`Journal of MetallurgyVolume 2012 (2012), Article ID 762125, 10 pageshttp://dx.doi.org/10.1155/2012/762125`
Research Article

## Surface Modification of Light Alloys by Low-Energy High-Current Pulsed Electron Beam

1Key Laboratory of Materials Modification, Department of Materials Engineering, Dalian University of Technology, Dalian 116024, China
2Laboratoire d'Etude des Microstructures et de Mécanique des Matériaux (LEM3), CNRS UMR 7239, Université Paul Verlaine-Metz, Ile du Saulcy, 57045 Metz, France
3Shanghai Engineering Research Center of Mg Materials and Applications, School of Materials Science and Engineering, Shanghai Jiao Tong University, Shanghai 200240, China
4School of Materials Science and Engineering, Shenyang University, Shenyang 200240, China

Received 16 February 2011; Revised 17 August 2011; Accepted 9 December 2011

Copyright © 2012 X. D. Zhang et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

#### Abstract

This paper reviews results obtained by the research groups developing the low-energy high-current pulsed electron beam (LEHCPEB) in Dalian (China) and Metz (France) on the surface treatment of light alloys. The pulsed electron irradiation induces an ultra-fast thermal cycle at the surface combined with the formation of thermal stress and shock waves. As illustrated for Mg alloys and Ti, this results in deep subsurface hardening (over several 100 μm) which improves the wear resistance. The analysis of the top surface melted surface of light alloys also often witnesses evaporation and condensation of chemical species. This phenomenon can significantly modify the melt chemistry and was also suggested to lead to the development of specific solidification textures in the rapidly solidified layer. The potential use of the LEHCPEB technique for producing thermomechanical treatments under the so-called heating mode and, thus, modify the surface crystallographic texture, and enhance solid-state diffusion is also demonstrated in the case of the FeAl intermetallic compound.

#### 1. Introduction

Light alloys, such as Mg-, Al-, and Ti-based alloys, have attracted increasing attention in the past few decades owing to their low density and, correspondingly, their high strength/ductility ratio. Because of this, light alloys are increasingly used to replace steels in industrial components. However, these light alloys are all facing some serious surface-related disadvantages such as poor wear or corrosion resistance that have strongly limited their potential for some specific industrial applications. Therefore, surface treatment techniques should be applied on these light alloys in order to improve their global performance.

The low-energy high-current pulsed electron beam (LEHCPEB) process is a fairly new surface modification technique [1, 2]. The LEHCPEB sources have been first developed for surface treatment of materials by Proskurovsky and Ozur in Tomsk (Russia) [13]. As one kind of high-power charged particle beam, LEHCPEB exhibits essential advantages over pulsed laser and ion beams by its high efficiency, simplicity, and reliability. The pulsed electron irradiation induces (i) a rapid heating and cooling of the surface together with (ii) the formation of thermal stress and stress waves [4, 5]. As a result, improved surface properties of the material, often unattainable with conventional surface treatment techniques, can be obtained fairly easily. This is particularly true for tribological [2, 4, 6, 7] and corrosion properties [710]. Proskurovsky et al. [14] have carried out pioneer investigations of the LEHCPEB treatment on a series of Al- and Ti-base alloys and the results obtained showed an increase of corrosion and strength properties for the treated alloys. The group in Dalian University of Technology (China) has more recently done research on various light materials such as pure Al [11, 12], pure Ti [13], pure Mg [14, 15], and Mg alloys [6, 16, 17]. In particular, though collaboration with the University of Metz (France), they have detailed the microstructure evolution of LEHCPEB treated alloys and their corrosion properties [1823]. Also, the group has investigated the LEHCPEB treatment of a FeAl intermetallic compounds [24, 25], which can be used to replace refractory steels for high-temperature weight saving applications. This paper reviews the main results obtained from their studies on light alloys treated with LEHCPEB in connection to improvements in wear and corrosion resistances as well as specific features related to texture and microstructure modifications, deep hardening, and evaporation phenomenon.

#### 2. The Surface Treatment System

The samples investigated in the present manuscript were treated in Dalian using a “Nadezhda-2” system. A schematic diagram of this LEHCPEB source is given in Figure 1. The “Nadezhda-2” electron-beam source can produce electron beams with the parameters as follows: electron energy 10–40 keV, peak current 102–103 A/cm2, pulse duration 0.5–5 μs, energy density 0.5–40 J/cm2, beam cross-section area 10–50 cm2, and repeating pulse interval 10 s. The electron beam is generated by an explosive emission graphite cathode. Spark plasma sources are placed evenly in a circle behind the anode, providing anode plasma that conducts the beam to the collector where the specimen to be treated is placed. An external magnetic field is applied to confine the beam to prevent the beam from pinching and dispersing. The accelerating voltage, magnetic fields intensity, and anode-collector distance control the beam energy density. They are simple and reliable in operation.

Figure 1: Schematic diagram of the LEHCPEB source based on vacuum spark plasma. 1: cathode, 2: anode, 3: collector, 4: vacuum chamber, 5: cathode plasma, 6: anode plasma, 7: solenoid, 8: spark plasma sources, 9: specimen, 10: plasma sheath, 11: electron beam [4].

#### 3. Improvement of Wear and Corrosion Resistances

The pulsed electron irradiation generated by this surface treatment technique induces rapid melting of the surface followed by extremely fast solidification. This process leads to the dissolution of second-phase particles and, after sufficient number of pulses, to the formation of 2-3 μm thick homogeneous melted surfaces [18, 22, 26]. The so-formed homogeneous layers were demonstrated to improve the corrosion properties of dual-phase alloys such as the 316L stainless steel [7, 21] and the D2 steel [18] as well as NiTi shape memory alloys [20]. The LEHCPEB treatment also often induces in steels the formation of nanoscale structures formed by rapid solidification in the melted layer [18, 21, 27, 28]. Some extent of grain refinement was also observed in the subsurface that remained solid of a D2 steel because of the heavy deformation induced by the thermal stress wave accompanying the very fast thermal cycles [29]. In steels, these finer grains together with the strain hardening imparted by the thermal stresses are believed to be the major contributors to surface/subsurface hardening and associated wear resistance improvement [7]. In the following section, we present some results obtained on light alloys in terms of wear and corrosion resistances.

##### 3.1. Mg and Its Alloys

The AZ31 (Mg-3Al-0.5Zn-0.5Mn) is a commercial α (Mg) single-phase Mg alloy while the AZ91 (Mg-8.9Al-0.5Zn-0.2Mn-0.04Si) one consist of a two-phase α (Mg) + -Mg17Al12 mixture. The LEHCPEB surface treatments were carried out for 5, 10, and 15 pulses using electron beam energy densities of 2.5 J/cm2 and of ~3 J/cm2 for the number AZ31 and AZ91 alloys, respectively. Wear tests were carried out without lubricant using a ball (WC-Co)-on-flat apparatus. Figure 2 gives the evolution of the wear rate with the number of pulses for the AZ31 alloy while the wear volume and the friction coefficients for the AZ91 alloy are shown in Figure 3. For both alloys, the wear mechanism was abrasive wear and the wear tracks were much wider for the untreated samples than for the treated ones. This indicates that a hardening effect occurred due to the LEHCPEB treatment.

Figure 2: Evolution of the wear rate with the number of pulses for the AZ31 Mg alloy [6].
Figure 3: Evolution of the wear volume and the friction coefficient with the number of pulse for the AZ91 Mg alloy [17].

For the AZ31 alloy, the wear rate decreases when increasing the number of LEHCPEB pulses and the best wear resistance was obtained after 15 pulses of treatments. This corresponds to an improvement in wear resistance by a factor of 6.7.

As illustrated in Figure 3, there is also a general trend for both the wear volumes and the friction coefficients of the AZ91-treated samples to decrease after the LEHCPEB treatment. However, the best wear resistance was obtained for the sample treated for 10 pulses only.

In terms of corrosion resistance, it is also the 10 pulsed treated sample that displayed the best behavior. This is illustrated in Figure 4 that gives the evolution of the corrosion rate with the number of pulses for the AZ91 alloy. The immersion corrosion experiments were performed in a 5% NaCl solution for 72 h on both the intial and LEHCPEB-treated AZ91 samples. The corrosion results indicated that the average corrosion rate decreased after the LEHCPEB treatment with the 10-pulsed sample showing the best corrosion resistance (the lowest corrosion rate). It is, therefore, clear that both the best wear and corrosion resistance are obtained after 10 pulses and not after the highest number of pulses (15 pulses). As will be discussed later in the text, this is likely due to some evaporation phenomena taking place more significantly after 15 pulses.

Figure 4: Evolution of the corrosion rate with the number of pulses [16].

Such improvements of the wear and corrosion resistance can be attributed to the formation of an extended graded structure (a nanograined MgO layer and a melted layer) at the surface layer of the irradiated AZ91 Mg alloy after the LEHCPEB treatment. The thin nanograined MgO layer present on the top surface played an important role of lubricant during wear tests and a protective layer during corrosion test. The melted layer formed beneath the oxide layer consists of Al oversupersaturated α (Mg) solid solution due to the solute trapping effect during the fast solidification process. Such a melted layer is favorable for the formation of a homogenous passive film during the corrosion test and thereby protects the substrate.

##### 3.2. Ti and Its Alloys

LEHCPEB treatments were performed on the commercially pure Ti (CP-Ti) samples [13] with the accelerating voltage 25.2 kV and pulse times 15 and 25. Electrochemical corrosion tests for both the initial and treated samples were carried out using the conventional three-electrode cell in a 5% NaCl water solution.

Figure 5 shows the potentiodynamic polarization curves. There is a significant improvement in corrosion resistance after the LEHCPEB treatments evidenced by a shift of the whole polarization curve towards the region of lower current density and higher potential. The improvement in corrosion performance can be ascribed to two major factors. Firstly, it is well established that ultrafine structures in CP-Ti lead to improved corrosion resistance. This is due to the redistribution of impurities that segregate at grain boundaries and higher reactivity to form a protective oxide layer. Secondly, the LEHCPEB technique is very effective for removing top surface contaminants or self-purification helping to form more homogeneous protective layers.

Figure 5: Potentiodynamic polarization curves of CP-Ti samples before and after LEHCPEB treatments [9].

#### 4. Deep Hardening Effects

The hardness of a material depends on several factors: the grain size via the Hall-Petch hardening, the alloying elements via the solid solution, and/or precipitation hardenings, the presence of structural defects such as vacancies or dislocations as well as the residual stress state. The understanding of hardening in iron and steels treated by LEHCPEB has already been investigated in detail recently. Two interesting behaviours are generally reported in steels concerning the hardness evolution on the LEHCPEB-treated samples. First, a modification of the hardness is obtained in the melted layer (hardening or softening) [7, 30]. Second, below this melted layer, the hardened subsurface—which extends over slightly more than 100 micron—consists in fact of two successive hardened zones. It is well established that the high dislocation density in the surface layer of the target material usually increases dramatically after the LEHCPEB treatment [31, 32]. For example, Valyaev et al. have shown the dependence of hardness on dislocation densities in pure iron treated by pulsed electron beam treatment [31, 32]. The LEHCPEB irradiation also induced vacancy type of defects that should also favour the increased hardness in steels [33, 34]. The first hardness peak was attributed essentially to the quasi-static thermal stress and the repeated action of the beam induced the formation of microdeformation bands. The second peak—of lower intensity—was related to deeper hardening induced by the thermal stress wave [7]. In some cases, the tensile stress that is created in the rapidly quenched melted layer has been suggested to induce a top surface softening over the top first few microns. For example, Rotshtein et al. [30] and Zou et al. [7] have also observed a decrease in hardness at the top surface layer of a 316LS steel. They considered that this was due to the residual tensile stress generated by the LEHCPEB treatment [7, 30].

Figure 6 gives the evolution of the cross-section microhardness with depth for the LEHCPEB-treated Mg alloys AZ31 and AZ91, pure Mg, and pure Al. Although the hardness was measured from different light alloys treated with different LEHCPEB parameters, the hardness profiles often show some common characteristic features: an overall increase in subsurface hardness with the possibility of some local sharp increase. It is interesting to notice that the increase in hardness is generally obtained over a depth of more than 100 μm for the LEHCPEB-treated samples, sometimes reaching a depth of nearly 500 μm (Figure 6(a)). These increases in hardness must be attributed to the action of the stress waves which can propagate far beyond the heat affected zone (HAZ). Hence, deformation occurs below the HAZ and the hardness can be increased due to the work-hardening effect [6, 14]. In fact, such deformation induced by thermal stress wave propagation was revealed by TEM observations in LEHCPEB treated pure Al. Figure 7 gives a TEM bright field image showing the deformation marks (stacking fault-like contrast) about 1 μm beneath the surface having orientations of about 45° with respect to the surface. Moreover, a direct experimental proof of the existence of the stress far below the surface is illustrated in the TEM image of Figure 8, where two wave fronts are observed about 0.5 mm beneath the surface.

Figure 6: Evolution of cross-section microhardness with depth for the LEHCPEB-treated samples: (a) AZ31 Mg alloy (27 kV, 10 pulses); (b) AZ91 Mg alloy (27 kV, 10 pulses); (c) pure Mg (27 kV, 10 pulses); (d) pure Al (28 kV, 1 pulse).
Figure 7: The stacking faults-like contrast about 1 μm beneath the surface melted layer [11].
Figure 8: Two wavy fronts approximately 0.5 mm beneath and perpendicular to the treated surface. They are parallel to a grain boundary [15].

It is usually accepted that the increase in hardness plays the major role for improving the wear resistance of LEHCPEB-treated samples. It is the subsurface hardening that is in fact responsible for the improved wear behaviour and diminution of the wear volumes depicted in Figures 2 and 3.

#### 5. Microstructure Evolution and Evaporation Phenomena

The LEHCPEB surface treatment on light alloys is normally accompanied by significant surface evaporation of chemical species. Under intensive evaporation, a special surface morphology is observed after LEHCPEB treatment. Figure 9 shows a typical SEM surface micrograph of pure Mg irradiated by LEHCPEB with an energy density of about 3 J/cm2. Two distinct features can be clearly observed. The first one is the wavy aspect of the surface consisting of a succession of hills and valleys at the sample surface, which is different from common feature of many LEHCPEB treated metal surfaces. The second feature is the presence of many isolated particles on the surface, which is due to the condensation of the Mg vapor.

Figure 9: SEM micrographs showing typical surface morphology of pure Mg after evaporation treatment, energy density 3 J/cm2, 5 pulses [16].

After treatment in evaporation mode, it is expected that the selective evaporation taking place on the surface results in composition changes. Figure 10 gives the electron probe microanalyzer (EPMA) line scan analysis of the melted layer present locally at the surface of the AZ31 Mg alloy samples. The results clearly indicated a depletion of the Mg element and a corresponding increase of Al element in the melted layer. Such a selective evaporation of Mg over Al element is clearly the consequence of the LEHCPEB treatment operating in the evaporation mode at the sample surface.

Figure 10: EPMA line scan analysis of the melted layer present locally at the surface of the samples after the LEHCPEB treatment 15 pulses [6].

Results of SNMS (sputter neutral mass spectrometry, VG instrument) analysis are shown in Figure 11 where the evolution of the amount of the major elements—Ti and Al—is plotted as a function of the distance from the surface for the near α titanium TA15 samples treated with 23.4 kV. Chemical modifications are clearly visible at the top surface of the melted layers: the Ti concentrations increase while the Al concentrations decrease when approaching the surface. For the 5 pulsed sample (Figure 11(a)), starting from a depth of about 250 nm, the Ti content can reach about 88.5 at%, slightly higher than the average concentration in matrix (87.7 at%). Comparatively, the Al concentration decreases to about 10.5 at% instead of the initial 11.3 at%. For the 10 pulsed sample (Figure 11(b)), the chemical modifications in the surface layer are more pronounced. They start from a depth of about 400 nm and the Ti content reaches the maximum value at about 89 at% at the top surface while the Al concentration decreases to about 9.8 at%. Numerical calculation also confirmed that the Al element is more prone to evaporate than the Ti element. The evaporation of Al is more pronounced at higher number of pulses indicated that more energy input can generate a more significant evaporation phenomenon. This more pronounced change in chemistry modification in terms of magnitude and depth with increasing number of pulses when the evaporation mode is taking place is consistent with previous results on a NiTi alloy [20].

Figure 11: SNMS composition profiles in Ti and Al for the TA15 near α titanium alloy. Experimental conditions are (a) 23.4 KeV 5 pulses; (b) 23.4 KeV 10 pulses.

#### 6. Modification of Surface Crystallographic Textures

An interesting effect of the LEHCPEB surface treatment is the modification of the surface crystallographic texture without changing the macroscopic shape of the sample. In a classical manner, this can be done when the top surface that has been melted resolidifies by the nucleation and growth of new grains. The growth of the new grains follows the major thermal gradient (perpendicular to the surface) along which some preferred orientations can grow more rapidly; creating thereby a solidification texture. As previously stated, it is also well established that evaporation can become significant at high energy densities [2, 35]. This phenomenon was suggested to lead to a modification of the atomic attachment along the growing solidification interface leading to the development of specific solidification textures in the rapidly solidified layer [20]. Another interesting phenomenon reported recently is the modification of crystallographic surface texture by treating the material below the onset of melting (the so-called heating mode) [24, 25].

Figure 12 shows the EBSD analysis of the surface of an FeAl alloy before and after the LEHCPEB treatment. The standard triangle is shown inset. The initial extruded bar was obtained from milled powder and the initial sample was cut perpendicular to the extrusion axis. The EBSD map in Figure 12(a) shows that a majority of grains have a green color. This illustrates that the as-extruded bar is characterized by a <110> fiber texture along the extrusion axis [36]. This is typical of extruded body-centered cubic metals. Figure 12(b) shows an EBSD map obtained from the surface of a sample treated for 20 pulses of LEHCPEB under the heating mode [25]. The fraction of large angle grain boundaries (LAGBs) is increased quite substantially due to the creation of new subgrains inside the initial grains, as witnessed by the presence of numerous LAGBs (in white) visible in Figure 12(b). These LAGBs must have been formed by the effect of the thermomechanical treatment associated with the LEHCPEB irradiation. Indeed, the material adjacent to the zone of energy transfer is rapidly heated, leading to the formation of a nonequilibrium temperature field coupled with dynamic stress fields propagating into the material. The maximum amplitude of thermal stress during treatment can reach values much higher than the yield strength of the material [5]. From the comparison of the maps in Figure 12, it is clear that many of the initially green grains (Figure 12(a)) have changed their colour, thereby indicating that the texture at the top surface has also been modified by the LEHCPEB treatment. The blue colour in the map—see the colour code in the inset standard suggests that the orientation of most of the grains has rotated towards <111> // the normal direction (ND) or in its vicinity. This modification is due to the heavy deformation and thermal cycles generated during each pulse that also lead to a complex combination of dynamic recovery and strain-induced grain boundary migration. Clearly, the thermomechanical treatment associated with the LEHCPEB treatment in the heating mode has drastically changed the surface texture and microstructure and, contrary to many processes involving plastic deformation, this is done without changing the macroscopic shape of the sample.

Figure 12: EBSD analysis showing the evolution of microstructure and texture of a FeAl alloy: (a) in the as-received state (extruded) and (b) after 20 pulsed of LEHCPEB treatment.

The treatment under the heating mode also modified the mechanical properties of the surface. Indeed, even after only 2 pulses, an increase of about 50 HV in hardness was associated with the LEHCPEB treatment at the surface of the FeAl sample (initially at 300 Hv). This was attributed to the formation of quenched-in vacancies, structural defects such as dislocation and subgrains, as well as the combination of grain refinement and texture modification toward the much stiffer <111> orientation [25]. In addition, LEHCPEB carried out on samples having their surface covered by graphite powder also demonstrates solid-state surface hardening and rapid solid-state surface alloying effects. This led to an increase of more than 100 HV (about 30%) associated with the thermally enhanced solid-state diffusion of C [25]. A final interest of the treatment under the heating mode is that the surface is free of any crater. Thereby, the corrosion resistance remains almost unchanged while other properties such as texture, grain size, and hardness can be modified to a significant extent [24].

As attested by the increasing number of papers published recently from different research groups [3746], the LEHCPEB surface treatment technique is now spreading worldwide seeking for additional new applications including, for example, surface cleaning, surface alloying [14, 32, 41, 42], surface strengthening, polishing, perforating, homogenization, and pre- or posttreatment.

#### 7. Summary and Conclusion

This article deals with the application of the low-energy high-current pulsed electron beam surface treatment technique on light alloys, such as pure Mg and Ti, Mg and Al alloys as well as FeAl.

The pulsed electron irradiation induces an ultra-fast thermal cycle at the surface combined with the formation of thermal stress and shock waves. The LEHCPEB-modified layer is usually divided into three successive regions having different orders of penetration depth: (i) a melted and rapidly solidified layer on the top surface (~1 μm), (ii) a heat-affected zone where solid state phase transformation, deformation and recrystallization may occur (~10 μm), and (iii) a stress-wave-affected zone that can be hardened (~100 μm).

The detailed analysis of Al and Mg alloys revealed that the plastic deformation associated with the imparted stresses results in deep subsurface hardening that can extend over several 100 μm. To this hardening is associated a significant improvement in the wear resistance.

The analysis of the top surface melted surface of light alloys also often witnesses evaporation and condensation of chemical species. This evaporation phenomenon can significantly modify the melt chemistry. Through second-phase dissolution and microstructure refinement in the melted layer, significant corrosion improvement can also be obtained.

Crystallographic texture modifications are also revealed by detailed analysis of the top surface of LEHCPEB-treated samples. The evaporation process was, for example, suggested to lead to the development of specific solidification textures in the rapidly solidified layer. Comparatively, as demonstrated by the analysis of FeAl samples, the potential use of the LEHCPEB technique for producing thermomechanical treatments under the so-called heating mode modifies the surface crystallographic texture without any melting of the surface or any macroscopic change of the sample size.

An additional interest of the heating mode is that the surface is free of any crater. Thereby, the corrosion resistance remains almost unchanged while other properties such as texture, grain size, and hardness can be modified to a significant extent.

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