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Study on the reaction mechanism of (αααα-Al2O3+TiB2+TiC)/Al composites
fabricated by Al-TiO2-B4C system
Heguo Zhua, Jin Minb, Da Chuc and Huan Wangd
College of Materials Science and Engineering of Nanjing University of Science and Technology,
Nanjing, 210094, China
[email protected],[email protected],[email protected], [email protected]
Keywords: Exothermic Dispersion Synthesis, Thermal Analysis, Composites, Reaction Mechanism
Abstract The composites (α-Al2O3+TiB2+TiC)/Al has been fabricated by using exothermic
dispersion synthesis. Thermodynamic analysis indicated that the reaction between the Al and TiO2
can spontaneously occur due to the negative Gibbs free energy of the Al-TiO2 reaction system. With
the increase of B4C/TiO2 mole ratios, the exothermic peaks increase move to the higher temperature
and the corresponding ignite temperatures also increase. The reaction results indicate that when the
B4C/TiO2=0, the reinforcements are composed of α-Al2O3, Al3Ti, with the increase of B4C/TiO2,
the amount of Al3Ti decreases and the TiC and TiB2 form simultaneously. When the B4C/TiO2
increases to 1/3, the Al3Ti almost disappear and the reinforcements of the composites are consisted
of α-Al2O3, TiC and TiB2.
Introduction
In-situ aluminum matrix composites have many excellent advantages such as clean particle-matrix
interface, fine and thermodynamically stable reinforcements, good compatibility and high bonding
strength between the reinforcements and the matrix and low fabrication costs [1-3]. So they have
been widely used in air navigation and automobile industries. The Al-TiO2 is a very interesting
system for fabricating the aluminum matrix composites [4]. But the reacted product Al3Ti is a bad
phase to increase the properties of the composites. So, the substances such as B, B2O3 and C are
added into the system [5-7]. As we known that the TiB2 and TiC all are good reinforcements of the
aluminum matrix composites [8-10]. In order to attain the good reinforcements TiB2 and TiC, the
B4C phase has been added into the Al-TiO2 system. In the present paper, we focus on investigating
the reaction mechanism of the Al-TiO2-B4C system by using DSC(difference scanning calorimetric),
SEM(scanning electronic microscope), and XRD(X-ray diffraction) methods. The reaction results
will also be helpful to understand the reaction mechanisms.
Experimental procedure
The B4C(99% purity), TiO2 powders (99% purity), and Al powders (99.0% purity) with average
sizes of 20~30µm, 50~100µm and 20~30µm, respectively, were used as raw materials. According
to stoichiometric calculations, the four samples were prepared. The samples 1, 2 and 3 had the same
reinforcement volume fraction of 30% and different mole ratios of B4C/TiO2 of 0, 1/6 and 1/3,
respectively. The mixed powders were bal1-milled in a stainless steel vacuum jar for 2h, and then
cold compacted into green billets with a diameter of 20mm by a pressure of 120MPa. The compacts
Advanced Materials Research Vols. 150-151 (2011) pp 84-87Online available since 2010/Oct/27 at www.scientific.net© (2011) Trans Tech Publications, Switzerlanddoi:10.4028/www.scientific.net/AMR.150-151.84
All rights reserved. No part of contents of this paper may be reproduced or transmitted in any form or by any means without the written permission of TTP,www.ttp.net. (ID: 128.252.67.66, Washington University in St. Louis, St. Louis, United States of America-13/03/13,13:40:58)
were heated in a vacuum furnace to a temperature to allow the combustion reactions to occur, then
held for about 10 min and subsequently cooled down to room temperature in the furnace. The
samples made from the reacted compacts were mechanically polished and then were investigated by
using methods of XRD and SEM. Some of the mixed powders were cold compacted into a slice
with the thickness of about 0.5mm by a pressure of 120MPa. A tiny block with the weight of
5~10mg cut from the slice was put into STA449C thermal analyzer to test the DSC curves at
heating rate of 20 /min.
Results and Discussion
According to the thermodynamics analysis as done in the literature [4], the possible reaction in the
Al-TiO2 system can be described as follows:
TiAl3OAl2TiO313Al 3322 +−→+ α (1)
And the reaction process between Al and TiO2 consists of two step reactions as follows:
Ti][3OAlTiO32Al 322 +−→+ α TGT 5.275350380+−=∆ (2)
3[Ti] 3Al Al Ti+ → 0 144242 21T TG = − +∆ (3)
The Al firstly reacts with TiO2 to form the stable α-Al2O3 particles and active Ti atoms; and then
the active Ti atoms react with Al to form the Al3Ti. When B4C powders are added into Al-TiO2
system, the B4C can not react with the Al as proved in Fig.1. From Fig.1, we can see that only an
endothermic peak in the DSC curve during the heating process from room temperature to 1100 ,
obviously, it is corresponded to the melt process of the aluminum matrix. So, there is no reaction
occurred between the Al and B4C. Fig.2 shows the DSC curves of the B4C-TiO2 system and single
phase B4C and TiO2, respectively. it is evident that the DSC curve of the B4C-TiO2 system is the
simple superposition of the B4C and TiO2. It is further proved that the B4C can not react with TiO2.
In the Al-TiO2-B4C system, Al first reacts with TiO2 to form the active Ti atoms and α-Al2O3
ceramic particles, and then, the active Ti atoms leave the reacted area and diffuse into the matrix,
they can react with B4C or aluminum. All the possible reactions can be described as equation 3 and
following equation:
24 2TiBTiCCB3[Ti] +→+ TGT
78.377602340+−=∆ (4)
Fig.1 DSC curve of the Al-B4C
system at heating rate of 20 /min
Fig.2 DSC curves of the TiO2-B4C system and TiO2,
B4C, respectively, at heating rate of 20 /min
Advanced Materials Research Vols. 150-151 85
On the base of the standard Gibbs free energy variations changed with temperature of the equation
(3) and equation (4), it is concluded that the reaction (4) will happen previous to the reaction (3).
Certainly, when the content of the B4C is not enough to make all active Ti atoms consume over, the
active Ti atoms will react with the aluminum matrix to form the Al3Ti. Fig.3 shows the DSC curves
of the composites with different mole ratios of B4C/TiO2 at heating rate of 20 /min under argon
protective atmosphere, respectively. Form Fig.3, we can see that with the increase of the mole ratios
of B4C/TiO2, the slops of the exothermic peaks increase, so the reaction velocity and the initiation
temperature of the reactions increase obviously. The reason of this may be that the diffuse distance
of the Ti atoms decrease and the collection degree of the reaction promoted and released reaction
heat with the increase of the B4C content. So, the whole reactions of the Al-TiO2-B4C system will
change with the mole ratio of the B4C/TiO2 and they can be described as following equations:
rB4C/TiO2=1/6: 2 4 2 3 2 323 6 2 5 4Al TiO B C TiC TiB Al Ti Al Oα+ + → + + + − (5)
rB4C/TiO2=1/3: 2 4 2 2 34 3 2 2Al TiO B C TiC TiB Al Oα+ + → + + − (6)
(a),(d) rB4C/TiO2=0 (b), (e) rB4C/TiO2=1/6 (c), (f) rB4C/TiO2=1/3
Fig.4 SEM images and their respective XRD patterns of the composites varied with different molar
ratios of the B4C/ZrO2. (a), (d) rB4C/TiO2=0; (b), (e) rB4C/TiO2=1/6; (c), (f) rB4C/TiO2=1/3
Fig.3 DSC curves with different mole ratios of B4C/TiO2:1-rB4C/TiO2=0; 2-rB4C/TiO2=1/6; 3-rB4C/TiO2=1/3
86 Advances in Composites
Fig.4 shows the SEM micrographs and XRD patterns of the composites with different molar
ratios of B4C/TiO2 and with the reinforcement volume fraction of 30%. When the B4C/TiO2 mole
ratio is 0, the reaction products are composed of rod-like phase, fine particles and the matrix as
shown in Fig.4 (a). Its corresponded XRD patterns as shown in Fig.4 (d) proves that compounded
phases of the composites are Al, Al3Ti and α-Al2O3. The EDS patterns confirm that the block-like
phase is Al3Ti [4], so, the particle phase is α-Al2O3. As the B4C/TiO2 mole ratio increases to 1/6, the
amount of the rod-like phase Al3Ti decreases as shown in Fig. 4 (b). Its corresponded XRD patterns
as shown in Fig. 4 (e) indicates that there are new phases TiC and TiB2 occurred in the final
products except for the former phases of the Al, Al3Ti and α-Al2O3, which is accordance with the
thermodynamic analysis in the section 3.1. When the B4C/TiO2 mole ratio is 1/3, the rod-like phase
Al3Ti almost disappears as shown in Fig. 4 (c). Its corresponded XRD pattern shows that the
reaction products are Al, α-Al2O3, TiC and TiB2 as shown in Fig. 4 (f). From the Fig. 4 (c), we can
see that the distribution of the reinforcements improves greatly. Therefore, the results of the
combustion reactions are compatible with the conclusions of the above thermodynamic analysis.
Conclusions
1. In the Al-TiO2-B4C reaction system, when the B4C/TiO2 mole ratio is 0, the Al first reacts with
TiO2 to form the α-Al2O3 and Al3Ti. With increasing the B4C/TiO2 mole ratios, the amount of rod
Al3Ti decreases gradually. When the B4C/TiO2 mole ratio reaches 1/3, the Al3Ti rods almost
disappear and the reinforcements of the composites are consisted of α-Al2O3, TiC and TiB2.
2. DSC curves indicates that the B4C can not react with TiO2 and that with the increase of the mole
ratios of B4C/TiO2, the reaction velocity and the ignite temperature of the reactions increase
obviously.
Acknowledgments
This work was supported by grant No.BK2006207 from the Natural Science Foundation of Jiangsu
Province.
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Advanced Materials Research Vols. 150-151 87
Advances in Composites 10.4028/www.scientific.net/AMR.150-151 Study on the Reaction Mechanism of (α-Al2O3+TiB2+TiC)/Al Composites Fabricated by Al-TiO2-B4C
System 10.4028/www.scientific.net/AMR.150-151.84
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