials
are utilized. The
excellent
conventional
are added to the basic resin, dimethacrylates), bis-phenol
methacrylate
substances, Moreover,
of the
composites,
resin
mechanical
(> 10 P so’) different diluents such as poly(ethylene glycol
the existence
silica of very fine particle
Despite greater
and colour stability5
to the material. Owing
(2) microfine of pyrolytic
products
diluents
and content
The SEM analysis
indicated
sorption
based composites
applications
consist of the same type of base resin, different fillers
process were determined.
of the water uptake on the temperature
methods.
names analysis,
and producers. it was
found
resin, with diluents
From that
all
belonging
to
dimethacrylates)‘. surface were
spectrometry,
area and size distribution
determined
respectively
ash analysis,
Each commercial
product
by
BET tests and is applied
in
19-05 Biomatenals
1990,
Vol
1 1 April
219
Properties of dental composites: C. Bastioli et al.
Table 1 Composition composites
and other characteristics
of the tested
dental
Product name
Adaptic
Miradapt
Profile
Silar
Manufacturer
Johnson Et Johnson Quartz
Johnson Et Johnson Barium silicate 8 1.o 0.37 17.0
S.S. White
3M
Strontium silicate 81.7 0.97 15.8
Pyrolitic silica 50.0 -
40 20 16
26 18 14
Filler type
Filler content (wt%) 77.4 Surface area (m2/g) 0.92 Average diameter (pm) 17.9 Filler size’ s95 40 S60 25 SlO 6
b
*Expressed as wt% of filler with size higher than that indicated in the first column.
components: catalyst and activator. The catalyst contains matrix, filler and benzoyl peroxide; the activator contains matrix, filler and an aromatic amine (NJ/-diidrossi ethyl paratoluidine). Samples were prepared from a catalystactivator of 1 : 1 ratio. two
Methods Differential scanning calorimetry (DSC) measurements were performed by using a differential scanning calorimeter Mettler model DSC30 with a scanning rate of 20”C/min. Water sorption and desorption kinetics were determined on flat samples 0.045 X 3 X 0.5 cm3, using a protocol where the polymerization of the samples was conducted in a mylar mould for 15 min at r.t. After polymerization, all samples were immersed in distilled water at 60°C and then dehydrated under vacuum at 6O”C, until constant weight was attained. Sorption and desorption kinetics were measured by weighing at different times the previously conditioned samples after immersion in water (sorption) and then suspended in a closed bottle on silica gel (desorption), at 37, 48 and 60°C. The fracture surfaces of the samples were observed with a scanning electron microscope (SEM) (Cambridge Stereoscan model 604, Cambridge Instruments, Cambridge, UK). The flexural mechanical properties were measured in air at r.t. (25”C, 50% r.h.) using an lnstron machine on samples previously aged in water for 3, 15 and 60 d, at a crosshead speed of 0.1 cm/min.
RESULTS AND DISCUSSION DSC diagrams of Miradapt, after different times of immersion in water at 37 “C, are shown in Figure 1. The curves obtained with the other materials are very similar. A wide exotherm peak can be observed for the samples aged for 10 min. being associated with the residual curing of the low molecular weight unreacted components. After 24 h. the exothermic peak is no longer evident (in some samples and in other measurements it still appears) and no more residual reactivity can be detected for all samples aged for 60 d in water. The water acts as a plasticizer and favours both the reaction and the desorption of low molecular weight molecules. Generally an increase of the resin glass transition temperature (T,) occurs, which is particularly relevant for the longer time aged samples, indicating the lowering of the Tg due to the presence of water is less important than the effect, due to unreacted species initially present in the composite". Sorption and desorption experiments were performed in order to evaluate the water diffusion coefficients at 37,48
220
Biomaterials
1990, Vol 11 April
I -20
I
I
I
I
I
I
I
0
20
40
60
80
100
120
T,Oc Figure 1 DSC thermograms for Miradapt after (a) 10 min. (b) 24 h and (c) 60 d of immersion in water at 37°C.
and 60°C and the activation energies of the diffusion process. The curves reported in Figures 2 and 3 refer to samples which have undergone a previous sorption/ desorption cycle at 60°C. in order to remove any unreacted monomer. The initial linear dependence of M,, the water content of the sample at the time, t, on the square root of time divided by the sample thickness (t o.5I-’ ), suggests a Fickian behaviour of the transport phenomenon”. The diffusion coefficients can be calculated from the initial slope of the sorption and desorption curve through Equation 1 “: M,/M
= 1 - exp [-7.3
(Df/p2)o.75]
(1)
where D is the diffusion coefficient and M the equilibrium water content. The water diffusion coefficients calculated from the sorption and desorption experiments at 37, 48 and 60°C. are reported in Table 2. In the same table, the percent weight loss after the first conditioning cycle at 60°C. M, and the equilibrium water uptakes in the following sorption cycle, referred to the composite total weight, Mg,,c, and to the amount of resin in the composite, M, r, are indicated. At each temperature, the diffusion coefficients for sorption are lower than the ones for desorption and the difference increases with increasing T. The activation energies of water transport in all materials were calculated by assuming an Arrhenius dependence of the diffusion coefficients on the temperature as shown in Figure 3. where the logarithm of D is plotted versus 1/T. The slopes of the straight lines which correlate D and 1/T, divided by the gas constant, R, give the activation energies, which appear to be higher for sorption (Table 3). The result is frequently found for glassy polymers and can be explained in terms of overall plasticizing effects due to the incoming water. No deviations from the ideal were observed in the sorption kinetic curves (Figure 2) as a consequence of filler/ matrix debonding. In fact, this phenomenon would be characterized by an increase of water uptake with temperature.
Properrim
&
4
Ii
Yt/l Figure 2
at Rj
Table 2 Sorption /O,) and dasffrptkx? fDJ diffusion coefficients (cm2/si: water uptakes after sorption referred to the composite weight lMII. J and to rhe resin weight f M, ,I; wt% decrease IMJ of the dry samples after the firsi conditioning cycle in water at 60°C M,
Adaptic
0.31
37°C
-
Miradapt
0.25
Profile
0.47
Silar
0.88
D, 0, M %C M 9.r D, D, M 9.c M 9.’ D, 0, M 9.c Y?. r 0, D, M Q.C &l9,’
4.97 1.10 4.87 7.11 1.58 0.953 5.01 4.40 8.27 0.788 4.31 8.75 1.11 2.89 5.78
x 10-g
x 10-g x 10-E
x 1O-9 x 10-9
x lo-’ x lo-.8
48 “C
60°C
1.11 1.16 1.04 4.60 1.02 2.30 1.07 5.63 9.89 1.19 0.732 4.00 1.74 2.00 2.44 4.88
2.06 2.57 1.04 4.60 2.55 3.20 1.00 5.26 2.94 3.29 0.690 3.77 3.25 3.52 2.46 4.92
x 10-g x 10-8
x 10-B x 1O-8
x lo-’ x 1O-’
x 1C?-8 x 10-8
Miradapt Profite Silar Adaptic
48.75 65.83 47.48 51.66
26.20 51.29 43.47
37°C. fA/ 48°C and #)
1’0
72
Matertal
immersion time (d) __________ ,--...
X 1O-8 X lo-*
x ?O-8 x IO-’
15
-.. 60
E (GPa)
x 10-a x 10-a
x lo-* x lo-’
60°C as indicated
Table 4 Herural modulus (E] after different ageing times in water 8? 3 7 “C. and weight loss &I,/ and gain @A,) after 60 d of immersion in water
3
Activation energies for water sorption /E,J and the waterdesorption IEd) processes
Table 3
I3
- I raea, secClrGm
Sorption (a/ and desorption lb) curves of Miradapt and War
Material
composites: C. Bastioli et al.
a
silar
0
of den&
Adaptic Miradapt Profile SilW
8.4 6.2 13.5 4.3
9.5 8.6 9.3 5.4
10.4 12.1 9.9 5.9
0.76 0.60 1.40 2.35
0.85 1.07 1.09 2.97
On the contrary, the water uptake decreases with temperature (Table 2). Furthermore, the SEM of.the fracture surface of composites after the water ageing cycle at 60°C (Figure 4), do not show any debonding between filler and matrix. Flexurai mechanical properties were determined in samples aged in water at 37°C for 3, 15 and 60 d. Data for the modulus are reported in Table 4, together with the percent weight loss, M,, and weight gain, M,, determined after 60d. These quantities differ from those reported in Table 2, being measured at 37 “C and on thicker samples not previously conditioned. The difference can be explained, considering that at 60 “C, the polymerization proceeds faster rhan at 37 “C, causing a decrease of the low molecular weight substances that can diffuse out from the material, even if the diffusion coefficients increase. The trend, however, is the same and an approximately similar ratio among the weight losses of different composites was
Biomaterials
1990, Vol 1 1 April
221
Properties of dental composites: C. Bastioli et al.
-17
-12
-1s
-17
0 c -18
-1s
b -17
-12
-IQ
a
310
.
.
3.1
3.2
Figure 3 Arrhenius plot for (0) water sorption and (0) desorption processes of (a} Silar. (b) Profile and (c) Miradapt.
observed. As for the data of Table 2, the water loss and gain of Silar, which contains less filler, is higher. All composites display an elastic modulus which is higher than that of the Silar composite, consistent with their higher filler content. Moreover, whilst, for Adaptic, Miradapt and Silar, an increase of the elastic modulus with the ageing time is observed, a large initial reduction is caused by the aging phenomenon in the flexural modulus of the Profile cement, indicating a different effect of the overall plasticization associated with the incoming water and the outcoming monomers’“. In conclusion, water sorption and desorption experiments demonstrated that the Fick’s law can be used to model the sorption and the desorption behaviour of the tested composites, with diffusion coefficients depending on the temperature following an Arrhenius-type equation. Immersion in water ages the materials and the mechanism appears to be associated with an overall plasticization effect, caused by the release of the unreacted species and the sorption of water. An increase of the elastic flexural modulus for Miradapt, Silar and Adaptic was observed, whilst, for Profile, the modulus decreases after immersion in water. The
222
Biomaterials
1990, Vol 11 April
Figure 4 SEM of fracture surfaces of Profile (a, c) and Silar (6. d) samples before (a, b) and after (c, d) the water sorption at 60°C.
Properties
difference can be explained by a different role played on plasticization by the outcoming species and the incoming water. No debonding occurs for any material between resin and filler, as observed by SEM and demonstrated from the water sorption curves.
5
6
7
REFERENCES 8 Bowen. R.L., Properties of a silica-remforced polymer for dental restoratlons, J. Am. Dent Assoc. 1963, 66, 57-64 Hirasawa, T.. Hlerano, S., Hirabayashi, S., Harashima. I. and Aizawa. M.. Initial dimensional change of composites in dry and wet conditions, J. Dent. Res. 1983, 62, 28-33 Antonucci, J.M. and Toth, E.E., Extent of polymerization of dental resins by differential scanning calorimetry. J. Dent Res. 1983, 62, 121-126 Fletcher,A.M., Purnaveja,S..Amin.W.M., Rltchie.G.M., M0radians.S. and Dodd, A.W.,The level of residual monomer in self-curing denture base materials, J. Dent Res. 1983, 62, 1 18-l 20
9
10
11 12
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C. Basfioli ef al
Powers, J.M., Demlnson. J.8. and Koran, A., Color stability of restorative resins under accelerated aging, J. Den?. Res. 1978, 57, 964-968 Bowen, R.L., Barton, J.A. and Mullineax, A.L., Composite restorative materials, In Dental Marerials Research. National Bureau of Standards Special Publication 354, (Eds G.R. DIckson and J.M. Cassel). US Government Printing Dfflce, Washington DC, 1972, p 379 St. Germain, H., Swartz. M.L., Phillips, R.W., Moore, 8.K. and Roberts, T.A., PropertIes of microfilled composite resins as Influenced by filler content, J. Dent Res. 1985, 64, 155-l 60 Braden, M. and Clarke, R.L., Water absorption characteristics of dental microfmecomposltefilling matenals,Biomarena/s 1984,5,369-372 Cowperthwaite, G.F., Fey, J.J. and Malloy, M.A., The nature of the crosslinking matrix found in dental composite fillmg materials and sealants, In Biomedical and DenralApplicarions of Polymers (Eds C.G. Gebelein and F.F. Koblitz). Plenum Press, New York, 1981, p 379 Apicella. A., Migliaresi. C., Nlcodemo. L., Nvzolals, L.. laccanno. L. and Roccotelli. S., Water sorption and mechanical propertIes of a glass reinforced polyester resin, Composites 1982, 13, 406-410 Barrie, J.A.. in Diffusion in Polymers (Eds J. Crank and G.S. Park), Academic Press, London, 1968, p 259 Crank, J.. MarhemaricsofDiffusion, Clarendon Press, Oxford, 1975
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