U.S. patent application number 16/112347 was filed with the patent office on 2018-12-20 for metal-doped cu(in,ga)(s,se)2 nanoparticles.
The applicant listed for this patent is Nanoco Technologies, Ltd.. Invention is credited to Ombretta Masala, Christopher Newman, Chet Steinhagen.
Application Number | 20180366599 16/112347 |
Document ID | / |
Family ID | 52450515 |
Filed Date | 2018-12-20 |
United States Patent
Application |
20180366599 |
Kind Code |
A1 |
Newman; Christopher ; et
al. |
December 20, 2018 |
Metal-doped Cu(In,Ga)(S,Se)2 Nanoparticles
Abstract
Various methods are used to provide a desired doping metal
concentration in a CIGS-containing ink when the CIGS layer is
deposited on a photovoltaic device. When the doping metal is
antimony, it may be incorporated by: adding an antimony salt
together with copper-, indium- and/or gallium-containing reagents
at the beginning of the synthesis reaction of Cu(In,Ga)(S,Se).sub.2
nanoparticles; synthesizing Cu(In,Ga)(S,Se).sub.2 nanoparticles and
adding an antimony salt to the reaction solution followed by mild
heating before isolating the nanoparticles to aid antimony
diffusion; and/or, using a ligand that is capable of capping the
Cu(In,Ga)(S,Se).sub.2 nanoparticles with one end of its molecular
chain and binding to antimony atoms with the other end of its
chain.
Inventors: |
Newman; Christopher;
(Holmfirth, GB) ; Masala; Ombretta; (Manchester,
GB) ; Steinhagen; Chet; (St. Paul, MN) |
|
Applicant: |
Name |
City |
State |
Country |
Type |
Nanoco Technologies, Ltd. |
Manchester |
|
GB |
|
|
Family ID: |
52450515 |
Appl. No.: |
16/112347 |
Filed: |
August 24, 2018 |
Related U.S. Patent Documents
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Application
Number |
Filing Date |
Patent Number |
|
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14607882 |
Jan 28, 2015 |
|
|
|
16112347 |
|
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61933616 |
Jan 30, 2014 |
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Current U.S.
Class: |
1/1 |
Current CPC
Class: |
Y02E 10/541 20130101;
H01L 21/02579 20130101; H01L 31/0323 20130101; H01L 21/02601
20130101; H01L 31/0322 20130101; H01L 21/02568 20130101; H01L
21/02628 20130101 |
International
Class: |
H01L 31/032 20060101
H01L031/032; H01L 21/02 20060101 H01L021/02 |
Claims
1. A process for preparing metal-doped nanocrystals comprising:
adding an antimony salt to a mixture of copper-, indium-, and
gallium-containing reagents at the beginning of a synthesis
reaction of Cu(In,Ga)(S,Se).sub.2 nanoparticles.
2. The process of claim 1, wherein the antimony salt is an antimony
halide.
3. The process of claim 2, wherein the antimony halide is antimony
chloride.
4. The process of claim 2, wherein the antimony halide is antimony
fluoride.
5. The process of claim 2, wherein the antimony halide is antimony
iodide.
6. The process of claim 2, wherein the antimony halide is antimony
bromide.
7. The process of claim 1, wherein the antimony salt is an organic
antimony salt.
8. The process of claim 7, wherein the organic antimony salt is
antimony acetate.
9. The process of claim 7, wherein the organic antimony salt is
triphenylantimony.
10. The process of claim 7, wherein the organic antimony salt is
tris(dimethylamino)antimony.
11. The process of claim 7, wherein the organic antimony salt is an
antimony dialkyldithiocarbamate.
12. The process of claim 11, wherein the antimony
dialkyldithiocarbamate is antimony diethyldithiocarbamate.
13. The process of claim 11, wherein the antimony
dialkyldithiocarbamate is antimony dimethyldithiocarbamate.
14. The process of claim 11, wherein the antimony
dialkyldithiocarbamate is antimony methylhexyldithiocarbamate.
15. The process of claim 11, wherein the antimony
dialkyldithiocarbamate is antimony ethylhexyldithiocarbamate.
16. A photovoltaic device comprising a layer of metal-doped
nanocrystals prepared by the process of claim 1.
17. An ink composition, the ink composition comprising: a solvent;
and metal-doped nanocrystals dispersed in the solvent, wherein the
metal-doped nanocrystals are prepared by a process according to
claim 1.
18. A method of producing a film, the method comprising: printing
an ink according to claim 17 on a substrate; and sintering the
printed ink to coalesce the metal-doped nanocrystals and form a
film on the substrate.
Description
CROSS-REFERENCE TO RELATED APPLICATIONS
[0001] This application is a divisional of U.S. Non-Provisional
application Ser. No. 14/607,882, filed on Jan. 28, 2015, which
claims the benefit of U.S. Provisional Application No. 61/933,616,
filed on Jan. 30, 2014, the contents of which are incorporated by
reference herein in their entirety.
BACKGROUND OF THE INVENTION
1. Field of the Invention
[0002] The present invention generally relates to photovoltaic
devices. More particularly, it relates to copper indium gallium
diselenide/disulfide-based, thin film, photovoltaic devices.
2. Description of the Related Art Including Information Disclosed
Under 37 CFR 1.97 and 1.98
[0003] Semiconductor materials like copper indium gallium
diselenides and sulfides (Cu(In,Ga)(S,Se).sub.2, herein referred to
as "CIGS") are strong light absorbers and have band gaps that match
well with the optimal spectral range for photovoltaic (PV)
applications. Furthermore, because these materials have strong
absorption coefficients, the active layer in the solar cell is
required to be only a few microns thick.
[0004] Copper indium diselenide (CuInSe.sub.2) is one of the most
promising candidates for thin film PV applications due to its
unique structural and electrical properties. Its band gap of 1.0 eV
is well-matched with the solar spectrum. CuInSe.sub.2 solar cells
can be made by selenization of CuInS.sub.2 films because, during
the selenization process, Se replaces S and the substitution
creates volume expansion, which reduces void space and reproducibly
leads to a high quality, dense CuInSe.sub.2 absorber layers. [Q.
Guo, G. M. Ford, H. W. Hillhouse and R. Agrawal, Nano Lett., 2009,
9, 3060] Assuming complete replacement of S with Se, the resulting
lattice volume expansion is .about.14.6%, which is calculated based
on the lattice parameters of chalcopyrite (tetragonal) CuInS.sub.2
(a=5.52 .ANG., c=11.12 .ANG.) and CuInSe.sub.2 (a=5.78 .ANG.,
c=11.62 .ANG.). This means that the CuInS.sub.2 nanocrystal film
can be easily converted to a predominantly selenide material, by
annealing the film in a selenium-rich atmosphere. Therefore,
CuInS.sub.2 is a promising alternative precursor for producing
CuInSe.sub.2 or CuIn(S,Se).sub.2 absorber layers.
[0005] The theoretical optimum band gap for absorber materials is
in the region of 1.2-1.4 eV. By incorporating gallium into
CuIn(S,Se).sub.2 thin films, the band gap can be manipulated such
that, following selenization, a
Cu.sub.xIn.sub.yGa.sub.zS.sub.aSe.sub.b absorber layer is formed
with an optimal band gap for solar absorption.
[0006] Conventionally, costly vapor phase or evaporation techniques
(for example metalorganic chemical vapor deposition (MO-CVD), radio
frequency (RF) sputtering, and flash evaporation) have been used to
deposit the CIGS films on a substrate. While these techniques
deliver high quality films, they are difficult and expensive to
scale to larger-area deposition and higher process throughput.
Thus, solution processing of CIGS materials has been explored. One
such approach involves depositing CIGS nanoparticles, which can be
thermally processed to form a crystalline CIGS layer.
[0007] One of the major advantages of using nanoparticles of CIGS
is that they can be dispersed in a medium to form an ink that can
be printed on a substrate in a similar way to inks in a
newspaper-like process. The nanoparticle ink or paste can be
deposited using low-cost printing techniques such as spin coating,
slit coating and doctor blading. Printable solar cells could
replace the standard conventional vacuum-deposited methods of solar
cell manufacture because the printing processes, especially when
implemented in a roll-to-roll processing framework, enables a much
higher throughput.
[0008] The synthetic methods developed so far offer limited control
over the particle morphology, and particle solubility is usually
poor which makes ink formulation difficult.
[0009] The challenge is to produce nanoparticles that overall are
small, have low melting point, narrow size distribution and
incorporate a volatile capping agent, so that they can be dispersed
in a medium and the capping agent can be eliminated easily during
the film baking process. Another challenge is to avoid the
inclusion of impurities, either from synthetic precursors or
organic ligands that could compromise the overall efficiency of the
final device.
[0010] U.S. Publication No. 2009/0139574 [Preparation of
Nanoparticle Material, published 4 Jun. 2009], the entire contents
of which are incorporated herein by reference, describes the
synthesis of colloidal CIGS nanoparticles with a monodisperse size
distribution, capped with organic ligands that enable solution
processing and can be removed at relatively low temperatures during
thermal processing.
[0011] One of the challenges associated with the nanoparticle-based
CIGS deposition approach is to achieve large grains after thermal
processing. Grain sizes on the order of the film thickness are
desirable since grain boundaries act as electron-hole recombination
centres. Elemental dopants, such as sodium [R. Kimura, T. Mouri, N.
Takuhai, T. Nakada, S. Niki, A. Yamada, P. Fons, T. Matsuzawa, K.
Takahashi and A. Kunioka, Jpn. J. Appl. Phys., 1999, 38, L899] and
antimony, [M. Yuan, D. B. Mitzi, W. Liu, A. J. Kellock, S. J. Chey
and V. R. Deline, Chem. Mater., 2010, 22, 285] have been reported
to enhance the grain size of CIGS films and thus the power
conversion efficiency (PCE) of the resulting devices.
[0012] The incorporation of sodium into CIGS is a well-known method
for increasing maximum photovoltaic cell efficiencies. The effect
of sodium is thought to be an increase in the net carrier
concentration and film conductivity, and possibly enhancement of
grain growth. Sodium is typically added in concentrations ranging
between 0.1-1.0% by weight.
[0013] A common method used to incorporate sodium is by diffusion
from soda-lime glass (SLG) substrates through a molybdenum back
contact layer into an adjacent CIGS layer. The processes limiting
or enabling sodium diffusion from the SLG during crystal growth are
currently not well understood. One drawback of this method is that
the diffusion of sodium is not easily controlled.
[0014] Other known incorporation methods include diffusion from a
thin sodium-containing precursor layer that is deposited either
below or above the CIGS absorber layer, co-evaporation of a sodium
compound during the growth of CIGS or soaking the CIGS films into a
sodium salt solution. For example, Guo et al. incorporated sodium
into films prepared from CIGS nanoparticles by soaking the films in
1 M aqueous sodium chloride solution, prior to selenization. [Q.
Guo, G. M. Ford, R. Agrawal and H. Hillhouse, Prog. Photovolt. Res.
Appl., 2013, 21, 64]
[0015] These methods require either sodium-free substrates or
alkali-diffusion barriers (such as Al.sub.2O.sub.3 or very dense
molybdenum). Otherwise, too much sodium may be incorporated into
the CIGS if SLG substrates are used.
[0016] Examples of sodium compounds typically used in the methods
mentioned above include sodium fluoride (NaF), sodium selenide
(Na.sub.2Se), and sodium sulfide (Na.sub.2S).
[0017] These incorporation methods involve a multi-step process
where the sodium-containing compound is produced at a separate
stage, before or after the growth absorber layer. This is achieved
by using expensive vacuum deposition techniques and cannot be
applied to printable photovoltaic devices produced by printing a
CIGS ink on flexible substrates on a roll-to-roll process.
[0018] Soaking in a sodium salt solution is a simple method but it
is not clear how well the incorporation of sodium may be tuned
using this process.
[0019] In the prior art, where CIGS films have been prepared by the
sputtering of Cu--In--Ga precursors followed by selenization,
sodium doping may result in phase segregation of CuInSe.sub.2 and
CuGaSe.sub.2, despite promoting grain growth within the
CuInSe.sub.2 layer. [F. Hergert, S. Jost, R. Hock, M. Purwins and
J. Palm, Thin Solid Films, 2007, 515, 5843] Thus, a
nanoparticle-based approach, where the quaternary CIGS phase is
inherent within the nanoparticles, may enable sodium-enhanced grain
growth without phase segregation.
[0020] A method to dope Cu.sub.2ZnSnS.sub.4 (CZTS) nanoparticles
with sodium has previously been described by Zhou et al. [H. Zhou,
T.-B. Song, W.-C. Hsu, S. Luo, S. Ye, H.-S. Duan, C. J. Hsu, W.
Yang and Y. Yang, J. Am. Chem. Soc., 2013, 135, 15998] The
sodium-doped CZTS nanoparticles were prepared by a "hot-injection"
method, whereby a sulfur precursor was injected into a solution of
copper, zinc and tin precursor salts dissolved in oleylamine at
elevated temperature. Following a period of annealing, a solution
of sodium trifluoroacetate (CF.sub.3COONa) in oleic acid was
injected into the CZTS nanoparticle solution, then annealed for a
further time period. The ratio of Na/(Cu+Zn+Sn) was tunable from
0.5-10%, and characterization suggested that the sodium was
distributed on the nanoparticle surface, rather than homogeneously
throughout the nanoparticles. To date, adaptation of the method for
the preparation of sodium-doped CIGS nanoparticles has not been
reported.
[0021] Mitzi and co-workers have explored the incorporation of
antimony into CIGS devices formed using a hydrazine solution-based
deposition approach. Significant grain growth was observed using
Sb.sub.2S.sub.3/S in hydrazine, with an improvement in PCE from
10.3% for undoped films to 12.3% for films doped with 0.2 mol. %
Sb. [M. Yuan, D. B. Mitzi, W. Liu, A. J. Kellock, S. J. Chey and V.
R. Deline, Chem. Mater., 2010, 22, 285] At 1.2 mol. %, grain growth
could be observed for films annealed at low temperatures
(<400.degree. C.). [M. Yuan, D. B. Mitzi, O. Gunawan, A. J.
Kellock, S. J. Chey and V. R. Deline, Thin Solid Films, 2010, 519,
852] Despite the improvements in grain size and PCE with antimony
doping, the deposition approach carries significant risk owing to
the toxic and unstable nature of hydrazine. In addition, the
precautions required to safely handle hydrazine pose a significant
challenge when scaling the method.
[0022] Carrate et al. described ligand exchange process to displace
organic ligands on the surface of CZTS nanoparticles, substituting
them with an antimony salt (SbCl.sub.3), via a biphase system. [A.
Carrate, A. Shavel, X. Fontane, J. Montserrat, J. Fan, M. Ibanez,
E. Saucedo, A. Perez-Rodriguez and A. Cabot, J. Am. Chem. Soc.,
2013, 135, 15982] The CZTS-SbCl.sub.3 nanoparticles were stable in
solution for sufficient time to allow spray deposition.
[0023] Though the nanoparticles fabricated by Carrate et al. could
be deposited by spray-coating, the lack of organic ligands on the
nanoparticle surface may render the material difficult to process
using other coating techniques, for which organic components of the
ink formulation are critical to its coating properties.
[0024] The preparation of antimony-coated CIGS nanoparticles has
not yet been reported in the prior art.
[0025] Grain growth in CuInSe.sub.2 thin films has also been
reported upon doping of the CuInSe.sub.2 flux with 2 wt. % cadmium
or bismuth, followed by localised, pulsed annealing using an
electron beam. [R. J. Gupta, D. Bhattacharya and O. N. Sullivan, J.
Cryst. Growth, 1988, 87, 151] Grain sizes of up to 10 .mu.m were
observed by transition electron microscopy (TEM). However, pulsed
annealing may not be an easy process to scale. Additionally, doping
with toxic cadmium may be unfavourable.
[0026] Thus, a method to form doped CIGS films using a
nanoparticle-based deposition approach would be beneficial.
BRIEF SUMMARY
[0027] The method described herein incorporates metal dopants
directly during the growth of the CIGS nanoparticles without the
need of a multi-step process or expensive vacuum techniques.
[0028] The metal-doped nanoparticles may be dispersed into a
solvent to form an ink that is printed and sintered to form thin
films by melting or fusing the nanoparticle precursor material such
that the nanoparticles coalesce to form large-grained, thin films.
FIG. 1 is a flow diagram summarizing a preparative procedure for
forming a CIGS film from CIGS nanoparticles and subsequently
fabricating a PV device.
[0029] The method provides a desired doping metal concentration in
a CIGS-containing ink when the CIGS layer is deposited on a
photovoltaic device.
[0030] When the doping metal is sodium, it may be incorporated by:
[0031] adding a sodium salt, for example sodium acetate, together
with the copper-, indium- and/or gallium-containing reagents at the
beginning of the synthesis reaction of Cu(In,Ga)(S,Se).sub.2
nanoparticles; [0032] synthesizing Cu(In,Ga)(S,Se).sub.2
nanoparticles and adding a sodium salt to the reaction solution
followed by mild heating before isolating the nanoparticles to aid
sodium diffusion; and/or, [0033] using a ligand that is capable of
capping the Cu(In,Ga)(S,Se).sub.2 nanoparticles with one end of its
molecular chain and binding to sodium atoms with the other end of
its chain.
[0034] When the doping metal is antimony, it may be incorporated
by: [0035] adding an antimony salt, for example antimony acetate,
together with the copper-, indium- and/or gallium-containing
reagents at the beginning of the synthesis reaction of
Cu(In,Ga)(S,Se).sub.2 nanoparticles; [0036] synthesizing
Cu(In,Ga)(S,Se).sub.2 nanoparticles and adding an antimony salt to
the reaction solution followed by mild heating before isolating the
nanoparticles to aid antimony diffusion; and/or, [0037] using a
ligand that is capable of capping the Cu(In,Ga)(S,Se).sub.2
nanoparticles with one end of its molecular chain and binding to
antimony atoms with the other end of its chain.
BRIEF DESCRIPTION OF THE SEVERAL VIEWS OF THE DRAWING(S)
[0038] FIG. 1 is a flowchart depicting a method for formulating a
CIGS nanoparticle-based ink that can be processed to form a thin
film and then fabricate a photovoltaic device incorporating such a
film.
[0039] FIG. 2 is a schematic depiction of a process for
incorporating metals into CIGS nanoparticles.
[0040] FIG. 3 is a schematic depiction of a ligand-capped
nanoparticle according to the invention.
DETAILED DESCRIPTION
[0041] The present disclosure involves a method to controllably
incorporate metals, such as sodium and/or antimony, into CIGS
nanoparticles. The metal-doped CIGS nanoparticles may be deposited
with different printing methods to form films of suitable
thickness.
[0042] The following are different methods that incorporate sodium
(by way of example) into CIGS nanoparticles:
[0043] In a first embodiment, a sodium salt, for example sodium
acetate, is added together with the copper-, indium- and/or
gallium-containing reagents at the beginning of the synthesis
reaction of Cu(In,Ga)(S,Se).sub.2 nanoparticles (e.g., that
disclosed in U.S. Pub. No. 2009/0139574). Suitable sodium salts
other than sodium acetate include, but are not limited to,
inorganic salts such as sodium chloride, sodium fluoride, sodium
bromide and other organic salts such as sodium oleate and sodium
alkyldithiocarbamate salts such as sodium diethyldithiocarbamate,
sodium dimethyldithiocarbamate, sodium methylhexyldithiocarbamate
and sodium ethylhexyldithiocarbamate.
[0044] In a second embodiment, the Cu(In,Ga)(S,Se).sub.2
nanoparticles are synthesized and a sodium salt is subsequently
added to the reaction solution, followed by mild heating, before
isolating the nanoparticles to aid sodium diffusion. This method
permits the incorporation of sodium without the need for having
sodium salts present throughout the synthesis of the CIGS
nanoparticles. This method is particularly useful when the sodium
salt may interfere at some stage during the synthesis. This method
may also be performed as a separate step after the isolation of the
nanoparticles, as illustrated in FIG. 2 wherein "TOP" is
trioctylphosphine and "NC" is nanocrystal. In some embodiments, the
sodium salt is incorporated at room temperature. In alternative
embodiments, the sodium salt is added to a dispersion of the CIGS
nanoparticles, followed by heating, for example at 200.degree.
C.
[0045] In a third embodiment, a sodium-containing ligand is used
that is capable of capping the Cu(In,Ga)(S,Se).sub.2 nanoparticles
with one end of its molecular chain and binding to sodium atoms
with the other end of the chain. An example of this type of ligand
is a thiol ligand with a carboxylate group at the other end capable
of binding sodium as illustrated in FIG. 3.
[0046] This method may be extended to the doping of CIGS
nanoparticles with other metals, for example antimony (Sb).
Suitable antimony salts include, but are not restricted to,
antimony acetate, triphenylantimony and
tris(dimethylamino)antimony, antimony halides such as antimony
chloride, antimony fluoride, antimony bromide and antimony iodide,
and antimony dialkyldithiocarbamates such as antimony
diethyldithiocarbamate, antimony dimethyldithiocarbamate, antimony
methylhexyldithiocarbamate and antimony
ethylhexyldithiocarbamate.
[0047] The method allows the incorporation of a metal directly in
the nanoparticle precursor without the use of vacuum
techniques.
[0048] The methods described above allow the incorporation of a
metal while the nanoparticle precursor is being synthesized thereby
removing the need for an additional step to include the metal.
Because the synthetic method enables control of the amount of metal
introduced, levels of incorporated metal may be accurately tuned.
The metal distribution is likely preserved during the sintering
process to produce metal-doped CIGS films.
[0049] A process for producing nanoparticles incorporating ions
selected from groups 13 [Al, Ga, In], 16 [S, Se, Te], and 11 [Ce,
Ag, Au] or 12 [Zn, Cd] of the periodic table is disclosed in U.S.
Publication No. 2009/0139574 by Nigel Pickett and James Harris the
disclosure of which is hereby incorporated by reference in its
entirety. In one embodiment, the disclosed process includes
effecting conversion of a nanoparticle precursor composition
comprising group 13, 16, and 11 or 12 ions to the material of the
nanoparticles in the presence of a selenol compound. Other
embodiments include a process for fabricating a thin film including
nanoparticles incorporating ions selected from groups 13, 16, and
11 or 12 of the periodic table as well as a process for producing a
printable ink formulation including the nanoparticles.
[0050] Although particular embodiments have been shown and
described, they are not intended to limit what this patent covers.
One skilled in the art will understand that various changes and
modifications may be made.
[0051] Various embodiments are illustrated by the following
examples.
Example 1: Preparation of Sodium-Doped CuInS.sub.2 Nanoparticles
Using Sodium Diethyldithiocarbamate
[0052] An oven-dried 250 mL round-bottom flask was charged with
copper(I) acetate (2.928 g, 23.88 mmol), indium(III) acetate (9.706
g, 33.25 mmol) and benzyl ether (50 mL). The flask was fitted with
a Liebig condenser and collector, and the mixture was degassed at
100.degree. C. for 1 hour. The flask was then back-filled with
nitrogen. Degassed 1-octanethiol (40 mL, 230 mmol) was added to the
mixture, which was subsequently heated to 200.degree. C. for 2
hours. A suspension of sodium diethyldithiocarbamate trihydrate
(1.390 g, 6.169 mmol) in benzyl ether (18 mL)/oleylamine (2 mL) was
added and the residue was rinsed with a small amount of methanol.
The temperature was maintained at 200.degree. C. for a further 30
minutes, before being allowed to cool to 160.degree. C. and
stirring for .about.18 hours. The mixture was then cooled to room
temperature.
[0053] The nanoparticles were isolated in aerobic conditions, via
centrifugation, using isopropanol, toluene, methanol and
dichloromethane, then dried under vacuum.
[0054] Characterization by inductively coupled plasma organic
emission spectroscopy (ICP-OES) gave the following elemental
composition by mass: 13.04% Cu; 30.70% In; 0.628% Na; 20.48% S.
This equates to a stoichiometry of
CuIn.sub.1.30Na.sub.0.13S.sub.3.11, i.e. 13% sodium compared to the
number of moles of copper. The organo-thiol ligand contributes to
the total sulfur content.
Example 2: Preparation of Sodium-Doped CuInS.sub.2 Nanoparticles
Using Sodium Oleate
[0055] An oven-dried 250 mL round-bottom flask was charged with
copper(I) acetate (2.929 g, 23.89 mmol), indium(III) acetate (9.707
g, 33.25 mmol) and benzyl ether (50 mL). The flask was fitted with
a Liebig condenser and collector, and the mixture was degassed at
100.degree. C. for 1 hour. The flask was then back-filled with
nitrogen. Degassed 1-octanethiol (40 mL, 230 mmol) was added to the
mixture, which was subsequently heated to 200.degree. C. for 2
hours. A suspension of sodium oleate (1.879 g, 6.172 mmol) in
benzyl ether (20 mL) was added and the residue was rinsed with a
small amount of methanol. The temperature was maintained at
200.degree. C. for a further 30 minutes, before being allowed to
cool to 160.degree. C. and stirring for .about.18 hours. The
mixture was then cooled to room temperature.
[0056] The nanoparticles were isolated in aerobic conditions, via
centrifugation, using isopropanol, toluene, methanol and
dichloromethane, then dried under vacuum.
[0057] Characterization by inductively coupled plasma organic
emission spectroscopy (ICP-OES) gave the following elemental
composition by mass: 13.04% Cu; 28.31% In; 0.784% Na; 19.86% S.
This equates to a stoichiometry of
CuIn.sub.1.20Na.sub.0.17S.sub.3.02, i.e. 17% sodium compared to the
number of moles of copper. The organo-thiol ligand contributes to
the total sulfur content.
Example 3: Preparation of Sodium-Doped CuInS.sub.2 Nanoparticles
Using Sodium Oleate
[0058] An oven-dried 250 mL round-bottom flask was charged with
copper(I) acetate (2.928 g, 23.88 mmol), indium(III) acetate (9.705
g, 33.24 mmol), sodium oleate (0.743 g, 2.44 mmol) and benzyl ether
(50 mL). The flask was fitted with a Liebig condenser and
collector, and the mixture was degassed at 100.degree. C. for 1
hour. The flask was then back-filled with nitrogen. Degassed
1-octanethiol (40 mL, 230 mmol) was added to the mixture, which was
subsequently heated to 200.degree. C. for 2 hours, before being
allowed to cool to 160.degree. C. and annealing for .about.18
hours. The mixture was then cooled to room temperature.
[0059] The nanoparticles were isolated in aerobic conditions, via
centrifugation, using isopropanol, toluene, methanol,
dichloromethane and acetone, then dried under vacuum.
[0060] Characterization by inductively coupled plasma organic
emission spectroscopy (ICP-OES) gave the following elemental
composition by mass: 13.43% Cu; 28.56% In; 0.96% Na; 20.19% S. This
equates to a stoichiometry of CuIn.sub.1.18Na.sub.0.20S.sub.2.98,
i.e. 20% sodium compared to the number of moles of copper. The
organo-thiol ligand contributes to the total sulfur content.
Example 4: Preparation of Antimony-Doped Cu(In,Ga)S.sub.2
Nanoparticles Using Triphenylantimony
[0061] A 100 mL round-bottom flask was charged with copper(I)
acetate (0.369 g, 3.01 mmol), indium(III) acetate (0.7711 g, 2.641
mmol), gallium(III) acetylacetonate (0.4356 g, 1.187 mmol),
triphenylantimony (0.055 g, 160 .mu.mol), benzyl ether (6 mL) and a
1 M solution of sulfur in oleylamine (9 mL, 9 mmol). The mixture
was degassed at 100.degree. C. for 1 hour, then the flask was
back-filled with nitrogen. 1-Octanethiol (4.8 mL, 28 mmol) was
injected into the flask, which was subsequently heated to
200.degree. C. and held for 2 hours. The temperature was decreased
to 160.degree. C. and held overnight. The mixture was then cooled
to room temperature.
[0062] The nanoparticles were isolated in aerobic conditions, via
centrifugation, using toluene and methanol.
[0063] Characterization by inductively coupled plasma organic
emission spectroscopy (ICP-OES) gave the following elemental
composition by mass: 15.47% Cu; 26.09% In; 6.41% Ga; 0.25% Sb;
20.67% S. This equates to a stoichiometry of
CuIn.sub.0.93Ga.sub.0.38Sb.sub.0.01S.sub.2.65, i.e. 1% antimony
compared to the number of moles of copper. The organo-thiol ligand
contributes to the total sulfur content.
Example 5: Preparation of Antimony-Doped Cu(In,Ga)S.sub.2
Nanoparticles Using Antimony Acetate
[0064] A 100 mL round-bottom flask was charged with copper(I)
acetate (0.369 g, 3.01 mmol), indium(III) acetate (0.7711 g, 2.641
mmol), gallium(III) acetylacetonate (0.4356 g, 1.187 mmol),
antimony(III) acetate (0.047 g, 160 .mu.mol), benzyl ether (6 mL)
and a 1 M solution of sulfur in oleylamine (9 mL, 9 mmol). The
mixture was degassed at 100.degree. C. for 1 hour, then the flask
was back-filled with nitrogen. 1-Octanethiol (4.8 mL, 28 mmol) was
injected into the flask, which was subsequently heated to
200.degree. C. and held for 2 hours. The temperature was decreased
to 160.degree. C. and held overnight. The mixture was then cooled
to room temperature.
[0065] The nanoparticles were isolated in aerobic conditions, via
centrifugation, using toluene and methanol.
[0066] Characterization by inductively coupled plasma organic
emission spectroscopy (ICP-OES) gave the following elemental
composition by mass: 15.39% Cu; 26.02% In; 6.17% Ga; 0.92% Sb;
21.20% S. This equates to a stoichiometry of
CuIn.sub.0.94Ga.sub.0.37Sb.sub.0.03S.sub.2.73, i.e. 3% antimony
compared to the number of moles of copper. The organo-thiol ligand
contributes to the total sulfur content.
[0067] Although particular embodiments of the present invention
have been shown and described, they are not intended to limit what
this patent covers. One skilled in the art will understand that
various changes and modifications may be made without departing
from the scope of the present invention as literally and
equivalently covered by the following claims.
* * * * *