Introduction

It is well known [1] that the surface properties are a major factor in determining the functional life of a component. Due to the limitations inherent in the fabrication processes, many components made out of metals and their alloys usually possess poor mechanical and tribological properties, such as strength, hardness, corrosion resistance, fatigue, and wear resistance [2].

To improve and enhance these properties, metal matrix composites (MMCs) have been developed in which a secondary phase material is introduced in the primary metal or alloy generally known as matrix in order to enhance the mechanical and tribological properties [3–7]. Magnesium alloys are widely being used in various industrial sectors where weight reduction is a major concern, such as aerospace, automotive, and defence industries. In the context of automotive and aerospace industries, a reduction in weight while preserving the strength has major implications in terms of the reduction in vehicle weight, which consequently leads to a substantial reduction in the amount of fuel consumed. This, in turn, reduces the fuel costs and alleviates the environmental pollution levels. Sustained efforts of researchers [8–10] in this direction have led to the emergence of magnesium based MMCs as the most promising candidate materials. The processes used to fabricate MMCs are usually classified as solid state, liquid state or deposition type methods [11–17]. Among these, the solid state processing is preferred, as there is no phase transformation of material (to liquid phase) involved, due to which no surface defects are produced [18–20].

Since the last two decades, FSP is considered as the most promising solid state processing method for surface modification and fabrication of surface composites [21–26]. Mishra et al., developed the concept of FSP while working on friction stir welding (FSW), and they were remarkably successful in the fabrication of surface composites of 7075 aluminum alloy [27]. In FSP, a tool with two distinct parts, namely, the shoulder and the pin are used. The former is given a rotational motion while the latter is given a simultaneous linear motion. The softening of material takes place due to generation of heat by friction between the tool and work piece. The pin of the tool is inserted completely into the work piece for the uniform mixing of material in the processed zone. Severe plastic deformation that takes place during stirring of the tool results in grain refinement and surface modification, essentially caused by the dynamic re-crystallization of grains [21, 28–33]. In material processing field, FSP is considered a simple and a promising route to fabrication of materials with improved properties. The advantages of the FSP method are summarized in Table 1 and applications of FSP in industry are shown in Fig. 1. For making a surface composite by FSP, the secondary phase material is introduced in the matrix by employing different strategies. In one of the strategies of surface composite fabrication, a groove is made on the work piece surface and closed with a pin-less shouldered tool to prevent ejection of secondary material from the groove during FSP phase particles are than dispersed throughout the processed zone by FSP, thus formation of surface MMC. The mechanism of dispersion of these particles in the matrix during FSP involves the deformation processes such as forging and extrusion and was first explained by Mishra et al., and other researchers [27, 34].

Fig. 1
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Applications of FSP in Industry

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Table 1 Advantages of FSP
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Methods

The magnesium alloys are fast superseding materials like aluminum, titanium etc., due to their higher strength-to-weight ratio [57]. For this reason, the number of studies on FSP have substantially increased in recent years, particularly on development of magnesium alloys consisting of varying different alloying elements so as to improve their mechanical and tribological properties [58, 59]. The properties of these magnesium alloys can be further enhanced by the FSP. The main challenge is that FSP involves a considerable number of process parameters and the effect of these parameters on various properties is, many a times, contradictory in nature. Furthermore, the properties of magnesium MMCs depend mainly on the type of reinforcement particles, size of reinforcement particles, the percentage of reinforcement material added to matrix, bonding between matrix and reinforcement material and distribution of inter-metallic compounds in the matrix. In this brief, the state of the art of magnesium alloy modification through FSP is presented broadly in two systems, viz., Mg-Al-Zn (Mg-AZ) system and the Mg/rare earth system. The state of the art of magnesium-based surface composite fabrication through FSP is presented broadly in three systems viz., magnesium-metal oxide (Mg-MO) system, magnesium-metal carbide (Mg-MC) system, and magnesium-carbon nano tube (Mg-CNT) system.

Mg-AZ system

In this system, the surfaces of aluminum and zinc (AZ-series) magnesium alloys such as AZ31, AZ61 and AZ91 are modified through FSP and same is shown in Table 2. Mg17Al12 is a general appearing reinforcing phase of Mg-AZ system due to the presence of Al% and the amount of zinc [60–63]. The heat of formation of this phase is − 4.36 kj/mol which means that this reinforcing phase is existing stably in the Mg-AZ system [64, 65]. But the coarse eutectic Mg17Al12 phase at the grain boundaries is susceptible to instigate cracks under low stress during tensile deformation, thus leads to decrease in mechanical properties of material [66]. Due to FSP, breaking of Mg17Al12 takes place and is completely dissolved in the magnesium matrix which results in micro structural modification and homogenization of grains [66, 67].

Table 2 Brief summary of surface modification of Mg-AZ system alloys by FSP available in the literature
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As per literature FSP is found to be the most promising method of producing fine- grained magnesium alloys [68, 69]. Various researchers also worked on processing of Mg-AZ system by underwater FSP, also known as submerged FSP, and they reported that the resulting microstructure and thus mechanical properties are significantly affected by the surrounding temperature and cooling rate [70]. The submerged FSP is carried under water to provide a better cooling rate as compared to FSP carried in open air. The cooling rate results in decrease of tool wear and time consumed by the processed material above a certain temperature. This suppress the grain growth and as per Hall-Petch relation increase in mechanical properties [71–74]. The multi-pass FSP (MFSP) for Mg-AZ system have also been proven as the most effective FSP technique which results in more grain refinement of the material as compared to single pass FSP. The is because during MFSP, Mg17Al12 phase is significantly dissolved in magnesium matrix and due to effect of dynamic re-crystallization the micro structure is further refined as shown in Fig. 2a–c [77, 82, 84]. However, attaining optimum pass number is critical as each pass is associated with energy consumption.

Fig. 2
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a SEM image of base material b EBSD image of single pass FSP and c EBSD image of multi-pass FSP [77]

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Mg/rare-earth system

After Mg-AZ system alloys, Mg/rare earth system alloys are most widely used for several automobile and aerospace applications [85]. The most common alloys of this series are WE43, WE54, and ZE41 and they possess various desirable properties depending upon the type of alloying elements added such as Y, Ce, Nd, Gd. The FSP results in fine grain refinement and improved mechanical properties in Mg-Gd-Y-Zr alloy due to complete dissolution of coarse Mg5(Gd, Y) phase [86, 87]. Palanivel et al. [88] used a modified FSP technique also known as friction stir additive manufacturing to fabricate high strength with considerable ductility WE43 alloys. Their results show fine, uniform, closely populated and well organized precipitates with sizes 2–7nm. Strength of 400 Mpa and 17% ductility of the alloy was also achieved. Venkataiah et al. [45] studied the effect of FSP on the mechanical properties, machining behavior and corrosion rate of ZE41 magnesium alloy. Increase in hardness and decrease in grain size from 110μm to 3μm was achieved after FSP due to the complete dissolution of Mg7Zn3RE inter-metallic phase in the matrix. However, they had not observed any change in the corrosion behavior of the alloy after FSP.

Studies on the precipitation behavior of Mg-Y-Nd alloy during FSP were conducted experimentally by Cao et al. [89]. Afterwards, FSPed alloy was aged to modify the microstructure and to investigate the mechanical properties. They achieved grain refinement upto 2.7μm, along with enhanced tensile strength (303 MPa), yield strength (290 Mpa) and elongation (11%) as compared to cast Mg-Y-Nd alloy. Genghua and Zhang Datong [90], processed Mg-Y-Nd alloy by FSP and a tremendous improvement in grain refinement was achieved. The intermetallic phase was observed as Mg12Nd which was completely broken into discontinuous particles by FSP resulting in microstructural modification and hence increase in mechanical properties. Kondaiah et al. [91] studied the effect of FSP process parameters (rotational speed and traverse speed of tool) on micro structural modification and hardness of ZE41 Mg alloy. They reported the formation of super saturated grains, increase in hardness with tool rotational speed and increase in material flow rate during FSP with tool traverse speed. Vasu et al. [92] successfully added calcium (Ca) to ZE41 Mg alloy by FSP targeted for biodegradable implant applications. They achieved a grain refinement up to 7μm due to which the hardness was also increased. They also noticed that with the increase in immersion time, ZE41-Ca composite degrades at a very less rate as compared to unprocessed ZE41 Mg alloy.

Magnesium metal oxide (Mg-MO) system

A summary of suitable metal oxides used with magnesium alloys for producing magnesium MMCs by FSP are given in Table 3.

Table 3 Brief summary of Mg-MO surface MMCs by FSP as available in the literature
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Mg- Al 2 O 3 MMCs

Magnesium on combining with aluminum oxide (Al2O3) results in the formation of Mg, MgO, γ−Al2O3, and Mg17Al12 phases and is shown in Fig. 3 [93].

Fig. 3
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XRD showing various phases formed after reaction betwen pure Mg and Al2O3 [93]

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As per Mg- Al phase diagram, the dissolution of coarse eutectic Mg17Al12 precipitate in magensium matrix requires a heating temperature of 427∘C [94]. Due to slow diffusion rate of aluminum in magnesium matrix, a time duration of approximately 40 h is required for complete dissolution of eutectic Mg17Al12 phase in magnesium matrix [95]. But rigorous plastic deformation by FSP and a strain rate up to 0.4% facilitates complete dissolution of aluminum oxide in the magnesium matrix within a short time as during FSP the maximum time that the temperature stays above 200∘C is 25 s [96, 97]. Farji and Asadi [94] produced AZ91- Al2O3 MMC by FSP using square and circular tools and the produced composite showed improved hardness and wear resistance. The role of tool rotational speed and tool traverse speed was an important observation in their study. It was easily understood from their microstructural studies that the lower traverse speed results in better Al2O3 particle distribution and less agglomeration as compared to higher traverse speed. This was because the higher traverse speed decreases the rotational speed/traverse speed ratio which leads to poor stirring and mixing of Al2O3 in the matrix. The homogenous microstructure was produced with square tool at 900 rpm tool roational speed and 40 mm/min tool traverse speed. Ahmadkhaniha et al. [98] produced AZ91D- Al2O3 MMC by FSP and demonstrated the effect of the ratio of tool rotational speed and tool traverse speed on the better distribution of Al2O3 in the magnesium matrix by FSP. They demonstrated clearly that increase in the tool rotational speed /traverse speed ratio increases the heat and strain of material which resulted in better dispensation and less agglomeration of Al2O3 in the magnesium alloy (see Fig. 4). The micro hardness of FSPed AZ91D- Al2O3 composite increases to 95 HV as compared to FSPed AZ91 (78HV) without Al2O3. This was explained because of the pinning effect of Al2O3 particles in the matrix due to which the grain size was significantly reduced and as per Hall-Petch equation, increase in hardness of the material. They also noticed that improved hardness of FSPed specimen with the addition of Al2O3 particles limits the deformation and resist the penetration and thus increases the wear resistance.

Fig. 4
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SEM images of friction stirred AZ91D/ Al2O3 processed at a RS= 800 rpm, TS = 40 mm/min, b RS = 800 rpm, TS = 80 mm/min [98]

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Azizieh et al. [99] produced AZ31- Al2O3 nano composites by FSP using tools with three different pin profiles namely circular pin with no threads, with threads and with threads and three flutes. They studied the effect of rotational speed of tool with constant traverse speed, pin profile and FSP pass number on the distribution of Al2O3 in the Mg- matrix. The formation of onion ring type patterns were observed in the micro structures of the composites processed with threaded pin profile at a tool rotational speed of 1000 rpm and 1200 rpm as shown in Fig. 5. The reason behind the formation of onion patterns was explained as improvement in material flow with threaded pin profile due to downward movement of material. They also noticed that the two pass FSP leads to more gain refinement (2.9μm) as compared to single pass FSP (4.4μm). Due to the pinning effect with the addition of Al2O3 in the matrix, a grain size of 3.4μm was also achieved.

Fig. 5
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The onion ring patterns formed with threaded pin profile at 1200 rpm [99]

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Abbasi et al. [104] fabricated surface composites on AZ91 magnesium alloy using Al2O3 and SiC as reinforcement particles. Their results showed increase in both mechanical and tribological properties of AZ91 magnesium alloy by the incorporation of the reinforcement particles.Their results also showed that samples processed using SiC particles had better mechanical characteristics and corrosion resistance than samples processed using Al2O3 particles, although particle type did not have significant effect on wear rate.

Mg- SiO 2 MMCs

Mg- SiO2 reaction produces Mg2Si and MgO and is shown by the following reaction [105]

$$4\text{Mg} + {SiO}_{2} = {Mg}_{2}Si + 2\text{MgO} $$

The reaction is exothermic and the heat produced in the reaction is responsible to form Mg2Si and MgO by a self-propagating high temperature synthesis [106]. The formation of intermetallic coarsened Mg2Si results in degrading the strength and elongation of magnesium alloy. With multi pass FSP, more number of passes will only result in the formation of nano sized phases of Mg2Si and MgO which are still in fine scale [107]. Khayyamin et al. [101] employed nano SiO2 with 8% volume fraction in AZ91 magnesium alloy by FSP. The effect of traverse speed and number of FSP passes in the composite fabrication was a key finding in their study. Their micro structural studies revealed the uniform distribution of SiO2 in the AZ91 matrix with multi pass FSP as compared to single pass FSP. Further, they also observed that increase in traverse speed decreases the grain size and increases the hardness. This is because when the traverse speed is increased, the material gets affected by the process heat for a less time which restricts the grain growth during dynamic recrystalization. The maximum hardness of composite was achieved as 124 HV in three pass FSP at a traverse speed of 63 mm/min.

Lee et al. [100] incorporated 5−10% nano SiO2 in AZ61 magnesium alloy matrix using FSP. TEM analysis of their study clearly indicates the formation of Mg2Si and MgO phases in the matrix as shown in Fig. 6. The authors explained the formation of these phases as a result of reaction between SiO2 and Mg during FSP. They further concluded that four passes resulted in the uniform distribution of SiO2 in the matrix and the incorporation of nano SiO2 paticles in the magnesium matrix increases the hardness to two times as compared to base material.

Fig. 6
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TEM evidence showing the presence of Mg2Si in the fabricated composite sample [100]

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Mg- ZrO 2 MMCs

On combining ZrO2 with magnesium there is no new phase formed except for a weak ZrO2 reinforcement phase. This indicates the stability of ZrO2 in the magnesium matrix as no intermetallic compound is formed between Mg- ZrO2 during FSP as shown in the SEM and EDS result of Fig. 7 [107]. Due to plastic deformation during FSP, ZrO2 particles are distributed uniformly ahead the grain boundaries which restricts the movement of dislocations and results increase in hardness of the processed material [103]. Navazani and Dehghani [102] incorporated ZrO2 to Mg-matrix by FSP. The mechanical properties were enhanced and fine refinement in grains was observed due to addition of ZrO2 to Mg - matrix. They observed the enhancement in mechanical properties due to the pinning effect of ZrO2 particles on the grain boundaries. Further they also observe that multi-pass FSP also improves the pinning effect of particles which results in less agglomeration and fine refinement of particles which is shown in Fig. 8.

Fig. 7
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SEM and EDS images showing dispersion and phases of ZrO2 in Mg-matrix [102]

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Fig. 8
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Effect of ZrO2 particles and multi pass FSP on microstructure of Mg-matrix [102]

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Magnesium–metal carbide (Mg-MC) system

In this approach, various metal carbides such as silicon carbide (SiC) and titanium carbides (TiC) are added to magnesium matrix by FSP which is summarized in Table 4.

Table 4 Brief summary of Mg-MC surface MMCs by FSP as available in the literature
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Mg-SiC MMCs

Morisada et al. [108] incorporated SiC particles in magnesium AZ31 matrix by FSP and observed the effect of addition of SiC particles on microstructure and hardness of the matrix. They found that addition of SiC to Mg-AZ31 matrix resulted in significant refinement of grains due to severe plastic deformation by tool rotation and pinning effect by SiC particles. Further the change in grain size at the elevated temperatures was also observed. It was seen at above 300∘C temperature, the abnormal grains were formed in FSPed sample without the addition of SiC particles. This resulted in lower hardness values of the processed material due to high temperature generated in the processed region. However the authors found normal and stable grains even at 400∘C by the addition of SiC to AZ31- Mg matrix as shown in Fig. 9.

Fig. 9
figure 9

Micro-structural images of the stir zone after the heat treatment [108]

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Erfan and Kashani [109] fabricated the AZ31-SiC composites by incorporating nano SiC particles to AZ31-Mg matrix. They studied the effect of tool tilt angle on performance of composites. It was found that a tool tilt angle of 0∘ exhibits tunnelling defect in the track during FSP and a tool tilt angle of 3∘ eliminated tunnelling defect. They also confirmed the better distribution and less agglomeration of SiC particles in the AZ31-Mg matrix with the increase in tool rotational speed to tool traverse speed ratio. Asadi et al. [110] added the SiC particles to AZ91-Mg matrix and studied the effect of its addition on micro-structure and hardness of AZ91-Mg alloy.They investigated the effect of tool rotational speed, tool traverse speed and the number of FSP passes on the quality of fabricated composite. The authors concluded that the increase in tool rotational speed decreases the hardness of the composite due to increase in grain size and decrease in tool traverse speed decreases the grain size and increase the hardness of the composite as per hall-Petch equation. Further more they also observed uniform distribution of SiC particles in AZ91 Mg-matrix by multi pass FSP.

Mg–TiC MMCs

TiC is considered as a glamorous reinforcement because of its high elastic modulus, very high hardness and high thermal stability as compared to other ceramic particles [113, 114]. From the work of Balakrishnan et al. [112] it was found that addition of TiC to magnesium matrix by FSP resulted in uniform distribution of TiC particles without undergoing any chemical reaction and the formation of any secondary phase. However their experimental results revealed a complete change in the micro-structure by different volume fractions of TiC used in the Mg- matrix (see Fig. 10). The formula used for calculating the volume fraction is given below

$$ \mathrm{Vol.~ fraction= (Groove~ area/Tool~ pin~ area)}*100 $$
(1)
Fig. 10
figure 10

SEM images of AZ31/TiC composite containing a 0 vol.% TiC, b 6 vol.% TiC, c 12 vol.% TiC, and d 18 vol.% TiC [112]

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$$ \mathrm{Groove~area= Groove~width * Groove~depth} $$
(2)
$$ \mathrm{Tool~pin~area= Dia.~ of~ pin*Length~of~pin} $$
(3)

With the increase in volume fration of TiC particles, the spacing between the particles was seen reduced and viceversa.

Magnesium carbon nano tubes (Mg-CNTs) system

Carbon nano tubes are considered as an excellent reinforcing material because of their low density, high elastic modulus (1000 GPa) and high tensile strength (50 GPa) [115, 116]. Single walled carbon nano tubes and multi- walled carbon nano tubes (MWCNTs) are generally used depending upon the desired applications [117]. The composites with carbon nano tubes as a reinforcement material formed by the conventional techniques such as casting ([118] and powder metallurgy [119]) resulted in agglomeration and weak bonding at the interface due to which the uniform distribution of these tubes in the matrix becomes difficult. FSP, being a solid state processing technique, can distribute MWCNT’s in the matrix uniformly which in turn resulted in improved mechanical, metallurgical and tribological properties and the same is summarized in Table 5 [120].

Table 5 Brief summary of Mg-MWCNTs surface MMCs by FSP as available in the literature
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The uniform distribution along with the morphology of CNTs in Mg-6Zn alloy by FSP was recently reported by Haung et al. [121]. From the TEM results, they observed the singly dispersement of CNTs after FSP without formation of any clusters (see Fig. 11). Their TEM results also confirmed the fecilitation of the sites for nueleation of dynamic recrystilization by incorporation of CNTs. The yeild strength of fabricated composite (Mg-6Zn-CNT) seen was increased to 171Mpa (70 Mpa Mg-6Zn in (cast)), the ultimate tensile strength to 300 Mpa (129 Mpa Mg-6Zn(cast)) and the elongation 15% (8.1% Mg-6Zn in (cast))

Fig. 11
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TEM images of FSPed Mg-CNT MMC: (a–c) Dispersion of CNTs, (d, e) CNTs morphology in MMC, (f) nano sub grains next to CNT [121]

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Morisada et al. [122] dispersed multiwalled carbon nano tubes (MWCNT’s) in AZ31-Mg matrix by FSP and successfully develop a fine-grained composite with hardness twice (78Hv) as compared to that of base metal (41HV). The role of travel speed in the dispersion of MWCNT’s in AZ31-Mg matrix was alo a key finding in their study and they concluded that travel speed of 25mm/min resulted in fine and uniform grains by keeping a constant 1500 rpm rotational speed.

The wear behavior of AZ31-Mg alloy with the incorporation of MWCNT’s by FSP was studied by Jamshidijam et al. [123]. The addition of MWCNT’s to AZ31-Mg increases the wear resistance with almost two times. The grain size was also reduced to 5 μm and hardness was increased twice with MWCNT’s.

In the work of [124], the effect of different pin profiles of tools along with the speed ratio, number of passes and CNT amount on the quality of developed surface composites were investigated. They noticed a uniform and fine grained micro structure with stepped pin profile, low speed ratio, multi pass FSP, and higher amount of CNT.

Modified friction stir processing techniques

In recent years, several modified methods of FSP have been used to fabricate the surface MMCs and are discussed as follows:

Direct friction stir processing (DFSP)

A modified technique in producing a better surface MMCs without using a pin in the FSP tool also known as direct FSP (DFSP) was firstly reported by Huang et al. [111].

This technique was observed to produce better surface composites in single pass as compared to conventional multi-pass FSP. They used a hollow pin less tool with the outer diameter or shoulder diameter 24 mm and inner diameter 8mm as shown in Fig. 12. Like in conventional FSP, the secondary phase material by DFSP was not preplaced on the base metal but in the hollow portion of the DFSP tool. When the rotating tool traversed in the longitudinal direction of the base metal surface, the secondary phase particles flowed into the encaged space between the base metal plate and the moving shoulder through the hollow space in the tool. Thus, without using a pin, these particles were stirred and pressed into the base metal dispersedly. Therefore, uniform distribution of particle throughout the processed region was successfully obtained with only single pass FSP.

Fig. 12
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Images of DFSP tool: a front view, b shoulder view, and c the clamping end [111]

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Friction stir vibration (FSVP)

FSP with vibration (FSVP), a novel technique for making surface MMCs was recently introduced by Behrouz Bagheri and Mahmoud Abbasi [125]. The only difference between the two is that in FSVP along with the tool rotational and traverse motions like in FSP the workpiece is vibrated normal to the processing direction. Their results confirmed the more refinement of grains in FSPV as compared to simple FSP. This was because of the induced vibrations in workpiece during FSP due to which the material deformation was increased which results in breaking of agglomerated reinforcement particles by enhanced dynamic recrystallization.

In another work of Bagheri et al. [126], FSVP was used to fabricate AZ91/SiC surface MMCs. Their microstructural results revealed a better homogenous distribution of SiC particles in AZ91 matrix. Their results also showed more refinement of grains and increase in ultimate tensile strength by FSVP ((26.43 ±2.00) μm and 361.82 MPa) as compared to conventional FSP ((39.43 ±2.00) μm and 324.97 MPa).

Ultrasonic assisted friction stir processing (UaFSP)

Baradarani et al. [127] used the novel UaFSP to enhace the mechanical properties and corrosion resistance of Mg-AZ91 alloy. A remarkable refinement of grains (1.6 μm) with low current density (2.09 μA/cm2) was observed with UaFSP as compared to simple FSP. This is due to the fact that due to UaFSP the intermetallic β-Mg 17Al12 phase was distributed more homogenously in the AZ91 matrix as compared to simple FSP.

Conclusions

In this review paper the basic understanding of enhancement of mechanical and tribological properties with or without the addition of reinforcement particles during FSP of magnesium alloys have been addressed. From this review paper it is concluded that:

  • The mechanical and tribological properties such as tensile strength, hardness, corrosion resistance and wear resistance of magnesium alloys can be improved by making a surface composite layer of reinforcement particles on magnesium alloys by FSP.

  • The FSP process parameters epecially the tool geometry, i.e., shoulder diameter, pin diameter and pin shape plays an important role in the performance of composite.

  • Selection of optimum tool rotational speed and tool traverse speed in FSP plays a crucial role in producing sound composites of magnesium alloy. Higher tool rotational speed results in better distribution of reinforcement particles across the work piece surface because of more heat generation and more shattering effect of rotation while as low traverse speed results in formation of coarse grains due to increase in material processing time which increases the heat input and results in grain growth. So, obtaining the optimum values of rotational and traverse speed are recommended.

  • Multiple pass FSP results in more grain refinement and uniform distribution of reinforcement particles by accumulating higher degree of strain and dynamic recrystallization.

  • A lot of work has been done on AZ system magnesium alloys as compared to RE system magnesium alloys. It is expected that more number of composites of RE system magnesium alloys will be developed in future by FSP for aerospace, automotive and biodegradable applications.

  • Majority of magnesium metal matrix surface composites are produced using reinforcements of metal oxide system as compared to metal carbide and CNTs system. Its anticipated to produce more number of magnesium surface composites in future by using CNTs system because of its excellent properties as compared to other systems.