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09.02.2021 | Full Research Article | Ausgabe 2/2021 Open Access

Zeitschrift:
Progress in Additive Manufacturing > Ausgabe 2/2021
Autoren:
Florian Kuisat, Fernando Lasagni, Andrés Fabián Lasagni

## 1 Introduction

Additive manufacturing (AM) processes are becoming more and more important for industrial applications because complex parts can be easily manufactured. A wide range of materials can be used for AM processes. Common metals are Ti64 and Scalmalloy ®. Due to their low weight and excellent strength properties, both materials are excellent materials for a wide range of applications, such as in the aerospace industry [ 1, 2]. The AM components are fabricated layer by layer from three-dimensional models, as opposed to traditional subtractive fabrication technologies. Numerous technologies such as Powder Bed Fusion (PBF) or Direct Energy Deposition (DED) exist for this purpose. Most of these technologies have in common that the powder particles are locally melted and solidified [ 3]. In the case of PBF process, a laser or electron beam scans and melts the powder layer to create the component. Due to the nature of the fabrication process, the manufactured parts have a relatively high roughness level on their surface, typically between 8 and 30 µm (Ra) for Laser PBF, which in some cases reduces their fatigue behavior and mechanical performance [ 4]. For instance, Sakar et al. demonstrated an improvement in fatigue life of laser-treated AM components of more than 100% compared to its as-built counterpart [ 5]. Other researchers have also shown enhancement of the stress resistance caused by surface post-treatment processes [ 6, 7]. This means that this is an extremely important characteristic of the surface quality, which is relevant to improve the technical capacities of these components such as fatigue lifetime [ 8, 9].
To improve the surface quality of AM parts, further production steps are frequently necessary [ 10]. Therefore, the roughness has to be decreased by means of a surface finishing process. Common surface finishing techniques are milling, blasting and vibration grinding [ 4, 11, 12]. However, the limited ability to treat complex shapes and geometries is often a challenge for these technologies [ 13, 14].
Another flexible post-processing technology for improving the quality of the 3D-manufactured parts consists of using laser surface treatments. Laser polishing has become a significant importance in the last 10 years and has several advantages against conventional polishing techniques [ 1518]. For example, laser-based methods work without employing mechanical forces and deformations and make it possible to polish complex three-dimensional geometries or workpieces with thin materials [ 19]. Due to the characteristic of the laser treatment process, the surface morphology can be changed based on re-melting, without the addition of polishing agents, chemicals or grinding materials [ 20].
Many ongoing research works concentrate on laser-based surface smoothing techniques. Mainly, continuous wave operating laser sources (cw) are used for macro-applications with remelting depths up to 200 µm. In contrast, pulsed laser sources (pw) are generally used for micro polishing with remelting depths of several micrometers [ 21]. Lambarri et al. investigated the laser surface smoothing process of nickel-based alloys and were able to show a reduction in roughness as a function of the scanning speed and laser power using cw laser radiation [ 22]. Similarly, Marimuthu et al. have examined that cw laser polishing of SLM components can be an effective way to improve the surface quality in Ti-6Al-4 V [ 23]. Pulsed laser radiation is partially used for micro polishing processes where the beam irradiates the material with laser pulses at a fluence level that causes surface melting and ablation. For example, Perry et al. showed a reduction of the average surface roughness Ra from 0.206 to 0.070 µm using a Nd:YAG laser source with 650 ns long pulses [ 24]. Also, Chow et al. have indicated that the surface quality can be improved by adjustment of the focal offset position of the laser radiation [ 25]. Many other research studies concerning laser polishing have been published by Propawe and other researchers [ 2629], reporting that the quality of the smoothing process can be controlled by diverse parameters such as the pulse duration, the laser power or the focal position. In addition, the quality of the smoothed surface depends on the base material and the initial surface topography and roughness. The reached results up to now have shown that laser smoothing can be used to successfully compete with conventional polishing processes. However, only a few publications are available on laser smoothing of the innovative additive manufactured Scalmalloy ® or Titanium 64 substrates [ 16, 2325, 30], defining the main objective of the present research. In particular, the use of an industrial laser system providing pulses in the nanosecond range for the post-treatment process of AM materials has not been sufficiently researched.
This work examines the utilization of nanosecond pulsed laser smoothing as innovative method to improve the surface quality of additive manufactured parts of Scalmalloy ® and Titanium 64. An important aspect of the investigation is to determine the achievable surface roughness levels. The experiments are conducted using a nanosecond-pulsed infrared laser source with variable pulse durations between 8 and 200 ns was applied. The topography of the treated samples is investigated using confocal microscopy as well as scanning electron microscopy.

## 2 Experimental procedure

### 2.1 Materials

Specimens of Ti6Al4V, also known as Titanium 64 (Ti64), and Scalmalloy ® (Al–Mg–Sc) were used in this study. The samples were produced by laser-Powder Bed Fusion which belongs to the category of additive manufacturing processes. This technology brings the best resolution and accuracy of current metal AM methods. These materials are characterized by high strength and high ductility combined with lightweight and are today the most used additively manufactured alloys for aerospace components [ 31, 32].
Ti6Al4V and Scalmalloy ® used powders were supplied by Renishaw and TOYAL Europe, respectively. The chemical composition of the main alloying elements for the Al–Mg–Sc alloy used in this study ranged from 4.5–4.9 Mg, 0.68–0.80 Sc, 0.2–0.4 Zr and 0.2–0.7 Mn (all compositions in wt%). More detailed information can be found in [ 1]. The particle size distribution for this alloy was D10 = 30.6 µm, D50 = 48.0 µm, D90 = 69.1 µm with an average particle size of 51.0 µm. Particles were mostly spherical, with circularity values (obtained from optical microscopy) between 0.78 and 1.00 for more than 50% of the particles.
For the case of Ti64, the composition of the main alloying elements ranged between 5.5 and 6.75 Al, 3.5–4.5 V (see details in [ 33]). The average particle size was 36.8 µm, with the following particle size distribution: D10 = 24.2 µm, D50 = 35.8 µm, D90 = 61.2 µm. Also, in this case, mostly spherical particles were observed, with circularity values between 0.85 and 1.00 for more than 50% of the particles.
The samples were manufactured on Renishaw AM250 and RenAM 500 systems for Ti6Al4V and Scalmalloy ®, respectively, under argon atmosphere. The layer thickness was set to 30 µm in both cases. Samples were also thermally treated before extraction at 325 °C during 4 h (annealing/aging) in air atmosphere followed by slow cooling for Scalmalloy ®, and at 730 °C during 1.5 h (annealing) in a vacuum with Argon atmosphere following by slow cooling.
Based on the used manufacturing process, the initial surface roughness ( Sa) was 21.20 ± 2.85 µm for Ti64 and 19.58 ± 9.04 µm for Scalmalloy ®. Prior to the laser smoothing process, the samples were cleaned with isopropanol to remove dirt particles.

### 2.2 Direct laser smoothing

The laser experiments were realized using the direct laser writing (DLW) technology, which were performed on an industrial laser system (GF machining solutions P 600). The setup is illustrated in Fig.  1a. The DLW workstation uses a Ytterbium fiber laser source which emits light with a wavelength of 1064 nm with a maximal output power of 30 W depending on the pulse duration. The maximal available laser power decreases for shorter pulse durations at constant repetition rate. For instance, the maximal laser power at a frequency of 30 kHz is approximately 30 W for a pulse duration of 200 ns, 14 W for 100 ns and 2.5 W for 8 ns. The pulse duration can be set between 4 and 200 ns. The laser beam was focused on the sample with an f-theta lens with a focal length of 254 mm. This results in a working distance of approx. 280 mm from the laser head.
In this study, the highest laser power was used for all pulse durations. The laser fluence F per pulse can be adjusted by changing the laser spot diameter at the irradiated region which is controlled by the working position. This methodology has been already used by Mai and Lim [ 34] as well as Chow et al. [ 25]. The focused laser beam has a spot diameter of approx. 70 µm, where the highest fluence level can be achieved. Three different working positions were utilized. The laser beam was scanned over the surface using a galvanometer scanner, with a maximal speed of 3.6 m/s. To achieve a homogenous smooth surface, two different scan strategies were examined. Parallel process strategy and 90° rotated process strategy were considered as shown in Fig.  1b, c.
The number of scans for both process strategies were also examined and varied between 1 and 10. The pulse overlap in y-direction and the hatch distance in x-direction were varied between 80 and 99%. This can be calculated by the pulse separation distance and the laser spot diameter [ 35]. The pulse overlap was adjusted by constant triggering the laser pulses with 30 kHz and changing the scan speed (30 mm/s up to 3600 mm/s). Using Eq. ( 1), it possible to calculate the laser fluence ( F) at the laser spot:
$$F\; = \;\frac{{P_{L} }}{f\;A^{\prime}},$$
(1)
where P L is the average laser power, f is the repetition rate (or frequency) and A is the irradiated area. The parameters used in this study are summarized in Table 1.
Table 1
Overview of selected parameters
Parameter
Value/range
Laser fluence (J/cm 2)
0.57–24.0
Focus offset position (mm)
0.0, 3.0, 6.0
Frequency (kHz)
30
Pulse duration (ns)
8, 20, 50, 100, 200
Overlap/hatch distance (%)
0–99
Number of scans
1–10
For the smoothening test, matrices with areas of 2 × 2 mm were processed for each parameter. All experiments were performed in air, at normal conditions of pressure and temperature.

### 2.3 Surface characterization

For the examination of the morphology of the laser-treated surfaces, a confocal microscope (Sensofar S Neox) with 20 × magnification was used. The roughness parameter Sa (arithmetical mean height), which is an extension of Ra to a surface, was measured according to ISO 25178. For statistical analyses, different positions in each treated are were measured. A Scanning Electron Microscope (ZEISS Supra 40 VP) was used to analyze the surface topology of the samples at an operating voltage of 5.0 kV.

## 3 Results and discussion

Using the infrared DLW setup, Ti64 and Scalmalloy ® substrates were laser treated to examine the influence of the processing parameters on the surface roughness. Firstly, the effect of the pulse duration and the laser fluence were investigated, as shown in Effect of pulse duration and focus position on the surface roughness. The laser fluence was varied by changing the offset position of the DLW configuration. A second set of experiments was performed with the previously selected focus offset position and pulse duration for both materials. In this case, the influence of the pulse overlap, moving direction as well as the number of scans on the surface roughness were tested. These results are shown in Surface smoothing by changing of number of passes and moving directions. Finally, the ablation characteristic caused by the laser treatment process with the used ns-pulses is described in detail in Material removal due to the smoothing process.

### 3.1 Effect of pulse duration and focus position on the surface roughness

In the first set of experiments, the effect of the pulse duration and the amount of energy applied into the workpiece on the surface roughness were investigated. Three different focus positions were chosen to determine the spot diameter and, therefore, the energy which was applied to the material. Depending on the position where the beam interacts the surface, the laser can either heat, melt or ablate the material. The process strategy follows the approach described in detail by Chow et al. [ 25]. The laser fluence also depends on the pulse duration and was varied between 8 and 200 ns. Shorter pulse durations are accompanied by smaller laser fluence. A summarized overview of the parameters used here is shown in Table 2.
Table 2
Overview parameter screening set 1
Focus position (mm)
Spot diameter (µm)
Laser fluence (J/cm 2)
0.0
70
2.1 (8 ns)–23.4 (200 ns)
3.0 (position 1)
90
1.3 (8 ns)–14.1 (200 ns)
6.0 (position 2)
135
0.5 (8 ns)–6.2 (200 ns)
Based on the state of the art, it is clear that the choice of parameters plays an important role in the quality of the final surface finish. In this regard, the change of Sa, by varying the focus position between 0 and 6 mm as well as the pulse duration between 8 and 200 ns, is shown in Fig.  2. As it can be observed, these parameters strongly influenced the surface topography depending on the material. For a better understanding of the effect of the laser processes on the surface roughness, the initial surface roughness is marked in green in Fig.  2, where the dashed lines denote the standard deviation. The large observed standard deviation for the reference surfaces can be explained by the quite irregular topography of these specimens. The obtained results show that the pulse duration is the most relevant parameter influencing the surface roughness, as it can be observed for Ti64 in Fig.  2a and for Scalmalloy ® in Fig.  2b.
The treatment of the Ti-alloy (Fig.  2a) follows a comparable scheme for all pulse durations depending on the focus positions. No significant variation in surface roughness was observed for pulse durations below 20 ns. This suggests that the applied energy was insufficient and the material was only heated. By increasing the pulse duration, the surface roughness begins to decrease which can be explained by the higher applied energy into the material. As a result of the higher energy input, the material begins to melt and the initial high roughness peaks are reduced by re-melting. This phenomenon can be observed at all examined focus offset positions. By increasing the pulse duration up to 100 ns, the roughness of the Ti64 samples could be significantly reduced. For example, the Sa-value was reduced from 21.20 to 7.9 µm when using the focus offset position 2. In general, it can be observed that a focus offset has a positive effect on the roughness which can be explained by the increased spot diameter and thus a decreased applied energy per area. A further increasing of the pulse duration to 200 ns leaded to an increase of the roughness, which indicates that the amount of energy introduced into the material was too high, producing a larger volume of molten material and even starting an ablation process. For this pulse duration (200 ns), the strongest increase of the surface roughness was observed on the sample treated at the focus offset position 1. In this case, the surface roughness increases from 21.2 to 41.7 µm. In consequence, the optimal process condition for smoothing the surface of the titanium alloy was at a pulse duration of 100 ns and a focus offset position of 6.0 mm, and were used for the rest of the experiments performed in this study.
A different behavior was observed for Scalmalloy ®. In this case, the effectiveness of the roughness reduction sing short pulse durations (up to 100 ns) is low. As it can be seen in Fig.  2b, all measured surface roughness was in the range of the statistic standard deviation of the reference sample (from 10.5 to 28.6 µm). A positive effect on the surface roughness was only visible when longer pulses (200 ns) were used. This leads to the assumption that the thermal energy input was too low to sufficiently affect the material with pulse durations below 200 ns. For instance, at the focus position, the surface roughness decreased from 19.6 to 8.6 µm. This suggests that the complete irradiated area was remelted using the focused beam. As a result, the molten material flows into the valleys and reduces the roughness. However, for the focus offset position 2, the roughness was not affected, while at the focus position 1, the surface roughness increased to 38.4 µm. This effect can be explained due to the fact, that the thermal applied energy was too low at the focus offset position 2 to affect the material. The material was neither ablated nor remelted. When using the focus offset position 1, the thermal energy introduced into the material was higher, which resulted in more molten material. Nevertheless, the applied energy was not sufficient to remelt the roughness peaks and thus reduce the roughness. It also seems, that the valleys of the material were affected by the laser and created material craters. The created craters and the initial roughness peaks had a negative effect on the roughness, which resulted in an increase in the roughness value. The optimal parameters in these experiments for Scalmalloy ® were at a pulse duration of 200 ns and the focused laser spot, without offset (0.0 mm).
In summary, the first experiments performed have shown that laser pulses with longer durations are more effective for reducing surface roughness: 100 ns and 200 ns for Ti64 and Scalmalloy ®, respectively. Based on these results, the above-mentioned pulse durations were used in the rest of this study.

### 3.2 Surface smoothing by changing of number of passes and moving directions

After the preliminary laser treatment experiments described in 3.1, a second set of experiments was performed. In this case, a large number of parameter variations were realized to find a correlation between the pulse-to-pulse overlap (OV = 80–99%) and the scanning strategy (parallel and 90° rotated, see Fig.  1) with the aim of reducing the surface roughness.
Figure  3 shows representative 3D images of the surface topography of both materials depending on the pulse overlap (OV). The surface topography images for the Ti64 (a–c) and Scalmalloy ® (d–f) samples provide evidence that the surface roughness can be significantly influenced by the laser process. In all cases, 10 passes were used. The confocal microscope images of Fig.  3 show that, for example, for a pulse overlap of 99% a very rough topography is obtained in both materials, which can be explained by the large amount of produced molten material due to the very high cumulated energy density (see Fig.  3a, d). In contrast, when the pulse overlap was lower, the amount of the molten material reduced and different surface conditions, depending on the material were observed, as shown in Fig.  3b, c, e–f.
Further evaluations were done to quantify the effects in detail. The measured results in terms of varying pulse-to-pulse distance and the movement strategy are summarized in Fig.  4a, b for Ti64 and in Fig.  4c, d for Scalmalloy ®. The measured surface roughness, or arithmetical mean height Sa, illustrates the strong effect of the laser treatment. As it can be seen in the figure, the highest pulse overlap (99%) led to the highest surface roughness (see confocal images in Fig.  3a, d for both materials). In this case, the amount of molten material strongly increased due to the high pulse overlap and thus the high amount of cumulated energy. This effect was observed for all number of performed scans (passes).
A different behavior was observed for smaller pulse overlaps. In this case, the effectiveness of roughness reduction using pulse overlaps between 80 and 95% was higher. As it can be seen in Fig.  4, many measured roughness values were below the statistical standard deviation of the reference samples. In particular, the surface roughness strongly decreased with the number of passes and the lowest value was achieved after 10 passes.
Clearly, the most important observation is that both materials can be smoothed, but with different parameters. In case of Ti64, the best results were obtained at 100 ns (as explained in the previous section) and a laser fluence of 3.1 J/cm 2. Differently, for Scalmalloy ®, the optimal conditions were with 200 ns pulses and a significantly higher laser fluence of 23.4 J/cm 2. These noticeable differences can be attributed to the different optical and thermal properties of the used materials, such as the reflection and thermal conductivity. For example, the reflectivity at normal incidence R (φ = 0) is approximately 0.55 for pure titanium and 0.95 for pure aluminum in the near-infrared region [ 36]. Due to the higher reflection and thus less absorption of the aluminum alloy (Scalmalloy ®), more energy per unit of area is required to treat the material. In addition, the higher thermal conductivity for Scalmalloy ® is responsible for a longer thermal diffusion length and thus higher fluences are needed to reach higher temperatures at the material surface.
From Fig.  4a, b, it can be also seen that in case of Ti64, the smoothest surface was achieved using a pulse overlap of 95%. Based on the surface topography analysis, it was found that in case of lower pulse overlaps (90%) and number of passes, the surface roughness was just marginally affected by the laser treatment. An important effect on the roughness reduction was only visible after 10 passes. In this case, the surface roughness was decreased from 21.20 to 14.20 µm, using the strategy “parallel” (10 passes and 90% Overlap). This means that each laser scan partially remelted the material surface, contributing positively to the reduction of the surface roughness.
Further improvements were observed for a pulse to pulse overlap of 95%. In this case, the roughness decreases continuously as function of the number of passes. This leads to the assumption that due to the higher cumulated energy, a continuous smoothing process takes place since more material peaks were remelted with each pass. The average surface roughness for the mentioned overlap after 10 passes was 7.22 ± 2.31 µm and 3.45 ± 1.30 µm for both strategies used, being parallel (Fig.  4a) and rotated (Fig.  4b), respectively. In consequence, the smoothest surface was obtained with a pulse overlap of 95% and 10 passes with rotated scanning strategy, which means a reduction of 84% of the initial surface roughness.
As indicated before, any positive effect could be observed by further increasing the pulse overlap (e.g., 99%). In this case, these high overlaps significantly increased the cumulated energy and in consequence, a significant of material can be molten or ablated (note that 95% overlap denotes that 20 pulses reached the same positions while for 99%, 100 pulses provide the laser energy to the material surface).
In contrast, in the case of Scalmalloy ®, different processing conditions were found to be more satisfactory for reducing the surface roughness. First of all, the standard deviation of the initial surface roughness of Scalmalloy ® was significantly higher compared to Ti64, as can be seen in Fig.  4c, d (see green area). As mentioned before, using a pulse overlap of 99% resulted in a strong increase in the roughness. This is an indication that the surface was strongly affected by the laser process. The higher pulse overlap results in a larger amount of molten material and even in local material ablation, which leads to additional surface features on the surface. Similarly, to Ti64, when using pulse overlaps of 90% and 95%, any significant variation on the roughness was observed since all evaluated conditions are in the range of standard deviation of the initial surface roughness. However, the lowest surface roughness for both used strategies was achieved when using 80% of pulse overlaps, which means that at 90% and 95% the laser process is also modifying the Scalmalloy ® surface. This leads to the assumption that the material was mainly heated and sparsely melted or ablated. Furthermore, by increasing the number of passes (up to 10 runs) and a pulse overlap of 90% or 95% an increase in surface roughness was observed, which leads to the assumption that not only the roughness peaks were remelted, but also that material was ablated and melt bulges were created. For a pulse overlap of 80%, the surface roughness was reduced by increasing the number of passes up to 10. In the last case, the measured surface roughness was significantly lower than the initial roughness. The average surface roughness after 10 runs for both scanning strategies was 6.84 ± 3.73 µm (Fig.  4c) and 8.60 ± 3.58 µm (Fig.  4d), respectively.
To closer examine the difference between the initial surface and the treated surface, SEM images of both states and materials were considered. The images of the initial and selected laser-treated surface are shown in Fig.  5. The results of the laser-treated samples with 10 scans show the best outcomes, as it was explained above. Comparing the original surface (Fig.  5a, c) and the treated surface (b, d), it is clear that the laser process has strongly modified the surface of both materials. As it can be observed, the untreated surfaces are characterized by drop-shaped roughness peaks, which is typical of non-treated surfaces in the as-manufactured condition. They have the largest roughness levels mainly caused by the partially melted powder particles attached to the surfaces. In contrast, the topography of the treated surfaces is very different. In the case of Ti64 (Fig.  5a, b), it is visible that the treated surface shows a very flat and homogeneous surface topography. In addition, very few melt drops with sizes below 2–5 µm are observed. In the case of Scalmalloy ®, it is also visible that large droplets in the untreated material were removed (Fig.  5c), but the final surface topography (Fig.  5d) is quite different compared to Ti64. A probable explanation for the observed topography can be related to nanoparticles and clusters of molten metal that are deposited from the ablation cloud, which were formed during the ns laser process. Such an effect has been already observed in other aluminum-based alloys as described by Boinovich et al. [ 37]. Furthermore, also other processes take place during multi-pulse laser treatment, such as high-temperature interactions between the melted surface layers and droplets of molten material as well as its suboxides in the laser ablation plume which could favor the formation of this topography.
Based on the experimental data presented before, several statements can be made about adjusting laser parameters and the general laser smoothing process. Firstly, it is clear that the surface quality, in terms of reducing the mean roughens Sa, can be achieved by adjusting the pulse-to-pulse overlap. The results also indicate that several passes of the laser beam over the same area can have a positive effect on surface flattening if the correct overlap is used. Thus, in general, it can be said, that it is more effective to work with a lower pulse overlap but more laser scan runs. A further observation is that the surface roughness was not significantly influenced by the scan strategy. In addition, it has to be mentioned that the standard deviation of the surface roughness after the laser process is significantly lower than the deviation of the initial surface roughness, which was observed for both materials. This means that the roughness peaks have been remelted and that the surface was leveled.

### 3.3 Material removal due to the smoothing process

After evaluating and defining the most relevant processing parameters for the smoothing process of the different materials, the surface levels of the untreated and treated areas were measured (ablation depth). A graphical representation of the increasing ablation depth due to the number of passes is shown in Fig.  6a. To quantify the ablation depth, the height difference of the untreated and laser-treated area was measured. An example is shown in Fig.  6b for Ti64 treated with an overlap of 95% and 10 passes.
From Fig.  6a, it can be seen that the ablation depth is relatively small for one or two laser scans (< 2.5 µm). However, a significant increase in the depth can be observed for more than two passes. The increased ablation depth is clearly related to the cumulated applied energy due to the repeated passes. Thus, these results indicate that the material was not only melted but also ablated. The maximum obtained ablation depths were 44.6 ± 7.5 µm for Ti64 and 60.4 ± 7.6 µm for Scalmalloy ®. These ablation depths were produced after 10 passes and pulse durations of 100 ns and 200 ns, respectively. This effect is nearly independent of the movement strategy, as mentioned in the previous section. In general, it can be said that the ablation depth is slightly higher for Scalmalloy ® than for Ti64 and can be attributed to the higher laser fluence used (3.1 J/cm 2 and 23.4 J/cm 2 for Ti64 and Scalmalloy ®, respectively). In consequence, the material removal due to the laser smoothing process has to be considered in the design of the 3D part to match the required dimensions.

## 4 Summary and conclusions

In this study, experimental research was carried out to better understanding the smoothing process of additive manufactured components of Ti64 and Scalmalloy ® using ns-laser pulses. The following most relevant findings can be drawn from this work:
(i)
First, it was demonstrated the capability of nanosecond pulses for reducing the surface roughness of additive manufactured Ti64 and Scalmalloy ® alloys.

(ii)
The reached surface roughness significantly depended on the material and the used parameter such as applied fluence, pulse duration, pulse-to-pulse overlap and number of passes.

(iii)
The laser treatments permitted the reduction of the surface roughness from 21.20 ± 2.85 µm to 3.45 ± 1.3 µm for Ti64 and from 19.58 ± 9.04 µm to 6.84 µm ± 3.73 for Scalmalloy ®, which corresponds to 84% and 65%, respectively.

(iv)
It was also shown that not only the roughness can be reduced, but also its standard deviation (by more of 50%) which means that the larger particles are molten or ablated. This lead to a more homogeneous surface topography and could consequently increase the mechanical performance.

(v)
It was observed that the pulsed laser treatment method is partially ablating the used materials, and that the ablation depth strongly depends on the number of passes. In consequence, the material removal due to the laser smoothing process has to be considered in the design of the 3D part

In future investigations, the effect of laser polishing on the alloy fatigue life will be explored, assessing also the microstructural differences of the heat-affected zone in comparison with the bulk material.

## Compliance with ethical standards

### Conflict of interest

On behalf of all authors, the corresponding author states that there is no conflict of interest.
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