# Ab Initio Study of Electronic Transport in Cubic-HfO2 Grain Boundaries

Authors: Elena Degoli; Eleonora Luppi; Nathalie Capron
Journal: Journal of Nanomaterials
 (2017)

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## Abstract

In polycrystalline materials the grain boundaries (GBs) are particularly important as they can act as a sink for atom defects and impurities, which may drive structural transformation of the materials and consequently modify their properties. Characterising the structure and properties of GBs is critical for understanding and controlling material property. Here, we investigated how GBs can modify the structural, electronic, and transport properties of the polycrystalline materialHfO2. In general, grain boundaries are considered to be detrimental to the physical stability and electronic transport in HfO2. Anyway, studying by first principles the two most stable and common types of GBs, the tilt and the twist, we found substantial differences on the impact they have on the material properties. In fact, while tilt defects create channels of different sizes and shapes in hafnia along which the electronic transport is stronger in relation to leakage current through GBs, twist defects create a sort of amorphous structure that tends to resemble the bulk and which is independent of the number of rotated planes/atoms.


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## Body

## 1. Introduction

Grain boundary (GB) in a solid crystalline material is a region separating two crystals (grains) of the same phase. These two grains differ in mutual orientations and the grain boundary represents a transition region, where the atoms are shifted from their regular positions as compared to the crystal. In general, polycrystalline materials contain a wide variety of interfaces between grains that can be influenced by numerous factors, such as growth conditions and thermal treatment.In polycrystalline materials the GB is particularly important as it can act as a sink for atom defects and impurities, which may drive structural transformation of the materials and consequently modify their properties. In fact, GBs can change the mechanical strength, thermal dissipation, and electrical transport of the crystals and have consequences on their performance for specific applications in optoelectronics and photovoltaics. Therefore, characterising the structure and properties of grains and grain boundaries is critical for understanding and controlling material property.GBs appeared to severely weaken the mechanical strength [1] and to impede electrical transport [2] and transmission [3] of graphene. In crystalline monolayer molybdenum disulphide MoS2, depending on the type of GB formed in the crystal, an enhancement or a quenching of the photoluminescence and electrical conductivity was observed [4]. The presence of GBs can also trap electrons in semiconducting and insulating materials which is important for optoelectronic and photovoltaics applications [5]. Moreover, recently the presence of GBs in Si has been studied in order to engineer these defects to improve electronic and optical properties of Si in photovoltaic devices [6].In recent years, a particular interest was given to understand the role of GBs in the modification of the electronic and transport properties of transition-metal oxide hafnia (HfO2). In fact, HfO2 is nowadays considered the most promising candidate to replace silicon dioxide (SiO2) as the gate dielectric material in metal-oxide-semiconductors (MOS) and complementary MOS (CMOS) technology [7, 8]. Moreover, HfO2 is also very promising as material for resistive random access memories (RRAMs) [9, 10]. HfO2 has wide bandgap (5.7 eV) and high dielectric constant (22) and exhibits good thermodynamic stability. However, HfO2 suffers from important current leakage which has been related to neutral and charged oxygen vacancies [11, 12] and oxygen interstitials [13, 14] close to region where the GB is formed in HfO2. The leakage currents are related to the structure of the GB which presents favourable percolation paths for electron tunnelling [15–17]. For this reason, GBs are generally considered to be detrimental to the physical stability and electronic transport in HfO2. A clearer understanding and controlling of GBs become essential for optimising device performance and reliability.The aim of this work is to investigate how the GBs can modify the structural, electronic, and transport properties of the polycrystalline materialHfO2. We decided to start considering HfO2 in its cubic phase and to construct two different types of GBs: tilt and twist. We first studied the changes in the structural and electronic properties of cubic HfO2 due to the presence of GBs. Next, we investigated the transport properties in the framework of the Boltzmann transport equations. In order to interpret the results with respect to the experimental value we interpret the oxygen vacancy as donor which means that the system is n-doped and the interstitial oxygen as acceptor which means that the system is p-doped [18]. We do not consider possible relaxation or change in the band structures. The change of the doping is discussed as a function of the chemical potential. With this approach we want to clarify the mechanisms of electronic transport in GBs. We expect that our findings are general enough to be relevant in experimental conditions.


## 2. Computational Methodology

The structural and electronic properties of the systems studied in this work were calculated using first-principle density functional theory (DFT) as implemented in the plane-wave based Vienna Ab initio Simulation Package (VASP) [19, 20]. We employed the generalised gradient approximation (GGA) for the exchange-correlation functional in the parametrisation proposed by Perdew and Wang (PW91) [21]. We adopted projector augmented-wave pseudopotentials including the valence 5p, 5d, and 6s electrons for Hf and the 2s and 2p electrons for O. We used a plane-wave cut-off of 400 eV and Γ centered Monkhorst-Pack [22] k-mesh of 9×9×9 for the bulk, of 24×8×12 for the tilt, and of 12×12×16 for the twist GB structures. All the structures were relaxed until the Hellmann-Feynman forces exerted on each atom become less than 0.01 eV/Å. The electronic transport properties were calculated using the BoltzTraP (BoltzmannTransportProperties) code [23]. In particular, we analysed the conductivity σ in the rigid-band and constant relaxation-time approximation.


## 3. Results

### 3.1. Theoretical Models for HfO2 Grain Boundaries

We started by consideringHfO2 in its cubic phase and we found a lattice parameter of 5.07 Å, in agreement with other theoretical calculations and experiments [24–27]. From the cubic HfO2 we obtained tilt GBs by cutting the crystal along the (0  −1  3) plane and rotating it of 36.86° with respect to the [1  0  0] axis belonging to the plane of the boundary (see left panel of Figure 1). In a similar way we built the twist GBs by cutting the cubic HfO2 along the (3  1  0) plane and by rotating it of 36.86° with respect to the [0  0  1] axis perpendicular to the plane of the boundary (see right panel of Figure 1).Figure 1
The cubic phase ofHfO2 is presented where Hf atoms are in yellow and O atoms in red. A cartoon representation is presented to schematise the way tilt (left) and twist (right) GBs are constructed.In this way, we constructed two tilt GBs of the typeΣ5 36.86° (0  −1  3)/[1  0  0] and two twist GBs of the type Σ5 36.86° (3  1  0)/[0  0  1]. The Σ5 notation refers to the degree of site matching. Σ5 indicates a high symmetry and possibly low formation energy. Σ is simply evaluated as(1)Σ=δ×h2+k2+l2,where (hkl) is the plane of the boundary and δ is equal to 1 as (h2+k2+l2) is odd in our case [25]. The two tilt GBs differ in the number of atoms per unit cell: 72 atoms (Tilt72) and 108 atoms (Tilt108), and they are shown in Figure 2 before and after geometrical relaxation. The unit cell is orthorhombic and in the case of Tilt72 the cell parameters are a=5.11 Å, b=16.16 Å, and c=9.70 Å while in the case of the Tilt108 the parameters are a=5.11 Å, b=16.16 Å, and c=14.54 Å. In the case of the twist GBs the number of atoms per unit cell is 90 (Twist90) and 120 (Twist120) and they are shown in Figure 3 before and after geometrical relaxation. The unit cell is tetragonal and for the Twist90 the cell parameters are a=b=5.11 Å and c=8.18 Å while for the Twist120 they are a=b=5.11 Å and c=10.22 Å.Figure 2
Tilt72 and Tilt108 are shown before and after geometrical relaxation.Figure 3
Twist90 and Twist120 are shown before and after geometrical relaxation.The effects of the geometrical relaxation in the GBs structures are immediately observable in Figures2 and 3 and quantitatively shown in Tables 1 and 2 where we reported the distances between the atoms before (dnR) and after relaxation (dR), together with the percentage of relaxation (R). This percentage was calculated as R=(dR-dnR)/dnR∗100.Table 1
We report the distances between the atoms as labelled in Figure2 for Tilt72 and Tilt108 before (dnR) and after geometry relaxation (dR). We also report the percentage of relaxation R which is calculated as R=(dR-dnR)/dnR∗100.
d
n
R (Å)
d
R (Å)
R (%)
Tilt72
d
1
–
3
=
d
2
–
4
=
d
13
–
15
=
d
14
–
16
2.213
2.070
−6.46
d
3
–
5
=
d
4
-
5
=
d
15
–
17
=
d
16
-
17
2.213
2.016
−8.90
d
3
–
7
=
d
4
–
6
=
d
15
–
19
=
d
16
–
18
2.213
1.979
−10.57
d
5
–
9
=
d
5
–
8
=
d
17
–
21
=
d
17
–
20
2.213
2.875
29.9
d
7
–
9
=
d
6
–
8
=
d
19
–
21
=
d
18
–
20
2.213
2.190
−1.04
d
9
–
11
=
d
8
–
10
=
d
21
–
23
=
d
20
–
22
2.213
1.971
−10.94
d
11
-
12
=
d
10
–
12
=
d
23
-
24
=
d
22
–
24
2.213
2.114
−4.47
d
12
-
13
=
d
12
–
14
=
d
24
–
1
=
d
24
–
2
2.213
2.231
0.81
d
1
-
2
=
d
13
-
14
3.232
2.685
−16.9
d
3
-
4
=
d
15
-
16
1.616
2.527
56.4
d
7
-
6
=
d
19
-
18
4.848
4.848
0.0
d
9
-
8
=
d
21
-
20
3.232
3.895
20.5
d
11
-
10
=
d
23
-
22
1.616
2.325
43.9
d
5
–
12
=
d
17
–
24
4.237
4.453
5.1
d
12
–
17
=
d
24
–
5
4.237
4.037
−4.7
Tilt108
d
1
–
3
=
d
2
–
4
=
d
19
–
21
=
d
18
–
22
2.213
2.179
−1.5
d
3
–
5
=
d
4
-
5
=
d
21
–
27
=
d
22
–
27
2.213
1.966
−1.1
d
3
–
7
=
d
4
–
6
=
d
21
–
25
=
d
22
–
26
2.213
1.930
−1.27
d
5
–
13
=
d
5
–
12
=
d
27
–
29
=
d
27
-
28
2.213
3.602
62.7
d
7
–
9
=
d
6
–
8
=
d
25
–
31
=
d
26
–
30
2.213
1.880
−15.0
d
7
–
13
=
d
6
–
12
=
d
25
–
29
=
d
26
–
28
2.213
3.114
40.7
d
9
–
11
=
d
8
–
10
=
d
31
–
35
=
d
30
–
34
2.213
2.104
−4.9
d
11
–
13
=
d
10
–
12
=
d
29
–
35
=
d
28
–
34
2.213
2.081
−5.9
d
13
–
15
=
d
12
–
14
=
d
29
–
33
=
d
28
–
32
2.213
1.953
−11.7
d
15
–
20
=
d
14
–
20
=
d
33
–
36
=
d
32
–
36
2.213
2.116
−4.4
d
20
-
19
=
d
20
–
18
=
d
36
–
1
=
d
36
–
2
2.213
2.192
−1.0
d
5
–
15
=
d
5
–
14
=
d
27
–
33
=
d
27
–
32
2.213
2.971
34.2
d
1
-
2
=
d
19
-
18
3.232
2.524
−21.9
d
3
-
4
=
d
21
-
22
1.616
2.439
50.9
d
7
-
6
=
d
25
-
26
4.848
5.489
13.2
d
9
-
8
=
d
31
-
30
8.080
7.921
−2.0
d
11
-
10
=
d
35
-
34
6.464
7.771
20.2
d
13
-
12
=
d
29
-
28
3.232
5.065
56.7
d
15
-
14
=
d
33
-
32
1.616
2.288
56.4
d
17
-
16
=
d
37
-
38
4.848
3.709
23.5
d
5
–
20
4.237
4.188
−1.2
d
20
–
27
4.237
4.285
−1.1Table 2
Distances between Hf at the interface of the twisted planes and its neighbouring O atoms for Twin90 and Twin120 before and after relaxation. We also report the percentage of relaxationR which is calculated as R=(dR-dnR)/dnR∗100. In the bulk the distance between O and Hf is 2.195 Å.
d
n
R (Å)
d
R (Å)
R (%)
Twin90
d
1
1.512
2.064
36.51
d
2
2.213
2.000
−9.62
d
3
2.213
2.006
−9.35
d
4
2.213
2.032
−8.18
d
5
2.213
2.170
−1.94
d
6
2.213
2.199
−0.63
Twin120
d
1
1.512
2.017
33.40
d
2
2.213
1.988
−10.17
d
3
2.213
1.996
−9.81
d
4
2.213
2.074
−6.70
d
5
2.213
2.113
−4.82
d
6
2.213
2.160
−2.56In the case of the Tilt72, we labelled from 1 to 24 the atoms which play the most important role in the relaxation. All these atoms are symmetric with respect to thexy plane. The geometrical relaxation creates two almost spherical large channels and two small channels with a hexagonal structure. The initial distances between first neighbouring atoms are of 2.213 Å and then there is a compensation between elongation and compression which is at the origin of these channels. In particular, we observe that the bigger channels are due to a strong modification of the distances between atoms 5 (17) and 9 (21) and between atoms 5 (17) and 8 (20). The percentage of deformation is R=29.9%. The deformation can be also investigated by studying the change of distances along the z direction. Here, the maximum deformation is related to atoms 3 (15) and 4 (16) which is R=56.4%. Those atoms that do not play a role in the creation of the channels still keep the initial bulk distances. As a consequence, when repeating the unit cell in the space, we found that our structures are made of small and large channels with bulk-like regions in between. The mean extension of these regions is of the order of 6 Å.A similar result was obtained for the Tilt108 where we labelled from 1 to 38 the atoms which play the most important role in the relaxation. Also in this case, all the atoms are symmetric with respect to the plane of symmetryxOy before and after the geometrical optimisation. The relaxation creates two elongated large and small channels still with a hexagonal form. The smaller channels have similar relaxation distances and percentages of the Tilt72. The elongated channels are due to a strong modification of the distances between atoms 5 (27) and 13 (29) and between atoms 5 (27) and 12 (28). The percentage of deformation is R=62.7%. Also in this case, those atoms that do not play a role in the creation of the channels still keep the initial bulk distances leaving bulk-like regions in between channels. The mean extension of these regions is of the order of 6.3 Å.The twist GBs have a quite different behaviour. The rotation with respect to an axis perpendicular to the plane of the grain boundary does not create any channels in the structures as shown in Figure3 for the Twist90 and Twist120. In fact, the twist GB alternates planes of O and Hf with a different inclination. Through an analysis of the O and Hf distances, before and after relaxation, we observed that the structure has a general tendency to rearrange as in the bulk even if it is more compact. After relaxation, the Hf-O distances have almost the same value which is around 2.000 Å which is close but smaller than the one calculated in the bulk of 2.195 Å. We showed this behaviour in Table 2 where we considered an Hf atom at the interface between the twisted planes and its distances with the neighbouring O atoms.Moreover, it is also worth noticing the effect imposed by the size of the periodic cell on the structural relaxation of tilt and twist GBs. In the case of the tilt, going from 72 to 108 atoms imposes a stronger constraint on the structure which creates larger channels. Instead, in the case of the twist, going from 90 to 120 atoms does not really seem to change. In both cases the structure tries to rearrange as in the bulk.


### 3.2. Formation Energies

The stability of the GBs was studied by calculating the formation energy of the grain boundary with respect to the cubicHfO2. In Table 3 we indicated for each structure, in parenthesis, the number of motifs (nmotif) per unit cell. We also reported the total energy and the total energy per motif to calculate the formation energy of the GB as (2)Ef=EGBnmotif-Ebulknmotif.Table 3
For each structure studied, we report the number of motif,nmotif, in the unit cell (in parenthesis), the total energies E (eV), the total energies per motif E/nmotif (eV) and the formation energies Ef (eV) which are calculated as Ef=(EGB/nmotif-Ebulk/nmotif).
E (eV)
E
/
n
m
o
t
i
f (eV)
E
f (eV)
E
f (J/m2)
Bulk (4)
−121.49
−30.37
Twist90 (30)
−896.83
−29.89
0.48
0.29
Twist120 (40)
−1202.51
−30.06
0.31
0.19
Tilt72 (24)
−691.62
−28.82
1.55
0.30
Tilt108 (36)
−1011.99
−28.11
2.26
0.43E
f of the twist GBs is lower than tilt GBs which demonstrates that twist GBs are the most stable structures. We put these evidences in relation to the important structural differences between tilt and twist GB. Even, if the twist structures loose most of the symmetries of the HfO2 in the bulk phase, the distances between the atoms are very close to those of the cubic HfO2, while in the case of the tilt structures the creation of channels induces an extensive rearrangement of the atoms at the interface as confirmed from the calculated distances reported in Table 1. Therefore, the tilt and twist GBs induce a substantially different redistribution of density charge in the structures which is manifest in the very different formation energies. Moreover, differences exist within the same class of GBs. Actually, while for the twist GBs Ef is very similar for both structures, the tilt GBs are very sensitive to their dimension: the larger the tilt GBs are, the larger its formation energy is (i.e., the system is progressively less stable).In literature, tilt GBs have been studied which have a different formation energy per unit area. McKenna et al. [15, 17] investigated a monoclinic HfO2 tilt GB with a formation energy of 0.6 J/m2. This has a relatively low formation energy with respect to others they studied and it was chosen based on the principle that the most stable boundaries should have a high degree of site coincidence between grains. Instead, Xue et al. [25] studied cubic HfO2 and reported higher formation energy of 2.92 J/m2, 3.14 J/m2, and 3.50 J/m2.


### 3.3. Electronic Properties

We investigated also which is the effect of the different atoms rearrangements and charge redistributions of tilt and twist GBs on their electronic properties. We always consider as our reference the cubic-HfO2 bulk for which we obtained an energy band gap (Eg) of 3.81 eV (in good agreement with literature [28]). The energy gap for the GBs studied diminished with respect to the bulk and this is particularly evident for the tilt defects. In fact, we obtain Eg=0.84 eV for the Tilt72, Eg=0.27 eV for the Tilt108, Eg=2.84 eV for the Twist90, and Eg=3.31 eV for the Twist120.In Figure4 we also report the density of states (DOS) where, for all the systems, we took the zero energy reference to be the valence band maximum energy. The DOS is reported in an energy range close to the bulk gap energy region as our goal is to investigate the presence of new states within the gap. In fact, the current leakage measured in GBs can be due to electron trapping and tunnelling in the band gap [15, 17].Figure 4
DOS and energy gaps of the tilt and twist GBs studied.The Twist90 and Twist120 have few new states close to the conduction bands that slightly diminish the cubicHfO2 gap. Instead, the tilt GBs present many new localised states that reduce the gaps of around 2 eV. These new states are almost flat and are due to the channels formation in the bulk structure. These new states induce a transition in HfO2 from insulator to semiconductor.From these observations, we conclude that tilt GB defect seems to be favourite for current leakage with respect to twist GBs. However, tilt defect seems to be the most advantageous to tune the electronic properties ofHfO2 as it permits a higher degree of manipulation.The presence of these new states in the gap has been observed also in the GBs presented in [15, 17, 25]. However, it is worth noticing that the type of modulation of these new states in the gap strongly depends on the type of GBs. In fact, this defect can create a different number of undercoordinated O and Hf at the origin of these states.To deepen the origin of these new states inside the gap, we plotted in Figure5 the isosurfaces of the band-decomposed partial charge density considering for the valence the energy range, HOMO − 1 eV (a), and for the conduction the energy range: LUMO + 1 eV (b). For both tilt and twist GBs the valence states are localised on the oxygen atoms while the states in the conduction are localised on the Hf-O bonds around the Hf atoms. In particular for the tilt, the atoms related to these states seem to be also those which are involved in the channels. The same is observed in the twist but in this case the charge is delocalised on planes related to the rotation of the boundary.Figure 5
Isosurfaces of the band-decomposed partial charge density for both tilt and twist GBs. The energy range for the valence states is HOMO − 1 eV (a) while the energy range for the conduction states is LUMO + 1 eV (b).
(a)
(b)


### 3.4. Boltzmann Electronic Transport: The Conductivity

The correlation between GBs and increased leakage current has been demonstrated both theoretically and experimentally [15–17]. This effect is a result of a number of related factors such as (i) the intrinsic electronic properties of GBs which enhance direct tunnelling relative to the bulk, (ii) segregation of oxygen vacancies which increases trap assisted tunnelling currents, and (iii) ionic transport via interstitial sites [15–17].Here, we focused on GBs and their intrinsic electronic properties. We interpreted an oxygen vacancy as a donor which means that the system is n-doped and an interstitial oxygen as an acceptor which means that the system is p-doped [18]. Therefore, the GB can be n- and p-doped and the transport properties can therefore be studied as a function of the electron chemical potential in the framework of the Boltzmann transport equations. In particular, we used the Boltzmann transport theory within the constant scattering-time approximation as implemented in the BoltzTraP code [23].The Boltzmann equations for transport are obtained in the thermodynamic limit and under some conditions such that the interactions involving more than two particles can be neglected, the collisions are elastic and involve only uncorrelated particles. This means that particles which have already collided are expected not to recollide in the future. This approach is a simplified model to study transport which appeared to work well in many different cases [29–31]. However, this model does not take into account effects such as electron-hole trapping [32].The Boltzmann equation for the calculation of the electronic conductivity tensorσαβ(μ,T) as a function of the chemical potential μ and temperature T is(3)σαβμ,T=1Ω∫σαβϵ-∂f0μ,T,ϵ∂ϵdϵ,where α,β=x,y,z are tensor index, Ω is the volume of the unit cell, f0 is the Boltzmann distribution function, and σαβ(ϵ) is defined as(4)σαβϵ=1N∑i,kσαβi,kδϵ-ϵi,kδϵ.N is the number of k-points and ϵi,k are the energy bands indexed by bands (i) and k-points (k). The quantity σαβ(i,k) is(5)σαβi,k=e2τi,kvαi,kvβi,k,where e is the electron charge, τi,k is the relaxation time, and vα(i,k)=1/ħ∂ϵi,k/∂kα component of group velocities.In our calculations we assume thatτi,k is constant. This approximation is often adopted in first-principle calculations [33, 34], and despite its simplicity it often turns out to be a good approximation for bulk materials, even in the case of anisotropic systems [35]. Moreover, in our analysis we assume that τ does not strongly change in GBs with respect to bulk. For this reason, we assume that all the structures have the same value. This is a strong statement, which, however, does not substantially change the results.In Figure6 we show σ/τ where we used τ=1 fs for all the structures [23]. σ/τ as a function of the electron chemical potential has to be interpreted as if the system were n-doped (O vacancies) in the case of positive μ or p-doped (O interstitials) in the case of negative μ.Figure 6
σ
/
τ as a function of the chemical potential for the tilt and twist GBs structures studied.Considering the conductivity of bulk as a reference we observe thatσ/τ is particularly large for the tilt GBs. The magnitude is higher than twist and it is more important in the gap region. The new electronic states give a strong contribution to increase current.The behaviour ofσ/τ is strongly related to the DOS. The tilt defects create new states in the gap which appeared to be crucial in enhancing electronic transport. Instead, the transport in the twist defects, despite some few new states in the gap, seems to be generally quenched in particular for positive μ.We also considered the role of anisotropy in electronic transport as we show in Figure7. In the case of Tilt72 and Tilt108 the anisotropy is much higher than in Twist90 and Twist120. In particular, it is interesting to note that a huge increasing of the conductivity is observed along the direction of the channels in the tilt GBs. These put in evidence the role of the channels in the leakage current.Figure 7
σ
/
τ projected along a, b, and c axis as a function of the chemical potential for the tilt and twist GBs structures studied.


## 3.1. Theoretical Models for HfO2 Grain Boundaries

We started by consideringHfO2 in its cubic phase and we found a lattice parameter of 5.07 Å, in agreement with other theoretical calculations and experiments [24–27]. From the cubic HfO2 we obtained tilt GBs by cutting the crystal along the (0  −1  3) plane and rotating it of 36.86° with respect to the [1  0  0] axis belonging to the plane of the boundary (see left panel of Figure 1). In a similar way we built the twist GBs by cutting the cubic HfO2 along the (3  1  0) plane and by rotating it of 36.86° with respect to the [0  0  1] axis perpendicular to the plane of the boundary (see right panel of Figure 1).Figure 1
The cubic phase ofHfO2 is presented where Hf atoms are in yellow and O atoms in red. A cartoon representation is presented to schematise the way tilt (left) and twist (right) GBs are constructed.In this way, we constructed two tilt GBs of the typeΣ5 36.86° (0  −1  3)/[1  0  0] and two twist GBs of the type Σ5 36.86° (3  1  0)/[0  0  1]. The Σ5 notation refers to the degree of site matching. Σ5 indicates a high symmetry and possibly low formation energy. Σ is simply evaluated as(1)Σ=δ×h2+k2+l2,where (hkl) is the plane of the boundary and δ is equal to 1 as (h2+k2+l2) is odd in our case [25]. The two tilt GBs differ in the number of atoms per unit cell: 72 atoms (Tilt72) and 108 atoms (Tilt108), and they are shown in Figure 2 before and after geometrical relaxation. The unit cell is orthorhombic and in the case of Tilt72 the cell parameters are a=5.11 Å, b=16.16 Å, and c=9.70 Å while in the case of the Tilt108 the parameters are a=5.11 Å, b=16.16 Å, and c=14.54 Å. In the case of the twist GBs the number of atoms per unit cell is 90 (Twist90) and 120 (Twist120) and they are shown in Figure 3 before and after geometrical relaxation. The unit cell is tetragonal and for the Twist90 the cell parameters are a=b=5.11 Å and c=8.18 Å while for the Twist120 they are a=b=5.11 Å and c=10.22 Å.Figure 2
Tilt72 and Tilt108 are shown before and after geometrical relaxation.Figure 3
Twist90 and Twist120 are shown before and after geometrical relaxation.The effects of the geometrical relaxation in the GBs structures are immediately observable in Figures2 and 3 and quantitatively shown in Tables 1 and 2 where we reported the distances between the atoms before (dnR) and after relaxation (dR), together with the percentage of relaxation (R). This percentage was calculated as R=(dR-dnR)/dnR∗100.Table 1
We report the distances between the atoms as labelled in Figure2 for Tilt72 and Tilt108 before (dnR) and after geometry relaxation (dR). We also report the percentage of relaxation R which is calculated as R=(dR-dnR)/dnR∗100.
d
n
R (Å)
d
R (Å)
R (%)
Tilt72
d
1
–
3
=
d
2
–
4
=
d
13
–
15
=
d
14
–
16
2.213
2.070
−6.46
d
3
–
5
=
d
4
-
5
=
d
15
–
17
=
d
16
-
17
2.213
2.016
−8.90
d
3
–
7
=
d
4
–
6
=
d
15
–
19
=
d
16
–
18
2.213
1.979
−10.57
d
5
–
9
=
d
5
–
8
=
d
17
–
21
=
d
17
–
20
2.213
2.875
29.9
d
7
–
9
=
d
6
–
8
=
d
19
–
21
=
d
18
–
20
2.213
2.190
−1.04
d
9
–
11
=
d
8
–
10
=
d
21
–
23
=
d
20
–
22
2.213
1.971
−10.94
d
11
-
12
=
d
10
–
12
=
d
23
-
24
=
d
22
–
24
2.213
2.114
−4.47
d
12
-
13
=
d
12
–
14
=
d
24
–
1
=
d
24
–
2
2.213
2.231
0.81
d
1
-
2
=
d
13
-
14
3.232
2.685
−16.9
d
3
-
4
=
d
15
-
16
1.616
2.527
56.4
d
7
-
6
=
d
19
-
18
4.848
4.848
0.0
d
9
-
8
=
d
21
-
20
3.232
3.895
20.5
d
11
-
10
=
d
23
-
22
1.616
2.325
43.9
d
5
–
12
=
d
17
–
24
4.237
4.453
5.1
d
12
–
17
=
d
24
–
5
4.237
4.037
−4.7
Tilt108
d
1
–
3
=
d
2
–
4
=
d
19
–
21
=
d
18
–
22
2.213
2.179
−1.5
d
3
–
5
=
d
4
-
5
=
d
21
–
27
=
d
22
–
27
2.213
1.966
−1.1
d
3
–
7
=
d
4
–
6
=
d
21
–
25
=
d
22
–
26
2.213
1.930
−1.27
d
5
–
13
=
d
5
–
12
=
d
27
–
29
=
d
27
-
28
2.213
3.602
62.7
d
7
–
9
=
d
6
–
8
=
d
25
–
31
=
d
26
–
30
2.213
1.880
−15.0
d
7
–
13
=
d
6
–
12
=
d
25
–
29
=
d
26
–
28
2.213
3.114
40.7
d
9
–
11
=
d
8
–
10
=
d
31
–
35
=
d
30
–
34
2.213
2.104
−4.9
d
11
–
13
=
d
10
–
12
=
d
29
–
35
=
d
28
–
34
2.213
2.081
−5.9
d
13
–
15
=
d
12
–
14
=
d
29
–
33
=
d
28
–
32
2.213
1.953
−11.7
d
15
–
20
=
d
14
–
20
=
d
33
–
36
=
d
32
–
36
2.213
2.116
−4.4
d
20
-
19
=
d
20
–
18
=
d
36
–
1
=
d
36
–
2
2.213
2.192
−1.0
d
5
–
15
=
d
5
–
14
=
d
27
–
33
=
d
27
–
32
2.213
2.971
34.2
d
1
-
2
=
d
19
-
18
3.232
2.524
−21.9
d
3
-
4
=
d
21
-
22
1.616
2.439
50.9
d
7
-
6
=
d
25
-
26
4.848
5.489
13.2
d
9
-
8
=
d
31
-
30
8.080
7.921
−2.0
d
11
-
10
=
d
35
-
34
6.464
7.771
20.2
d
13
-
12
=
d
29
-
28
3.232
5.065
56.7
d
15
-
14
=
d
33
-
32
1.616
2.288
56.4
d
17
-
16
=
d
37
-
38
4.848
3.709
23.5
d
5
–
20
4.237
4.188
−1.2
d
20
–
27
4.237
4.285
−1.1Table 2
Distances between Hf at the interface of the twisted planes and its neighbouring O atoms for Twin90 and Twin120 before and after relaxation. We also report the percentage of relaxationR which is calculated as R=(dR-dnR)/dnR∗100. In the bulk the distance between O and Hf is 2.195 Å.
d
n
R (Å)
d
R (Å)
R (%)
Twin90
d
1
1.512
2.064
36.51
d
2
2.213
2.000
−9.62
d
3
2.213
2.006
−9.35
d
4
2.213
2.032
−8.18
d
5
2.213
2.170
−1.94
d
6
2.213
2.199
−0.63
Twin120
d
1
1.512
2.017
33.40
d
2
2.213
1.988
−10.17
d
3
2.213
1.996
−9.81
d
4
2.213
2.074
−6.70
d
5
2.213
2.113
−4.82
d
6
2.213
2.160
−2.56In the case of the Tilt72, we labelled from 1 to 24 the atoms which play the most important role in the relaxation. All these atoms are symmetric with respect to thexy plane. The geometrical relaxation creates two almost spherical large channels and two small channels with a hexagonal structure. The initial distances between first neighbouring atoms are of 2.213 Å and then there is a compensation between elongation and compression which is at the origin of these channels. In particular, we observe that the bigger channels are due to a strong modification of the distances between atoms 5 (17) and 9 (21) and between atoms 5 (17) and 8 (20). The percentage of deformation is R=29.9%. The deformation can be also investigated by studying the change of distances along the z direction. Here, the maximum deformation is related to atoms 3 (15) and 4 (16) which is R=56.4%. Those atoms that do not play a role in the creation of the channels still keep the initial bulk distances. As a consequence, when repeating the unit cell in the space, we found that our structures are made of small and large channels with bulk-like regions in between. The mean extension of these regions is of the order of 6 Å.A similar result was obtained for the Tilt108 where we labelled from 1 to 38 the atoms which play the most important role in the relaxation. Also in this case, all the atoms are symmetric with respect to the plane of symmetryxOy before and after the geometrical optimisation. The relaxation creates two elongated large and small channels still with a hexagonal form. The smaller channels have similar relaxation distances and percentages of the Tilt72. The elongated channels are due to a strong modification of the distances between atoms 5 (27) and 13 (29) and between atoms 5 (27) and 12 (28). The percentage of deformation is R=62.7%. Also in this case, those atoms that do not play a role in the creation of the channels still keep the initial bulk distances leaving bulk-like regions in between channels. The mean extension of these regions is of the order of 6.3 Å.The twist GBs have a quite different behaviour. The rotation with respect to an axis perpendicular to the plane of the grain boundary does not create any channels in the structures as shown in Figure3 for the Twist90 and Twist120. In fact, the twist GB alternates planes of O and Hf with a different inclination. Through an analysis of the O and Hf distances, before and after relaxation, we observed that the structure has a general tendency to rearrange as in the bulk even if it is more compact. After relaxation, the Hf-O distances have almost the same value which is around 2.000 Å which is close but smaller than the one calculated in the bulk of 2.195 Å. We showed this behaviour in Table 2 where we considered an Hf atom at the interface between the twisted planes and its distances with the neighbouring O atoms.Moreover, it is also worth noticing the effect imposed by the size of the periodic cell on the structural relaxation of tilt and twist GBs. In the case of the tilt, going from 72 to 108 atoms imposes a stronger constraint on the structure which creates larger channels. Instead, in the case of the twist, going from 90 to 120 atoms does not really seem to change. In both cases the structure tries to rearrange as in the bulk.


## 3.2. Formation Energies

The stability of the GBs was studied by calculating the formation energy of the grain boundary with respect to the cubicHfO2. In Table 3 we indicated for each structure, in parenthesis, the number of motifs (nmotif) per unit cell. We also reported the total energy and the total energy per motif to calculate the formation energy of the GB as (2)Ef=EGBnmotif-Ebulknmotif.Table 3
For each structure studied, we report the number of motif,nmotif, in the unit cell (in parenthesis), the total energies E (eV), the total energies per motif E/nmotif (eV) and the formation energies Ef (eV) which are calculated as Ef=(EGB/nmotif-Ebulk/nmotif).
E (eV)
E
/
n
m
o
t
i
f (eV)
E
f (eV)
E
f (J/m2)
Bulk (4)
−121.49
−30.37
Twist90 (30)
−896.83
−29.89
0.48
0.29
Twist120 (40)
−1202.51
−30.06
0.31
0.19
Tilt72 (24)
−691.62
−28.82
1.55
0.30
Tilt108 (36)
−1011.99
−28.11
2.26
0.43E
f of the twist GBs is lower than tilt GBs which demonstrates that twist GBs are the most stable structures. We put these evidences in relation to the important structural differences between tilt and twist GB. Even, if the twist structures loose most of the symmetries of the HfO2 in the bulk phase, the distances between the atoms are very close to those of the cubic HfO2, while in the case of the tilt structures the creation of channels induces an extensive rearrangement of the atoms at the interface as confirmed from the calculated distances reported in Table 1. Therefore, the tilt and twist GBs induce a substantially different redistribution of density charge in the structures which is manifest in the very different formation energies. Moreover, differences exist within the same class of GBs. Actually, while for the twist GBs Ef is very similar for both structures, the tilt GBs are very sensitive to their dimension: the larger the tilt GBs are, the larger its formation energy is (i.e., the system is progressively less stable).In literature, tilt GBs have been studied which have a different formation energy per unit area. McKenna et al. [15, 17] investigated a monoclinic HfO2 tilt GB with a formation energy of 0.6 J/m2. This has a relatively low formation energy with respect to others they studied and it was chosen based on the principle that the most stable boundaries should have a high degree of site coincidence between grains. Instead, Xue et al. [25] studied cubic HfO2 and reported higher formation energy of 2.92 J/m2, 3.14 J/m2, and 3.50 J/m2.


## 3.3. Electronic Properties

We investigated also which is the effect of the different atoms rearrangements and charge redistributions of tilt and twist GBs on their electronic properties. We always consider as our reference the cubic-HfO2 bulk for which we obtained an energy band gap (Eg) of 3.81 eV (in good agreement with literature [28]). The energy gap for the GBs studied diminished with respect to the bulk and this is particularly evident for the tilt defects. In fact, we obtain Eg=0.84 eV for the Tilt72, Eg=0.27 eV for the Tilt108, Eg=2.84 eV for the Twist90, and Eg=3.31 eV for the Twist120.In Figure4 we also report the density of states (DOS) where, for all the systems, we took the zero energy reference to be the valence band maximum energy. The DOS is reported in an energy range close to the bulk gap energy region as our goal is to investigate the presence of new states within the gap. In fact, the current leakage measured in GBs can be due to electron trapping and tunnelling in the band gap [15, 17].Figure 4
DOS and energy gaps of the tilt and twist GBs studied.The Twist90 and Twist120 have few new states close to the conduction bands that slightly diminish the cubicHfO2 gap. Instead, the tilt GBs present many new localised states that reduce the gaps of around 2 eV. These new states are almost flat and are due to the channels formation in the bulk structure. These new states induce a transition in HfO2 from insulator to semiconductor.From these observations, we conclude that tilt GB defect seems to be favourite for current leakage with respect to twist GBs. However, tilt defect seems to be the most advantageous to tune the electronic properties ofHfO2 as it permits a higher degree of manipulation.The presence of these new states in the gap has been observed also in the GBs presented in [15, 17, 25]. However, it is worth noticing that the type of modulation of these new states in the gap strongly depends on the type of GBs. In fact, this defect can create a different number of undercoordinated O and Hf at the origin of these states.To deepen the origin of these new states inside the gap, we plotted in Figure5 the isosurfaces of the band-decomposed partial charge density considering for the valence the energy range, HOMO − 1 eV (a), and for the conduction the energy range: LUMO + 1 eV (b). For both tilt and twist GBs the valence states are localised on the oxygen atoms while the states in the conduction are localised on the Hf-O bonds around the Hf atoms. In particular for the tilt, the atoms related to these states seem to be also those which are involved in the channels. The same is observed in the twist but in this case the charge is delocalised on planes related to the rotation of the boundary.Figure 5
Isosurfaces of the band-decomposed partial charge density for both tilt and twist GBs. The energy range for the valence states is HOMO − 1 eV (a) while the energy range for the conduction states is LUMO + 1 eV (b).
(a)
(b)


## 3.4. Boltzmann Electronic Transport: The Conductivity

The correlation between GBs and increased leakage current has been demonstrated both theoretically and experimentally [15–17]. This effect is a result of a number of related factors such as (i) the intrinsic electronic properties of GBs which enhance direct tunnelling relative to the bulk, (ii) segregation of oxygen vacancies which increases trap assisted tunnelling currents, and (iii) ionic transport via interstitial sites [15–17].Here, we focused on GBs and their intrinsic electronic properties. We interpreted an oxygen vacancy as a donor which means that the system is n-doped and an interstitial oxygen as an acceptor which means that the system is p-doped [18]. Therefore, the GB can be n- and p-doped and the transport properties can therefore be studied as a function of the electron chemical potential in the framework of the Boltzmann transport equations. In particular, we used the Boltzmann transport theory within the constant scattering-time approximation as implemented in the BoltzTraP code [23].The Boltzmann equations for transport are obtained in the thermodynamic limit and under some conditions such that the interactions involving more than two particles can be neglected, the collisions are elastic and involve only uncorrelated particles. This means that particles which have already collided are expected not to recollide in the future. This approach is a simplified model to study transport which appeared to work well in many different cases [29–31]. However, this model does not take into account effects such as electron-hole trapping [32].The Boltzmann equation for the calculation of the electronic conductivity tensorσαβ(μ,T) as a function of the chemical potential μ and temperature T is(3)σαβμ,T=1Ω∫σαβϵ-∂f0μ,T,ϵ∂ϵdϵ,where α,β=x,y,z are tensor index, Ω is the volume of the unit cell, f0 is the Boltzmann distribution function, and σαβ(ϵ) is defined as(4)σαβϵ=1N∑i,kσαβi,kδϵ-ϵi,kδϵ.N is the number of k-points and ϵi,k are the energy bands indexed by bands (i) and k-points (k). The quantity σαβ(i,k) is(5)σαβi,k=e2τi,kvαi,kvβi,k,where e is the electron charge, τi,k is the relaxation time, and vα(i,k)=1/ħ∂ϵi,k/∂kα component of group velocities.In our calculations we assume thatτi,k is constant. This approximation is often adopted in first-principle calculations [33, 34], and despite its simplicity it often turns out to be a good approximation for bulk materials, even in the case of anisotropic systems [35]. Moreover, in our analysis we assume that τ does not strongly change in GBs with respect to bulk. For this reason, we assume that all the structures have the same value. This is a strong statement, which, however, does not substantially change the results.In Figure6 we show σ/τ where we used τ=1 fs for all the structures [23]. σ/τ as a function of the electron chemical potential has to be interpreted as if the system were n-doped (O vacancies) in the case of positive μ or p-doped (O interstitials) in the case of negative μ.Figure 6
σ
/
τ as a function of the chemical potential for the tilt and twist GBs structures studied.Considering the conductivity of bulk as a reference we observe thatσ/τ is particularly large for the tilt GBs. The magnitude is higher than twist and it is more important in the gap region. The new electronic states give a strong contribution to increase current.The behaviour ofσ/τ is strongly related to the DOS. The tilt defects create new states in the gap which appeared to be crucial in enhancing electronic transport. Instead, the transport in the twist defects, despite some few new states in the gap, seems to be generally quenched in particular for positive μ.We also considered the role of anisotropy in electronic transport as we show in Figure7. In the case of Tilt72 and Tilt108 the anisotropy is much higher than in Twist90 and Twist120. In particular, it is interesting to note that a huge increasing of the conductivity is observed along the direction of the channels in the tilt GBs. These put in evidence the role of the channels in the leakage current.Figure 7
σ
/
τ projected along a, b, and c axis as a function of the chemical potential for the tilt and twist GBs structures studied.


## 4. Conclusions

We investigated how tilt and twin GBs modify the structural, electronic, and transport properties of the polycrystallineHfO2. The different structural properties of these defects have a strong impact on their electronic and transport properties. In fact, in the case of the tilt it is possible to create channels of different sizes and shapes while for the twist GBs the defect creates a sort of amorphous structure that tends to resemble the bulk, independent of the number of rotated planes/atoms. These structural differences and the strong anisotropy of tilt GBs reflect a major stability of twist with respect to tilt GBs. Nevertheless tilt defects result to be crucial for the enhancing of the electronic transport that results to be stronger along their channels in relation to leakage current through GBs. The different behaviour of the tilt and twist GBs can be used, for example, to properly engineer innovative materials in order to change the electrical resistance of the device between two distinct levels (this is actually a common characteristic of the metal-oxide-based resistance switching memories), that is, the High- and Low-Resistance-State, associated with different atomic arrangements of the same dielectric material.



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*Source: 2404378-2017-07-05.xml*