阅读说明：本技术 制备多孔碳材料的方法和通过这种方法可获得的多孔碳材料 (Method for producing porous carbon material and porous carbon material obtainable by such method ) 是由 J·米肖-伯恩罗希纳 A·库恩 E·科玛洛娃 B·克鲁纳 J·贝克尔 于 2020-03-19 设计创作，主要内容包括：制备具有分级孔隙率的多孔碳材料的已知方法包含步骤：a)提供至少一种碳源和至少一种两亲物类,b)合并碳源和两亲物类以获得前体材料,和c)加热所述前体材料以获得具有模态孔径和孔隙体积的多孔碳材料。为了避免漫长的水热处理并实现碳材料中的孔径、孔径分布和孔隙体积的可调谐性,提议加热步骤c)包含低温处理,其中将前体材料加热到在300℃至600℃之间的第一温度以获得自组装多孔碳质材料,并且其中加热到第一温度包含在0.5℃/min至5℃/min的范围内的第一平均加热速率。(Known methods for preparing porous carbon materials having graded porosity comprise the steps of: a) providing at least one carbon source and at least one amphiphilic species, b) combining the carbon source and the amphiphilic species to obtain a precursor material, and c) heating the precursor material to obtain a porous carbon material having a modal pore size and pore volume. In order to avoid lengthy hydrothermal treatment and to achieve tunability of pore size, pore size distribution and pore volume in the carbon material, it is proposed that the heating step c) comprises a low temperature treatment, wherein the precursor material is heated to a first temperature between 300 ℃ and 600 ℃ to obtain the self-assembled porous carbonaceous material, and wherein the heating to the first temperature comprises a first average heating rate in the range of 0.5 ℃/min to 5 ℃/min.)

1.A method of making a porous carbon material comprising the steps of:

a) providing at least one carbon source and at least one amphiphilic species,

b) combining a carbon source and an amphiphilic species to obtain a precursor material, an

c) Heating the precursor material to obtain a porous carbon material having a modal pore size and pore volume,

wherein the heating step c) comprises a low temperature treatment, wherein the precursor material is heated to a first temperature between 300 ℃ and 600 ℃ to obtain the self-assembled porous carbonaceous material, and wherein the heating to the first temperature comprises a first average heating rate in the range of 0.5 ℃/min to 5 ℃/min.

2. The method according to claim 1, wherein the first average heating rate is set to a value in the range of 0.6 to 2.5 ℃/min.

3. The method according to any one of the preceding claims, wherein the first average heating rate is set according to a predetermined modal pore size and a predetermined pore volume of the porous carbon material,

wherein setting the average heating rate comprises the step of establishing a calibration curve relating the dependence of the pore size and/or pore volume on the average heating rate.

4. The method according to any of the preceding claims, wherein the heating according to step c) is started within 1 hour, preferably within 20 minutes, more preferably within 10 minutes, more preferably within 1 minute of the combining step b).

5. The method according to any of the preceding claims, wherein the cryogenic treatment comprises a temperature residence time of 15 to 240 minutes at a holding temperature lower than the first temperature, the holding temperature preferably being less than 450 ℃, the residence time preferably being in the range of 15 to 60 minutes.

6. The method according to any of the preceding claims, characterized in that the heating of the precursor material in the heating step c) comprises an oxidation stage, wherein the precursor material is treated in an oxidant-containing atmosphere.

7. Method according to claim 6, characterized in that the oxidant-containing atmosphere during heating of the precursor material in the oxidation stage is an atmosphere containing oxygen in molecular form, preferably an atmosphere having an oxygen content of less than 25% by volume, particularly preferably air.

8. Method according to claim 6 or 7, characterized in that the heating of the precursor material during the oxidation stage is carried out at a temperature in the range of 150 ℃ to 520 ℃, preferably 200 ℃ to 470 ℃.

9. Process according to any one of claims 6 to 8, characterized in that the oxidation stage has a duration of 60 to 360 minutes, preferably 120 to 300 minutes.

10. The method according to any one of the preceding claims, wherein the heating step c) comprises a high temperature treatment during which the self-assembled porous carbonaceous material is subjected to a second temperature of at least 700 ℃ and at most 3000 ℃.

11. A method according to any one of the preceding claims, wherein the precursor material has a modal pore size of more than twice the average heating rate of 2 ℃/min when subjected to cryogenic treatment at an average heating rate of 5 ℃/min.

12. A method according to any preceding claim, wherein the amphiphilic species comprises a first amphiphilic compound comprising two or more adjacent ethylene oxide based repeat units, preferably 5 or more, more preferably 7 or more, more preferably 20 or more, or 30 or more, or 50 or more, and up to 1000 adjacent ethylene oxide based repeat units.

13. A method according to any preceding claim, wherein the precursor material comprises a block copolymer of propylene oxide and ethylene oxide containing from 15% to 25% by weight ethylene oxide.

14. A method according to any preceding claim, wherein the precursor material comprises a surfactant comprising 50 to 80% by weight ethylene oxide.

15. The process according to any one of the preceding claims, wherein the carbon source is selected from the group consisting of novolac-type phenol-formaldehyde resins, in particular novolac-type resorcinol-formaldehyde resins or alternatively novolac-type phenol-formaldehyde resins, hydrolysable tannins, lignin, cellulose resins.

16. A method according to any preceding claim, wherein the precursor material is solvent free.

17. A porous carbon material obtainable by the process according to any one of claims 1 to 16, having pores defined by a modal pore size between 50 and 280nm, and having a standard deviation of the modal pore size of less than 50nm, preferably less than 30nm, most preferably less than 25nm, for at least 3 sample numbers.

Technical Field

The present invention relates to a method for preparing porous carbon materials using improved amphiphilic species.

The invention relates in particular to a method for producing a porous carbon material, in particular a macroporous carbon material, comprising the steps of:

a) providing at least one carbon source and at least one amphiphilic species,

b) combining a carbon source and an amphiphilic species to obtain a precursor material, an

c) Heating the precursor material to obtain a porous carbon material having a modal pore size and a pore volume.

The invention further relates to a porous carbon material.

Prior Art

Porous carbon materials are needed, particularly for applications where both electrical conductivity and material permeability are needed in the same substance. Such applications are for example ion transfer batteries, where the electrode material interacts with charge carriers at the solid-liquid interface.

The application of porous carbon is generally based on the nature of the pore structure. Methods of shaping carbon to produce porous carbon materials using a template acting as a negative mould (negative) are known in the art, for example from US 2012/0301387 a 1. Wherein the pore structure of the carbon material is predetermined substantially by the structure of the template material. The template may for example be made of silicon oxide and it is subsequently removed, which amounts to a loss of material and results in a costly and complex process in terms of health and safety.

In another method, microporous, mesoporous, and macroporous carbon materials are obtained by a polymerization-type process. The method involves mixing a carbon precursor and a structure directing agent, typically an amphiphilic molecule, in a solvent. Evaporation of the solvent causes self-assembly, which sets the porosity of the carbon precursor.

An improvement of the polymerization type process is proposed in WO 2014/060508 a1, which avoids a long evaporation step. It describes the formation of a solution of a polymerizable organic monomer and an amphiphilic poly (alkylene oxide) block copolymer as precursors of a macroporous and mesoporous structured material; impregnating a polymer foam with the solution, and subjecting the impregnated polymer foam to a hydrothermal treatment. This thermal treatment initiates the self-assembly of the macroporous and mesoporous structured material and amphiphilic molecules in the polymer foam. The carbon precursor is a phenolic resin obtained by the reaction of formaldehyde and phenol. The block copolymer is a poly (ethylene oxide) having a poly (propylene oxide) moiety. The hydrothermal treatment is carried out in an autoclave at autogenous pressure and temperatures of 40 to 200 ℃ for typically 1 to 4 days. The coated polymer foam is removed from the autoclave and subjected to a carbonization process at a temperature of about 500 ℃ to about 1000 ℃ in an inert atmosphere to thermally crosslink the phenolic resin. The heating ramp during carbonization is controlled to avoid shrinkage of the polymer foam and the rate can be 0.5 ℃ to 10 ℃/min. The carbonized carbon foam is subjected to catalytic graphitization.

The resulting graded carbon material has a bimodal pore size distribution due to porosity from polymer foam and self-assembly, with a major fraction being macropores and a minor fraction being mesopores. The macropores contribute to improved transport properties in electrochemical and other applications.

EP 2921468 a1 describes a method of producing a flexible graphitized carbon foam comprising a structure of interconnected large pores with mesoporous walls. The method comprises providing a carbon source and an amphiphilic species, combining the carbon source and the amphiphilic species to obtain a precursor material, and heating the precursor material to obtain the macroporous carbon material. Carbonization is achieved by heating to a temperature of 500 ℃ to 1000 ℃ at a heating rate of 0.5 ℃/min to 10 ℃/min.

Panbo Liu et al in "Ordered mesoporous carbon particulate from triblock copolymers/novolacs composites" (J. porous Materials (2013)20: 107-) 113 describe a process for producing mesoporous carbon by self-organization using "Novolak" as a carbon precursor and two types of triblock copolymers (Pluronic F127 and P123) as amphiphiles. Pluronic F127 was dissolved in ethanol at a ratio of 1:30 and the solvent was evaporated at room temperature. Calcination was carried out in a tube furnace under nitrogen atmosphere by heating at 500 ℃ and 700 ℃ for 3 hours. The heating rate is 1 ℃/min at temperatures below 600 ℃ and 5 ℃/min above 600 ℃.

WO 2002/12380 a2 describes porous carbon materials and methods for producing them by self-assembly using carbon precursors and amphiphilic species. The dependence of the pore size distribution of the porous carbon material was investigated. The average pore diameter is in the range of 2 to 50nm (or more).

Ordered macroporous carbons with a narrow particle size distribution of about 62nm are described by Soonki Kang et al in the Synthesis of an ordered macroporous carbon with 62nm specific pores, which are not at the external corner of the catalyst, Chem Communications (Camb).21.August 2002; (16): 1670-. Which is produced here by the colloidal crystal templating method.

Technical purpose

The known methods require lengthy hydrothermal treatment and use polymer foams as template materials.

There remains a need to provide improved methods of making porous carbon materials, particularly by polymerization-type processes that do not use solid templates and have short polymerization steps. There is also a need for porous carbon materials having properties most suitable for specific applications.

It is an object of the present invention to provide a method which avoids the disadvantages of the known methods and achieves tunability of pore size, pore size distribution and pore volume in carbon materials having a hierarchical porosity.

Summary of The Invention

The independent claims contribute to achieving at least one of the above objects. The dependent claims provide preferred embodiments of the invention which also contribute to solving at least one of the above mentioned objects.

In the method of the invention, the heating step c) comprises a low temperature treatment, wherein the precursor material is heated to a first temperature between 300 ℃ and 600 ℃, preferably between 300 ℃ and 500 ℃, even more preferably between 450 and 500 ℃, wherein heating to the first temperature comprises a first average heating rate in the range of 0.5 ℃/min to 5 ℃/min.

During low temperature processing, the amphiphilic species decompose and leave the system, and crosslinking of the carbon source (e.g., phenolic resin) occurs. The amphiphilic species helps to guide the formation of a three-dimensional structure from the carbon source during the heating step c), followed by thermal decomposition. Amphiphilic species are considered soft (or sacrificial) templates; the method does not require a hard template material. This makes the process cheaper and more easily scalable.

The precursor material undergoes a self-assembly process that preferably initiates and ends during cryogenic processing. The result of the cross-linking and pyrolysis of the carbon source/amphiphilic species mixture is a self-assembled porous carbonaceous material. The final heating temperature during cryogenic processing in the temperature range of 300 ℃ to 600 ℃, referred to herein as the "first temperature", is determined for a particular formulation to be the temperature at which decomposition of the amphiphile is sufficiently complete. In most cases, the first temperature is between 300 ℃ and 500 ℃, even more preferably between 450 and 500 ℃. Once the first temperature is reached, a self-assembled porous carbonaceous material is obtained and the low temperature treatment is terminated so that the average heating rate is no longer critical to the pore size and pore size distribution. Thus, the average heating rate may or may not change during any further heating of the self-assembled porous carbonaceous material.

The low temperature treatment produces a solid self-assembled porous carbonaceous material. The decomposition of a particular amphiphilic material can be determined by thermogravimetric analysis of a sample of the material. The parameters of the thermogravimetric analysis were as follows:

initial mass of sample about 10-20mg

Constant heating rate of 5 deg.C/min from 25 deg.C

Argon flow 20ml/min.

Here, it is determined that complete decomposition is sufficient if the residual mass Δ m (in%) of the sample is at most 40% of the initial weight. The remaining mass was determined by [ { (sample mass at temperature T-apparent mass from buoyancy at temperature T)/initial sample mass } × 100], shown as percent [% ].

When the temperature at which "sufficiently complete" decomposition is achieved in the low temperature heating process, the "first temperature" is reached and the heating process may be terminated, but it is generally and preferably continued until the temperature at which complete decomposition is achieved is reached.

The average heating rate is determined as the quotient of the temperature interval between the starting temperature and the first temperature, wherein the starting temperature is the temperature of the precursor material after combining the components according to step b) and before the start of the heating process. A suitable starting temperature is 25 ℃.

Generally, the modal pore size, pore size distribution and pore volume of the final carbon material depend on the individual constituents and compositions (hereinafter also referred to as "specific formulations") of the specific precursor material formed in the combining step b). It has surprisingly been shown that the heating rate during low temperature treatment also has a significant influence on the pore size, pore size distribution and pore volume. Generally, as the heating rate increases, the pore volume increases as well as the pore size and pore size distribution. Thus, the final modal pore size and the final average pore volume and the final pore size distribution may vary within the specific ranges allowed for a particular precursor. Thus, according to one aspect of the invention, the average heating rate in the low temperature treatment step is set to a value in the range of 0.5 ℃/min to 5 ℃/min to adjust and tailor the modal pore size, pore size distribution and pore volume of the final carbon material.

The porous carbon material can be used in a number of technical applications. Preferred applications are as follows: an electrochemical cell; fuel cells, in particular hydrogen fuel cells, in particular proton exchange membranes; a capacitor; an electrode; and a catalyst. Preferred electrochemical cells in this respect are lead-acid cells and lithium-ion cells. A preferred fuel cell in this regard is a hydrogen cell. A preferred capacitor in this respect is an electric double layer capacitor. Each application may require different properties of the porous carbon material, particularly different pore volumes and pore diameters. The tunability of pore size and pore volume according to the present invention enables tailoring of the carbon additive for a particular application. For example, optimal values for the pore volume and the modal pore size may be determined for a particular application, such that values to be established for the average pore volume and the pore size may be specified and predetermined for the porous carbon material used for that particular application.

A predetermined modal pore size, pore size distribution and predetermined pore volume can be achieved if appropriate formulation of the precursor material happens to be known. On the other hand, the invention allows the use of formulations that only partially meet the requirements, since this can be handled in a way that meets the predetermined values during the low-temperature treatment. Thus, according to a preferred embodiment of the method, the first average heating rate is set in dependence on the predetermined modal pore size, pore size distribution and pore volume of the porous carbon material.

If the heating rate dependence of pore size and pore volume is not known for a particular formulation, the setting of the average heating rate may comprise the step of establishing a calibration curve relating the dependence of pore size and/or pore volume on the average heating rate.

To establish a calibration curve, it may be sufficient to determine the modal pore size, pore size distribution and/or pore volume at two or more different heating rates, for example, heating rates defining a range of 0.5 ℃/min to 5 ℃/min, so that the modal pore size, pore size distribution and/or pore volume at intermediate heating rates can be extrapolated or calculated.

The most preferred modal pore size of the porous carbon material is in the range of 50 to 280 nm. For pores with diameters in the range of 10nm to 10,000nm, a total pore volume in the range of 0.4 to 1.75cm is preferred³In the range of/g; and the most preferred pore size distribution is as narrow as possible. If the standard deviation of the modal pore size is less than 50nm, preferably less than 30n, for at least 3 sample numbersm, most preferably less than 25nm, a narrow pore size distribution is considered.

The precursor material obtained in step b) may comprise, in addition to the carbon source and the amphiphilic species, a cross-linking agent, a solvent and/or a dispersant. The amphiphilic species may be a dispersant, or the dispersant may be one of several amphiphilic species. The combining step typically requires mixing of the components that form the precursor materials. The mixing step is preferably performed before the heating step.

In one embodiment, the heating according to step c) is started within 1 hour, preferably within 20 minutes, more preferably within 10 minutes, more preferably within 1 minute of the combining step b).

In a preferred embodiment, the cryogenic treatment comprises a temperature residence time of 15 to 60 minutes at a holding temperature lower than the "first temperature" defined above, preferably less than 450 ℃, most preferably less than 350 ℃.

The residence time may be set at a temperature at which conversion of the precursor material, such as evaporation or decomposition of the components, occurs, particularly at high heating rates. It was found that if the temperature is kept below 200 ℃ and the residence time is less than 15 minutes, the residence time has little effect on the pore size and pore volume.

During which crosslinking and pyrolysis of the carbon source (e.g., phenolic resin) and amphiphilic species occurs. The carbon source decomposes during the heat treatment and forms carbon in yields of typically 30-50 wt%. The amphiphilic species almost completely decompose and act as pore formers, which reduces the overall carbon yield of the mixture (e.g., to 15-33 wt%). The crosslinking and pyrolysis steps are typically carried out in an inert atmosphere at atmospheric or slightly sub-atmospheric pressure. This is because it is presumed that the oxidizing atmosphere may cause carbon burn-out at high temperatures. The crosslinking and pyrolysis steps can also be carried out under reduced pressure or under vacuum, for example under an absolute pressure of less than 500 mbar, preferably less than 300 mbar.

It has surprisingly been found that the carbon yield (expressed in%) in the precursor material can be increased by at most about 10% (absolute value) if the heating step c) comprises an oxidation stage, wherein the precursor material is treated in an atmosphere comprising an oxidant. The oxidizing agent may contain oxygen, and preferably contains at least one selected from the group consisting of oxygen, carbon dioxide and waterAnd (4) dividing. One possible, but non-limiting explanation for the higher yield is that oxygen from the oxidant is incorporated into the polymer network. However, this incorporation does not allow oxygen to pass as CO or CO during further carbonization₂Is removed from the product so as to reduce the overall carbon yield, but instead the incorporated oxygen stabilizes the polymer network during crosslinking and this stabilization reduces further carbon loss.

Thus, in a preferred embodiment, the heating of the precursor material in step c) comprises an oxidation stage, wherein the precursor material is heated in an oxidant-containing atmosphere.

It has been found to be advantageous that the oxidant-containing atmosphere during heating of the precursor material in the oxidation stage may be in a molecular-containing form (as O)₂) Preferably an atmosphere having an oxygen content of less than 25% by volume, particularly preferably air.

The "oxidation" of the atmosphere results in the oxidation of the precursor material, particularly the carbon source. The intensity (rate) of the oxidation reaction depends on the temperature. At the lower temperature limit mentioned above, the intensity is high enough to avoid long heating times. At the upper temperature limit, the oxidant-containing atmosphere is changed and further heating is carried out under an inert gas. The upper temperature limit may (but need not) correspond to the "first temperature" for the low temperature process at the same time.

The heating of the precursor material during the oxidation stage is preferably carried out at a temperature in the range of from 150 ℃ to 520 ℃, more preferably from 200 ℃ to 470 ℃.

The degree of oxidation also depends on the content of oxidizing agent (e.g. oxygen in molecular form) in the oxidizing atmosphere and the duration of the oxidation phase.

It has proven advantageous for the oxidation stage to have a duration of 60 to 360 minutes, preferably 120 to 300 minutes.

In a preferred embodiment, the heating step c) comprises a high temperature treatment during which the solid porous precursor material is subjected to a second temperature of at least 700 ℃ and at most 3000 ℃.

During the high temperature treatment, carbonization is completed and graphitization of the carbonized material may occur, if still necessary. Graphitization takes place at a temperature in the range of 1200 to 3000 c, more preferably in the range of 1500 to 2800 c, most preferably in the range of 1700 to 2500 c.

The low temperature treatment and the high temperature treatment may be performed in a single heating step without any cooling and without any lengthy residence time, such as 1 to 4 days of hydrothermal treatment as known in the art. On the other hand, once carbonization has started, the initial heating rate dependence of the pore size disappears, so the heating step can be interrupted and divided into two or more temperature ramps, one for the initial ramp, then cooled and possibly mechanically treated, then the final heating ramp up to any final treatment temperature. This provides additional flexibility in view of possible production processes.

The tunability of the pore size and pore volume according to the invention is especially suitable if the precursor material is very sensitive to the heating rate, i.e. where the pore size and pore volume show a strong dependence on the heating rate.

With particular regard to this high sensitivity to heating rate, the precursor material preferably has a modal pore size of more than twice the average heating rate of 2 ℃/min when subjected to cryogenic treatment at an average heating rate of 5 ℃/min.

The amphiphilic species is preferably present in the precursor material in the form of micelles and three-dimensional structures, and it has both hydrophilic and lipophilic behaviour. Preferred amphiphiles comprise a first amphiphile comprising two or more adjacent ethylene oxide based repeat units, preferably 5 or more, more preferably 7 or more, more preferably 20 or more, or 30 or more, or 50 or more, and up to 1000 adjacent ethylene oxide based repeat units.

The first amphiphilic compound preferably comprises more than 10 wt% of ethylene oxide based repeating units, preferably more than 20 wt%, more preferably more than 30 wt%, most preferably more than 40 wt%, especially at most 90 wt%, based on the total weight of the first amphiphilic compound. It may comprise further repeating units, preferably based on a monomer selected from: one of propylene oxide, butylene oxide, ethylene, propylene and butylene, preferably propylene oxide. The ethylene oxide repeat unit has the formula- (CH)₂CH₂O) -. The glycidyl repeating unit has the formula- (CHCH)₃CH₂O)-。

The carbon source may be a carbon compound comprising a ring, especially an aromatic ring having one or more hydroxyl groups attached thereto.

In a preferred embodiment, the carbon source is selected from Novolac type phenol-formaldehyde resins (Novolac type phenolic formaldehyde resins), in particular Novolac type resorcinol-formaldehyde resins or alternatively Novolac type phenol-formaldehyde resins, hydrolysable tannins, lignin, cellulose resins. The carbon source is a single material or a mixture thereof containing two or more carbon source materials.

The ratio of the amount by weight of carbon source to the amount by weight of amphiphilic species is for example in the range of 10:1 to 1:10, preferably in the range of 8:1 to 1:5, also preferably in the range of 5:1 to 1:3, more preferably in the range of 5:2 to 1: 2.

Precursor materials meeting this requirement may comprise a block copolymer of propylene oxide and ethylene oxide containing from 15 to 25% by weight ethylene oxide, especially 20% by weight ethylene oxide, or alternatively a surfactant containing from 50 to 80% by weight ethylene oxide, and/or the precursor material comprises an aqueous resorcinol-formaldehyde novolac resin, a solid resorcinol-formaldehyde novolac resin or a solid phenol-formaldehyde novolac resin.

Solvent-free precursor materials are preferred. Organic solvents are generally flammable or toxic, and aqueous solvents can only be removed with great effort.

The porous carbon material of the present invention can be obtained by the above-described method. Characterized in that it contains pores defined by a modal pore size between 50 and 280nm, and the standard deviation of the modal pore size is less than 50nm, preferably less than 30nm, most preferably less than 25nm for at least 3 sample numbers.

Test methods and Definitions

The following test methods were used in the present invention. In the absence of a test method, the ISO test method of the feature to be measured, which was newly disclosed before the earliest filing date of the present application, was employed. Standard Ambient Temperature and Pressure (SATP) is used, such as a temperature of 298.15K (25 deg.C, 77 deg.F.) and an absolute pressure of 100kPa (14.504psi, 0.986atm) in the absence of unique measurement conditions.

Mercury porosimetry (pore size and pore volume)

Specific pore volume, cumulative pore volume and porosity of different pore diameters were measured by mercury porosimetry. Mercury porosimetry analysis was performed according to ISO15901-1 (2005). In this test, mercury is pressed into the pores of the porous material under external pressure against a counter surface tension (external pressure). The force required is inversely proportional to the pore size, so that in addition to the cumulative total pore volume, the pore size distribution of the sample can also be determined.

With a modal aperture of 140.2nm and 924.4mm³Porous glass spheres of pore volume/g (from ERMFD122 reference material of BAM) Thermo Fisher Scientific PASCAL 140 (low pressure up to 4 bar) and PASCAL 440 (high pressure up to 4000 bar) were calibrated and soid Version 1.6.3(26.11.2015) software (both from Thermo Fisher Scientific inc.). The pressure is continuously increased or decreased during the measurement and is automatically controlled by the instrument operating in the PASCAL mode, the speed being set to 8 for the pressing in and 9 for the pressing out. The density of Hg was evaluated using the Washburn method and corrected for actual temperature. The value of the surface tension was 0.48N/m and the contact angle was 140 deg.. The sample amount was about 25 to 80 mg. The sample was heated to 150 ℃ in vacuo for 1 hour before starting the measurement.

Mercury porosimetry is suitable for measuring relatively large pores (meso-porous to macroporous). Mesoporous refers to pores with a pore size between 2 and 50nm, macroporous refers to pores with a pore size above 50nm, and microporous refers to pores with a pore size less than 2 nm.

"Modal pore size" refers to the pore size in the mercury intrusion curve. Here, it means a pore diameter exhibiting the maximum value of the logarithmic differential pore volume in a graph in which the logarithmic differential pore volume (dV/D (logd) is plotted against the pore diameter measured with a mercury porosimeter, where V represents the mercury intrusion volume and D represents the pore diameter), and is based on the volume. The dV/d (logd) curve is a function of the probability density of the aperture. The "modal pore size" corresponds to the pore size at which the abundance is greatest. In particular, the most frequent pore size can be measured by the above-described method.

_{total ext}Gas adsorption (Total specific surface area (BET) and external surface area (BET))

BET measurements were carried out according to DIN ISO 9277:2010 to determine the specific surface area of the particles. NOVA 3000 (from Quantachrome) working according to the SMART Method (transduction Method with Adaptive dosing Rate) was used for this measurement. As a reference material, Quantachrome Alumina SARM Catalog No.2001 (13.92 m in the multipoint BET method) was used²/g) and SARM Catalog No.2004 available from Quantachrome (214.15 m in multipoint BET method)²In terms of/g). Filler rods were added to the reference and sample tubes to reduce dead volume. The test tube was mounted on a BET apparatus. Measurement of saturated vapor pressure (N) of Nitrogen gas₂4.0). The sample was weighed into a glass tube in an amount to completely fill the tube with the fill rod and produce the lowest dead volume. The sample was kept at 200 ℃ for 1 hour under vacuum to dry it. After cooling, the sample weight was recorded. The glass test tube containing the sample was mounted on the measuring device. To degas the sample, the material was evacuated to a final pressure of 10 mbar at a selected pumping speed without sucking it into the pump.

The degassed sample mass was used for this calculation. For data analysis, novawn 11.04 software was used. Multipoint analysis with 5 measurement points was performed and the total specific surface area (BET) obtained_total) In m²The ratio of the specific component is given in terms of/g. The dead volume of each cell was determined once before the measurement using helium (He 4.6, humidity 30 ppmv). The glass test tube was cooled to 77K using a liquid nitrogen bath. For adsorption, at 77K, it has a wavelength of 0.162nm²N of the molecular cross-sectional area of₂4.0 was used for this calculation.

The contributions from micropores and the remaining pores at relative pressures greater than 0.1 (i.e. the mesoporosity, macroporosity and external surface area contributions) were distinguished and the micropore surface area (BET) was calculated according to ISO15901-3:2007 using empirical t-plot method (empirical t-plot method)_micro) And micropore volume. Selecting low pressure isotherm data points until a cutoff p/p₀Disclosure of the inventionOften up to 0.1p/p₀To determine the linear region (linear section) of the t-plot. Data point selection is verified by obtaining a positive C constant. Micropore volume was determined from the ordinate intercept. The micropore specific surface area (BETmicro) can be calculated from the slope of the t-plot.

Determination of the external specific surface BET by subtracting the specific surface of the micropores from the total specific surface_ext，BET_ext＝BET_total-BET_micro。

Thermogravimetric analysis (TGA)

The thermogravimetric analysis was performed on a Netzsch TG 209F1 Libra thermal analyzer with Netzsch Proteus software. TG209 standard sample holder and standard type K thermocouple for sample temperature measurement were used. A typical initial sample mass is about 15-30 mg. No preconditioning step was performed prior to the measurement.

When the flow rate is 20cm³Al is recorded when the temperature in the measuring chamber is increased from 25 ℃ to 1000 ℃ at a heating rate of 5 ℃/min under an argon atmosphere (purity 5.0)/min₂O₃Sample mass in crucible.

To correct for buoyancy variations during the experiment, inert Al charged with similar volumes were recorded separately under similar conditions₂O₃Powdered Al₂O₃The apparent mass of the crucible and subtracted from the measured signal.

The data collected is plotted as the measured percent mass remaining (which is determined by [ { (sample mass at temperature T-apparent mass from buoyancy at temperature T)/initial sample mass } × 100], shown as percent [% ]) (on the primary y-axis) and the sample temperature T (on the secondary y-axis) vs time from the thermocouple, or the curve can take the temperature directly as the x-axis.

Brief Description of Drawings

The invention will now be further elucidated with reference to the drawing. The drawings and the accompanying description are exemplary and should not be taken as limiting the scope of the invention.

Figure 1 shows a thermogravimetric analysis of a particular amphiphilic material,

figure 2 shows an SEM image of the surface of a material prepared according to the present invention using a first formulation and a heating rate of 0.67 c/min,

figure 3 shows an SEM image of the surface of a material prepared according to the present invention using a first formulation and a heating rate of 1 c/min,

figure 4 shows an SEM image of the surface of a material prepared according to the present invention using a first formulation and a heating rate of 2 c/min,

figure 5 shows an SEM image of the surface of a material prepared according to the present invention using a first formulation and a heating rate of 5 c/min,

figure 6 shows an SEM image of the surface of a material prepared according to the present invention using a second formulation and a heating rate of 0.67 c/min,

figure 7 shows an SEM image of the surface of a material prepared according to the present invention using a second formulation and a heating rate of 1 c/min,

figure 8 shows an SEM image of the surface of a material prepared according to the present invention using a second formulation and a heating rate of 2 c/min,

figure 9 shows an SEM image of the surface of a material prepared according to the present invention using a second formulation and a heating rate of 5 c/min,

figure 10 shows a graph of the dependence of pore volume on heating rate for four different formulations,

figure 11 shows a graph of the dependence of modal aperture on heating rate for four different formulations,

FIG. 12 shows a graph of the dependence of the total BET surface area on the heating rate for four different formulations,

figure 13 shows a graph showing the dependence of the external BET surface area on the heating rate for four different formulations,

FIG. 14 shows a graph of standard deviation vs heating rate for modal apertures for four different formulations, an

Figure 15 shows the results of thermogravimetric analysis (TGA) of a particular precursor material heated to 1000 ℃ in argon and in synthetic air.

Examples

In a preferred embodiment, the porous carbon material is made by combining solid pellets of an aqueous resorcinol-formaldehyde resin (novolac resin) or a resorcinol-formaldehyde/phenol-formaldehyde resin (novolac type) and an amphiphilic molecule (block copolymer or surfactant or (non-ionic) emulsifier or combination of amphiphilic molecules). The components are mixed to obtain a homogeneous precursor material.

The heat treatment thereof is carried out in one step in an inert atmosphere (nitrogen or argon). The heating rate from room temperature to 400 ℃ is 0.67 ℃/min to 5 ℃/min. Thereafter heating is resumed to the desired final temperature of 600 to 3000 c, preferably above 900 c. The porous carbon material thus obtained is cooled, removed from the furnace and mechanically crushed/ground to the desired particle size.

The formulation of the composition of the particular precursor material sets the initial parameters of the resulting porous carbon material. Additional tuning of the modal pore size and pore volume can be achieved by heating ramps during the critical self-assembly step.

To understand the heating rate dependence of the carbon material, a series of heating ramps (9 total) were performed on four different precursor materials (formulations). The experimental data are summarized in table 1.

TABLE 1

r_H1Is the average heating rate from room temperature

T1 is the first holding temperature

t1 is the first residence time at the first holding temperature

r_H2Is a heating rate from a first holding temperature

T2 is the second holding temperature

t2 is the second residence time at the second holding temperature

In the low temperature region (here up to 400 ℃), heating ramp 9 provides an average heating rate of 0.67 ℃/min, heating ramp 8 provides an average heating rate of 2 ℃/min, heating ramp R6 provides an average heating rate of 5 ℃/min, and the remaining heating ramps have an average heating rate of 1 ℃/min

Various residence times were tested to see if potential processes were important to the final product, especially in the temperature range where conversion of the precursor material might be expected to occur.

It was found that the effect of residence time on pore size and pore volume was not as great as the initial heating ramp up to 400 ℃. Furthermore, it was demonstrated that the heating rate dependence of the modal pore size and pore volume is only present during low temperature heat treatment up to about 500 ℃ and starts earlier than carbonization of the precursor material.

Table 2 lists the tested formulations No.1 to No.4:

TABLE 2

The "weight ratio" given in the fourth column refers to the ratio of the total mass of the respective substances. 779W 50 Askofen resin is for example a novolak type waterborne resorcinol-formaldehyde resin and contains 50 wt% solids resin and 50 wt% liquid phase. Thus, 5 parts by weight of this substance corresponds to 2.5 parts by weight of resin.

For each formulation, four crucibles were filled in each run to observe the temperature uniformity of the furnace and the reproducibility of the formulation.

The graph of figure 1 shows the results of thermogravimetric analysis of the amphiphilic material up to 1000 ℃ under argon. The residual mass Δ m (in%) of the sample compared to the original sample mass is plotted on the ordinate against the heating temperature T (in ℃). The heating temperature is a linear function of the heating rate kept constant at 5 ℃/min until a final temperature of 1000 ℃ is reached.

Curve a in fig. 1 shows the mass evolution vs temperature of the sample and curve B shows the mass flow rate for an argon purge (constant at 20 ml/min). Weight loss can be explained by the sustained thermal decomposition of the amphiphilic species. Accordingly, up to a temperature of about 200 ℃, the loss of mass of the amphiphilic material is small. At temperatures above 500 ℃, the mass loss is almost complete, indicating that the amphiphilic soft template material is nearly completely decomposed. The amphiphilic material lost about 98.85% of its initial weight when treated to 1000 ℃.

At a temperature of about 380 ℃, the amphiphilic species has lost 60% of their initial weight. In this particular case, the temperature of 380 ℃ represents the "first temperature" of the low-temperature treatment process. Most of the amphiphilic species decompose during the cryogenic treatment to set the porosity of the remaining material until the "first temperature" is reached. At higher temperatures, the porosity does not change significantly, so further temperature treatment is not required with such a slow heating ramp.

The scanning electron diagrams in fig. 2 to 5 show impressively that the porosity properties of the carbon material made from the precursor material of formulation No.1 vary with the heating rate during the low-temperature treatment. At a heating rate of 0.67 deg.C/min (FIG. 2), the porosity is significantly lower than at a heating rate of 5 deg.C/min (FIG. 5). In each SEM photograph, the scale bar had a length of 10 μm.

The scanning electron diagrams in fig. 6 to 9 show the same dependence of formulation No. 2. The pore size dependent effect is less pronounced than formulation No.1, since the formulation itself generates smaller pores. In each SEM photograph, the scale bar still had a length of 10 μm.

In the graph of fig. 10, the initial heating rate r during the low-temperature treatment in the temperature interval of 25 ℃ to 400 ℃ is compared_HThe average pore volume V for each of the four formulations is plotted (in ℃/min)_p(in cm)³In terms of/g). The pore volume increases slightly as the heating rate increases.

In the graph of fig. 11, the initial heating rate r during the low-temperature treatment in the temperature interval of 25 ℃ to 400 ℃ is compared_HThe respective modal pore diameters D of the four formulations are plotted (in ℃/min)_p(in nm). When the heating rate was increased to above 1 ℃/min, the modal pore size showed a sharp increase. Formulations 1 and 3 showed the clearest dependence between pore size and heating rate. A heating rate of 5 ℃/min results in a pore size that is more than twice the heating rate of 2 ℃/min, and a heating rate of 2 ℃/min results in a pore size that is more than twice the heating rate of 1 ℃/min.

The values plotted in figures 10 and 11 are the average of four replicates for each formulation.

Figures 12 and 13 are graphs showing the recipe for all four tested formulasBET surface area, including Total BET (BET)_totalIn m is²In/g) and external BET (BET)_ext.In m is²In g) to initial heating rate r_HDependence (in ℃/min). Values plotted are the average of four replicates for each formulation. Total BET_totalIt did not show a continuous change with heating rate change, but when the heating rate was increased above 1 ℃/min, the external BET of most formulations_ext.Showing a decrease.

Determination of the external specific surface BET by subtracting the specific surface of the micropores from the total specific surface_ext，BET_ext＝BET_total–BET_micro。

Figure 14 shows the sample standard deviation vs ramp number of modal pore size (in nm) obtained for four crucibles of each formulation (see table 1).

The standard deviation of the sample is

Where { x₁、x₂、…,x_NAnd is the measured value of the modal pore size of each sample.Is the average of the modal pore size (sum of the sample values divided by the number of measurements N, where N is 4).

The standard deviation increases with increasing initial heating rate (5 ℃/min formulation ramp 6 and 2 ℃/min formulation ramp 8). Formulation ramp 5 has no hold period and goes from room temperature up to 900 ℃ at 1 ℃/min. The ramp with the lowest standard deviation is formulation ramp 3, which is held at 325 ℃ for 30 minutes. The low standard deviation values obtained from the claimed cryogenic treatment represent narrow pore size distributions.

The precursor material mixture typically contains a novolac resin and an amphiphilic surfactant. An example of a novolak resin isPN320(Allnex) examples of surfactants arePF20(Clariant) orPE/L64 (Croda). The resin to surfactant ratio is typically 5 (1.5-9).

FIG. 15 shows the use of Alnovo PN320 andresults of thermogravimetric analysis (TGA) of a 5:5 mixture of PF20Synperonic PE/L64, wherein the mixture was heated separately to 1000 ℃ in an atmosphere of argon (curve 151) and synthetic air (curve 152). Similar to fig. 1, the residual mass Δ m (in%) of the sample compared to the original sample mass is plotted on the ordinate against the heating temperature T (in ℃). The heating temperature is a function of the heating rate of 3 ℃/min up to a temperature of 600 ℃ and a function of the heating rate of 5 ℃/min up to a final temperature of 1000 ℃. The TGA curves 151, 152 of samples heated in different atmospheres have quite similar profiles up to about 400 ℃. At 400 ℃, the argon pyrolysis sample (151) showed a large mass loss and its slope subsequently decreased. The air pyrolyzed sample (152) had a plateau in the temperature range of about 400 to 450 c where the mass loss of carbon was about 10 wt% lower than the mass loss of the argon pyrolyzed sample (151). However, when oxidation occurs at temperatures above 450 ℃, the mass loss is greatly increased. The difference in carbon yield at 450 ℃ is indicated by distance bar 153.

For the product composed ofPN445 andprecursor materials made from mixtures of PF20(5:5) revealed similar thermogravimetric analysis results. The mass loss of the sample crosslinked in an argon atmosphere at a temperature of 450 ℃ is several times greater than that of the sample crosslinked in synthetic air15% by weight.

Based on these thermogravimetric analysis results, an experiment was designed to confirm that the increase in carbon yield (decrease in carbon mass loss) during pyrolysis can be attributed (transferred to) to the synthesis of a porous carbon material by the method of the present invention. Make itPN320 andthe 5:5 mixture of PF20 was crosslinked and pyrolyzed up to 600 ℃ with the following heating ramp profile: at 20-350 deg.C, 0.5 deg.C/min → 350-. At a temperature of 450 ℃, the decomposition of the amphiphile is sufficiently complete and the atmosphere is switched from containing oxidant to containing only inert gas. This temperature (450 ℃) is both the maximum temperature of the oxidation stage (in which the precursor material is heated in an oxidant-containing atmosphere) and the "first temperature" of the low-temperature treatment.

In the first test, the mixture was pyrolyzed in a nitrogen atmosphere. In a second test, the mixture was heated in an open retort (restore) to ensure an oxidant-containing atmosphere (air) up to 450 ℃ during pyrolysis. Once this temperature was reached, the flask was closed and a nitrogen stream was introduced to prevent further oxidation of the carbonaceous material by air at the higher temperatures (450-. Table 3 shows a comparison of the yields of porous carbon material after pyrolysis in nitrogen and in air (up to 450 ℃).

TABLE 3

The sample treated in nitrogen had a yield of 30.3 wt% at 600 ℃, while the air crosslinked sample had a higher yield of 32.7 wt%. The statistical error in yield is typically 0.5 wt%. In fact, the yield of the carbonized air crosslinked sample was 3.4 wt% greater than the nitrogen crosslinked sample. This improvement is even greater than the 2.4 wt% yield gain found at 600 ℃. This means that oxygen stabilizes the polymer network and can maintain this improvement. In the first experiment the air was replaced by nitrogen at a temperature of 470 ℃. It is possible by other experiments to show that even higher carbon yields can be obtained by process optimization, e.g. by switching to an inert atmosphere at 400 ℃ and lower. Crosslinking and pyrolysis produce a macroporous carbon material.

Cross-linking and pyrolysis of the precursor material mixture results in a composite having greater than 0.4cm³A cumulative pore volume in g and a macroporous carbon of modal pore size between 50-280 nm.