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High-strength boehmite-acrylate composites for 3D
printing: reinforced filler-matrix interactions
Yanyang Han,a FuKe Wang,b Haimei Wang ,a Xiuling Jiao a,* and
Dairong Chena,*
aSchool of Chemistry & Chemical Engineering, Shandong University, Jinan 250100, P. R. China. Email:
[email protected]; [email protected]
bPolymeric Materials Department, Institute of Materials Research and Engineering, Agency for Science,
Technology and Research (A*STAR), 2 Fusionopolis Way, #08-03 Innovis, Singapore 138634.
Experimental section
1. Materials. Aluminum nitrate nonahydrate and ammonia (25%) were
purchased from Sinopharm Chemical Reagent, 1,6-hexanediol diacrylate (HDDA,
90%) and poly(ethylene glycol) diacrylate (PEGDA, average Mn=600), Bisphenol
A glycerolate dimethacrylate(Bis-GMA), triethylene glycol dimethacrylate
(TEGDMA), 3-trimethoxysilylpropyl methacrylate (TMSPM) and β-carboxyethyl
acrylate (β-CEA) were purchased from Aladdin, and photoinitiator phenylbis
(2,4,6-trimethylbenzoyl)-phosphine oxide (97%) was purchased from Sigma-
aldrich. All materials were used as received without further purification.
2. Synthesis of boehmite nanowires. AlOOH nanowires were synthesized by
a hydrothermal process as reported with minor modification [45]. Typically, 15 g
of Al(NO)3·9H2O was dissolved in 30 mL of deionized water under vigorously
stirring to form a transparent solution. Then, ammonium hydroxide (25%) was
dropwise added to the solution until the pH of the reaction mixture was 4. The
lacteous precipitates were collected by centrifugation and redispersed in 30 mL
of deionized water. The resulting mixture was transferred into a 40 mL Teflon-
lined autoclave, which was then sealed and kept in an oven at 160 C. After 48h,
the autoclave was air-cooled to room temperature. The resultant product was
centrifuged and washed with deionized water. The final product was freeze-dried
for 10 h.
3. Surface modification of boehmite nanowires. To improve the dispersity
of boehmite nanowires in acrylates, the as-prepared boehmite nanowires were
functionalized by two strategies. β-carboxyethyl acrylate (β-CEA) was employed
as a linker between boehmite nanowires and polymer matrix. Typically, 0.3 g
boehmite nanowires were refluxed with 50 mL ethanol containing 1.44 g β-CEA
for 16 h. The final product was washed with copious amounts of ethanol and
water and then freeze-dried. Meanwhile, 3-Trimethoxysilylpropyl methacrylate
(TMSPM) modification was realized using similar strategies to those carried out
on silica surfaces. The boehmite nanowires (0.3 g) were added to the TMSPM
solution consisting of 1 mL TMSPM, 50 mL ethanol, and 9 mL DI water and
sonicated to get homogeneous solution. The solution was then refluxed for 16 h.
After the surface functionalization step, the solution became viscous and was
rinsed with copious amounts of ethanol and water and then freeze-dried.
4. Photopolymerization of boehmite-acrylate composites. The
appropriate amount of powders of neat, TMSPM and β-CEA modified AlOOH were
incorporated in acrylate resins by sonication. For UV curing, 1 wt% of
photoinitiator (PI) bis-(2,4,6-trimethylbenzoyl) phenylphosphine oxide was
dissolved in the resins by stirring in dark at room temperature overnight. The as-
obtained resins were cured by UV irradiation (irradiation intensity: 150 mW/cm -2)
and then thermal cured for further characterization.
5. 3D printing. The resins with boehmite nanowires and acrylates were
injected to the tray of 3D printer (Sprintray StarRAY, SP-DD230, LED light source,
405 nm). The geometry was designed and sliced by the software, and printing
procedure was accomplished layer-by-layer (slice thickness: 0.05 mm, exposure
time: 10 s). Post-UV curing was also conducted on the printed objects.
6. Characterization. The morphology of the as-prepared boehmite nanowires
was characterized by transmission electron microscopy (TEM, JEOL JEM-1011,
accelerating voltage: 100 kV). The X-ray diffraction (XRD) patterns of the
powder samples were collected on a Rigaku D/MAX 2200PC diffractometer with
a graphite monochromator and CuKα (λ=0.15418 nm) radiation. The infrared
spectra were examined on a Brüker ALPHA-T Fourier Transform Infrared (FT-IR)
spectrometer using the KBr pellet technique. Cross-sectional characterization of
the resins after fracture was accomplished by scanning electron microscopy
(SEM, HITACHI, SU8010). Thermalgravimetric analysis (TGA) was carried out on
a Netzsch STA449F3 Jupiter thermal gravimetric analyzer at a heating rate of
10.0 C/min under air atmosphere. Elemental analysis was conducted on Vario
EL CUBE (Elementar) to determine the carbon content in modified AlOOH
nanowires. Rheological properties of neat and composite acrylate resins were
characterized on a rheometer (Anton Paar MCR 302), shear rate: 0.01~100 s-1.
7. Mechanical testing. Three-point bending flexural tests were conducted on
standard specimen (L=50.8 mm, W=12.7 mm, ASTM D790) with Universal
Testing Machine HZ-1004A (Lixian Instrument), results were average of at least
five specimens.
Fig. S1. Characterization of boehmite nanowires: (a-b), TEM and SEM images of the boehmite
nanowires prepared by hydrothermal reaction; (c), XRD pattern of freeze-dried boehmite powder.
Fig. S2. Structural illustration of the as-involved reagents: photoreactive monomer (HDDA) and
modifiers (TMSPM and β-CEA). TMSPM was commonly used as coupling agents for the affinity of
its siloxy groups to nanoparticles and lipophilicity of its alkyl groups; while β-CEA was first
employed as surface modifier in this report. TMSPM was expected to undergo siloxy hydrolysis to
connect boehmite nanowires and acrylate matrix. However, the weak acid surface of boehmite
nanowires may lead to fast hydrolysis reaction and condensation of TMSPM, which resulted in
decrease of surface modification effects. And this was why we claimed that TMSPM was not
coupling agent for all purpose.
Fig. S3. Schematic illustration of grafting of β-CEA onto the surface of boehmite nanowires and co-
crosslink of β-CEA-AlOOH with acrylate matrix. The carboxyl groups of β-CEA interacted with
surface hydroxyls of boehmite nanowires to graft acrylate groups onto boehmite nanowires. And
consequently, better dispersion of boehmite nanowires and strong filler-matrix interaction were
obtained.
Thermal test.
The representative thermalgravimetric (TG) and the corresponding differential thermogravimetric
(DTG) curves were shown in Fig. S4. The peak of DTG curve illustrates the highest mass loss of
sample at corresponding temperature, in other words, decomposition of the sample. Accordingly, the
decomposition temperature of neat HDDA and composites with certain amount (2 wt%) of
nanofillers were obtained through DTG curves and listed in Table S1. A slight improvement of
decomposition temperature was found in both modified boehmite nanowire incorporated composites.
As aforementioned, the filler content in the tested samples was 2 wt%, thus, it was inferred that such
small incorporation amount would induce limited extent of improvement in thermal stability of
composites.
Fig. S4. TGA curves (a) and the corresponding DTG curves (b) of neat HDDA and HDDA composite
resins with neat and modified boehmite nanowires. Note that the amount of boehmite nanowires in
composite resins was 2 wt%.
Tab. S1. Peak temperature of neat HDDA and composite resinsa obtained from DTG curves.
Sample Tpeak/C
Neat HDDA 427
HDDA+neat AlOOH 426
HDDA+TMSPM-AlOOH 433
HDDA+β-CEA-AlOOH 437aNote that the mass content of boehmite nanowires in composites was kept at 2%.
Fig. S5. Rheological characterization of neat HDDA resin and composite resins with neat and
modified AlOOH nanowires.
Fig. S6. Dispersion stability of HDDA resins with β-CEA-AlOOH (labeled as β) and neat AlOOH
(labeled as N): a, after sonication; b, 4 h after sonication; c, 24 h after sonication. The amount of neat
and β-CEA modified boehmite nanowires were 2 wt% for both resins.
Fig. S7. Illustration of printing performance: (a) HDDA resin with β-CEA modified boehmite
nanowires (4 wt%) and (b) neat HDDA resin. The dimensions of printed Fullerene model was 5 cm*5 cm*4.7 cm. The exquisite and delicate structure of Fullerene made it difficult to
manufacture by traditional processes. The successful fabrication of Fullerene model confirmed the
excellent performance in DLP-based 3D printing.
Tab. S1 Relative peak intensity calculated from FTIR spectra.
Sample Relative peak intensity
1070 cm-1 3290 cm-1
Neat AlOOH 0.75 0.75
β-CEA-AlOOH 0.74 0.65
TMSPM-AlOOH 0.82 0.76
Fig. S8. The acidity of AlOOH-H2O dispersion.