Fabrication of TiB₂/Al composite by melt-SHS process with different content of titanium powder

Abstract

Melt-SHS (self-propagating high-temperature synthesis), based on the SHS process and oxide reaction method, was used for preparation of TiB₂/Al composites. The mass ratio of two reactants, Ti powder/TiO₂, in initial powder mixture was varied from 0:1 to 1:0. The results showed that the 5 wt% TiB₂/Al composites could be successfully produced by a reaction of aluminum powder, TiO₂, and B₂O₃ in Al melt at 950 °C, while the reaction rate was slow. The addition of titanium powder helps to reduce the content of Al₂O₃ and destroy the coating structure of Al₂O₃ covered TiB₂ particles, which leads to the acceleration of reaction process and improvement of particle concentration. A significant improvement was that TiB₂ particles were dispersively distributed when the mass ratio of Ti powder/TiO₂ was 2:3. As a result, the 5 wt% TiB₂/Al composites fabricated by melt-SHS process with modified reactants ratio showed excellent tensile properties with the ultimate tensile strength as high as 114.24 MPa. Besides, the composite also showed superior ductility.

I. INTRODUCTION

Insitu particulate reinforced aluminum matrix composites (Al MMCs) are widely used in the aerospace and automotive industries due to their excellent properties, such as high specific strength, low weight, and chemical inertness.1 It consists of matrix and the reinforcement, and the reinforcement is one of the most important parts. TiB₂ particles reinforced Al MMCs is one of the most widely used particulate reinforced Al MMCs because of its outstanding properties, such as low density, high melting point, high elastic modulus, and good lattice matching relations with the aluminum matrix.2

It has been reported in many studies that TiB₂ particles can be synthesized by in situ synthesis method, and the process offers significant advantages over the conventional processing from both technical and economic standpoints,2,3 such as its excellent interfacial compatibility between matrices and reinforcements, thermodynamically stable, and distribution uniformity of the reinforcements in the matrix.

In situ TiB₂ particles reinforced aluminum matrix composites can be synthesized by the salt-metal reaction, self-propagating high-temperature synthesis (SHS), hot pressing, pressureless sintering, and mechanochemical synthesis.3,4 The salt-metal reaction is the most commonly used in situ methods.5 In this processing, the mixed K₂TiF₆ and KBF₄ were used as reactants, which reacted with molten Al at a high temperature to form TiB₂ particles in the Al matrix.6 However, the method has fluoride emissions and the dross needs to be disposed. As one of the fabrication techniques to synthesize in situ ceramic particulate reinforced MMCs, SHS technology has received much attention because of its low energy consumption and high product purity. Nevertheless, the price of the reactants is expensive, and procedure is complicated and time consuming because the final products are porous and need to combine with a densification step; the react temperature cannot be controlled easily as well. To decrease the cost of reactants, Al–TiO₂–B,7 TiO₂–B₄C–C,8 Al–Ti–B,9,10 Al–TiO₂–B₂O₃–Na₃AlF₆,11 and Al–TiO₂–B₂O₃12 systems were studied to fabricate TiB₂ particles reinforced aluminum matrix composites. Due to the high price of the elemental powder, the oxide and compounds of titanium and boron were popular as reactants in the new system. However, another main product, Al₂O₃, needs to be cleared, and this undoubtedly leads the amount of reactants and reaction process to be more difficult to control.

In this study, a modified method melt-SHS process which combined the advantages of low price of oxide reactant and SHS process was used to synthesize Al/TiB₂ composites. Furthermore, the melt-SHS method is environmentally friendly due to the clean products. The reactants, H₃BO₃, TiO₂, Al powder, and Ti powder, were used in the process since Ti powder could be used as a reductant and a combustion promoter. To confirm the optimum reactant ratio and produce the low-cost and efficient composites, the different ratios of H₃BO₃, TiO₂, and Ti powder were applied.

II. EXPERIMENTAL PROCEDURE

A. Raw materials

High purity aluminum (>99.9 wt%) was used as the base metal. Two kinds of chemical powders, namely TiO₂ (200 mesh) and H₃BO₃ (200 mesh), and two types of metal powders, namely Al powder (300 mesh) and Ti powder (300 mesh), were used to synthesize the TiB₂ particles.

B. Processing

With the atomic ratio Ti/4B, TiO₂ and H₃BO₃ were first dried at 200 °C for 2 h, and then a percentage of aluminum and titanium powder were added in the mixed powder and mechanical stirred homogeneously. The final mixed powder was pressed into a cylinder (φ62.5 × 12 mm³) to make a powder block. After that, Al ingot was melted in a graphite crucible resistance furnace as the temperature reached 950 °C, which was measured by a thermocouple, then the prepared powder block was pressed into the melt. Melt-SHS reaction between the powder cylinder and the molten Al to form TiB₂ particles. The whole preparation process is shown in Fig. 1, and the synthesis process is in the air. Two times were marked: one is the response time t₁ which is the time from the cylinder touched aluminum melt to the emergence of the spark. The other is the reaction time denoted as t₂, which indicates the time from the emergence of the spark until the spark went out. After the reaction, the melt was mechanically stirred for 10 min, the reaction holding time was set as 30 min at 800 °C, and finally the melt was poured into a steel mold (φ95 × 150 mm³) at 720 °C. Then the TiB₂/Al composite billets were extruded into bar composites with an extrusion ratio of 25:1 at about 400 °C. The four composites correspond to the four quality ratio of Ti powder/TiO₂ in the initial powder mixture which varied from 0:1 to 1:0 (showed in Table I).

FIG. 1

The whole preparation process.

TABLE I Particulate material additions for the production of 5 wt% TiB2/Al composites.

The mechanical properties were evaluated by the tensile test, which was carried out on a computerized universal testing machine at a velocity of 0.05 mm/s. Three tests were conducted for each composite to get a precise value for each property.

C. Characterization

The metallographic specimens were intercepted from each bottom of the samples. X-ray diffraction (D8 ADVANCE, Bruker, Karlsruhe, Germany) was used to analyse the diffraction phases in the composite. Scanning electron microscopy (QUANTA200, FEI Company, Hillsboro, Oregon) equipped with an energy-dispersive X-ray spectroscopy (EDS) was used to observe the morphology and distribution of particles in the composites. Besides, the software Image-Pro plus 6 (Media Cybernetics, Rockville, Maryland) was used to statistically analyze the particle size distribution.

III. RESULTS AND DISCUSSION

A. Thermodynamic analysis

Before the preparation of powder block, TiO₂ and H₃BO₃ mixture was dried to remove the water in boric acid. It was easier to produce crystalline lumps since boric acid was dried separately. The reaction of the dehydration process can be written as function (1),

$$2{{\rm{H}}_3}{\rm{B}}{{\rm{O}}_3}({\rm{s}}) \to 3{{\rm{H}}_2}{\rm{O}}({\rm{g}}) + {{\rm{B}}_2}{{\rm{O}}_3}({\rm{s}})\quad .$$

(1)

The formation of ceramic particles via melt-SHS process is a thermodynamically chemical reaction. The possible reaction basically has the following several parts: (i) at a predetermined temperature, Al powder produces sparks as an igniter composition, and the combustion wave diffuses along the powder cylinder. (ii) The aluminothermy reduction of B₂O₃ and TiO₂ at the molten flux-liquid metal interface forms B, Ti atoms, and Al₂O₃, which can be written as Eqs. (2) and (3). (iii) The formation of Al₃Ti, AlB₂, and TiB₂ by combination reaction of B, Ti, and Al. The reactions are shown in Eqs. (4), (5), and (7). (iv) The boron atoms react with Al₃Ti and generate TiB₂. The last part reaction is exhibited as Eq. (6),

$${{\rm{B}}_2}{{\rm{O}}_3}\left( {\rm{s}} \right) + 2{\rm{Al}}\left( {\rm{l}} \right) \to 2\left[ {\rm{B}} \right] + {\rm{A}}{{\rm{l}}_2}{{\rm{O}}_3}\left( {\rm{s}} \right)\quad ,$$

(2)

$$3{\rm{Ti}}{{\rm{O}}_2}\left( {\rm{s}} \right) + 4{\rm{Al}}\left( {\rm{l}} \right) \to 3\left[ {{\rm{Ti}}} \right] + 2{\rm{A}}{{\rm{l}}_2}{{\rm{O}}_3}\left( {\rm{s}} \right)\quad ,$$

(3)

$$3{\rm{Al}}\left( {\rm{l}} \right) + \left[ {{\rm{Ti}}} \right] \to {\rm{A}}{{\rm{l}}_3}{\rm{Ti}}({\rm{in}}\;{\rm{alloy}})\quad ,$$

(4)

$${\rm{Al}}\left( {\rm{l}} \right) + 2\left[ {\rm{B}} \right] \to {\rm{Al}}{{\rm{B}}_2}({\rm{in}}\;{\rm{alloy}})\quad ,$$

(5)

$${\rm{A}}{{\rm{l}}_3}{\rm{Ti}}({\rm{in}}\;{\rm{alloy}}) + 2\left[ {\rm{B}} \right] \to 3\left[ {{\rm{Al}}} \right] + {\rm{Ti}}{{\rm{B}}_2}({\rm{in}}\;{\rm{alloy}})\quad ,$$

(6)

$$\left[ {{\rm{Ti}}} \right] + 2\left[ {\rm{B}} \right] \to {\rm{Ti}}{{\rm{B}}_2}({\rm{in}}\;{\rm{alloy}})\quad .$$

(7)

The temperature dependence of the reaction enthalpy (ΔH_T) and free energy (ΔG_T) changes for these six reactions are summarized in Fig. 2. The results indicate that the values of ΔH_T and ΔG_T in all functions are negative, and further illustrate that the reactions are exothermic reactions and can proceed spontaneously. The lower the ΔG_T is, the higher possibility the reaction goes. It is easy to observe that Eq. (7) has the greatest possibility over other functions in the parts (iii) and (iv), and TiB₂ particle is the most stable phase. A notable finding is that the TiB₂ is the main product, and TiAl₃ and AlB₂ are much less competitive due to the higher ΔG_T.

FIG. 2

Relationship between the temperature and the reaction enthalpy (ΔH_T) and free energy (ΔG_T) change for these six reactions.

The SHS reaction maintains by the heat released in the process of the reaction. It is necessary to analyse the thermodynamics which enables a SHS reaction to proceed successfully. For the SHS reaction, an experience criterion was put forward; when T_ad ≥ 1527 °C, the SHS reaction sustains itself, otherwise needs supplement system energy.13 The adiabatic temperature can be calculated according to the materials formed in the process of reaction and enthalpy of phase changes. The overall reaction showing the formation of TiB₂ can be written as

$$10{\rm{Al}} + 3{\rm{Ti}}{{\rm{O}}_2} + 3{{\rm{B}}_2}{{\rm{O}}_3} = 5{\rm{A}}{{\rm{l}}_2}{{\rm{O}}_3} + 3{\rm{Ti}}{{\rm{B}}_2}\quad .$$

(8)

According to the first law of thermodynamics,

$${C_{\rm{p}}} = {{{\rm{d}}H} \over {{\rm{d}}T}}\quad .$$

The former equation at the interval of room temperature and temperature T is integrated, and the solid phase transformation and melting phenomenon of the material within the scope of the studied temperature T range are considered. Ignoring the vaporization phenomenon, the equation is as follows:

$$\eqalign{ & H_T^\Theta - H_{298}^\Theta = \int_{298}^{{T_{{\rm{tr}}}}} {{C_{{\rm{p}},{\rm{m}}}}{\rm{d}}T + \Delta {H_{{\rm{tr}}}}} + \int_{{T_{{\rm{tr}}}}}^{{T_{\rm{m}}}} {C_{{\rm{p}},{\rm{m}}}^\prime {\rm{d}}T} \cr & \,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\, + \Delta {H_{\rm{m}}} + \int_{{T_{\rm{m}}}}^T {C_{{\rm{p}},{\rm{m}}}^{\rm{d}}T} \quad , \cr} $$

$$\eqalign{ & {C_{\rm{p}}} = a + b \times {10^{ - 3}}T + c \times {10^5}{T^{ - 2}} + d \times {10^{ - 6}}{T^2} \cr & \,\,\,\,\,\,\,\,\,\, + e \times {10^8}{T^{ - 3}}\quad . \cr} $$

${C_{{\rm{p}},{\rm{m}}}},C_{{\rm{p}},{\rm{m}}}^\prime ,\>{\rm{and}}\>C_{{\rm{p}},{\rm{m}}}$ are the molar constant pressure heat capacity of substance, J/(mol K). $H_T^\Theta - H_{298}^\Theta$ is the relative material mole enthalpy, J/mol. T_tr and T_m are the phase transition temperature and melting point of material, K. ΔH_tr and ΔH_m are the solid phase transformation and melting heat of material, J/mol.

According to the Kirchhoff equation,

$${\rm{d}}\Delta H_T^\Theta = \Delta {C_{\rm{p}}}{\rm{d}}T\quad .$$

In the equation, ΔC_p is the D-value between the sum isobaric heat capacity of products and reactants, namely, the heat capacity difference,

$$\Delta {C_{\rm{p}}} = \sum {{{\left( {{n_{\rm{i}}}{C_{{\rm{p}},{\rm{i}}}}} \right)}_{{\rm{product}}}}} - \sum {{{\left( {{n_{\rm{i}}}{C_{{\rm{p}},{\rm{i}}}}} \right)}_{{\rm{reactant}}}}} \quad .$$

In the equation, n_i is the mole of reactants participate in the reaction and C_p is the molar constant pressure heat capacity.

Assuming that the reactants are involved in the reaction completely under the condition of adiabatic temperature, the release of heat will be all applied to the reaction. If the reaction proceeds at room temperature (298 K), the equation is as follows:

$$\Delta H_{298}^\Theta + \sum {{n_{\rm{i}}}{{\left( {H_T^\Theta + H_{298}^\Theta } \right)}_{{\rm{i}},{\rm{product}}}}} = 0\quad .$$

$\Delta H_{298}^\Theta$ is the heating effect of the reaction at room temperature. If the reactants are preheated at T₀,

$$\eqalign{ & \sum {{n_{\rm{i}}}} {\left( {H_{298}^\Theta + H_{{T_0}}^\Theta } \right)_{{\rm{i}},{\rm{reactant}}}} + \sum {{n_{\rm{i}}}} {\left( {H_T^\Theta + H_{298}^\Theta } \right)_{{\rm{i}},{\rm{product}}}} \cr & \,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\,\, + \Delta H_{298}^\Theta = 0\quad . \cr} $$

If the adiabatic temperature of reaction is 1527 °C, preheat temperature T₀ is easily figured out. After calculation, the T₀ is 892 °C. Considering that the experiment is under atmospheric conditions, to ensure the smooth progress of the reaction, the starting reaction temperature of 950 °C was used.

B. X-ray diffractions analysis

XRD patterns of the four composites and the reaction slag are shown in Fig. 3. The presence of TiB₂ peaks and TiAl₃ peaks in the 1#, 2#, and 3# composites [Fig. 3(a)] confirms the formation of TiB₂ and TiAl₃. The TiB₂ peaks in 4# composite are not obvious. XRD patterns of the reaction slag [Fig. 3(b)] confirm the formation of TiB₂ and Al₂O₃ in the fabrication of four composites. It can be seen that the 4# slag has more obvious peaks of TiB₂ and Al₂O₃, which means that TiB₂ particles which failed to spread to aluminum melt mainly exist in the slag. It is interesting to note that there are no obvious peaks of AlB₂ and Al₂O₃ in the spectra of the TiB₂/Al composites, while Al₂O₃ mainly exists in the reaction slag which had been cleared out of the Al melt.

FIG. 3

XRD spectra of (a) 5% TiB₂/Al composites and (b) reaction slag.

C. Microstructures of reaction slag

To make sure TiB₂ and Al₂O₃ particles exist in the reaction slag, microstructures and energy spectrum analysis of the slag are shown in Fig. 4. Combining XRD and energy spectrum analysis [Figs. 4(c) and 4(d)], accumulation area of Al₂O₃ [Fig. 4(a)] and TiB₂ [Fig. 4(b)] was found in the slag. It can be concluded that Al₂O₃ particles were taken away with the reaction slag, and there was still a percentage of TiB₂ particles that have not been able to diffuse into the Al melt. This is mainly because the Al₂O₃ particles gathered in the block after the reaction. Besides, the initial size of TiB₂ particles formatted in the block were much less than the holes in the block, which results in the smaller size TiB₂ particles diffused to the aluminum melt easily at the end of the reaction. With the increase of the reaction holding time, part of TiB₂ particles in the block grew up to a bigger size and stayed in the melt.

FIG. 4

Microstructures and energy spectrum analysis of 1# composite reaction slag: (a) accumulation area of Al₂O₃, (b) accumulation area of TiB₂, (c) energy spectrum analysis of Zone A, and (d) energy spectrum analysis of Zone B.

D. Microstructure and properties of composites

Microstructures and the particle size distribution of four composites with different mass ratios of Ti powder/TiO₂ in raw materials are showed in Fig. 5. And the mechanical properties of 5 wt% TiB₂/Al composites were shown in Table II.

FIG. 5

Microstructures and particle size distribution of four composites with different quality ratio of Ti powder/TiO₂ in raw materials: (a) 1#, (b) 2#, (c) 3#, (d) 4#, (e) EDS analysis of Zone A, and (f) particle size distribution.

TABLE II Mechanical properties of 5 wt% TiB2/Al composites.

According to XRD [Fig. 3(a)] and EDS analysis [Fig. 5(e)], it can be confirmed that the white particles are TiB₂. The morphology of TiB₂ particles in composite 1# [Fig. 5(a)] presents the hexagonal shape, and the average size is nearly 0.91 µm [Fig. 5(f)]. Compared to composite 1#, composite 2# [Fig. 5(b)], which has additional Ti powder in raw materials mixture and with a mass ratio of Ti powder/TiO₂ of 2:3, exhibits a uniform distribution of TiB₂ particles in the Al matrix, the average size is nearly 0.67 µm [Fig. 5(f)], and the contents of TiB₂ particles increased. It is seen that when Ti powder was added into the powder block, the assimilation of B increased and showed an increase in the number of the TiB₂ particles. Thus the 2# composite showed excellent tensile properties: the ultimate tensile strength (UTS) is up to 114.24 MPa, the hardness is 25.54 HB, and the elongation is 33.15% which is also a superior ductility. After the fast exothermic combustion reaction, the temperature in the combustion zone decreases sharply and the desired phases are vigorously formed in great numbers. With increasing of Ti powder mass ratio further, the contents of TiB₂ particles decrease as shown in Figs. 5(c) and 5(d), and the average size increases to 0.72 µm and 0.95 µm, respectively [Fig. 5(f)]. Besides, the distributions of TiB₂ particles were uneven when the quality ratio of Ti powder/TiO₂ was larger than 2:3 which resulted from the relatively higher adiabatic temperature induced by the addition of Ti powder. And the tensile properties were also not that good, which showed lower UTS, because high temperature led to a large amount of evaporation of aluminum melt and made the TiB₂ diffusion become more difficult. According to the data of XRD spectra and the microstructures, it was confirmed that the amount of TiAl₃ phase was too few to show in the microstructure. It may be because a long enough reaction holding time results in less available TiAl₃ in the melt, as a result of its continuing decomposition to form TiB₂.

E. In situ formation of TiB₂ particulates

The response time t₁ and the reaction time t₂ are showed in Table III.

TABLE III Composite reaction waiting time t1 and the actual reaction time t2.

After the powder block was put into an aluminum melt, the composite 1# did not spark immediately. Approximately 60 s later, the spark appeared and extinguished in 2 min. While the composites with the additions of Ti powder (the composite 2#, 3#, 4#) appeared the spark in 10 s and kept for 1 min until the reaction finished. The reactants of composite 1# are H₃BO₃ and TiO₂ which resulted in the products containing a mass of Al₂O₃. A mount of the reactants was forbidden to touch the Al melt because the powder cylinder was surrounded by the formed Al₂O₃ which could be deduced from the microstructure of the slag as shown in Figs. 6(a) and 6(b); thus, the reaction speed was reduced greatly. Majority of nanometer TiB₂ particles were trapped in the melt slag and could not spread out as shown in Fig. 6(c).

FIG. 6

Microstructure of reaction slag of 1# composite: (a) coating structure, (b) local amplification figure, and (c) nanometer TiB₂ particles in the slag.

According to the thermodynamic analysis and the microstructures, the reaction process analysis was described in Fig. 7. This reaction process used the heat released by the reaction to synthesise TiB₂/Al composites. When the mixed powder cylinder was pressed into the high temperature aluminum liquid, parts of titanium powder first ignition where the powder and liquid aluminum contact because of the flammable properties of titanium powder, and aluminum powder melted due to the low melting point. TiO₂ and B₂O₃ reacted with the molten aluminum to form free B atoms and Ti atoms. Since the Gibbs free energy of aluminum oxide is lower than that for boron oxide, chemical reactions occur at the interface between molten aluminum and boron oxide.12,14 As boron atoms go into solution in the molten aluminum, aluminum oxide covers the top of melt as slag and formed a coating structure. The reaction released heat to melt the rest of the parts of solid titanium powder, but it only occurred in a few atomic layers of the Ti particles surface, and the molten titanium reacted with the free boron to produce TiB₂ particles. According to the thermodynamic analysis, it is easy to form AlB₂ and TiAl₃ phases, respectively, when the free B and Ti atoms met the molten Al. It has been reported15,16 that the dominant bonding in TiB₂ is covalent, which leads to its great structural stability at high temperature and the dominant bonding in AlB₂ is ionic due to the large charge transfer from aluminum to boron. It means that AlB₂ phases were relatively unstable from the view of thermodynamics, and it would decompose back to Al and B atoms. The free B atoms not only combined with Ti atoms to form TiB₂ but also took part in the reduction reaction with TiAl₃ to form TiB₂. The Al₂O₃ particles were cleaned out of the Al melt with the reaction slag. It has been reported that the removal of Al₂O₃ promotes the particle wetting.17 With the Al₂O₃ out of the melt, the wetting angle between the liquid Al and TiB₂ decreased, hence also producing a good interfacial integrity. The addition of titanium powder helps to reduce the content of Al₂O₃ and destroy the coating structure of Al₂O₃ covered TiB₂ particles, which lead to the acceleration of reaction process and improvement of particle concentration. Therefore, the addition of titanium powder could reduce the generation and accumulation of Al₂O₃ and proceed the reaction.

FIG. 7

Reaction process analysis.

F. Fractograph

Figure 8 shows the fractographs of the composites fabricated by the melt-SHS with the ratio of Ti powder/TiO₂ as 2:3 (2# composite) which has the high UTS of 114.24 MPa. As shown in Fig. 8(a), a large number of micron and deep equiaxed dimples dominate in the fracture of the matrix, which indicates that ductile fracture happened during tensile test. TiB₂ particles were discovered in the equiaxed dimples as shown in Fig. 8(b). It has been reported that TiB₂ particles act as effective barriers to the growth and coalescence of the voids which resulted in the matrix grain refinement.18,19 Due to the great coherent relationship between TiB₂ particles and Al matrix, the good wetting, and the strong interface bonding, the composites achieved excellent tensile properties.

FIG. 8

The fractographs of the composite fabricated by melt-SHS with the ratio of Ti powder TiO₂ as 2:3: (a) macroscopic fracture and (b) TiB₂ particles in the fracture.

IV. CONCLUSIONS

Using the melt-SHS method, 5 wt% TiB₂/Al composites were prepared by the reaction of Al powder, Ti powder, TiO₂, and H₃BO₃ in Al melt successfully. The results are showed as follows:

• (1) 5 wt% TiB₂/Al composite could be produced at 950 °C, but the reaction rate is slow when only adding TiO₂ as the main source of Ti. The addition of Ti powder into the powder block significantly reduces the response time from more than 40 s to less than 10 s and improves the reaction rate. With the increase of titanium powder in the raw powder materials, the reaction rate increased.

• (2) Al₂O₃ particles mainly exist in the melt slag and can be cleared directly. The addition of titanium powder helps to reduce the content of Al₂O₃, destroy the coating structure of Al₂O₃ covered TiB₂ particles, speed up the reaction process, and improve particle concentration.

• (3) The microstructure of composites mainly presents sub-micron TiB₂ particles, and the average size of the particles is 0.67 µm with Ti powder addition to the reactants and the optimized ratio of Ti powder/TiO₂ is 2:3. While the distribution of TiB₂ particles were heterogeneous and the particle size increased when the quality ratio of Ti powder/TiO₂ is larger than 2:3 which resulted from the relatively increased adiabatic temperature induced by the additions of Ti powder.

• (4) The 5 wt% TiB₂/Al composite fabricated by melt-SHS process with modified reactants ratio showed excellent tensile properties with the UTS as high as 114.24 MPa, and the composite also showed superior ductility.