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Al composites fabricated by accumulative roll bonding
Accepted Manuscript High damping capacity and low density M2052/Al composites fabricated by accumulative roll bonding Y.X. Gao, X.P. Wang, W.B. Jiang, J.F. Yang, L.F. Zeng, Q.F. Fang PII:
S0925-8388(18)31789-4
DOI:
10.1016/j.jallcom.2018.05.104
Reference:
JALCOM 46077
To appear in:
Journal of Alloys and Compounds
Received Date: 20 January 2018 Revised Date:
7 May 2018
Accepted Date: 8 May 2018
Please cite this article as: Y.X. Gao, X.P. Wang, W.B. Jiang, J.F. Yang, L.F. Zeng, Q.F. Fang, High damping capacity and low density M2052/Al composites fabricated by accumulative roll bonding, Journal of Alloys and Compounds (2018), doi: 10.1016/j.jallcom.2018.05.104. This is a PDF file of an unedited manuscript that has been accepted for publication. As a service to our customers we are providing this early version of the manuscript. The manuscript will undergo copyediting, typesetting, and review of the resulting proof before it is published in its final form. Please note that during the production process errors may be discovered which could affect the content, and all legal disclaimers that apply to the journal pertain.
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High damping capacity and low density M2052/Al composites fabricated by accumulative roll bonding
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Y.X. Gao a, X.P. Wang a, W.B. Jiang a, J.F. Yang a , L.F. Zeng a, b, Q.F. Fang a, b Key Laboratory of Materials Physics, Institute of Solid State Physics, Chinese Academy of Sciences, Hefei 230031, China
University of Science and Technology of China, Hefei 230026, China
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b
Abstract
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High damping capacity and low density M2052/Al composites were successfully fabricated using the accumulative roll bonding (ARB) method, by taking advantages of high damping capacity for M2052 alloy (Mn-20Cu-5Ni-2Fe, at%) particles and excellent mechanical properties and low density for Al matrix. The 15 wt% M2052 particles were uniformly dispersed in Al-matrix after 10 ARB process cycles. M2052/Al composites have a low density of 2.9 g/cm3, which is just a little higher
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than that of Al. After ARB process and a subsequent hydrogen annealing, the M2052/Al composites exhibit both high room temperature damping capacity and good mechanical properties: the highest damping capacity is 0.01 at 270K, 5 times that of pure Al at the comparative temperature; the
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ultimate tensile strength is about 70 MPa (about 35% higher than that of pure Al), and the total elongation reaches 24%. The simultaneous enhancements on damping capacity and tensile strength
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of the M2052/Al composites can be attributed to the high damping capacity and the dispersion strengthening of M2052 phase, as well as the good bonding between the M2052 particles and Al matrix resulted from the ARB technique. Keywords: Al-matrix composites (AMCs), M2052 (Mn-20Cu-5Ni-2Fe, at%) alloy, Damping capacity, Low density alloy, Accumulative roll bonding (ARB).
Corresponding authors. QF Fang: [email protected]
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1 Introduction Aluminum and its alloys have attracted considerable interests because of their excellent mechanical properties and low density [1], and are widely used in fields such as aircraft, aerospace and defense applications. However, the low damping capacity [2-4] limits their engineering
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applications for controlling noise and suppressing mechanical vibration. In previous studies, Al-matrix composites (AMCs) were designed using hard particles like Al2O3, SiC, and TiB2 [5-10] as reinforcement phases, mainly to improve the strength of the composites. Although the damping capacity of the composites increases a little, owing to the thermal
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stress induced dislocations in Al matrix and the weak bonded interface between the matrix and reinforced particles [11], such increment is not high enough to meet the needs of application as high
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damping materials. Furthermore, the dislocation and interface mechanisms can only enhance the damping capacity of AMCs at temperatures higher than 200°C. On the other side, the weak bonded interface would seriously damage the mechanical properties of AMCs. As a result, in the traditional damping composites based on the motion of dislocations and interfaces in the matrix, the damping capacity was enhanced at a cost of decreasing the mechanical properties.
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Recently, a novel design concept to obtain the AMCs with both excellent mechanical properties and high damping capacities was suggested [12]. The main idea of this concept is to add some unique particles with superior intrinsic damping capacity into the Al matrix. In such designed
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composites, the damping capacity and mechanical properties can be enhanced simultaneously because the mechanism responsible for the damping (from the particle) is independent of the
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mechanism that controls the mechanical properties (from the matrix). Examples of such particles are graphite [13, 14], piezoelectric [15, 16] and lithium ionic electrolytes Li-La-M-O (M=Ta, Nb, Zr, Bi) particles [17-21], among which the Li-La-M-O ceramics exhibit the highest intrinsic damping capacity of 0.12 at room temperature. In order to obtain a strong interface between the matrix and additives, Li-La-M-O/Al composites were fabricated by accumulative roll bonding (ARB) methods for the first time in our lab with a high damping capacity of 0.01 (five times higher than that of pure Al) at room temperature [21]. More importantly, the total elongation to failure of the Li-La-M-O/Al composites fabricated by ARB can achieve 34% at room temperature. It has been evidenced that the ARB method is suitable for preparing particles reinforced metal based composites with full density, 2
ACCEPTED MANUSCRIPT uniform distribution of reinforcement particles in the matrix, and good bonding interfaces between additives and matrix [22-24]. Manganese-rich Mn-Cu alloys, especially for Mn-20Cu-5Ni-2Fe (atomic fraction, %, M2052) [25-27], have been developed for a good balance between the damping capacity, strength and
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workability. The M2052 alloys exhibit a large damping peak extending in a wide temperature range from 223K to 348K. However the high density (>7.8 g/cm3) of M2052 alloys limits their large-scale application in aerospace fields.
Therefore, in this paper the novel M2052 particulate reinforced Al composites was fabricated by
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the ARB method, in order to simultaneously achieve low density, high damping capacity, high strength and good ductility. The microstructures, dispersion of Mn-Cu alloy particles, mechanical
enhancement was discussed.
2 Experimental methods
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and damping properties of the composites were characterized and the mechanism for property
2.1 Design concept of M2052 particles reinforced AMCs
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Theoretically, the corresponding microscopic mechanisms of high damping capacity of materials are generally associated with stress induced movement of crystalline defects in materials. Such defects includes point defects, dislocations and planar defects (twin boundaries and magnetic
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domain boundaries), among which, the planar defects give rise to the highest damping capacity per unit concentration and are usually chosen as the major damping source in the engineering design [11].
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The high damping of the M2052 (Mn-20Cu-5Ni-2Fe, at%) alloys is just originated from the twin boundaries relaxation in its martensitic phase. Combined the high intrinsic damping capacity of M2052 powders with the good mechanical properties of Al-matrix and followed the novel design concept of high damping composites [12], a new kind of M2052/Al-matrix composites simultaneously achieving high damping and excellent mechanical properties was designed, where the main mechanism responsible for the energy dissipation (from the twin boundaries relaxation in M2052 particles) is independent of the main mechanism that controls the mechanical properties (from the Al matrix). 2.2 ARB fabrication of M2052/Al composites 3
ACCEPTED MANUSCRIPT The raw materials were commercial 1A99-Al sheets (purity 99.99%, metallic base) and M2052 (Mn-20Cu-5Ni-2Fe, at%) alloy particles (high damping additive). The 1A99-Al sheets were cut into a size of 40mm×60mm×1mm. Before the roll-bonding process, the Al sheets were cleaned in acetone and subsequently scratched by wire brushing to remove the surface oxides and to promote bonding
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between Al sheets. After that, a thin layer of M2052 particles was sprayed on the Al sheet with ethyl alcohol as solvent. Then, two Al sheets covered with M2052 particles were stacked and fixed at both ends using a steel wire. The stacked Al sheets were roll-bonded with a reduction of 65% in thickness at room temperature, which is necessary for a good bonding between the neighboring Al layers with
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particles on the surface [28]. This initial roll-bonding step was designated as the 1st cycle. Finally, the well roll-bonded sheet was cut into two sheets, which were re-stacked and roll-bonded with 50%
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reduction in thickness with a similar surface treatment mentioned above, this step was designated as the 2nd cycle. In order to attain a uniform distribution of M2052 powders, the above ARB step was repeated until to the 10th cycles. A detailed schematic illustration of the ARB process was shown in Fig. 1. It was worthwhile to note that an intermittent annealing (673K for 2h) is necessary for Al sheets after two or three roll-bonded processes to avoid cracking. To evaluate the effect of the
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intermittent annealing atmosphere on the damping and mechanical properties of M2052/Al composites, the H2 and Ar gas with the purity of higher than 99.999% were used comparatively. At last, the well 10th ARB cycle processed sheet was annealed at 673K for 2 h in H2. Hereafter, in this
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work, the samples are named as M2025/Al-I(H)-L(H), M2052/Al-I(Ar)-L(H) and M2052/Al-I(H),
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which correspond to different annealing conditions as indicated in Table 1.
2.3 Experimental characterization The X-ray diffraction (XRD) technique was employed to characterize the phase of the produced M2052/Al composites after 10 ARB cycles at room temperature, by using Cu-Kα radiations in a scanning range from 20° to 90° with a step of 0.033°. The novel X-ray 3D microscopy system (micro CT) (NanoVoxel-2000, Sanying, China) was employed to characterize the distribution of M2052 particles in roll-bonded M2052/Al composites. The surface morphology and tensile fracture surface of M2052/Al composites were examined by field emission scanning electron microscope (SEM) (Sirion200, FEI, USA) equipped with an energy dispersive spectroscopy (EDS). The mechanical properties of M2052/Al composites were performed by using an Instron-5967 4
ACCEPTED MANUSCRIPT testing machine at room temperature with a constant speed of 0.06 mm/min, which corresponds to an initial strain rate of 2×10-4 s-1. The dog-bone-shaped tensile samples were cut from the M2052/Al composites in a size of 1.5 mm×1.7 mm in cross section and 5 mm in working length. All tensile specimens were mechanically polished before the tensile tests.
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The damping capacity of M2052/Al composite strips with a dimension of 20 mm×2 mm×1mm was measured on a computer-controlled inverted torsion pendulum under the forced-vibration mode. The measuring frequency of the pendulum was chosen as 0.5, 1, 2 and 4 Hz. The maximum strain
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amplitude was kept at 5×10-5 and the heating rate was maintained at 2K/min in all the experiments.
3 Results and discussion
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3.1 Microstructure analysis
The room temperature XRD patterns of the M2052 powders and 10 ARB processed M2052/Al composites are shown in Fig.2. It can be seen that only the pure Al and M2052 XRD diffraction peaks are detected in the composite sample, which demonstrates that after the continual annealing
other impurity phase.
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and ARB processing there is no reaction between the M2052 particles and Al-matrix and no any
Fig. 3 shows the cross section SEM micrographs of M2052/Al composites produced by 1st, 3rd and 10th ARB cycles. As can be seen in Fig. 3(a), after the first ARB cycle the M2052 particles
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cluster as a layer, which poorly bonded with the two neighboring Al layers. As expected, with the increasing cycle number of the ARB process, the M2052 particles would be dispersed more and more
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uniformly in the bulk of the aluminum matrix. This is true because after 3rd ARB cycles, the M2052 layers are fractured into small clusters as shown in Fig 3(b). After 10 ARB cycles, a homogeneous dispersion of M2052 particles in Al matrix was achieved as shown in Fig. 3(c). In the case of 10 ARB cycles, the number of Al layers would be 2×29 and the layer thickness is only about 980 nm, if the Al layers could be distinguishable. This means that the hard M2052 particles with a size of 10µm would definitely penetrate these Al nano-layers during the ARB process and redistribute more homogeneously in the Al-matrix. It is easier to establish a good bonded interface between M2052 particles and Al matrix because of the similar metallic features than in the case of ceramics/Al composites. 5
ACCEPTED MANUSCRIPT The macro-view of the 10 ARB processed M2052/Al composites is also shown in the lower part of Fig.3(c). The size of the sample depends on the primary size of the 1A99-Al sheet and the thickness reduction of the roll-bonded process. Based on the concept of designing low density and high damping composites, M2052 alloy particles are added as the damping phase into Al matrix with
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a mass fraction of 15 wt%, corresponding to a density of 2.9 g/cm3. The density of M2052/Al composites is much lower than that of M2052 alloys (7.8 g/cm3) and only a little higher than that of pure Al (2.7 g/cm3).
Fig. 4(a) shows the surface morphology of M2052/Al composites after 10 ARB cycles. It can be
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seen that the reinforcement particles size is about 10µm, and the line scanning EDS spectra of M2052/Al composites shown in the upper part of Fig. 4(a) indicate that these particles are Mn-Cu
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alloy phase because the Mn and Cu signals are all detected simultaneously. Fig. 4(b) shows the X-ray 3D image of M2052/Al composites after 10 ARB cycles, in which M2052 particles are indicated by the yellow dots. It can be seen that in a macroscopic region, the M2052 particles are well uniformly distributed in Al-matrix with very few regions of particle clustering, which provides further evidence
3.2 Damping performance
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for forming a uniform distribution of M2052 particles in AMCs after 10 ARB process.
3.2.1 Internal friction test principle
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An inverted torsion pendulum for the internal friction test is schematically shown in Fig. 5(a), where a permanent magnet is fixed on the upper part of the pendulum, and two excitation coils (drive coils) are installed at the corresponding horizontal position. The sample is installed between the
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movable upper rod and the fixed bottom supporter. During the internal friction test, a sinusoidal excitation signal generated by the computer is amplified and sent to the excitation coil. As a result, an alternating electromagnetic torque is generated, which acts on the magnet to force the sample to vibrate sinusoidally. The mirror installed on the upper rod reflects the light to the photoelectric displacement sensor, which generates the strain signals of the sample. After amplification, the strain signal of the sample is sent to the computer and compared with the stress signal (excitation signal). According to the definition of the internal friction (Q-1), we have 1 ∆W Q −1 = 2π W
(1)
Where ∆W is the dissipated energy per unit volume in one vibration cycle, and W is the maximum 6
ACCEPTED MANUSCRIPT stored energy per unit volume. For the forced vibration test mode, by comparing the stress and strain signals of the sample, the phase difference (loss angle) ϕ by which the strain lags behind the stress, can be obtained, and the internal friction can be written as Q −1 = tan ϕ
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(2)
3.2.2 Damping capacity of the M2052 alloys and M2052/Al composites
Fig. 5(b) and (c) show the temperature dependence of internal friction (Q-1) for M2052 alloys
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before and after the annealing at 673K in H2, respectively, where two damping peaks can be detected. The main-peak at about 270K shifts to higher temperature with the increasing frequency, and is
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associated with the relaxation process of the twin boundaries in the face-centered tetragonal (fct) phase. The other small sub-peak at about 333K is frequency-independent, and corresponds to the martensitic phase transformation (fct↔face-centered cubic (fcc)) [27]. The annealing at 673K in hydrogen in this investigation will promote the spinodal decomposition to form the Mn-rich and Cu-rich phases from the fcc γ-MnCu solid solution [25] and the fct phase (a kind of martensitic
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phase) are formed from the Mn-rich phase via martensitic transformation. Therefore, the annealing at 673K in hydrogen is important to obtain a high density of twin boundaries which give rise to high damping of M2052 alloys. As a result, the internal friction values of the main peak for hydrogen annealed M2052 alloy (Fig. 5(b)) are higher than that for the un-annealed M2052 alloy (Fig. 5(c)),
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because the twin boundaries and hydrogen are both indispensable prerequisites for the appearance of the twin boundaries relaxation peak, as evidenced in the shape memory alloys such as Ti-Ni-Fe,
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Ti-Ni-Pd, Ti-Pd, Mn-Cu, Au-Cd, and Cu-Al-Ni [29]. Fig.6 shows the internal friction of M2052/Al-I(H)-L(H) sample as a function of temperature at different measurement frequencies. It can be seen that a prominent damping peak located around 270K is observed in M2052/Al composites, which shifts also to higher temperature with increasing frequency. It is noted that the damping peak of martensitic transformation at about 333K is absent in the composite because of its low damping level when combined with the Al-matrix. The peak position (~270K) and peak shift trend with frequency in M2052/Al composite is consistent with the results of pure M2052 alloy as shown in Fig. 5(c), which implying that this peak is the same one in the pure M2052 alloys. On the other side, in the ARB prepared M2052/Al 7
ACCEPTED MANUSCRIPT composites, a repeated roll-bonded process makes a good bonding interface between the dispersion phase and Al-matrix and a uniform dispersion of M2052 particles in Al-matrix as shown in Fig.3(c). In the damping test of the composite materials, the stress applied onto the M2052/Al composite sample can be totally transmitted from the Al-matrix to dispersion phase owing to the well bonded
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interfaces, which is helpful to activate the damping mechanism in the M2052 particles. Because the damping capacity of Al-matrix is very low (10-3), it is clear that this damping enhancement of M2052/Al composite is mainly attributed to the addition of the M2052 particles and the dominant damping mechanisms of M2052/Al composite is originated from the motion of twin boundaries in
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M2052 martensitic phase.
In addition, the damping capacity of the present ARB M2052/Al composite was compared with
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values of the conventional Al-matrix composites, as listed in Table 2 [8, 10, 12, 21, 30, 31]. It can be seen that using M2052 powders as additives can effectively improve the room temperature damping capacity of the Al-matrix composites comparing with that by adding the conventional additive powders, such as Al2O3, SiC, TiB2, graphite, etc., in which the dislocation and interface mechanisms can only enhance the damping capacity of Al-matrix composites at temperatures higher than 200oC.
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Such an enhancement of damping capacity of M2052/Al composites in the lower temperature region is very important for the practical application of such a novel M2052/Al composites. In addition, as shown in Fig. 6, the high damping capacity (>7.5×10-3) of M2052/Al composites extends in a wide temperature range because of its twin-boundary relaxation mechanisms in M2052 phase, however for
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Li-La-M-O (M=Ta, Nb, Zr, Bi)/Al composites, the high damping (>7.5×10-3) distributes in a narrower temperature range, which is associated with the point defects relaxation [21].
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In Fig.7 the internal friction of M2052/Al-I(H) and M2052/Al-I(H)-L(H) samples at 1 Hz as a function of temperature was compared, where the result of the annealed pure Al is also presented as a comparison. The results indicate that the room temperature damping capacity of annealed pure Al is as low as 0.002. However, the damping capacity (Q-1) of both M2052/Al-I(H) and M2052/Al-I(H)-L(H) samples at 1Hz is 3-5 times that of pure Al at the comparative temperature. This enhancement of damping capacity mainly results from the addition of damping phase M2052. Meanwhile, it also benefits from the uniform dispersion of M2052 alloy particles, elimination of micro-pores and the well bonding interface between the damping phase and the Al-matrix resulted from the ARB processing, as shown in Fig.3(c) and 4(a). In addition, as expected, 8
ACCEPTED MANUSCRIPT M2052/Al-I(H)-L(H) sample exhibits higher damping values (with a maximum of 0.01 at 270K) than that of M2052/Al-I(H), owing to the last hydrogen annealing. This result is consistent with that of pure M2052 alloys as shown in Fig.5. Therefore, the last annealing process at 673K for 2 h in H2 indeed has a large effect on the damping property.
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Fig.8 shows the internal friction of M2052/Al-I(H)-L(H) and M2052/Al-I(Ar)-L(H) samples at 1Hz as a function of temperature. The results indicate that the peak height (0.008) at 270K at 1Hz of M2052/Al-I(Ar)-L(H) sample is a little lower than that (0.01) of M2052/Al-I(H)-L(H). To understand this phenomenon, the room temperature XRD pattern of the M2052/Al-I(Ar)-L(H) has
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been measured, as shown in the inset of Fig.8, where additional reflections corresponding to impurity phase of MnO2 (JCPDS: 01-0799) have been detected. This illustrates that a small amount of MnO2
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has been generated during the intermittent annealing in Ar because Mn are highly oxygenated, which as the second phase are distributed in the M2052/Al composites, including at the twin boundaries and grain boundaries of M2052 alloy and phase interfaces between M2052 and Al. Because the dominant high damping mechanism of M2052/Al composite is originated from the motion of twin boundaries in M2052 martensitic phase, the MnO2 impurities distributed at the twin boundaries will hinder the
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motion of the twin boundaries during the damping test process, and result in the decrease of damping values of relaxation peaks in the temperature range of 200K-300K for M2052/Al composites.
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3.3 Mechanical properties
The engineering tensile stress-strain curves of the M2052/Al-I(H), M2052/Al-I(H)-L(H) and M2052/Al-I(Ar)-L(H) samples are shown in Fig. 9, where the results of the pure annealed Al are also
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presented as a comparison. It can be seen that the M2052/Al-I(H) sample exhibits a high ultimate tensile strength (UTS) of 112 MPa and a low total tensile elongation to failure (TE) of 5%. After the last annealing in H2, although the UTS decreases significantly to 70 MPa, which is still about 35% higher than that of pure Al (52.0 MPa) as shown in Fig.9, the TE of the M2052/Al-I(H)-L(H) sample is improved significantly to 24% comparing with that of the M2052/Al-I(H) sample. Generally speaking, for the M2052/Al-I(H) sample, the deformation in the last ARB cycle may result in high density of dislocations and grain boundaries, which is responsible for the high UTS and low TE values. However for the M2052/Al-I(H)-L(H) sample, the last annealing process (673K for 2h in H2) definitely results in the full recrystallization of the Al matrix and decrease of the density of 9
ACCEPTED MANUSCRIPT dislocations and grain boundaries, which is the reason of UTS decline and TE increment. However, the UTS of the M2052/Al-I(H)-L(H) sample is still higher than that of pure Al because of the dispersion strengthening of the M2052 particles. Plenty of evenly distributed dimples in the cross section micrograph as shown in Fig. 9(b) indicate the ductile failure mode of the
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M2052/Al-I(H)-L(H) sample, which is consistent with the apparent increase in the TE (24%). A lot of M2052 alloy particles in the composites locate at the core of the dimples, which suggests that the shear ductile fracture begins at the interface of particles and matrix [32].
In addition, by comparing the results of the M2052/Al composites with the different intermittent
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annealing atmosphere of Ar and H2 as shown in Fig.9(a), it is noted that the Ar annealing results in a higher UTS of 83.8 MPa and a lower TE of 13%. The UTS enhancement of the M2052/Al-I(Ar)-L(H)
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may be partially associated with the strengthening mechanism of second phase MnO2. However, like most structural materials, the second phase MnO2 inevitably decreases the ductility of M2052-I(Ar)-L(H) composite because of the effect of work hardening. The MnO2 may be also served as the crack nucleation sites to decrease the TE of composites under tensile loading
4 Conclusions
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conditions.
In the present study, M2052/Al composites were successfully fabricated via the ARB process.
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All investigated M2052/Al composites after 10 ARB cycles show a uniform distribution of M2052 particles in Al-matrix and well bonding interfaces. The M2052/Al samples with intermittent and the
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last annealing in hydrogen exhibit the best comprehensive properties: the lower density of 2.9 g/cm3 (much lower than that of M2052 alloy); the high damping capacity of 0.01 at 270K, 5 times that of pure Al at the comparative temperature; the UTS value of 70 MPa, about 35% higher than that of pure Al; and the high TE of 24%. The M2052/Al samples with intermittent in argon and the last annealing in hydrogen exhibit a little lower damping capacity owing to the pinning down of twin boundaries by a few MnO2 impurities that formed in the intermittent annealing. Such MnO2 impurities result in at same time an enhancement of UTS and a decrease of TE due to the strengthening mechanism of second phase. All the enhanced properties of ARB prepared M2052/Al composites can be attributed to the full density, uniform distribution of particles and a good bonding 10
ACCEPTED MANUSCRIPT interface between M2052 particles and Al matrix. Such a high performance M2052/Al composites fabricated by ARB method could find promising application as damping materials for eliminating noise and reducing mechanical vibration. Furthermore, It is expected that if other commercial Al alloys, such as 6061Al and 2A14Al, were used to prepare M2052/metal (matrix) composites, better
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comprehensive properties would be obtained because such Al alloys have much better mechanical properties than the pure Al (1A99Al) [33].
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Acknowledgment
This work was supported by the National Natural Science Foundation of China [Grant Numbers
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11405203, 51771181 and 51502300]; and the CASHIPS Director’s fund [Grant Number YZJJ201703].
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capacity of LLZNO/Al composites fabricated by accumulative roll bonding, Mater. Sci. Eng. A 689 (2017) 306-312.
[22] M. Naseri, A. Hassani, M. Tajally, An alternative method for manufacturing Al/B4C/SiC hybrid composite strips by cross accumulative roll bonding (CARB) process, Ceram. Int. 41 (2015)
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13461-13469.
[23] C.Y. Liu, Q. Wang, Y.Z. Jia, B. Zhang, R. Jing, M.Z. Ma, Q. Jing, R.P. Liu, Evaluation of
process, Mater. Des. 43 (2013) 367-372.
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mechanical properties of 1060-Al reinforced with WC particles via warm accumulative roll bonding
[24] R. Jamaati, M.R. Toroghinejad, Manufacturing of high-strength aluminum/alumina composite by accumulative roll bonding, Mater. Sci. Eng. A 527 (2010) 4146-4151. [25] K. Adachi, T. Yamashita, Y. Taneda, D.M. Farkas, J. Perkins, dynamical transmission electron
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microscopy microstructure associated with electron-phonon interaction in high damping Cu-Mn alloys, Philos. Mag. A 73 (1996) 1009-1034.
[26] Q. Wu, F.X. Yin, K. Hono, The decomposed γ-phase microstructure in a Mn-Cu-Ni-Fe alloy
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studied by HRTEM and 3D atom probe, Scripta Mater. 46 (2002) 717-722. [27] M. Fukuhara, F.X. Yin, Y. Ohsawa, S. Takamori, High-damping properties of Mn-Cu sintered alloys, Mater. Sci. Eng. A 442 (2006) 439-443.
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[28] M. Alizadeh, M.H. Paydar, Fabrication of nanostructure Al/SiCp composite by accumulative roll-bonding (ARB) process, J. Alloy. Compd. 492 (2010) 231-235. [29] A. Biscarini, B. Coluzzi, G. Mazzolai, F.M. Mazzolai, A.Tuissi, Mechanical spectroscopy of the H-free and H-doped Ni30Ti50Cu20 shape memory alloy, J. Alloy. Compd. 356-357 (2003) 669-672. [30] J. Zhang, R.J. Perez, M. Gupta, E.J. Lavemia, Damping behavior of particulate reinforced 2519 Al metal matrix composites, Scripa Metallurgica et Materialia 28 (1993) 91-96. [31] Z. M. Zhang, B. Hu, Damping behavior and mechanism of graphite and Al2O3 particles reinforced Al matrix composites, Materials Science Forum 682(2011) 225-229. [32] H.F. Dehkordi, M.R. Toroghinejad, K. Raeissi, Fabrication of Al/Al2O3/TiC hybrid composite 13
ACCEPTED MANUSCRIPT by anodizing and accumulative roll bonding processes and investigation of its microstructure and mechanical properties, Mater. Sci. Eng. A 585 (2013) 460-467. [33] S. Roy, B.R. Nataraj, S. Suwas, Accumulative roll bonding of aluminum alloys 2219/5086
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laminates: microstructural evolution and tensile properties, Mater. Des. 36 (2012) 529-539.
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Figures captions Fig. 1 Schematic illustration of the ARB process.
Fig. 2 The room temperature XRD patterns of the M2052 powders and 10 ARB cycles processed
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M2052/Al composites.
Fig. 3 The cross section SEM micrographs of M2052/Al composites after different ARB cycles of (a) 1, (b) 3, and (c) 10. Inset in (c): the macro-view of the 10 ARB cycles processed M2052/Al
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composites.
Fig. 4 (a) The surface morphology and line scanning EDS spectra of M2052/Al composites after 10 ARB cycles; (b) X-ray 3D image of M2052 particles dispersed in M2052/Al composites.
Fig. 5 (a) The schematic diagram of a torsion pendulum and internal friction (Q-1) as a function of
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temperature for the M2052 alloys (b) unannealed and (c) annealed at 673K in H2.
Fig. 6 Internal friction (Q-1) as a function of temperature at different frequencies for the sample of
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M2052/Al-I(H)-L(H).
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Fig. 7 Internal friction (Q-1) as a function of temperature at 1 Hz for samples of M2052/Al-I(H)-L(H), M2052/Al-I(H) and the annealed Al.
Fig. 8 Internal friction (Q-1) as a function of temperature for the samples of M2052/Al-I(H)-L(H) and M2052/Al-I(Ar)-L(H). Inset: The room temperature XRD patterns of M2052/Al-I(Ar)-L(H).
Fig. 9 (a) The engineering stress-strain curves of the 10 ARB cycles processed M2052/Al composites: M2052/Al-I(H), M2052/Al-I(H)-L(H), M2052/Al-I(Ar)-L(H) and the annealed pure Al; (b) SEM images of the fractured surface of M2052/Al-I(H)-L(H). 15
ACCEPTED MANUSCRIPT Table 1 The abbreviation illustration of the M2052/Al samples with different annealing conditions.
Abbreviation
Annealing conditions
M2052/Al-I(H)-L(H)
M2052/Al composite with intermittent and the last annealing in H2
in H2
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M2052/Al composite with intermittent annealing in Ar and the last annealing M2052/Al-I(Ar)-L(H)
M2052/Al composite with intermittent annealing in H2 without the last M2052/Al-I(H)
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annealing
Reinforcement content
SiC/Al Al2O3/Al TiB2/Al Li6.25La3Zr1.75Nb0.25O12/ Al Graphite/Al2O3/Al
10 wt.%
f (Hz)
Ref.
0.004 0.003 0.005
1Hz 1Hz 1Hz
[8][12] [12] [30] [10]
0.009
1Hz
[21]
Graphite-3 vol% and Al2O3-10 vol.% 15 wt.%
0.009
5Hz
[31]
0.01
1Hz
Present work
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M2052/Al
11 vol.% 15 vol.% 5 wt%
Loss tangent tanφ
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Materials
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Table 2 Damping capacity of the M2051/Al composites and conventional Al-matrix composites at room temperature.
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Highlights M2052 particle reinforced Al composites was prepared by accumulative roll bonding.
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Good bonding between uniformly distributed particles and matrix after 10 ARB cycles. Lower density of 2.9 g/cm3, just a little higher than that of pure Al.
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High damping capacity of 0.01 at 270K, 5 times that of pure Al.
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The UTS of 70 MPa, about 35% higher than that of pure Al, and the high TE of 24%.
S0925-8388(18)31789-4
DOI:
10.1016/j.jallcom.2018.05.104
Reference:
JALCOM 46077
To appear in:
Journal of Alloys and Compounds
Received Date: 20 January 2018 Revised Date:
7 May 2018
Accepted Date: 8 May 2018
Please cite this article as: Y.X. Gao, X.P. Wang, W.B. Jiang, J.F. Yang, L.F. Zeng, Q.F. Fang, High damping capacity and low density M2052/Al composites fabricated by accumulative roll bonding, Journal of Alloys and Compounds (2018), doi: 10.1016/j.jallcom.2018.05.104. This is a PDF file of an unedited manuscript that has been accepted for publication. As a service to our customers we are providing this early version of the manuscript. The manuscript will undergo copyediting, typesetting, and review of the resulting proof before it is published in its final form. Please note that during the production process errors may be discovered which could affect the content, and all legal disclaimers that apply to the journal pertain.
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High damping capacity and low density M2052/Al composites fabricated by accumulative roll bonding
a
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Y.X. Gao a, X.P. Wang a, W.B. Jiang a, J.F. Yang a , L.F. Zeng a, b, Q.F. Fang a, b Key Laboratory of Materials Physics, Institute of Solid State Physics, Chinese Academy of Sciences, Hefei 230031, China
University of Science and Technology of China, Hefei 230026, China
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b
Abstract
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High damping capacity and low density M2052/Al composites were successfully fabricated using the accumulative roll bonding (ARB) method, by taking advantages of high damping capacity for M2052 alloy (Mn-20Cu-5Ni-2Fe, at%) particles and excellent mechanical properties and low density for Al matrix. The 15 wt% M2052 particles were uniformly dispersed in Al-matrix after 10 ARB process cycles. M2052/Al composites have a low density of 2.9 g/cm3, which is just a little higher
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than that of Al. After ARB process and a subsequent hydrogen annealing, the M2052/Al composites exhibit both high room temperature damping capacity and good mechanical properties: the highest damping capacity is 0.01 at 270K, 5 times that of pure Al at the comparative temperature; the
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ultimate tensile strength is about 70 MPa (about 35% higher than that of pure Al), and the total elongation reaches 24%. The simultaneous enhancements on damping capacity and tensile strength
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of the M2052/Al composites can be attributed to the high damping capacity and the dispersion strengthening of M2052 phase, as well as the good bonding between the M2052 particles and Al matrix resulted from the ARB technique. Keywords: Al-matrix composites (AMCs), M2052 (Mn-20Cu-5Ni-2Fe, at%) alloy, Damping capacity, Low density alloy, Accumulative roll bonding (ARB).
Corresponding authors. QF Fang: [email protected]
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1 Introduction Aluminum and its alloys have attracted considerable interests because of their excellent mechanical properties and low density [1], and are widely used in fields such as aircraft, aerospace and defense applications. However, the low damping capacity [2-4] limits their engineering
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applications for controlling noise and suppressing mechanical vibration. In previous studies, Al-matrix composites (AMCs) were designed using hard particles like Al2O3, SiC, and TiB2 [5-10] as reinforcement phases, mainly to improve the strength of the composites. Although the damping capacity of the composites increases a little, owing to the thermal
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stress induced dislocations in Al matrix and the weak bonded interface between the matrix and reinforced particles [11], such increment is not high enough to meet the needs of application as high
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damping materials. Furthermore, the dislocation and interface mechanisms can only enhance the damping capacity of AMCs at temperatures higher than 200°C. On the other side, the weak bonded interface would seriously damage the mechanical properties of AMCs. As a result, in the traditional damping composites based on the motion of dislocations and interfaces in the matrix, the damping capacity was enhanced at a cost of decreasing the mechanical properties.
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Recently, a novel design concept to obtain the AMCs with both excellent mechanical properties and high damping capacities was suggested [12]. The main idea of this concept is to add some unique particles with superior intrinsic damping capacity into the Al matrix. In such designed
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composites, the damping capacity and mechanical properties can be enhanced simultaneously because the mechanism responsible for the damping (from the particle) is independent of the
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mechanism that controls the mechanical properties (from the matrix). Examples of such particles are graphite [13, 14], piezoelectric [15, 16] and lithium ionic electrolytes Li-La-M-O (M=Ta, Nb, Zr, Bi) particles [17-21], among which the Li-La-M-O ceramics exhibit the highest intrinsic damping capacity of 0.12 at room temperature. In order to obtain a strong interface between the matrix and additives, Li-La-M-O/Al composites were fabricated by accumulative roll bonding (ARB) methods for the first time in our lab with a high damping capacity of 0.01 (five times higher than that of pure Al) at room temperature [21]. More importantly, the total elongation to failure of the Li-La-M-O/Al composites fabricated by ARB can achieve 34% at room temperature. It has been evidenced that the ARB method is suitable for preparing particles reinforced metal based composites with full density, 2
ACCEPTED MANUSCRIPT uniform distribution of reinforcement particles in the matrix, and good bonding interfaces between additives and matrix [22-24]. Manganese-rich Mn-Cu alloys, especially for Mn-20Cu-5Ni-2Fe (atomic fraction, %, M2052) [25-27], have been developed for a good balance between the damping capacity, strength and
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workability. The M2052 alloys exhibit a large damping peak extending in a wide temperature range from 223K to 348K. However the high density (>7.8 g/cm3) of M2052 alloys limits their large-scale application in aerospace fields.
Therefore, in this paper the novel M2052 particulate reinforced Al composites was fabricated by
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the ARB method, in order to simultaneously achieve low density, high damping capacity, high strength and good ductility. The microstructures, dispersion of Mn-Cu alloy particles, mechanical
enhancement was discussed.
2 Experimental methods
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and damping properties of the composites were characterized and the mechanism for property
2.1 Design concept of M2052 particles reinforced AMCs
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Theoretically, the corresponding microscopic mechanisms of high damping capacity of materials are generally associated with stress induced movement of crystalline defects in materials. Such defects includes point defects, dislocations and planar defects (twin boundaries and magnetic
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domain boundaries), among which, the planar defects give rise to the highest damping capacity per unit concentration and are usually chosen as the major damping source in the engineering design [11].
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The high damping of the M2052 (Mn-20Cu-5Ni-2Fe, at%) alloys is just originated from the twin boundaries relaxation in its martensitic phase. Combined the high intrinsic damping capacity of M2052 powders with the good mechanical properties of Al-matrix and followed the novel design concept of high damping composites [12], a new kind of M2052/Al-matrix composites simultaneously achieving high damping and excellent mechanical properties was designed, where the main mechanism responsible for the energy dissipation (from the twin boundaries relaxation in M2052 particles) is independent of the main mechanism that controls the mechanical properties (from the Al matrix). 2.2 ARB fabrication of M2052/Al composites 3
ACCEPTED MANUSCRIPT The raw materials were commercial 1A99-Al sheets (purity 99.99%, metallic base) and M2052 (Mn-20Cu-5Ni-2Fe, at%) alloy particles (high damping additive). The 1A99-Al sheets were cut into a size of 40mm×60mm×1mm. Before the roll-bonding process, the Al sheets were cleaned in acetone and subsequently scratched by wire brushing to remove the surface oxides and to promote bonding
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between Al sheets. After that, a thin layer of M2052 particles was sprayed on the Al sheet with ethyl alcohol as solvent. Then, two Al sheets covered with M2052 particles were stacked and fixed at both ends using a steel wire. The stacked Al sheets were roll-bonded with a reduction of 65% in thickness at room temperature, which is necessary for a good bonding between the neighboring Al layers with
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particles on the surface [28]. This initial roll-bonding step was designated as the 1st cycle. Finally, the well roll-bonded sheet was cut into two sheets, which were re-stacked and roll-bonded with 50%
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reduction in thickness with a similar surface treatment mentioned above, this step was designated as the 2nd cycle. In order to attain a uniform distribution of M2052 powders, the above ARB step was repeated until to the 10th cycles. A detailed schematic illustration of the ARB process was shown in Fig. 1. It was worthwhile to note that an intermittent annealing (673K for 2h) is necessary for Al sheets after two or three roll-bonded processes to avoid cracking. To evaluate the effect of the
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intermittent annealing atmosphere on the damping and mechanical properties of M2052/Al composites, the H2 and Ar gas with the purity of higher than 99.999% were used comparatively. At last, the well 10th ARB cycle processed sheet was annealed at 673K for 2 h in H2. Hereafter, in this
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work, the samples are named as M2025/Al-I(H)-L(H), M2052/Al-I(Ar)-L(H) and M2052/Al-I(H),
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which correspond to different annealing conditions as indicated in Table 1.
2.3 Experimental characterization The X-ray diffraction (XRD) technique was employed to characterize the phase of the produced M2052/Al composites after 10 ARB cycles at room temperature, by using Cu-Kα radiations in a scanning range from 20° to 90° with a step of 0.033°. The novel X-ray 3D microscopy system (micro CT) (NanoVoxel-2000, Sanying, China) was employed to characterize the distribution of M2052 particles in roll-bonded M2052/Al composites. The surface morphology and tensile fracture surface of M2052/Al composites were examined by field emission scanning electron microscope (SEM) (Sirion200, FEI, USA) equipped with an energy dispersive spectroscopy (EDS). The mechanical properties of M2052/Al composites were performed by using an Instron-5967 4
ACCEPTED MANUSCRIPT testing machine at room temperature with a constant speed of 0.06 mm/min, which corresponds to an initial strain rate of 2×10-4 s-1. The dog-bone-shaped tensile samples were cut from the M2052/Al composites in a size of 1.5 mm×1.7 mm in cross section and 5 mm in working length. All tensile specimens were mechanically polished before the tensile tests.
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The damping capacity of M2052/Al composite strips with a dimension of 20 mm×2 mm×1mm was measured on a computer-controlled inverted torsion pendulum under the forced-vibration mode. The measuring frequency of the pendulum was chosen as 0.5, 1, 2 and 4 Hz. The maximum strain
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amplitude was kept at 5×10-5 and the heating rate was maintained at 2K/min in all the experiments.
3 Results and discussion
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3.1 Microstructure analysis
The room temperature XRD patterns of the M2052 powders and 10 ARB processed M2052/Al composites are shown in Fig.2. It can be seen that only the pure Al and M2052 XRD diffraction peaks are detected in the composite sample, which demonstrates that after the continual annealing
other impurity phase.
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and ARB processing there is no reaction between the M2052 particles and Al-matrix and no any
Fig. 3 shows the cross section SEM micrographs of M2052/Al composites produced by 1st, 3rd and 10th ARB cycles. As can be seen in Fig. 3(a), after the first ARB cycle the M2052 particles
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cluster as a layer, which poorly bonded with the two neighboring Al layers. As expected, with the increasing cycle number of the ARB process, the M2052 particles would be dispersed more and more
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uniformly in the bulk of the aluminum matrix. This is true because after 3rd ARB cycles, the M2052 layers are fractured into small clusters as shown in Fig 3(b). After 10 ARB cycles, a homogeneous dispersion of M2052 particles in Al matrix was achieved as shown in Fig. 3(c). In the case of 10 ARB cycles, the number of Al layers would be 2×29 and the layer thickness is only about 980 nm, if the Al layers could be distinguishable. This means that the hard M2052 particles with a size of 10µm would definitely penetrate these Al nano-layers during the ARB process and redistribute more homogeneously in the Al-matrix. It is easier to establish a good bonded interface between M2052 particles and Al matrix because of the similar metallic features than in the case of ceramics/Al composites. 5
ACCEPTED MANUSCRIPT The macro-view of the 10 ARB processed M2052/Al composites is also shown in the lower part of Fig.3(c). The size of the sample depends on the primary size of the 1A99-Al sheet and the thickness reduction of the roll-bonded process. Based on the concept of designing low density and high damping composites, M2052 alloy particles are added as the damping phase into Al matrix with
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a mass fraction of 15 wt%, corresponding to a density of 2.9 g/cm3. The density of M2052/Al composites is much lower than that of M2052 alloys (7.8 g/cm3) and only a little higher than that of pure Al (2.7 g/cm3).
Fig. 4(a) shows the surface morphology of M2052/Al composites after 10 ARB cycles. It can be
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seen that the reinforcement particles size is about 10µm, and the line scanning EDS spectra of M2052/Al composites shown in the upper part of Fig. 4(a) indicate that these particles are Mn-Cu
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alloy phase because the Mn and Cu signals are all detected simultaneously. Fig. 4(b) shows the X-ray 3D image of M2052/Al composites after 10 ARB cycles, in which M2052 particles are indicated by the yellow dots. It can be seen that in a macroscopic region, the M2052 particles are well uniformly distributed in Al-matrix with very few regions of particle clustering, which provides further evidence
3.2 Damping performance
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for forming a uniform distribution of M2052 particles in AMCs after 10 ARB process.
3.2.1 Internal friction test principle
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An inverted torsion pendulum for the internal friction test is schematically shown in Fig. 5(a), where a permanent magnet is fixed on the upper part of the pendulum, and two excitation coils (drive coils) are installed at the corresponding horizontal position. The sample is installed between the
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movable upper rod and the fixed bottom supporter. During the internal friction test, a sinusoidal excitation signal generated by the computer is amplified and sent to the excitation coil. As a result, an alternating electromagnetic torque is generated, which acts on the magnet to force the sample to vibrate sinusoidally. The mirror installed on the upper rod reflects the light to the photoelectric displacement sensor, which generates the strain signals of the sample. After amplification, the strain signal of the sample is sent to the computer and compared with the stress signal (excitation signal). According to the definition of the internal friction (Q-1), we have 1 ∆W Q −1 = 2π W
(1)
Where ∆W is the dissipated energy per unit volume in one vibration cycle, and W is the maximum 6
ACCEPTED MANUSCRIPT stored energy per unit volume. For the forced vibration test mode, by comparing the stress and strain signals of the sample, the phase difference (loss angle) ϕ by which the strain lags behind the stress, can be obtained, and the internal friction can be written as Q −1 = tan ϕ
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(2)
3.2.2 Damping capacity of the M2052 alloys and M2052/Al composites
Fig. 5(b) and (c) show the temperature dependence of internal friction (Q-1) for M2052 alloys
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before and after the annealing at 673K in H2, respectively, where two damping peaks can be detected. The main-peak at about 270K shifts to higher temperature with the increasing frequency, and is
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associated with the relaxation process of the twin boundaries in the face-centered tetragonal (fct) phase. The other small sub-peak at about 333K is frequency-independent, and corresponds to the martensitic phase transformation (fct↔face-centered cubic (fcc)) [27]. The annealing at 673K in hydrogen in this investigation will promote the spinodal decomposition to form the Mn-rich and Cu-rich phases from the fcc γ-MnCu solid solution [25] and the fct phase (a kind of martensitic
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phase) are formed from the Mn-rich phase via martensitic transformation. Therefore, the annealing at 673K in hydrogen is important to obtain a high density of twin boundaries which give rise to high damping of M2052 alloys. As a result, the internal friction values of the main peak for hydrogen annealed M2052 alloy (Fig. 5(b)) are higher than that for the un-annealed M2052 alloy (Fig. 5(c)),
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because the twin boundaries and hydrogen are both indispensable prerequisites for the appearance of the twin boundaries relaxation peak, as evidenced in the shape memory alloys such as Ti-Ni-Fe,
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Ti-Ni-Pd, Ti-Pd, Mn-Cu, Au-Cd, and Cu-Al-Ni [29]. Fig.6 shows the internal friction of M2052/Al-I(H)-L(H) sample as a function of temperature at different measurement frequencies. It can be seen that a prominent damping peak located around 270K is observed in M2052/Al composites, which shifts also to higher temperature with increasing frequency. It is noted that the damping peak of martensitic transformation at about 333K is absent in the composite because of its low damping level when combined with the Al-matrix. The peak position (~270K) and peak shift trend with frequency in M2052/Al composite is consistent with the results of pure M2052 alloy as shown in Fig. 5(c), which implying that this peak is the same one in the pure M2052 alloys. On the other side, in the ARB prepared M2052/Al 7
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interfaces, which is helpful to activate the damping mechanism in the M2052 particles. Because the damping capacity of Al-matrix is very low (10-3), it is clear that this damping enhancement of M2052/Al composite is mainly attributed to the addition of the M2052 particles and the dominant damping mechanisms of M2052/Al composite is originated from the motion of twin boundaries in
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M2052 martensitic phase.
In addition, the damping capacity of the present ARB M2052/Al composite was compared with
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values of the conventional Al-matrix composites, as listed in Table 2 [8, 10, 12, 21, 30, 31]. It can be seen that using M2052 powders as additives can effectively improve the room temperature damping capacity of the Al-matrix composites comparing with that by adding the conventional additive powders, such as Al2O3, SiC, TiB2, graphite, etc., in which the dislocation and interface mechanisms can only enhance the damping capacity of Al-matrix composites at temperatures higher than 200oC.
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Such an enhancement of damping capacity of M2052/Al composites in the lower temperature region is very important for the practical application of such a novel M2052/Al composites. In addition, as shown in Fig. 6, the high damping capacity (>7.5×10-3) of M2052/Al composites extends in a wide temperature range because of its twin-boundary relaxation mechanisms in M2052 phase, however for
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Li-La-M-O (M=Ta, Nb, Zr, Bi)/Al composites, the high damping (>7.5×10-3) distributes in a narrower temperature range, which is associated with the point defects relaxation [21].
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In Fig.7 the internal friction of M2052/Al-I(H) and M2052/Al-I(H)-L(H) samples at 1 Hz as a function of temperature was compared, where the result of the annealed pure Al is also presented as a comparison. The results indicate that the room temperature damping capacity of annealed pure Al is as low as 0.002. However, the damping capacity (Q-1) of both M2052/Al-I(H) and M2052/Al-I(H)-L(H) samples at 1Hz is 3-5 times that of pure Al at the comparative temperature. This enhancement of damping capacity mainly results from the addition of damping phase M2052. Meanwhile, it also benefits from the uniform dispersion of M2052 alloy particles, elimination of micro-pores and the well bonding interface between the damping phase and the Al-matrix resulted from the ARB processing, as shown in Fig.3(c) and 4(a). In addition, as expected, 8
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Fig.8 shows the internal friction of M2052/Al-I(H)-L(H) and M2052/Al-I(Ar)-L(H) samples at 1Hz as a function of temperature. The results indicate that the peak height (0.008) at 270K at 1Hz of M2052/Al-I(Ar)-L(H) sample is a little lower than that (0.01) of M2052/Al-I(H)-L(H). To understand this phenomenon, the room temperature XRD pattern of the M2052/Al-I(Ar)-L(H) has
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been measured, as shown in the inset of Fig.8, where additional reflections corresponding to impurity phase of MnO2 (JCPDS: 01-0799) have been detected. This illustrates that a small amount of MnO2
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has been generated during the intermittent annealing in Ar because Mn are highly oxygenated, which as the second phase are distributed in the M2052/Al composites, including at the twin boundaries and grain boundaries of M2052 alloy and phase interfaces between M2052 and Al. Because the dominant high damping mechanism of M2052/Al composite is originated from the motion of twin boundaries in M2052 martensitic phase, the MnO2 impurities distributed at the twin boundaries will hinder the
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motion of the twin boundaries during the damping test process, and result in the decrease of damping values of relaxation peaks in the temperature range of 200K-300K for M2052/Al composites.
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3.3 Mechanical properties
The engineering tensile stress-strain curves of the M2052/Al-I(H), M2052/Al-I(H)-L(H) and M2052/Al-I(Ar)-L(H) samples are shown in Fig. 9, where the results of the pure annealed Al are also
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presented as a comparison. It can be seen that the M2052/Al-I(H) sample exhibits a high ultimate tensile strength (UTS) of 112 MPa and a low total tensile elongation to failure (TE) of 5%. After the last annealing in H2, although the UTS decreases significantly to 70 MPa, which is still about 35% higher than that of pure Al (52.0 MPa) as shown in Fig.9, the TE of the M2052/Al-I(H)-L(H) sample is improved significantly to 24% comparing with that of the M2052/Al-I(H) sample. Generally speaking, for the M2052/Al-I(H) sample, the deformation in the last ARB cycle may result in high density of dislocations and grain boundaries, which is responsible for the high UTS and low TE values. However for the M2052/Al-I(H)-L(H) sample, the last annealing process (673K for 2h in H2) definitely results in the full recrystallization of the Al matrix and decrease of the density of 9
ACCEPTED MANUSCRIPT dislocations and grain boundaries, which is the reason of UTS decline and TE increment. However, the UTS of the M2052/Al-I(H)-L(H) sample is still higher than that of pure Al because of the dispersion strengthening of the M2052 particles. Plenty of evenly distributed dimples in the cross section micrograph as shown in Fig. 9(b) indicate the ductile failure mode of the
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M2052/Al-I(H)-L(H) sample, which is consistent with the apparent increase in the TE (24%). A lot of M2052 alloy particles in the composites locate at the core of the dimples, which suggests that the shear ductile fracture begins at the interface of particles and matrix [32].
In addition, by comparing the results of the M2052/Al composites with the different intermittent
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annealing atmosphere of Ar and H2 as shown in Fig.9(a), it is noted that the Ar annealing results in a higher UTS of 83.8 MPa and a lower TE of 13%. The UTS enhancement of the M2052/Al-I(Ar)-L(H)
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4 Conclusions
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conditions.
In the present study, M2052/Al composites were successfully fabricated via the ARB process.
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All investigated M2052/Al composites after 10 ARB cycles show a uniform distribution of M2052 particles in Al-matrix and well bonding interfaces. The M2052/Al samples with intermittent and the
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last annealing in hydrogen exhibit the best comprehensive properties: the lower density of 2.9 g/cm3 (much lower than that of M2052 alloy); the high damping capacity of 0.01 at 270K, 5 times that of pure Al at the comparative temperature; the UTS value of 70 MPa, about 35% higher than that of pure Al; and the high TE of 24%. The M2052/Al samples with intermittent in argon and the last annealing in hydrogen exhibit a little lower damping capacity owing to the pinning down of twin boundaries by a few MnO2 impurities that formed in the intermittent annealing. Such MnO2 impurities result in at same time an enhancement of UTS and a decrease of TE due to the strengthening mechanism of second phase. All the enhanced properties of ARB prepared M2052/Al composites can be attributed to the full density, uniform distribution of particles and a good bonding 10
ACCEPTED MANUSCRIPT interface between M2052 particles and Al matrix. Such a high performance M2052/Al composites fabricated by ARB method could find promising application as damping materials for eliminating noise and reducing mechanical vibration. Furthermore, It is expected that if other commercial Al alloys, such as 6061Al and 2A14Al, were used to prepare M2052/metal (matrix) composites, better
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comprehensive properties would be obtained because such Al alloys have much better mechanical properties than the pure Al (1A99Al) [33].
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Acknowledgment
This work was supported by the National Natural Science Foundation of China [Grant Numbers
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11405203, 51771181 and 51502300]; and the CASHIPS Director’s fund [Grant Number YZJJ201703].
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Figures captions Fig. 1 Schematic illustration of the ARB process.
Fig. 2 The room temperature XRD patterns of the M2052 powders and 10 ARB cycles processed
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M2052/Al composites.
Fig. 3 The cross section SEM micrographs of M2052/Al composites after different ARB cycles of (a) 1, (b) 3, and (c) 10. Inset in (c): the macro-view of the 10 ARB cycles processed M2052/Al
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composites.
Fig. 4 (a) The surface morphology and line scanning EDS spectra of M2052/Al composites after 10 ARB cycles; (b) X-ray 3D image of M2052 particles dispersed in M2052/Al composites.
Fig. 5 (a) The schematic diagram of a torsion pendulum and internal friction (Q-1) as a function of
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temperature for the M2052 alloys (b) unannealed and (c) annealed at 673K in H2.
Fig. 6 Internal friction (Q-1) as a function of temperature at different frequencies for the sample of
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M2052/Al-I(H)-L(H).
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Fig. 7 Internal friction (Q-1) as a function of temperature at 1 Hz for samples of M2052/Al-I(H)-L(H), M2052/Al-I(H) and the annealed Al.
Fig. 8 Internal friction (Q-1) as a function of temperature for the samples of M2052/Al-I(H)-L(H) and M2052/Al-I(Ar)-L(H). Inset: The room temperature XRD patterns of M2052/Al-I(Ar)-L(H).
Fig. 9 (a) The engineering stress-strain curves of the 10 ARB cycles processed M2052/Al composites: M2052/Al-I(H), M2052/Al-I(H)-L(H), M2052/Al-I(Ar)-L(H) and the annealed pure Al; (b) SEM images of the fractured surface of M2052/Al-I(H)-L(H). 15
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Abbreviation
Annealing conditions
M2052/Al-I(H)-L(H)
M2052/Al composite with intermittent and the last annealing in H2
in H2
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M2052/Al composite with intermittent annealing in Ar and the last annealing M2052/Al-I(Ar)-L(H)
M2052/Al composite with intermittent annealing in H2 without the last M2052/Al-I(H)
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Reinforcement content
SiC/Al Al2O3/Al TiB2/Al Li6.25La3Zr1.75Nb0.25O12/ Al Graphite/Al2O3/Al
10 wt.%
f (Hz)
Ref.
0.004 0.003 0.005
1Hz 1Hz 1Hz
[8][12] [12] [30] [10]
0.009
1Hz
[21]
Graphite-3 vol% and Al2O3-10 vol.% 15 wt.%
0.009
5Hz
[31]
0.01
1Hz
Present work
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M2052/Al
11 vol.% 15 vol.% 5 wt%
Loss tangent tanφ
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Table 2 Damping capacity of the M2051/Al composites and conventional Al-matrix composites at room temperature.
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Highlights M2052 particle reinforced Al composites was prepared by accumulative roll bonding.
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Good bonding between uniformly distributed particles and matrix after 10 ARB cycles. Lower density of 2.9 g/cm3, just a little higher than that of pure Al.
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High damping capacity of 0.01 at 270K, 5 times that of pure Al.
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The UTS of 70 MPa, about 35% higher than that of pure Al, and the high TE of 24%.