Cu.SUB.2.XSnY.SUB.4 .nanoparticles

Abstract

Materials and methods for preparing Cu.sub.2XSnY.sub.4 nanoparticles, wherein X is Zn, Cd, Hg, Ni, Co, Mn or Fe and Y is S or Se, (CXTY) are disclosed herein. The nanoparticles can be used to make layers for use in thin film photovoltaic (PV) cells. The CXTY materials are prepared by a colloidal synthesis in the presence of labile organo-chalcogens. The organo-chalcogens serves as both a chalcogen source for the nanoparticles and as a capping ligand for the nanoparticles.

Claims

1. A method for preparing an absorber layer for a photovoltaic (PV) device, the method comprising: dissolving or dispersing a population of nanoparticles in a solvent to form a nanoparticle ink, each nanoparticle comprising: a semiconductor nanocrystal having an outer surface, the semiconductor nanocrystal having the formula Cu.sub.2XSnY.sub.4, where X is Cd, Hg, Ni, Co, Mn, or Fe and Y is S or Se; and a surface coating on the outer surface of the semiconductor nanocrystal and consisting of labile organo-chalcogen ligands; depositing the nanoparticle ink on a substrate to form a nanoparticle film; annealing the substrate and nanoparticle film at a first temperature for a first time interval; and annealing the substrate and nanoparticle film at a second temperature for a second time interval, wherein the second temperature is higher than the first temperature.

2. The method of claim 1, wherein the solvent is a non-polar solvent.

3. The method of claim 1, wherein the nanoparticle ink is deposited on the substrate by any one of spin-coating, slit-coating, drop-casting, doctor blading, and inkjet printing.

4. The method of claim 1, wherein the first temperature is between 260 and 350 C.

5. The method of claim 1, wherein the first time interval is between 3 and 10 minutes.

6. The method of claim 1, wherein the second temperature is between 350 and 440 C.

7. The method of claim 1, wherein the second time interval is between 3 and 10 minutes.

8. The method of claim 1, further comprising annealing at a third temperature for a third time interval, wherein the third temperature is higher than the second temperature.

9. The method of claim 8, wherein the third temperature is between 500 and 600 C.

10. The method of claim 8, wherein the third time interval is between 30 minutes and 3 hours.

11. The method of claim 8, wherein annealing at the third temperature for the third time interval is conducted under a chalcogen-rich atmosphere.

12. The method of claim 1, wherein the population of nanoparticles further comprises copper selenide.

Description

BRIEF DESCRIPTION OF THE FIGURES

(1) FIG. 1 is a flow chart summarising the process for preparing CXTY nanoparticles according to the method described herein.

(2) FIG. 2 is a flow chart summarising the process for preparing a PV device from CXTY nanoparticles according to the method described herein.

(3) FIG. 3 shows the X-ray diffraction (XRD) pattern for CZTSe nanoparticles prepared according to Example 1.1, which matches well with the CZTSe stannite and Cu2Se3 umangite phases. Wurtzite ZnSe [K. Yvon et al., J. Appl. Cryst., 1977, 10, 73], a common impurity in CZTSe materials is included for reference, but does not appear to exist in this material.

(4) FIG. 4 shows thermogravimetric analysis (TGA) of CZTSe nanoparticles capped with 1-octane selenol, prepared according to Example 1.1, showing an inorganic content of 65%.

(5) FIG. 5 shows the XRD pattern of CZTSe nanoparticles synthesised with 1-dodecane selenol, as described in Example 1.2. The peak positions match well with the wurtzite crystal structure of ZnSe. [K. Yvon et al., J. Appl. Cryst., 1977, 10, 73] Differences in the relative peak intensities and slight shifting of the peak positions may be attributable to the partial substitution of Zn with Cu and Sn.

(6) FIG. 6 is a TGA plot of CZTSe nanoparticles capped with 1-dodecane selenol, as prepared in Example 1.2, showing removal of the ligand between approximately 200-320 C.

(7) FIG. 7 is an XRD pattern of CFTS nanoparticles as prepared in Example 2.1. The peak positions are well matched to those of mawsonite CFTS. [J. T. Szymanski, Canad. Mineral., 1976, 14, 529]

(8) FIG. 8 is a TGA plot of CFTS nanoparticles capped with 1-dodecanethiol, as prepared in Example 2.1.

(9) FIG. 9 is an XRD pattern of CZTSSe nanoparticles prepared according to Example 3.1. The peak positions are well matched to those of stannite CZTSe. [Olekseyuk et al., J. Alloys Compd., 2002, 340, 141]

(10) FIG. 10 is an XRD pattern of CCdTSe nanoparticles prepared according to method 4.1. The peak positions are well matched to those of stannite CCdTSe. [Olekseyuk et al., J. Alloys Compd., 2002, 340, 141] Low intensity, unidentified peaks suggest the presence of a minor, secondary phase.

DESCRIPTION

(11) Applicant's co-pending U.S. Patent Application 61/798,084 (filed 15 Mar. 2013) describes the synthesis of CZTS nanoparticles capped with an organo-thiol ligand, and is hereby incorporated by reference in its entirety. As used herein, the term CXTY refers to compounds of the form Cu.sub.2XSnY.sub.4, where X is a d-block metal and Y is a chalcogen. It will be understood that the formula is not meant to imply a stoichiometry where the ratio of Cu:X:Sn:Y is exactly 2:1:1:4; one of skill in the art will appreciate that those ratios are estimates only. As used herein, low temperature synthesis refers to a heating-up method of synthesis wherein the reaction solution is heated at temperatures of 300 C. or below, more particularly 250 C. or below, or 240 C. or below, to effect the conversion of the precursors to nanoparticles. In a heating-up method, the nanoparticles are combined at modest temperatures, for example, between room temperature and 200 C., and the reaction solution is subsequently heated to induce nanoparticle formation. Thus, a low temperature synthesis is different than a hot-injection synthesis because the precursors are combined at significantly lower temperatures and the concentration of the precursors in the reaction solution is significantly higher than for a hot-injection reaction.

(12) As explained above, the surfaces of nanoparticles are generally capped with organic ligands that prevent the nanoparticles from agglomerating and that aid in the solution and deposition of the nanoparticles to make films. Generally, prior art techniques utilise high boiling ligands, such as oleylamine. The organic ligands must be removed, e.g. by evaporation, prior to sintering, since residual carbon can be detrimental to the performance of the absorber layer. Aspects of the processes described herein provide CXTY nanoparticles that having surface coatings consisting essentially of labile organo-chalcogen ligands. As used herein, the term labile organo-chalcogen refers to an organo-chalcogen with a boiling point less than 300 C. According to some embodiments, nanoparticles having surface coatings consisting essentially of labile organo-chalcogens readily lose those capping ligands when the nanoparticles are heated to moderate temperatures. According to some embodiments, greater than 50% of the surface coating consisting essentially of labile organo-chalcogen is removed from the nanoparticle surface when the nanoparticle is heated to 350 C. Since the surface coatings provided by the methods described herein are removable at lower temperatures than those described in the prior art, the resulting nanoparticles are more easily processed and yield higher performing films. The nanoparticles described herein, having surface coatings consisting essentially of labile organo-chalcogens provide an advantage over the CXTY nanoparticles described in the art, which have high-boiling capping ligands, such as oleylamine or oleic acid.

(13) The process disclosed herein comprises a relatively low-temperature, high yield synthesis of nanoparticles of the form CXTY, where X is a d-block metal (e.g., Zn, Cd, Hg, Ni, Co, Mn or Fe) and Y is a chalcogen (e.g., S or Se). The CXTY material can be used as an alternative to CIGS materials as an absorber layer in thin film photovoltaic devices.

(14) An embodiment of a process for forming CXTY nanoparticles is summarised in FIG. 1. The process comprises: (a) combining Cu, X and Sn precursors in a solvent at a first temperature; (b) adding an organo-chalcogen ligand; (c) heating to a second temperature for a first time interval to form the CXTY nanoparticles; (d) cooling the reaction mixture; and (e) isolating the CXTY nanoparticles. Using the illustrated method, it is possible to produce a wide range of CXTY nanoparticle material.

(15) Suitable Cu precursors include, but are not restricted to: acetates, e.g. Cu(ac), Cu(ac).sub.2; acetylacetonates, e.g. Cu(acac).sub.2; and chlorides, e.g. CuCl, CuCl.sub.2. X can be one or more d-block elements, including, but not restricted to: Zn, Cd, Hg, Ni, Co, Mn, Fe. Suitable precursors may include, but are not restricted to: acetates, e.g. Zn(ac).sub.2, Cd(ac).sub.2, Cd(ac).sub.2.2H.sub.2O, Hg(ac).sub.2, Ni(ac).sub.2.4H.sub.2O, Co(ac).sub.2.4H.sub.2O, Mn(ac).sub.2.2H.sub.2O, Fe(ac).sub.2; acetylacetonates, e.g. Cd(acac).sub.2, Ni(acac).sub.2, Ni(acac).sub.3, Co(acac).sub.2, Co(acac).sub.3, Mn(acac).sub.2, Mn(acac).sub.3, Fe(acac).sub.2, Fe(acac).sub.3; chlorides, e.g. ZnCl.sub.2, CdCl.sub.2, HgCl.sub.2, NiCl.sub.2, CoCl.sub.2, MnCl.sub.2, FeCl.sub.2, FeCl.sub.2.4H.sub.2O, FeCl.sub.3, FeCl.sub.3.6H.sub.2O; and stearates, e.g. Zn(st).sub.2, Ni(st).sub.2, Co(st).sub.2.

(16) Suitable Sn precursors include, but are not restricted to, chlorides, e.g. SnCl.sub.4, SnCl.sub.4.5H.sub.2O, tin(IV)acetate, tin(IV) bis(acetylacetonate) dichloride and triphenyl(trimethyl) tin. A particularly suitable Sn precursor is SnCl.sub.4 as a solution in dichloromethane, due to its relative ease and safety in handling. The dichloromethane solvent can be removed by distillation during the nanoparticle synthesis.

(17) The solvent is used to dissolve or suspend the Cu, X and Sn precursors. In some embodiments, the solvent is dichloromethane. Other suitable examples include, but are not restricted to, non-coordinating solvents such as 1-octadecene and Therminol 66 [Eastman Chemical Company]. One skilled in the art will realise that, where the boiling point of the solvent is lower than the reaction temperature required to effect the conversion of the precursors to CXTY nanoparticles, it may be necessary to distil the solvent during the course of heating the reaction mixture to the second (reaction) temperature.

(18) The first temperature, at which the Cu, X and Sn precursors are combined with the solvent, is substantially below the boiling point of the solvent. In some embodiments, the first temperature is room temperature.

(19) The organo-chalcogen ligand is of the form RYH, where R is an alkyl or aryl group and Y is sulphur or selenium. In some embodiments, the organo-chalcogen ligand functions as both the reaction solvent and the nanoparticle capping agent. In some embodiments, the organo-chalcogen ligand comprises two or more organo-chalcogen compounds. In particular embodiments, it may be desirable for the boiling point(s) of the organo-chalcogen ligand(s) to fall within the range 180-300 C., to allow both synthesis of phase-pure CXTY nanoparticles and to effect the removal of the ligand(s) during subsequent device processing. Examples of suitable organo-chalcogen ligands include, but are not restricted to: 1-octanethiol, 1-dodecanethiol, t-dodecanethiol, 2-naphthalenethiol, 1-octane selenol, and 1-dodecane selenol.

(20) According to some embodiments, the organo-chalcogen ligand is combined with the Cu, X and Sn precursors and the first solvent at a temperature not greater than 50 C., for example, room temperature.

(21) In some embodiments, two or more d-block metals (X) and/or two or more chalcogens (Y) are combined to form an alloyed material.

(22) The reaction mixture is heated to a second temperature for a first time interval to effect the conversion of the precursors to CXTY nanoparticles. In some embodiments, the second temperature lies in the range 180-300 C., for example around 220-240 C. The first time interval lies in the range of 30 minutes-5 hours, for example around 1 hour.

(23) Optionally, a secondary chalcogen precursor can be added to the reaction solution during synthesis to maintain particle growth. Suitable precursors include, but are not restricted to, trioctylphosphine sulphide, and trioctylphosphine selenide.

(24) Following nanoparticle formation, the reaction mixture is cooled and the CXTY nanoparticles are isolated. The nanoparticles may be isolated via any method known in the prior art, for example, by precipitating the nanoparticles using a combination of solvents and non-solvents, then collecting the nanoparticles via centrifugation. Examples of suitable solvent/non-solvent combinations include chloroform and acetone, and dichloromethane and methanol.

(25) The CXTY nanoparticles can be processed and incorporated into a photovoltaic device. A process preparing a thin film using CXTY nanoparticles is shown in FIG. 2. The method comprises: (a) dissolving or dispersing the CXTY nanoparticles in one or more solvents to form an ink; (b) depositing the ink on a substrate; (c) annealing at a first temperature, for a first time interval, under an inert atmosphere to remove the ligand; (d) annealing at a second temperature, for a second time interval, under an inert atmosphere to induce crystallisation of the film; and (e) optionally annealing at a third temperature, for a third time interval, under a chalcogen-rich atmosphere. Subsequent layers can then be deposited to form a photovoltaic device.

(26) The CXTY nanoparticles can be dissolved or dispersed in one or more solvents by any method known to one skilled in the art, including shaking, stirring or ultrasonication. In some embodiments, the solvent(s) is/are non-polar. Examples include, but are not restricted to, toluene, alkanes (e.g. hexane), chlorinated solvents e.g. (dichloromethane, chloroform, etc.), ketones (e.g. isophorone), ethers (e.g. anisole), and terpenes (e.g. -terpinene, limonene, etc.). Optionally, other additives, such as binders, rheology modifiers, and the like, may be incorporated into the ink formulation to modify its coating properties.

(27) The ink can be deposited on a substrate using any method known to one skilled in the art. Examples include, but are not restricted to, spin-coating, slit-coating, drop-casting, doctor blading, and inkjet printing.

(28) Once deposited, the ink is annealed at a first temperature to remove the solvent, ligand, and other organic components of the ink formulation. This eliminates carbon residues, which can be detrimental to device performance, from the film. It will be apparent to one skilled in the art that the first annealing temperature depends on the boiling points of the organic components of the nanoparticle ink. In particular embodiments, the first annealing temperature lies in the range 260-350 C., for example around 300 C. In some embodiments, the first time interval preferably lies in the range 3-10 minutes, for example around 5 minutes. In some embodiments, the first annealing step is conducted under an inert atmosphere.

(29) The films are annealed at a second temperature to induce crystallisation of the CXTY layer (sintering). In some embodiments, the second annealing temperature is higher than the first annealing temperature. For example, the second annealing temperature may lie in the range 350-440 C., for example around 400 C. In particular embodiments, the second time interval lies in the range 3-10 minutes, for example around 5 minutes. In some embodiments, the sintering step is conducted under an inert atmosphere.

(30) The ink deposition, first and second annealing steps may be repeated until a desired film thickness is achieved. Optionally, the films may be annealed under a chalcogen-rich atmosphere. Examples of sulphurisation sources include, but are not restricted to, H.sub.2S and elemental sulphur. Examples of selenisation sources include, but are not restricted to, H.sub.2Se and elemental selenium. In some embodiments, the third annealing temperature lies in the range 500-600 C., for example around 550 C. The third time interval may, for example, lie in the range 30 minutes-3 hours, more particularly around 1-2 hours.

(31) Additional layers can be deposited on top of the CXTY layer to form a PV device. The method of forming CXTY nanoparticles is illustrated in the following examples.

EXAMPLES

Example 1: Synthesis of CZTSe Nanoparticles

Example 1.1

(32) Synthesis of CZTSe nanoparticles using 1-octane selenol as the selenium precursor. 1.0 g of Cu(ac) (8.2 mmol; ac=acetate), 0.74 g of Zn(ac).sub.2 (4.0 mmol), and 4.1 mL of a 1 M solution of SnCl.sub.4 in dichloromethane (4.1 mmol) were stirred at room temperature in a 50 mL three-necked round-bottomed flask fitted with a magnetic stirrer and a condenser with a side-arm. 5 mL of dichloromethane were added to dissolve/suspend the salts, forming a grey solution. The mixture was degassed by bubbling through nitrogen at room temperature. After stirring under nitrogen for 1 hours the solution had turned a beige/cream colour. 11.6 mL of 1-octane selenol (65.0 mmol) were injected quickly into the flask; the mixture turned instantly dark red. The temperature was raised to 50-55 C. and held for 5 minutes to allow the dichloromethane, which collected in the side-arm of the condenser, to distil off. The mixture turned a bright golden orange colour. The temperature was raised to 140 C., whereupon a brown/black slurry formed. The temperature was held at 140 C. for 1 hour, before cooling to room temperature. The product, a black solid (1.63 g), was isolated with chloroform and acetone. The solid was collected by centrifugation. The particles were dispersible in non-polar solvents.

(33) Elemental analysis by inductively coupled plasma optical emission spectrometry (ICP-OES) gave the following elemental ratios: C 21.44%; H 3.78%; Cu 22.63%; Zn 4.50%; Sn 8.82%; Se 37.24%. Normalising to Sn, this gives a stoichiometry of Cu.sub.4.79Zn.sub.0.92Sn.sub.1.00Se.sub.6.35, suggesting that the material is Cu- and Se-rich. The selenol ligand contributes to the total Se content. X-ray diffraction (XRD) analysis (FIG. 3) suggests the presence of both the stannite phase of CZTSe and an umangite Cu.sub.2Se.sub.3 impurity phase. For thin film PV applications, copper selenide impurity phases can act as a sintering flux. Afterwards, they can be selectively removed from the absorber layer via KCN etching, [Q. Guo et al., Nano Lett., 2009, 9, 3060] leaving behind a stoichiometric, phase pure CZTSe film.

(34) The stoichiometry can be tuned by altering the ratios of the metal precursors. Phase purity may be achieved by controlling the reaction conditions. For example, in the colloidal synthesis of CZTS nanoparticles using metal acetate precursors, Kameyama et al. reported the presence of copper selenide impurity phases at low temperatures, which could be eliminated by increasing the reaction temperature above 180 C. [T. Kameyama et al., J. Mater. Chem., 2010, 20, 5319] Similarly, to synthesise phase-pure CZTSe nanoparticles using the current method, 1-octane selenol may be substituted for a higher boiling selenol precursor, acting as both the reaction solvent and ligand, to facilitate a higher reaction temperature and thus preferential formation of the CZTSe phase. Suitable higher boiling selenol compounds include, but are not restricted to, 1-dodecane selenol, as in Example 1.2, where CZTSe nanoparticles with a pure wurtzite crystal structure were synthesised at 240 C.

(35) Thermogravimetric analysis (TGA, FIG. 4) shows that the material has an inorganic content of approximately 65%. The ligand is completely removed below 300 C., which would enable relatively low temperature optoelectronic device processing.

Example 1.2

(36) Synthesis of CZTSe nanoparticles using 1-dodecane selenol as the selenium precursor. 1.00 g of Cu(ac) (8.2 mmol) and 0.74 g of Zn(ac).sub.2 (4.0 mmol) were purged with nitrogen in a 50 mL three-necked round-bottomed flask fitted with a magnetic stirrer and a condenser with a side-arm. 5 mL of dichloromethane and 4.1 mL of a 1 M solution of SnCl.sub.4 in dichloromethane (4.1 mmol) were stirred at room temperature, under nitrogen, for 90 minutes to form a beige suspension. 15 mL of 1-dodecane selenol were injected quickly into the flask. The temperature was raised to 50-60 C. to allow the dichloromethane, which collected in the side-arm of the condenser, to distil off. The temperature was raised to 240 C. and held for 1 hour, before cooling to room temperature. The product, a black powder (2.49 g), was isolated with chloroform/acetone and dichloromethane/methanol, and collected by centrifugation. The particles were dispersible in non-polar solvents.

(37) Elemental analysis of the inorganic content by ICP-OES gave the following elemental ratios: Cu 15.76%; Zn 7.53%; Sn 20.13%; Se 53.62%. Normalising to Sn, this gives a stoichiometry of Cu.sub.1.46Zn.sub.0.67Sn.sub.1.00Se.sub.4.00, where the selenol ligand contributes to the total Se content, therefore it is reasonable to assume that the material is Sn-rich. The stoichiometry can be tuned by altering the ratios of the metal precursors. XRD analysis (FIG. 5) suggests a wurtzite crystal structure; the peak positions match well with those of wurtzite ZnSe. [K. Yvon et al., J. Appl. Cryst., 1977, 10, 73] Slight shifting of the peak positions may be attributable to the partial substitution of Zn with Cu and Sn. Four-coordinate Zn.sup.2+ has an ionic radius of 60 pm, while those of Cu.sup.+ and Sn.sup.4+ are 46 pm and 74 pm, respectively; [C. E. Housecroft and E. C. Constable, Chemistry (3.sup.rd Edition); Pearson Education Limited: Harlow, 2006; pp. 1195-1197] the slight shift of the XRD pattern of CZTSe to lower angles compared to those of ZnSe suggests an overall expansion of the wurtzite unit cell upon the incorporation of Cu and Sn. Differences in the relative peak intensities of the CZTSe nanoparticles compared to wurtzite ZnSe may suggest preferential crystal growth in one or more directions.

(38) TGA indicates that the 1-dodecane selenol ligand begins to evaporate at around 200 C. and is totally removed by around 320 C., as shown in FIG. 6. Further mass loss above 350 C. may be due to loss of inorganic material, suggesting the dodecane selenol-capped CZTSe nanoparticles are particularly suited to relatively low temperature thermal processing (<350 C.).

Example 2: Synthesis of CFTS Nanoparticles

Example 2.1

(39) Synthesis of CFTS nanoparticles using Fe(acac).sub.3 (acac=acetylacetonate) as the iron precursor. 1.0 g of Cu(ac) (8.2 mmol), 1.48 g of Fe(acac).sub.3 (4.2 mmol), and 4.1 mL of a 1 M solution of SnCl.sub.4 in dichloromethane (4.1 mmol) were stirred at room temperature in a 50 mL three-necked round-bottomed flask fitted with a magnetic stirrer and a condenser with a side-arm. 5 mL of dichloromethane were added to dissolve/suspend the salts, forming a dark red mixture. The mixture was degassed by bubbling through nitrogen at room temperature for 1 hours. 15.5 mL of 1-dodecanethiol (64.7 mmol) were injected quickly into the flask; the mixture turned instantly brown. The temperature was raised to 60 C. and the dichloromethane, which collected in the side-arm of the condenser, was distilled off. The temperature was raised to 220-240 C., then held and stirred for 1 hour, before cooling to room temperature. The product, a black powder (1.57 g), was isolated with chloroform and acetone. The solid was collected by centrifugation and dried under vacuum. The particles were dispersible in non-polar solvents.

(40) Elemental analysis by ICP-OES gave the following elemental ratios: C 15.12%; H 2.98%; Cu 35.31%; Fe 2.53%; Sn 16.15%; S 19.69%. Normalising to Sn, this gives a stoichiometry of Cu.sub.4.08Fe.sub.0.33Sn.sub.1.00S.sub.4.51, suggesting that the material is Cu-rich, and that Cu may be doping Fe vacancies and interstitial positions. The thiol ligand contributes to the total S content. XRD analysis (FIG. 7) shows that the material closely matches the mawsonite crystal structure of CFTS, [J. T. Szymanski, Canad. Mineral., 1976, 14, 529] without any obvious impurity phases. The stoichiometry can be tuned by altering the ratios of the precursors.

(41) TGA (FIG. 8) indicates that the material has an inorganic content of approximately 72% at 600 C. Loss of the 1-dodecanethiol ligand is accounted for by the high negative gradient of the curve between 250-350 C. Further mass loss beyond 350 C. is likely to be that of elemental sulphur from the nanoparticles (boiling point: 444.7 C.). The TGA thus highlights that a low boiling ligand is advantageous for thin film optoelectronic applications, since the ligand can be removed at lower boiling temperatures without concomitant loss of inorganic sulphur from the nanoparticles.

Example 2.2

(42) Synthesis of CFTS nanoparticles using Fe(acac).sub.2 as the iron precursor. 1.0 g of Cu(ac) (8.2 mmol), 1.06 g of Fe(acac).sub.2 (4.2 ml), and 4.1 mL of a 1 M solution of SnCl.sub.4 in dichloromethane (4.1 mmol) were stirred at room temperature in a 50 mL three-necked round-bottomed flask fitted with a magnetic stirrer and a condenser with a side-arm. 5 mL of dichloromethane were added to dissolve/suspend the salts, forming a dark brown mixture. The mixture was degassed by bubbling through nitrogen at room temperature for 1 hours. 15.5 mL of 1-dodecanethiol (64.7 mmol) were injected quickly into the flask; the mixture remained brown. The temperature was raised to 60 C. and the dichloromethane, which collected in the side-arm of the condenser, was distilled off. The mixture was heated to 240 C. At 170 C. the mixture became orange/brown, darkening with further increases in temperature. The solution was then held and stirred at 230-240 C. for 1 hour, before cooling to room temperature. The product, a black solid (1.2 g), was isolated with chloroform and acetone. The solid was collected by centrifugation and dried under vacuum. The particles were dispersible in non-polar solvents, including toluene, cyclohexane, and hexanethiol.

(43) Elemental analysis by ICP-OES gave the following elemental ratios: C 18.68%; H 3.41%; Cu 38.25%; Fe 4.20%; Sn 12.49%; S 18.57%. Normalising to Sn, this gives a stoichiometry of Cu.sub.5.72Fe.sub.0.71Sn.sub.1.00S.sub.5.50, suggesting that the material is Cu-rich, and that Cu may be doping Fe vacancies and interstitial positions. The thiol ligand contributes to the total S content. The stoichiometry can be tuned by altering the ratios of the precursors.

Example 3: Synthesis of CZTSSe Nanoparticles

(44) As the current method can be used to synthesise CZTSe nanoparticles and the applicant's co-pending U.S. patent application 61/798,084 (filed 15 Mar. 2013) describes the synthesis of CZTS nanoparticles, it will be obvious to one skilled in the art that by using a combination of one or more alkyl and/or aryl thiol and one or more alkyl and/or aryl selenol compounds, nanoparticle material of the form Cu.sub.2ZnSn(S,Se).sub.4 can be produced, as shown in Example 3.1. The stoichiometry of the material, and thus the band gap, can be tuned by controlling the thiol:selenol ratio. The upper limit to the reaction temperature will be restricted by the lowest boiling point of the organo-chalcogen compounds. The organo-chalcogen compounds can be mixed prior to their addition to the reaction solution, or alternatively they can be injected concurrently or sequentially.

(45) In some embodiments, the organo-thiol compound(s) have a boiling temperature greater than 180 C. but substantially below the boiling points of elemental sulphur and selenium, for example below 300 C. Suitable examples include, but are not restricted to: 1-octanethiol, 1-dodecanethiol, t-dodecanethiol, 2-naphthalenethiol.

(46) In some embodiments, the organo-selenol compound(s) have a boiling temperature greater than 180 C. but substantially below the boiling points of elemental sulphur and selenium, for example below 300 C. Suitable examples include, but are not restricted to: 1-octane selenol, 1-dodecane selenol.

Example 3.1: Synthesis of CZTSSe nanoparticles using 1-octane thiol and

(47) 1-octane selenol as the chalcogen precursors. 1.00 g of Cu(ac) (8.2 mmol) and 0.74 g of Zn(ac).sub.2 (4.0 mmol) were purged with nitrogen in a 100 mL three-necked round-bottomed flask fitted with a magnetic stirrer and a condenser with a side-arm. 480 L of SnCl.sub.4 in 4 mL of dichloromethane (4.1 mmol) were added, followed by a further 5 mL of dichloromethane, then the mixture was stirred at room temperature, under nitrogen, for 1 hour. 6.0 mL of 1-octanethiol (35 mmol) and 6.0 mL of 1-octane selenol (34 mmol), both pre-degassed, were injected quickly into the flask. The temperature was raised to 55 C. and held to allow the dichloromethane, which collected in the side-arm of the condenser, to distil off. The temperature was raised to 220 C. and held for 1 hour, before cooling to room temperature. The product (2.58 g), a black powder, was isolated with chloroform/acetone and dichloromethane/methanol. The solid was collected by centrifugation. The particles were dispersible in non-polar solvents.

(48) Elemental analysis of the inorganic components of the material by ICP-OES gave the following elemental ratios: Cu 15.99%; Zn 6.89%; Sn 19.24%; S 1.8%; Se 47.28%. Normalising to Sn, this gives a stoichiometry of Cu.sub.1.55Zn.sub.0.65Sn.sub.1.00S.sub.0.35Se.sub.3.69, suggesting that the material is slightly Sn-rich. The organo-chalcogen ligands contribute to the total S and Se content. XRD analysis (FIG. 9) shows that the material closely matches the stannite crystal structure of CZTSe, [Olekseyuk et al., J. Alloys Compd., 2002, 340, 141], supporting the relatively low proportion of S to Se as determined by ICP. A number of low intensity, unidentified peaks suggest the presence of a small proportion of an impurity phase. The stoichiometry can be tuned by altering the ratios of the metal precursors.

(49) The inorganic content, as determined by TGA, was approximately 77% at 600 C. The TGA profile was similar to that of the 1-octane selenol-capped CZTSe nanoparticles in FIG. 4, with complete removal of the ligands below 350 C.; co-evaporation of the thiol and selenol ligands is facilitated by their relatively similar boiling points.

Example 4: Synthesis of CCdTSe Nanoparticles

Example 4.1

(50) Synthesis of CCdTSe nanoparticles using 1-octane selenol as the selenium precursor. 1.00 g of Cu(ac) (8.2 mmol), 1.076 g of Cd(ac).sub.2.2H.sub.2O (4.0 mmol) and 10 mL of 1-octadecene where degassed under vacuum for 1 hour in a 100 mL three-necked round-bottomed flask fitted with a magnetic stirrer and a condenser with a side-arm. The flask was purged with nitrogen. 480 L of SnCl.sub.4 in 4 mL of dichloromethane (4.1 mmol) were added, then the mixture was stirred at room temperature for 1 hour. 12.0 mL of 1-octane selenol (67 mmol) were injected quickly into the flask. The temperature was raised to 55 C. and held to allow the dichloromethane, which collected in the side-arm of the condenser, to distil off. The temperature was raised to 225 C. and held for 1 hour, before cooling to room temperature. The product, a black powder (2.72 g), was isolated with chloroform/acetone and dichloromethane/methanol. The solid was collected by centrifugation. The particles were dispersible in non-polar solvents.

(51) Elemental analysis of the inorganic components of the material by ICP-OES gave the following elemental ratios: Cu 15.47%; Cd 11.62%; Sn 17.78%; Se 42.16%. Normalising to Sn, this gives a stoichiometry of Cu.sub.1.63Cd.sub.0.69Sn.sub.1.00Se.sub.3.56, suggesting that the material is slightly Sn-rich. The inorganic content, as determined by TGA, was approximately 96% at 600 C., suggesting the particles are capped with relatively little ligand. XRD analysis (FIG. 10) shows that the major peaks closely match the stannite crystal structure of CCdTSe. [Olekseyuk et al., J. Alloys Compd., 2002, 340, 141] Low intensity, unidentified peaks suggest the presence of a minor, secondary phase, possibly a binary, ternary or quaternary selenide phase. The stoichiometry can be tuned by altering the relative ratios of the precursors.