# Novel Composite Powders with Uniform TiB2 Nano-Particle Distribution for 3D Printing

Mengxing Chen, Xiao Peng Li, Gang Ji, Yi Wu, Zhe Chen, Wouter Baekelant, Kim Vanmeensel, Haowei Wang, Jean-Pierre Kruth

► To cite this version:

Mengxing Chen, Xiao Peng Li, Gang Ji, Yi Wu, Zhe Chen, et al. Novel Composite Powders with Uniform TiB2 Nano-Particle Distribution for 3D Printing. Applied Sciences, 2017, Applied Sciences, 7, pp.250. 10.3390/app7030250. hal-02368000

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Article

# Novel Composite Powders with Uniform TiB₂
## Nano-Particle Distribution for 3D Printing

Mengxing Chen<fnref n="1" />, Xiaopeng Li<fnref n="2" />*, Gang Ji<fnref n="3" />, Yi Wu<fnref n="1" />, Zhe Chen<fnref n="1" />*, Wouter Baekelant<fnref n="4" />, Kim Vanmeensel<fnref n="5" />, Haowei Wang<fnref n="1" /> and Jean-Pierre Kruth<fnref n="2" />

Academic Editor: Giorgio Biasiol

Received: 5 January 2017; Accepted: 16 February 2017; Published: 6 March 2017

**Abstract:** It is reported that the ductility and strength of a metal matrix composite could be concurrently improved if the reinforcing particles were of the size of nanometers and distributed uniformly. In this paper, we revealed that gas atomization solidification could effectively disperse TiB₂ nanoparticles in the Al alloy matrix due to its fast cooling rate and the coherent orientation relationship between TiB₂ particles and α-Al. Besides, nano-TiB₂ led to refined equiaxed grain structures. Furthermore, the composite powders with uniformly embedded nano-TiB₂ showed improved laser absorptivity. The novel composite powders are well suited for selective laser melting.

**Keywords:** 3D printing; nanocomposites; powders; laser absorptivity

## 1. Introduction

In the last decade, powder-based additive manufacturing (AM) techniques, such as selective laser melting (SLM), and their applications have evolved significantly. Thus, more and more efforts have been made to develop novel specialized powders, especially in the field of metal matrix composite powders. In general, micrometer-sized ceramic particles are integrated into a metal matrix with the aim of enhancing mechanical properties such as the Young's modulus and strength, while they often severely degrade the plasticity and machinability of the matrix. The ductility and toughness of such metal matrix composites (MMCs) can be maintained or even improved with a simultaneous increase in strength by reducing the particle size to the nanometer range [1,2], hence the so-called nanocomposites. However, to homogeneously distribute nanoparticles in the metal matrix is still a challenging task [3,4]. For example, during powder metallurgy processing, only a low volume fraction of nanoparticles can be dispersed well in a metal matrix under optimized conditions. However, when the volume fraction of nanoparticles exceeds 2 vol. %, the dispersion is worse even after high-energy ball milling for a long time. The nanoparticles tend to agglomerate along the grain boundaries [4].

Titanium diboride (TiB₂) is an attractive candidate as a reinforcement in the Al matrix since it exhibits a high melting point (3173 K), high modulus (565 GPa), high hardness (2500 HV), and

<footnote n="1">¹ State Key Laboratory of Metal Matrix Composites, Shanghai Jiao Tong University, Shanghai 200240, China; chenmengxing@sjtu.edu.cn (M.C.); eagle51@sjtu.edu.cn (Y.W.); hwwang@sjtu.edu.cn (H.W.)</footnote>

<footnote n="2">² Department of Mechanical Engineering, University of Leuven (KU Leuven), Leuven 3001, Belgium; jean-pierre.kruth@kuleuven.be</footnote>

<footnote n="3">³ Unité Matériaux et Transformations, CNRS UMR 8207, Université Lille 1, Villeneuve d'Ascq 59655, France; gang.ji@univ-lille1.fr</footnote>

<footnote n="4">⁴ Department of Chemistry, University of Leuven (KU Leuven), Leuven 3000, Belgium; wouter.baekelant@chem.kuleuven.be</footnote>

<footnote n="5">⁵ Department of Materials Engineering, University of Leuven (KU Leuven), Leuven 3000, Belgium; kim.vanmeensel@mtm.kuleuven.be</footnote>

<footnote>* Corresponding author: xiaopeng.li@kuleuven.be (X.L.); zhe.chen@sjtu.edu.cn (Z.C.); Tel.: +32-16-321-212 (X.L.); +86-21-5474-7597 (Z.C.)</footnote>
good thermal stability. One of the advantages of these particles is that they have a well-documented crystallographic orientation relationship [5,6] which provides high coherency, thus (1) acting as a nucleus during the solidification of Al [5]; and (2) lowering the solid-particle interfacial energy to improve particle engulfment during solidification [6]. Besides, previous works have proved that the rapid solidification process and the decrease of the particle size can improve the particle engulfment during solidification [7–10].

Here we show that a uniform distribution of a high fraction of TiB₂ nanoparticles in Al-based metal matrix powders was achieved by gas atomization solidification processing through the combined effects of coherency among the metal-diboride interface, supercooling and a nanoscale particle size. The resulting Al-based composite powders exhibited a fine grain structure, with uniformly dispersed TiB₂ nanoparticles, and thereby are promising candidates for nanocomposite synthesis. Since one of the major challenges in the laser-based additive manufacturing (AM) field (e.g., selective laser melting) is the severe limitation of powder materials with acceptable laser processability [11–13], the introduction of pre-embedded nanometer-sized TiB₂ into the metal matrix (e.g., Al-Cu-Mg in this study) would help to expand the powder materials’ palette for AM due to the higher laser absorptivity of TiB₂ compared to the Al matrix [14]. Furthermore, since the nanometer-sized TiB₂ particles are embedded into spherical, micrometer-sized composite powders obtained by gas atomization, the powder flowability is not jeopardized.

## 2. Experimental Procedures

In a previous study, the nanometer sized TiB₂ reinforced Al composites were synthesized via an in-situ reaction process. The size of the in-situ synthesized particles ranged from 20 to 500 nm, but with a predominant number of nanometer sized particles (less than 100 nm) [15]. In the present study, Pure Al was melted at 900 °C with electrical resistance furnace under the protection of an argon atmosphere. The mixed salts of K₂TiF₆ and KBF₄ according to an atomic ratio of Ti/2B were preheated at 250 °C for 2 h and were introduced into the molten aluminum in 15 min. Mechanical stirring of 600 rpm was carried out and heating was maintained at 900 °C for 30 min to allow the in situ TiB₂ particulates to form in the matrix. The reaction slag was skimmed from the surface of the melt. Mg and Al-10Cu master alloys were subsequently added into the melt and homogenized for 10 min. Afterwards, the composite powders were produced by conventional gas atomization. Atomization of the Al-Cu-Mg composite melt was carried out in a confined nozzle atomizer. A schematic diagram of a gas atomization unit and the facility used in the work are shown in Figure 1a,b, respectively. The capacity of the facility used in this experiment is 25 kg melt for a single charging. Prior to melting and atomization, both the melting and the cooling chambers were evacuated to 10⁻² Pa several times, each time being back filled with nitrogen. During heating of the alloy, its temperature is acquired by means of a thermocouple in the melt. The atomization temperature is 800 °C with a gas pressure of 2.8 MPa. The atomized powder was allowed to cool down to room temperature in the nitrogen gas atmosphere of the atomizer. Afterward, the powders were collected in air. The chemical composition of the composite powders was 3.8 wt. % Cu, 1.3 wt. % Mg and 7.6 wt. % TiB₂ particles with Al balance (a prototype of a 2024 Al alloy with TiB₂ addition), measured by inductively coupled plasma atomic emission spectroscopy analysis (ICP-AES). The powder size distribution was measured by Mastersizer 2000 analyzer. In order to study its microstructure, the as-synthesized powder was sieved into four different size ranges: 63–75 µm (group A); 45–53 µm (group B); 10–26 µm (group C); ≤10 µm (group D). The microstructure of the different gas atomized TiB₂/Al composite powder fractions as well as the distribution of TiB₂ particles was investigated by scanning electron microscopy (SEM), energy dispersive X-ray (EDX) and electron backscattered scattering detection (EBSD). EBSD samples were prepared by Focused Ion beam (FIB) in order to detect both the TiB₂ and Al phase. The crystal structure was characterized by synchrotron radiation X-ray diffraction at the beamline BL14B1 of the Shanghai Synchrotron Radiation Facility (SSRF) using a diffractometer of negligible instrumental
broadening (less than 0.001°), equipped with a double crystal monochromator and a position sensitive
point detector. The wavelength of the X-ray used was 0.124 nm.

<figure><img src="image_2.png" /><figcaption>**Figure 1.** (a) Schematic drawing describing the principal of gas atomization technique and (b) set-up of the facility used in this work.</figcaption></figure>

Diffuse reflectance spectroscopy (DRS) was measured from 200–2500 nm using an UV-Visible-NIR Lambda 950 Perkin Elmer spectrometer equipped with a 150 mm diameter integrating sphere coated with Spectralon with 1 nm spectral resolution. A Spectralon reference was used to measure the 100% reflectance and internal attenuators were used to determine 0% reflectance in order to remove background and noise. The samples were placed in a quartz cuvette, sealed, and mounted on a Teflon sample holder for the DRS measurement. The reflectance spectra were subsequently converted to Kubelka-Munk (K-M) to calculate the absorption spectra of the powder. This conversion is performed by the device software, using the K-M equation: $f(R) = \frac{(1 - R)^2}{2R}$, where R is reflectivity.

**3. Results and Discussion**

As shown in Figure 2a, the largest Al-3.8Cu-1.3Mg composite powder particles are around 70 µm. All the powders have a spherical morphology. Figure 2b shows the size distribution of the composite powders measured by laser diffraction and the average powder size is 3.68 µm. The atomized composite powders exhibited a typical rapid solidification microstructure with a fine equiaxed grain structure, as shown in Figure 2(c1-f1). The grain size of the different powder fractions was measured from SEM images (more than 1000 grains were measured for each fraction), and the statistical results are illustrated in Figure 2(c2-f2). The equiaxed grain structure had a median grain size of 2.88 µm in fraction A, and then decreased with the decrease of the powder size to 0.81 µm in group D. Figure 2g shows the variation of the average grain size versus the powder size. The grain size decreased as the powder size decreased. Hong et al. [10,16] proved that the average grain size depends linearly on the powder size and is proportional to the cooling rate of the powders. The fine structure of the powders benefits from the high rate of solidification of the gas atomization process, in which the crystallization process has been suppressed due to the large under-cooling. TiB₂ particles distributed both inside the α-Al grains and along the grain boundaries, as indicated by the arrows in Figure 2(e1,f1).

Figure 3a shows a synchrotron X-ray diffraction pattern of TiB₂-reinforced Al-3.8Cu-1.3Mg composite powders. The diffraction peaks of Al, TiB₂ and Al₂Cu were detected correspondingly, as shown in Figure 3a. From the diffraction pattern, the calculated value (7.1 wt. %) of the TiB₂ mass fraction was obtained through the reference intensity ratio (RIR) method [17], which is in agreement with the ICP result. Figure 3b shows the modified Williamson-Hall plot [18] obtained from the diffraction peaks of aluminum. The intercept of the plot indicates that the average grain size was 731.7 nm while the weighted average grain size calculated from the raw data of Figure 2b,g was 870 nm. The difference is due to the fact that synchrotron X-ray diffraction is more sensitive to low-angle grain boundaries,
while the SEM can only show relatively high-angle grain boundaries. It suggests small-angle grain boundaries exist in the composite powders, which was later observed in the EBSD.

<figure><img src="image_3.png" /><figcaption>**Figure 2.** SEM morphology (a) and powder size distribution (b) of the atomized TiB₂-reinforced Al-3.8Cu-1.3Mg composite powder; SEM micrograph and corresponding grain size distribution of the atomized TiB₂-reinforced Al-3.8Cu-1.3Mg composite powder: (c1,c2) group A: 63-75 µm; (d1,d2) group B: 45-53 µm; (e1,e2) group C: 10-26 µm; and (f1,f2) group D: ≤10 µm; (g) Variation of average grain size with powder size.</figcaption></figure>

<figure><img src="image_4.png" /><figcaption>**Figure 3.** (a) Synchrotron X-ray diffraction patterns of the TiB₂-reinforced Al-3.8Cu-1.3Mg composite powder; (b) Modified Williamson-Hall plot.</figcaption></figure>

It is pointed out in [19] that along with the decreasing powder size, the rapid solidification microstructure can change from dendritic grains to cellular and even to equiaxed grains. In a recent
study, Zheng et al. [14] investigated atomized Al–Cu–Mg (grade 2024) alloy powders, which exhibit a large dendrite structure. In the current study, the composite powders had a much finer equiaxed grain structure (Figure 2(c1–f1)). The modification of the grain structure was due to the effect of TiB₂ nanoparticles on the solidification process, since TiB₂ particles can significantly improve the crystal nucleation rate of α-Al to refine the grains due to the interfacial effect reported in [5,20].

The powders with typical particle sizes of 50 and 10 µm, respectively, were analyzed by EBSD, applying a fine scan with a 0.1 µm step size. Figure 4a shows an example of an EBSD IPF map of the 50 µm composite powder with TiB₂ phase particles in black contrast. It shows that the micrometer-sized equiaxed grains exhibited random orientations. Figure 4b shows EDS mapping of the elemental distribution of titanium of the same powder, which evidences the homogeneous particle dispersion. In conventional solidification microstructures obtained by casting [6,21], the majority of TiB₂ particles are clustered at the grain boundaries among the equiaxed α-Al grains. In the case of the gas-atomized powders, however, SEM observation shows that TiB₂ particles (indicated by arrows) were distributed both within the grain and along the grain boundaries (as shown in Figures 2(c1–f1) and 4). According to [9,22], the particles are engulfed when the moving front is above the critical velocity. The improved distribution of TiB₂ particles is obtained thanks to the high cooling rate, which promotes the velocity of the advancing solidification front. Furthermore, the transition between particle pushing and engulfment is mainly determined by the interfacial energies between the phases in the system. It has been proven that the TiB₂ particles and the α-Al grains tend to form a high-coherency orientation relationship between the two atomic structures to reduce the solid-particle interfacial energy [6], which assists the engulfment to ensure the uniform distribution of the TiB₂ particles.

<figure><img src="image_5.png" /><figcaption>**Figure 4.** (a) EBSD IPF map of a 50 µm composite powder; (b) EBSD EDS map of a 50 µm composite powder. Orientation relationships of TiB₂ particles within a grain: (c) small particles; (d) large particles. (e1,e2): The {0001} and <11-20> pole figures of certain engulfed TiB₂ particles; (f1,f2): The {111} and <−110> pole figures of the surrounding aluminum; (g1,g2): The {0001} and <2-1-10> pole figures of other engulfed TiB₂ particles; (h1,h2): The {001} and <110> pole figures of the surrounding aluminum.</figcaption></figure>
There are two commonly reported orientation relationships of the nucleation of α-Al on TiB₂ during solidification, noted as OR1 and OR2. OR1 is more commonly encountered according to previous studies [6,23]. Figure 4c,d give an example of small and large particles, respectively, in one grain. It was observed that most TiB₂ particles within one grain have two Euler angles which means that they have two orientation relationships with the surrounding aluminum. OR 1 and OR2 co-exist within one grain, as shown in Figure 4c; Figure 4d shows an example of the big particle with OR1.

Figure 4(e1,e2,f1,f2) present the {0001}<11-20> pole figures of certain engulfed TiB₂ particles and the {111}<−110> pole figures of the surrounding aluminum. The paralleled crystallographic planes and orientations are marked by red and green circles, respectively. The orientation relationship is consistent with OR1:

$$
\begin{array}{l}
(0001)_{\text{TiB}_2} \parallel (111)_{\text{Al}} \\
[11-20] \quad \text{TiB}_2 \parallel [-110] \quad \text{Al}
\end{array}
$$

Figure 4(g1,g2,h1,h2) present the {0001} <2-1-10> pole figures of other engulfed TiB₂ particles and the {001}<110> pole figures of the surrounding aluminum. The orientation relationship matches with OR2:

$$
\begin{array}{l}
(0001)_{\text{TiB}_2} \parallel (001)_{\text{Al}} \\
[2-1-10] \quad \text{TiB}_2 \parallel [110] \quad \text{Al}
\end{array}
$$

The statistical analyses of the orientation relationship of recorded TiB₂ particles inside grains and along grain boundaries are summarized in Tables 1 and 2, respectively. Overall, the majority of particles inside the grains (Table 1) form an OR1 relationship with Al as the [0001]TiB₂ direction is closest to the [111]Al direction [23]. Especially for large-sized TiB₂ particles, OR1 appears more frequently. According to the work by Sen and co-workers [8], the faces of the TiB₂ particles in Al that provide the greatest contact area are the basal faces which form OR1. This enhances the engulfment of particles. It should be noted that three of 34 small TiB₂ particles of the 10 µm powder and four of 13 big particles of the 50 µm powder within the Al grains form neither OR1 nor OR2. This indicates that particle engulfment can take place without a coherent interface in the condition of fast-cooling. However, a well-documented crystallographic orientation relationship can lower the solid-particle interfacial energy to improve particle engulfment during solidification [5]. Most TiB₂ particles segregated at grain boundaries (Table 2) rarely develop any relationship with Al. It is proposed that such a phenomenon mainly results from the restriction of α-Al solid volume fractions (v<sub>fs</sub>). At the beginning, when the v<sub>fs</sub> is low, TiB₂ particles are relatively unconstrained and can reorient freely to the growing α-Al in order to reduce the interface energy of TiB₂ and α-Al σ<sub>SP</sub> by forming OR1 or OR2. As v<sub>fs</sub> increases, reorientation of TiB₂ becomes increasingly difficult due to the impingement by either neighboring TiB₂ particles or α-Al from multiple directions. Further, during the final stage of solidification, a high v<sub>fs</sub> along with a high degree of particle-particle interaction will hinder particle motion. Only relatively unconstrained particles will be able to reorient and obtain OR1 or OR2 [6,24]. From the statistical analysis of the orientation relationship, it can be concluded that a uniform dispersion of TiB₂ particles is favored by a coherency interface, supercooling and a nanoscale particle size.

As shown in Figure 5, the composite powder has a reflectivity of ~43% and a corresponding K-M absorption factor of ~0.37 at a wavelength of 1.06 µm, which is typically used for most SLM processes. The K-M absorption factor is comparable to most Al-Si alloy powders between 0.3–0.4. So the laser absorptivity increased significantly due to the addition of TiB₂.

The resulting Al-based composite powders with improved laser absorptivity provide promising candidates for nanocomposite synthesis via AM. The reasons for this are three-fold: (1) the composite powders with higher laser absorptivity will benefit the melt formation during SLM [14]; (2) the introduced nano-sized TiB₂ was pre-embedded mainly into the powder and only a limited proportion was distributed on the powder surface, thus not imposing any negative effect on the flowability of the matrix Al-Cu powder; (3) the interfacial bonding between the nano-sized TiB₂ and the Al-Cu matrix was strong in the gas-atomized composite powder, which can help limit the interface de-bonding during rapid solidification in SLM.
<table><caption>**Table 1.** Orientation relationship summary of all the recorded TiB₂ particles inside the grain by EBSD.</caption><thead><tr><th></th><th>Powder Size</th><th>Total Number of Recorded<br>Small TiB<sub>2</sub> Particles</th><th>Orientation</th><th>Number of<br>TiB<sub>2</sub> Particles</th><th>Proportion</th></tr></thead><tbody><tr><td rowspan="4">Small TiB<sub>2</sub> Particles<br>(&lt;200 nm)</td><td rowspan="2">50 µm</td><td rowspan="2">26</td><td>OR1</td><td>24</td><td>92%</td></tr><tr><td>OR2</td><td>1</td><td>4%</td></tr><tr><td rowspan="2">10 µm</td><td rowspan="2">34</td><td>OR1</td><td>27</td><td>79%</td></tr><tr><td>OR2</td><td>4</td><td>12%</td></tr><tr><td rowspan="4">Big TiB<sub>2</sub> particles<br>(&gt;300 nm)</td><td rowspan="2">50 µm</td><td rowspan="2">13</td><td>OR1</td><td>9</td><td>69%</td></tr><tr><td>OR2</td><td>0</td><td>0</td></tr><tr><td rowspan="2">10 µm</td><td rowspan="2">4</td><td>OR1</td><td>3</td><td>75%</td></tr><tr><td>OR2</td><td>0</td><td>0</td></tr></tbody></table>

<table><caption>**Table 2.** Orientation relationship summary of all the recorded TiB₂ particles at the grain boundaries by EBSD.</caption><thead><tr><th>Average Size of<br>TiB<sub>2</sub> Particles</th><th>Powder Size</th><th>Total Number of<br>Recorded TiB<sub>2</sub> Particles</th><th>Orientation</th><th>Number of<br>TiB<sub>2</sub> Particles</th><th>Proportion</th></tr></thead><tbody><tr><td rowspan="4">&gt;300 nm</td><td rowspan="2">50 µm</td><td rowspan="2">17</td><td>OR1</td><td>1</td><td>6%</td></tr><tr><td>OR2</td><td>0</td><td>0</td></tr><tr><td rowspan="2">10 µm</td><td rowspan="2">4</td><td>OR1</td><td>0</td><td>0</td></tr><tr><td>OR2</td><td>0</td><td>0</td></tr></tbody></table>

<figure><img src="image_6.png" /><figcaption>**Figure 5.** The laser reflectivity and K-M absorption factor of the atomized TiB₂-reinforced Al–3.8Cu–1.3Mg composite powder.</figcaption></figure>

## 4. Conclusions

Gas-atomized, TiB₂-reinforced Al–3.8Cu–1.3Mg composite powders were synthesized by gas atomization solidification. The composite powders exhibited a fine-grained structure benefiting from the fast cooling condition and the integration of TiB₂ particles, which improved the nucleation rate greatly. The engulfment of TiB₂ particles was achieved, benefiting from the fast cooling rate and the two high-coherency orientation relationships between the particles and α-Al, resulting in a relatively uniform particle distribution in the interior of the grains. The resulting Al-based composite powders with a fine grain structure and uniformly dispersed high-fraction TiB₂ nanoparticles provide promising candidates for nanocomposite synthesis via AM because the TiB₂ pre-embedded nanocomposite powders with improved laser absorptivity largely expand the powder materials palette for AM processes, since the alloy element composition can be easily modified.
**Acknowledgments:** This work is financially supported by the National Natural Science Foundation of China (Grant No. 51201099 and No. 51301108). Many thanks are also due to the faculty of BL14B beamline at the Shanghai Synchrotron Radiation Facility for their help on synchrotron experiments.

**Author Contributions:** M.X. Chen and Z. Chen: Co-organized the work, prepared the materials, characterized the materials with SEM, EBSD and Synchrotron X-ray diffraction, wrote the manuscript draft. X.P. Li and W. Baekelant: Materials characterized with laser reflectivity, commented on the manuscript draft. G. Ji: Materials characterized with SEM and TEM analysis, commented on the manuscript draft. Y. Wu: Materials prepared with casting process, commented on the manuscript draft. K. Vanmeensel: commented on the manuscript draft. H.W. Wang and J.P. Kruth: Supervised the materials preparation process, commented on the manuscript draft.

**Conflicts of Interest:** The authors declare no conflict of interest.

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