Low-temperature particulate calcium phosphates for bone regeneration: Low-temperature particulate...
-
Upload
independent -
Category
Documents
-
view
0 -
download
0
Transcript of Low-temperature particulate calcium phosphates for bone regeneration: Low-temperature particulate...
Low-temperature particulate calciumphosphates for bone regeneration
M. V. F. AraujoV. C. MendesP. ChattopadhyayJ. E. Davies
Authors’ affiliations:M. V. F. Araujo, V. C. Mendes, P. Chattopadhyay,J. E. Davies, Faculty of Dentistry, University ofToronto, 124 Edward Street, Toronto, ON, CanadaM5G 1G6Institute of Biomaterials and BiomedicalEngineering, University of Toronto, 164 CollegeStreet, Toronto, ON, Canada M5S 3G9.
Correspondence to:J. E. DaviesInstitute of Biomaterials and BiomedicalEngineeringUniversity of Toronto164 College StreetToronto, ONCanada M5S 3G9Tel.: (416) 978 1471Fax: (416) 946 5639e-mail: [email protected]
Key words: anorganic bone, bioactive glass, bone substitutes, calcium phosphates, demi-
neralized bone matrix
Abstract
Background: Low-temperature synthesized calcium phosphates are produced by mixing
calcium phosphate powders in an aqueous solution resulting in a precipitated phase. These
compounds can be formulated in several forms (e.g. injectable cements and implantable
blocks), and are commonly used as bone substitutes and drug delivery systems for the
treatment of bone defects. As bone substitutes, calcium phosphates in general offer the
advantages of being biocompatible and osteoconductive.
Aims: The present work employed a machine-based process to derive a reproducible
preparation method for low-temperature calcium phosphate particulate (LTCP). The in vivo
outcomes of LTCP were compared with those of three commercially available bone
substitutes by histomorphometric measurements of bone formation and material
degradation in a rat femur implantation model.
Materials & Methods: Specifically, LTCP, anorganic bovine bone (AB), bioactive glass (BG),
and demineralized bone matrix (DBM) were implanted in defects created in the distal
aspect of rat femora. Reparative bone and particulate volumes of these biomaterials were
evaluated post-operatively using micro-computed tomography and histological analyses at
3, 6, 12, and 16 weeks.
Results & Discussion: Results showed that, despite invoking bone formation, AB, BG, and
DBM were found un-resorbed in situ at 16 weeks. Conversely, LTCP showed an early increase
in bone formation as well as clear evidence of complete degradation and reparative
bone remodelling, resulting in the total reconstitution of the marrow cavity and marrow
tissue.
Conclusion: LTCP promoted increased early bone formation, associated with an improved
degradation rate, compared with the other three bone-substitute biomaterials tested.
Effective bone grafts should provide ade-
quate support during repair without delay-
ing the remodelling process. Thus, one of
the great challenges in the bone biomater-
ials field is to develop bone substitutes that
favor repair, but are resorbed and substi-
tuted by natural bone during tissue turn-
over (Schwartz et al. 2008).
Low-temperature synthesized calcium
phosphates (LTCaP) consist of biomater-
ials obtained from the mixing of equimolar
amounts of calcium phosphate powders in
aqueous solutions at or below room tem-
perature. In the preparation process of these
materials, the grinding of the powders is
done using a machine, whereas the mixing
of the solid with the liquid phase is done by
hand (Brown & Chow 1986; Fukase et al.
1990; Bohner et al. 2005; Ambard & Mue-
ninghoff 2006). These biomaterials are
Date:Accepted 26 September 2009
To cite this article:Araujo MVF, Mendes VC, Chattopadhyay P, Davies JE.Low-temperature particulate calcium phosphates forbone regeneration.Clin. Oral Impl. Res. 21, 2010; 632–641.doi: 10.1111/j.1600-0501.2009.01864.x
632 c� 2010 John Wiley & Sons A/S
biocompatible and osteoconductive, and
are often used as bone substitutes in differ-
ent forms, such as in situ setting injectable
cements (Miyamoto et al. 1997, 1999;
Ooms et al. 2003), solid or porous litho-
morphs (Takagi & Chow 2001; Zhang
et al. 2006), and as set cement granules
(Tamimi et al. 2006, 2007, 2008).
However, the diverse reagent chemistry
described for the preparation of calcium
phosphates, allied with the various implan-
tation models, have resulted in great varia-
bility of the reported in vivo outcomes.
Little calcium phosphate cement resorp-
tion and bone formation were reported at
18 months post-operative in a cat sinus
obliteration model (Friedman et al. 1991);
however, in rat tibial defects, such cements
showed increased bone formation but no
osteoclastic resorption at 8 (Miyamoto
et al. 1997) and 24 weeks (Ooms et al.
2003) after implantation. Conversely, the
replacement of in situ setting calcium
phosphates by bone was reported in cat
parietal defects at 6 months (Costantino
et al. 1992) and in dog facial defects at 9
months (Shindo et al. 1993).
Among the formulations reported in the
literature, particulate CaP biomaterials are
especially attractive as they have an in-
creased surface area, are osteoconductive,
biocompatible (Ginebra et al. 2006), and
can fill any defect size or shape (Gautier et
al. 2001; Tas 2008). The implantation of
three size ranges (10–20; 80–100; 200–
400mm) of ceramic particulate biphasic
calcium phosphate [hydroxyapatite
(HA)þ b-tricalcium phosphate (b-TCP)]
showed that 10–20 and 200–400 mm parti-
cles presented significant bone formation
compared with controls. However, despite
invoking an increased inflammatory reac-
tion, 10–20mm particles promoted both
increased bone formation and particulate
resorption (Malard et al. 1999). An in-
creased bone mineral density, granule re-
sorption, and bone formation were found
after calvaria implantation of brushite at 4
weeks post-operative compared with
BioOsss
(Tamimi et al. 2006) and empty
defects (Tamimi et al. 2007). Similarly, the
implantation of monetite granules (0.2–
1 mm in size) in rabbit’s calvaria showed
signs of particulate resorption and an in-
creased mineral content compared with
empty defects at 4 and 8 weeks post-
operative (Tamimi et al. 2008).
One of the most important characteris-
tics of LTCaP is their resorbability in vivo,
which occurs by the combination of two
processes: (1) dissolution in the in vivo
fluidic environment and (2) cell-mediated
resorption, mainly by osteoclasts. The
in vivo dissolution of these biomaterials is
strictly related to their composition and
particle size (LeGeros & LeGeros 2003),
while their resorption is dictated by the
gradual dissolution of the apatitic phase in
the acidic environment created by protons
secreted through osteoclastic membrane-
bound vacuolar proton pumps (V-ATPases)
(Farina & Gagliardi 1999).
In fact, it has long been known that the
characteristics of calcium phosphates are
related to their preparation methods.
Brown & Chow (1986) developed the first
formulation of LTCaP and, since then,
different formulations have been used for
the production of effective grafting materi-
als (Ambard & Mueninghoff 2006). For
instance, the pore sizes of conventional
calcium phosphate blocks range from a
nanoscale to 10 mm with limited intercon-
nectivity. Therefore, cellular invasion
through the scaffold is constrained and
cell–implant interactions are restricted to
their surface (Apelt et al. 2004). However,
Chow (2000) incorporated macropores into
the matrix of calcium phosphate cements
by the addition of large polyssacharides.
After the cements hardened, they were
soaked in an aqueous solution to dissolve
the polyssacharides, which left large, inter-
connected voids within the material struc-
ture (Chow 2000). Alternative approaches
have been proposed by del Real et al. (2003)
using gas flux and more recently by Tas
(2008) using spherical, porous, CaP gran-
ules produced with NaCl as the porogen.
While the above-mentioned authors
have used different strategies to increase
the biomaterial surface area, the present
work uses a low-temperature calcium
phosphate particulate (LTCP), produced
through a novel self-setting cement pro-
cess, as an alternative bone substitute to
harness the known advantages of increase
in surface area (Araujo 2008), increased
bone formation (Ginebra et al. 2006), and
biodegradation rate (Tamimi et al. 2006,
2007, 2008). Thus, we compared the in
vivo outcomes of LTCP with those of
anorganic bovine bone (AB), bioactive glass
(BG), and demineralized bone matrix
(DBM) in a rat model. We show that
LTCP invokes improved osteogenesis, but
also allows its resorption and substitution
during bone remodelling.
Material and methods
Preparation of LTCP
Calcium phosphate cement was obtained
using the same chemistry proposed by
Brown & Chow (1986). An equimolar
mixture of two calcium phosphate powders
with a phosphate solution was produced,
with a powder to liquid ratio fixed at 2 mg/
ml. The powder reagents were dicalcium
phosphate anhydrous (CaHPO4 – DCPA),
tetracalcium phosphate (Ca4(PO4)2O –
TTCP), and the liquid phase was a 0.2 M
solution of Na2HPO4 and NaH2PO4 in a
4 : 1 ratio (vol/vol).
In order to obtain more reactive cements,
commercial ultrapure DCPA (Sigma, St
Louis, MO, USA) and TTCP with purity
495% (Clarkson Chromatography Pro-
ducts Inc., South Williamsport, PA, USA)
were wet-ground with 100% ethanol at a
vibrational frequency of 30 rps for 25 and
20 min, respectively, using a mixer mill
machine (MM301, Retsch, Burlington,
ON, Canada). The resultant TTCP and
DCPA pastes were allowed to dry for 24 h
in a fume hood and subsequently stored in
a desiccator at 601C. The final particle size
ranges were 0.6–20mm for DCPA and 2–
35 mm for TTCP.
Next, 0.068 g of DCPA and 0.183 g of
TTCP were mixed with 125ml of the
neutral phosphate solution using a 45 ml
zirconium oxide jar with a 20 mm zirco-
nium oxide ball, for 30 s at a vibrational
frequency of 20 rps. The final paste-like
cement was allowed to set for 24 h in the
incubator at 371C, with 5% CO2 and
100% relative humidity. It was subse-
quently ground manually into particles,
using a pestle and mortar, and sieved into
a size range of 90–355 mm. The final LTCP
was stored in glass vials, labelled and
g-sterilized at 2.5 Mrads 60Co.
Other tested biomaterials
Commercial brands of particulate AB
(BioOsss
, Geistlich Biomaterials, Wolhu-
sen, CH, Switzerland) with a particle size
range of 200–1000 mm, BG particles (Bio-
Grans
, Biomet-3i, Palm Beach Gardens,
Araujo et al �Low-temperature particulate calcium phosphates
c� 2010 John Wiley & Sons A/S 633 | Clin. Oral Impl. Res. 21, 2010 / 632–641
FL, USA) with sizes ranging from 300 to
350mm, and granulated DBM provided in a
lipid carrier (Allogenixt, Biomet Micro-
fixation, Jacksonville, FL, USA) were also
tested in this study.
Scanning electron microscopy (SEM)
Qualitative surface analysis was conducted
for AB, BG, and DBM using a Hitachi
S3400 model SEM (Oakville, ON, Canada)
with a resolution of 5 nm and an accelerat-
ing voltage of 5 kV, without any sputter
coating. On the other hand, a quantitative
analysis of LTCP was conducted because it
represents a new compound that needs
complete characterization. For this pur-
pose, a Hitachi S-5200 model of field-
emission scanning electron microscope
with a resolution of approximately 1.8 nm
and an accelerating voltage of 5 kV was
used. The particulate material was car-
bon-coated and affixed to an aluminum
stub using conductive carbon paint (Struc-
ture Probe Inc., West Chester, PA, USA).
Surface area, porosity, and pore size
Gas adsorption (Autosorbs
-1, Quanta-
chrome Instruments, Boynton Beach, FL,
USA) was used to analyze the surface area
of LTCP, AB, and BG through the BET
(Brunauer–Emmett–Teller) method (Bru-
nauer et al. 1938) while pore volumes
were calculated using the BJH (Barret–
Joynet–Halenda) method (Barret et al. 1951).
Specifically, adsorption analysis was con-
ducted by adding successive volumes of
nitrogen gas to the samples cell (at
� 1961C), followed by the measurement
of the equilibrium pressure (P0). Next,
desorption of the samples was obtained
through successively lowering the pressure
of the cell (P) while gas removal was
quantified. Finally, qualitative and quanti-
tative data are obtained by the resulting
isotherms (Gregg & Sing 1982).
Powder X-ray diffraction (PXRD)
Cement reaction kinetics were analyzed
using PXRD. Hand-made CaP cement
ground into particles was also prepared to
serve as control group. Briefly, these ce-
ments were produced using 0.068 g of
DCPA and 0.183 g of TTCP, which were
placed in a sterilized glass dish and mixed
with a glass stirring-rod for 30 s. Next,
125mL of the neutral phosphate solution
was added to the powders and the phases
were mixed thoroughly for 3 min to a
paste-like consistency. The final cement
was allowed to set for 24 h in the incubator
at 371C, with 5% CO2 and 100% relative
humidity. It was subsequently ground into
particles, using a pestle and mortar, and
sieved into a size range of 90–355 mm. Two
grams of hand-made CaP particles and
LTCP were stored in 1.5 ml eppendorf
tubes, which were frozen in liquid nitrogen
(�801C) at 1, 3, 5, and 10 days, and
weekly from 1 to 8 weeks (n¼ 3). The
freezing of the samples aimed at the arrest-
ing of the cement reaction at specific time
points.
The samples were run using a normal
front packing technique on a Bruker AXS
D8 Discover Microdiffraction system (Ma-
dison, WI, USA) with CuKa point-focus
X-ray source operating at 40 kV/40mA.
The system was equipped with a curved
primary graphite monochromator and two-
dimensional (2D) proportional detector.
Data were collected on two frames at
1200 s exposure, which cover a range of
20–581 and the 2D diffraction images were
then integrated with a step size of 0.0051 2yand converted to standard I vs. 2y diffraction
patterns. The phase identification was per-
formed by Diffrac Plust data processing
software Evat v. 8.0 and Search/Matcht
routine. This qualitative phase composition
was established by comparison with the
reference PXRD patterns stored in the Uni-
versity of Toronto Chemistry Department
PDF-2 Database (2001) via Search-Matcht
software. The profile fitting applications
such as Rietveld refinement, quantitative,
and microstructure analyses were performed
using Topast v. 2.1 software.
Surgical procedure and sample harvesting
The surgical protocol was approved by the
Local Animal Care Committee of the
Faculty of Dentistry at the University of
Toronto. Forty male Wistar rats (200–
250 g, Charles River Laboratories, Senne-
ville, QC, Canada) were anesthetized by
inhalation of isofluorane in nitrous oxide
and oxygen (900 ml total flow rate – 4% for
induction and 2% as maintenance). Bupre-
norphine (0.01–0.05 mg/kg) was adminis-
tered subcutaneously as analgesic both
before and after the surgery. To ensure
the same volume of test biomaterial was
implanted at each surgical site, custom-
made stainless-steel syringes with end
tips matching the diameter of the defects
were used to deliver the implants into the
defects. Following placement, a Teflon
membrane was used to cover the bony
defects to prevent the washing out of the
particles by blood from the marrow cavity.
In this manner, 10 mm3 of LTCP, AB, BG,
or DBM (n¼5 samples/group/time-point)
were randomly implanted bilaterally in
single bone defects created in the distal
femoral metaphyses using a 2.3 mm round
dental bur under constant saline irrigation.
After implantation, the muscle layer was
repositioned and sutured (4-0 Polysorbt,
Norwalk, CT, Syneture, USA), and the
skin was closed with 9 mm wound clips
(Becton Dickinson, MD, USA).
During the post-operative period, the
animals were monitored on a daily basis
in the animal care facility of the Faculty of
Dentistry of the University of Toronto.
Five animals were euthanized by cervical
dislocation after CO2 exposure at each of
the 3, 6, 12, and 16 weeks post-operation.
The femora were harvested, trimmed, and
fixed in 10% neutral formalin for at least
24 h.
Micro-computed tomography (MicroCT)
MicroCT scans of each femur were con-
ducted with a microtomography system
(MicroCT40, Scanco Medical, Basserdorf,
Switzerland). All trimmed femoral samples
were stacked (in groups of six) in a cylind-
rical holder (8.5 mm inner diameter,
43 mm height) and scanned at 70 kV and
114 mA. The specimens were scanned in
high-resolution mode.
The final 2D images were composed of
500–700 axial-cut slices, each one with
6 mm in thickness. After scanning and
reconstruction, a standardized region of
interest (ROI) comprising the defect with
the implant and surrounding reparative
bone within the marrow tissue was drawn
at different depths (approximately every 50
slices) of the 2D dataset, so that the final
drawings could be morphed and render a
3D ROI. The quantification of both bone
and particulate material volumes was
possible through their segmentation in dif-
ferent threshold values, which were deter-
mined by the gray-level distribution. In
addition, the values obtained were divided
by an averaged defect size (10 mm3), so that
the measurements were consistently re-
lated to the volume of the initial defect.
Araujo et al �Low-temperature particulate calcium phosphates
634 | Clin. Oral Impl. Res. 21, 2010 / 632–641 c� 2010 John Wiley & Sons A/S
Because the DBM putty was not visible
in the MicroCT images, the histomorpho-
metric evaluation of this group was done
using histology slides. Two slides per sam-
ple per interval were selected and the putty
area was measured using the Image J 1.37v
software (National Institute of Health,
Bethesda, CT, USA) (Abramoff et al.
2004). However, bone volume measure-
ments for this group were conducted using
the MicroCT thresholds as described
above.
Histological analysis
The most representative samples for each
interval observed in the MicroCT analysis
were chosen for histological processing.
The samples were initially dehydrated at
room temperature in increasingly concen-
trated ethanol solutions (70, 95, 100 v/v).
Then, they were embedded in polymethyl-
methacrylate (Osteo-Bed, Polysciences,
Warrington, PA, USA). Thin sections of
the specimens (30–40mm) were produced
by the Exakt cutting and grinding system
(Exakt Technologies Inc., Oklahoma City,
OK, USA) and stained by toluidine blue.
Images in different magnifications were
retrieved using a Leitz Aristoplan micro-
scope, Q imaging Micropublisher 5.0 RTV
digital camera, and Openlab 4.0.4 software
(Improvision Ltd, Coventry, West Mid-
lands, UK).
Statistical analyses
Statistical analyses were performed using
the computer software Statistical Analysis
System (SAS Institute Inc., Cary, NC,
USA). Linear generalized estimating equa-
tions (GEE) were used to examine the
effects of treatment, time, and treatment
over time on bone and particulate volume.
GEE were used rather than traditional ana-
lysis of variance due to the correlated
nature of the data (treatments were applied
bilaterally on each rat) (Liang & Zeger
1986). A Bonferroni correction was used
when conducting post hoc analyses of sta-
tistically significant main effects. For each
model, residuals were analyzed for normal-
ity, and when found to be non-normal,
sensitivity analyses were conducted re-
moving outliers to evaluate the impact on
findings.
Differences among the HA conversion of
hand-made CaP particles and LTCP were
compared using ANOVA analysis of var-
iance followed by Tukey adjustment for
multiple comparisons. P-values o0.05
were considered significant.
Results
Qualitative SEM and histological analyses
Figure 1 shows SEM micrographs of LTCP,
AB, BG, and DBM as received. A qualita-
tive analysis of LTCP revealed more com-
plex features than those of AB and BG.
A topographical comparison between
DBM putty and LTCP was not feasible,
because the former is presented as demi-
neralized bone particles embedded in a lipid
carrier and therefore displays a smooth
surface.
Figure 2 shows histological sections of
LTCP, AB, BG, and DBM at 3 and 16
weeks. A qualitative histological evalua-
tion depicted reparative bone in close con-
tact to all samples at 3 weeks. This was
identified as woven bone, as could be ex-
pected in the rat, due to the large, randomly
arranged, osteocyte lacunae. Small marrow
spaces were observed in the peri-implant
bone, which were populated by neutro-
phils, round mononuclear polarized cells,
and large multinucleated cells suggestive of
osteoclasts. These multinucleated cells
were more often seen around LTCP than
AB, BG, and DBM. Defects filled with
LTCP showed complete remodelling of
the reparative bone resulting in restitution
of the marrow tissue at 16 weeks. Repaired
marrow consisted of colonies of small cells
dispersed among round (fat) cells. There
was no evidence of inflammatory or osteo-
clast-like cells.
Using visual inspection, a comparison
between histological and SEM data showed
the maintenance of the shape and size of
the particulate AB and BAG until the 16-
week mark, demonstrating little sign of
long-term resorption (Figs 1 and 2). Histo-
logical sections of DBM displayed separated
masses of demineralized bone particles sur-
rounded by a thin layer of bony tissue, with
little infiltration of cells (Fig. 2).
Reaction kinetics analysis of hand-madeCaP particulate and LTCP
X-ray diffraction analysis of hand-made
CaP particulate and LTCP confirmed HA
as the major final component of the ce-
ment reaction (approximately 51% and
67%, respectively). In LTCP, the residuals
of DCPA and TTCP were greater than the
Fig. 1. Scanning electron micrographs (SEM) of ‘as received’ (a) low-temperature calcium phosphate particulate
(LTCP), (b) anorganic bovine bone (AB), (c) bioactive glass (BG), and (d) demineralized bone matrix (DBM). The
particulates have sizes ranging from 90 to 355 mm (LTCP), 300 to 350 mm (BG), and 200 to 1000mm (AB). The
demineralized bone particles of DBM are delivered in a lipid carrier, and are thus not visible as individual
particles by SEM.
Araujo et al �Low-temperature particulate calcium phosphates
c� 2010 John Wiley & Sons A/S 635 | Clin. Oral Impl. Res. 21, 2010 / 632–641
second (approximately 4%) b-TCP end
product (Table 1). Thus, LTCP shows an
increased and more consistent HA conver-
sion than hand-made samples, which may
be a result of the mechanized activation
employed in the preparation process of
LTCP (Fig. 3).
Surface area, porosity, and pore size
Table 2 shows the surface area and pore
volume analyses for LTCP, AB, and BG.
LTCP presented higher surface area
(77.2 m2/g) than AB (61.14 m2/g) and BG
(0.231 m2/g). Similarly, an increased
microporosity was found for LTCP (14.61
cm3/g) compared with AB (6.71 cm3/g) and
BG (0.036 cm3/g). On the other hand, AB
showed higher pore volumes (0.36 cm3/g
for pores diameter smaller than 768 A at
maximum pressure¼ 0.974 atm.) com-
pared to LTCP (0.11 cm3/g for pores dia-
meter smaller than 772.8 A at maximum
pressure¼ 0.974 atm.) and BG (0.000413
cm3/g for pores diameter smaller than
848 A at maximum pressure¼ 0.977 atm.).
LTCP increased surface area could be ex-
plained by its small particle size range
allied with high pore interconnectivity gen-
erated by the interlocking of HA crystals
during cement setting (Ginebra et al.
2006). The decreased surface area of BG
beads can be attributed to its solid compo-
sition with absent internal porosity while
the surface area and pore volume values
found for AB are a result of its bovine HA
architecture.
Reparative osteogenesis and particulatedegradation
The post-operative period was uneventful
for all animals, except for two animals that
had fractured femora (AB 16 weeks and
DBM 3 weeks). However, the defects of
contralateral legs were still included in this
study (DBM 16 weeks and AB 3 weeks).
MicroCT slices of the bone and particulate
volumetric measurements for LTCP, AB,
BG, and DBM at 3 and 16 weeks are shown
in Fig. 4. LTCP and BG showed increased
values of reparative bone volume at 3
weeks post-operative, which were statisti-
cally significant compared with AB
(P¼ 0.0005 for LTCP and P¼ 0.0014 for
Table 1. Powder X-ray diffraction of hand-made CaP particulate and low-temperaturecalcium phosphate particulate (LTCP)
Hand-made CaP particulate LTCP
HA DCPA TTCP b-TCP HA DCPA TTCP b-TCP
1d 46.6 32.5 12.7 8.3 79.7 8.1 8.5 3.73d 44.6 30.6 10.1 14.7 81.7 8.2 6.3 3.95d 45.4 34.4 7 13.3 75.8 8.2 15.1 0.91w 67.7 20.4 10.4 1.6 73.1 8.5 17 1.410d 55.4 27 4.1 13.5 78.6 4.7 13.3 3.42w 57.6 23.8 3.9 14.7 72.9 10.1 13.5 4.23w 62.3 21.7 3.3 12.7 71.1 10.4 14.1 4.44w 63.7 23.9 3.9 8.5 73.7 13.8 9 3.45w 58.7 25.4 3.7 12.2 67.7 12.2 15.3 4.86w 55.7 27.6 5.2 11.4 80.6 8.1 9 2.37w 57.6 24 4.8 12.3 84.7 3.6 9.1 2.78w 50.6 31.3 5.5 12.6 67.2 16 12.7 4.1
LTCP reaction occurred faster and resulted in increased HA conversion with decreased amounts of
residual DCPA and b-TCP.
DCPA, dicalcium phosphate anhydrous; TTCP, tetracalcium phosphate; HA, hydroxyapatite; b-TCP,
b-tricalcium phosphate; d, days; w, weeks.
Fig. 2. Toluidine blue-stained resin-embedded sections of low-temperature calcium phosphate particulate (LTCP), anorganic bovine bone (AB), bioactive glass (BG), and
demineralized bone matrix (DBM) at 3 (a, b, c, and d) and 16 weeks (e, f, g, and h). (a) At 3 weeks bone formed an intimate contact with the particulate material of LTCP.
However, the latter was no longer visible, at the same magnification, at 16 weeks due to its almost complete degradation (not shown). However, at higher magnification
(e) it was still possible to see some evidence of residual particles enveloped in cortical bone (see also Fig. 4e). Conversely, reparative trabecular bone was very evident at
both 3 and 16 weeks for the AB, BG, and DBM samples. The lack of obvious differences in the trabecular bone volume at 3 and 16 weeks is evidence of the lack of
degradation of each of these materials in this site. Field widths (a, b, c, d, f, g, h)¼ 810mm; (e)¼142.3 mm.
Araujo et al �Low-temperature particulate calcium phosphates
636 | Clin. Oral Impl. Res. 21, 2010 / 632–641 c� 2010 John Wiley & Sons A/S
BG). Higher bone volumes were found for
BG compared with DBM at 6 weeks
(P¼ 0.0002) and AB at 12 weeks
(P¼ 0.0006). LTCP displayed lower bone
volume compared with all other bio-
materials (Po0.0001) at 12 weeks post-
operative. Moreover, the bone surrounding
LTCP had almost completely remodelled
with restoration of the marrow compart-
ment at 16 weeks post-operative, whereas
the other materials still presented increased
bone volumes within the implantation site
(Po0.0001) (Fig. 5).
Particulate volumes of AB and BG were
statistically higher than those of LTCP at
all intervals. Similar volumes of AB and
BG were observed at 3 (P¼ 0.8051) and 6
weeks (P¼ 0.1646) post-operative. How-
ever, increased amounts of AB and BG
compared with LTCP were found at 3
and 6 weeks (Po0.0001). A slow particle
degradation was observed for AB and BG at
12 weeks post-operative (P¼ 0.0115),
whereas LTCP had almost completely re-
sorbed (Po0.0001). Similarly, increased in
situ volumes of AB and BG were seen at 16
weeks post-operative, while LTCP had
completely remodelled. Little sign of re-
sorption was found for AB particles until
the 12th week mark, time at which it
presented a decrease of 8.6% in volume.
From 12 to 16 weeks post-operative, AB
implants were unchanged (resorption of
8.6% in volume from 3 to 16 weeks post-
operative). BG beads showed a decrease of
23.5% in volume from 3 to 6 weeks post-
operative, degradation which decreased to
11.5% from 6 to 12 weeks post-operative.
Similarly to AB, the volume of BG was
kept the same from 12 to 16 weeks post-
operative (volume degradation of 32.4%
from 3 to 16 weeks post-operative). LTCP
presented a decrease of particulate volume
of 33.3%, 75%, and 100% from 3 to 6, 6 to
12, and 12 to 16 weeks, respectively (Fig.
6). Results of area measurements for DBM
showed increased putty values at the final
interval studied and a decreased degrada-
tion rate from 3 to 16 weeks (Fig. 7). This
material was kept un-resorbed from 3 to 6
weeks, but resorbed 28% from 6 to 12
weeks and 16.7% from 12 to 16 weeks
(resorption of 37.5% in area from 3 to 16
weeks post-operative).
Discussion
The concept of producing granulated
LTCaP for bone regeneration has been
explored by Tamimi et al. (2006, 2007,
2008). However, the histomorphometric
analysis for these studies was obtained
from six randomly chosen histological
slices per sample and evaluated the total
mineral density of the implantation site at
4 weeks (Tamimi et al. 2006, 2007) and 4
and 8 weeks post-operative (Tamimi et al.
2008). Traditional tissue evaluation using
histological 2D sections has been broadly
applied in the bone biomaterial field due to
its ability to generate high-resolution
images, allowing for the analysis at the
cell level. However, quantitative histomor-
phometric analysis of histological sections
may result in inaccurate values of the 3D
material measured (Muller et al. 1998). On
the other hand, MicroCT evaluation does
not render the imaging of cellular composi-
tion, but represents a non-invasive techni-
que, which enables a precise 3D analysis of
bone architecture and healing. In the dental
field, MicroCT has been used mainly for
the characterization of bone architecture,
the quantification of bone–implant con-
tact, and the analysis of dynamic condi-
tions, such as bone formation and
resorption rates (Rebaudi et al. 2004).
Therefore, the correlated histological (qua-
litative) and MicroCT (quantitative) eva-
luations of this work aimed at a thorough
analysis of LTCP, AB, BG, and DBM
in vivo effects.
It should be emphasized that complete
healing of the rat femora model used
herein, where there is initially no trabecu-
lar bone, requires repair of the cortex,
regeneration of the marrow cavity and
marrow tissue, and an absence of reparative
trabecular bone. Thus, while we could
observe that AB, BG, and DBM invoked
bone formation, the presence of high vo-
lumes of these materials within the im-
plantation site at 16 weeks, together with
surrounding reparative trabecular bone, is
evidence of their poor in vivo resorbability.
Moreover, SEM and histological analyses
showed only small structural changes in
AB, BG, and DBM throughout the study.
Fig. 3. Temporal HA conversion of hand-made CaP particulate and LTCP (n¼ 3). The mechanical activation
proposed for low-temperature calcium phosphate particulate (LTCP) may have rendered this material more
reactive because it presented a faster and increased HA conversion than hand-made CaP particulate samples.
Table 2. Surface area and pore volume analyses for low-temperature calcium phosphateparticulate (LTCP), anorganic bovine bone (AB), and bioactive glass (BG)
Surface area (m2/g) Microporosity (cm3/g) Pore volume (cm3/g)
LTCP 77.22 14.61 0.11AB 61.14 6.71 0.36BG 0.231 0.036 0.000413
The BJH method allowed for the measurement of pores diameter smaller than 768 A at 0.974 atm.
maximum pressure for AB, pores diameter smaller than 773 A at 0.974 atm. maximum pressure for
LTCP, and pores diameter smaller than 848 A at 0.977 atm. maximum pressure for BG. LTCP presented
higher surface area and microporosity than AB and BG. AB showed higher pore volumes.
BJH, Barret–Joynet–Halenda.
Araujo et al �Low-temperature particulate calcium phosphates
c� 2010 John Wiley & Sons A/S 637 | Clin. Oral Impl. Res. 21, 2010 / 632–641
On the contrary, complete healing was
achieved in the case of LTCP where, by
16 weeks, the cortex, marrow cavity, and
marrow tissue were all completely regen-
erated, without any residual artificial ma-
terial remaining. Specifically, LTCP was
able to maintain its osteoconductivity even
after significant resorption without imped-
ing tissue turnover. In addition, this im-
proved resorption profile of LTCP may be
the result of the novel preparation methods
used to produce LTCaP, resulting in in-
creased surface area and microporosity (as
showed by BET and BJH analyses). These
characteristics, allied with the smaller par-
ticulate size, offered an increased surface
area for both bone deposition and osteo-
clastic activity.
The slow degradation rate of AB has been
attributed to its composition (bovine HA),
particle size (250–1000 mm) (Yildirim et al.
2000; Araujo et al. 2001), and to possible
structural changes caused by its heating
(approximately 4001C) preparation process
(Tadic & Epple 2004), whereas the degrada-
tion rate of BG depends on the hydrolysis
of the glass network, which disrupts the
granules and favors phagocytosis of its
silica-gel core (Lai 2000; Cordioli et al.
2001; Huygh et al. 2002). DBM purported
osteoinductivity derives from its growth
factor content [bone morphogenetic pro-
teins (BMPs)]. However, there is a great
variability reported concerning DBM
which may be a result of differences in
the total amount of BMPs remaining fol-
lowing processing and sterilization of the
material, carrier (Peterson et al. 2004),
particle size, porosity, and shape (Louis-
Ugbo et al. 2004). This variability is also
partly related to the bone donor. Thus,
Fig. 5. Bone volumes for low-temperature calcium phosphate particulate (LTCP), anorganic bovine bone (AB),
bioactive glass (BG), and demineralized bone matrix (DBM). AB, BG, DBM displayed higher bone volume
values than seen in the normal medullary cavity, with little sign of reparative bone remodelling. LTCP showed
similar reparative bone formation compared with the other biomaterials but an increased remodelling profile by
16 weeks.
Fig. 4. Micro-computed tomography images for bone and particulate volumes of low-temperature calcium phosphate particulate (LTCP), anorganic bovine bone (AB),
bioactive glass (BG), and demineralized bone matrix (DBM) at 3 (a, b, c, d) and 16 weeks (e, f, g, h). (a) At 3 weeks, LTCP was surrounded by trabecular bone within the
marrow cavity and cortical wound site. (e) At 16 weeks both the LTCP, and the surrounding trabecular bone, were completely remodelled; although some particulate
could still be seen enveloped in the healed cortical bone (arrows). The presence of both AB and BG particles, and their enveloping thin trabecular bone, is evident at both 3
and 16 weeks (b & c; f & g, respectively). Similarly, reparative trabecular bone formation is also evident at both 3 and 16 weeks for DBM samples (d and h). Although the
demineralized particulate was not radio-opaque, the presence of trabecular bone at 16 weeks in these samples suggests that residual DBM still exists in the marrow cavity.
Interestingly, while LTCP and DBM samples showed complete healing of the cortical bone (e and h), the margins of the cortical defects for AB and BG samples are still
visible at 16 weeks.
Araujo et al �Low-temperature particulate calcium phosphates
638 | Clin. Oral Impl. Res. 21, 2010 / 632–641 c� 2010 John Wiley & Sons A/S
characteristics such as age, health condi-
tions, drug therapy, and genetic alterations
could be related to donor–host site incom-
patibility (Haas et al. 2002), resulting in
the osteoinductivity of DBM being incon-
sistent (Schwartz et al. 1998).
During early peri-implant healing, osteo-
conductive materials stimulate the recruit-
ment and migration of osteogenic cells,
which deposit bone matrix onto their sur-
faces (Davies 1998; Davies & Hosseini
2000). Ideal bone biomaterials should sti-
mulate increased bone formation during
early endosseous healing but, over time,
should be remodelled by the joint activity
of osteoclasts and osteoblasts (Kohri et al.
1993). In this context, the long-term pre-
sence of bone substitutes in the implanta-
tion site may affect new bone growth and
interfere in the characteristics of the newly
forming tissue (Tamimi et al. 2006), possi-
bly by restricting the formation of new
bone through the granulation tissue (Stav-
ropoulos et al. 2004). Moreover, the total
reconstruction of the natural bone struc-
ture in an endosseous defect site permits
maximal functional tissue remodelling,
which may otherwise be compromised by
the presence of residual biomaterials
(Ooms et al. 2003).
Implantable LTCaPs are osteoconduc-
tive and show a faster resorption than
high-temperature synthesized ceramics
(Ohura et al. 1996). However, information
on their biological performance (i.e. disso-
lution, resorption times, and bone forma-
tion) varies due to inconsistencies in the
reagent chemistry and models used
(Bohner et al. 2005). These materials have
been the targets of several studies. A vast
majority of these reports have focused on
the in vitro evaluation of self-setting ce-
ments, cement blocks, and granules aim-
ing at their mechanical properties (Fukase
et al. 1990; Liu et al. 1997; Ambard &
Mueninghoff 2006; Tas 2008), drug release
capabilities (Bohner et al. 2000), as well as
the effects of powdered cement on cellular
function (Pioletti et al. 2000). On the other
hand, in vivo analyses have been conducted
on CaP blocks (Hamanishi et al. 1996),
injectable cements (Miyamoto et al. 1997,
1999; Ooms et al. 2003), and set cement
particles (Tamimi et al. 2006, 2007, 2008).
Several studies have reported changes in
the initial chemistry of LTCaP aiming at the
modulation of characteristics such as parti-
cle size, surface area, porosity, and pore
sizes. Varying (i) the powder to liquid ratio,
(ii) the particle sizes of the reagents, (iii) the
proportions of the starting powders, (iv)
the composition of the reactants, and (v)
the aqueous solution are all possible. Adding
nucleating agents (Bohner et al. 2005; Gi-
nebra et al. 2006), soluble crystals (Chow
2000; Tas 2008), or gas bubbles (del Real
et al. 2003) to the setting reaction are addi-
tional approaches. As part of the premise of
this work, it was anticipated that machine-
prepared LTCaPs would yield high bone
volumes but, with time, be remodelled and
allow for the complete regeneration of the
marrow tissue. In the current study, we used
a novel, machine-based preparation method
for the production of particulate LTCaP
because they exhibited: (i) a less variable,
and increased, HA conversion and (ii) a
more stable, and decreased, in vitro dissolu-
tion at pH 7.4 than their hand-made coun-
terparts (Araujo 2008).
Conclusion
The LTCP used invoked an increased early
bone formation and improved degradation
rate compared with three currently avail-
able commercial bone substitute materials.
Therefore, LTCP represents an easy and
reproducible means of producing effective
implantable calcium phosphates for bone
regeneration.
Acknowledgements: The authors
would like to acknowledge the Canada
Foundation for Innovation (CFI) and
the Ontario Research and Development
Fig. 6. Particle volumes for low-temperature calcium phosphate particulate (LTCP), anorganic bovine bone
(AB), and bioactive glass (BG). At all intervals, significantly smaller volumes were found for LTCP compared
with AB and BG. AB and BG showed little sign of degradation while LTCP was completely degraded by 16
weeks.
Fig. 7. Demineralized bone matrix area measurements. Increased values and a decreased degradation rate of the
material were found. As demineralized bone matrix (DBM) is not radio-opaque, these area measurements were
derived from histological sections, as explained in the text.
Araujo et al �Low-temperature particulate calcium phosphates
c� 2010 John Wiley & Sons A/S 639 | Clin. Oral Impl. Res. 21, 2010 / 632–641
Challenge Fund (ORDCF) for financial
support, together with an unrestricted
grant-in-aid of research from Biomet 3i,
who also kindly provided the
commercially available biomaterials
used in our experiments. M.V.F.A. was a
recipient of a University of Toronto
Scholarship. We are also grateful for
the technical assistance of Susan Carter
(animal care), Limin Guan (materials
processing), and Charles Victor
(statistical analysis).
References
Abramoff, M.D., Magelhaes, P.J. & Ram, S.J. (2004)
Image Processing with ImageJ. Biophotonics In-
ternational 11: 36–42.
Ambard, A.J. & Mueninghoff, L. (2006) Calcium
phosphate cement: review of mechanical and
biological properties. Journal of Prosthodontics
15: 321–328.
Apelt, D., Theiss, F., El-Warrak, A.O., Zlinszky, K.,
Bettschart-Wolfisberger, R., Bohner, M., Matter,
S., Auer, J.A. & von Rechenberg, B. (2004) In vivo
behavior of three different injectable hydraulic
calcium phosphate cements. Biomaterials 25:
1439–1451.
Araujo, M.G., Carmagnola, D., Berglundh, T., Thi-
lander, B. & Lindhe, J. (2001) Orthodontic move-
ment in bone defects augmented with BioOsss
.
An experimental study in dogs. Journal of Clin-
ical Periodontology 28: 73–80.
Araujo, M.V.F. (2008) Calcium phosphate cements
loaded with Pantoprazole as novel bone substitutes.
MSc Thesis, University of Toronto, Toronto.
Barret, E.P., Joyner, L.G. & Halenda, P.P. (1951)
The determination of pore volume and area dis-
tributions in porous substances. I. Computations
from nitrogen isotherms. Journal of the American
Chemical Society 73: 373–380.
Bohner, M., Gbureck, U. & Barralet, J.E. (2005)
Technological issues for the development of more
efficient calcium phosphate bone cements: a cri-
tical assessment. Biomaterials 26: 6423–6429.
Bohner, M., Lemaitre, J., Merkle, H.P. & Gander, B.
(2000) Control of gentamicin release from a calcium
phosphate cement by admixed poly(acrylic acid).
Journal of Pharmaceutical Sciences 89: 1262–1270.
Brown, W.E. & Chow, L.C. (1986) A new calcium
phosphate, water-setting cement. In: Brown, P.W.,
ed. Cements Research Progress, 352–379. Wester-
ville, OH: American Ceramic Society.
Brunauer, S., Emmett, P.H. & Teller, E. (1938)
Adsorption of gases in multimolecular layers.
Journal of the American Chemical Society 60:
309–319.
Chow, I.C. (2000) Calcium phosphate cements:
chemistry, properties, and applications. Materials
Research Society Symposium Proceedings 599:
27–37.
Cordioli, G., Mazzocco, C., Schepers, E., Brugnolo,
E. & Majzoub, Z. (2001) Maxillary sinus floor
augmentation using bioactive glass granules and
autogenous bone with simultaneous implant pla-
cement. Clinical and histological findings. Clin-
ical Oral Implants Research 12: 270–278.
Costantino, P.D., Friedman, C.D., Jones, K., Chow,
L.C. & Sisson, G.A. (1992) Experimental hydro-
xyapatite cement cranioplasty. Plastic and Recon-
structive Surgery 90: 174–185.
Davies, J.E. (1998) Mechanisms of endosseous in-
tegration. International Journal of Prosthodontics
11: 391–401.
Davies, J.E. & Hosseini, M.M. (2000) Histody-
namics of endosseous wound healing. In: Davies,
J.E., ed Bone Engineering, 1–13. Toronto: em2.
del Real, R.P., Ooms, E., Wolke, J.G., Vallet-Regi,
M. & Jansen, J.A. (2003) In vivo bone response to
porous calcium phosphate cement. Journal of
Biomedical Materials Research Part A 65: 30–36.
Farina, C. & Gagliardi, S. (1999) Selective inhibitors
of the osteoclast vacuolar proton ATPase as novel
bone antiresorptive agents. Drug Discovery Today
4: 163–172.
Friedman, C.D., Costantino, P.D., Jones, K., Chow,
L.C., Pelzer, H.J. & Sisson, G.A (1991) Hydro-
xyapatite cement II: obliteration and reconstruc-
tion of the cat frontal sinus. Archives of
Otolaryngology: Head and Neck Surgery 117:
385–389.
Fukase, Y., Eanes, E.D., Takagi, S., Chow, L.C. &
Brown, W.E. (1990) Setting reactions and
compressive strengths of calcium phosphate
cements. Journal of Dental Research 69:
1852–1856.
Gautier, H., Daculsi, G. & Merle, C. (2001) Asso-
ciation of vancomycin and calcium phosphate by
dynamic compaction: in vitro characterization
and microbiological activity. Biomaterials 22:
2481–2487.
Ginebra, M.P., Traykova, T. & Planell, J.A. (2006)
Calcium phosphate cements as bone drug delivery
systems: a review. Journal of Controlled Release
113: 102–110.
Gregg, S.J. & Sing, K.S.W. (1982) Adsorption, Sur-
face Area, and Porosity. 2nd edition. London:
Academic Press.
Haas, R., Haidvogl, D., Donath, K. & Watzek, G.
(2002) Freeze-dried homogeneous and heteroge-
neous bone for sinus augmentation in sheep. Part
I: histological findings. Clinical Oral Implants
Research 13: 396–404.
Hamanishi, C., Kitamoto, K., Ohura, K., Tanaka, S.
& Doi, Y. (1996) Self-setting, bioactive, and
biodegradable TTCP–DCPD apatite cement. Jour-
nal of Biomedical Materials Research 32:
383–389.
Huygh, A., Schepers, E.J.G., Barbier, L. & Duch-
eyne, P. (2002) Microchemical transformation of
bioactive glass particles of narrow size range, a
0–24 months study. Journal of Materials Science:
Materials in Medicine 13: 315–320.
Kohri, M., Miki, K., Waite, D.E., Nakajima, H. &
Okabe, T. (1993) In vitro stability of biphasic
calcium phosphate ceramics. Biomaterials 14:
299–304.
Lai, W. (2000) Bioactive glass degradation products:
distribution and pathway removal. Ph.D. Disser-
tation, University of Pennsylvania, Philadelphia.
LeGeros, R.Z. & LeGeros, J.P. (2003) Calcium
phosphate bioceramics: past, present and future.
Key Engineering Materials 240–242: 2–10.
Liang, K.Y. & Zeger, S.L. (1986) Longitudinal data
analysis using generalized linear models. Biome-
trika 73: 13–22.
Liu, C., Shen, W., Gu, Y. & Hu, L. (1997) Mechan-
ism of the hardening process for a hydroxyapatite
cement. Journal of Biomedical Materials Re-
search 35: 75–80.
Louis-Ugbo, J., Murakami, H., Kim, H.S., Mina-
mide, A. & Boden, S.D. (2004) Evidence of
osteoinduction by Grafton demineralized bone
matrix in nonhuman primate spinal fusion. Spine
29: 360–366.
Malard, O., Bouler, J.M., Guicheux, J., Heymann,
D., Pilet, P., Coquard, C. & Daculsi, G. (1999)
Influence of biphasic calcium phosphate granulo-
metry on bone ingrowth, ceramic resorption, and
inflammatory reactions: preliminary in vitro and
in vivo study. Journal of Biomedical Materials
Research 46: 103–111.
Miyamoto, Y., Ishikawa, K., Takechi, M., Toh, T.,
Yoshida, Y., Nagayama, M., Kon, M. & Asaoka,
K. (1997) Tissue response to fast-setting calcium
phosphate cement in bone. Journal of Biomedical
Materials Research 37: 457–464.
Miyamoto, Y., Ishikawa, K., Takechi, M., Toh, T.,
Yuasa, T., Nagayama, M. & Suzuki, K. (1999)
Histological and compositional evaluations of
three types of calcium phosphate cements when
implanted in subcutaneous tissue immediately
after mixing. Journal of Biomedical Materials
Research 48: 36–42.
Muller, R., Van Campenhout, H., Van Damme, B.,
Van der Perre, G., Dequeker, J., Hildebrand, T. &
Ruegsegger, P. (1998) Morphometric analysis of
human bone biopsies: a quantitative structural
comparison of histological sections and micro-
computed tomography. Bone 23: 59–66.
Ohura, K., Bohner, M., Hardouin, P., Lemaitre, J.,
Pasquier, G. & Flautre, B. (1996) Resorption of,
and bone formation from, new beta-tricalcium
phosphate–monocalcium phosphate cements: an
in vivo study. Journal of Biomedical Materials
Research 30: 193–200.
Ooms, E.M., Wolke, J.G.C., van de Heuvel, M.T.,
Jeschke, B. & Jansen, J.A. (2003) Histological
evaluation of the bone response to calcium phos-
phate cement implanted in cortical bone. Bioma-
terials 24: 989–1000.
Peterson, B., Whang, P.G., Iglesias, R., Wang, J.C. &
Lieberman, J.R. (2004) Osteoinductivity of com-
mercially available demineralized bone matrix.
Preparations in a spine fusion model. Journal of
Bone and Joint Surgery (American Volume) 86-A:
2243–2250.
Pioletti, D.P., Takei, H., Lin, T., Van Landuyt, P.,
Ma, Q.J., Kwon, S.Y. & Sung, K.L. (2000)
The effects of calcium phosphate cement particles
on osteoblast functions. Biomaterials 21:
1103–1114.
Araujo et al �Low-temperature particulate calcium phosphates
640 | Clin. Oral Impl. Res. 21, 2010 / 632–641 c� 2010 John Wiley & Sons A/S
Rebaudi, A., Koller, B., Laib, A. & Trisi, P. (2004)
Microcomputed topographic analysis of the peri-
implant bone. International Journal of Perio-
dontics and Restorative Dentistry 24: 316–325.
Schwartz, Z., Doukarsky-Marx, T., Nasatzky, E.,
Goultschin, J., Ranly, D.M., Greenspan, D.C.,
Sela, J. & Boyan, B.D. (2008) Bone graft substi-
tutes and marrow restoration. Clinical Oral Im-
plants Research 19: 1233–1245.
Schwartz, Z., Somers, A., Mellonig, J.T., Carnes,
D.L.Jr., Dean, D.D., Cochran, D.L. & Boyan,
B.D. (1998) Ability of commercial demineralized
freeze-dried bone allograft to induce new bone
formation is dependent on donor age but not
gender. Journal of Periodontology 69: 470–478.
Shindo, M.L., Costantino, P.D., Friedman, C.D. &
Chow, L.C. (1993) Facial skeletal augmentation
using hydroxyapatite cement. Archives of Otolar-
yngology: Head and Neck Surgery 119: 185–190.
Stavropoulos, A., Kostopoulos, L., Nyengaard, J.R.
& Karting, T. (2004) Fate of bone formed by
guided tissue regeneration with or without graft-
ing of BioOsss
or BioGrans
. An experimental
study in the rat. Journal of Clinical Perio-
dontology 31: 30–39.
Tadic, D. & Epple, M. (2004) A thorough physico-
chemical characterization of 14 calcium phos-
phate-based bone substitution materials in
comparison to natural bone. Biomaterials 25:
987–994.
Takagi, S. & Chow, L.C. (2001) Formation of
macropores in calcium phosphate cement im-
plants. Journal of Materials Science: Materials
in Medicine 12: 135–139.
Tamimi, F., Torres, J., Kathan, C., Baca, R., Clem-
ente, C., Blanco, L. & Lopez-Cabarcos, E. (2008)
Bone regeneration in rabbit calvaria with novel
monetite granules. Journal of Biomedical Materi-
als Research 87A: 980–985.
Tamimi, F.M., Torres, J., Tresguerres, I., Blanco, L.J.
& Lopez-Cabarcos, E. (2007) Vertical bone aug-
mentation with granulated brushite cement set in
glycolic acid. Journal of Biomedical Materials
Research 81A: 93–102.
Tamimi, F.M., Torres, J., Tresguerres, I., Clemente, C.,
Lopez-Cabarcos, E. & Blanco, L.J. (2006) Bone
augmentation in rabbit calvariae: comparative study
between BioOsss
and a novel b-TCP/DCPD granu-
late. Journal of Clinical Periodontology 33:
922–928.
Tas, A.C. (2008) Preparation of porous apatite gran-
ules from calcium phosphate cement. Journal of
Materials Science: Materials in Medicine 19:
2231–2239.
Yildirim, M., Spiekermann, H., Biesterfeld, S. &
Edelhoff, D. (2000) Maxillary sinus augmentation
using xenogenic bone substitute material
BioOsss
in combination with venous blood. A
histologic and histomorphometric study in hu-
mans. Clinical Oral Implants Research 11:
217–229.
Zhang, Y., Xu, H.H., Takagi, S. & Chow, L.C.
(2006) In-situ hardening hydroxyapatite-based
scaffold for bone repair. Journal of Materials
Science: Materials in Medicine 17: 437–445.
Araujo et al �Low-temperature particulate calcium phosphates
c� 2010 John Wiley & Sons A/S 641 | Clin. Oral Impl. Res. 21, 2010 / 632–641