Patent Application
20220089446
The present invention relates to fluorescent diamond particles and methods of fabricating such particles for use in applications such as fluorescent markers and labels in biological applications and medical diagnostics.
Many point defects have been studied in synthetic diamond material including: silicon containing defects such as silicon-vacancy defects (Si-V), silicon di-vacancy defects (Si-V2), silicon-vacancy-hydrogen defects (Si-V:H), silicon di-vacancy hydrogen defects (S-V2:H); nickel containing defect; chromium containing defects; and nitrogen containing defects such as nitrogen-vacancy defects (N-V), di-nitrogen vacancy defects (N-V-N), and nitrogen-vacancy-hydrogen defects (N-V-H). These defects are typically found in a neutral charge state or in a negative charge state.
Fluorescent point defects in synthetic diamond material have been proposed for use in various sensing, detecting, and quantum processing applications including: magnetometers; spin resonance devices such as nuclear magnetic resonance (NMR) and electron spin resonance (ESR) devices; spin resonance imaging devices for magnetic resonance imaging (MRI); and quantum information processing devices such as for quantum computing.
In addition to the above, it has also been proposed to use fluorescent point defects in diamond material as fluorescent markers or labels in biological applications and medical diagnostics. For example, Rabeau et al. (Nano Letters, vol. 7, No. 11, 3433-3437, 2007) disclose the use of nanodiamonds as fluorescent labels in biological systems. As indicated by Rabeau et al, key advantages of nanodiamonds compared to other conventional fluorescent biolabels include their non-cytotoxicity, room-temperature photostability, and the relative ease with which surfaces can be functionalized. It is further indicated that biological applications demand bright fluorescence from small crystals. In this regard, Rabeau et al. have performed an analysis of diamond particle size versus nitrogen-vacancy (NV) centre content and found a strong dependence of NV centre content and crystal size for diamond nano-crystals grown via a chemical vapour deposition technique. They report that a particle size of 60-70 nm is optimal for single NV centre incorporation per diamond nano-particle.
A problem with the diamond nano-particles described by Rabeau is that they have a low NV centre content and thus have a relatively low fluorescent intensity which is not ideal for many fluorescent marker applications. The Rabeau et al. document itself indicates that biological applications demand bright fluorescence from small crystals. However, there is no indication of how to incorporate a high concentration of NV centres into small diamond nano-crystals to increase their fluorescent intensity. The diamond nano-crystals described in the Rabeau et al. document have a low NV centre content and thus will have a relatively low fluorescent intensity not suited to many fluorescent marker applications.
US2014/0065424 discloses a method of producing light-emitting nano-particles of diamond. In the method described in this document, micron scale diamond particles are irradiated and annealed and then the particles are ground to nano-particles having a size between 15 and 20 nanometres.
A further problem is that the NV content is not uniform throughout all micron scale diamond particles in a powder after irradiation and annealing. This means that amplitude of the fluorescence (or brightness) will vary from particle to particle. A measurement of the amplitude of fluorescence of a large number of particles (perhaps in biological tissue) will not necessarily indicate the number of diamond particles present, as individual diamond particles will display a different fluorescent response.
It is an object to provide a powder of fluorescent diamond particles in which the brightness of the fluorescence of individual diamond particle has a high degree of uniformity.
According to a first aspect, there is provided a diamond powder comprising diamond particles having an average particle size of no more than 20 μm and a vacancy or impurity-vacancy point defect concentration of at least 1 ppm. At least 70% of the volume of diamond in the powder is formed from a single crystal growth sector. This leads to a substantially uniform concentration of vacancies or impurity-vacancy point defects in the diamond particles because the rate of impurity take-up during growth is heavily dependent on the growth sector. One advantage of having a substantially uniform concentration of vacancies or impurity-vacancy point defects in the diamond particles is that a fluorescence response of the particles will be substantially the same.
Examples of suitable growth sectors include a {100} growth sector and a {111} growth sector.
As an option, the diamond particles are crushed from larger precursor diamond particles.
The vacancy or impurity-vacancy point defect concentration in the diamond particles is optionally is selected from any one of at least: 5 ppm; 10 ppm; 20 ppm; 50 ppm; or 100 ppm.
The impurity-vacancy point defects are optionally selected from any of nitrogen-vacancy point defects and silicon-vacancy point defects.
As an option, the particles in the powder have an average vacancy or impurity-vacancy point defect concentration, and a variation about the average vacancy or impurity-vacancy point defect concentration is selected from any one of no more than: 50%; 40%; 30%; 20% or 10%.
The average particle size of the diamond particles is optionally selected from any of no more than 1 μm, no more than 500 nm and no more than 200 nm. Smaller particle sizes may be useful in biological applications.
The diamond powder optionally comprises one or more organic functional groups bonded to an outer surface of the diamond particles.
As an option, the volume of diamond in the powder formed from a single crystal growth sector is selected from any of greater than 80% and greater than 90%. The higher the volume percentage, the more uniform the vacancy or impurity-vacancy point defect concentration is likely to be.
According to a second aspect, there is provided a precursor diamond powder comprising diamond particles having an average particle size of no more than 1 mm and a vacancy or impurity-vacancy point defect concentration of at least 1 ppm, wherein at least 70% of the volume of diamond in the powder is formed from a single crystal growth sector. Such a powder can, if required, be crushed to smaller sizes.
As an option, the volume of diamond in the precursor diamond powder formed from a single crystal growth sector is selected from any of greater than 80% and greater than 90%.
According to a third aspect, there is provided a method of fabricating a diamond powder comprising diamond particles having an average particle size of no more than 20 μm. A precursor diamond powder is crushed to form a diamond powder with an average particle size of no more than 20 μm. The diamond powder comprises diamond particles having a vacancy or impurity-vacancy point defect concentration of at least 1 ppm, wherein at least 70% of the volume of diamond in the crushed diamond powder is formed from a single crystal growth sector.
As an option, the growth sector is selected from one of a {100} growth sector and a {111} growth sector.
In an optional embodiment, precursor diamond particles are irradiated, prior to crushing, to generate vacancy defects in the precursor diamond particles.
In an alternative optional embodiment, precursor diamond particles are irradiated after crushing, to generate vacancy defects in the precursor diamond particles.
The precursor diamond particles optionally have a nitrogen or silicon concentration selected from any one of at least: 10 ppm; 20 ppm; 50 ppm; 100 ppm; or 200 ppm.
As an option, the irradiating is performed at a temperature selected from any one of no more than: 500° C.; 400° C.; 300° C.; 200° C.; 100° C.; or 50° C.
As an option, the irradiating step is controlled to introduce isolated vacancy point defects into the initial diamond particles at a concentration selected from any one of at least: 5 ppm; 10 ppm; 20 ppm; 50 ppm; 100 ppm; or 200 ppm.
As an option, the method comprises, after irradiating, annealing the diamond particles.
Annealing is optionally performed at a temperature selected from any one of at least: 600° C.; 700° C.; or 750° C. The annealing step is optionally performed at a temperature selected from any one of no more than: 1000° C.; 900° C.; 850° C.; or 800° C.
As an option, after the irradiating and annealing steps the diamond particles have an impurity-vacancy point defect concentration selected from any one of at least: 5 ppm; 10 ppm; 20 ppm; 50 ppm; or 100 ppm. As a further option, the impurity-vacancy point defects are nitrogen-vacancy point defects or silicon-vacancy point defects.
As a further option, the method further comprises, prior to crushing the precursor diamond powder to form the diamond powder with an average particle size of no more than 20 μm, sorting the precursor diamond powder to select diamond particles formed from substantially a single crystal growth sector.
As an option, the volume of diamond in the powder formed from a single crystal growth sector is selected from any of greater than 80% and greater than 90%. The higher the volume percentage, the more uniform the vacancy or impurity-vacancy point defect concentration is likely to be.
For a better understanding of the present invention and to show how the same may be carried into effect, embodiments of the present invention will now be described by way of example only with reference to the accompanying drawings, in which:
By careful control of the temperature and pressure during the HPHT process, desired growth sectors can be achieved at the expense of others. For example, conditions can be provided that favours the growth of {100} growth sectors, which means that after a certain amount of time the volume of a diamond crystal will almost entirely consist of {100} growth sectors.
Note also that synthetic diamond powders may be obtained by process other than HPHT, such as chemical vapour deposition (CVD).
During HPHT synthesis of diamond particles, nitrogen is typically present in the diamond lattice as an impurity. It is known that nitrogen is incorporated into the lattice with different concentrations depending on the orientation of growth surfaces, as described in Kanda, “Nonuniform distributions of color and luminescence of single crystal diamonds”, New Diamond and Frontier Carbon Technology, 105-116 Vol. 17, No. 2, 2007. For example, the nitrogen impurity concentration in the {100} growth sectors of a diamond particle is typically around three times higher than the nitrogen impurity concentration in the {111} growth sectors of the same diamond particle. However, for a given batch of synthetic diamond particles, the nitrogen impurity concentration for a given growth sector will be substantially uniform for all particle volumes having that growth sector. Note that other factors can affect the uptake of impurities, such as the rate of growth of a growth sector, the concentration of the impurity in the solvent, and the temperature. However, to a certain extent these factors can be controlled to make the rate of nitrogen uptake predominantly dependent upon the growth sector.
It therefore follows that where diamond particles are obtained by crushing a standard diamond precursor powder that contains a mixture of cubic, octahedral and cuboctahedral particles, the resultant powders will have a range of different growth sectors and therefore a range of different nitrogen contents. In order to obtain diamond powders, some of the nitrogen impurities must be converted to nitrogen vacancies.
In addition to well-formed cubic, octahedral or cuboctahedral particles, a typical distribution of high-pressure high-temperature synthesised diamond also contains a proportion of irregular, granular or fragmentary particles. These may contain levels of nitrogen significantly different from that of the previously described well-formed particles (often lower, as they may grow in regions of a synthesis volume that are depleted of N). These particles must also be eliminated from the mixture of particles comprising the powder that is to be crushed to form the desired uniformly fluorescent product. Techniques well-known in the art, including sieving, magnetic separation or shape separation using vibrating tables may be used to remove these poorly shaped particles.
It is known that nitrogen vacancy (NV) centre concentration can be increased by irradiating and annealing nitrogen-containing diamond material. Irradiating diamond material, e.g. with electrons or neutrons, introduces vacancy defects into the diamond lattice by knocking carbon atoms off their lattice sites. If the diamond material is then annealed, e.g. at a temperature around 800° C., the vacancies migrate through the diamond lattice and pair up with single substitutional nitrogen defects to form NV centres.
The following description refers to precursor diamond particles, diamond particles and intermediate diamond particles. These terms are used for the purpose of describing examples only, and ‘precursor does not necessarily mean that there were no previous processing steps involved in obtaining the precursor diamond particles. Precursor diamond particles are the particles obtained from initial synthesis (e.g. HPHT or CVD). Where irradiation is performed before crushing, intermediate diamond particles are obtained by irradiating and optionally annealing the precursor diamond particles to increase the NV centre concentration. Diamond particles are obtained by crushing precursor diamond particles to the required size (either before or after irradiation).
A problem is that irradiation introduces a lot of energy into diamond particles, and can graphitize nano-scale diamond particles for use a bio-markers. One solution to this problem is to irradiate larger diamond particles on a cooling block, anneal the irradiated diamond particles to form a high concentration of NV centres, and then crush the diamond particles to reduce their size in order to form a diamond nano-powder with a high NV content. Such a fabrication method is described in US2014/0065424 discussed in the background section of this specification. This fabrication route is viable but not optimal. The reason why this fabrication route is not optimal is that many applications require diamond particles which lie within a relatively tight particle size distribution and/or a relatively uniform fluorescent intensity. However, a crushing process performed after irradiation and annealing will yield a relatively large particle size distribution and also a relatively large variation in fluorescent intensity because the particles have different or multiple growth sectors.
A solution would be to ensure that the diamond powder has the desired particle size distribution prior to subjecting the material to irradiation and annealing such that the treated material does not require further crushing and particle size-filtering steps. However, as previously indicated, irradiation of diamond nano-particles with a sufficient dosage of irradiation to form very bright, high NV content diamond nano-particles can cause thermal management issues such as graphitization of the diamond nano-particles and/or annealing out of vacancies during the irradiation treatment. Furthermore, handling loose diamond nano-powder during irradiation and annealing treatments can be difficult and hazardous and also subject to problems of achieving uniformity.
It has been appreciated that crushing a precursor diamond powder formed from diamonds having substantially a single growth sector will ensure that the resultant diamond powders have a substantially uniform NV concentration after irradiation. To achieve the maximum fluorescence it is preferred to use the {100} growth sectors, but it will be appreciated that using precursor diamond particles predominantly having {111} growth sectors will also give rise to a uniform distribution of NV centres after irradiation.
By ensuring that at least 70% of the volume of a precursor diamond powder is from a single growth sector, on average each irradiated and crushed diamond particle will produce substantially the same amount of fluorescence. This leads to a very tight distribution of fluorescence amplitude.
S1. A precursor diamond powder is provided. The precursor diamond powder is irradiated to form intermediate diamond particles having a vacancy or impurity-vacancy point defect concentration of at least 1 ppm and an average particle size of up to 1 mm. At least 70% of the volume of diamond in the precursor diamond powder is formed from a single crystal growth sector, such as {100}.
S2. The intermediate diamond particles are crushed to an average particle size of no more than 20 μm.
In the example of
S3. A precursor diamond powder is provided. The precursor diamond powder has an average particle size of up to 1 mm. At least 70% of the volume of diamond in the precursor diamond powder is formed from a single crystal growth sector, such as {100}.
S4. The precursor diamond powder is crushed to an average particle size of no more than 20 μm.
S5. The crushed diamond powder is irradiated to provide a crushed diamond powder having a vacancy or impurity-vacancy point defect concentration of at least 1 ppm.
A disadvantage of the method of
Diamond powders obtained by the processes shown in
S5. Crushed or precursor diamond particles are irradiated to generate vacancy defects in the diamond particles. Various techniques outside the scope of this disclosure may be used to mitigate the effects of applying a large amount of energy to small particles to reduce the risk of thermal damage and/or graphitization. The irradiating step may be controlled to introduce isolated vacancy point defects into the initial diamond particles at a concentration selected from any one of at least: 10 ppm; 20 ppm; 50 ppm; 100 ppm; or 200 ppm.
S6. After irradiation, the irradiated diamond particles may be annealed at a temperature suitable to cause migration of vacancy defects through the diamond lattice and formation of nitrogen-vacancy defects. This may be performed at a temperature selected from any one of at least: 600° C.; 700° C.; or 750° C. The annealing temperature may be selected from any one of no more than: 1000° C.; 900° C.; 850° C.; or 800° C. The annealing step may be performed under vacuum or under an inert atmosphere to prevent graphitization of the diamond material during the annealing process.
After steps S5 and S6, the precursor diamond particles may have an impurity-vacancy point defect concentration selected from any one of at least: 5 ppm; 10 ppm; 20 ppm; 50 ppm; or 100 ppm. The impurity-vacancy point defect concentration may be selected from any one of no more than: 500 ppm; 400 ppm; 300; or 200 ppm.
Note that annealing step S6 may be performed immediately after irradiation step S5, or in the case where precursor diamond particles are irradiated, the annealing step may be carried out before or after subsequent crushing.
If it is required to achieve highly fluorescent diamond particles having a high nitrogen-vacancy content, the initial diamond particles should be selected to have a high nitrogen content. For example, the initial diamond particles may have a nitrogen concentration of between at least 10 ppm and 500 ppm, as described above.
Furthermore, to achieve highly fluorescent diamond particles having a high nitrogen-vacancy content, the irradiation step should be controlled to introduce a large concentration of isolated vacancy point defects into the diamond material. For example, the irradiating step may be controlled to introduce isolated vacancy point defects into the diamond particles at a concentration of at least 10 ppm and/or a concentration of no more than 500 ppm as described above.
The irradiation may be via electrons, neutrons, ion bombardment; or gamma rays with electron irradiation being preferred for certain applications. In addition, the use of a heat sink on which the diamond body is placed allows the temperature to be controlled. For example, the irradiating may be performed at a temperature of no more than 500° C., 400° C., 300° C., 200° C., 100° C., or 50° C. The initial diamond powder may be merely placed on the heat sink. Alternatively, a thermal contact fluid, paste, or bonding may be used to control the thermal contact between the initial diamond powder and the underlying heat sink.
While the methodology has been described above in relation to the formation of fluorescent nitrogen-vacancy point defects, it is also envisaged that the fluorescent defects may be formed by the vacancy defects themselves or by other impurity-vacancy defects such as silicon-vacancy defects. Where vacancy defects are utilized as the active functional defect, no annealing step is required after irradiation. For other impurity-vacancy defects such as silicon-vacancy defects an irradiation treatment followed by an annealing treatment can be applied in a similar manner to the nitrogen-vacancy based fluorescent diamond particles as described previously.
The above description refers to average particle size. There are many ways in which particle size may be measured. For example a size range of particles may be expressed in terms of U.S. Mesh size, in which two mesh sizes are provided, the first being a mesh size through which the grains would pass and the second being a mesh size through which the grains would not pass. Mesh size may be expressed in terms of the number of openings per (linear) unit length of mesh. For smaller particle size (say, less than 20 μm), the particle size can be expressed in terms of equivalent circle diameter (ECD), in which each particle is regarded as though it were a sphere. The ECD distribution of a plurality of particles can be measured by means of laser diffraction, in which the particles are disposed randomly in the path of incident light and the diffraction pattern arising from the diffraction of the light by the particles is measured. The diffraction pattern may be interpreted mathematically as if it had been generated by a plurality of spherical particles, the diameter distribution of which being calculated and reported in terms of ECD. Aspects of a particle size distribution may be expressed in terms of various statistical properties using various terms and symbols. Particular examples of such terms include mean, median and mode. The size distribution can be thought of as a set of values Di corresponding to a series of respective size channels, in which each Di is the geometric mean ECD value corresponding to respective channel i, being an integer in the range from 1 to the number n of channels used.
While this invention has been particularly shown and described with reference to embodiments, it will be understood to those skilled in the art that various changes in form and detail may be made without departing from the scope of the invention as defined by the appended claims. For example, while the present invention has been described in the context of fluorescent marker applications, certain embodiments may also be utilized in other applications including quantum sensing applications such as diamond-based magnetometry.
| Number | Date | Country | Kind |
|---|---|---|---|
| 1522512.1 | Dec 2015 | GB | national |
This application is a continuation of U.S. patent application Ser. No. 16/064,016, filed on Jun. 20, 2018, which is a U.S. national phase of International Patent Application No. PCT/EP2016/081654, filed on Dec. 19, 2016, which claims the benefit of United Kingdom Patent Application No. 1522512.1, filed on Dec. 21, 2015, each of which is incorporated herein by reference in its entirety.
| Number | Date | Country | |
|---|---|---|---|
| Parent | 16064016 | Jun 2018 | US |
| Child | 17302597 | US |
