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Review

Current Progress in Rheoforming of Wrought Aluminum Alloys: A Review

by
Gan Li
1,2,
Hongxing Lu
2,*,
Xiaogang Hu
1,
Feng Lin
2,
Xinwei Li
1 and
Qiang Zhu
1,*
1
Department of Mechanical and Energy Engineering, Southern University of Science and Technology, Shenzhen 518055, China
2
School of Innovation and Entrepreneurship, Southern University of Science and Technology, Shenzhen 518055, China
*
Authors to whom correspondence should be addressed.
Metals 2020, 10(2), 238; https://doi.org/10.3390/met10020238
Submission received: 31 December 2019 / Revised: 4 February 2020 / Accepted: 6 February 2020 / Published: 11 February 2020
(This article belongs to the Special Issue Net-Shape Die Casting of Semi-solid Alloys)
Browse Figures
Review Reports Versions Notes

Abstract

:
Semi-solid processing (SSP), including rheoforming and thixoforming, offers a promising opportunity to manufacture net-shaped parts with complex structure and excellent mechanical properties. Owing to its low cost and short process, rheoforming has been the subject of extensive study over the last two decades. The interest in the rheoforming of wrought aluminum alloys is progressively growing among both the research and industrial communities. This review starts with reviewing the recent efforts and advances on preparation of semi-solid slurry of wrought Al alloys, followed by discussing the correlation between microstructure and performance of these alloys. Finally, special attention is paid in the industrial application and the future trends of rheoforming of wrought aluminum alloys.

1. Introduction

Wrought aluminum alloys, as a class of pervasive structural materials, are broadly used in aerospace and automobile sectors due to their low density, high strength to weight ratio and natural availability [1,2,3,4]. Currently, most parts made of wrought aluminum alloys are fabricated by plastic forming and precision machining [5,6]. However, these traditional approaches usually remain a few issues in terms of cost, production efficiency and complex geometry, which restrict their wider applications seriously. Semi-solid processing (SSP), as a promising near net-shape forming method for the metallic materials, is a competitive technique to satisfy the increasing demand of parts with complex structure and excellent mechanical properties [7,8,9].
Generally, SSP is categorized into two routes: rheoforming, in which the alloy is controlled cooling to the semi-solid state and then injected into a die without an intermediate solidification step, and thixoforming, which involves reheating of solid billets to a semi-solid temperature range and followed by forming operation. Over the past two decades, an obvious trend can be found that rheoforming has been the subject of extensive study due to many merits, such as its lower cost and shorter process [10,11,12,13].
The key success and first step of rheoforming is to produce excellent semi-solid slurries with qualitied spheroidal microstructure and certain solid fraction as a feedstock, which play a critical role in properties of the final parts [14]. The unique slurry, which is temperature- and time-dependent, ensure the alloy manifest thixotropic behavior when sheared [15,16,17]. The practical result of this rheology is laminar, smooth die filling and hence the common defects found in conventional die casting can be easily averted, resulting in structural parts with excellent mechanical properties which can also undergo means of heat treatment [18,19,20,21,22]. Furthermore, lower processing temperature always leads to less solidification shrinkage, reducing thermal shock to the die and closer to net shape. On the other hand, in contrast to forging, complex products can be made in one shot with less cost. Therefore, SSP can benefit from both casting and forging.
At present, the most common Al alloys for rheoforming that have been applied practically are Al-Si cast alloys, especially the A356, A357 and 319s alloys [23,24,25]. However, the mechanical and some physical properties of these alloys are usually relatively poor, making it hard to fully fulfill the requirements of lightweight and low energy consumption. Hence, there is a strong drive to develop Al alloys with better properties, such as the 2xxx series, 6xxx series, and 7xxx series wrought aluminum alloys. In recent years, rheoforming of wrought Al alloys has attracted increasing interest and some progress has been achieved. Nevertheless, from the many technologies available, only a handful is able to produce parts that meet the demands of industrial applications.
Even though a series of review papers has been published on semi-solid processing of Al alloys [15,23,24,26,27,28,29,30,31,32,33,34,35,36], no comprehensive review about rheoforming of wrought Al alloys has been reported. This paper aims at reviewing the recent development of rheoforming of wrought aluminum alloys. In Section 2, recent efforts and advances on preparation of semi-solid slurry of wrought Al alloys are reviewed. The correlation of microstructure and properties of these alloys will be discussed in Section 3. In Section 4, special attention is paid in the industrial application, and the future trends and prospects of the rheoforming of wrought Al alloys are put forward in Section 5.

2. Slurry Preparation of Wrought Al Alloys

2.1. Possibility Analysis of Slurry Preparation

Slurry preparation is one of the most critical steps for rheoforming, and its primary goal is to prepare slurry with uniformly distributed fine globules. Considering that there is a controlled cooling from the liquid state to the liquid-solid region in the slurry preparation process, the solidification behaviors of the alloy wrought 7075 analyzed by Differential Scanning Calorimetry (DSC) under virous kinetic conditions (1, 5, 10, 15, 20 min/°C). The cast Al-Si alloy 319s was also analyzed for comparison between the two type of alloys. The measured DSC cooling curves of 7075 and 319s alloys are shown in Figure 1a,b. Three exothermic peaks (labeled peak 1, peak 2 and peak 3) can be evidently found in these curves. According to the thermodynamic simulation under the non-equilibrium Scheil model, the phase transformations are recognized and illustrated. It can be easily found that faster cooling rates lead to higher exothermic peaks. This is because the phase transformations at faster rate leads to less time to occur and always need more output of thermal energy, resulting in larger exothermic peaks. It can also be noted that a slight increase in semi-solid range is observed as the cooling rates increase.
As shown in Figure 1c,d, the liquid fraction versus temperature curves of 7075 and 319s at different cooling rates are calculated using tangent method based on the cooling curves. In addition, the variations in liquid fraction with temperature under Scheil model are also shown for reference. Generally, the “processing window” for rheoforming means that temperature interval for a certain liquid/solid fraction, and the prepared slurry with a solid fraction of 0.3~0.5 is suitable. The liquidus, solidus and rheofoming windows for 7075 and 319s alloys at different cooling rates and thermodynamic predictions are given in Table 1. As for 319s, the solidification range of 7075 also increases with increasing cooling rate, while the rheoforming window is relative stable in comparison with the change of the solidification range in both alloys. However, it is clear that there are an extremely narrow rheoforming window and time window for 7075 alloy, indicating that in order to obtain qualitied slurry, the solidification process should be controlled much more accurately than for the cast Al-Si 319s alloy.
According to the study by Tzimas and Zavalianglos [37], a key parameter to control the SSP has been initially proposed that the variation in liquid fraction with temperature dfL/dT of the alloy should be as low as possible to ensure the stability and reproducibility of the process. Lower values of dfL/dT lead to a smaller change of solid fraction sensitive to temperature change and hence the solid fraction is easier to control. Since the study by Tzimas, many authors have contributed to the development of the temperature sensitive of solid fraction. Liu et al. [38] established the famous and widely used criteria: a maximum temperature sensitive of 0.03 °C−1 to determine whether the process is stable. The temperature sensitive of the 7075 and 319s alloys are presented in Figure 1e,f. For the 319s alloy, all the temperature sensitivities between 0.3–0.5 solid fraction at different kinetic conditions and thermodynamic simulation are below this criterion, while the 319s alloy is a suitable alloy for semisolid processing. In contrast, the same results can be obtained at higher cooling rates (15–20 min·°C−1) for 7075 alloy while almost all the temperature sensitivities between 0.3–0.5 solid fraction at lower rates (1–10 min·°C−1) exceed 0.03 °C−1. Obviously, increasing the cooling rates improve the processability but with a shorter time window simultaneously (see Table 1).
On the other hand, very recently, the enthalpy sensitivity of liquid fraction has been suggested by Hu et al. [39] as a novel and effective criterion for assessing the semi-solid processability. Likewise, their results also indicated that the wrought alloys with higher enthalpy sensitivity are more difficult to be rheoformed than the cast alloys.
Figure 2 demonstrates the liquid fraction curves of some common wrought and Al-Si cast alloys used in rheoforming. Comparing the solidification routes and liquid fraction curves of wrought and cast alloys, it can be noted that there is a “knee” (eutectic point) at around 0.6 solid fraction for the cast Al-Si alloys, resulting from the presence of silicon (Si), to have a reminder for the slurry preparation. Virtually, adding silicon into the wrought alloys can not only depress the temperature sensitivity significantly and reduce solidification shrinkage, but also improve the flowability, but with an inevitable decrease in mechanical behaviors.
Surprisingly, inspired by the experiments by Curle et al. on rheocasting of Al-Si binary eutectic alloy [40], pure Al [41], Zhang and co-workers [42] found that rheoforming can occur even there is no theoretical temperature interval between the solidus and liquidus because of the kinetics of solidification. Accordingly, for the wrought alloys, ideal slurry in which the primary particles are fine, spherical, and uniformly dispersed in the matrix can also be prepared if the solidification process is strictly controlled in spite of their higher temperature and enthalpy sensitivity.

2.2. Methods of Slurry Preparation

In practice, the slurry was usually prepared in a container. If no measures are taken during the solidification process, and then strictly controlled, there will be a steep temperature gradient (i.e., a larger solid fraction difference) from the edge to the center along the radius because the exterior slurry is chilled by the container wall. That can result in more complex flow behavior and increased possibility of turbulence formation, which pose limitations on the performance of the parts. So far, based on diverse solidification conditions, around 30 kinds of methods for reducing the temperature difference during slurry preparation process have been developed. These methods can be divided into two main categories: agitation and non-agitation. In historical terms, it was generally acknowledged that only though the dendrite fragmentation can obtain slurry in the infancy stage of SSP development [43]. To achieve that many methods based on diverse agitation such as mechanical or electromagnetic stirring, were proposed to obtain semi-solid slurry with thixotropic structure. Subsequently, in the early 21st century, some researchers found that semi-solid structure of spherical primary alpha phase can also be prepared without breaking off dendrites. Several powerful methods were introduced, including new rheocasting (NRC) [44], continuous rheoconversion process (CRP) [43] and the semi-solid rheocasting (SSR) [45], etc. Essentially, both categories require numerous nuclei during the initial stage of solidification to obtain better stability of the growing spheroids in a semi-solid bath. If the grain density is not sufficiently high, the resulting structure is traditional coarse dendrites, unbecoming for rheoforming [46].
Among all the methods, only approximately a half of them have been used to prepare the slurry of wrought alloys. As listed in Table 2, the solid fraction (fs), the average particles diameter (APD) and the shape factor (SF) of the primary particles and the required time, as well as the mass of the liquid metal for some wrought alloys are presented and compared to those of cast alloys A356/A357 for different methods derived from literature. Almost all the methods can prepare good slurry with APD less than 100 μm and SF more than 0.5 within 1 min. In addition, with the same method, there is no obvious distinction between the wrought and cast alloys at a certain solid fraction in terms of shape factor, the average particles diameter and required time.
From a different perspective, most methods can prepare high-quality slurry while still demonstrating some common issues. Firstly, many methods have not been developed for making high solid fraction, which cannot show its great potential and obtain maximum benefits [47]. In high solid fraction rheoforming, the slurry commonly flows in a laminar manner, resulting in higher product quality with near porosity-free, faster cycle time and extended tool life [47,48]. The second problem, as displayed in Table 2, is that few of these methods is able to produce slurry with heavier mass (e.g., 3 kg) at one shot, which poses limitation on good combination between production efficiency and product weight. In fact, increasing the mass of the poured metal usually deteriorates the quality of the prepared slurry. Moreover, entrainment defects always formed during the slurry preparation, leading to parts with non-competitive mechanical properties [49]. In essential, slurry preparation is a melt treatment technology before forming and hence the slurry was easily involved in gas and oxide film in various ways [50]. For example, in some methods, such as SEED [51] or CSIP-RCS [52], the melt scours the channel or crucible intensely during pouring, causing entrainment defects. In addition, in some methods like LSPSF [53], SIM [54], and SCP [55], the melt flows through a certain length of pouring channel under the combination action of pouring and gravity while scouring the inner wall of the pouring channel intensely, leading to entrapment defects. These defects can also occur when the melt flowing out of the pouring channel is injected directly into the slurry collection crucible, mold cavity or injection chamber due to strong turbulence resulting from its high flow velocity.
In addition to these methods mentioned in Table 2, there are some other processes focusing on the rheoforming of wrought alloys, such as Cooling Slope (CS) [56], CSIR-RCS [57,58], and Enthalpy Compensation Process (ECP) [59,60], whereas no more details about the prepared slurry can be found in existed literatures. The addition of rare elements such as Sc, Zr is also effective in further refining the α-Al grains. For example, Zhao et al., [61] successfully prepared slurry of 7A04 alloy (a Chinese code) with 5 kg with the addition of Sc and Zr elements, which can generate large quantities of Al3(Zr, Sc) particles to act as good heterogeneous nucleants for α-Al grains, thus leading to finer microstructure. Interestingly, air-cooled stirring rod (ACSR) processing [62], a relatively novel method initially invented by Kang et al., that can produce excellent slurry with the solid fraction of 55% and the grain size of 15 μm and the shape factor of 0.86 in a short time. Unfortunately, this amazing method has not been used to wrought alloys.

2.3. Flow Behavior and Filling Capacity

In order to better utilize the rheoforming process, understanding the flow behavior and filling capacity of semi-solid slurry and molten alloy is required. Regarding the molten alloys, Flemings [85] showed that the flow stoppage a thin channel of an alloy is caused by broken dendrite accumulation near the tip when the solid fraction is at the critical solid fraction where the solid particles near the tip develop coherency or interlocking such that there was a sharp decrease in the viscosity and hence the flow is stopped, as illustrated in Figure 3a. Bäckerud et al. [86] suggested that dendrites start impinging and form a network that prevents further flow at a solid fraction of approximately 30 to 35 pct.
For the semi-solid slurry, on the other hand, microstructure characterizations show uniform dispersed primary solid particles of the slurry before and during the flow in the channel [64]. When the solid particles grow to the size and fraction that yield sufficiently high viscosity, the slurry front stops to flow. Figure 3b shows this flow behavior schematically. Rheological behavior experiments and fluidity test results illustrated that the 7075 Al slurries can flow quite well even at medium initial solid fractions [64,87,88]. The unique slurry containing fine and solid particles resulting in fine microstructure is in demand as an alternative to the coarse microstructure of conventional manufacturing. A comparison between the microstructure of the 7075 alloy developed by normal casting and rheoforming is shown in Figure 3c,d, respectively.
Furthermore, Wu’s group [89] asserted that the filling capacity of Al slurry has no significant difference with the molten alloy at the same injection condition, even though much lower than high Silicon containing Al alloys [90]. The fine and homogeneous microstructure of rheofomed 5052 Al parts can be obtained by optimizing the injection pressure and injection speed. Similar results have been reported for 7075 [91] and 7A04 [92] alloys.

3. Performance of Rheoformed Wrought Al Alloys

Essential to deal with rheoformed wrought alloys’ increasing popularity, the estimation of the feasibility of its use for structural parts through mechanical characterization is ever booming. The microstructural features resulting from unique slurry can potentially yield improved performance. However, the presence of defects from the process, especially for hot cracking, if not sufficiently regulated, may detrimentally affect the performance.
Compared with the Al-Si series alloys, the high strength Al alloys contain low-cost alloying elements (such as Cu, Zn, Mg, Mn) strictly chosen to engender complex strengthening phases during subsequent ageing. These elements usually bring about large solidification intervals of more than 130 °C, as shown in Figure 1c and Figure 2, thereby leading to hot tearing during the final stages of solidification due to material shrinkage, a challenging issue that has been hard to grapple with since the first age-hardenable alloy, namely duralumin, was introduced. Owing to the fine global grains and reduced shrinkage offered by the rheoforming, it has been proved that this kind of processing path can immensely minimize and even eliminate crack susceptibility for the wrought Al alloys. With the rapid advancements in rheoforming over the past two decades, massive experiments have been conducted to investigate the superior performance of rheoformed wrought alloys. This section will present a sequence of performance that have received researchers’ attention in the literature.

3.1. Mechanical Properties

3.1.1. Tensile Behavior

In recent years, rheoforming of wrought Al alloys was realized by a sound combination of slurry preparation and different forming paths, such as rolling, squeeze casting (SC) and high pressure die casting (HPDC). Guan et al., for instance, reported that the mechanical properties of rheoformed 2017 [93] and 6201 [94] Al alloys are comparable with conventionally wrought alloys.
The fine spheroidal microstructure and reduced defects resulting from rheoforming primarily leads to enhanced tensile strength and elongation in the as-fabricated condition. Qi et al. [73], for example, showed that compared with conventional HPDC, significantly enhanced tensile strength (543 MPa) and elongation (4.1%) of rheo-HPDC 7075 alloy after T6 heat treatment can be obtained because of the refinement of primary particles and reduction in porosity. Porosity is a destructive structural factor to any casting while the fine-grained structure contributes to an increase of yield strength due to the Hall-Petch effect. A relevant work by Li et al. [56], confirmed that rheo-squeeze casting can form defect-free 7075 part and its mechanical properties are close to forging after appropriate heat treatment. Also, Guo et al. [69] presented that the rheoforming leads to an enhanced increase in tensile strength and elongation of 7075 alloy in comparison with conventional casting because of the reduced occurrence of hot tearing, fine-grained structure as well as the increased relative density. Likewise, the noticeably enhanced mechanical properties resulting from the increased density and finer microstructure of rheoformed parts are also identified in 2xxx, 5xxx, and 6xxx series alloys. Nevertheless, the effect of microstructural features in their studies is not reported.
Chen et al. [95] demonstrated the effect of ultrasonic power on the average grain size and mechanical properties of 2024 alloy. With the increase of power, the mechanical properties increase while the grain size decreases gradually, as displayed in Figure 4. This correlation of grain size and properties is also confirmed by studies on Al-Si alloys [96]. In addition, in order to further minimize the defects and reduce the grain size of the rheoformed parts, the vacuum atmosphere [97] and grain refiner [57] can also be introduced.
In addition to the effect of reduced defects and fine primary α-Al grains, the effect of different alloying elements and secondary phases on the properties of rheoformed alloys were also investigated. Möller et al. [98], for instance, exploring the influences of Cu content and the (Mg + Si) content as well as the Mg:Si ratio on the mechanical properties of rheo-HPDC 6xxx series Al-Mg-Si-(Cu) alloys, noted that the addition of Cu and excess Si result in higher strength and hardness in both T4 and T6 conditions and a natural pre-ageing has a major effect on the subsequent T6 properties of 6xxx alloys. They concluded that the good combination of strength and ductility can be achieved for the 6063 alloy, which has the highest Mg:Si ratio and hence incipient melting during solution heat treatment is limited.
Regarding the influence of secondary phases, some experiments have been conducted to understand how the precipitation, distribution and shape of secondary phases contribute to the performance of rheoformed alloys. In general, the solidification of the melt in the rheoforming process always experiences two stages. Take rheo-HPDC as an example, the former solidification mainly occurs in slurry preparation, including rapid cooling, stirring or other ways, and then quick transfer to HPDC machine while the latter mainly occurs when the slurry enters the shot chamber and mold cavity during filling, as depicted in Figure 5. For example, Li et al. [70], after analyzing the solidification process of the rheoformed 2024 alloy, pointed that the second solidification can be divided into three stages: (1) the secondary primary (α2-Al) phase directly grows from the surface of the primary α-Al phase particles without renucleation, (2) independent nucleation and growth of α3-Al from residual liquid, and (3) eutectic reaction at the end.
Lü et al. [99] compared the morphology of brittle phase Mg2Si of 5052 alloy in the conventional squeeze casting (SC) samples and Rheo-SC samples, noting that some dendritic Mg2Si phase with a length of over 50 μm was concentrated on grain boundaries in the conventional SC samples, whereas in Rheo-SC sample the Mg2Si phase with Chinese-script morphology was uniformly distributed among the primary a-Al particles (Figure 6). The dendritic Mg2Si phase can reduce the tensile properties of the alloy, especially the elongation because it acts as stress raiser with poor ductility under a load. Furthermore, they also analyzed SEM images of the tensile fracture for the 5052 Al alloy formed by different process, and concluded that the fine and uniform microstructure of rheo-HPDC and rheo-SC samples led to better tensile behavior than traditional casting.
For the heat-treatable wrought alloys, such as 2xxx, 7xxx series alloys, heat treatment can further enhance their strength, as shown in Figure 7. According to Zhao [100], the solution heat treatment increased the ductility and ultimate tensile strength of non-defects rheo-HPDC 7050 part by 1000% and 76%, respectively. The conventional T6 heat treatment, on the other hand, provided the 7050 alloy with a peak strength at the expense of its elongation which dropped by 12% compared with T4 condition. Similarly, Li et al. [101] compared the effects of different heat treatment conditions on rheoformed 7075 alloy, concluded that T6 heat treatment can yield a compromise between the strength and ductility. Mahathaninwong et al [102], further investigating the effects of T6 condition on the microstructures and tensile behaviors of rheo-HPDC 7075 alloy, noticing that the higher strength can be contributed to the higher number density and finer precipitate size of η’ phase, which was regarded as the main hardening phase while early nucleation of η phase in higher aging temperature parts resulted in lower strength.
Despite having higher strength, the brittleness cannot be overlooked. It should be pointed that even after heat treatment, however, the elongation of rheoformed samples is normally quite lower while the strength can near and even exceed the strength targets of the forging alloys. Serious shrinkage porosity that cannot be eliminated after solution and aging treatment in the rheoformed samples is the main cause of the very low resultant elongation, as reported for the Al-Zn-Mg-Cu alloy [91]. Curle [57] also found the porosity in 6082-T6 and 7075-T6 samples caused by incipient melting during solution heat treatment have a negative effect on the elongation, suggesting that optimizing or redesigning the solution heat treatment procedure after determining the melting points of precipitated phase may be beneficial to improve the brittleness. Recent studies on 7050 alloy [100] confirmed their statement and the author proposed that further controlling impurity contents in the alloy would be profitable to the elongation and strength as the eutectic Si and Al7Cu2Fe phases still exist at grain boundaries as the fracture source after heat treatment.
On the other hand, the comparison of tensile and compressive behavior of rheoformed alloys is still lacking since investigating the compressive behavior of Al alloys is not generally common due to the material’s ductility. Such alloys usually buckle or barrel under compressive tests and the sample size can strongly affect the material’s response to compressive loading, complicating the analysis of the detected stress-strain curve.
Overall, it can be concluded that, owing to the unique microstructure of the rheoformed parts and short process, the rheoforming of wrought Al alloys offers the possibility of fabricating parts benefitting from enhanced strength, ductility, and low cost, concurrently. This combination of properties is an advantage unachievable using the conventional processing techniques.

3.1.2. Creep Resistance

An alloy’s creep resistance is a very important assessment factor of its time-dependent mechanical properties at elevated temperatures [111]. As for Al alloys, they are widely known to creep at around 200–300 °C. Contrary to the tensile behavior, creep resistance is normally enhanced for larger grain-sized materials. This is because the larger grain size depresses the diffusion rate and limits grain boundaries sliding, which are two phenomena critical for creep. For instance, a prominent enhancement in creep resistance of semi-solid processing A356 alloy in comparison with conventional casting was proved by ESGANDARI et al. [112], who noticed such improvement was contributed to the reduction in the stacking fault energy contributing from the significant dissolution of Mg in the α-Al phase.
Mahathaninwong et al. [113], also reported that although the mechanical response of the rheo-HPDC 7075-T6 Al alloy showed slightly inferior to the wrought counterpart at room temperature while its creep behavior was superior at 200 °C, concluding that slower precipitate coarsening of the rheoformed 7075-T6 Al alloy resulted in lower minimum creep rate and longer creep rupture time (Figure 8). As expected, creep resistance deteriorated as the testing temperature or the stress applied increased [114].
Even though the creep behavior of rheoformed wrought Al alloys has not attracted a lot of consideration previously, it is becoming more valuable now since they are progressively being employed in automobile and aerospace industries, where creep resistance is usually of general interest.

3.2. Thermal Conductivity

Investigations on the thermal conductivity of rheoformed Al alloys are more recent. It is generally acknowledged that the reduced porosity and increased density lead to better thermal conductivity, and hence the thermal conductivity of rheo-HPDC Al alloy is higher than that of HPDC. Similarly, internal work by the authors has demonstrated that the thermal conductivity of rheo-HPDC A357 samples are superior to conventionally HPDC sample. So far, several alloys with high thermal conductivity, including Al-8Si [13,115,116], Al-20Si [117], and Al-25Si [118,119,120], that are suitable for rheoforming have been developed. However, the thermal conductivity value of these Al-Si alloys is normally less than 180 W·m−1·K−1.
Interestingly, A test report on thermal conductivity by Wannasin et al. [121] showed exceptional thermal conductivity of rheoformed 6063 alloy after T6 treatment, in the order of 275 W·m−1·K−1, indicating an excellent combination of good mechanical property and superior thermal conductivity. That is because the Mg2Si phase can efficaciously increase the diffraction of electrons and hence reducing the average free path of electrons, resulting in satisfactory thermal conductivity. A comparation of thermal conductivity of some popular Al alloys widely used in electronic and communication industries is shown in Figure 9, indicating that rheoforming can observably improve the thermal conductivity, posing an impactful resolvent to remove excessive heat produced during the operation of equipment. Concomitantly, it is worth mentioning that the rheoformed wrought alloy with higher thermal conductivity is also a good conductor for electricity according to the Wiedemann-Franz law. Coupled with its density and price compared to copper (Cu), silver (Ag), and gold (Au), it is attractive for a range of electrical applications.

4. Industrial Application and Opportunities

In today’s manufacturing industry, it is undeniable that the rate of change and innovation is accelerating, leading to robust and sustained development [125,126]. In addition to the traditional incremental innovation, the radical innovation has become strategically significant and used as a source of competitive advantage in the global marketplace. In general, the real value of an innovation lies in practical effectuation. The rapid development of rheoforming is a typical example of the full spectrum of experiences involved in turning a “research idea” to a successful “commercial product”, particularly in the fields of automobile and communication [127,128,129].

4.1. Automobile Parts

In order to grapple with increasingly severe environmental and energy problems, the rheoformed wrought Al parts have gained more and more popularity in automobile industry due to wrought to weight ratio and low cost. Automobile parts such as shell parts, auto control arm parts, brake calipers or wheel hubs could have improved performance and production efficiency by rheoforming approaches. At present, the rheoforming of Al-Si alloys has been a broadly received industrial manufacturing path to produce high-quality automobile components. Notably, the rheoformed wrought Al alloy parts could provide further enhanced mechanical properties and better fatigue properties in dynamic applications, but low cast for load beating components. Rheoforming can manufacture near net-shape and good surface quality automobile parts thanks to the better mold-filling capacity and reduced shrinkage. As shown in Figure 10a, the outlines of the shell part of the 7075 alloy. As shown in Figure 10a, the outlines of the shell part are clearly discernible without obvious defects even though its edge is thin. Figure 10b,c display the color anodized wrought parts with good appearance, high surface quality and mechanical properties, indicating that these rheoformed wrought Al parts are satisfactory. The 2024 alloy frame-shaped part prepared by conventional and ultrasonic assisted conventional SC is displayed in Figure 10d and the thickness of the its thinnest part is only 4 mm. The contours of the part are clear without obvious defects, manifesting that the mold filling of the rheoforming process is well-pleasing. It should be attributed to the good flow behavior of the slurry and high forming pressure during SC. Therefore, it can be concluded that wrought Al parts with complex shape and thin wall could be fabricated by the rheoforming process.

4.2. Communication Parts

With the advent of the 5G era and the further upgrade of modern communication technology, the demand for communication parts with high thermal conductivity and good mechanical properties gradually grows. These communication components usually have multifarious shapes and sizes which are often highly customized for various applications. Furthermore, they always have complex structure with thin-wall shapes and hence they are often made of Al alloys because the parts must have both good mechanical properties and high efficiency for conducting heat concurrently. Rheoformed Al-Si parts can satisfy these meets in most cases, but the parts with further improved thermal conductivity and electroconductibility provided by wrought alloys are still highly desired. As shown in Figure 11, the telecom component fabricated by 6063Al RheoMetal with thin wall can reach 28.0 mΩ/m and 180 W·m−1·K−1 at 20 °C [116]. It confirmed that the rheoforming of wrought alloys can render the creation of unique microstructure, leading to better thermal and electrical properties than conventional cast alloys. Also, Li et al. [101] showed that rheoforming of high strength Al alloy 7075 is also suitable for fabricating thin-welled communication parts with complex internal structure and higher accuracy compared to traditional casting routes. The thickness of inner wall and external wall can reach 0.5 mm and 1 mm, respectively, while no defects were detected according to the X ray test.
On the other hand, anodizing of wrought Al alloy parts can improve the surface appearance and corrosion resistance, which can be used for decorative purposes, proposing another direction for the rheoformed wrought Al alloys [131,132]. For instance, the new generation smart phones provided by the world’s largest cell phone makers, such as Apple iPhone 11, HUAWEI P30 Pro, and SAMSUNG NOTE 10+, choose the wrought Al alloys as their frame due to not only lightweight and high mechanical properties, but also more choices of color.

5. Summary and Outlook

Rheoforming of wrought Al alloys is becoming more common—both on the research and industrial levels—with recent breakthroughs and efforts made in the field. This paper demonstrates a comprehensive review of recent progress on rheoforming of wrought Al alloys. The challenges and current advancements of the semi-solid slurry preparation have been identified and compared. In addition, the performance, advantages and industrial applications of rheoformed wrought Al alloys have been discussed.
From half a century of study on rheoforming, several benefits can be obtained in comparison with competivitive manufacturing routes, such as conventional HPDC, plastic forming, and even selective laser melting. However, rheoforming has not been seen as a common technology and its market is relatively limited. As a consequence, some confinement is required to direct the future study into the aspects that can better improve the standing of the technology. Several future trends and prospects are proposed, based on the existing papers about rheoforming and materials-science, as following:
(1) Alloys need to be designed for their processing route. Specific ‘wrought alloys’ and ‘cast alloys’ have been developed while so far research and development (R & D) on ‘rheoforming (or SSP) alloys’ are far from enough. Up until now, almost all the Al alloys used in rheoforming were developed for conventional manufacturing processes, especially the wrought alloys. Due to this, effective control during the slurry preparation is still poor, and the complete understanding of structure–property relationship to further enhance the mechanical properties of the final parts, are still to be realised. Therefore, besides the advances regarding the readily-available alloys, there is a strong drive to develop new and reliable alloys specifically for rheoforming for the process that take into account the process needs and the target properties concurrently. For example, there are various requirements for automotive industrial spplications, some need high strength, while some need high fatigue resistance, corrosion resistance and/or wear resistance. Different alloys systmes are needed to fulfill more requirements for industrial applications.
The common approaches to develop new alloys mostly relied on CALPHAD and targeted experiments [133,134,135,136], which can not develop a large number of suitable alloys rapidly. The Material Genomic technology such as materials’ design softwares and high-throughput methods to experimentally validate the candidate alloys are needed to exploit this capability effectively. This should aim at understanding the effect of the alloying constituents on the processability of the material by rheoforming and ultimately the properties of the fabricated parts in application. Additionally, over the past few years, artificial neural networks (ANN), as a powerful technology that has won numerous contests in pattern recognition and machine learning [137], has also achieved great success in designing new wrought alloys [138], as well as optimizing process parameters in SSP [139].
(2) As disscussed in Section 2.2, the current slurry prepration methods cannot prepare slurry with heavier mass and high solid fraction at a short time. Thus, it is of great importance to develop new methods that can improve the production efficiency and stability of slurry and subsequent forming. Furthermore, owing to the relative movement of liquid and solid phases under pressure forming, there is a certain degree of non-uniformity in the different positions of the larger parts, potentially causing the difference in the performance of the final parts. Accordingly, the performance of rheoformed parts currently is, on the whole, difficult to reach the same level of the forged parts, which is also one of the reasons why rheoforming is difficult to be widely used.
(3) The studies on the performance of rheoformed wrought Al alloy mainly focused on the tensile behavior, but less on the corrosion resistence, fatigue performance, wear resistence as well as mechanical properties at elevated temperature, which are very signifacant and proprobly a precious guide to the broader application of rheoforming in industries. For example, the tribological behavior of a part is of significant importance for applications in the automotive industry where a part can experience a significant amount of friction in the actual use. Hence, such properties need to be ulteriorly explored in future studies.
(4) The market, espcially the automotive industry is very exacting on price and lead time. With a continuous deep development of the artificial intelligence application technology, the highly integrated design and intelligent control of the rheoforming system is the shape of things to come. Special dies and moulds for rheoforming have been designed to enhance the mechanical properties while reducing the cost [140,141,142,143]. Moreover, even though the rheoforming of wrought Al alloy can offer considerable cost saving, high performance, and complex struture of parts, it is a quite long process to redesign a new part for rheofoming to replace the original product while meeting the acutual needs of industry, as displayed in Figure 12. Consequently, close cooperation between alloy and process developers and part users, and perseverance at the infancy stage of commercialization are highly needed to bring the rheoforming of wrought Al alloys to a commercially acceptable level.

Author Contributions

G.L. and F.L. prepared the manuscript under the supervision of Q.Z. and H.L.; X.H. and X.L. revised the manuscript. All authors contributed to the general discussion. All authors have read and agreed to the published version of the manuscript.

Funding

This work is financially supported by Shenzhen Science and Technology Innovation Commission (Projects JCYJ20170817110144233, KQTD20170328154443162), National Natural Science and Foundation of China (Grant No. 51805238).

Acknowledgments

The authors would like to thank Cheng Le for his great assistance in DSC experiments.

Conflicts of Interest

The authors declare no conflict of interest.

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Figure 1. Measured DSC signal of 7075 (a) and 319s (b) alloys at different cooling rates, calculated liquid fraction curves of 7075 (c) and 319s (d) alloys, the temperature sensitivity of 7075 (e) and 319s (f) alloys.
Figure 1. Measured DSC signal of 7075 (a) and 319s (b) alloys at different cooling rates, calculated liquid fraction curves of 7075 (c) and 319s (d) alloys, the temperature sensitivity of 7075 (e) and 319s (f) alloys.
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Figure 2. The liquid fraction curves based on the results of numerical simulaiton for some common aluminum alloys employed in rheoforming (Thermo-Calc 2019a software under the Scheil model).
Figure 2. The liquid fraction curves based on the results of numerical simulaiton for some common aluminum alloys employed in rheoforming (Thermo-Calc 2019a software under the Scheil model).
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Figure 3. Diagrams of the flow state in a thin channel of (a) liquid metal [85] and (b) semi-solid slurry [64]. Microstructure of 7075 Al alloy fabricated by (c) conventional casting and (d) rheocasting [73], with permission from Elsevier, 2019.
Figure 3. Diagrams of the flow state in a thin channel of (a) liquid metal [85] and (b) semi-solid slurry [64]. Microstructure of 7075 Al alloy fabricated by (c) conventional casting and (d) rheocasting [73], with permission from Elsevier, 2019.
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Figure 4. (a) Average grain size and (b) tensile mechanical properties of 2024 aluminum parts prepared by ultrasonic assisted casting [89], with permission from Elsevier, 2019.
Figure 4. (a) Average grain size and (b) tensile mechanical properties of 2024 aluminum parts prepared by ultrasonic assisted casting [89], with permission from Elsevier, 2019.
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Figure 5. Typical solidification process of the rheo-HPDC (solid line) process and conventional HPDC process (dotted line).
Figure 5. Typical solidification process of the rheo-HPDC (solid line) process and conventional HPDC process (dotted line).
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Figure 6. SEM images showing the morphology of Mg2Si phase in (a) conventional SC and (b) rheo-SC 5052 Al parts [83].
Figure 6. SEM images showing the morphology of Mg2Si phase in (a) conventional SC and (b) rheo-SC 5052 Al parts [83].
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Figure 7. Comparation of tensile behaviors of some wrought Al alloys and A356 alloy fabricated by conventional casting and rheoforming in the as-fabricated and heat-treated condition [56,57,69,70,73,78,79,91,95,102,103,104,105,106,107,108,109,110].
Figure 7. Comparation of tensile behaviors of some wrought Al alloys and A356 alloy fabricated by conventional casting and rheoforming in the as-fabricated and heat-treated condition [56,57,69,70,73,78,79,91,95,102,103,104,105,106,107,108,109,110].
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Figure 8. (a) The stress dependence of minimum creep rate and (b) creep rupture time [107], with permission from Elsevier, 2019.
Figure 8. (a) The stress dependence of minimum creep rate and (b) creep rupture time [107], with permission from Elsevier, 2019.
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Figure 9. Thermal conductivity of some common Al alloys fabricated by conventional casting and rheoforming [115,116,120,121,122,123,124].
Figure 9. Thermal conductivity of some common Al alloys fabricated by conventional casting and rheoforming [115,116,120,121,122,123,124].
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Figure 10. (a) 7075 Al shell part farbricated by the FCR [73], with permission from Elsevier, 2019. (b) Color anodized 7075 brake caliper parts and (c) gear fabricated by GISS [121]. (d) 2024 Al frame-shaped part fabricated by UV [95], with permission from Elsevier, 2019.
Figure 10. (a) 7075 Al shell part farbricated by the FCR [73], with permission from Elsevier, 2019. (b) Color anodized 7075 brake caliper parts and (c) gear fabricated by GISS [121]. (d) 2024 Al frame-shaped part fabricated by UV [95], with permission from Elsevier, 2019.
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Figure 11. 6063 Al telecom part farbricated by the RheoMetal [130].
Figure 11. 6063 Al telecom part farbricated by the RheoMetal [130].
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Figure 12. Flow chart of designing a new part for rheofoming to replace the original product.
Figure 12. Flow chart of designing a new part for rheofoming to replace the original product.
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Table
Table 1. Rheoforming windows and solidification ranges for the 7075 and 319s alloys.
Table 1. Rheoforming windows and solidification ranges for the 7075 and 319s alloys.
AlloyCooling RateSolidusLiquidusSolidification RangeRheoforming WindowTime Window
(°C/s)(°C)(°C)(°C)(°C)(s)
7075Scheil461.3630.316910.9-
1-644.7-4.6276
5478.6634.8156.25.566
10470.9633.5162.66.539
15464.5627.4162.95.536
20463.0626.5163.57.923.7
319sScheil508.4611.5103.126.1-
1498.0609.9111.919.61176
5494.8612.4117.622.8273.6
10492.1609.6117.523.6141.6
15490.6609.4118.822.188.4
20489.3608.4119.122.467.2
Table
Table 2. Statistics of fraction solid, particle size, shape factor, preparation time and mass of slurry of some cast and wrought alloys prepared by different method.
Table 2. Statistics of fraction solid, particle size, shape factor, preparation time and mass of slurry of some cast and wrought alloys prepared by different method.
ProcessAffiliation (Country)AlloyFs (%)Dp (μm)SFTimeMass
1 Gas Induced Semi-solid (GISS)Massachusetts Institute of Technology (USA)A356 [63]0–14.67.3–68.40.79–0.735–45 s2 kg
7075 [64]13.3–27.229.3–44.7-5–20 s1 kg
2 Swirled Enthalpy Equilibration Device (SEED)Aluminum Company of Canada (Canada)A356 [51]30–4570–110-30–60 s1–6 kg
7075 [65]45106.650.61-1 kg
7108 [66]~55800-~220 s2.3 kg
3 Indirect Ultrasonic Vibration (IUV)Huazhong University of Sci. & Tech. (China)A356 [67]22.2740.6250 s~450 g
5083 [68]25600.5450 s~450 g
4 Low Superheat Pouring with a Shear Field (LSPSF)Nanchang University (China)A356 [53]41650.84--
2024 [69]55730.79~25 s1.5 kg
7075 [70]~3620.78--
5 Self-inoculation method (SIM)Lanzhou University of Technology (China)A356 [54]2754.580.753 min-
2024 [71]~2570.80.763 min-
6061 [72]40760.85 min-
6 Forced convection stirring (FCS)University of Sci. & Tech. Beijing (China)7075 [73]-770.7630 s2 kg
7075 [74]-640.8815 s5.3 kg
7 Inverted Cone-Shaped Pouring ChannelUniversity of Sci. & Tech. Beijing (China)7075 [75]~15600.86~1 min-
7075 [76]46780.85--
8 Annular Electromagnetic Stirring (A-EMS)General Research Institute for NonferrousA357 [77]-44-10 s-
Metals (China)7075 [78]-490.51--
9 Serpentine Channel Pouring (SCP)University of Sci. & Tech. Beijing (China)A356 [55]~15500.8910 s3.5 kg
7075 [79]~20640.784 s1.6 kg
10 Pulsed magnetic field process (PMF)Nanchang Hangkong University (China)A356 [80]~20790.584 min600 g
2024 [81]-780.6-~1 kg
11 Rheo-diecasting process (RDC)Brunel University (UK)A357 [82]42410.8730 s-
2014 [82]-50-30 s-
12 Rotate Casting MethodHarbin Institute of Technology (China)7A09 [83]-520.67--
13 A self-developed stirring methodFerdowsi University of Mashhad (Iran)2024 [84]30460.77-350 g

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Li, G.; Lu, H.; Hu, X.; Lin, F.; Li, X.; Zhu, Q. Current Progress in Rheoforming of Wrought Aluminum Alloys: A Review. Metals 2020, 10, 238. https://doi.org/10.3390/met10020238

AMA Style

Li G, Lu H, Hu X, Lin F, Li X, Zhu Q. Current Progress in Rheoforming of Wrought Aluminum Alloys: A Review. Metals. 2020; 10(2):238. https://doi.org/10.3390/met10020238

Chicago/Turabian Style

Li, Gan, Hongxing Lu, Xiaogang Hu, Feng Lin, Xinwei Li, and Qiang Zhu. 2020. "Current Progress in Rheoforming of Wrought Aluminum Alloys: A Review" Metals 10, no. 2: 238. https://doi.org/10.3390/met10020238

APA Style

Li, G., Lu, H., Hu, X., Lin, F., Li, X., & Zhu, Q. (2020). Current Progress in Rheoforming of Wrought Aluminum Alloys: A Review. Metals, 10(2), 238. https://doi.org/10.3390/met10020238

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