Some questions about the calculationof FCC solid solution phase

[HaihuiZhang]

For Ag-Cu binary phase diagram, there are only liquid phase and FCC solid solution phase. For Ag-Cu FCC solid solution phase(FCC_A1), "sublattice_model": [["AG", "CU"], ["VA"], "sublattice_site_ratios": [1,1].
In this case, how to calculate the enthalpy change of FCC solid solution at different temperatures by phonopy? If we use the primitive cell to calculate the enthalpy with temperature, such as Ag3Cu, "sublattice_occupancies" is empty, because this is stoichiometric phase, not solid solution phase, so I am very confused.

[bocklund]

In DFT our group commonly uses dilute substitution (e.g. 1 Cu atom substituted onto a Ag site in a 64 atom Ag supercell) or special quasirandom structures [1] for more concentrated mixing.

You can see an example of how these are combined for CALPHAD modeling by looking at this paper by Xuan Liu [2]. Ozoliņš and others [3] calculated some compounds and SQS for Ag-Cu and a couple other related systems, which you might find insightful for how these types of calculations compare to each other.

[1] https://doi.org/10.1103/PhysRevLett.65.353
[2] https://doi.org/10.1016/j.calphad.2013.02.006
[3] https://doi.org/10.1103/PhysRevB.57.6427

[HaihuiZhang]

If 1 Cu atom substituted onto a Ag site in a 64 atom Ag supercell, then "sublattice_occupancies": [ [0.015, 0.985], 1] , and then use this structure for phonon calculation. so that the thermodynamic properties of solid solution phase can be obtained. Am I right in understanding that?

[bocklund]

The occupancies should be [[0.985, 0.015], 1] (the elements must be in alphabetic order within a sublattice), but in principle your understanding is correct. You should be aware that the symmetry of the crystal will be lost, so phonon calculations may be expensive. For a computationally cheaper (but more approximate) calculation, you can use the Debye model, which is also briefly described in reference 2 in my response above.

[HaihuiZhang]

Thank you very much for providing me with a new idea. I have not known debye model before. I found the relevant software on Google is gibbs2 or 1. May I ask what software you use for debye model calculation？
Another question is, I use the primordial cell containing four Ag atoms to replace one, two and three Cu atoms for phonon calculation, and write Ag3Cu, AgCu, AgCu3. Can this data be used as solid solution input, that is, for AgCu3, "sublattice_occupancies": [[0.25, 0.75], 1]?
I think it's strange. I don't think it's a solid solution.

[HaihuiZhang]

When I used the SQS model from https://www.phases.psu.edu/?page_id=77 for fcc solid solution phase of Ag-Cu to calculating the static total energy by DFT, errors always occur because ions are too close or superimposed. So I always lack the data of thermodynamic properties of solid solutions. 😔

[bocklund]

The Debye model is fairly simple and implanted many places. I haven’t used the gibbs program, so I can’t comment on that. One of the easier and more flexible tools to get up and running is in pymatgen (See the pymatgen Debye docs). A drawback of their implementation is that the thermal electronic contributions to the free energy are not included. dfttk is a package that we have developed that, among other things, builds on top of pymatgen to include the thermal electronic part, but the package is still in development.

You are correct that substituting Cu into the conventional cell creates compounds and not solid solutions, this is why the SQS were created :) - an alternative to predict the solution behavior using many compounds is the cluster expansion method.

For the SQS on the PRL website, the volume of that structure is probably too small for the atoms - you can just increase the volume by changing the scaling factor in the second row of the POSCAR file until the volume of the structure is large enough for the calculations to work. Usually a good rule of thumb for a guess of the volume is to make it so the structure has density equal to the weighted average density of fcc Ag and fcc Cu. Because of the atom collision issue, it’s usually safer to start with a cell that is a little larger, rather than a little smaller.

[HaihuiZhang]

“Usually a good rule of thumb for a guess of the volume is to make it so the structure has density equal to the weighted average density of fcc Ag and fcc Cu. ” That is to say when expanding the volume, we should pay attention to the concentration ratio if the weighted average density is equal to the density of the new structure. Because ρ ̅=ρ_Ag X_Ag+ρ_Cu X_Cu=m_Ag/V+m_Cu/V，conversion formula we can obtain V_Ag/V_Cu =X_Cu/X_Ag =1.44. Do I understand this correctly?

[bocklund]

I agree with the expression

ρ ̅=ρ_Ag X_Ag+ρ_Cu X_Cu

which will give you a target density of

ρ ̅=10.49 g/cm^3 * 0.75 + 8.96 g/cm^3 * 0.25 = 10.1075 g/cm^3

This is your target density. You need to set the volume of your structure to match that target density. If you have pymatgen installed, this is pretty easy:

from pymatgen import Structure
s = Structure.from_file('mysqs', fmt='POSCAR')

target_density = 10.1075
cur_volume = s.volume
cur_density = s.density
s.scale_lattice(s.volume * float((cur_density/target_density)))
print(s.density)  # should be the target

s.to(filename='scaled.sqs.POSCAR',  fmt='POSCAR')

[HaihuiZhang]

Now I get it! Thank you for your patience. Your advice to me is very valuable.

[bocklund]

I'm happy to help!

[HaihuiZhang]

According to your advice, the volume of that structure was increased when using the SQS on the PRL website, such as the scaling factor is 2. Is the total energy of the original SQS structure twice that of the changed structure? That is, E(SQS-origin)=E(SQS-changed)*2?

[HaihuiZhang]

1. And if I want to calculate the phase diagram of the ternary system, for example, Ag-Cu-Co, What I should do for preparing input data and how to fit the ternary phase diagram by ESPEI.？
2. I have focused on calculating the thermodynamic data of the Ag-Cu binary system, should I do that on Cu-Co, Ag-Cu or just calculating the Ag-Cu-Co ternary system?
   To be honest, my main purpose is to calculate ternary phase diagrams😔.

[bocklund]

According to your advice, the volume of that structure was increased when using the SQS on the PRL website, such as the scaling factor is 2. Is the total energy of the original SQS structure twice that of the changed structure? That is, E(SQS-origin)=E(SQS-changed)*2?

No, the energy is not linear in volume, but roughly parabolic around the minimum energy. See figure 2 in [1], which shows how the energy changes with changing volume for Ni and Ni3Al. You can expect the trend to be similar, but you cannot know what the energy is until you calculate it.

1. And if I want to calculate the phase diagram of the ternary system, for example, Ag-Cu-Co, What I should do for preparing input data and how to fit the ternary phase diagram by ESPEI.？
2. I have focused on calculating the thermodynamic data of the Ag-Cu binary system, should I do that on Cu-Co, Ag-Cu or just calculating the Ag-Cu-Co ternary system?
   To be honest, my main purpose is to calculate ternary phase diagrams

Calphad databases are heavily dependent of the extrapolation of binary systems, so you will need to have assessed Ag-Cu, Ag-Co, and Cu-Co. You can assess these yourself (as you have been doing with Ag-Cu), or use existing assessments from the literature (if you think they are appropriate) to combine all the binaries into a database, then use ESPEI to assess any ternary parameters.

[1] https://doi.org/10.1016/j.commatsci.2009.12.006

[HaihuiZhang]

I don't quite understand the volume-energy problem. If we expand the volume by two times, even according to the method of Ni and Ni3Al in the literature, we should calculate the volume by 1.5-2.5 times, and get the lowest energy after two times the volume, not the original SQS model energy that we want.

[bocklund]

we should calculate the volume by 1.5-2.5 times, and get the lowest energy after two times the volume, not the original SQS model energy that we want.

This is correct. More generally, any structure you calculate should have all the degrees of freedom (cell volume, lattice parameters, and ionic positions) relaxed in a way that minimizes the forces on the atoms and the stress on the cell while preserving the symmetry of the structure.