Abstract
In-situ TiB2 particles can be synthesized via the salts-Al reaction by adding mixed K2TiF6 and KBF4 (Ti/B=1/2) salts into Al melt. In this research, a novel electroslag melting technology was proposed to synthesize TiB2 particles by the salts-Al reaction in order to reduce the reaction time period and purify the melt of composite. The effects of current of electroslag melting on the synthesis of TiB2 particles and mechanical properties of composite were investigated. The results showed that TiB2 particles could be in-situ synthesized by electroslag melting at 600 A for 15min. Compared with 60 min at 850°C of traditional LSM method, the efficiency of preparation was greatly improved. In addition, the dispersion of TiB2 particles in the composite prepared by electroslag melting was improved, meanwhile the non-metallic inclusions in the composite was reduced. The values of YS, UTS and El pct of composite prepared by electroslag melting were higher than that of the composite prepared by traditional LSM method.
1 Introduction
In-situ particles reinforced Al matrix composites have attracted a great deal of attentions in the automotive and aerospace industries due to their good performances, such as high specific strength, low weight, excellent wear resistance [1, 2]. In recent years, in-situ TiB2/Al composite was widely investigated since the fine particles (<1 μm), clean interface and strong interfacial bonding between particle and matrix, and better mechanical properties [3]. It is well known that the in-situ TiB2 particle can be synthesized via a salts-Al exothermic reaction by adding K2TiF6 and KBF4 mixed salts into Al melt, and the method is relatively simple. Because the method was first proposed by London Scandinavian Metallurgical Co., Ltd. [4], it is called the LSM method. Figure 1 shows a schematic illustration of LSM method. Plenty of researchers [5, 6, 7, 8, 9] have fabricated in-situ TiB2/Al composites via the traditional LSM method. Studies showed that a total synthesis period of in-situ TiB2 particles by the traditional LSM method needed 60 min at 850°C, and the TiB2 particles existed in the matrix in the form of aggregation. In addition, the slag produced by the salts-Al reaction was difficult to remove completely. This not only limits the preparation efficiency of composite, but also makes it difficult to give full play to the strengthening effect of TiB2 particles.
A schematic illustration of mixed salts in-situ reaction process (LSM method).
At present, in order to solve the problems encountered in traditional LSM method, many works have been done. Agrawal et al. [10] synthesized in-situ TiB2 for 60 min at 850°C and employed a rotary electromagnetic stirring during solidification of composites to improve the distribution of TiB2 particles. The result showed that the distribution of particles is almost homogenous only near the surface of the solidified castings. Wang et al. [11] introduced a blade paddle mixer during the salts-Al reaction to reduce the reaction time and improve the dispersion of particles. The results indicated that TiB2 particles could be synthesized at 850°C for 30 min, but the dispersion of particles was not changed significantly. Researches indicated that the TiB2 particle clusters in composites took the adverse effect on the mechanical strength of composites. These effects can cause the practical mechanical properties severely deviated from the theoretical prediction. Liu et al. [12] introduced a high-intensity ultrasound into melt for 5 minutes after the salts-Al reaction was completed. Although the dispersion of TiB2 particles was improved, most of particles still distributed in the grain boundaries. Chen et al. [13] also introduced the impeller during salts-Al reaction to stir the salts/Al interface and a total synthesis period was still at 860°C for 60 min. The results showed that proper stirring intensity and duration were helpful to suppress the formation of severe agglomeration. Previous studies showed that the additional melt treatment device can improve the dispersion of in-situ TiB2 particles to some extent, but the preparation process was complex. In addition, the efficiency of preparation was low, and more non-metallic inclusions was introduced in preparation process. Xue et al. [14] prepared the in-situ TiB2/Al composites at 860°C for 60 min by adding CeO2 during the salts-Al reaction. Good results have been achieved on the dispersion of particles, refine matrix grains and purify the melt, but the preparation efficiency was still low.
Electroslag melting is a secondary refining process, which has already been well established for producing steels and other high performance alloys [15, 16]. In the process of electroslag melting, the metal consumable electrode melts layer by layer along the surface, and reacts with molten slag in the form of droplet, which results in the high contact area between metal melt and molten slag. Researches [17] showed that the current density of tip of metal consumable electrode in the slag pool is 10 times higher than that of the inner wall of slag pool, which leaded to the formation of concentrated high temperature region in slag pool, and accelerated the reaction process between metal melt and molten slag. At present, the electroslag refining of Al has been studied. Chen et al. [18, 19, 20] investigated the effects of electroslag refining on removals of iron impurity and alumina inclusion from aluminum using KCl-NaCl-Na3AlF6 slag containing Na2B4O7. The results indicated that Fe could be removed effectively due to the effective chemical reaction between Fe in Al melt and Na2B4O7 in molten slag. In addition, alumina inclusion in Al was also removed effectively. Therefore, Al melt can interact sufficiently with molten slag during the electroslag melting of Al.
In view of the advantages of electroslag melting, in this work, we attempt to prepare in-situ TiB2/Al composite by the electroslag melting technology to improve preparation efficiency and microstructures and refine composite melt, thereby increasing the mechanical properties of composite. During electroslag melting, melting current has a direct effect on the melting rate of consumptive electrode and the temperature distribution of slag pool. Thus, it is one of the key parameters in the preparation of TiB2/Al composites by electroslag melting. In this paper, the effect of melting current on the synthesis of TiB2 particle is explored. The microstructures and mechanical properties of composite prepared by electroslag melting are investigated.
2 Experimental procedures
2.1 Raw materials and preparation
The slag agent of electroslag melting used for the preparation of in-situ TiB2/Al composite was a mixture of K2TiF6, KBF4 used to synthesize TiB2 and the basic slag agent used to refine Al melt. The K2TiF6 and KBF4 were mixed with a molar ratio of Ti/B=1/2, and the amount added in slag agent corresponded to form 5wt % TiB2/Al composite. Basic slag agent was common refining agent that contained 47% KCl, 30% NaCl and 23% Na3AlF6 (mass fraction). The slag agent was dried in drying oven at 300°C for 2 h and mixed in ball mill at 300 rpm for 30 min, and then were poured out and sealed. Commercial purity aluminum (CP) was cast to consumable electrodes with size of Φ40mm×800mm, as shown in Figure 2. The composition of CP is listed in Table 1.
The photograph of Al consumable electrode.
Composotion of commercial purity aluminum (wt.%).
| Fe | Si | Cu | Ga | Mg | Zn | Na | K | B | Al |
|---|---|---|---|---|---|---|---|---|---|
| 0.120 | 0.110 | 0.002 | 0.014 | 0.003 | 0.003 | 0.016 | 0.009 | 0.004 | Balance |
2.2 Composite preparation
The electroslag melting experiments were carried out in a 60 kVA single phase AC unit. The apparatus is shown in Figure 3. The principle of electroslag melting is shown in Figure 4. The CP Al consumable electrode was clamped in electrode clamp. The solid starting technique was used through the arc striking agent. An appropriate amount of arc striking agent was placed in the center of bottom of crystallizer, and was ignited at 50 V. Then, the slag agent was added into crystallizer, and melted to form a slag pool.
The apparatus of experiment (a) and the size of crystallizer (b).
Principle of the electroslag melting.
The consumable electrode was immersed in slag pool, and subjected to electroslag melting to obtain composite ingots with size of Φ70mm×(250~300) mm under a voltage of 15V, a current of 400~700A and a descending speed of 26~126mm/min.
For comparison, in-situ 5wt.% TiB2/Al composite was prepared by conventional LSM method. CP Al ingot was melted in a graphite crucible in an electrical resistance furnace. Mixed fluoride salts of K2TiF6 and KBF4 was wrapped and inserted in batches into Al melt by bell at 850°C, then the melt was hold for 60 min. Periodic stirring was carried out to ensure complete reaction between salts and Al melt. Molten slag was scooped away from the melt surface. Finally, the composite melt was refined by using C2Cl6 at 730°C, then cast into graphite mould at room temperature.
2.3 Sample analysis
The test samples of composite were taken from the middle of ingots. Chemical composition was analysed by using inductively coupled plasma mass spectrometry (ICP-MS). The phase compositions of composite were detected by X-ray diffraction (XRD, D/MAX 2550 VB/PC) using Cu K radiation at 40 kV and 40 mA and scan rate of 5°/min. The slag crust on the surface of ingot of electroslag melting was also analyzed by XRD to examine the composition of slag after reaction.
The microstructures of samples etched using 0.5% HF solution were analyzed by field emission scanning electron microscopy (SEM, Sirion 200) equipped with an energy dispersive spectroscope (EDS) device for identifying the components in samples. Tensile properties were tested at room temperature by zwick/roell test machine at a crosshead speed of 1mm/min. Each value of the tensile properties reported was the average of three tests at the same condition. The size of specimen for mechanical properties testing was shown in Figure 5. The tensile fracture surfaces were also analyzed using SEM.
Dimension of the tensile specimen (in mm).
3 Results and discussion
3.1 Effect of melting current on the synthesis of in-situ TiB2 particles
The electrical parameters of electroslag melting mainly include melting current and voltage, which controls the melting process, including the size and rate of formation of metal droplets, the size and temperature of slag pool, and the depth and volume of metal pool etc. In this works, the melting voltage was constant of 15 V, and different melting currents were set to study on the effect of currents on the formation of in-situ TiB2 particles. In-situ 5 wt% TiB2/Al composite was prepared at different melting currents. In the preparation of composites, the corresponding melting time and slag pool temperature were measured, as shown in Table 2. It is found that with increasing melting currents, the melting time decreases and the temperature of slag pool increases. Figure 6 is appearance of 5wt% TiB2/Al ingot prepared at 600A. A thin layer of slag crust is found on the surface of the ingot, which indicates that the slag agent can play an important role of insulation during electroslag melting. Moreover, some gases were also generated during electroslag melting due to the direct dissociation of the salts which may occur as follows [20]:
Melting times and slag pool temperatures in preparation of composite at different melting currents.
| I | II | III | IV | |
|---|---|---|---|---|
| Melting current I/A | 400 | 500 | 600 | 700 |
| Melting time t/min | 20 | 18 | 15 | 9 |
| Slag pool temperature T/°C | 735 | 778 | 820 | 905 |
Appearance of 5 wt.% TiB2/Al ingots prepared at 600A.
Figure 7 shows XRD patterns of slag crust on the surface of 5 wt.% TiB2/Al composite ingot prepared at 600 A. It can be seen that the slag crust mainly contains NaCl, KCl, KAlF4 and K3AlF6 phases. Among them, the phases of NaCl and KCl are basic slag agent, while the phases of KAlF4 and K3AlF6 are reaction products between K2TiF6, KBF4 and Al melt. Figure 8 shows XRD patterns of the ingot sample prepared at 600 A. The existence of obvious diffraction peaks of TiB2 phase indicates that TiB2 phase was in-situ formed in the ingot prepared by electroslag melting at 600A. Based on the XRD result of slag crust and ingot simple, the formation of TiB2 phase can be follow the reaction below:
XRD pattern of slag crust on the surface of 5 wt% TiB2/Al ingot prepared at 600A.
XRD pattern of the composite prepared at 600A.
Previous studies [22, 23] also proposed that the reaction formula to describe the synthesis of TiB2 phase was as follows:
In both formula (1) and (2), TiB2 phase was the only product that was kept in the matrix. However, in this work, the formula (1) might be more suitable to describe the formation of TiB2 particles in the reaction. The result is in accordance with previous reports [13, 22]. In addition, the XRD results prove that TiB2 particles can be synthesized by the method of electroslag melting.
Figure 9 shows the typical microstructures of 5 wt.% TiB2/Al composites prepared by electroslag melting at different melting currents. It is clear that melting current has a significant effect on the microstructures. Agglomerations with a size beyond 10 um are formed in the composite prepared at 400 A, a few blocky particles scatter around the agglomerations, as shown in Figure 9(a). EDS analysis is performed on the agglomerations in Figure 9(a), and the result is shown in Figure 10. It is found that a certain amount of F and K elements exists in the agglomeration. Early researches [2, 4, 12, 13, 14] have shown that the molten slag produced by the reaction of Al melt and K2TiF6, KBF4 salts could be decanted in the process of preparing the composite by traditional LSM method, and TiB2 phase was the only product that was kept in the matrix. So, it can be concluded that the reaction between Al melt and K2TiF6, KBF4 salts used to synthesize TiB2 was not complete in process of electroslag melting at 400 A. It can be seen from Table 2 that the slag pool temperature is 735°C at 400 A. Chen et al. [24] reported that a complete reaction between Al melt and K2TiF6, KBF4 salts was hard to be achieved at 750°C. Higher reaction temperature could increase the reactivity, which was beneficial for the formation of TiB2 phase. Liu et al. [22] also indicted that temperature played a key factor in the reaction of Al and K2TiF6, KBF4 salts. When the temperature was low, the transfer of Ti and B from molten salts to Al melt was hindered, leading to a limitation of the synthesis of TiB2 phase. Therefore, the above analysis indicates that the Al-salts reaction used to synthesize TiB2 was not complete in process of electroslag melting at 400 A, the low slag pool temperature hindered the synthesis of TiB2 phase.
Effect of melting current on the microstructures of TiB2/Al composites.
EDS spectrum and micro-area components of the agglomeration in composite prepared at 400A
Figure 9(b) shows the microstructural features of composite prepared at 500 A. A large number of cellular adhesions is found. And a small amount of particles exists in isolation around them. However, a significant change in microstructure of composite can be observed when the current increases to 600 A, as shown in Figure 9(c). It is clear that cellular adhesions disappear, and many particles with polygon exist in isolation except for a few particle adhesions. And the size of particle is less than 1 μm. In addition, clean interfaces of Al/particles can be observed. From Figure 8, it is clear that only Al and TiB2 phases are detected in sample at 600 A, which indicates that the particles in Figure 9(c) is TiB2 phase, and the Al-salts reaction used to synthesize TiB2 is complete in process of electroslag melting at 600 A. When current increases to 700 A, as shown in Figure 9(d), the particles with a size beyond 1 μm are observed, and their morphologies are hexagonal and rectangular. In addition, small particle adhesions at the interfaces of Al/particles is observed.
As mentioned above, the melting current has a significant effect on the synthesis of in-situ TiB2 phase via Al-salts reaction during electroslag melting. At low current, the Al-salts reaction is not complete due to low slag pool temperature. At the beginning of melting, Al consumable electrode immersed the slag pool. The first melting Al entered the slag pool and reacted with K2TiF6, KBF4 salts to form TiB2 particles. These particles mingled with the intermediates of subsequent reaction and unreacted salts to form large agglomerations. The slag pool temperature increased with current increasing, which facilitates the reaction of Al-salts. The large agglomerations formed at low current gradually disintegrated into cellular adhesions. When the current was increased to 600 A, the slag pool temperature was 820°C, which is enough to ensure that the Al melt could react fully with salt melts at optimal reaction temperature, melting rate and droplet size of Al consumable electrode. Finally, the in-situ TiB2/Al composite can be successfully prepared in only 15 min. Early researches [2, 10, 13, 14] indicated it took 60 min to synthesize in-situ TiB2 particles by traditional SLM method. It is visible that the preparation efficiency of composite is greatly improved by electroslag melting. When the current reached to 700 A, the slag pool temperature increased to 900°C, which resulted in the growth of preferentially synthesized TiB2 particles. In addition, melting time of Al consumable electrode decreased from 15 min of 600 A to 9 min of 700 A, which leaded to the Al melt has not sufficient time to react with molten salts. Therefore, unreacted salts particles adhered to the interfaces between TiB2 particles and Al matrix, as shown in Figure 9(d).
In the present research, it is demonstrated that the electroslag melting technology can promote effectively the synthesis of in-situ TiB2 particles via the Al-salts reaction at 600 A. Many earlier researches [22, 25] suggested that the salts-metal reaction of K2TiF6-KBF4-Al system is complex. After the mixed salts is added into the Al melt in the traditional LSM method, Ti and B released from the molten salts can diffuse into Al melt across the salts/Al interface to form rather small sized TiAl3, AlB2 by reduction reaction. These two phases can dissolve in the Al melt immediately. At a certain temperature, when the solutes Ti and B in Al melt reach saturation, TiB2 is formed since TiB2 is the most thermodynamically stable phase due to its lowest free energy formation among these three compounds. Thereby, the final formation of TiB2 phase is controlled by the transfer of Ti and B from molten salts to liquid Al and the transformation from TiAl3, AlB2 to TiB2 phase [22, 26]. In the electroslag melting process, on the one hand, the Al melt reacts with molten salts in the form of droplet, which results in hundreds of times more contact area between them than that of LSM method, therefore accelerating the transfer of Ti and B from molten salts to Al melt. On the other hand, in the process of electroslag melting consumable electrode tip is the high temperature region and the Al-salts reaction mainly occurs in the region near Al consumable electrode tip, which accelerates the diffusion rates of Ti and B, leading to a faster saturation of Ti and B in the Al melt. Consequently, TiB2 nuclei can be formed more easily. In addition, the molten salts flow continuously to high temperature region due to the vigorous movement of molten slag under electromagnetic action, which makes the interface of Al-salts renewed continuously, consequently fully reacting.
3.2 Microstructural features of composites
Table 3 is chemical composition of 5 wt% TiB2/Al composites prepared by electroslag melting and traditional LSM method. It can be seen that the absorption rates of Ti and B in Al melt in the process of electroslag melting are almost the same as that of the LSM method. Figure 11 shows the microstructures of composites prepared by two different methods. It is found that the TiB2 particles in the composite prepared by LSM method distribute along the boundaries of α-Al grains in coral-like form, and few particles exist within α-Al grains, as shown in Figure 11(a). A more detailed view of the area of grain boundary is shown in Figure 11(c). Most of the TiB2 particles adhere to each other and exist in the form of clusters. Only the particles at the edge of clusters exist in isolation. However, the significant changes in microstructure can be observed in the composite prepared by electroslag melting, as shown in Figure 11(b)(d). The dispersion of TiB2 particles is improved significantly although most of particles still tend to distribute in the boundaries of α-Al grains. Compared the composite prepared by LSM method, the particles more loose, that is, TiB2 particles tend to distribute from the grain boundaries to interior of α-Al grains, as shown in Figure 11(b). High magnification microstructure in the grain boundary areas, as shown in Figure 11(d), it is found that most of the particles exist in isolation, and the size is smaller than 1 μm. Clean interfaces between TiB2 particles and Al matrix are observed. In addition, compared with the composite prepared by traditional LSM method, the size of α-Al grains is decreased in the composite prepared by electroslag melting, as shown in Figure 11(d).
Chemical compositions of 5 wt% TiB2/Al composites prepared by different processes (wt.%).
| Element | Al | B | Ti | Si | Fe |
|---|---|---|---|---|---|
| LSM | Bal. | 1.56 | 3.42 | 0.15 | 0.14 |
| Electroslag melting | Bal. | 1.52 | 3.36 | 0.11 | 0.12 |
Microstructures of composites prepared by (a)(c) LSM method and (b)(d) electroslag melting.
The distribution of TiB2 particles in Al matrix mainly depends on the dispersion of particles in Al melt and solidification rate. In the composite prepared by electroslag melting the dispersion of TiB2 particles is improved, which mainly is attributed to the shorter Al-salts reaction time, faster solidification rate in water-cooled crystallizer.
3.3 Mechanical properties
Figure 12 presents the mechanical properties of CP aluminum and 5 wt% TiB2/Al composites prepared by LSM method and electroslag melting. Comparison with the un-reinforced CP aluminum has been made. It can be seen that the average values of yield strength (YS) and ultimate tensile strength (UTS) of composite prepared by LSM method are 40 MPa and 94 MPa, which are 53.8% and 56.7% higher than that of CP aluminum, but the elongation (El) is 32% and decreases by 22%. However, the average values of YS and UTS of composite prepared by electroslag melting are 45 MPa and 99 MPa, which are 73.1% and 65.0% higher than that of CP aluminum, and the elongation (El) is 36% and decreases by only 12.2%. It is visible that the YS, UTS and El of composite prepared by electroslag melting are further improved, and are 12.5%, 5.3% and 12.5% higher than the composite prepared by LSM method, respectively. Figure 13 shows the tensile fracture morphology of 5 wt.% TiB2/Al composite. It is found that some large inclusions exist in the composite prepared by LSM, as shown in Figure 13(a)(b). However, the tensile fracture of composite prepared by electroslag melting is clean and no obvious inclusion is observed, as shown in Figure 13(c)(d). This is mainly attributed to the function of basic slag agent used to refine Al melt. In the process of electroslag melting, the contact area between Al melt and slag agent was hundreds of times more than that of the conventional stirring method, and the slag pool is stirred strongly due to electromagnetic action. Therefore, the non-metallic inclusions in Al melt were adsorbed fully by the refining agent, and automatically migrated to the slag pool.
Mechanical properties of 5 wt.% TiB2/Al composites prepared by different processes.
The tensile fractures of TiB2/Al composites prepared by (a)(b) LSM and (c)(d) electroslag melting.
Previous studies have shown that the strength mechanism of in-situ TiB2/Al composite was mainly attributed to the load-bearing strengthening (ΔσLoad), the coefficient of thermal expansion (CTE) mismatch strengthening (ΔσCTE), and the orowan strengthening (ΔσOrowan). And the strengthening effect mainly depended on the dispersion of TiB2 particles in the matrix [11, 12]. In this research, the dispersion of TiB2 particles is further improved in the composite prepared by electroslag melting, that is, the effective TiB2 particle volume fraction increases, which leads to increases in ΔσLoad, ΔσCTE and ΔσOrowan, thereby increasing the YS of composite. In addition, the reduction of non-metallic inclusions and improvement of dispersion of TiB2 particles in the composite prepared by electroslag melting decrease crack initiation and propagation during tensile test, thereby increasing UTS and El.
4 Conclusions
In this research, the in-situ TiB2/Al composites were successfully prepared via the reaction of Al-K2TiF6-KBF4 by electroslag melting. The effects of electroslag melting process on the formation of TiB2 particles, and the microstructures and mechanical properties of composites were investigated. The following conclusions are drawn.
In the process of electroslag melting, the melting current has a significant effect on the formation of TiB2 particles. The Al-salts reaction is not complete at both too low current and too high current. TiB2 particles can be in-situ synthesized successfully at 600 A for 15min. Compared with 850°C for 60 min of LSM method, the preparation efficiency is greatly improved.
The dispersion of TiB2 particles is improved in the composite prepared by electroslag melting. TiB2 particles tend to distribute from the grain boundaries to interior of α-Al grains, and most of the particles exist in isolation. This mainly is attributed to the shorter Al-salts reaction time and faster solidification rate in water-cooled crystallizer. In addition, the size of α-Al grains is decreased due to faster solidification rate in electroslag melting.
The non-metallic inclusions are significantly reduced in the TiB2/Al composite prepared by electroslag melting. The values of YS, UTS and El pct of composite prepared by electroslag melting are 12.5%, 5.3% and 12.5% higher than that of the composite prepared by LSM method.
Acknowledgement
This work is supported by the National Natural Science Foundation of China (Grant No. 51804198). At the same time, the authors are grateful to the Instrumental Analysis Center of Shanghai Jiao Tong University for help in the microstructure analyses.
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