CN111489898A - Preparation method of low-cost ZnNCN material - Google Patents
Preparation method of low-cost ZnNCN material Download PDFInfo
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- QNRATNLHPGXHMA-XZHTYLCXSA-N (r)-(6-ethoxyquinolin-4-yl)-[(2s,4s,5r)-5-ethyl-1-azabicyclo[2.2.2]octan-2-yl]methanol;hydrochloride Chemical compound Cl.C([C@H]([C@H](C1)CC)C2)CN1[C@@H]2[C@H](O)C1=CC=NC2=CC=C(OCC)C=C21 QNRATNLHPGXHMA-XZHTYLCXSA-N 0.000 claims description 2
- 238000005119 centrifugation Methods 0.000 abstract description 3
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Images
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01G—CAPACITORS; CAPACITORS, RECTIFIERS, DETECTORS, SWITCHING DEVICES OR LIGHT-SENSITIVE DEVICES, OF THE ELECTROLYTIC TYPE
- H01G11/00—Hybrid capacitors, i.e. capacitors having different positive and negative electrodes; Electric double-layer [EDL] capacitors; Processes for the manufacture thereof or of parts thereof
- H01G11/22—Electrodes
- H01G11/30—Electrodes characterised by their material
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01G—CAPACITORS; CAPACITORS, RECTIFIERS, DETECTORS, SWITCHING DEVICES OR LIGHT-SENSITIVE DEVICES, OF THE ELECTROLYTIC TYPE
- H01G11/00—Hybrid capacitors, i.e. capacitors having different positive and negative electrodes; Electric double-layer [EDL] capacitors; Processes for the manufacture thereof or of parts thereof
- H01G11/22—Electrodes
- H01G11/24—Electrodes characterised by structural features of the materials making up or comprised in the electrodes, e.g. form, surface area or porosity; characterised by the structural features of powders or particles used therefor
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01G—CAPACITORS; CAPACITORS, RECTIFIERS, DETECTORS, SWITCHING DEVICES OR LIGHT-SENSITIVE DEVICES, OF THE ELECTROLYTIC TYPE
- H01G11/00—Hybrid capacitors, i.e. capacitors having different positive and negative electrodes; Electric double-layer [EDL] capacitors; Processes for the manufacture thereof or of parts thereof
- H01G11/22—Electrodes
- H01G11/26—Electrodes characterised by their structure, e.g. multi-layered, porosity or surface features
- H01G11/28—Electrodes characterised by their structure, e.g. multi-layered, porosity or surface features arranged or disposed on a current collector; Layers or phases between electrodes and current collectors, e.g. adhesives
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01G—CAPACITORS; CAPACITORS, RECTIFIERS, DETECTORS, SWITCHING DEVICES OR LIGHT-SENSITIVE DEVICES, OF THE ELECTROLYTIC TYPE
- H01G11/00—Hybrid capacitors, i.e. capacitors having different positive and negative electrodes; Electric double-layer [EDL] capacitors; Processes for the manufacture thereof or of parts thereof
- H01G11/22—Electrodes
- H01G11/30—Electrodes characterised by their material
- H01G11/32—Carbon-based
- H01G11/34—Carbon-based characterised by carbonisation or activation of carbon
Abstract
The invention belongs to the field of ZnNCN material preparation, and particularly relates to a low-cost ZnNCN material preparation method, which comprises the following steps: synthesis of truncated rhombohedral zeolite imidazolate framework-8 (TRD-ZIF-8) nanoparticles: will dissolve Zn (CH)3COO)2·2H2O (600 mg) in 10 ml of water was added to 10 ml of water containing 2-methylimidazole (0.54mM) and CTAB (2.58mM), slowly stirred for a few seconds, after 10 minutes, the clear solution became a white solution, which was left to stand at room temperature for 3 hours, concentrated in a 50m L centrifuge tube using 9000 r.p.m. centrifugation, and the obtained TRD-ZIF-8 nanoparticles were then washed 3 times with deionized waterThe diameter is small, the specific surface area is large, and the electrochemical performance is stable.
Description
Technical Field
The invention relates to the technical field of ZnNCN material preparation, in particular to a low-cost ZnNCN material preparation method.
Background
As a new generation of energy storage devices, supercapacitors are used due to, for example, high power density (>10,000W kg-1) Long cycle life (>105) And the method has the advantages of low maintenance cost, environmental friendliness and the like, and is widely concerned. Among many supercapacitor candidate species, pseudocapacitors show great potential due to their high energy density and rapid reversible surface redox reactions. At present, transition metal oxides (FeO)x,NiOx，CoOxEtc.) as common pseudocapacitance electrode materials, mainly because of their low cost, environmental friendliness and high abundance. However, transition metal oxide materials generally have problems of poor conductivity, rapid capacity fade, and poor cycling stability during energy storage, which severely limit their practical applications. In general, this can be solved by reducing the particle size of the material and designing special nanostructures (e.g., core-shell structures and hollow structures). However, these additional expensive and/or low yield processing methods seriously offset the inherent advantage of low cost transition metal oxide materials.
In order to reduce the cost of the synthesis method, studies on transition metal carbodiimide compounds (e.g., Mn (NCN))x，Fe(NCN)x，Co(NCN)x，Ni(NCN)x，Cu(NCN)x，Zn(NCN)xEtc.), they exhibit a similar structure to the corresponding transition metal oxides. Among these transition metal carbodiimide compound materials, zinc carbodiimide (ZnNCN) shows some interesting characteristics. For example, untreated ZnNCN (i.e., nanoscale tailoring, complex textures or coatings, etc.) may exhibit higher theoretical capacity, better cycle life, and robust rate capability than its oxide (ZnO). Unfortunately, ZnNCN generally requires an unconventional synthetic route, and the ZnNCN materials produced generally exhibit large crystal sizes and low surface areas. Given the size dependence of nanomaterials, if nanoscale znncns with high surface areas can be obtained, ZnNCN-based materials can be expected to have fascinating properties and to realize novel applications. To achieve this goal, combining the preferred high surface area, good conductivity and high stability carbon materials with ZnNCN may be a potentially low cost solution.
Graphitized carbon nitride (g-C)3N4) As a typical two-dimensional carbon material, it can be considered to be an N-doped graphene analog consisting of periodic heptazine subunits and bridging planar tertiary amino groups to form planar pores, thereby having high stability, extremely high N content, 2D layered structure and abundanceThe characteristics of the inner hole of the face. In view of g-C3N4The low cost, simple synthesis method and the customizable structure of the method are to mix ZnNCN with g-C3N4Combining the new composite materials with high conductivity prepared would be an interesting and challenging task.
Disclosure of Invention
The invention aims to solve the defects of high production cost, low yield, large particle size of prepared nano particles, small specific surface area and the like commonly existing in the existing nano ZnNCN preparation technology, and provides a preparation method of a ZnNCN material which is low in cost and can be prepared in a large area.
In order to achieve the purpose, the invention adopts the following technical scheme:
a preparation method of a low-cost ZnNCN material comprises the following steps:
s1: synthesis of truncated rhombohedral zeolite imidazolate framework-8 (TRD-ZIF-8) nanoparticles: will dissolve Zn (CH)3COO)2·2H2Adding 10 ml of O (600 mg) aqueous solution into 10 ml of aqueous solution dissolved with 2-methylimidazole (0.54mM) and CTAB (2.58mM), slowly stirring for a few seconds, after 10 minutes, changing the original transparent solution into white solution, standing at room temperature for 3 hours, concentrating in a 50m L centrifugal tube by using 9000r.p.m centrifugation, then washing the obtained TRD-ZIF-8 nanoparticles with deionized water for 3 times, and then transferring the collected wet particles to a vacuum drying oven to dry at 60 ℃ overnight to finally obtain TRD-ZIF-8 nanoparticles;
s2: cellular porous ZnNCN/g-C3N4Synthesis of (HPZC) nanocomposite the obtained TRD-ZIF-8 nanoparticles (2g) and melamine (2g) were mixed to a homogeneous state under a vortex shaker and then transferred to a 100m L alumina crucible with a lid, which was subsequently placed in a muffle furnace, set to a temperature-raising program to raise the temperature to 550 ℃ at a rate of 3 ℃/min, then maintained at this temperature for 3h, and naturally cooled to room temperature to obtain black HPZC powder.
Preferably, in the step S1, a monodisperse TRD-ZIF-8 colloid is synthesized as a parent colloid by using a double capping ligand of 2-methylimidazole and CTAB, and the TRD-ZIF-8 parent colloid contains 6 square {100} crystal planes and 12 hexagonal {110} crystal planes.
Preferably, in the S1, the TRD-ZIF-8 is a rhombohedron having six truncated corners.
Preferably, in the S1, the TRD-ZIF-8 nanoparticles are white powder.
Preferably, in S2, the muffle furnace is filled with nitrogen gas.
Preferably, in the S2, melamine is added as a self-sacrifice and catalyst.
Preferably, in S2, the surface of HPZC forms g-C3N4Nanoplatelets and ZnNCN nanoparticles.
Preferably, in the S2, TRD-ZIF-8 nanoparticles (2g) and melamine (2g) need to be mixed for 5-10min under a vortex shaker.
According to the invention, a unique 3D array stacking TRD-ZIF-8 material is obtained from zinc acetate and 2-methylimidazole, and then melamine is added and uniformly mixed, and after annealing at high temperature in a nitrogen atmosphere, a regular honeycomb porous structure is formed. In the process, zinc ions in the system are changed into ZnNCN nano particles, and g-C is generated3N4Are uniformly distributed on the surface of the HPZC. Furthermore, the HPZC electrode showed excellent specific capacitance capability (at 1A g)-1At time 2916F g-1) (ii) a At high current density (7A g)-1) Next, after 1000 cycles of deep charge-discharge, a high capacity retention rate (91.2%) was exhibited, and the average attenuation rate per cycle was only 0.0048%. After the nano-composite material is prepared into an asymmetric super capacitor (HPZC// AC ASC), research results show that the capacitor can respectively provide 3855W Kg-1And 110Wh Kg-1Maximum power density and energy density. The excellent electrochemical performance of HPZC may be due to nanoscale ZnNCN and g-C3N4The synergy of the nanosheets.
The ZnNCN material has the advantages of simple preparation process, high yield, small particle size of the obtained nano particles, large specific surface area and stable electrochemical performance.
Drawings
FIG. 1 is a low-cost cellular porous ZnNCN/g-C provided by the invention3N4A schematic diagram of a synthetic route of the (HPZC) nanocomposite;
FIG. 2 is a simulated ZnNCN powder, pure g-C, of a low cost ZnNCN material preparation method of the present invention3N4XRD patterns of powder and HPZC nanocomposites;
FIGS. 3 to 5 are all performance test charts of ZnNCN material prepared by the method for preparing the low-cost ZnNCN material provided by the invention.
Detailed Description
The technical solutions in the embodiments of the present invention will be described clearly and completely with reference to the accompanying drawings in the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments.
Referring to fig. 1 to 5, a method for preparing a low-cost ZnNCN material includes the steps of:
s1: synthesis of truncated rhombohedral zeolite imidazolate framework-8 (TRD-ZIF-8) nanoparticles: will dissolve Zn (CH)3COO)2·2H2Adding 10 ml of an aqueous solution of O (600 mg) into 10 ml of an aqueous solution dissolved with 2-methylimidazole (0.54mM) and CTAB (2.58mM), slowly stirring for a few seconds, after 10 minutes, changing the original transparent solution into a white solution, standing at room temperature for 3 hours, concentrating the white solution in a 50m L centrifugal tube by using 9000r.p.m centrifugation, then washing the obtained TRD-ZIF-8 nanoparticles with deionized water for 3 times, and then transferring the collected wet particles to a vacuum drying oven to be dried at 60 ℃ overnight to obtain TRD-ZIF-8 nanoparticles;
s2: cellular porous ZnNCN/g-C3N4Synthesis of (HPZC) nanocomposite the TRD-ZIF-8 nanoparticles (2g) obtained and melamine (2g) were mixed to a homogeneous state under a vortex shaker and then transferred to a 100m L alumina crucible with a lid, which was subsequently placed in a muffle furnace set to a temperature program increasing to 550 ℃ at a rate of 3 ℃/min and then maintained at this temperatureAnd naturally cooling to room temperature for 3h to obtain black HPZC powder.
In this example, in S1, monodisperse TRD-ZIF-8 colloid was synthesized using a double capping ligand of 2-methylimidazole and CTAB as a precursor colloid, the TRD-ZIF-8 precursor colloid contained 6 square {100} crystal planes and 12 hexagonal {110} crystal planes, in S1, TRD-ZIF-8 was a rhombic dodecahedron having six truncated corners, in S1, TRD-ZIF-8 nanoparticles were white powders, in S2, a muffle furnace was filled with nitrogen, in S2, melamine was added as a self-sacrifice catalyst, and in S2, the surface of HPZC formed g-C3N4Nanoplatelets and ZnNCN nanoparticles, S2, TRD-ZIF-8 nanoparticles (2g) and melamine (2g) required mixing under a vortex shaker for 5-10 min.
In the present invention, the porous ZnNCN/g-C honeycomb3N4(HPZC) nanocomposites were prepared by a simple two-step process, first, using a double capping ligand of 2-methylimidazole and CTAB to synthesize a monodisperse TRD-ZIF-8 colloid as a parent colloid, as shown in FIG. 1, the TRD-ZIF-8 parent colloid comprising 6 tetragonal {100} faces and 12 hexagonal {110} faces, and thus, in fact, TRD-ZIF-8 is a rhombohedral with six truncated corners. Secondly, adding melamine as a self-sacrifice catalyst, annealing at high temperature in the nitrogen atmosphere to obtain the HPZC of the array-shaped honeycomb porous nano composite material, and forming g-C on the surface of the HPZC3N4Nanoplatelets and ZnNCN nanoparticles. In this context, the precursors are cheap and the synthesis process is easy and will be available for future scale-up.
In the present invention, as shown in FIG. 2, the peaks at 27.4 ℃ and 13.1 ℃ can be expressed as g-C3N4The characteristic of (c). Of which 27.4 deg. corresponds to the {002} crystal plane, which is related to the interlayer stack structure of the aromatic system. 13.1 ℃ corresponds to g-C3N4The in-plane repeat unit of (a). Furthermore, diffraction peaks 19.2 °, 27.9 °, 28.6 °, 36.0 °, 38.9 °, 40.5 °, 45.6 ° and 54.7 ° correspond to {101}, {211}, {220}, {112}, {202}, {112}, {202}, {321}, {411} and {431} planes, respectively, and correspond to the {101}, {211}, {220}, {112}, and {431}, respectively
And
ZnNCN (JCPDSNo. 01-070-4898). A broad peak between 15-25 deg. may be derived from amorphous carbon. However, it should be noted that the presence of a large amount of carbon weakens g-C3N4And the signal strength of ZnNCN. These results indicate ZnNCN, g-C in HPZC3N4And the co-existence of carbon.
In the present invention, FIG. 3 is SEM and HRSEM images of (a) (b) arrayed TRD-ZIF-8 particles and (c) (d) HPZC nanocomposites on different scales; (e) TEM images of HPZC and (f) corresponding HRTEM images in the yellow box region, inset showing the crystal diffraction of ZnNCN; (g) SEM images of HPZC and (h) corresponding EDAX patterns in red circles; (i) is an enlarged SEM image of figure (g) in the yellow box region, and a mapping image of (j) Zn, (k) C and (l) N elements; as shown in fig. 3a and b, the prepared TRD-ZIF-8 nanoparticles showed a Truncated Rhombohedral (TRD) nanostructure with an average particle size of about 210 ± 20 nm. TRD-ZIF-8 formed from ZIF-8 precursors shows a self-assembled superstructure, in which the ZIF-8 particles are aligned in three directions (x, y, z) in space; after the addition of the melamine and calcination at high temperature, the original solid-state array-like nanostructures were destroyed and changed into honeycomb-like porous structures with rough wall surfaces under a nitrogen atmosphere (fig. 3c and d). Gray scale contrast in TEM images (FIGS. 3e and f) shows that the obtained HPZN nanocomposite consists of carbon, ZnNCN and g-C3N4Composition is carried out; HTTEM images of the snapshot mode showed lattice fringes with a spacing of 1.95nm corresponding to the {211} crystallographic plane of ZnNCN, which is consistent with previous XRD results; g-C3N4The layer is evenly distributed on the surface of the HPZN, which may result from thermal decomposition of the melamine (fig. 3 f). Furthermore, it can also be seen from the figure that the interface between ZnNCN/carbon and g-C3N4 is seamless, probably due to the g-C3N4Is formed in situThe result of the process; in FIG. 3h, the uniform distribution of C, N and Zn further indicates ZnNCN and g-C3N4Uniform distribution in HPZC.
In the present invention, FIG. 4(a) is CV curves of commercial ZnO powder, ZC material and HPZC material at a scanning rate of 5mVs-1(ii) a (b) CV curves of HPZC at various scan rates, (e) scan rate V of HPZC material1/2Square root of and peak current IpThe corresponding relation between the two; (c)1A g-1GCD curves of ZnO, ZC and HPZC; (d) GCD curves of HPZC scanned at various current densities, (f) the respective specific capacitances of HPZC; (d) nyquist plots of ZnO, ZC and HPZC; (e) at 7A g-1The current density of (a) ZnO, ZC and HPZC. For comparison, g-C free compositions have been synthesized3N4Of (a) a ZnO/C (ZC) material prepared in the same way as HPZC, except that no melamine is added. The oxidation reduction peaks present in ZnO, ZC and HPZC show their typical pseudocapacitance behaviour. The redox peak position of ZnO substantially coincides with that of ZC. However, in comparison with the CV curve of ZnO, the cathode potential (about 0.35V) and the anode potential (about 0.47V) of HPZC were higher than that of ZnO (about 0.32V and 0.45V), which is probably caused by ZnNCN/g-C in HPZC3N4The energy level of the heterojunction differs from that of ZnO. To date, no research has been reported on electron transport mechanism of ZnNCN system. By consulting a large body of relevant literature, and combining the facts that: the anions in ZnO and ZnNCN show the same charge, but the electronegativity values are different (NCN-group is 3.36, O atom is 3.47), and we believe that the intercalation and deintercalation process of alkali metal potassium ions may be accompanied by the following steps during this faradaic redox process:
ZnNCN+K++e-→ZnKNCN
this process can be described as the rapid passage of cations across the interface between the electrode and the electrolyte, and thus the reversible electrochemical adsorption at the electrode surface. In addition, the HPZC electrodes were scanned at different scan rates (from 1mV s)-1To 30mV s-1) Shows the same symmetric redox peaks, indicating that HPZC has excellent rate capability and phaseFor lower resistances (fig. 4 b). It is well known that at low discharge current densities both surface and bulk play an important role in redox activity, whereas at high discharge current densities surface activity predominates. Thus, the linear relationship between the square root of the scan rate and the peak current density of the anode/cathode further demonstrates that faradaic redox reactions rather than physical adsorption of the electric double layer occur in the process and that the reactions occur primarily at the electrode surface (fig. 4 e).
Constant current charge and discharge curves (GCD) for ZnO, ZC and HPZC as shown in figure 4c, the three non-linear charge curves and their corresponding discharge curves are almost symmetrical, indicating pseudocapacitive behavior in these electrochemical processes. The discharge time of HPZC is 2 times ZC and 4 times ZnO respectively, indicating its potentially superior capacitive capability. The specific discharge capacity of HPZC is 1A g calculated according to the peak area-12916mAh g-1Is obviously superior to many reported Zn base and g-C3N4A base material. High rate capability is another important parameter of supercapacitors. As shown in fig. 5d, the results indicate that the charge and discharge curve shapes are nearly identical at various current densities, indicating that highly reversible redox reactions occur on the electrode surface and that there is a high coulombic efficiency. The specific capacitance of HPZC decreases almost linearly with increasing current density, which may be due to electrode polarization (fig. 4 f). When the current density increased to 10A g-1The specific capacitance of HPZC is 463mAh g-1And 1A g-1Compared with the capacitor, the capacity retention rate is 15.8%, which shows that the HPZC has excellent rate performance.
FIG. 4g is a Nyquist plot of Electrochemical Impedance Spectroscopy (EIS) for ZnO, ZC and HPZC. The graph can be divided into a semicircle at the high frequency region and a straight line at the low frequency region, where the diameter of the semicircle at the high frequency represents the Faraday charge transfer resistance (R) of the redox reaction at the electrode-electrolyte interfacect) Typically related to the surface area and conductivity of the electrode material. As shown in FIG. 4g, no significant half-circle shape appeared in the ZnO and ZC samples, indicating that there was a high resistance during charge transfer. However, it can be clearly observed on HPZCTo a small semicircle, this may be due to ZnNCN and g-C3N4The synergy between the two reduces the charge transfer resistance and optimizes the conductivity of the electrode. In addition, the slope of the low frequency region line is generally equal to the Warburg impedance (R) generated during ion diffusionw) And (4) correlating. The slope of HPZC was greatest among the three samples tested, so RwThe lowest value is probably due to the porous structure and high specific surface area of HPZC which reduces the resistance to ion diffusion during ion diffusion in the electrode.
At 7A g-1The ZnO, ZC and HPZC electrode materials are subjected to durability evaluation of 1,000 continuous deep charge-discharge cycles under current density. As shown in FIG. 4h, after 1000 cycles, the specific capacitance of ZC has a capacitance retention of 91.2% compared to the original capacitance, but the capacitance curve shows a slight increase in 500-800 cycles, probably due to gradual activation of the electrode. Notably, the HPZC curve did not fluctuate abnormally over 1,000 cycles, indicating that the HPZC had good cycle stability. Furthermore, of these materials, HPZC exhibited the highest initial capacitance (990mAh g)-1) And the capacity retention rate after 1,000 cycles was 95.15%, and the decay rate per cycle was only 0.0048%. These results above show that supercapacitors based on HPZC materials can operate stably for long periods at high current densities.
In the present invention, FIG. 5(a) is a CV curve of HPZC// ACASC at different scan rates; (b) GCD curves for HPZC// ACASC at various current densities; (d) the corresponding specific capacitance; (c) HPZC// ACASC at 7A g-1The cycle performance of the following. FIG. 5a shows the CV curves of HPZC// ACASC at various scan rates in the range of 0-1.6V, it is clear that the scan rates do not significantly affect the shape of the CV curves, indicating that HPZC// ACASC can be applied in related devices requiring high work rates and good reversibility. FIG. 5b shows 1-10A g-1And a GCD curve at a potential window of 0-1V, the charge and discharge curves show significant symmetry, which means that the capacitor can provide considerable capacitive characteristics and electrochemical reversibility. In addition, the specific capacitance of HPZC// AC ASC is calculated according to a formula1A g-1，5A g-1And 10A g-1When are respectively 591F g-1，420F g-1，245F F g-1(FIG. 5 d). When the current density is from 1A g-1Increased to 10A g-1The HPZC// AC ASC still had a capacitance retention of 41.2%, indicating its excellent rate capability.
The cycle stability of the asymmetric super capacitor HPZC// AC ASC is 7A g-1The test was carried out under the conditions of (1). As shown in fig. 5c, the HPZC// AC ASC still retained 85.4% specific capacitance after 1,000 charge-discharge cycles compared to the initial capacitance value, corresponding to an average decay rate of 0.014% per cycle, indicating that the HPZC// AC ASC had excellent cycle stability. Furthermore, no significant shape change of the GCD curve was detected in 1,000 cycles, which also demonstrates the electrochemical stability of the asymmetric supercapacitor.
While there have been shown and described what are at present considered the fundamental principles of the invention and its essential features and advantages, it will be apparent to those skilled in the art that the invention is not limited to the details of the foregoing illustrative embodiments, but is capable of other specific forms without departing from the spirit or essential characteristics thereof. The present embodiments are therefore to be considered in all respects as illustrative and not restrictive, the scope of the invention being indicated by the appended claims rather than by the foregoing description, and all changes which come within the meaning and range of equivalency of the claims are therefore intended to be embraced therein. Any reference sign in a claim should not be construed as limiting the claim concerned.
Furthermore, it should be understood that although the present description refers to embodiments, not every embodiment may contain only a single embodiment, and such description is for clarity only, and those skilled in the art should integrate the description, and the embodiments may be combined as appropriate to form other embodiments understood by those skilled in the art.
Claims (8)
1. A preparation method of a low-cost ZnNCN material is characterized by comprising the following steps:
s1: synthesis of truncated rhombohedral zeolite imidazolate framework-8 (TRD-ZIF-8) nanoparticles: will dissolve Zn (CH)3COO)2·2H2Adding 10 ml of O (600 mg) aqueous solution into 10 ml of aqueous solution dissolved with 2-methylimidazole (0.54mM) and CTAB (2.58mM), slowly stirring for a few seconds, after 10 minutes, changing the original transparent solution into white solution, standing for 3 hours at room temperature, centrifuging by using 9000r.p.m, enriching in a 50m L centrifugal tube, then washing the obtained TRD-ZIF-8 nanoparticles by deionized water for 3 times, and then transferring the collected wet particles to a vacuum drying oven to dry at 60 ℃ overnight to finally obtain TRD-ZIF-8 nanoparticles;
s2: cellular porous ZnNCN/g-C3N4Synthesis of (HPZC) nanocomposite the obtained TRD-ZIF-8 nanoparticles (2g) and melamine (2g) were mixed to a homogeneous state under a vortex shaker and then transferred to a 100m L alumina crucible with a lid, which was subsequently placed in a muffle furnace, set to a temperature-raising program to raise the temperature to 550 ℃ at a rate of 3 ℃/min, then maintained at this temperature for 3h, and naturally cooled to room temperature to obtain black HPZC powder.
2. A low cost ZnNCN material preparation method as claimed in claim 1, wherein in S1, double capping ligand of 2-methylimidazole and CTAB is used to synthesize monodisperse TRD-ZIF-8 colloid as the precursor colloid, and the TRD-ZIF-8 precursor colloid contains 6 square {100} crystal planes and 12 hexagonal {110} crystal planes.
3. A low cost ZnNCN material preparation method as claimed in claim 1, wherein, in the S1, the TRD-ZIF-8 is a rhombic dodecahedron having six truncated corners.
4. The method for preparing ZnNCN material with low cost as claimed in claim 1, wherein the TRD-ZIF-8 nanoparticles in S1 are white powder.
5. A low cost ZnNCN material preparation method as claimed in claim 1, wherein in the S2, a muffle furnace is filled with nitrogen.
6. A low cost ZnNCN material preparation method as claimed in claim 1, wherein in S2, melamine is added as self-sacrifice and catalyst.
7. A low cost ZnNCN material preparation method as claimed in claim 1, wherein the S2 is characterized in that the surface of HPZC is covered with homogeneous g-C3N4Nanoplatelets and ZnNCN nanoparticles.
8. A low cost ZnNCN material preparation method as claimed in claim 1, wherein the TRD-ZIF-8 nanoparticles (2g) and melamine (2g) in S2 need to be mixed for 5-10min under a vortex shaker.
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