# Photoreflectance and Raman Study of Surface Electric States on AlGaAs/GaAs Heterostructures

Authors: Luis Zamora-Peredo; Leandro García-González; Julián Hernández-Torres; Irving E. Cortes-Mestizo; Víctor H. Méndez-García; Máximo López-López
Journal: Journal of Spectroscopy
 (2016)

---

## Abstract

Photoreflectance (PR) and Raman are two very useful spectroscopy techniques that usually are used to know the surface electronic states in GaAs-based semiconductor devices. However, although they are exceptional tools there are few reports where both techniques were used in these kinds of devices. In this work, the surface electronic states on AlGaAs/GaAs heterostructures were studied in order to identify the effect of factors like laser penetration depth, cap layer thickness, and surface passivation over PR and Raman spectra. PR measurements were performed alternately with two lasers (532 nm and 375 nm wavelength) as the modulation sources in order to identify internal and surface features. The surface electric field calculated by PR analysis decreased whereas the GaAs cap layer thickness increased, in good agreement with a similar behavior observed in Raman measurements (I
L
-
/
I
LO ratio). When the heterostructures were treated by Si-flux, these techniques showed contrary behaviors. PR analysis revealed a diminution in the surface electric field due to a passivation process whereas the I
L
-
/
I
LO ratio did not present the same behavior because it was dominated by the depletion layers width (cap layer thickness) and the laser penetration depth.


---

## Body

## 1. Introduction

GaAs, with five times higher electron mobility compared to silicon, has a potential to achieve ultrafast electronic and optoelectronic devices. However, this semiconductor suffers from pronounced effects associated with its surface or interfaces: in particular, the large densities of GaAs surface electronic states that pin the Fermi level at midgap and result in large surface recombination velocity (106 cm/s). In order to eliminate chemical instability that may cause undesired effects, it is well established that the surfaces of GaAs-based devices have to be treated suitably. Frequently, the surfaces of semiconductor devices are passivated in order to stabilize their chemical nature and to eliminate reactivity. Ammonium polysulfide (NH4)2Sx has been frequently used to passivate the surface of GaAs with covalently bonded sulfur atoms [1–9]. However, sulfur passivation only provides short-term surface stability. In order to get more stability, a silicon interface control layers (Si ICL) approach has been proposed by Hasegawa and Akazawa [10–12] as a complement to high-k dielectric oxide surface layers such as HfO2 [13–16], AlO3 [16, 17], and SiO [18]. Other studies have been made with self-assembled monolayers (SAMs) of octadecanethiol (ODT) and dodecanethiol (DDT) [19, 20].Specifically, with AlGaAs/GaAs heterostructures there are reports about the effect of the surface on the electronic properties. In particular, the relationship between the surface electric field and electron mobility in the two-dimensional electron gas (2DEG) achieved in the AlGaAs/GaAs interface has been studied [21–31]. Other studies with heterojunction bipolar transistors [32], high electron mobility transistors [33–35], quantum Hall effect [36], and nanostructure-based devices [37–41] have been reported.Photoreflectance and Raman spectroscopy are very useful approaches that have been widely used for the study of GaAs-based devices [4, 23–31]. The PR technique has been used to study the AlGaAs/GaAs system in numerous reports, which were focused on determining the origin of Franz-Keldysh oscillations (FKO) that usually are observed at the PR spectra [24–31]. Today we know that wide-period FKO observed between 1.42 and 1.7 eV are associated with the surface electric field and short-period FKO just above 1.42 eV originate from internal AlGaAs/GaAs interfaces [31]. In the Raman spectroscopy case, there are many reports where it is employed as a useful tool to explore the surface passivation of GaAs films and AlGaAs/GaAs heterostructures. It is well accepted that the relative intensity between longitudinal optical (LO) and coupled plasmon-phonon (L−) modes can reveal useful information about the surface passivation of GaAs [5–7, 20, 42–45].In this work, we studied a set of AlGaAs/GaAs heterostructures by photoreflectance and Raman spectroscopy in order to make a comparative study with both techniques. Samples with different thickness of the GaAs cap layer were grown in order to change the surface electric field. PR measurements with two different laser wavelengths were used in order to identify internal and surfaces features. In addition, we studied the effect generated by the in situ deposition of silicon monolayers (Si ML) over the cap layer of the heterostructure.


## 2. Experimental Details

A set of AlGaAs/GaAs heterostructures was grown on semi-insulating GaAs (100) substrate by molecular beam epitaxy. All samples have a 1μm thick GaAs buffer layer (BL), a first spacer layer (1SL) of 7 nm undoped AlxGa1−xAs, followed by an 80 nm thick Si-doped AlGaAs barrier (doping with 1.4 × 1018 atoms/cm3). Next, there is a second spacer layer (2SL) of 7 nm undoped AlxGa1−xAs. Nominal Al concentration of 32% was used for the AlGaAs layers. Finally, the structure was capped with an undoped GaAs layer (see Figure 1). The thickness of the top layer was 25, 60, and 80 nm for samples M1, M2, and M3, respectively. Additionally, two more samples were grown with a 25 nm-GaAs cap layer and an in situ surface passivation treatment with Si-flux in order to get a nominal thickness of 1 and 2 ML, labeled M4 and M5, respectively. When the silicon was deposited the substrate temperature was fixed at 600°C and the arsenic flux was maintained in order to get a good quality surface.Figure 1
Schematic diagram of semiconductor layers in the heterostructures.F
s and F
i label the surface and internal electric field region, respectively.Photoreflectance (PR) measurements were carried out alternately with two solid-state lasers as modulation source (543 nm and 375 nm wavelengths, with a maxima output power of 12 and 10 mW, resp.) and chopped with a frequency of 200 Hz. A Sciencetech monochromator of 0.5 m focal distance was used. The experimental setup used was similar to those that are described elsewhere [23]. Using the 543 nm laser, it is possible to get a PR signal from the GaAs buffer layer because the penetration depth is close to 120 nm; however with a 375 nm line laser, the penetration depth is reduced significantly (<50 nm) [46]. All measurements were carried out at room temperature. Raman spectra were acquired with a Thermo Scientific confocal microscopy system arranged in a 180° backscattering configuration and equipped with a 532 nm solid-state laser with output power of 10 mW, 100x objective, and a charged-coupled device (CCD). 100 exposures and 10 s as collection time were used to collect Raman scattering. All spectra were normalized using the LO-GaAs mode intensity.


## 3. Results and Discussion

### 3.1. Effect of the Capping Layer Thickness

Figure2 shows room temperature PR spectra of M1 obtained with two different lasers as modulation source: with 532 nm (black line) and with 375 nm (red line). In the PR spectrum obtained with 532 nm, it is possible to see three features: a short-period Franz-Keldysh oscillation (s-FKO) at 1.42 eV associated with the GaAs energy band gap, a wide-period Franz-Keldysh oscillation (w-FKO) between 1.42 and 1.6 eV, and a wide oscillation associated with the AlGaAs energy band gap. PR obtained with a 375 nm laser does not have the first feature, which indicates that it originates from an internal AlGaAs/GaAs-BL interface considering that the 375 nm laser has a penetration depth smaller than 50 nm. Bessolov et al. estimated a penetration depth of 108 nm with a 514.5 nm line laser and 50.8 nm for a 457.9 nm line [6]. The w-FKO is observable with both lasers, which indicates that it originates from the surface GaAs layer. In previous reports this feature has been associated with the surface electric field [31]. Finally, at 1.8 eV we can see the feature originates from the AlGaAs layers, which offers information about energy band gap and consequently of the Al concentration. Considering that PR spectra originate mainly from interfaces, it is possible to establish that this oscillation originates from the GaAs/AlGaAs interface nearest to the surface because it is observed with both lasers.Figure 2
PR spectra of M1 heterostructure obtained with 532 nm (black line) and 375 nm (red line) lasers as modulation source.In order to diminish the surface electric fieldF
s originating from the electron migration from the AlGaAs:Si layer to the surface (see Figure 1), the M2 and M3 samples were grown with a GaAs cap layer of 60 and 80 nm thickness, respectively. Figure 3 shows PR spectra obtained with the 375 nm laser. The s-FKO feature vanishes for all samples. The w-FKO shows a reduction on its periodicity originating from the diminution of the surface electric field. The feature associated with the AlGaAs layer is only observed in M1 and almost disappears in the M2 and M3 spectra, due to the increase in the distance between the surface and the AlGaAs layer (2SL).Figure 3
PR spectra of M1, M2, and M3 heterostructures, capped with 25, 60, and 80 nm GaAs layer, respectively. The 375 nm laser was used as modulation source.To determine the electric field magnitude associated with the FKO, we considered the asymptotic modulation expression for the electroreflectance proposed by Aspnes and Studna [47]:(1)
Δ
R
R
∝
1
E
2
E
-
E
g
exp
⁡
-
2
Γ
E
-
E
g
ℏ
θ
3
/
2
cos
⁡
4
3
E
-
E
g
ℏ
θ
3
/
2
+
χ
,where ℏ
θ is the electrooptic energy, Γ is the linewidth, E
g is the band gap energy, and χ is an arbitrary phase factor. The electric field F is related to ℏ
θ by the expression(2)
ℏ
θ
=
e
2
ħ
2
F
2
2
μ
1
/
3
,where μ is the electron-hole reduced mass and e is the electron charge.In this model, the position of annth extreme in the FKO is given by(3)
n
π
=
4
3
E
n
-
E
g
ℏ
θ
3
/
2
+
χ
,where n is the index and E
n is the corresponding energy.Equation (3) can be rearranged as(4)
4
3
π
E
-
E
g
3
/
2
=
ℏ
θ
3
/
2
n
-
ℏ
θ
χ
π
.As we can see, (4) corresponds to a linear function with slope ℏ
θ
3
/
2, which can be determined using experimental data by a linear fitting of the plot of 4
/
3
π
E
-
E
g
3
/
2 versus the index number n. Next, F can be determined using (2).Figure4 shows the linear fit obtained with experimental data from the w-FKO extreme in PR spectra of M1, M2, and M3 where it is evidence of the reduction of the surface electric field (F
s) as the cap layer thickness increases. As we can see in Table 1, the magnitude of F
s decreases from 5.99 to 3.57 and 3.40 × 105 V/cm (reduction of 43.2%) for M1, M2, and M3, respectively.Table 1
Cap layer thickness, surface electric field (F
s) obtained from PR measurements, and I
L
-/I
L
O ratio calculated from Raman measurements.
Sample
Cap (nm)
Si (ML)
F
s (107 V/m)
I
L
-/I
L
O
M1
25
0
5.99
0.1699
M2
60
0
3.57
0.1407
M3
80
0
3.40
0.1345
M4
25
1
5.91
0.1896
M5
25
2
5.08
0.1772Figure 4
Linear fit in w-FKO analysis from PR spectra of M1, M2, and M3.Figure5 shows Raman spectra of heterostructures M1, M2, and M3 (cap layer thickness of 25, 60, and 80 nm, resp.) where there are observed four vibration modes: the coupled plasmon-phonon (L−) and longitudinal optical (LO) from the GaAs cap layer localized at 268 and 291 cm−1, respectively and two modes originating from the AlGaAs layers (LO GaAs-like and LO AlAs-like) located at 281 and 377 cm−1, respectively. All Raman spectra were normalized at LO GaAs mode intensity. L− mode intensity is lower than the LO GaAs mode because the GaAs layers (cap and BL) are undoped. The effect of increasing the cap layer thickness is palpable with the LO GaAs-like and LO AlAs-like modes intensity because both decrease as the surface GaAs thickness increases.Figure 5
Raman scattering of M1, M2, and M3 heterostructures, capped with GaAs layer of 25, 60, and 80 nm, respectively.In n-doped GaAs films, the LO peak (291 cm−1) is attributed to the surface depletion layer whereas L− mode originates from the bulk where free carriers exist [3–7, 20, 42–44]. In this case, the cap layer thickness is the same as the wide depletion layer as we can see in Figure 1. Then the LO intensity (I
LO) will be increased as the cap layer thickness increases and therefore we can use the I
L
-
/
I
LO ratio to study the surface states. A summary of the measured values for the I
L
-
/
I
LO ratio acquired from Raman spectra in Figure 5 is presented in Table 1. Figure 6 plots the surface electric field obtained by PR (black point) and Raman ratio I
L
-
/
I
LO (red circle) as a function of cap layer thickness. As we can see, both techniques show a similar behavior of the surface electric field in these heterostructures. Similar comportment of the surface electric field has been found by Kudrawiec et al. in GaN Van Hoof structures studied by contactless electroreflectance [48].Figure 6
Behavior comparison of the surface electric field obtained by PR (black point) and Raman ratioI
L
-
/
I
LO (red circle) as a function of cap layer thickness.


### 3.2. Effect of Si Passivation

An analogous study was made with heterostructures passivated with Si-ML. In this case, the cap layer thickness remains constant and therefore a reduction of the surface states density is expected due to the passivation process originating from the formation of a SiO monolayer when the samples were exposed to the atmosphere. Figure7 shows PR spectra of M1, M4, and M5 in order to compare samples without (M1) and with Si-ML (M4 and M5). The oscillation at E > 1.7 eV associated with the AlGaAs layer did not disappear because the cap layer thickness was 25 nm for the three samples and the laser penetration depth is bigger. The w-FKO period has a similar behavior for M1 and M4; however it presents a notable change in M5. Linear fit with experimental data from w-FKO extreme is shown in Figure 8. As we can see in Table 1, the surface electric field magnitude changes from 5.99 to 5.91 and 5.08 × 105 V/cm for M1, M4, and M5, respectively. These results suggest that the surface passivation process is occurring but could be insufficient to eliminate the surface state because the Si deposition was made at high temperature (~600°C).Figure 7
PR spectra of M1, M4, and M5 heterostructures passivated with 0, 1, and 2 silicon monolayers, respectively. The 375 nm laser was used as modulation source.Figure 8
Linear fit in w-FKO analysis from PR spectra of M1, M4, and M5.Figure9 shows Raman spectra of heterostructures M1, M4, and M5 (treated with 0, 1, and 2 Si-ML, resp.) where the same four vibration modes that were observed in Figure 5 are observed. All Raman spectra were normalized at LO GaAs mode. When the heterostructure is treated with Si monolayers it is possible to see some changes. In this case the LO AlAs-like peak originating from the AlGaAs layer does not decrease because the cap layer is of a thicknesses of 25 nm for the three samples. The I
L
-/I
LO ratio changes from 0.170 to 0.189 and 0.177 for M1, M4, and M5, respectively (Table 1).Figure 9
Raman scattering of M1, M4, and M5 heterostructures capped with a 25 nm GaAs layer and passivated with 0, 1, and 2 Si-ML, respectively. A 532 nm laser was used as excitation source.Figure10 plots the surface electric field obtained by PR (black point) and Raman intensity ratio I
L
-
/
I
LO (red circle) as a function of the Si monolayers. In this case, the PR measurement analysis gives a slight decrease of the surface electric field for samples with 1 and 2 Si-ML but Raman scattering insinuates a contrary situation. Considering that the surface depletion layer remains constant, we would expect an unchanged ratio I
L
-
/
I
LO. This disagreement between PR and Raman spectroscopy could be associated with the laser penetration depth because the laser used in Raman system is similar to PR measurements (Figure 2) so that it excites the GaAs buffer layer. Consequently, both cap and deeper GaAs layers influence Raman spectra. In previous studies with these kinds of heterostructures, we found that if the surface electric field decreases (as is suggested by PR measurements) a wider depletion zone is originated in the AlGaAs/GaAs-BL interface [49], which changes the Raman intensity ratio I
L
-
/
I
LO. That means that PR measurements are the best approach to study the surface electric field because Raman spectra are influenced by deeper GaAs interface.Figure 10
Behavior comparison of the surface electric field obtained by PR (black point) and Raman ratioI
L
-
/
I
LO (red circle) as a function of Si-ML.The PR analysis in this work is in good agreement with the engineering of electric field distribution in AlGaN/GaN heterostructures that widely has been studied by other authors where electroreflectance spectroscopy has shown similar behavior when the cap layer is modified [48, 50, 51]. The above suggests that PR spectroscopy is an excellent tool that could be used to explore more complex heterostructures like GaN/graphene/Si [52] or GaAs/Graphene/Si [53] where the internal electric field can give information about crystal quality.


## 3.1. Effect of the Capping Layer Thickness

Figure2 shows room temperature PR spectra of M1 obtained with two different lasers as modulation source: with 532 nm (black line) and with 375 nm (red line). In the PR spectrum obtained with 532 nm, it is possible to see three features: a short-period Franz-Keldysh oscillation (s-FKO) at 1.42 eV associated with the GaAs energy band gap, a wide-period Franz-Keldysh oscillation (w-FKO) between 1.42 and 1.6 eV, and a wide oscillation associated with the AlGaAs energy band gap. PR obtained with a 375 nm laser does not have the first feature, which indicates that it originates from an internal AlGaAs/GaAs-BL interface considering that the 375 nm laser has a penetration depth smaller than 50 nm. Bessolov et al. estimated a penetration depth of 108 nm with a 514.5 nm line laser and 50.8 nm for a 457.9 nm line [6]. The w-FKO is observable with both lasers, which indicates that it originates from the surface GaAs layer. In previous reports this feature has been associated with the surface electric field [31]. Finally, at 1.8 eV we can see the feature originates from the AlGaAs layers, which offers information about energy band gap and consequently of the Al concentration. Considering that PR spectra originate mainly from interfaces, it is possible to establish that this oscillation originates from the GaAs/AlGaAs interface nearest to the surface because it is observed with both lasers.Figure 2
PR spectra of M1 heterostructure obtained with 532 nm (black line) and 375 nm (red line) lasers as modulation source.In order to diminish the surface electric fieldF
s originating from the electron migration from the AlGaAs:Si layer to the surface (see Figure 1), the M2 and M3 samples were grown with a GaAs cap layer of 60 and 80 nm thickness, respectively. Figure 3 shows PR spectra obtained with the 375 nm laser. The s-FKO feature vanishes for all samples. The w-FKO shows a reduction on its periodicity originating from the diminution of the surface electric field. The feature associated with the AlGaAs layer is only observed in M1 and almost disappears in the M2 and M3 spectra, due to the increase in the distance between the surface and the AlGaAs layer (2SL).Figure 3
PR spectra of M1, M2, and M3 heterostructures, capped with 25, 60, and 80 nm GaAs layer, respectively. The 375 nm laser was used as modulation source.To determine the electric field magnitude associated with the FKO, we considered the asymptotic modulation expression for the electroreflectance proposed by Aspnes and Studna [47]:(1)
Δ
R
R
∝
1
E
2
E
-
E
g
exp
⁡
-
2
Γ
E
-
E
g
ℏ
θ
3
/
2
cos
⁡
4
3
E
-
E
g
ℏ
θ
3
/
2
+
χ
,where ℏ
θ is the electrooptic energy, Γ is the linewidth, E
g is the band gap energy, and χ is an arbitrary phase factor. The electric field F is related to ℏ
θ by the expression(2)
ℏ
θ
=
e
2
ħ
2
F
2
2
μ
1
/
3
,where μ is the electron-hole reduced mass and e is the electron charge.In this model, the position of annth extreme in the FKO is given by(3)
n
π
=
4
3
E
n
-
E
g
ℏ
θ
3
/
2
+
χ
,where n is the index and E
n is the corresponding energy.Equation (3) can be rearranged as(4)
4
3
π
E
-
E
g
3
/
2
=
ℏ
θ
3
/
2
n
-
ℏ
θ
χ
π
.As we can see, (4) corresponds to a linear function with slope ℏ
θ
3
/
2, which can be determined using experimental data by a linear fitting of the plot of 4
/
3
π
E
-
E
g
3
/
2 versus the index number n. Next, F can be determined using (2).Figure4 shows the linear fit obtained with experimental data from the w-FKO extreme in PR spectra of M1, M2, and M3 where it is evidence of the reduction of the surface electric field (F
s) as the cap layer thickness increases. As we can see in Table 1, the magnitude of F
s decreases from 5.99 to 3.57 and 3.40 × 105 V/cm (reduction of 43.2%) for M1, M2, and M3, respectively.Table 1
Cap layer thickness, surface electric field (F
s) obtained from PR measurements, and I
L
-/I
L
O ratio calculated from Raman measurements.
Sample
Cap (nm)
Si (ML)
F
s (107 V/m)
I
L
-/I
L
O
M1
25
0
5.99
0.1699
M2
60
0
3.57
0.1407
M3
80
0
3.40
0.1345
M4
25
1
5.91
0.1896
M5
25
2
5.08
0.1772Figure 4
Linear fit in w-FKO analysis from PR spectra of M1, M2, and M3.Figure5 shows Raman spectra of heterostructures M1, M2, and M3 (cap layer thickness of 25, 60, and 80 nm, resp.) where there are observed four vibration modes: the coupled plasmon-phonon (L−) and longitudinal optical (LO) from the GaAs cap layer localized at 268 and 291 cm−1, respectively and two modes originating from the AlGaAs layers (LO GaAs-like and LO AlAs-like) located at 281 and 377 cm−1, respectively. All Raman spectra were normalized at LO GaAs mode intensity. L− mode intensity is lower than the LO GaAs mode because the GaAs layers (cap and BL) are undoped. The effect of increasing the cap layer thickness is palpable with the LO GaAs-like and LO AlAs-like modes intensity because both decrease as the surface GaAs thickness increases.Figure 5
Raman scattering of M1, M2, and M3 heterostructures, capped with GaAs layer of 25, 60, and 80 nm, respectively.In n-doped GaAs films, the LO peak (291 cm−1) is attributed to the surface depletion layer whereas L− mode originates from the bulk where free carriers exist [3–7, 20, 42–44]. In this case, the cap layer thickness is the same as the wide depletion layer as we can see in Figure 1. Then the LO intensity (I
LO) will be increased as the cap layer thickness increases and therefore we can use the I
L
-
/
I
LO ratio to study the surface states. A summary of the measured values for the I
L
-
/
I
LO ratio acquired from Raman spectra in Figure 5 is presented in Table 1. Figure 6 plots the surface electric field obtained by PR (black point) and Raman ratio I
L
-
/
I
LO (red circle) as a function of cap layer thickness. As we can see, both techniques show a similar behavior of the surface electric field in these heterostructures. Similar comportment of the surface electric field has been found by Kudrawiec et al. in GaN Van Hoof structures studied by contactless electroreflectance [48].Figure 6
Behavior comparison of the surface electric field obtained by PR (black point) and Raman ratioI
L
-
/
I
LO (red circle) as a function of cap layer thickness.


## 3.2. Effect of Si Passivation

An analogous study was made with heterostructures passivated with Si-ML. In this case, the cap layer thickness remains constant and therefore a reduction of the surface states density is expected due to the passivation process originating from the formation of a SiO monolayer when the samples were exposed to the atmosphere. Figure7 shows PR spectra of M1, M4, and M5 in order to compare samples without (M1) and with Si-ML (M4 and M5). The oscillation at E > 1.7 eV associated with the AlGaAs layer did not disappear because the cap layer thickness was 25 nm for the three samples and the laser penetration depth is bigger. The w-FKO period has a similar behavior for M1 and M4; however it presents a notable change in M5. Linear fit with experimental data from w-FKO extreme is shown in Figure 8. As we can see in Table 1, the surface electric field magnitude changes from 5.99 to 5.91 and 5.08 × 105 V/cm for M1, M4, and M5, respectively. These results suggest that the surface passivation process is occurring but could be insufficient to eliminate the surface state because the Si deposition was made at high temperature (~600°C).Figure 7
PR spectra of M1, M4, and M5 heterostructures passivated with 0, 1, and 2 silicon monolayers, respectively. The 375 nm laser was used as modulation source.Figure 8
Linear fit in w-FKO analysis from PR spectra of M1, M4, and M5.Figure9 shows Raman spectra of heterostructures M1, M4, and M5 (treated with 0, 1, and 2 Si-ML, resp.) where the same four vibration modes that were observed in Figure 5 are observed. All Raman spectra were normalized at LO GaAs mode. When the heterostructure is treated with Si monolayers it is possible to see some changes. In this case the LO AlAs-like peak originating from the AlGaAs layer does not decrease because the cap layer is of a thicknesses of 25 nm for the three samples. The I
L
-/I
LO ratio changes from 0.170 to 0.189 and 0.177 for M1, M4, and M5, respectively (Table 1).Figure 9
Raman scattering of M1, M4, and M5 heterostructures capped with a 25 nm GaAs layer and passivated with 0, 1, and 2 Si-ML, respectively. A 532 nm laser was used as excitation source.Figure10 plots the surface electric field obtained by PR (black point) and Raman intensity ratio I
L
-
/
I
LO (red circle) as a function of the Si monolayers. In this case, the PR measurement analysis gives a slight decrease of the surface electric field for samples with 1 and 2 Si-ML but Raman scattering insinuates a contrary situation. Considering that the surface depletion layer remains constant, we would expect an unchanged ratio I
L
-
/
I
LO. This disagreement between PR and Raman spectroscopy could be associated with the laser penetration depth because the laser used in Raman system is similar to PR measurements (Figure 2) so that it excites the GaAs buffer layer. Consequently, both cap and deeper GaAs layers influence Raman spectra. In previous studies with these kinds of heterostructures, we found that if the surface electric field decreases (as is suggested by PR measurements) a wider depletion zone is originated in the AlGaAs/GaAs-BL interface [49], which changes the Raman intensity ratio I
L
-
/
I
LO. That means that PR measurements are the best approach to study the surface electric field because Raman spectra are influenced by deeper GaAs interface.Figure 10
Behavior comparison of the surface electric field obtained by PR (black point) and Raman ratioI
L
-
/
I
LO (red circle) as a function of Si-ML.The PR analysis in this work is in good agreement with the engineering of electric field distribution in AlGaN/GaN heterostructures that widely has been studied by other authors where electroreflectance spectroscopy has shown similar behavior when the cap layer is modified [48, 50, 51]. The above suggests that PR spectroscopy is an excellent tool that could be used to explore more complex heterostructures like GaN/graphene/Si [52] or GaAs/Graphene/Si [53] where the internal electric field can give information about crystal quality.


## 4. Conclusions

The surface electronic states on AlGaAs/GaAs heterostructures were studied by photoreflectance and Raman spectroscopy techniques. The surface electric field calculated by PR analysis decreased whereas the GaAs cap layer thickness increases in good agreement with a similar behavior observed in Raman measurements (I
L
-
/
I
LO ratio). When the heterostructures were treated with a Si-flux, these techniques showed contrary behaviors originating from the penetration depth of the laser used in the PR and Raman measurements. PR analysis found a slow diminishment in the surface electric field whereas the I
L
-
/
I
LO ratio observed in Raman analysis showed higher values than the sample without a Si-ML. This work illustrates how it is possible to use PR and Raman spectroscopy to study the surface electronic states in AlGaAs/GaAs heterostructures and the passivation process in this kind of semiconductor device.



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*Source: 4601249-2016-10-16.xml*