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# Third tutorial on the Projector Augmented-Wave (PAW) technique

## Testing PAW datasets against an all-electron code

This tutorial will demonstrate how to test a generated PAW dataset against an all-electron code. We will be comparing results with the open Elk FP-LAPW code (a branch of the EXCITING code) available under GPLv3.

You will learn how to compare calculations of the equilibrium lattice parameter, the Bulk modulus and the band structure between ABINIT PAW results and those from the Elk code.
It is assumed you already know how to use ABINIT in the PAW case. The tutorial assumes no previous experience with the Elk code, but it is strongly advised that the users familiarise themselves a bit with this code before attempting to do similar comparisons with their own datasets.

This tutorial should take about 3h-4h.

## 1. Introduction - the quantities to be compared

When comparing results between all-electron and pseudopotential codes, it is usually impossible to compare total energies. This is because the total energy of an all-electron code includes the contribution from the kinetic energy of the core orbitals, while in the pseudopotential approach, the only information that is retained is the density distribution of the frozen core. This is typically so even in a PAW implementation.

Differences in total energies should be comparable, but calculating these to a given accuracy is usually a long and cumbersome process. However, some things can be calculated with relative ease. These include structural properties - such as the equilibrium lattice parameter(s) and the bulk modulus - as well as orbital energies, i.e. the band structure for a simple bulk system.

!!! Note We are here aiming to compare the results under similar numerical conditions. That does not necessarily mean that the calculations can be compared with experimental results, nor that the results of the calculations individually represent the absolutely most converged values for a given system. However, to ensure that the numerical precision is equivalent, we must take care to:

* Use the same (scalar-relativistic) exchange-correlation functional.
* Match the Elk muffin-tin radii and the PAW cutoff radii.
* Use a k-point grid of similar quality.
* Use a similar cutoff for the plane wave expansion.
* Freeze the core in the Elk code (whenever possible), to match the frozen PAW core in ABINIT.
* Use a similar atomic on-site radial grid.

We will use Carbon, in the diamond structure, as an example of a simple solid with a band gap, and we will use Magnesium as an example of a metallic solid. Naturally, it is important to keep things as simple as possible when benchmarking PAW datasets, and there is a problem when the element has no naturally occurring pure solid phase. For elements which are molecular in their pure state (like Oxygen, Nitrogen and so forth), or occur only in compound solids, one solution is to compare results on a larger range of solids where the other constituents have already been well tested. For instance, for oxygen, one could compare results for ZnO, MgO and MnO, provided that one has already satisfied oneself that the datasets for Zn, Mg, and Mn in their pure forms are good.

One could also compare results for molecules, and we encourage you to do this if you have the time. However, doing this consistently in ABINIT requires a supercell approach and would make this tutorial very long, so we shall not do it here. We will now discuss the prerequisites for this tutorial.

## 2. Prerequisites, code components and scripts

It is assumed that you are already familiar with the contents and procedures in tutorials PAW1 and PAW2, and so have some familiarity with input files for atompaw, and the issues in creating PAW datasets. To exactly reproduce the results in this tutorial, you will need:

• The ATOMPAW code for generating PAW datasets. This code is bundled as a plugin in abinit, and it is assumed that you are using this plugin (when installing from source, this can be activated by the --with-dft-flavor="...+atompaw" option in the configure script)

• the Elk code (this tutorial was designed with v1.2.15), available here. We will use the Elk code itself, as well as its eos (equation-of-state) utility, for calculating equilibrium lattice parameters.

• Auxiliary bash and python scripts for the comparison of band structures, available in the directory $ABI_HOME/doc/tutorial/paw3_assets/scripts/. There are also various gnuplot scripts there. You will of course also need a working copy of ABINIT. Please make sure that the above components are downloaded and working on your system before continuing this tutorial. The tutorial also makes extensive use of |gnuplot|, so please also ensure that a recent and working version is installed on your system. !!! Note By the time that you are doing this tutorial there will probably be newer versions of all these programs available. It is of course better to use the latest versions, and we simply state the versions of codes used when this tutorial was written so that specific numerical results can be reproduced if necessary. ## 3. Carbon (diamond) ### 3.1. Carbon - a simple datatset Make a working directory for the ATOMPAW generation (you could call it C_atompaw) and copy the file: C_simple.input to it. Then go there and run ATOMPAW by typing (assuming that you have set things up so that you can run atompaw by just typing atompaw): atompaw < C_simple.input  The code should run, and if you do an ls, the contents of the directory will be something like:  C C.LDA-PW.xml dummy ftkin.1 logderiv.1 tprod.1 wfn2 C.atomicdata compare.abinit fthatpot.0 ftkin.2 logderiv.2 tprod.2 wfn3 C.LDA-PW-corewf.abinit C_simple.input fthatpot.1 ftvloc NC vloc wfn4 C.LDA-PW-paw.abinit density fthatpot.2 logderiv.0 potential wfn1 wfn5 There is a lot of output, so it is useful to work with a graphical overview. Copy the gnuplot script plot_C_all.p to your folder. Open a new terminal window by typing xterm &, and run gnuplot in the new terminal window. At the gnuplot command prompt type: gnuplot> load 'plot_C_all.p' You should get a plot that looks like this: You can now keep the gnuplot terminal and plot window open as you work, and if you change the ATOMPAW input file and re-run it, you can update the plot by retyping the load.. command. The gnuplot window plots the essential information from the ATOMPAW outputs, the logarithmic derivatives, (the derivatives of the dataset are green), the wavefunctions and projectors for each momentum channel (the full wavefunction is in red, the PW part is green, and the projector is blue) as well as the Fourier transforms of the kinetic energy and potential of the occupied states. Finally, it shows the transform of the projector products (the x-axis for the last two is in units of Ha). The inputs directory also contains scripts for plotting these graphs individually, and you are encouraged to test and modify them. We can look inside the C_simple.input file:  C 6 ! Atomic name and number LDA-PW scalarrelativistic loggrid 801 logderivrange -10 40 1000 ! XC approx., SE type, gridtype, # pts, logderiv 2 2 0 0 0 0 ! maximum n for each l: 2s,2p,0d,0f.. 2 1 2 ! Partially filled shell: 2p^2 0 0 0 ! Stop marker c ! 1s - core v ! 2s - valence v ! 2p - valence 1 ! l_max treated = 1 1.3 ! core radius r_c n ! no more unoccupied s-states n ! no more unoccupied p-states vanderbilt ! Vanderbilt scheme for finding projectors 2 0 ! localisation scheme 1.3 ! Core radius for occ. 2s state 1.3 ! Core radius for occ. 2p state 2 ! Run atompaw2abinit converter prtcorewf noxcnhat nospline noptim ! Abinit conversion options 0 ! Exit Here we see that the current dataset is very simple, it has no basis states beyond the 2s and 2p occupied valence states in carbon. It is thus not expected to produce very good results, since there is almost no flexibility in the PAW dataset. Note that the scalarrelativistic option is turned on. While this is not strictly necessary for such a light atom, we must alway ensure to have this turned on if we intend to compare with results from the Elk code. We will now run basic convergence tests in abinit for this dataset. The dataset file for abinit has already been generated (it is the C.LDA-PW- paw.abinit file in the current directory). Make a new subdirectory for the test in the current directory (you could call it abinit_test for instance), go there and copy the files: ab_C_test.in and input_C_test.files into it. This ABINIT input file contains several datasets which increment the ecut input variable, and perform ground state and band structure calculations for each value of ecut. This is thus the internal abinit convergence study. Any dataset is expected to converge to a result sooner or later, but that does not mean that the final result is accurate, unless the dataset is good. The goal is of course to generate a dataset which both converges quickly and is very accurate. The .files file contains: ab_C_test.in ab_C_test.out ab_C_test_i ./outputs/ab_C_test_o ./outputs/ab_C_test ../C.LDA-PW-paw.abinit So it expects the newly generated dataset to be in the directory above. Also, to keep things tidy, it assumes the outputs will be put in a subdirectory called outputs/. Make sure to create it before you start the abinit run by writing: mkdir outputs You can now run the abinit tests (maybe even in a separate new xterm window), by executing: abinit < input_C_test.files >& log_C_test & There are 18 double-index datasets in total, with the first index running from 1 to 9 and the second from 1 to 2. You can check on the progress of the calculation by issuing ls outputs/. When the .._o_DS92.. files appear, the calculation should be just about finished. While the calculation runs you might want to take a look in the input file. Note the lines pertaining to the increment in ecut (around line 29):  ... # Cutoff variables ecut:? 5.0 ecut+? 5.0 pawecutdg 110.0 ecutsm 0.5 ... ecut is increased in increments of 5 Ha from an initial value of 5, to a final ecut of 45 Ha. Note that pawecutdg is kept fixed, at a value high enough to be expected to be good for the final value of ecut. In principle, a convergence study of pawecutdg should be performed as well, once a good value of ecut has been found. We can now check the basic convergence attributes of the dataset. The convergence of the total energy is easily checked by issuing some grep commands:  grep 'etotal' ab_C_test.out This should give you an output similar to this (though not the text to the left):  etotal (ecut) etotal11 -1.0972419844E+01 etotal21 -1.1443195800E+01 - 470.78 mHa (10 Ha) etotal31 -1.1507213147E+01 - 64.02 mHa (15 Ha) etotal41 -1.1517538732E+01 - 10.33 mHa (20 Ha) etotal51 -1.1518045259E+01 - 0.51 mHa (25 Ha) etotal61 -1.1518180302E+01 - 0.14 mHa (30 Ha) etotal71 -1.1518406425E+01 - 0.23 mHa (35 Ha) etotal81 -1.1518520623E+01 - 0.11 mHa (40 Ha) etotal91 -1.1518549151E+01 - 0.03 mHa (45 Ha) Your values might differ slightly in the last decimals. The calculation of diamond with the current PAW Carbon dataset converged to a precision of the total energy below 1 mHa for a cutoff of about 25 Ha (this is not particularly good for a PAW dataset). Also, the convergence is a bit jumpy after an ecut of about 25 Ha, which is an indication of a) that the number of projectors per angular momentum channel is low, and b) that other parameters apart from ecut dominate convergence beyond this point. If we turn to the ~band structure~, we can use the script comp_bands_abinit2abinit.py to check the convergence of the band structure. Copy the script to the directory where the ABINIT input file is and issue:  python comp_bands_abinit2abinit.py outputs/ab_C_test_o_DS12_EIG outputs/ab_C_test_o_DS92_EIG eV This will print a long series of columns and at the end you will see:  ... # nvals: 280 # average diff: 1.758813 eV # minimum diff: -4.437905 eV # maximum diff: 1.089000 eV # # NOTE: Abinit values are read in fixed format with five decimal # places. For low values, four or three decimal figures # may be the highest precision you can get. This provides you with some statistics of the difference in the band energies. Specifically this is the average difference between a the band structure calculated at an ecut of 5 Ha (in dataset 12) and another at an ecut of 45 Ha (in dataset 92). The differences between these datasets are naturally very large, about 1.8 eV on average, because the band-structure of the first dataset is far from converged. The columns output before the statistics are arranged so that if you pipe the output to a data file: python comp_bands_abinit2abinit.py outputs/ab_C_test_o_DS12_EIG outputs/ab_C_test_o_DS92_EIG eV > bands_5Ha_vs_45Ha.dat you can plot the two band structures in gnuplot directly, by entering:  gnuplot> plot 'bands_5Ha_vs_45Ha.dat' u 1:2 w lp title '5 Ha', 'bands_5Ha_vs_45Ha.dat' u 1:3 w lp title '45 Ha' This should furnish you with a graph that looks something like this: Not surprisingly, the band structures are very different. However, a search through the datasets of increasing index (i.e. DS22, DS32, DS42, …) yields that for dataset 42, i.e with an ecut of 20 Ha, we are already converged to a level of 0.01 eV. Issuing the command:  python comp_bands_abinit2abinit.py outputs/ab_C_test_o_DS42_EIG outputs/ab_C_test_o_DS92_EIG eV > bands_20Ha_vs_45Ha.dat and plotting this with:  gnuplot> plot 'bands_20Ha_vs_45Ha.dat' u 1:2 w lp title '5 Ha', 'bands_20Ha_vs_45Ha.dat' u 1:3 w lp title '45 Ha' Should give you a plot similar to this: You can convince yourself by zooming in that the band structures are very similar. The statistics at the end of the bands_20Ha_vs_45Ha.dat file shows that we are converged within abinit: ... # nvals: 280 # average diff: 0.003812 eV # minimum diff: -0.008980 eV # maximum diff: 0.000272 eV ... ### 3.2. Carbon - calculating the equilibrium lattice parameter That we have converged the dataset on its own does of course not mean that the dataset is good, i.e. that it reproduces the same results as an all-electron calculation. To independently verify that the dataset is good, we need to calculate the equilibrium lattice parameter (and the Bulk modulus) and compare this and the band structure with an Elk calculation. First, we will need to calculate the total energy of diamond in ABINIT for a number of lattice parameters around the minimum of the total energy. There are example input and “.files” files for doing this at: ab_C_equi.in and input_C_equi.files. The new input file has ten datasets which increment the lattice parameter, alatt, from 6.1 to 7.0 Bohr in steps of 0.1 Bohr. A look in the input file will tell you that ecut is set to 25 Hartrees. Copy these to your abinit_test directory and run: abinit < input_C_equi.files >& log_C_equi & The run should be done fairly quickly, and when it’s done we can check on the volume and the total energy by using “grep”  grep 'volume' log_C_equi and  grep 'etotal' log_C_equi The outputs should be something like this:  ... Unit cell volume ucvol= 5.6745250E+01 bohr^3 Unit cell volume ucvol= 5.9582000E+01 bohr^3 Unit cell volume ucvol= 6.2511750E+01 bohr^3 Unit cell volume ucvol= 6.5536000E+01 bohr^3 Unit cell volume ucvol= 6.8656250E+01 bohr^3 Unit cell volume ucvol= 7.1874000E+01 bohr^3 Unit cell volume ucvol= 7.5190750E+01 bohr^3 Unit cell volume ucvol= 7.8608000E+01 bohr^3 Unit cell volume ucvol= 8.2127250E+01 bohr^3 Unit cell volume ucvol= 8.5750000E+01 bohr^3 ... etotal1 -1.1461962668E+01 etotal2 -1.1480480413E+01 etotal3 -1.1494794567E+01 etotal4 -1.1505340658E+01 etotal5 -1.1512513911E+01 etotal6 -1.1516673105E+01 <- etotal7 -1.1518144233E+01 <- minimum around here etotal8 -1.1517223895E+01 <- etotal9 -1.1514182185E+01 etotal10 -1.1509265543E+01 ... If we examine the etotal values, the total energy does indeed go to a minimum, and we also see that given the magnitude of the variations of the total energy, an ecut of 25 Ha should be more than sufficient. We will now extract the equilibrium volume and bulk modulus by using the eos bundled with elk this requires us to put the above data in an eos.in file. Create such a file with your favorite editor and enter the following five lines and then the data you just extracted:  "C - Diamond" : cname - name of material 2 : natoms - number of atoms 1 : etype - equation of state fit type 50.0 95.0 100 : vplt1, vplt2, nvplt - start, end and #pts for fit 10 : nevpt - number of supplied points 5.6745250E+01 -1.1461962668E+01 5.9582000E+01 -1.1480480413E+01 6.2511750E+01 -1.1494794567E+01 6.5536000E+01 -1.1505340658E+01 6.8656250E+01 -1.1512513911E+01 7.1874000E+01 -1.1516673105E+01 7.5190750E+01 -1.1518144233E+01 7.8608000E+01 -1.1517223895E+01 8.2127250E+01 -1.1514182185E+01 8.5750000E+01 -1.1509265543E+01 When you run eos (the executable should be located in src/eos/ in the directory where Elk was compiled), it will produce several .OUT files. The file PARAM.OUT contains the information we need:  C - Diamond Universal EOS Vinet P et al., J. Phys.: Condens. Matter 1, p1941 (1989) (Default units are atomic: Hartree, Bohr etc.) V0 = 75.50872614 E0 = -11.51815408 B0 = 0.1564710308E-01 B0' = 3.685323465 B0 (GPa) = 460.3535890 This tells us the equilibrium volume and bulk modulus. The volume of our diamond FCC lattice depends on the lattice parameter as:$\frac{a^3}{4}. If we want to convert the volume to a lattice parameter, we have to multiply by four and then take the third root, so: alatt = (4*75.50872614)^(1/3) = 6.7095 Bohr (3.5505 Å) at equilibrium for this dataset. ### 3.3. Carbon - the all-electron calculation In order to estimate whether these values are good or not, we need independent verification, and this will be provided by the all-electron Elk code. There is an Elk input file matching our abinit diamond calculation at elk_C_diamond.in. You need to copy this file to a directory set up for the Elk run (why not call it C_elk), and it needs to be renamed to elk.in, which is the required input name for an Elk calculation. We are now ready to run the Elk code for the first time. If we take a look in the elk.in file, at the beginning we will see the lines:  ! Carbon, diamond structure (FCC) ! The tasks keyword defines what will be done by the code: ! 0 - Perform ground-state calculation from scratch ! 1 - Restart GS calc. from STATE.OUT file ! 20 - Calculate band structure as defined by plot1d tasks 0 20 ! Set core-valence cutoff energy ecvcut -6.0 ! Construct atomic species file 'C.in' species 6 : atomic number 'C' 'carbon' 21894.16673 : atomic mass 1.300000000 : muffin-tin radius 4 : number of occ. states 1 0 1 2 : 1s 2 0 1 2 : 2s 2 1 1 1 : 2p m=1 2 1 2 1 : 2p m=2 ... Any text after an exclamation mark (or a colon on the lines defining data) is a comment. The keyword tasks defines what the code should do. In this case it is set to calculate the ground state for the given structure and to calculate a band structure. The block ecvcut sets the core-valence cutoff energy. The next input block, species defines the parameters for the generation of an atomic species file (it will be given the name C.in). As a first step, we need to generate this file, but we will need to modify it before we perform the main calculation. Therefore, you should run the code briefly (by just running the executable in your directory) and then kill it after a few seconds (using Ctrl+C for instance ), as soon as it has generated the C.in file. If you look in your directory after the code has been killed you will probably see a lot of .OUT files with uppercase names. These are the Elk output files. You should also see a C.in file. When you open it, you should see:  'C' : spsymb 'carbon' : spname -6.00000 : spzn 39910624.40 : spmass 0.816497E-06 1.3000 29.6725 300 : sprmin, rmt, sprmax, nrmt 4 : spnst 1 0 1 2.00000 T : spn, spl, spk, spocc, spcore 2 0 1 2.00000 F 2 1 1 1.00000 F 2 1 2 1.00000 F 1 : apword 0.1500 0 F : apwe0, apwdm, apwve 0 : nlx 3 : nlorb 0 2 : lorbl, lorbord 0.1500 0 F : lorbe0, lorbdm, lorbve 0.1500 1 F 1 2 : lorbl, lorbord 0.1500 0 F : lorbe0, lorbdm, lorbve 0.1500 1 F 0 3 : lorbl, lorbord 0.1500 0 F : lorbe0, lorbdm, lorbve 0.1500 1 F -0.7512 0 T The first four lines contain information pertaining to the symbol, name, charge and mass of the atom. The fifth line holds data concerning the numerical grid: the distance of the first grid point from the origin, the muffin-tin radius, the maximum radius for the on-site atomic calculation, and the number of grid points. The subsequent lines contain data about the occupied states (the ones ending with “T” or “F”), and after that there is information pertaining to the FP-LAPW on-site basis functions. The first important thing to check here is whether all the orbitals that we have included as valence states in the PAW dataset are treated as valence in this species file. We do this by checking that there is an “F” after the corresponding states in the occupation list:  ... 1 0 1 2.00000 T : spn, spl, spk, spocc, spcore 2 0 1 2.00000 F 2 1 1 1.00000 F 2 1 2 1.00000 F ... The first two numbers are the n, l quantum numbers of the atomic state, so we see that the 2s states, and the 2p states are set to valence as in the PAW dataset. !!! Note This might not be the case in general, the version of Elk we use is modified to accept an adjustment of the cutoff energy for determining whether a state should be treated as core or valence. This is what is set by the line: ... ecvcut -6.0 : core-valence cutoff energy ... in the elk.in file. If you find too few or too many states are included as valence for another atomic species, this value needs to be adjusted downwards or upwards. The second thing we need to check is whether the number of grid points and the muffin-tin radius that we use in the Elk calculation is roughly equivalent to the PAW one. If you have a look in the PAW dataset we generated before, i.e. in the C_LDA.pawps file, there are a number of lines: … 1 2 493 2.1888410559E-03 1.3133046335E-02 : mesh 1, type,size,rad_step[,log_step] 2 2 488 2.1888410559E-03 1.3133046335E-02 : mesh 2, type,size,rad_step[,log_step] 3 2 529 2.1888410559E-03 1.3133046335E-02 : mesh 3, type,size,rad_step[,log_step] 4 2 642 2.1888410559E-03 1.3133046335E-02 : mesh 4, type,size,rad_step[,log_step] 1.3096246076 : r_cut(PAW) … These define the PAW grids used for wavefunctions, densities and potentials. To approximately match the intensity of the grids, we should modify the fifth line in the C.in file:  ... 0.816497E-06 1.3100 31.4101 300 : sprmin, rmt, sprmax, nrmt ... to: ... 0.816497E-06 1.3100 31.4101 500 : sprmin, rmt, sprmax, nrmt ... You now need to comment out the species generation input block in the elk.in file:  ... ! Construct atomic species file 'C.in' !species ! 6 : atomic number ! 'C' ! 'carbon' ! 21894.16673 : atomic mass ! 1.300000000 : muffin-tin radius ! 4 : number of occ. states ! 1 0 1 2 : 1s ! 2 0 1 2 : 2s ! 2 1 1 1 : 2p m=1 ! 2 1 2 1 : 2p m=2 ... !!! Note This is very important! If you do not comment these lines the species file C.in will be regenerated when you run Elk and your modifications will be lost. Now it is time to start Elk again. The code will now run and produce a lot of .OUT files. There is rarely anything output to screen, unless it’s an error message, so to track the progress of the Elk calculation you can use the tail command:  tail -f INFO.OUT You get out of tail by pressing CRTL+C. While the calculation is running, you might want to familiarise yourself with the different input blocks in the elk.in file. When the Elk run has finished, there will be a BAND.OUT file in your run directory. We can now do an analogous band structure comparison to before, by using the python script comp_bands_abinit2elk.py (you should copy this to your current directory). If your previous abinit calculation is in the subdirectory ../C_abinit/abinit_test above you write:  python comp_bands_abinit2elk.py ../C_atompaw/abinit_test/outputs/ab_C_test_o_DS42_EIG BAND.OUT eV This will get you the ending lines:  ... # nvals: 280 # average diff: 12.993572 eV # minimum diff: -13.266287 eV # maximum diff: -12.888489 eV ... So it looks like there is a huge difference! However, there is something we have forgotten. Pipe the data to a file by writing: python comp_bands_abinit2elk.py ../C_atompaw/abinit_test/outputs/ab_C_test_o_DS42_EIG BAND.OUT eV > bands.dat and plot it in gnuplot with: gnuplot> plot 'bands.dat' u 1:2 w lp title 'ABINIT', 'bands.dat' u 1:3 w lp title 'Elk' You should get a graph like this: As you can see, the band structures look alike but differ by an absolute shift, which is normal, because in a periodic system there is no unique vacuum energy, and band energies are always defined up to an arbitrary constant shift. This shift depends on the numerical details, and will be different for different codes using different numerical approaches. (Note in the Elk input file that the keyword xctype controls the type - LDA or GGA - of the exchange-correlation functional.) However, if we decide upon a reference pont, like the valence band maximum (VBM), or a point nearby, and align the two band plots at that point, there will still be differences. By comparing with the plot we just made, we see that the VBM is at the ninth k-point from the left, on band four. The script we used previously can accomodate a shift, by issuing the command: python comp_bands_abinit2elk.py ../C_atompaw/abinit_test/outputs/ab_C_test_o_DS42_EIG BAND.OUT align 9 4 eV So that if the keyword align is present followed by the k-point index and band number, we order the script to align at that point. Naturally, that will make the positions of that particular point fit perfectly, but if we look at the end of the output:  ... # AVERAGES FOR OCCUPIED STATES: # nvals: 106 # average diff: 0.021444 eV # minimum diff: -0.041138 eV # maximum diff: 0.066111 eV # # AVERAGES FOR UNOCCUPIED STATES: # nvals: 174 # average diff: 0.047334 eV # minimum diff: -0.284242 eV # maximum diff: 0.093556 eV ... we can tell that this is not true for the rest of the points. Since the script assumes alignment at the VBM, it now separates its statistics for occupied and unoccupied bands. The uppermost unoccupied bands can fit badly, depending on what precision was asked of abinit (especially, if nbdbuf is used). The fit is quite bad in general, an average of about 0.025 eV difference for occupied states, and about 0.05 eV difference for unoccupied states. If you plot the ouput as before, by piping the above to a bands.dat file and executing the same gnuplot command, you should get the plot below. On the scale of the band plot there is a small - but visible - difference between the two. Note that the deviations are usually larger away from the high-symmetry points, which is why it’s important to choose some points away from these as well when making these comparisons. However, it is difficult to conclude visually from the band structure that this is a bad dataset without using the statistics output by the script, and without some sense of what precision can be expected. As we are now creating our “gold standard” with an Elk calculation, we also need to calculate the equilibrium lattice parameter and Bulk modulus of diamond with the Elk code. Unfortunately, Elk does not use datasets, so the various lattice parameters we used in our abinit structural search will have to be put in one by one by hand and the code run for each. The lattice parameters in the abinit run were from 6.1 to 7.0 in increments of 0.1, so that makes ten runs in total. To perform the first, simply edit the elk.in file and change the keyword (at line 57):  ... scale 6.7403 : lattice parameter in Bohr ... to:  ... scale 6.1 : lattice parameter in Bohr ... !!! Note You also have to change the keyword frozencr to “.false.” because, at the time of writing, there is an error in the calculation of the total energy for frozen core-states. This means that the Elk input file must have the keyword (at line 65 ): ... frozencr .false. ... when you are determining parameters which depend on the total energy. (It can safely be set to “.true.” for band structure calculations however.) The difference in the lattice parameters when using frozen versus unfrozen core states in an all-electron calculation is expected to be of the order of 0.005 Bohr. Finally, you don’t need to calculate the band structure for each run, so you might wand to change the tasks keyword section (at line 7):  ... tasks 0 20 ... to just  ... tasks 0 ... After you’ve done these modifications, run Elk again. After the run has finished, look in the TOTENERGY.OUT and the LATTICE.OUT files to get the converged total energy and the volume. Write these down or save them in a safe place, edit the elk.in file again, and so forth until you’ve calculated all ten energies corresponding to the ten lattice parameter values. In the end you should get a list which you can put in an eos.in file:  "C - Diamond (Elk)" : cname - name of material 2 : natoms - number of atoms 1 : etype - equation of state fit type 50.0 95.0 100 : vplt1, vplt2, nvplt - start, end and #pts for fit 10 : nevpt - number of supplied points 56.74525000 -75.5773620914 59.58200000 -75.5945921584 62.51175000 -75.6076996622 65.53600000 -75.6171195448 68.65625000 -75.6232633666 71.87400000 -75.6265024368 75.19075000 -75.6271230861 78.60800000 -75.6254190892 82.12725000 -75.6216564850 85.75000000 -75.6160830267 (Your values might be slightly different in the last few decimals depending on your system.) By running the eos utility as before we get:  V0 = 74.34092358 B0 (GPa) = 467.7335903 alatt = (4*74.34092358)^(1/3) = 6.6747 Bohr (3.5321 Å) So we see that the initial, primitive, abinit dataset is about 11 GPa off for the Bulk modulus and about 0.04 Bohr away from the correct value for the lattice parameter. In principle, these should be about an order of magnitude better, so let us see if we can make it so. ### 3.4. Carbon - improving the dataset Now that you know the target values, is up to you to experiment and see if you can improve this dataset. The techniques are well documented in tutorial PAW2. Here’s a brief summary of main points to be concerned about: • Use the keyword series custom rrkj ..., or custom polynom ..., or custom polynom2 ..., if you want to have maximum control over the convergence properties of the projectors. • Check the logarithmic derivatives very carefully for the presence of ghost states. • A dataset intended for ground-state calculations needs, as a rule of thumb, at least two projectors per angular momentum channel. This is because only the occupied states need to be reproduced very accurately. If you need to perform calculations which involve the Fock operator or unoccupied states • like in GW calculations for instance - you will probably need at least three projectors. You might also want to add extra projectors in completely unoccupied l-channels. We will now benchmark a more optimized atomic dataset for carbon. Try and check the convergence properties, equilibrium lattice parameter, bulk modulus, and bands for the input file below:  C 6 ! Atomic name and number LDA-PW scalarrelativistic loggrid 801 logderivrange -10 40 1000 ! XC approx., SE type, gridtype, # pts, logderiv 2 2 0 0 0 0 ! maximum n for each l: 2s,2p,0d,0f.. 2 1 2 ! Partially filled shell: 2p^2 0 0 0 ! Stop marker c ! 1s - core v ! 2s - valence v ! 2p - valence 1 ! l_max treated = 1 1.3 ! core radius r_c y ! Add unocc. s-state 12.2 ! reference energy n ! no more unoccupied s-states y ! Add unocc. p-state 6.9 ! reference energy n ! no more unoccupied p-states custom polynom2 7 11 vanderbiltortho sinc ! more complicated scheme for projectors 3 0 ultrasoft ! localisation scheme 1.3 ! Core radius for occ. 2s state 1.3 ! Core radius for unoocc. 2s state 1.3 ! Core radius for occ. 2p state 1.3 ! Core radius for unocc. 2p state 2 ! Run atompaw2abinit converter prtcorewf noxcnhat nospline noptim ! Abinit conversion options 0 ! Stop marker Generate an atomic data file from this (you can replace the items in the old input file if you want, or make a new directory for this study). You might want to try and modify the gnuplot scripts so that they work correctly for this dataset. (The wfn* files are ordered just like the core radius list at the end, so now their meaning and the numbering of some other files have changed.) There is an example of the modifications in the plot script plot_C_all_II.p, which you can download and run in gnuplot. You should get a plot like this: Note the much better fit of the logarithmic derivatives, and the change in the shape of the projector functions (in blue in the wfn plots), due to the more complicated scheme used to optimise them. Generate the dataset like before and run the abinit ecut testing datasets in the ab_C_test.in abinit input file again. You should get an etotal convergence like this (again, the values to the left are just there to help):  etotal (ecut) etotal11 -1.0784567462E+01 etotal21 -1.1488776903E+01 - 704.21 mHa (10 Ha) etotal31 -1.1522195505E+01 - 33.42 mHa (15 Ha) etotal41 -1.1523171951E+01 - 0.98 mHa (20 Ha) etotal51 -1.1523269821E+01 - 0.10 mHa (25 Ha) etotal61 -1.1523317666E+01 - 0.15 mHa (30 Ha) etotal71 -1.1523327718E+01 - 0.01 mHa (35 Ha) etotal81 -1.1523354510E+01 - 0.03 mHa (40 Ha) etotal91 -1.1523374518E+01 - 0.02 mHa (45 Ha)  This dataset already seems to be converged to about 1 mHa at an ecut of 15 Ha, so it is much more efficient. A comparison of bands (in units of eV) between datasets 32 and 92 gives:  ... # nvals: 280 # average diff: 0.002181 eV # minimum diff: -0.010612 eV # maximum diff: 0.000544 eV ...  Which also shows a much faster convergence than before. Is the dataset accurate enough? Well, if you run the abinit equilibrium parameter input file in ab_C_equi.in, you should get data for an eos.in file:  "C - Diamond (second PAW dataset)" : cname - name of material 2 : natoms - number of atoms 1 : etype - equation of state fit type 50.0 95.0 100 : vplt1, vplt2, nvplt - start, end and #pts for fit 10 : nevpt - number of supplied points 5.6745250E+01 -1.1471683253E+01 5.9582000E+01 -1.1489338191E+01 6.2511750E+01 -1.1502854195E+01 6.5536000E+01 -1.1512663617E+01 6.8656250E+01 -1.1519157680E+01 7.1874000E+01 -1.1522691247E+01 7.5190750E+01 -1.1523587073E+01 7.8608000E+01 -1.1522138965E+01 8.2127250E+01 -1.1518614529E+01 8.5750000E+01 -1.1513257920E+01 And when fed to eos, this gives us the equilibrium data:  V0 = 74.72599563 B0 (GPa) = 465.6037415 alatt = (4*74.72599563)^(1/3) = 6.6862 Bohr (3.5381 Å) For comparison, we list all previous values again:  Equilibrium Bulk modulus lattice volume, V0 B0 parameter 75.5087 460.35 3.5505 Å (first primitive PAW dataset) 74.7260 465.60 3.5381 Å (second better PAW dataset) 74.3410 467.73 3.5321 Å (Elk all-electron) It is obvious that the second dataset is much better than the first one. A comparison of the most converged values for the bands using the command: python comp_bands_abinit2elk.py ab_C_test_o_DS92_EIG BAND.OUT align 9 4 eV (This assumes that you have all the files you need in the current directory.) As before, the extra command parameters on the end mean “align the 9-th k-point on the fourth band and convert values to eV”. This will align the band structures at the valence band maximum. The statistics printed out at the end should be something like this:  ... # AVERAGES FOR OCCUPIED STATES: # nvals: 106 # average diff: 0.014703 eV # minimum diff: -0.000748 eV # maximum diff: 0.042437 eV # # AVERAGES FOR UNOCCUPIED STATES: # nvals: 174 # average diff: 0.016659 eV # minimum diff: -0.011563 eV # maximum diff: 0.123488 eV ... Which shows a precision, on average, of slightly better than 0.01 eV for both the four occupied and the four lowest unoccupied bands. As before, you can pipe this output to a file and plot the bands for visual inspection. This is a better dataset, but probably by no means the best possible. It is likely that one can construct a dataset for carbon that has even better convergence properties, and is even more accurate. You are encouraged to experiment and try to make a better one. ## 4. Magnesium - dealing with the Fermi energy of a metallic system There is added complication if the system is metallic, and that is the treatment of the smearing used in order to eliminated the sharp peaks in the density of states (DOS) near the Fermi energy. The DOS is technically integrated over in any ground-state calculation, and for a metal this requires, in principle, an infinite k-point grid in order to resolve the Fermi surface. In practice, a smearing function is used so that a usually quite large - but finite - number of k-points will be sufficient. This smearing function has a certain spread controlled by a smearing parameter, and the optimum value of this parameter depends on the k-point grid used. As the k-point grid becomes denser, the optimum spread becomes smaller, and all values converge toward their ideal counterparts in the limit of no smearing and an infinitely dense grid. The problem is that, in ABINIT, finding the optimum smearing parameter takes a (potentially time consuming) convergence study. However, we are in luck. The elk code has an option for automatically determining the smearing parameter. Thus we should use the Elk code first, set a relatively dense k-mesh, and calculate the equilibrium bulk modulus, lattice parameter and band structure. Then we make sure to match the automatically determined smearing width, and most importantly, make sure that we match the smearing function used between the Elk and the abinit calculation. ### 4.1. Magnesium - The all-electron calculation There is an Elk input file prepared at: elk_Mg_band.in, we suggest you copy it into a subdirectory dedicated to the Mg Elk calculation (why not Mg_elk?), rename it to elk.in and take a look inside the input file. There will be sections familiar from before, defining the lattice vectors, structure, etc. (Mg has a 2-atom hexagonal unit cell.) Then there are a couple of new lines for the metallic case:  ... ! Metallic options stype 0 : Smearing type 0 - Gaussian autoswidth .true. : Automatic determination of swidth ... When you run Elk with this file, it will start a ground-state run (this might take some time due to the dense k-point mesh), all the while automatically determining the smearing width. At the end of the calculation the final value of swidth will have been determined, and can be easily extracted with a grep:  grep ' smearing' INFO.OUT this should furnish you with a list:  Automatic determination of smearing width New smearing width : 0.1000000000E-01 New smearing width : 0.4035700344E-02 New smearing width : 0.4107006728E-02 New smearing width : 0.4108879116E-02 New smearing width : 0.4108502343E-02 New smearing width : 0.4110133080E-02 New smearing width : 0.4110216093E-02 New smearing width : 0.4109823554E-02 New smearing width : 0.4109817386E-02 New smearing width : 0.4109816489E-02 New smearing width : 0.4109816512E-02 New smearing width : 0.4109816517E-02 where the last value is the one we seek, i.e. the smearing at convergence. Since this Elk file will also calculate the band structure, you will have a BAND.OUT file at the end of this calculation to compare your ABINIT band structure to. There is one more thing we need to check, and that is the Fermi energy:  grep 'Fermi ' INFO.OUT Fermi : 0.121777309929 Fermi : 0.130932333253 Fermi : 0.131278961043 Fermi : 0.131395483173 Fermi : 0.131577231948 Fermi : 0.131548959894 Fermi : 0.131499221547 Fermi : 0.131498356586 Fermi : 0.131498248517 Fermi : 0.131498251395 Fermi : 0.131498251982 Fermi : 0.131498251874 The last one is the Fermi energy at convergence. We will need this later when we compare band structures to align the band plots at the Fermi energy. Now it’s time to calculate the equilibrium lattice parameters. There is a prepared file at: elk_Mg_equi.in. As before copy this to your directory rename it to elk.in. The layout of this file looks pretty much like the one before, except the band structure keywords are missing, and now switdth is fixed to the value we extracted before:  ... ! Metallic options stype 0 : Smearing type 0 - Gaussian swidth 0.4109816517E-02 : Smearing width ... To calculate the equilibrium lattice parameters, we are going to use the bulk modulus, which is a quantity defined with respect to a scaling of the entire cell (as opposed to Young’s modulus, for instance, which is defined with respect to linear scaling along the lattice vectors). There is a handy scale keyword for Elk, which will accomplish this for us. If we look at the region where the lattice is defined:  ... ! Define lattice vectors ! Magnesium has an hexagonal native structure ! with a=b=3.20927 Å c=5.21033 Å alpha=90 beta=90 gamma=60 ! (experimental, at 25 degrees Celsius) ! Scale factor to be applied to all lattice vectors scale 1.00 with 6.0646414 0.0000000 0.0000000 3.0323207 5.2521335 0.0000000 0.0000000 0.0000000 9.8460968 ... We will here also need to perform several calculations (like we did for the diamond case) and we need to change the value of the scale keyword for each one. A good set of values would be: 0.94, 0.96, 0.98, 1.0, 1.02 1.04 and 1.06, i.e. a change of scale in steps of 2% with seven values in total spaced around the experimental equilibrium lattice structure. After each run, as before, you should collect the value of the unit cell volume and the total energy. After seven runs you should have a set of numbers which you can put in an eos.in file (depending on the system, your actual values may differ slightly from these):  "Mg - bulk metallic" 2 : natoms - number of atoms 1 : etype - equation of state fit type 260.0 374.0 100 : vplt1, vplt2, nvplt - start, end and #pts for fit 7 : nevpt - number of supplied points 260.4884939 -399.044398311 277.4716924 -399.046748766 295.1774734 -399.047369385 313.6208908 -399.046516326 332.8169982 -399.044519274 352.7808497 -399.041572824 373.5274988 -399.037858448 Upon using the eos utility you will get standard type of outputs in PARAM.OUT:  Mg - bulk metallic Universal EOS Vinet P et al., J. Phys.: Condens. Matter 1, p1941 (1989) (Default units are atomic: Hartree, Bohr etc.) V0 = 293.1890929 E0 = -399.0473679 B0 = 0.1329392525E-02 B0' = 4.212619901 B0 (GPa) = 39.11207186  Now we have to translate this in terms of the lattice parameters. The equilibrium scale factor is given by:scale = (\frac{V_0}{V_1})^{\frac{1}{3}} = (\frac{293.1890929}{313.6208908})^{\frac{1}{3}} = 0.9777945417\$

Where V1 is the volume with scale set to 1.0. Multiplying all basis vectors with this scale factor, we have that:

 Equilibrium        Bulk modulus       lattice
volume, V0         B0                parameters
293.1891           39.1121            a = b = 3.1380 Å  c = 5.0946 Å

Now we have all the information needed to proceed with the abinit calculation.

### 4.2. Magnesium - The abinit calculation

As usual, it’s best to prepare a separate subdirectory for the atomic data and the ABINIT test. We will assume that the subdirectories have been created as:

 mkdir Mg_atompaw
mkdir Mg_atompaw/abinit_test
mkdir Mg_atompaw/abinit_test/outputs

and that your current directory is ./Mg_atompaw. For the Mg ATOMPAW input, create a file Mg.input with the following content:

 Mg 12
LDA-PW scalarrelativistic loggrid 801 40. logderivrange -10 40 1000
3 3 0 0 0 0
3 1 0
0 0 0
c
v
v
v
v
1
1.9
n
n
custom polynom2 7 11 vanderbiltortho sincshape
2 0 ultrasoft
1.9
1.9
1.9
1.9
2
prtcorewf noxcnhat nospline noptim
0

Note that there are not really that many projectors in this dataset, only two per angular momentum channel. It should be possible to make this much better adding extra projectors, and maybe even unoccupied d-states. If you run atompaw with this, you can have a look with the bundled plot_MG_all.p file and others like it to get a feel for the quality of this dataset.

Generate the abinit dataset file, and make sure it’s given as: ./Mg_atompaw/Mg_LDA.pawps, then go to the subdirectory for the ABINIT test, and copy these files to it: ab_Mg_test.in, input_Mg_test.files, ab_Mg_equi.in and input_Mg_equi.files. The file for testing the convergence has already been set up so that the smearing strategy is equivalent to the Elk one, as evidenced by the lines:

 ...
# Parameters for metals
tsmear 0.4109816517E-02
occopt 7
...

inside it. The occopt 7 input variable corresponds exactly to the Gaussian smearing which is the default for the Elk code. (In fact it is the 0th order Methfessel-Paxton expression [[cite:Methfessel1989]], for other possibilities compare the entries for the keyword stype in the Elk manual and the entries for occopt in ABINIT).

Now run the test input file (if your computer has several cores, you might want to take advantage of that and run abinit in parallel). The test suite can take some time to complete, because of the dense k-point mesh sampling. Make sure you pipe the screen to a log file: log_Mg_test

When the run is finished, we can check the convergence properties as before, and we that an ecut of 15 Ha is definitely enough. The interesting thing will now be to compare the band structures. First we need to check the Fermi energy of the abinit calculation, if you do a grep:

 grep ' Fermi' log_Mg_test

you will see a long list of Fermi energies, one for each iteration, finally converging towards one number:

 ...
newocc : new Fermi energy is       0.103033 , with nelect=     20.000000
newocc : new Fermi energy is       0.103033 , with nelect=     20.000000
newocc : new Fermi energy is       0.103033 , with nelect=     20.000000

The last one of these is the final Fermi energy of the ABINIT calculation. The abinit2elk band comparison script can now be given the Fermi energies of the two different calculations and align band structures there. Copy the BAND.OUT file from the Elk calculation to the current directory, as well as the band comparison script comp_bands_abinit2elk.py. This script can also be used to align the bands at different Fermi energies. However, in the BAND.OUT file from Elk, the bands are already shifted so that the Fermi energy is at zero, so it is only the alignment of the abinit file that is required:

 python comp_bands_abinit2elk.py ./outputs/ab_Mg_test_o_DS32_EIG BAND.OUT Fermi 0.103033 0.0 eV

Issuing this command will provide the final lines:

 ...
#        nvals:   846
# average diff:    0.000949  eV
# minimum diff:   -0.001316  eV
# maximum diff:    0.004479  eV
...

Which means that we are on average accurate to about 0.001 eV. If you pipe the output to a file bands_abinit_elk.dat, and go into gnuplot and issue these commands:

 gnuplot> set yrange[-0.3:0.5]
gnuplot> plot 'bands_abinit_elk.dat' u 1:2 w lp t 'ABINIT'
gnuplot> replot 'bands_abinit_elk.dat' u 1:3 w lp t 'Elk'
gnuplot> replot 'bands_abinit_elk.dat' u 1:(0.0) w l t 'Fermi level'

You should get a plot that looks something like this:

As we can see, the bands should fit quite well. Finally, for the structural, a run of the ab_Mg_equi.in file gives us all the information we need for the creation of an eos.in file:

 "Mg - bulk metallic (ABINIT)"
2                      : natoms - number of atoms
1                      : etype - equation of state fit type
260.0 380.0 100        : vplt1, vplt2, nvplt - start, end and #pts for fit
7                      : nevpt - number of supplied points
2.6048849E+02  -1.2697536886E+02
2.7747169E+02  -1.2697769560E+02
2.9517747E+02  -1.2697830129E+02
3.1362089E+02  -1.2697744079E+02
3.3281700E+02  -1.2697541356E+02
3.5278085E+02  -1.2697240135E+02
3.7352750E+02  -1.2696861050E+02

When the eos utility is run, we get the equilibrium volume and Bulk modulus:

 ...
V0                =            293.0662989
...
B0 (GPa)          =            39.23340074

Converting this to lattice parameters as before, we can compare this with the Elk run:

 Equilibrium        Bulk modulus       lattice
volume, V0         B0                parameters
293.1891           39.1121        a = b = 3.1380 Å  c = 5.0946 Å  (Elk)
293.0663           39.2334        a = b = 3.1376 Å  c = 5.0939 Å  (ABINIT)

Which is very close.

Again, this is a decent dataset for ground-state calculations, but it can probably be made even better. You are encouraged to try and do this.

## 5. PAW datasets for GW calculations

There are a number of issues to consider when making datasets for GW calculations, here is a list of a few:

• Care needs to be taken so that the logarithmic derivatives match for much higher energies than for ground-state calculations. They should at least match well up to the energy of the unoccupied states used in the calculation. The easiest way of ensuring this is increasing the number of projectors per state.

• The on-site basis needs to be of higher quality to minimise truncation error due to the finite number of on-site basis functions (projectors). Again, this requires more projectors per angular momentum channel.

• As a rule of thumb, a PAW dataset for GW should have at least three projectors per state, if not more.

• A particularly sensitive thing is the quality of the expansion of the pseudised plane-wave part in terms of the on-site basis. This can be checked by using the density of states (DOS), as described in the first PAW tutorial.