Damping Capacities of (B4C+Ti) Hybrid Reinforced Mg and AZ91D Composites Processed by In Situ Reactive Infiltration Technique

doi:10.11900/0412.1961.2018.00108

Acta Metall Sin

2019, Vol. 55

Issue (1): 141-148 DOI: 10.11900/0412.1961.2018.00108

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Damping Capacities of (B₄C+Ti) Hybrid Reinforced Mg and AZ91D Composites Processed by In Situ Reactive Infiltration Technique

Yantao YAO¹(

), Liqing CHEN², Wenguang WANG¹

1 School of Mechanical Engineering, Liaoning Shihua University, Fushun 113001, China
2 Key Laboratory of Rolling and Automation, Northeastern University, Shenyang 110819, China

Cite this article:

Yantao YAO, Liqing CHEN, Wenguang WANG. Damping Capacities of (B₄C+Ti) Hybrid Reinforced Mg and AZ91D Composites Processed by In Situ Reactive Infiltration Technique. Acta Metall Sin, 2019, 55(1): 141-148.

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Abstract

Mechanical vibration causes lots of damage in automotive industry, machinery manufacturing and aerospace field. Noise control also causes much damage to human health. So it is of great significance to seek materials with high damping capacity to alleviate or eliminate mechanical vibration and noise. Pure Mg has the highest damping capacity among all of the commercial metal materials, but its low mechanical property impose restrictions on its pervasive application. Therefore, magnesium matrix composites reinforced with high mechanical property reinforcement can exhibit excellent damping capacity and mechanical property simultaneously, and this kind of material has attracted great attention and interest from researchers in recent years. A variety of preparation methods has been utilized to prepare magnesium matrix composites reinforced with different reinforcements. In situ reactive infiltration is a relatively new processing method to prepare metal matrix composites, which combines the advantages of in situ reaction synthesis and pressureless infiltration, and it has received increasing attention because of its cost-effectiveness, simplicity and high-efficiency, and near-net shaping capability. And by tailoring the relative density of preform, magnesium matrix composites with a high volume fraction of ceramic reinforcement can be obtained. In view of the poor wettability of B₄C/Mg system leading to low efficiency of composite, Ti particulates with high melting point and immiscible with magnesium was added. And (B₄C+Ti)/Mg and (B₄C+Ti)/AZ91D composites have been prepared successfully by in situ reactive infiltration method with high efficiency and low cost. Microstructure, phase composition and damping capacities of the as-fabricated composites were characterized and analyzed. Results showed that with increasing the preparation temperatures, the reaction between the starting materials is more complete, and the microstructure of (B₄C+Ti)/AZ91D composites tends to be interpenetrating networks from particle reinforced structure. The strain-dependent and temperature-dependent damping capacities of (B₄C+Ti)/Mg and (B₄C+Ti)/AZ91D composites improve gradually with the increase of strain amplitude and temperature respectively, and the dominant damping mechanisms are dislocation damping and interface damping.

Key words: magnesium matrix composite wettability in situ reactive infiltration microstructure damping capacity

Received: 21 March 2018

ZTFLH:

TG146.2

Fund: Supported by National Natural Science Foundation of China (No.51271051)

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https://www.ams.org.cn/EN/10.11900/0412.1961.2018.00108 OR https://www.ams.org.cn/EN/Y2019/V55/I1/141

Fig.1 Flow chart of in situ reactive infiltration technique for preparing (B₄C+Ti)/Mg and (B₄C+Ti)/AZ91D composites (PVA—polyvinyl alcohol)

Fig.2 SEM image of starting reinforcing particles of B₄C and Ti

Fig.3 SEM images of (B₄C+Ti)/Mg (a, c, e) and (B₄C+Ti)/AZ91D (b, d, f) composites prepared at 800 ℃ (a, b), 850 ℃ (c, d) and 900 ℃ (e, f)

Fig.4 XRD spectra of (B₄C+Ti)/Mg (a) and (B₄C+Ti)/AZ91D (b) composites prepared at different temperatures

Fig.5 Comparisons of strain dependent damping capacities between the fabricated (B₄C+Ti)/Mg composites and Mg matrix (a), (B₄C+Ti)/AZ91D composites and AZ91D matrix (b) at different temperatures (tanδ—loss factor, ε—strain amplitude)

Fig.6 Granato-Lücke plots for the fabricated (B₄C+Ti)/Mg composites and Mg matrix (a), (B₄C+Ti)/AZ91D composites and AZ91D matrix (b) at different temperatures (

Q h - 1

—strain amplitude dependent component)

Fig.7 TEM images of dislocations of (B₄C+Ti)/Mg (a) and (B₄C+Ti)/AZ91D (b) composites

Fig.8 Comparisons of temperature dependent damping capacities between the fabricated (B₄C+Ti)/Mg composites and Mg matrix (a), (B₄C+Ti)/AZ91D composites and AZ91D matrix (b) at different temperatures

Fig.9 TEM image and SAED pattern (inset) of TiB in (B₄C+Ti)/Mg composites

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