CC BY
43
DOI: 10.5862/JPM.242.5 UDC 538.9
A.I. Kartamyshev1, D.V. Dat2, A.G. Lipnitskii'
' Belgorod National Research University, Russian Federation 2 Ton Duc Thang University, Ho Chi Minh City, Vietnam
THE INTERACTIONS BETwEEN LIGHT IMPuRITIES AND VACANCIES IN TITANIuM AND ALuMINuM METALS: A DFT STuDY
In this paper, we present binding energies between an atom of hydrogen (H), carbon (C), nitrogen (N) and oxygen (O) with a vacancy in the hexagonal closed-packed (HCP) lattice of titanium (Ti) and the face centered cubic (FCC) lattice of aluminum (Al), calculated using the density functional theory (DFT). We have also investigated the trapping of up to five hydrogen atoms by a vacancy and the reduction of the vacancy formation energy, due to the formation of a hydrogen—vacancy complex. We used the molecular-dynamics modeling with consecutive relaxation at 0 K to obtain an atomic configuration of the vacancy—impurity complex, corresponding to the global energy minimum. According to our calculations, C— V, H—V, C—(H— V), N—(H— V) complexes are stable in the Al lattice with only H— V complex being stable in Ti. The formation of C—(H— V) and N—(H— V) complexes in the Al lattice results in the negative vacancy formation energy. The formation of H— V complex decreases the vacancy formation energy by 0.26 eV in the Ti lattice. A vacancy in the Ti lattice can trap up to four hydrogen atoms.
TITANIUM, ALUMINIUM, VACANCY, IMPURITY,DENSITY FUNCTIONAL THEORY.
1. Introduction
One of the outstanding implications of introducing hydrogen into metal is the possibility of increasing of the vacancy concentration in this material by several orders of magnitude, so-called superabundant vacancy (SAV) formation. The physical kernel of this effect is a trapping of hydrogen atoms into vacancies, leading to a decrease in the vacancy formation energy, until in 1993 the SAV was first discovered experimentally by Fukai and co-workers (in Pd [1] and Ni [2]). Since then SAV has been observed in many metallic systems such as Cu [3], Ti [4], Pd and Pd alloys [5 - 8], Al [9], Mn [10], Fe [10, 11], Mo [12], Cr [13], Co [10], Ni [14], Ni-Fe alloy [15], Nb [16 - 18].
In some cases, the concentration of vacancies can become as large as 10 % and more [10, 19, 20]. One of the reasons for this behavior is the formation of different defects, e.g., voids [21] as in the case of Al [9], Ni [22], Fe [23, 24], steels [25], and/or dislocation loops [26 - 28].
It is important to note, that H atoms may
have a high number of configurations inside a vacancy, leading to a higher configuration entropy of a crystal with H-vacancy complexes compared with a crystal with single vacancies and interstitial H atoms. To investigate the effects of SAV formation on materials from a theoretical point of view, one has to consider the positions of hydrogen atoms inside a vacancy and the maximum number of hydrogen atoms that can be trapped by this vacancy. In the aluminum lattice, it was observed that a hydrogen atom diffuses towards the lattice vacancy to occupy it
[29]. Instead of occupying the lattice site from which an aluminum atom has been removed during vacancy formation, the hydrogen atom locates at some asymmetrical point which is away from the vacancy's center. Lu and Kaxiras
[30] suggested that, in principle, up to 12 atoms can be accommodated in a single vacancy in the Al lattice. More recently, Gunaydin, et al. [31] reported that trapping of multiple H atoms in a single vacancy in Al is possible only for extreme H loading condition, i.e., for H concentration, it is many orders of magnitude above the solubility limit given by the equilibrium with H2
gas at ambient conditions (10-9 at 300 K and 1 atm). Instead, under H-loading conditions used in most diffusion experiments, empty vacancies would coexist with the vacancies filled by one or at most two H atoms. Reviewing the conflicting results, from Lu and Kaxiras [30] on one hand and from Gunaydin et al. [31] on the other hand, Lars Ismer et al. studied the interactions between hydrogen impurities and vacancies in FCC Al lattice by first-principle (ab initio) methods but with a more critical estimation on the binding energy of the H—vacancy complex [32]. They found that a single vacancy in Al lattice can trap 10 hydrogen atoms, not 12 as reported in the work of Lu and Kaxiras [30]. The difference occurs because of the definition of the trapping energy of hydrogen impurities in vacancies of each author. However, we can see the common result in the two works that hydrogen atoms can interact with the vacancies forming H—vacancy complexes. Moreover, trapping of multiple H atoms in a single vacancy in Al lattice decreases the vacancy formation energy and this phenomenon could be related to the observed hydrogen-induced superabundant vacancy formation and vacancy clustering.
However, until now combined influence on SAV of H and other light elements such as C, O and N as well as trapping of H atoms by the monovacancy in the Ti lattice were poorly studied. At the same time the possibility of such influence is indicated by experimental data on Al lattice with C and H impurities [33]. Number of pores increases after preliminary annealing. In this connection, in the present article, we investigate combined influence of H, C, N and O atoms on formation of their complexes with monovacancy and vacancy formation energy from first principles (ab initio). The investigation has been performed for FCC Al and HCP Ti lattices, their alloys being widely used because of their high specific strength and corrosion resistance.
2. Calculation method
Calculations were performed in the framework of the density functional theory (DFT) [34, 35] within the generalized gradient approximation (GGA) using the functional of J.P. Perdew et al. [36, 37] for description of
the exchange-correlation energy and the projected augmented wave (PAW) method [38] as implemented in ABINIT code [39]. Point defects were considered within supercell model. The list of point defects included an impurity atom in the interstitial site, a monovacancy and monovacancy—impurity complexes. Brillouin-zone (BZ) integrals were approximated using the special k-point sampling of H.J. Monkhorst and J.D. Pack [40]. Full energies of supercells were calculated after relaxation to equilibrium positions of atoms and volumes at 0 K. Relaxation was performed in several steps. Initial configurations included an impurity atom in the center of a monovacancy and the impurity atom in the center of interstitial site of the HCP lattice. Molecular-dynamics modeling were performed for initial configurations with using L. Verlet algorithm [41] at 300 K and consecutive cooling down to 100 K with using Nose—Hoover thermostat [42]. Final equilibrium configurations were determined by relaxation of supercells with the Broyden—Fletcher— Goldfarb—Shanno method [43] to the full energy minimum at 0 K. The relaxation was stopped when all forces acting on the atoms were converged to within 2.5 meV/A.
The favorable occupation site of an impurity is defined by a difference of solution energies of this impurity at different positions (AE) The solution energy is calculated by the following formula:
EX = E[XT/0 + Mn] - E[Mn] - 2 E[X2], (1)
where E[XT/O + Mn] are the total energies of the system with n atoms of metal M (M = Ti, Al) when atom X is at tetrahedral (T) or octahedral (O) interstitial site, E[Mn] is the energy of pure system with n atoms of metal M, E[X2] is the energy of molecule X2 (X = H, C, N and O) in the vacuum or in the case of carbon — the energy of graphene cell with two atoms.
In the case of vacancy—impurity system, the stability of each configuration is defined by the binding energy which was calculated by the following formula:
ECX-V = E[XT/O + Mn] + E[V + Mn-1] -- E[Mn] - E[XT/O - V + MnJ,
(2)
where E [XT/O + Mn ] is the total energy of the supercell with n atoms of metal M (M = Al, Ti) and the impurity Xin the T/O site (X= H, C, N and O), E[Mn ] is the total energy of the super-cell with n atoms of metal, E[ V + Mn is the total energy of the supercell with (n — 1) metal atoms and one vacancy, E[XT/O — V + Mn _1] is the total energy of the supercell with the complex X — vacancy and (n — 1) metal atoms. In the case of the X — (H — V ) complexes V is replaced by (H — V) in this equation.
Formation vacancy energies were calculated as follows:
E/ = E[V + Mn_i] -
n -1
E [Mn]
E/ [X] = EVf - ECX-V.
(3)
(4)
Here EVf and EVf [X ] are vacancy formation energies in pure metal and in the metal with (X — V) complexes, correspondingly. In the case of the (X — (H — V)) complexes ECX-H-V must be additionally subtracted from E f
EV .
L. Ismer et al. [32] suggested to determine changing of the energetic characteristics of (V — nH) complex (a vacancy and n atoms of hydrogen) stepwise form by adding impurity atoms one by one. Using this approach we can write the cohesive energy between a hydrogen atom and the (V — (n — 1)H) complex as follows:
E(n) = E[V - (n -1)H + Mn_i] + (5)
+ E[HO + Mn] - E[V - nH + Mn-i] - E[Mn],
where E[ V - (n - 1)H + Mn -1] is the total energy of the supercell with (V- (n — 1)H) complex, E[ V — n H + Mn —1] is the total energy of the supercell with (V — nH) complex.
3. Vacancy — impurity interactions in the aluminum lattice
The supercell contained 2^2x2 cubic unit cells of the FCC aluminum lattice. The calculations were performed using an energy cutoff of 600 eV for the plane-wave basis set and 2x2x2 A-points grid in the Brillouin zone. Such a choice of the main parameters ensures an energy convergence to 1 meV/atom. The solution energies of C, N, O and H atoms in the tetrahedral and octahedral sites calculated
Table 1
Calculated solution energies of light elements in the tetrahedral and octahedral sites in the aluminum lattice
Atom ET EO
eV
H 0.70 0.85
C 1.31 1.25
N - 2.87 - 2.00
O - 3.70 Unstable
Table 2
The binding energies between impurity atoms and vacancies ( V) or hydrogen-vacancy complexes (H- V) in the aluminum lattice
Interaction E,, eV b7
H-V 0.39
C-V 0.18
N-V - 0.69
O-V 0.02
c-(h-v> 0.77
N-(H-V) 0.56
O-(H-V) - 0.07
by Eq. (1) are shown in Table 1.
Solution energies for H atoms are consistent with the known experimental data (from 0.65 to 0.71 eV) [44 - 47]. We found O atom moving from octahedral to tetrahedral interstitials sites during simulation and so the corresponding solution energy was not calculated.
Energetic properties of the impurity-vacancy complexes in the aluminum lattice calculated by Eq. (2) are shown in Table 2.
The calculated binding energy ECH-Vbetween a hydrogen atom and a vacancy is close to the experimental value of 0.43 eV [48]. The negative binding energy for the N- V complex means that there is a repulsive interaction between them and a nitrogen atom is not responsible for an increase in the vacancy concentration. However, in the presence of a hydrogen atom the binding energy becomes positive and the formation of (N-(H- V)) complex is energetically favorable. The calculated N-H bond length of 1.04 A
Table 3
Vacancy formation energies in the aluminum lattice with impurities and in the pure one
Impurity Ef, eV v '
C 0.37
H 0.16
H, C -0.61
H, N - 0.40
0 (pure) 0.55
in the (N—(H— V)) complexes is close to the experimental data of 1.01 - 1.03 À [49]. A considerable increase in the binding energy was found for (C-(H- V)) complex in contrast to
the (C-V) one.
The vacancy formation energies in pure aluminum and those in the presence of impurities calculated by Eqs. (3) and (4) are listed in Table 3.
We can see from Table 3 that the vacancy formation energy values reduce from 0.55 eV in the pure aluminum to 0.37 eV in the presence of the vacancy-carbon complex and to 0.16 eV in the presence of the vacancy-hydrogen one. This explains an increase in the vacancy concentration in aluminum with hydrogen and carbon impurities [33]. Moreover, formations of the (C-(H-V)) and the (N-(H-V)) complexes result in the negative vacancy formation energies.
These vacancies are no longer thermally
Fig. 1. The configurations of the vacancy-impurity complexes C-V (a), H-V(b), C-(H- V) (c), N-(H- V) (d) in the aluminum lattice. H atoms are shown by white balls; C, N atoms are black ones; 12 Al atoms form the 1st coordination sphere around the vacancy ( V) site of the lattice
activated and new free vacancies are formed in order to keep the equilibrium concentration of the free vacancies. This mechanism can explain SAV formation in the aluminum lattice at the presence of both C and H impurities as reported in paper [33]. Configurations of stable complexes of the point defects are shown in Fig. 1.
4. Vacancy — impurity interactions in the titanium lattice
The supercell contained 3^3x2 unit cells of the HCP titanium lattice. The calculations were performed using an energy cutoff of 600 eV for the plane-wave basis set and 4x4x4 ^-points grid in the Brillouin zone. Such a choice of the main parameters ensures energy convergence to 1 meV/atom.
In the case of a hydrogen atom
AES = 0.06 eV (AES = ESX(tet.) — ESX(oct.)).
This value is in good agreement with the results of other DFT calculations being equal to 0.01 eV [50] and 0.12 eV [51]. Carbon, nitrogen and oxygen atoms also occupy octahedral interstitial sites with values of AES equal to 2.13, 1.70, and 1.16 eV correspondingly. We can see that the solution energy for hydrogen is less than the corresponding value for other impurities by the order of magnitude. Hence, we can expect a higher cohesive energy of a hydrogen atom with crystal defects (including vacancies) in comparison with that of carbon, nitrogen and oxygen atoms.
The energy properties of the impurity -vacancy complexes in the titanium lattice calculated by Eq. (2) are shown in Table 4.
As we can see from Table 4, the H— V complex only has positive binding energy,
Fig. 2. Configuration of the H— V complex in the Ti lattice.
H atom is shown by a white ball; 12 Ti atoms form the 1st coordination sphere around the vacancy ( V) site of the lattice
whereas other impurity — vacancy complexes being unstable. The negative binding energy between other impurities and vacancy shows that there will be repulsive interaction between them. The configuration of H— V complex in the Ti lattice is presented in Fig. 2.
From our calculations by Eq. (3) Ef = 2.12 eV. Difference between this value and
v _
other DFT calculations [52] is less than 1 %. Using Eq. (4) we found that the formation of H—V complex reduces the vacancy formation energy by 0.26 eV. It is considerably higher than the average kinetic energy of atoms ~3/2kBT = 0.039 eV at 300 K.
The binding energies Eb calculated by Eq. (5) for the titanium lattice are presented in Table 5.
We can conclude from Table 5 that the maximum number of hydrogen atoms that can be trapped by a monovacancy in HCP titanium
Table 4
The binding energies between an impurity atom and a vacancy ( V) in the titanium lattice
Interaction Eb, eV
H-V 0.26
C-V - 0.84
N-V - 1.72
O-V - 1.15
Tab le 5
The «-dependence of binding energies between a hydrogen atom and the V — (« — 1)H complex
n Eb, eV
2 0.25
3 0.38
4 0.08
5 -0.05
lattice is four. Earlier DFT calculations [51] have shown that a monovacancy in HCP titanium lattice can contain up to three these atoms. The difference between our calculations and those of Ref. [51] is explained by the simplified relaxation of initial atomic configurations of complexes used in Ref. [51] that led to a configuration in the local energy minimum. Using molecular-dynamics modeling before relaxation at 0 K we obtained more energetically favorable atomic configurations with number of hydrogen atoms more than three. Trapping of hydrogen atoms by vacancies can lead to reduction of the vacancy formation energy and consequently to an increase in the vacancy concentration by several orders of magnitude as was found by Y. Fukai in the nickel lattice for the first time [2].
5. Conclusions
Using density functional theory calculations, we investigated the interactions of the impurity atoms of hydrogen, carbon, nitrogen and oxygen with monovacancies in the HCP titanium and FCC aluminum lattices. The results of this work can be summarized as follows:
1. Impurities such as hydrogen, carbon, nitrogen and oxygen atoms occupy octahedral interstitial sites in the both Al and Ti lattices except for hydrogen and oxygen atoms in the Al one that occupy tetrahedral sites.
2. The C- V, H- V, C-(H- V), and N-(H- V) complexes are stable in the Al lattice. Except for the H— V complex with positive cohesive energy, other impurity—vacancy complexes are unstable in the Ti lattice.
3. The formation of C—(H— V) and N—(H— V) complexes in Al results in the negative vacancy formation energy. The formation of H— V complex in the HCP titanium lattice decreases the vacancy formation energy by 0.26 eV. This leads to an increase in the vacancy concentration and can result in the pore formation at the presence of corresponding impurities.
4. According to our calculations the maximum number of hydrogen atoms that can be trapped by a monovacancy in the HCP Ti lattice is four.
The work was financially supported by the Ministry of Education and Science of the Russian Federation under contract No. 3.1282.2014/K.
(Государственное задание № 3.1282.2014/K Министерства образования и науки РФ)
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THE AuTHORS
KARTAMYSHEV Andrey I.
Belgorod National Research University
85 Pobeda St., Belgorod, 308015, Russian Federation
andrei kart@mail.ru
DAT Duy Vo
Ton Duc Thang University
19 Nguyen Huu Tho Str., Tan Phong Ward, District 7, Ho Chi Minh City, Vietnam duydat_bel@yahoo.com
LIPNITSKII Alexey G.
Belgorod National Research University
85 Pobeda St., Belgorod, 308015, Russian Federation
lipnitskii@bsu.edu.ru
Картамышев А.И., Дат Д.В., Липницкий А.Г. ТЕОРЕТИЧЕСКОЕ ИССЛЕДОВАНИЕ ВЗАИМОДЕЙСТВИЯ МЕЖДУ ПРИМЕСЯМИ ЛЕГКИХ АТОМОВ И ВАКАНСИЯМИ В РЕШЕТКАХ ТИТАНА И АЛЮМИНИЯ.
В данной работе мы представляем значения энергии связи между атомами водорода, углерода, азота и кислорода с вакансией (V) в гексагональной плотноупакованной (ГПУ) решетке титана (Ti) и в гранецентрированной кубической (ГЦК) решетке алюминия (Al); значения рассчитаны в рамках теории функционала плотности. Мы также исследовали захват вакансией вплоть до пяти атомов водорода и уменьшение энергии образования вакансии в связи с формированием комплекса водород — вакансия. Использовано моделирование методом молекулярной динамики с последующей релаксацией при 0 K для получения атомной конфигурации комплекса вакансия — примесь, соответствующего глобальному минимуму энергии. Согласно нашим расчетам, комплексы C— V, H—V, C—(H— V), N—(H— V) стабильны в решетке Al, тогда как только комплекс Н— V устойчив в решетке Ti. Образование комплексов C—(H— V) и N—(H— V) в ГЦК решетке Al приводит к отрицательной энергии образования вакансии. Формирование комплекса H— V уменьшает энергию образования вакансии на 0,26 эВ в решетке Ti. Вакансия в ГПУ решетке титана может захватывать до четырех атомов водорода.
ТИТАН, АЛЮМИНИЙ, ВАКАНСИЯ, ПРИМЕСЬ, ТЕОРИЯ ФУНКЦИОНАЛА ПЛОТНОСТИ.
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сведения об авторах
КАРТАМЫШЕВ Андрей Игоревич — лаборант-исследователь кафедры наноматериалов и нанотех-нологий Белгородского государственного национального исследовательского университета. 308015, Российская Федерация, г. Белгород, ул. Победы, 85 andrei_kart@mail.ru
ДАТ Дуй Во — физик-исследователь Университета имени Тон Дык Тханга, г. Хошимин, Вьетнам. 19 Nguyen Huu Tho St., Tan Phong Ward, District 7, Ho Chi Minh City, Vietnam duydat_bel@yahoo.com
ЛИПНИЦКИй Алексей Геннадьевич — доктор физико-математических наук, заведующий лабораторией научно-образовательного и инновационного центра «Наноструктурные материалы и нанотезно-логии» Белгородского государственного национального исследовательского университета. 308015, Российская Федерация, г. Белгород, ул. Победы, 85 lipnitskii@bsu.edu.ru
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