Recycling Aluminium AA6061 Chips with Reinforced Boron Carbide (B₄C) and Zirconia (ZrO₂) Particles via Hot Extrusion

Abstract

Compared to the recycling process by remelting, hot extrusion significantly reduces the energy consumption and CO₂ emission and ensures good mechanical and microstructural properties. This study investigates the effects of reinforcing aluminium AA6061 chips with mixed boron carbide (B₄C) and zirconia (ZrO₂) particles by employing a design of experiment (DOE) under 550 °C processing temperature and three hours preheating time. The findings showed that compressive strength (CS) and hardness increased with up to 5% added particles, and beyond 5%, the yielded values decreased because of materials agglomeration. However, the decreasing density was dependent on the addition of ZrO₂ particles. The distribution of particles with different volume fractions of mixed particles was investigated by employing SEM, AFM, and EDS tests. Thus, the process can produce a net shape structure that utilises material-bonding consolidation to provide sufficient support to reuse the recovered materials in engineering applications, such as in the automotive industry.

1. Introduction

Due to its good combination of characteristics, such as light weight, high strength, and excellent resistance to corrosion, aluminium alloy has been widely utilised in transportation, construction, containers, power supply, and many related applications [1,2,3,4,5]. One efficient way to reduce emissions, such as CO₂, CO, and NOx, during the manufacturing process is to recycle waste materials with less energy consumption. Recycling industrial aluminium wastes also becomes a vital approach for manufacturers to reduce production costs [1]. Traditional recycling methods for aluminium scraps mostly involve remelting and recasting at high-energy usage. However, solid-state recycling (SSR) by forming techniques has been developed to reduce energy consumption during recycling. In this approach, the alloy scraps will undergo plastic deformation below solidus temperature [2]. SSR is a superior concept among light-metal recycling due to its high material recovery and fewer processing steps. The direct conversion process of aluminium machining chips into a finished product by the hot extrusion process was patented by Stern in 1945 to overcome the problem of material loss during the remelting process and reduce energy usage during aluminium production [3]. The SSR by hot extrusion resulted in high strength enhancement of the processed chips due to severe deformation induced during extrusion [6,7,8]. In addition, SSR by hot extrusion could be cost effective compared to other conventional concepts of material recovery, saving 40% of materials, 31% of energy, and 60% of labour [9,10].

Generally, the performance of the extrudes can be affected by die design, extrusion temperature, and extrusion speed (strain rate) [11,12,13,14]. Güley et al. [15] investigated the effect of the die design on the welding quality of the machining chips. The flat-face die and porthole die were employed to produce solid rectangular profiles using AA6060 chips. It was found that the porthole die resulted in better-welded chips, having 80% higher ductility than the flat-face die. Blindheim et al. [16] investigated the continuous extrusion of aluminium alloys via solid-state-bonding extrusion. The process was operated at a temperature lower than the material-melting point to avoid cracking and residual stresses compared to the conventional melting process. Some studies focused on recycling machined chips in hybrid forms reinforced with ceramic particles and compacted in cylindrical bars using the hot extrusion method. Sanusi et al. [17] reported the effects of processing temperature and reinforced particles on the Cu alloy composite structure and properties. Rezaei et al. [18] found that the processing temperature (ranging from room temperature to crystallisation temperature) directly affects the structural properties of Al-Cu-Ti extruded composites. The applied temperature affects the particle distribution and grain size. Higher temperature leads to increased density, hardness, and yield strength. Zhou et al. [19] also reported that increasing the processing temperature improved the distribution of the grains and particles of Mg-Al-1Si alloys. The mechanical properties of the materials were optimum at 330 °C due to the homogenous particle distribution and fine grain size. Nie et al. [20] studied the hot extrusion of 2024 aluminium chips reinforced with boron carbide (B₄C) particulates and found that the elastic modulus and ultimate tensile strength (UTS) of the extrudates were increased by adding B₄C particles into the matrix alloy. The highest UTS value for B₄C/AA2024 composites was 626.7 MPa at 20 vol% B₄C particles, compared to 489 MPa for pure 2024 aluminium alloy. Additionally, a strong interface bonding between B₄C and AA2024 was achieved through mechanical alloying and hot extrusion. Fogagnolo et al. [21] studied the recycling of AA6061 chips reinforced with Al₂O₃ using cold and hot pressing followed by a hot extrusion process. The authors found that the UTS and hardness of the recycled composite material were higher than the primary material producing the chips. Sabbar et al. [10] reviewed the processing of aluminium chips by hot extrusion with and without reinforcing particles. The researcher found that adding reinforced particles has an impact on the material structure and strength properties. Qi et al. [22] investigated the processing of AA6061-T651 commercial alloy by cyclic extrusion process. The electrical conductivity of the processed material increased by 10%, while the hardness slightly dropped. Larianovsky et al. [23] studied the production of Al metal matrix composites reinforced with carbon nanotubes using combined high-pressure die casting (HPDC) and cyclic extrusion (CE). More than 50% efficiency was achieved, and the resulting composites demonstrated improved mechanical properties.

The investigations of aluminium-alloy-based scraps in the pure or composite form are important for reuse of the materials in automotive and aircraft applications [24,25]. AA6061 reinforced with ceramic particles have been widely used in the automotive industry and AA7075 in the aerospace industry. This paper investigated the possibility of recycling aluminium alloy 6061 chips reinforced with B₄C and ZrO₂ particles via hot extrusion. The effects of B₄C and ZrO₂ on the UTS, microhardness, density, and microstructure of the extrudates were studied in detail. The findings will highlight the development of chip-based recycling with multi-reinforced particles towards recycling hybrid material structures.

2. Materials and Methods

2.1. Preparation of the Al6061-B₄C/ZrO₂ Composites

The AA6061-B₄C/ZrO₂ composites were made from AA6061-pulverised chips and B₄C, ZrO₂ ceramic particles. Then, the chips underwent a cleaning process by degreasing with acetone for 30 min in an ultrasonic bath, according to the ASTM G131-96 standard. After cleaning, the chips were dried in an oven at 100 °C for 30 min. Finally, the chips were mixed with B₄C, ZrO₂ particles using a 3D mixer for 2 h at the speed of 35 rpm.

Table 1. Process parameters for preparing the Al6061-B₄C/ZrO₂ composites and the subsequent hot extrusion process.

Parameters	Units	Values
Chips size	mm	1
B4C, ZrO2 size	µm	7 ± 3
Mixing time	hr	2
Mixing speed	rpm	35
Drying temperature	°C	100
Billet preheated temperature	°C	550
Billet preheated time	hr	3
Extrusion die temperature	°C	300

summarises the process parameters for preparing the Al6061-B₄C/ZrO₂ composites. The mixing was performed to ensure the distributions between the hybrid materials were uniform. The process depends on the density measurements of both alloys and ceramic constituents. The density of the hybrid materials was determined using the Archimedes’ principle, which depends on the densities and volume fractions of the reinforced B₄C, ZrO₂ particles and the AA6061 metal matrix [10,26,27].

2.2. Hot-Extrusion Experiment

The direct conversion process of aluminium-machining chips reinforced with B₄C and ZrO₂ particles into a finished product by the hot extrusion process will improve the energy usage of the aluminium production compared with the remelting process. The extrusion process parameters are given in Table 1. The chip-based hybrid reinforced by B₄C and ZrO₂ particles were developed by mixing and blending the chips with the reinforced particles. The composite was cold compacted to produce the billet of 80 mm in length and 30 mm in diameter. After cold compaction, the billet was homogenized in a furnace at 550 °C for 3 h. Subsequently, the hot extrusion of the chip-based composite in the form of a billet was conducted on a hydraulic extrusion press with a maximum extrusion force of 300 tonnes. The billet was preheated to 550 °C to increase the material ductility and deformability. The extrusion die temperature was set at 300 °C. The ram speed was set to 1 mm/s. Each of the extruded profiles were machined by following the ASTM E9 standard to produce the samples for the compressive strength test, carried out with an initial strain rate of 2.53 × 10⁻³ s⁻¹ at room temperature. Figure 1 summarises the experimental methods for material preparation and characterisation.

2.3. Material Characterisation

The extruded samples were prepared following ASTM E9-09 for test of compressive strength. The density of the material was investigated and measured in the air and distilled water by employing Archimedes’ principle. The investigated reinforced particles distribution, chips boundaries, and grains properties were characterised by AFM XE-100 (PSIA Corp., Sungnam, Korea) and SEM (Model No: JEOL JSM-6380la MP-19500014). Energy–dispersive X-ray spectroscopy (EDS) was conducted to investigate the distribution of the recycled composite elements.

Furthermore, microhardness investigations were conducted with a force of 0.980 N for 10 s of holding time following DIN EN ISO 6507-1:2005 standards. Five different points were measured and the uniformity of the formed materials and the mean microhardness values were recorded. The samples preparation involved sectioning, grinding, polishing, and etching. The process allowed the hybrid samples to dissolve the elevated particles above the samples and over a cleaned and dried surface to attain excellent microstructure findings. The tip of the AFM probe was very sharp, usually less than 100 Å in diameter at the end of a small cantilever. The probe was connected to a piezo scanner tube, which scanned the probe over a selected area of the sample surface. The interatomic force between the probe tip and the sample surface caused the cantilever to deflect as the sample changed the surface roughness (or other properties). The laser reflected from the back of the cantilever measured the deflection of the cantilever [28].

Table 2. Experimental design parameters.

Factor	Variation Levels
	Low (−1)	Medium (0)	High (+1)
Boron Carbide B4C (%)	5	10	15
Zirconia ZrO2 (%)	5	10	15

shows the studied different volume fractions of the B₄C and ZrO₂ particles, which affect the recycled material structure.

The design of experiment (DOE) was performed to validate the investigated parameters of 5–15% B₄C and ZrO₂ ceramic particles under a 550 °C processing temperature and 3 h preheating time. According to the Box Behnken design (BBD) method, the design introduced eight factorial points and three centre points. The purpose of applying this concept is to model and analyse the compressive strength response at a two-factor, second-order model:

$$Y=b_0+{\sum }_{i=1}^3 b_i{x}_i+{\sum }_{i=1}^3{b}_{ii} x_i{}^2+{\sum }_{i=1}^2 {\sum }_{j>i}^3 b_{ij}{x}_i{x}_j$$

(1)

where $b_0$, $b_i$, $b_{ii}$, $b_{ij}$, $x_i \left(x_j\right)$, and $Y$ are the regression coefficients for intercept value, linear model, quadratic number, interaction, extraction factor, and outcomes response, respectively [29].

By applying a design that could fit the two-factor, second-order model, the matrix X of the reinforced material for this design is given by:

$$\left[\begin{array}{cccccc}1& -1& 1& 1& 1& 1\\ 1& -1& 1& 1& 1& -1\\ 1& -1& -1& 1& 1& -1\\ 1& -1& 1& 1& 1& 1\\ 1& -\mathsf{\alpha }& 0& {\mathsf{\alpha }}^2& 0& 0\\ 1& \mathsf{\alpha }& 0& {\mathsf{\alpha }}^2& 0& 0\\ 1& 0& -\mathsf{\alpha }& 0& {\mathsf{\alpha }}^2& 0\\ 1& 0& \mathsf{\alpha }& 0& {\mathsf{\alpha }}^2& 0\\ 1& 0& 0& 0& 0& 0\end{array}\right]$$

(2)

$$X=\left[\begin{array}{cccccc}N& 0& 0& a& a& 0\\ 1& a& 0& 0& 0& 0\\ 0& 0& a& 0& 0& 0\\ a& 0& 0& b& F& 0\\ a& 0& 0& F& b& 0\\ 1& \mathsf{\alpha }& 0& {\mathsf{\alpha }}^2& 0& 0\\ 0& 0& 0& 0& 0& F\end{array}\right]$$

where N is the number of experiments, F is the factorial part of the central composites design, a is the axial variable, and b is the quantity variables [29,30,31]. Consider

$$\begin{array}{c}a=F+2{\mathsf{\alpha }}^2\\ b=F+2{\mathsf{\alpha }}^2\end{array}$$

(3)

where α is the distance from the central design and the experimental chosen value for the two-factor composites centre design. The response surface methodology (RSM) study uses a central composite design (CCD) at several points, which increases the response detection for optimum factor results. The investigated parameters are (−α, −1, 0, +1, α) in CCD, where levels −1 and +1 show the low- and high-representation values, and −α and α show the low- and high-extreme values [32]. The benefits of employing factorials and central and axial designs are to determine the optimum parameters of the investigated composites materials and obtain the best compressive-strength properties [33]. The parameter settings that resulted in an optimum compressive strength were then selected for material characterisations [16,34]. The Pareto chart of the parametric standards effects is shown in Figure 2, which is obtained by the minitab 18 software. The compressive strength was mainly affected by the amount of added volume fraction of the particles and the preheating temperature. The standardised effect and the influencing factors on the compressive-strength response are the volume fraction of ZrO₂ with the processing preheating temperature. The factors that do not exceed the reference line are insignificant and can be eliminated via backward elimination to refine the model. From the minitab software analysis, Figure 3 exhibits the residual plot for compressive strength. The residual for compressive strength is almost consistent in the normal probability plot. The closeness of the graph indicates that errors are negligible since they are in the tolerable margin. The plot of residuals versus fits response shows the consistency of variance in equal distribution, confirming the compressive strength’s approximation once it is correlated with the DOE analysis [35].

The DOE analysis helps reveal relationships between process parameters and compressive-strength findings,

Table 3. Compressive-strength analysis of variance by DOE.

Source	DF	Adj SS	Adj MS	F-Value	p-Value
Model	4	3758.36	939.59	44.23	0.000
Linear	2	3707.59	1853.80	87.26	0.000
Boron Carbide (B4C)	1	1404.77	1404.77	66.12	0.000
Zirconia (ZrO2)	1	2302.83	2302.83	108.40	0.000
2-Way Interactions	1	46.71	46.71	2.20	0.189
Boron Carbide (B4C) × Zirconia (ZrO2)	1	46.71	46.71	2.20	0.189
Curvature	1	4.06	4.06	0.19	0.677
Error	6	127.47	21.24
Total	10	3885.83

shows the compressive strength analysis of variance by DOE. The developed empirical model can be fully utilised to optimise the hot extrusion process. The analysis of variances (ANOVA) quadratic mathematical modelling is suggested to explain the relationship between the volume fraction of added ceramic particles and the resulting compressive strength, according to the regression model in Equation (4):

$$CS \left(\mathrm{MPa}\right)=208.13-3.617V_{{\mathrm{B}}_4\mathrm{C}}-4.360V_{{\mathrm{ZrO}}_2}+0.0966V_{{\mathrm{B}}_4\mathrm{C}}\times V_{{\mathrm{ZrO}}_2}-1.36\mathrm{CtPt}$$

(4)

where CS is the compressive strength, $V_{{\mathrm{B}}_4\mathrm{C}}$ is the volume fraction of Boron Carbide, $V_{{\mathrm{ZrO}}_2}$ is the volume fraction of Zirconia, CtPt are the central points of the experiment design.

The DOE model validated the volume fraction with a constant value of preheat temperature at 550 °C. However, the calculated p-value is less than the standard (p = 0.005) presented in Table 3. Hence, the model is practically correct according to the presented measurement. The values of S = 4.6092, R² = 96.72%, R² adj = 94.53%, and R² pred = 90.81% propose that the relationship between the processed parameters and responses have good agreement in this research, where S is an observed value and R² is a coefficient of determination and is adjusted (R² adj).

Table 4. Optimisation values over compressive-strength response.

Variable	Setting
Boron Carbide (B4C)	5
Zirconia (ZrO2)	5
Response	Fit	SE Fit	95% CI	95% PI
Compressive Strength (MPa)	170.66	3.26	(162.69, 178.64)	(156.85, 184.48)

presents the DOE design employed. It allows the experiments to be conducted at the optimum range only. Therefore, the constant range of the temperature is 550 °C, and the volume fraction of the ceramic particles was investigated under three hours of processing time. The compressive strength was increased by increasing the volume fraction up to 5%, and beyond this value, it decreased with the lowest observed compressive strength at 15% for both the B₄C and ZrO₂ volume fractions. The use of DOE investigates the range of volume fractions.

3. Results and Discussion

Table 5. Compressive strength, microhardness, and density of hybrid materials reinforced by different volume fractions of B₄C and ZrO₂ particles.

No.	Sample Notation	B4C (%)	ZrO2 (%)	Density kg/m3	Hardness (VH)	Max Strain %	Compressive Strength (MPa)
1.	S1	5	5	2.65	70.65	16.477	171.44
2.	S2	15	5	2.49	65.42	13.239	143.56
3.	S3	5	15	2.62	57.55	21.669	131.07
4.	S4	15	15	2.57	55.78	11.977	111.16
5.	S5	5	5	2.65	69.83	12.130	169.89
6.	S6	15	5	2.47	55.99	11.149	135.10
7.	S7	5	15	2.62	53.02	9.531	132.73
8.	S8	15	15	2.58	55.69	10.597	109.30
9.	S9	10	10	2.6	54.43	10.497	130.41
10.	S10	10	10	2.59	61.81	15.675	136.01
11.	S11	10	10	2.59	56.27	11.555	143.58

is presented to investigate the relationship between the processed factors (B₄C and ZrO₂ particles) which affect the response outputs of the recycled aluminium. The compression tests and microhardness and density measurements were carried out. The response of compressive strength was used to predict the optimisation of different volume fractions of reinforced B₄C and ZrO₂ ceramic particles. The statical analysis was used to obtain related parameters which cause higher material strength by employing the CCD model of analysis, following the experimental design [36]. Compressive strength, micro hardness, and density are presented separately in the following sections.

3.1. Compressive Strength

After the DOE design experimental procedures, the samples for hot extrusion were prepared at different volume fractions of reinforced B₄C and ZrO₂ ceramic particles (5–15%) following the DOE design experimental procedures. The samples were annealed in a furnace preheated at a temperature of 550 °C for three hours for all samples. The compression strength of the interlayers recycled hybrid materials with multiple B₄C and ZrO₂ reinforced particle size ratios was compared in Figure 4. The effects of the reinforced fractions on the recycled hybrid materials were analysed. From Figure 4, the compressive strengths of the samples are gradually enhanced up to the volume fraction of 5% in each design. Beyond the 5% volume fraction, the compression strengths dropped for 10% and 15% volume fraction of the ceramic particles. Samples four and eight obtained the lowest compressive strength values at 15% of B₄C and ZrO₂ contents. This is due to the agglomeration of the particles and pores availability. Increasing the content percentage beyond 15% yields large pores and increases the voids in size, which directly affects the recycled hybrid material concentrations [37]. The highest reported values of compressive strength were samples one and five. The material properties were strengthened by producing dislocations that pile up the total work hardening of the processed deformed specimens [38]. Therefore, the compression strength differed depending on the percentage values of reinforced particles mixed to aluminium AA6061 chips during the forming process.

3.2. Microhardness

Microhardness is the material resistance to the deformed surface localisation [39]. In general, adding ceramic contents increases the microhardness distribution values of the tested hybrid samples. From Figure 5, the microhardness increased by increasing the ceramic particles up to 5% volume fraction (B₄C and ZrO₂). Beyond 5% volume fraction (B₄C and ZrO₂), the microhardness declined due to the increasing pores and cracks from the material agglomeration and inhomogeneous distribution of particles [40]. It is noted that an optimum amount of ceramics particles addition of B₄C and ZrO₂ refers to their wettability, conductivity, and entrapping dislocations. According to Equation (5) [41]:

$$\lambda =4\left(1-f\right)r/ 3f$$

(5)

where λ is the distance of reinforced particles, r is the radius of ceramic particles, and f is the volume fraction of ceramic particles. Increasing the reinforced volume fraction will decrease the distance between the added particles. Equation (6) illustrates those effects:

$${\tau }_0=\left(Gb∕\lambda \right)$$

(6)

where ${\tau }_0$ is the shearing stress, G is the shearing module, b is the Burger’s crystal vector, and λ is the distance of reinforced particles. The Equations (5) and (6) conclude that the distance between particles decreases, and the shear of material dislocations would increase. This phenomenon will continue until the pores appear as a result of material agglomeration which causes low material strength. Increasing the microporosity, the discontinuity of the material phases will be greater, and the stress concentration level will be higher.

3.3. Density

The samples for density tests were 10 mm × 10 mm × 10 mm, calculated using Archimedes’ principle under different conditions in the air and water.

The density values were increased as a result of increasing the preheating processing temperature. This is because ZrO₂ particles have a high density of 5.68 g/cm³ which increases the total density of the recycled hybrid materials, while increasing the B₄C particles results in a decrease in the density of recycled materials because B₄C particles have a lower density of 2.52 g/cm³. As shown in Figure 6, the density reduction was compensated as a result of the extrusion-processing temperature. This is because activation energy requires the temperature derivation of the lead mechanism to the neck growth under the effects of thermal-processing surface and volume diffusion [36]. The recycled hybrid materials were characterised by localised plastic deformation in the matrix at a 550 °C processing temperature. The processing temperature causes cracking at grain boundaries which coalesce during repeated loading fracture. Therefore, the accumulation of thermal gradient stresses of the recycled hybrid materials yields density dislocation at a high-processing temperature [42,43].

3.4. Metallographic FE-SEM and AFM Analysis

The metallographic analysis is a good investigation tool for microstructural research of recycled metals in composites or hybrid forms. The selected samples of different mix percentages of ZrO₂ and B₄C reinforced ceramic particles with AA6061 chips have been investigated. Figure 7 shows that development of most grains occurred within the deformation die due to die shear stress, strain, and applied preheating temperature. The processed chips with reinforced particles have been elongated and transformed into fine weld lines. This is due to the broken oxide layers that form fine fragments of oxide layers [15]. Figure 7 presents that the fine fragments oxide layers are homogenously distributed within the extruded workpiece structures and have a good weld line that results in good compressive strength. In addition, the effects of adding ZrO₂ and B₄C ceramic particles cause the growth of the grains’ boundary region. However, a higher concentration of reinforced ceramic particles beyond the optimised parameters could cause more agglomeration of particles and greater grains. Hence, a higher level of processing temperature of 550 °C is participating to bond the surrounding aluminium chips in less solidification time. Increasing the solidification time leads to poor distribution of ceramic particles in the stage of bonding chips and particles at the solidified zone [41].

AFM scanning was introduced to investigate the problems of cantilevers along the material surface. The material-profiling deflection was measured with 3D profile at a magnification of a million times. It is necessary to show the material topography compared to optical scanning microscopes. This presentation shows the material combination of B₄C, ZrO₂ particles with AA6061 hybrid materials in terms of roughness and 3D surfaces profiles [28,44]. AFM was introduced to show the agglomeration of recycled hybrid materials under 550 °C preheating temperature. The results were altered during the hot-extrusion process depending on the added B₄C and ZrO₂ ceramics particles.

Table 6. Effects of AFM mean area, volume, and length on surface roughness.

Samples	Grain Area (μm2)	Grain Volume (μm2)	Grain Length (μm2)	Rq	Ra
Al/5% B4C-5% ZrO2	0.026	0.001	0.228	11.85	9.36
Al/15 B4C-15% ZrO2	0.041	0.002	0.232	8.70	6.77
Al/10 %B4C-10% ZrO2	0.024	0.001	0.221	14.06	11.03
Al/5 %B4C/15% ZrO2	0.033	0.001	0.257	10.70	8.37
Al/15 %B4C/5% ZrO2	0.025	0.001	0.226	15.27	12.11
Al-chips	0.038	0.002	0.282	14.24	11.24

summarises effects of AFM mean area, volume, and length on surface roughness; it shows that the grains were less distributed depending on the extra volume fraction of the added particles. Hence, measuring grains exhibited the thin film’s polycrystalline structure dependents of ceramic particles to the aluminium chips, as presented in Figure 8. The thin films kept decreasing all the grain’s length as the root mean square because of the enlargement added particles time growth. Thus, the decrease in the film’s thickness causes a decrease in the surface of the hybrid material characterisations [45].

To estimate the distribution of chemical elements, energy-dispersive X-ray spectroscopy (EDS) was conducted, which has been a widely applied technique [46]. The X-ray spectroscopy results showing the distribution of material chemical elements are presented in Figure 9 and

Table 7. Detailed EDS elements analysis of the investigated samples.

Samples Type	Elements
Al/5% B4C-5% ZrO2	Element	C	O	Mg	Al	Si
	Weight %	7.29	12.42	0.69	75.58	2.47
	Atomic %	13.85	17.72	0.65	63.92	2.00
Al/15% B4C-15% ZrO2	Element	C	O	Mg	Al	Si
	Weight %	19.75	10.47	0.72	62.36	0.60
	Atomic %	34.53	13.74	0.62	48.54	0.45
Al/10% B4C-10% ZrO2	Element	C	O	Mg	Al	Si
	Weight %	14.94	16.23	0.95	63.76	4.12
	Atomic %	25.88	21.10	0.81	49.16	3.05
Al/5% B4C/15% ZrO2	Element	C	O	Mg	Al	Si
	Weight %	16.14	14.73	0.67	66.41	2.05
	Atomic %	27.85	19.07	0.57	51.00	1.51
Al/15% B4C/5% ZrO2	Element	C	O	Mg	Al	Si
	Weight %	15.80	33.19	0.54	48.16	2.31
	Atomic %	24.91	39.29	0.42	33.81	1.56
Al − chips	Element	C	O	Mg	Al	Si
	Weight %	23.33	19.70	-	54.99	1.44
	Atomic %	36.81	23.34	-	54.99	1.44

. The agglomeration of reinforced particles, such as C, O, Si, and Mg, was not removed by processing treatments and was contaminated with the Al matrix. The Al matrix and other elements incorporated during the forming process cause smaller grains depending on the kinetic reactions of the elements’ composites. Poovazhagan et al. [47] and Fang et al. [48] showed that the presence of reinforced particles elements had direct effects on the microstructures of the material solidification, and they confirmed the possible chemical reactions between the process and workpiece substances of the contents.

4. Conclusions

This paper presents the investigations conducted on aluminium AA6061 chips reinforced with B₄C- and ZrO₂-based ceramic particles, which became AA6061-B₄C/ZrO₂ composites. The composite was assessed for its durability and restorative, mechanical, and physical properties. The B₄C and ZrO₂ parameters were validated by employing DOE under a 550 °C preheating temperature. The solid-state recycling of hybrid materials by hot extrusion was also conducted using the central composite design. The ANOVA revealed that factor A (B₄C) and factor B (ZrO₂) volume fractions were the most influential parameters for all responses. The combination of AB (volume fractions) directly affects the empirical model’s accuracy between the predicted and actual values. The physical and microstructure have good agreement with compressive strength and hardness. Thus, increasing the volume fractions up to 5% of each reinforced ceramic particle enhanced the hybrid material properties. Higher percentages only caused inhomogeneity and decreased the properties due to particles distribution and agglomeration. Additional investigations, such as heat treatment and fatigue tests, are highly recommended for the determination of the hybrid material’s mechanical and microstructure properties.