Hi Alex
I think conograph does well for tof.
Best
Jon
On April 13, 2020 8:24:55 PM GMT+02:00, Alexandros Lappas
wrote:
>Dear colleagues,
>
>
>
>We are working on some neutron time-of-flight (TOF) data and attempt to
>index them within GSAS-II.
>
>
>
>As the low-angle detector banks contain
Hello,
In the photo, the pellet is black and the powder is white. Why is that?
Best
Jon
On December 8, 2017 3:35:20 PM GMT+01:00, "François Goutenoire"
wrote:
>Dear Rietveld users,
>
>We observe an unusual asymmetric peak shape on pellet and not when the
Hi Alan,
In the limiting case of orienting all crystals in 3D you get a mosaic
single crystal (e.g. [1], or using an XFEL to measure 1 at a time). Then
the refined the crystal structure has somewhat better accuracy than with
a 1D Rietveld fit. Perhaps not the most popular idea for this
Dear Kurt,
You can peaksearch the images with any number of packages and then look
at the extracted spot positions. The stuff we wrote lives at
http://sourceforge.net/projects/fable/ and it is normally used to fit
grain-by-grain strain tensors. If you can isolate the spots you do
indeed get a
On 08/08/2013 18:04, led15 wrote:
Is possible confirm the presence of delta ferrite in steel by xrd.
Yes: http://dx.doi.org/10.1007/s11661-010-0371-7
++
Please do NOT attach files to the whole list alan.he...@neutronoptics.com
Send
On 31/07/2013 20:19, Brian Toby wrote:
To perform R-free with powder data, one must excise multiple complete
peaks from the pattern, say a few sections making up 10-20% of
pattern.
Hi Brian,
It is not so bad, you only need to throw in some peak intensities as
variables (a partial Pawley).
I can't resist adding one more to Mike's excellent list:
5. When peaks overlap strongly it becomes difficult to determine the
background level. Negative Uiso is a consequence of the background
refining to a value which is too low, especially where the peaks are
most dense in the pattern
Just use mask polygon and draw a little triangle inside the pixel you
want to mask. It helps to zoom in first. (Usually it is easier to find
the hot pixels with a threshold mask anyway).
Best,
Jon
Yang, Ling wrote:
Hi,
Does anyone know how to mask single pixel in Fit2d? I found it
According to Caglioti relation, the dimensions of U,V,W are as (angle)^2.
Quick question - does anyone have a trick to stop the Cagliotti formula
going negative? Prodd currently has a habit of bugging out on a
sqrt(negative) and I'm wondering how other folks worked around that, or
if I've
Alan Hewat wrote:
Jon Wright said:
Quick question - does anyone have a trick to stop the Cagliotti formula
going negative?
This can happen if the resolution is relatively flat, so that there is no
well defined minimum.
Seems to be the problem - also rather close to zero anyway
Alan Hewat wrote:
... your name appears as ½¨²¨Áº
The problem is your mail reader, thunderbird displays some chinese
characters. Liang's mail correctly uses a MIME encoded word as the ascii
string:
=?GB2312?B?vaiyqMG6?=
Which means character set GB2312 (chinese), Base64 encoding, and
Olga Smirnova wrote:
Did anyone try to calculate simple mean deviance and compare with
popular R factors?
OS
For simple mean deviance do you mean like in:
http://en.wikipedia.org/wiki/Deviance_(statistics)
Seems we normally call that chi^2. If that's what you meant, then yes,
people do
Dear Olga,
As you've noticed, the Rietveld R-factors tell you how well you fit the
pattern, but don't tell you how well you fit the peaks. There is a
correlated intensities R-factor which follows from the methods outlined in:
J. Appl. Cryst. (2004). 37, 621-628[
Out of curiousity, I'm wondering, do many people use ionic scattering
factors instead atomic ones for Rietveld refinement?
Cheers,
Jon
Lubomir Smrcok wrote:
Just one question : have you asked your supervisor before sending such a
mail ? Though I understand your position it seems that you
You are warmly invited to attend a 3-day Workshop in Grenoble, which
aims at explaining the TotalCryst methods and demonstrating the FABLE
software package.
http://www.esrf.fr/events/conferences/TotalCryst/TotalCryst/
Please bring this to the attention of your colleagues. Registration is
open
Markus Valkeapää wrote:
Any comments on these two different geometries here on Rietveld list?
It depends on the sample? Reflection geometry helps when there is a lot
of absorbtion.
Jon
Try this:
ftp://ftp.ccp4.ac.uk/ccp4/6.0.2/source/chooch-5.0.2-src.tar.gz
Best,
Jon
Jean-Marc Joubert wrote:
Hello,
I am looking for a program able to calculate f' and f'' from absorption
data for a resonnant diffraction experiment. I know that CHOOCH program
was able to do that. This
Hi,
If you have the usual environment variables set :
GSAS=c:\gsas
PATH=...;c:\gsas\exe
PGPLOT_FONT=c:\gsas\pgl\grfont.dat
then it should all run from a dos prompt (run - cmd or command.com). Or
at least, you can type expedt, powpref and genles etc and the
programs run and even deal with
in Bckgrnd
Subtr.zip), I'll send then to you directly.
--- In [EMAIL PROTECTED] mailto:sdpd%40yahoogroups.com, Jon Wright
[EMAIL PROTECTED] wrote:
Hello Yetta,
If you can also add a jpg of the image too, it would show whether there
is a high background in the actual data too. Otherwise try
We have also limited the size of Rietveld list messages to 0.5 Kbytes
0.5 KBytes is only 512 characters? I would h8 2 c text message style
language as a consequence :-)
Best,
Jon
William,
The ELF usually means it is the equivalent of a .exe file? Try:
chmod a+x setup_fullprof_suite ; ./setup_fullprof_suite
Something came up on the list a while ago about a upx issue. You
previously needed something like:
$ sudo apt-get install upx-ucl
$ upx -d fp2k
But perhaps
Alan Hewat wrote:
Many theoretical arguments about signal/noise forget that the
experimentalist has a finite time to collect his data :-)
The finite time to analyse and publish can also be rate limiting! In
this respect a high background is a fine addition to any instrument; it
gives a much
Kurt Leinenweber wrote:
... with wRp of 25% and crystallographic R also near 25% ..
Maybe the background is too low :-?
Jon
Works for me. Just fill out a BANK line with FXY or FXYE as described in
the manual :-)
Cheers,
Jon
[EMAIL PROTECTED] wrote:
Isn't GSAS able to handle XY data??
Cheers
Matthew
Matthew Rowles
CSIRO Minerals
Box 312
Clayton South, Victoria
AUSTRALIA 3169
Ph: +61 3
Yetta Porter wrote:
Hello all, I am interested in finding software that can convert 2D
diffraction rings into 1D diffraction patterns AND allow phase/pattern
matching using the ICDD's PDF database. Currently, I am using Fit2D to
convert my rings to patterns and then Match! to phase match my
Hello Everyone,
Some reviews have just come out in the first 2008 issue of Acta A: 60
years of Acta Crystallographica and the IUCr:
http://journals.iucr.org/a/issues/2008/01/00/issconts.html
Start citing now for a nicely skewed impact factor in a few years time :-)
Happy Christmas,
Jon
Just a quick plug for a program called chooch which does a very nice
job of calculating f' and f from an edge scan, see:
http://www.gwyndafevans.co.uk/chooch.html
For Fe/Cu then neutrons may help.
Cheers,
Jon
[...]
Each edge to be used is recorded, this allow to calculate using
Did anyone look into the effects of using circularly polarised x-rays?
Just wondering...
Jon
Larry Finger wrote:
Franz Werner wrote:
Dear Rietvelders
Is it in principle impossible to determine the absolute structure from powder
data due to reflection overlap or is there a way via multiple
Easiest is to click on the top corner of the plot window and select
options copy to clipboard. Or directly write to gif via:
gnuplot set terminal gif
Terminal type set to 'gif'
Options are 'small size 640,480 '
gnuplot set output test.gif
gnuplot plot sin(x)
gnuplot set terminal win
Terminal
Hi everyone,
Three responses saying it might be a lower spacegroup? I wonder if the
emperors have their clothes on today?
(006) reflections can't split in R-3c as they only have a multiplicity
of 2 in the first place (0,0,6 and 0,0,-6). You were lucky enough to
split (00l) which rules out
Hi Everyone; Just in case you don't follow ccp4bb or nature methods:
http://www.nature.com/nmeth/journal/v4/n3/full/nmeth0307-189.html
I thought that some of you might be interested that the journal Nature
has clarified the publication requirements regarding source code
accessibility. It is
AlanCoelho wrote:
Not sure what to make of all this Jon
Don't shoot the messenger, I was surprised enough by it to forward it to
the list. I guess they imply if you want to keep all implementation
details secret you should be patenting instead of publishing? (Patents
seems to be free
Let's say one gets a value of 0.1% strain.
= width of the distribution of cell parameters in the sample
But on the other hand there are also the unit cell sigmas.
= error bar on the average value of the cell parameters
How can one visualise this?
There is a distribution of cell
Brian H. Toby wrote:
I am trying to convert a GSAS ESD file to a GSAS STD file
BTW, I would be surprised if FullProf does not have a way to input
intensities with uncertainties rather than assuming intensities are
counts.
Indeed it does! INSTRM=10 is x, y, sigma format for fullprof where
I've attached a python script below which will convert a gsas rfl file
into shelx hklf 4 format - it assumes there is no peak overlap at all,
so it is *not* hklf 5 format and *not* suitable for refinement!
After installing python from www.python.org and copying the script into
your working
I did some tests on the profile of the first diffraction peak of LaB6,
where I added a secondary soller angle, since I used secondary
soller slits, and I added also the parameter for the horizontal
divergence in the equitorial plane. Finally I added a crystallite-size
parameter CS_L. I did
Its best to use the terms axial plane and horizontal plane to avoid
confusion.
Alan, I'm confused! What do you mean by those terms? I thought axial
divergence was beam hits different points along the two theta axis -
is that a misconception?
Last point, what do you mean by vertical
Dear Bhuv
pattern and I have corrected possible graininess with spherical
[...]
The data I have collected is on a image plate (only one frame).
Not sure I understand? If you have a 2D image showing powder rings then
you should have some very good ideas about the level of granularity or
texture
Brian Toby wrote:
If the numbers are real values then they are not counts. They may be
counts per second or something else. One needs to have uncertainty
estimates for these intensities before one can do a meaningful
Rietveld refinement (with any code). Following the above procedure, by
Xianqin,
How did you calibrate the sample detector distance? For reliable
absolute cell parameters it is very difficult to get good data with an
area detector. One approach is to mix a standard material into the sample.
As a gross approximation for small angles (in radians):
sin(theta) ~ theta
Alan,
The planned plugin architecture sounds interesting. How concrete are
the plans? I'm interested in auto-generation of restraints for proteins
and fourier mapping at the moment...
Regards,
Jon
alan coelho wrote:
Dear all,
An academic version of BRUKER-AXS TOPAS is now available to
Well, that is an old chestnut that Cooper and Rollet used to oppose to
Rietveld refinement. I think Rollet eventually agreed that Rietveld was
the better method. Has Bill really gone back on that ?
The difference between the two approaches are just an interchange of the
order of summations
Is the fundamental parameter approach better than
mathematical approach used in most of the Rietveld
refinement programs?
Perhaps someone is about to explain the difference is between
fundamental parameters and anything else? I used to think it might
mean convoluting something which was
... to answer to your (too) long questions. May be later, OK?
Going back to this quartics versus ellipsoids peak broadening stuff,
maybe I can summarise:
Why should the distribution of lattice parameters (=strain) in a sample
match the crystallographic symmetry? If the sample has random,
Not violating symmetry restrictions you may either
have the sphere with the terms 11=22=33 and 12=13=23=0
or something else allowing the 12=13=23 terms to be equal
but different from 0. These two possibilities are all you can do
in cubic symmetry with h,k,l permutable. If I am not wrong.
The
Nicolae Popa wrote:
the condition to not violate some elementary principles, in particular,
here, the invariance to symmetry.
Dear Prof Popa,
I had been meaning to implement the quartic form for peak width in a
refinement program for some time, but did not figure out how to generate
the
I am amazed by the flow of miss information that flows on this list whenever an
apparent problem with a space group comes up.
I asked a related question on sci.techniques.xtallography a few weeks
ago, but have yet to hear anything, misinformation or otherwise. If
anyone here can give me some
Ozhan Unverdi wrote:
Could someone give me the magnetic scattering factors of Ru+4 please?
www.google.com searching for Ru4+ magnetic form factor gives 17 results.
One of them is Sidis et al, Evidence for Incommensurate Spin
Fluctuations in Sr2RuO4, Phys. Rev. Lett (1999) 83, 3320.
In
Paolo,
On Fri, 15 Sep 2000, Radaelli, PG (Paolo) wrote:
.
Finally, here is a question for Bob and Juan. To me, it would be much more
natural to remove Vo from the scale factor, that is to redefine a new S' so
that
Y=S'*L*A*E*|F|^2/Vo^2 and S'=K*Ltot*f
This way, the scale factor
Alex,
There's something below which might help you. You'd need to set up a
refinement with a .exp file and a .raw file with the same root name (eg
fit.raw and fit.exp). The batch file then takes two arguments, the data
file name (eg run1.raw) and the root of name of the .exp file (eg. fit for
low angle
asymmetry correction) would be also be appreciated.
Thanks in advance,
Jon Wright
Dept. of Chemistry, Lensfield Road, Cambridge, CB2 1EW
Phone-Office 01223 (3)36396; Lab 01223 (3)36305; Home 01223 462024
Asymmetry is discussed in:
J.Appl.Cryst (1984) 17, p.47 - van Laar Yelon (+ ref's therein)
The above method is implemented in:
J.Appl.Cryst (1994) 27, p.892 - Finger, Cox Jephcoat.
and source code for this peakshape is available. (They also talk about
secondary monochromators).
Hope
on is only a problem
when the peaks disappear.
Hope this helps,
Jon Wright
PS: Can anyone tell me if sigma_abs goes as 1/v for Gd?
Dept. of Chemistry, Lensfield Road, Cambridge, CB2 1EW
Phone-Office 0122
On Fri, 7 Jan 2000, Armel Le Bail wrote:
15mn for checking a crystallography set is about my
performance too.
Just out of interest, how long does it take people to pick up the
error in entry number 17280, attached below. It's just a cell
transformation from the cubic spinel [a-(a+b)/2,
matrix rather than the real
space unit cell parameters? I haven't picked up yet on why the derivatives
cannot be converted from w.r.t A* etc to w.r.t a etc. Is it just a time
saving?
Thanks
Jon Wright
Dept
... not at all for magnetism, ...
Ahem, magnetism - resolution is very useful, in certain (rare) cases. I
guess that magnetic structures are not Armel's primary interest
but in at least one case resolution was essential. (FeAsO4 from IRIS (TOF
neutron) dataset, J.Phys:Condens.Matter 11 (1999)
On Thu, 23 Sep 1999, Ed Cussen wrote:
We're forced to use CCSL for the superior peak shape description and
so simply changing refinement program is not an option. I'm sure
that this problem must have been encountered before and I'm suprised that
there's not a 'standard' solution to it.
On Thu, 16 Sep 1999, Dr.Joerg Bergmann wrote:
(high systematic error, bad difference plot, but low e.s.d.'s)
(low systematic error, good difference plot, but high e.s.d.'s).
Apologies for diving off onto the general case, but does this make sense?
You improve your model and the quality of
, sometimes it's the
quickest way to learn.
Jon Wright
PS: Sorry to pick at your comments Paolo, it's a shame I'm not at RAL at
the moment. Could have discussed it out over a coffee...
in the x-ray model :) Maybe not if one looks on the x-ray refinement as
fitting of the electron density function, rather than the nuclear
positions. For bonding studies it is the differences which are of
interest!
Jon Wright.
PS: Any offers other than GSAS and multipattern fullprof for actually
ta
version. It appears you can assign the statistical weight to each pattern,
and in the example x-rays and neutrons are weighted equally. I'm wondering
what the best choice is. Each observation comes with a statistical weight
from the experiment? Isn't it a sin to alter that?
ld try MI/X. The URL to download MI/X from MicroImages' is
http://www.microimages.com/ in the "Free Downloads" section.
Hope this helps,
Jon Wright
On Tue, 30 Mar 1999, Hongwu Xu wrote:
Hi, Everyone,
We have some neutron diffraction data collected and stored in the VAX
co
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