Patent Application
20230035022
The present invention relates to a novel gold-based porous material, the use of said gold-based porous material as a precursor of a negative active material, the preparation process of said gold-based porous material, a novel gold-based porous material comprising lithium, the use of said gold-based porous material comprising lithium as a negative electrode material, a lithium-ion battery comprising said gold-based porous material comprising lithium, and a process for the preparation of said gold-based porous material comprising lithium.
The invention deals more particularly, but not exclusively, with lithium batteries and microbatteries having improved cycling stability.
With the emergence of connected objects able to collect data, interact with the environment and communicate wirelessly over the internet for a plethora of applications such as healthcare, self-driving vehicles, environmental monitoring and smart manufacturing, thin-film lithium microbatteries have been extensively researched. Thin-film lithium microbatteries are generally formed by two electrodes (positive and negative) separated by an electrolyte. Such a microbattery further comprises metallic current collectors. All the layers of the microbattery are in the form of thin films, for example obtained by PVD (Physical Vapor Deposition) or CVD (Chemical Vapor Deposition). The total thickness of the stack with the packaging layers can be less than 100 µm.
In a microbattery, the negative electrode is generally a metallic lithium negative electrode so as to obtain a lithium-metal microbattery, or it comprises a carbon-based material such as graphite, or an insertion material such as LiNiO2, SnO, indium, or lead oxide, or a crystal growth material (Si, Ge, C, etc) so as to obtain a lithium-ion (or Li-ion) microbattery. The lithium-metal microbatteries usually present the best electrochemical properties in particular in terms of potential and stability of the charging and discharging capacity, but are difficult to fabricate. Moreover, lithium metal is very flammable, air- and water-sensitive, and minute lithium dendrites can form on the anodes when such lithium batteries are rapidly charged, inducing short circuits, causing the battery to rapidly overheat and catch fire. By contrast, lithium-ion microbatteries enable the usual microfabrication techniques to be used, but generally presents lower electrochemical performances on cycling. For example, graphite has been widely used as an anode material for commercial Li-ion batteries, due to the advantages of low cost, low and flat working voltage, and excellent reversibility. However, it cannot satisfy the requirements of higher storage capacity/energy density for thin-film Li-ion batteries due to its insufficient theoretical capacity of 372 mAh/g. Concerning insertion materials, lithium is able to form well-defined intermetallic phases (LixM) with numerous metals M (M=Sn, Mg, Al, Sb, Ge, Si, etc.) at room temperature, which offer much higher lithium-storage capacities than lithiated graphite (LiC6). However, alloying of such large amounts of lithium with these metals to form intermetallic phases is associated with huge volume changes (+ 400%). The large volume changes accompanying lithium insertion and extraction often gives rise to fragmentation of the material and the exposure of a large surface area in contact with the electrolyte, and the formation of the passivating layer on the negative electrode requires from 25% to 40% of the initial capacity, resulting in poor cycling stability.
Sn-based alloys and their oxides have attracted considerable interest because of their high theoretical specific capacities. However, Sn anodes also suffer from a variety of issues like volume expansion (up to 360%), related continuous solid electrolyte interface(SEI) formation, and consequent capacity fading. Such issues are magnified in context of microbatteries, where there are not many amenities for structural engineering due to limited space. Nevertheless, there have been several efforts to utilize them in microbatteries, through alloying with other metal, constructing porous 3D architectures, makinghomogenous/ordered carbon composites, etc. However, most of them still fail to achieve long cyclability and high rate capability.
From US 2013/295461 A1 is known the preparation and the use of a nano-porous gold/SnO2 nanocomposite in a lithium-ion battery. The nanoporous gold/SnO2 nanocomposite is obtained by chemically dealloying a silver-gold alloy so as to form a porous gold structure of bicontinuous channels, precipitating (plating) nanocrystalline tin on the surfaces of the interior walls of the channels of the porous gold structure, and oxidizing the tin so as to form a 100 nm-thick 3D nanoporous gold/ceramic composite. However, cyclability and rate capability are not optimized. For example, the cycling stability for battery performance is meagre (<150 cycles). Additionally, such a structure obtained using top down approach utilizes strong acid (hence difficult for wafer level integration), is time consuming, and lacks flexibility for extension to other porous metal systems.
Thus, the aim of the present invention is to overcome the drawbacks of the cited prior art, and more particularly, to provide a negative electrode material which can lead to a (micro)battery having an improved areal capacity and/or longer life cycle, and which can be confined in an embedded microsystem with limited space available.
The gold-based porous material
A first object of the present invention is a gold-based porous material, preferably in the form of a film, wherein said gold-based porous material comprises a gold porous substrate and a coating comprising a tin gold alloy.
The gold-based porous material leads to a battery having rate capabilitity with flat discharge profile even at high rates, and robust cycling stability. Furthermore, the gold-based porous material can be used as a precursor of an electrode material in miniaturized devices, where size and compactness are critical, and cost is mainly determined by the microfabrication process and not by the minute amount of active material involved.
Indeed, the applicant discovered that this gold-based material when used in a lithium battery can insert lithium and act as an anode active material. It can lead to excellent electrochemical performances, in terms of initial specific capacity, and cycling stability. This result is surprising, bearing in mind that tin is known to trigger considerable volume expansion, leading to a deterioration of the electrochemical performances. Against all expectation, however, it was found that the gold-based porous material of the invention has a limited volume expansion, and leads to a substantial improvement in electrochemical performances of the battery.
In the present invention, the term "substrate" can be defined as a support and by reference to a layer which is deposited on said substrate, the layer being said coating comprising a tin gold alloy. In other words, the thickness of the substrate is greater than the thickness of the coating.
The coating comprising a tin gold alloy preferably represents an outermost layer of the gold-based porous material. In other words, there are no other layer(s) deposited on said coating comprising a tin gold alloy.
The coating comprising a tin gold alloy preferably covers at least partly, and more preferably entirely, the gold porous substrate. In other terms, the gold porous substrate is preferably at least partly, and more preferably entirely, covered with the coating comprising a tin gold alloy. In other terms, the porous surface (i.e. the surface of the pores) of the gold porous substrate is preferably at least partly, and more preferably entirely, covered by the coating comprising a tin gold alloy.
In a preferred embodiment, the coating comprising a tin gold alloy is in direct physical contact with the gold porous substrate. In other words, the gold-based porous material of the invention does not comprise any intermediate coating(s) positioned between the gold porous substrate and the coating comprising a tin gold alloy.
The coating is preferably composed of a tin gold alloy.
Within the gold-based porous material, the porous coating enables reversible interaction with lithium, and the gold porous material provides electronic conductivity.
The tin gold alloy preferably responds to the chemical formula SnAu. In other words, said tin gold alloy is an equiatomic intermetallic compound (i.e. it contains from about 48 to 52 mol% of Au and from about 48 to 52 mol% of Sn, with respect to the total number of moles of the tin gold alloy, which is equal to 100 mol%).
The tin gold alloy has preferably an hexagonal crystal structure.
The coating preferably does not comprise SnOz. In other terms, there is no peak corresponding to SnOz according to XRD analysis.
The coating has preferably a thickness ranging from about 100 nm to 1000 nm.
The gold porous substrate has preferably a thickness ranging from about 5 to 200 µm, and more preferably from about 10 µm to 100 µm.
The gold-based porous material has a porous structure which arises from the porous structure of the gold porous substrate. In particular, the gold porous substrate is obtained by a dynamic hydrogen bubble template (DHBT) method.
The gold-based porous material has preferably a cellular structure or a honeycomb-like structure.
Said cellular or honeycomb-like structure is advantageously a hierarchical structure, that-is-to-say a structure exhibiting a multiple porosity. More particularly, the gold-based porous material of the invention comprises a hierarchical porous network composed of interconnected pores having several sizes, such as macropores, mesopores, and eventually micropores.
The gold-based porous material of the invention can have at least macropores with a diameter ranging from about 0.1 µm to 50 µm, and preferably from about 20 to 40 µm.
The term « diameter » means the mean diameter in number of the whole pores of a given population, this diameter being generally determined by methods well known to a person skilled in the art. The diameter of one pore or pores according to the present invention can be determined by microscopy, notably by scanning electron microscopy (SEM) or by transmission electron microscopy (TEM), and preferably by scanning electron microscopy (SEM).
In one preferred embodiment, the gold-based porous material has an apparent porosity p of at least 80% approximately, and more preferably ranging from 85 to 90% approximately.
Since the gold-based porous material has a porous structure which arises from the porous structure of the gold porous substrate, the gold porous substrate has preferably an apparent porosity p of at least 80% approximately, and more preferably ranging from 85 to 90% approximately.
In the present invention, the apparent porosity p (in %) describes the fraction of void space in said gold-based porous material or on said gold porous substrate. It can be calculated using the following equation:
in which Vp is the pore volume of the gold porous substrate, V is the apparent volume of the gold porous substrate, S is the geometric surface of the gold porous substrate, t is the thickness of the gold porous substrate, w is the weight of the gold used to form the gold porous substrate, and ρAu is the density of gold set at 8.9 g.cm-3. By considering that the gold porous substrate is a 3D-substrate and is represented by three dimensions: L (length), wd (width), and t (thickness), its thickness t is the smallest dimension and the geometric surface is considered to be L x wd. It is noted that the porosity calculations do not take into account the coating of the gold-based porous material.
The gold-based porous material of the invention can have pores with an internal wall structure comprising multi-branched dendrites and nodules.
In one preferred embodiment, the gold-based porous material is in the form of a film.
More preferably, the gold-based porous material is in the form of a macroporous film with nanostructured pore walls.
The gold-based porous material, and preferably the film, can have a thickness ranging from about 10 µm to 100 µm.
The gold-based porous material of the invention is a conductive film, and more particularly an electrically conductive film.
The gold-based porous material of the present invention can be characterized by an aspect ratio (AR), which is also called "roughness factor".
The aspect ratio (AR) corresponds to the ratio of the electrochemical active surface area (EASA) of the gold-based porous material (in cm2) to the geometric surface area of the gold-based porous material (in cm2).
The electrochemical active surface area (EASA) of the gold-based porous material can be calculated as described in Trasatti, S. et al., Pure Appl. Chem., 1991, 63, 711-734, more particularly from the coulombic charge involved in the reduction of gold process (in µC.cm-2).
The aspect ratio (AR) can then be determined as follows:
Accordingly, the aspect ratio (AR) of the gold-based porous material can range from 500 to 1200 cm2/cm2 approximately, and preferably from 700 to 1100 cm2/cm2 approximately.
Since the gold-based porous material has a porous structure which arises from the porous structure of the gold porous substrate, the aspect ratio (AR) of the gold porous substrate can range from 500 to 1200 cm2/cm2 approximately, and preferably from 700 to 1100 cm2/cm2 approximately.
The supported gold-based porous material
The gold-based porous material as defined in the first object of the present invention can be a supported gold-based porous material.
The supported gold-based porous material may comprise the gold-based porous material as defined in the first object of the present invention and a support, said support being coated with said gold-based porous material.
The gold porous substrate of the gold-based porous material is preferably in direct physical contact with the support.
The support can comprise:
The support can further comprise intermediate layer(s) between the substrate and the conductive layer. Said intermediate layer(s) can enhance bonding properties between the conductive layer and the substrate.
Preferably, the support comprises sequentially an oxidized silicon substrate, a layer of titanium, and a layer of gold (i.e. Si/SiO2/Ti/Au support).
The coating of the gold-based porous material is preferably not in direct physical contact with the support.
The support can have a thickness ranging from about 100 µm to 1000 µm, and preferably from about 250 µm to 850 µm.
Use of the (supported) gold-based porous material
A second object of the present invention is the use of a gold-based porous material, preferably of a supported gold-based porous material, as defined in the first object of the present invention as a precursor of a negative electrode material.
Indeed, the gold-based porous material can insert lithium to provide an anode active material, which leads to excellent electrochemical performances, in terms of initial specific capacity, and cycling stability.
The gold-based porous material can thus evolve upon reaction with lithium into a further gold-based porous material comprising lithium which is disclosed hereinafter and which has unexpected electrochemical performances.
A third object of the present invention is a process for the preparation of a gold-based porous material as defined in the first object of the present invention, wherein said process comprises at least the following steps:
The process of the invention is simple, fast, clean, and leads easily to a highly porous gold-based material. This process can also be easily transferable to pilot production line with microelectronic facilities.
Thanks to the dynamic hydrogen bubble template method, it is possible to obtain a highly porous gold substrate which is already defined in the first object of the present invention.
More preferably, the gold porous substrate is in the form of a macroporous film with nanostructured pore walls
The DHBT method is a known electrodeposition at high overpotentials, where metal deposition is accompanied by the evolution of hydrogen (H2) bubbles.
In one preferred embodiment, step i) is performed with constant current (i.e. galvanostatic deposition). Constant current is preferred by comparison with constant potential for facilitating upscaling.
Step i) can involve the use of a solution comprising at least one gold precursor, which can be selected from the group consisting of HAuCl4.3H2O, AuCl3, K(AuCl4), AuBr3, and mixture thereof.
The gold precursor preferably comprises gold ions at the oxidation state +III (i.e. Au3+).
The concentration of the gold ions or Au3+ in said solution preferably ranges from 1 × 10-3 mol/l to 10 × 10-3 mol/l approximately.
The solution can further comprise an acid compound, which can be selected from the group consisting of sulfuric acid, hydrochloric acid, nitric acid, and mixtures thereof.
Alternatively, the solution can comprise a salt such as NH4Cl, which is able to generate H2 as follows: 2NH4 + + 2e- →H2 + 2NH3.
The concentration of the acid compound or the salt in said solution preferably ranges from 1 mol/l to 5 mol/l approximately.
Step i) can be performed at room temperature (i.e. 18-25° C.).
More particularly, step i) is performed by electrodepositing gold, preferably on a support, from a solution as defined above.
The deposition time during step i) preferably ranges from 1 min to 30 min approximately, and more preferably from 10 min to 20 min approximately.
The support can be as defined in the first object of the present invention.
When a support is used in step i), a supported gold porous substrate is obtained.
Advantageously, step i) is carried out by immersing the support in said solution, and applying a given potential vs a reference electrode, or a given current with respect to the geometrical surface area of the support.
Step i) can be performed under a constant current per surface ranging from about 1 A/cm2 to 5 A/cm2, where the surface is the geometrical surface area to which current is applied for deposition.
Electrodeposition is generally carried out with a 3-electrode configuration, namely a platinium counter electrode, a standard calomel electrode as the reference, and a support as defined in the invention such as Si/SiO2/Ti/Au as the working electrode.
During step ii), electrodeposition of tin is achieved without affecting the morphology of the gold porous substrate. Surprisingly, formation of a SnAu alloy occurs during the electrodeposition step ii).
In one preferred embodiment, step ii) is performed with constant potential. This is preferred for controlled reduction of Sn2+ ions on Au surface.
Step ii) can be performed in an acidic medium, preferably at a pH of less than 2, and preferably ranging from 1) to 1.2.
The solution comprising at least one tin precursor is preferably an acidic solution.
The tin precursor preferably comprises tin ions at the oxidation state +II (i.e. Snz2+).
The tin precursor can be selected from the group consisting of SnCl2, SnSO4, Tin (II) oxalate, Tin (II) citrate, Tin (II) ethylhexanoate, and mixture thereof.
The concentration of the tin ions or Sn2+ in said solution preferably ranges from 1 × 10-3 mol/l to 10 × 10-3 mol/l approximately.
To provide an acidic solution, the solution can further comprise an acid compound, which can be selected from the group consisting of sulfuric acid, hydrochloric acid, nitric acid, and mixture thereof.
The concentration of the acid compound in said solution preferably ranges from 0.01 mol/l to 0.1 mol/l approximately.
The deposition time during step ii) preferably ranges from 1 min to 10 min approximately, and more preferably from 3 min to 6 min approximately.
Step ii) can be performed at room temperature (i.e. 18-25° C.).
Step ii) can be carried out by immersing the gold porous substrate in said solution, and applying a given potential vs a reference electrode, or a given current with respect to the surface of the gold porous substrate.
Step ii) is advantageously performed under a constant potential ranging from about -1.5 to -2.5 vs SCE (saturated calomel electrode as the reference electrode).
Electrodeposition is generally carried out with a 3-electrode configuration, namely a platinium counter electrode, a standard calomel electrode as the reference, and a working electrode made of the gold-porous substrate obtained in step i) or the supported gold-porous substrate obtained in step i) such as a Si/SiO2/Ti/Au/Au DHBT electrode.
When a support is used in step i), a supported gold-based porous material as defined in the first object of the present invention is obtained in step ii).
During step ii), deposition of tin on gold porous substrate is homogeneous.
The process can further comprise between steps i) and ii), a washing step i'), so as to wash the obtained gold porous substrate.
Step i') can be performed by using water or dionized water, preferably several times.
The process can further comprise after step i'), a drying step i"), so as to dry the obtained gold porous substrate.
Step i") can be performed by vacuum drying.
The process can further comprise after step ii), a drying step ii'), so as to dry the obtained gold-based porous material.
Step ii) can be performed by vacuum drying.
The support optionally used in step i) can be previously prepared by conventional microfabrication methods.
For example, a Ti/Au thin film can be deposited by evaporation on an oxidized silicon substrate so as to obtain a support comprising a silicon substrate sequentially coated with a layer of SiOz (oxidized silicon substrate), a layer of Ti, and a layer of Au.
The (supported) gold-based porous material comprising lithium
A fourth object of the present invention is a gold-based porous material comprising lithium, preferably in the form of a film, wherein said gold-based porous material comprising lithium includes a gold porous substrate and a coating comprising a lithium tin gold alloy.
The gold porous substrate is as defined in the present invention.
More particularly, the porous structure of the gold-based porous material or the gold porous substrate as defined in the present invention is maintained after incorporating lithium.
The gold-based porous material comprising lithium provides rate capabilitity with flat discharge profile even at high rates, and robust cycling stability. Furthermore, the gold-based porous material comprising lithium can be used as an electrode material in miniaturized devices, where size and compactness are critical, and cost is mainly determined by the microfabrication process and not by the minute amount of active material involved.
Said coating comprising a lithium tin gold alloy is a layer deposited on said gold porous substrate. In other words, the thickness of the substrate is greater than the thickness of the coating.
The coating comprising a lithium tin gold alloy preferably represents an outermost layer of the gold-based porous material comprising lithium. In other words, there are no other layer(s) deposited on said coating comprising a lithium tin gold alloy.
The coating comprising a lithium tin gold alloy preferably covers at least partly, and more preferably entirely, the gold porous substrate. In other terms, the gold porous substrate is preferably at least partly, and more preferably entirely, covered with the coating comprising a lithium tin gold alloy. In other terms, the porous surface (i.e. the surface of the pores) of the gold porous substrate is preferably at least partly, and more preferably entirely, covered by the coating comprising a lithium tin gold alloy.
The coating is preferably composed of a lithium tin gold alloy.
The gold-based porous material comprising lithium has preferably a cellular structure or a honeycomb-like structure.
Said cellular or honeycomb-like structure is advantageously a hierarchical structure, that-is-to-say a structure exhibiting a multiple porosity. More particularly, the gold-based porous material comprising lithium of the invention comprises a hierarchical porous network composed of interconnected pores having several sizes, such as macropores, mesopores, and micropores.
The gold-based porous material comprising lithium of the invention can have at least macropores with a diameter ranging from about 0.1 µm to 50 µm, and preferably from about 20 to 40 µm.
In one preferred embodiment, the gold-based porous material comprising lithium has an apparent porosity p of at least 80% approximately, and more preferably ranging from 85 to 90% approximately.
The gold-based porous material comprising lithium of the invention can have pores with an internal wall structure comprising multi-branched dendrites and nodules.
In one preferred embodiment, the gold-based porous material is in the form of a film.
More preferably, the gold-based porous material comprising lithium is in the form of a macroporous film with nanostructured pore walls.
The gold-based porous material comprising lithium, and preferably the film, can have a thickness ranging from about 10 µm to 100 µm.
The lithium tin gold alloy can respond to the following formula : Li2+xSnAu, in which x is such that 0 ≤ x < 2.
In a preferred embodiment, the coating comprising a lithium tin gold alloy is in direct physical contact with the gold porous substrate.
The gold-based porous material comprising lithium is preferably obtained by submitting the gold-based porous material as defined in the first object of the present invention to at least one charge in a lithium battery.
Indeed, when submitting the gold-based porous material as defined in the first object of the present invention to at least one charge in a lithium battery, lithium is inserted into at least one part of the tin gold alloy, and preferably the whole tin gold alloy, so as to form a lithium tin gold alloy.
More particularly, the porous structure of the gold-based porous material as defined in the present invention is maintained after cycling.
Preferably, the lithium tin gold alloy responds to the following formula : Li2SnAu (i.e. x = 0). This lithium tin gold alloy is very stable and can be used as a negative electrode material.
In one preferred embodiment, the gold-based porous material comprising lithium is a supported gold-based porous material comprising lithium.
The supported gold-based porous material comprising lithium may include the gold-based porous material comprising lithium as defined in the fourth object of the present invention and a support, said support being coated with said gold-based porous material comprising lithium.
The support can be as defined in the first object of the present invention.
A fifth object of the present invention is the use of a gold-based porous material comprising lithium, preferably of a supported gold-based porous material comprising lithium, as defined in the fourth object of the present invention, as a negative electrode material.
The gold-based porous material comprising lithium displays a good cycling stability, whatever the mass loadings of said gold-based porous material comprising lithium.
For example, long-term cycling involves the lithiation of Li2SnAu into further LixSnAu lithiated phases, with an × value varying between 2 to ∼4.
Surprisingly, unlike LixSn, the variation in volume during lithiationdelithiation process of Li2AuSn is very low: first lithiation of Li2AuSn to Li3AuSn has minor volume change of ∼26% with following steps having lower associated volume expansion while transitioning from individual lithiated phases (total calculated volume expansion of 44.4%). Moreover, the void space of the porous structure can accommodate this limited volume expansion of the anode active material, making porous Li2SnAu a very promising anode for long-term cycling microbatteries.
A sixth object of the present invention is a lithium-ion battery comprising:
The positive electrode material can comprise a positive electrode active material, for example selected from the group consisting of lithiated metal oxides (LiCoOz, LiNiOz, LiMn2O4 etc); lithium phosphates (LiFePO4, Li3V2(PO4)3, LiCoPO4, LiMnPO4, LiNiPO4; and active materials of LiMOz lamellar oxide type with M representing a mixture of at least two metals chosen from Al, Ni, Mn and Co, such as LiNi⅓Mn⅓Co⅓O2 (NMC family), LiNi0.8CO0.15Al0.05O2 (NCA family) or LiNi0.5Mn0.5O2.
The positive electrode material can further comprise at least one polymeric binder, and optionally a material conferring electronic conduction.
The electrolyte can be a solid electrolyte, a polymer gelled electrolyte, or a liquid electrolyte.
The electrolyte is preferably a non-aqueous electrolyte.
The electrolyte preferably comprises at least one lithium salt.
The lithium salt can be selected from LiPF6, LiClO4, LiBF4, LiNO3, LiN(SO2CF3), LiAsF6, LiCF3SO3, Li(CF3SO2)3C, LiB(C2O4)2, LiBF2(C2O4), LiN(C4F9SO2)(CF3SO2), and mixtures thereof.
When the electrolyte is a liquid electrolyte, it can further comprise an aprotic solvent.
The aprotic solvent can be selected from ethylene carbonate, propylene carbonate, butylene carbonate, dimethyl carbonate, diethyl carbonate, methyl propyl carbonate, dipropyl carbonate, ethyl methyl carbonate, vinylene carbonate, 1,3-dimethoxyethane, 1,3-diethoxyethane, 1,3-dioxolane, tetrahydrofurane, and mixtures thereof.
When the electrolyte is a liquid electrolyte, the battery can further comprise a separator impregnating said liquid electrolyte.
The separator acts as electrical insulator and allows the transport of ions.
It is noted that in the battery of the present invention, the negative electrode material or the negative electrode material precursor does not require to comprise a polymeric binder and/or a material conferring electronic conduction such as a carbon-based compound.
A seventh object of the present invention is a process for the preparation of a gold-based porous material comprising lithium, preferably of a supported gold-based porous material comprising lithium, as defined in the fourth object of the present invention, wherein said process comprises at least a step of submitting to a charge a cell comprising:
The electrolyte is as defined in the sixth object of the present invention.
The present invention is illustrated in more detail in the examples below, but it is not limited to said examples.
A support was first prepared so as to receive the gold porous substrate.
Accordingly, a Ti(100 nm)/Au(300 nm) thin film is deposited by evaporation on an oxidized silicon substrate which is electrochemically pretreated by cycling the potential at a scan rate of 100 mV s-1 between -0.3 and +1.7 V versus saturated calomel electrode (SCE) in 1 M H2SO4 until a stable voltammogram is obtained. Thus, the obtained support comprises a silicon substrate sequentially coated with a thin layer of SiO2, a thin layer of Ti, and a thin layer of Au.
A solution was prepared by mixing dionized water, HAuCl4.3H2O, and sulfuric acid, such that the concentration of gold ions [Au3+] in said solution is 2x10-3 mol/l, and the concentration of sulfuric acid is 3 mol/l.
Electrodeposition of gold on said support is performed by immersing the support in said solution, and applying at room temperature a constant current of 5 A/cm2, in a 3-electrode configuration, namely a Pt counter electrode, a standard calomel electrode as the reference, and the support previously prepared as the working electrode.
The deposition time during step i) is about 20 min.
A supported porous gold substrate in the form of a film is obtained, washed several times in de-ionized water, and vacuum drying for 30 min.
Then, a solution was prepared by mixing dionized water, SnCl2, and hydrochloric acid, such that the concentration of tin ions [Sn2+] in said solution is 7.5x10-3 mol/l, and the concentration of hydrochloric acid is 0.02 mol/l.
Electrodeposition of tin on the gold porous substrate is performed by immersing the supported porous gold substrate in said solution, and applying at room temperature a constant potential of -2 V vs SCE, in a 3-electrode configuration, namely a Pt counter electrode, a standard calomel electrode as the reference, and the supported porous gold substrate previously prepared as the working electrode.
The deposition time during step i) is about 10 min.
SnAu alloy is thus formed with mass loadings of ~2.9 mg cm-2 of SnAu per min.
The gold-based porous material obtained is further dried to remove any moisture content.
The supported gold-based porous material is in the form of a film having a thickness of 55-75 µm.
SEM images were obtained on a Hitachi S-4800 field emission electron microscope.
The crystallographic structures were analyzed by grazing incidence X-ray diffraction (XRD) measurements on a Bruker D8 Advanced X-ray diffractometer with Cu Kα radiation (1.54184 A°), operating at 40 kV and 40 mA.
The gold-based porous material obtained in example 1 (0.8 cm2) was tested using a Li-ion half-cell (EL-Cell) assembled in a glove box with purified argon, with lithium foil as counter and reference electrode, and glass fiber separator soaked with 1 M LiPF6 in ethylene carbonate (EC) / diethyl carbonate (DEC) (1:1 volume ratio).
Presence of Li2SnAu after long cycling indicates efficient Li+ transport properties in the electrode. The electrochemical lithiation of conformally deposited SnAu alloy not only gives high reversible specific areal capacity, but also results in intermediates, which favor Li+ ion diffusion kinetics, displaying its superiority as a prospective anode material for Li-ion microbatteries.
The gold-based porous material obtained in example 1 (0.8 cm2) was tested using a Li-ion half-cell (EL-Cell) assembled in a glove box with purified argon, with lithium foil as counter and reference electrode, and glass fiber separator soaked with 1 M LiPF6 in ethylene carbonate (EC) / diethyl carbonate (DEC) (1:1 volume ratio).
Extra long-term cyclability of the electrode is evaluated at 3 C rate (
| Number | Date | Country | Kind |
|---|---|---|---|
| 20305185.9 | Feb 2020 | EP | regional |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/EP2021/054673 | 2/25/2021 | WO |
