New video from SciVPro has been published this
New video from SciVPro has been published this
New video from SciVPro has been published this
The perovskite field has been subject to an incredible momentum and is moving forward very fast. Here is a selection of interesting papers published in January.
In 2009, Tsutomu Miyasaka published in JACS a paper reporting halide perovskite as a DSSC sensitizer. The editorial of Nature Energy in January reminds us of the greatest advances since then.
Garten and co-workers from NREL published in Science Advances last month this paper confirming ferroelectricity in MAPI single crystals. Ferroelectricity in halide perovskite is still a subject under debate, with many papers claiming the effect may or may not be screened in these materials. This paper claims confirmation of the existence of a ferroelectric behaviour in MAPI perovskites. The strength of this paper is the use of different techniques to draw the conclusion and may give rise to ferroelectricity control within perovskite, to tune the Fermi level or electrical response.
Wei et al. published in Nature Energy probed layered perovskites to understand the dynamics of energy transfer in these systems. They observe energy transfer on the scale of the picosecond. They show narrowband exciton routing with very high PLQY. Thus they produce luminescent solar concentrators with a fourfold enhancement in internal concentration.
For a couple of years, more and more papers have been reporting the use of 2D halide perovskites. I’ve found it quite confusing. These paper usually describe slabs of corner-sharing BX₆ octahedra, separated by large organic cations. In most cases, these materials are processed as thin films or large (about 1cm×0.5cm×0.5cm) single crystals. In fact, what is said to be 2D (or quasi-2D) perovskites is always a Ruddlesden-Popper, a Dion-Jacobson or an Aurivillius phase, that are all bulk materials.
In the 2D materials community, and more generally in solid state physics, we describe two-dimensional atomic crystals as sheets thinner than the Fermi wavelength (or in some cases the De Broglie wavelength). In these materials, the electrons are allowed to move in two directions, but are confined in the c direction. Several names describe
In the perovskite community, the study of these so-called two dimensional (or quasi-two-dimensional) halide perovskites hasn’t lead, to my knowledge, to the report of any 2D electron gas. It would be very surprising to observe some of these, given the high density of defects in these materials that make large mono layers hard to achieve.
I propose to use the terminology layered perovskite, to differentiate this from the 2D materials, and hopefully allow those two different fields to move beyond current limitations and come together. No one would imagine talking about 2D carbon to describe graphite. Nonetheless, this is exactly what the perovskite community has started to do.
As well, it’s been reported “1D perovskites” and “0D” perovskites. I suggest using “perovskite
Addendum (24 January 2019): Aron Walsh tweeted yesterday this commentary from Joachim Breternitz and Susan Schorr, highlighting their view about what could or couldn’t be defined as a perovskite. This reads:
In particular for the Ruddlesden–Popper phases, we would like to draw the attention of the reader to the original publications of Ruddlesden and Popper where the authors point out that these compounds contain perovskite layers. Perovskite layers are, however, not layered perovskites and no matter how small the change in semantics may appear, the latter would not be correct.Joachim Breternitz and Susan Schorr
Indeed, what has been named layered perovskites in the oxide perovskite community are compounds of the form La2-xBaxCuO₄, Sr2VO₄, LaSrMO₄ where alternating A-site cation are considered as different layers. This is also quite confusing given that layered materials are usually considered as materials forming strong bonds in two directions and a weaker bond in the third direction, as in lead iodide (PbI₂), molybdenum disulphide (MoS₂) or tungsten diselenide (WSe₂). However, the discussion remains open!
Metal halide perovskite present outstanding electronic properties. One hypothesis that explains those properties is the presence of a very strong bulk Rashba effect, reportedly the greatest among any other materials. This blog post introduces the Rashba effect in halide perovskites, explaining the origin of both the reported static and dynamic effects. Finally, I give some details about the theory from Byschkov & Rashba and about the photogalvanic effect.
Metal halide perovskites (structure ABX₃ where X is a halide) have been subject to an unparalleled interest in the materials science community for the past 6 years. One reason for such an interest is their incredible long carrier diffusion lengths of up to 1 micron in polycrystalline films and as high as tens of microns in single crystals, driving outstanding photovoltaic performance. It has also been observed a strong optical absorption, with incredibly low non-radiative recombination rates, leading long carrier lifetimes — up to tens of microseconds. These parameters are surprisingly high for the unavoidable presence of defects in solution-processed polycrystalline films. This differs from the image of conventional semiconductors in which defects and impurities are
Therefore, many fundamental questions underlying these outstanding optoelectronic properties still remain unanswered. Particularly, the origin of carrier mobilities, of long lifetimes and very low rate of non-radiative recombination need further studies. In fact, different hypotheses have been proposed to explain both the origin of long-carrier lifetimes and low rate of non-radiative recombination:
The Rashba effect would explain both the long carrier lifetimes and the intriguing low-rate of non-radiative recombination.
Let’s start with the example of MAPI (perovskite phase where the A-site cation is methylammonium – CH₃NH₃, the metal, lead, and the halide is iodide), that is the most studied halide perovskite. In this structure, the presence of heavy atoms such as lead or iodine introduces spin-orbit coupling, that, along with inversion-symmetry breaking in the crystal, the electrons behave as if they were subject to an effective magnetic field which due to the spin-orbit coupling (SOC). This results in a momentum-dependent splitting of electron bands commonly referred to as the Rashba splitting. This effect yields a lifting of the degeneracy in k-space, inducing the shift of both the valence band (VB) maxima and conduction band (CB) minima, away from the high symmetry points of the Brillouin zone. This results in an indirect band gap, as shown in the figure below. Particularly, the splitting of the conduction band suppresses the rate of band-to-band recombination of charge carriers that has been proposed to be the origin of increased carrier lifetimes.
The inversion-symmetry breaking can happen either in the bulk of non-centrosymmetric crystals, or at surfaces and interfaces. It has been originally theorised for two-dimensional electron gases (2DEG, see below). There are two main mechanisms that lead to the Rashba effect, breaking the inversion symmetry in the bulk of the MAPI crystals, one is static, the other dynamic.
First, lead iodide sub-lattice can distort from a set of ideal corner-sharing octahedra (tetragonal structure). As recently suggested (Rakita et al, PNAS 2017), this forms a non-centrosymmetric phase that is the source of the static Rashba effect. Particularly, the room-temperature of MAPI is the tetragonal I4/mcm phase, which is not centrosymmetric, that may not be subject to spin-splitting. In other phases, when the orbitals with spin-orbit splitting are not subject to inversion symmetry, the spin-orbit coupling causes a spin-dependent shift of the electronic bands along the k-direction. The double spin-degenerate band reportedly splits into two bands, shifted in k-space by k₀. Thus, the bandgap becomes slightly indirect, as the optical transition become spin-dependent. Particularly, these effects are responsible for a high Rashba parameter, whose intensity has been reported to be ɑR = 2 E₀ / k₀ = 7± 1 eV Å in the orthorhombic perovskite and 11 ± 4 eV Å in the cubic
This effect on the optical transition can be probed with a photogalvanic effect (see below), expected if coherent spin transport takes place on length scales large enough for spin-polarised currents to get through devices. That’s what Niesner and co-workers reported with their systematic study of the circular photogalvanic effect in MAPI single crystals.
The spin-splitting also causes a minimum of energy at the central high symmetry point, of depth E₀. Particularly, in the room temperature tetragonal phase, they observed (Niesner et al, 2016) a circular photogalvanic effect for excitations 110meV below the direct optical gap, indicating that the transitions between spin-polarised electronic bands happened below the direct gap.
Circular dichroism has also been observed in pump-probe spectroscopy, and spin dependence of the charge dissociation has been reported. This may allow for the creation of perovskite-based spintronic devices.
Recently, it has been proposed the existence of a dynamical Rashba effect, allowing for quantification of its magnitude. In fact, the cubic perovskite lattice allows high mobility of the organic dipolar cation that locally
Particularly, the soft nature of the lead-iodide bond allows it to be easily deformed under symmetry-breaking, due to the important fluctuation of the organic cations. At high temperature, this local structural disorder induces the dynamical Rashba effect.
The amplitude of this dynamical effect is very similar to the one that is observed for bulk Rashba systems (static Rashba). Hence, a change in the direction of the current, that is associated with the circular photogalvanic effect at the orthorhombic-tetragonal phase transition, demonstrates that this dynamical effect has two different physical origins in the two phases.
At room temperature, the perovskite is tetragonal, thus the energy splitting between spin-polarised transition and direct optical transition increase with the temperature, as well as the amplitude of the circular photogalvanic effect. Both
The orthorhombic lattice is centrosymmetric. Hence, the bulk Rashba effect is impossible in this low-temperature phase. Thus the temperature-independent circular photogalvanic effect that has been measured is attributed to the reduced symmetry at the surface and interfaces.
Finally, this Rashba effect explains the reported indirect-direct band gap and thermally activated radiative recombination in tetragonal MAPI (Hutter et al, Nature 2018). Particularly, this provides an evidence for the spin-splitting mechanism at elevated temperatures, that should be seen in materials with inversion symmetry that contains heavy elements like lead, and exhibit soft phonon modes.
The Rashba mechanism described herein would potentially be very attractive for both optoelectronics and spintronics. Notably, the exploration of Rashba physics has now been at the heart of the growing research field of spin-orbitronics that focuses on the manipulation of non-equilibrium materials properties using SO coupling.
The reported Rashba effect in metal halide perovskites could pave the way towards new applications, thanks to the unique transport properties that emerge with such an effect. The tremendous field of spin manipulation using spin-orbit coupling could notably lead to a quantum spin Hall effect, to the possibility of creating spin-orbit Torque, spin-orbit Qubits or spin transistors or even study topological insulators and Majorana fermions…
I’m looking forward to reading papers involving halide perovskites in the fantastic field of spin manipulation. Given this, I now expect perovskite to have a pivotal role in modern physics with marvellous applications.
In non-centrosymmetric crystals, the electronic energy bands are split by spin-orbit coupling. In those systems with structural inversion symmetry breaking, SOC becomes odd in momentum p, that, in two-dimensional electron gas (2DEG), reduces to a linear dependence of the Rashba effect in momentum.
For electrons moving in an electric field (even in the absence of external magnetic field), and effective magnetic field is felt by the electrons in their frame of motion. This is called the spin-orbit field, and couples to the electron’s magnetic moment. When inversion symmetry breaking is present, this SO field becomes odd in electron momentum. Let’s take the mathematical expression to better understand this:
Let’s chose an electron with momentum p moving across a magnetic field B. This electron experiences a Lorentz force in the direction perpendicular to its motion, F= -ep×B/m and possesses a Zeeman energy μB σ·B, where σ is the vector of Pauli spin matrices, m the mass of the electron, e its charge, and μB is the Bohr magneton.
If this electron moves across an electric field E, it experiences the effective magnetic field Beff ~ E×p/mc² in its rest-frame (c is the speed of light), and this field induces a momentum-dependent Zeeman energy called spin-orbit coupling
ĤR = ɑR/ℏ * (z × p) · σ
Here, ɑR is the Rashba parameter. This formula has been derived for 2D plane
The spin of electrons and holes in solid state systems has been intensively studied in quantum
Under illumination with a circularly polarised light, it is possible to generate a transformation of the photon angular momentum into a translational motion of free charge carriers. To better understand this phenomenon, one can imagine it as the electronic analogue of a
The cover photo shows ARPES on beamline 5-4 at SSRL. Courtesy of SLAC National Accelerator Laboratory. ARPES is a technique allowing to observe the band dispersion.
The perovskite field has been evolving so rapidly that it’s been hard to follow all its evolution. Here I give a list of the papers published last year that I think advanced perovskite research and marked the important research milestone. I also extended this list to other papers I’ve particularly enjoyed reading in 2018.
There are currently huge debates about whether metal halide perovskites present ferroelectric properties, as do their oxide counterparts. In a Science paper this summer, Heng-Yun Ye et al. proposed metal free halide perovskite compositions showing ferroelectricity properties. This could trigger new ferroelectric studies in this field.
Layered halide perovskites (usually called “2D-perovskites”)
The Rashba effect had been theorised for a long time to happen in halide perovskites, as it would explain both the high electron diffusion length and low recombination rates. In May, Kyle Frohna et al. reported in a Nature Communications paper a static Rashba effect, induced by the breaking of inversion symmetry in some phases. In their PNAS paper published in September, Daniel Niesner and co-workers provided experimental evidence of a dynamical Rashba effect, characterised by spin-splitting at elevated temperature.
In September, Roald Hoffman and Maarten Goesten published in JACS a theoretical study: “Mirrors of Bonding in Metal Halide Perovskites”. In this article they investigate the different interactions within CsPbBr₃, providing new insights both on the hydrogen bonding and the band structure of this incredible material.
If I had to highlight a review about tandem solar cells this year, that would be undoubtedly Tomas Leijtens’ in Nature Energy, published this summer. He and his co-workers discuss the latest developments in perovskite tandem solar cells and give perspectives to move this kind of research
Ming-Min Yang et al. reported in Science a flexo-photovoltaic effect in some non-centrosymmetric crystals like strontium titanate SrTiO₃ (a structural analogue of the photovoltaic halide perovskite CsPbBr₃). This effect is different from the typical photovoltaic effect originating from p-n junction. The presence of such an effect may allow boosting the power-conversion efficiency of solar devices. In my mind, this might provide further explanations of the already incredible solar conversion properties of halide perovskites, in the presence of the debated ferroelectric properties in these compositions.
On a completely different ground, Pablo-Jarillo-Herrero from MIT presented in two Nature papers the presence of superconductivity in twisted graphene bilayers. According to many observers, this is likely to be the breakthrough of the year, in a field that hasn’t seen such enthusiasm since the discovery of graphene in 2004.
These results took everyone in the community by surprise because although superconductivity had been previously observed in heterostructures made with graphene, they always involved another superconductive material. Here, they’ve shown that bilayers, rotated with an angle of 1.1° allowed the generation of a non-conducting state (Mott insulator) that can be turned into a superconducting state if charge carriers are added to the graphene system, under 1.7K. Interestingly, this paper caught attention because superconductivity appears in a much simpler system than what has been studied previously (cuprates), making graphene bilayers a possible Rosetta stone for the understanding of unconventional superconductivity.
In the semiconductors community, Eve Stenson from Max Plank Institute reported in PRL that a beam of positrons could boost semiconductor luminescence, more than 100 times that what an electron beam could provide. This suggests that the electron antiparticles may annihilate on collision with particles in the semiconductor, boosting the efficiency of luminescent devices.
Another paper that sparked a huge interest on Twitter has been Thapa & Pandey’s claim of the discovery of a superconducting material at -37°C. This claim has been largely criticized, notably by Brian Skinner, who discovered a weird noise pattern.
A large part of condensed matter chemistry is moving toward machine learning to be able to predict new molecules. In the perovskite field, this has been highlighted at MRS Fall by Marina Leite who proposed to build an open-access library, useful for all the perovskite community. With a much larger materials science background, Aron Walsh and collaborators published a Nature review detailing tools and principles for this emerging field.
Early this year, new kind of chemical reactions has been intended. Whereas typical chemical reactions are carried out with a number of molecules about the Avogadro number, a reaction on the atomic scale has been encountered by these
I started this blog by being deeply convinced of the need to tackle climate change, and that the latest research advances in solar energy could be of great help in this domain.
Without a surprise, climate science has continued to evolve this year, providing new proofs of the disaster that already started. In a Nature paper, Springmann and co-workers presented options for keeping the food system within environmental limits. This convinced me to turn vegetarian to preserve life on earth as we know it.
Finally, the mainstream press has been enthusiast about a paper from two of my friends published in Nature Physics this summer. With a groundbreaking experiment, they provide new insights
The cover photo has been taken from this Youtube video.
Happy new year to all my readers! I’m sure 2019 will bring new exciting advancement in the field. At a minimum, there’ll be new stability developments and increased efficiency of halide perovskite solar cells. There also will be more and more fundamental studies. I’ll try to keep pushing with more new posts this year.
I’ve been carrying research in two different labs in 2018 so it’s been a bit hard to manage writing blog posts, engage with the community and curate a twitter feed. Now that I’m carrying out my own research at the University of Manchester for the next 3 years, things will go smoothly.
This year I’d like to talk here about Rashba-Dresselhaus effects and spin-physics within perovskites, the use of machine learning to predict perovskite properties and materials, and the all expanding field of so-called “2D perovskites” (even though I prefer the terminology layered perovskites to describe those systems). More to come pretty soon.
Finally, here is a video on Scientific Video Protocols about the history of perovskite photovoltaics, featuring Prof Henry Snaith:
Tandem solar cells are a very promising technology that would allow to overpass the Shockley-Queisser efficiency limit for photovoltaic devices. They can be manufactured by stacking two solar devices, one of low band-gap (to absorb low-energy photons), on top of which is placed a high band-gap absorber (that would absorb the high-energy photons, therefore reducing the heat losses inside the solar cell). Mixed halide perovskite are particularly interesting for the assembly of those tandem solar cells, because compositional arrangements can allow acute band-gap tuning.
In perovskite of the form ABX₃, where X is a mixture of halide ions, generally iodide and bromide, researchers have observed a phase segregation under illumination. In fact, the halide ions form clusters inside the perovskite, leading to a hysteresis cycle in the J-V characteristic curves and other instabilities. This issue is currently one of the most important to address before perovskite can hit the market.
Here is a collection of a few papers on the subject, that I have found particularly interesting:
The cover photo is taken from Bischak et al. in ACS Energy Letters. It shows the evolution of perovskite films emission wavelengths (blue = homogeneous film, yellow = iodine clusters).
Tuning the active materials for the engineering of tandem solar cells is an arising field of research among the perovskite community. In this post, I present the main targets of tandem solar cells engineering: band-gap tuning. Then, I showcase two solutions that have been reported by students I am currently working with.
Metal halide perovskites, of the form ABX₃ (where A can be methyl ammonium, formamidinium, caesium or a mixture of both, B lead or tin and X a halide, typically iodide, bromide, or mix of both), are gaining much attention for thin film photovoltaics, thanks to their long carrier diffusion lengths, their defect tolerance enabling versatile solution (or vapour) processing and a very strong optical absorption. The efficiencies of so-called perovskite solar cells are comparable to the one achieved with the incumbent silicon technologies.
Two market solutions can be proposed for perovskites: either challenging the incumbent silicon or use perovskite as a layer that can be stacked on top of the silicon cell, boosting its efficiency. For this later solution, a wide band-gap needs to be achieved with perovskites, in order to maximise the energy collection. In fact, the silicon solar cells have a very low band-gap. It means that every incident photon having an energy higher than the silicon band-gap will be collected, but the energy difference (the energy higher than the band-gap), will be dissipated as heat loss. Thus the need of a layer that would extract a portion of higher voltage photo-generated carriers will be valuable in order to overpass the fundamental efficiency limit for single junctions solar cells, commonly known as the Shockley-Queisser limit.
Because the perovskite has a tunable band-gap, that can be controlled with halide substitution (for example), they tend to be considered as the best solution for more efficient solar cells. Their ability to be solution-processed or vapour-deposited would allow benefiting high quality scalable inexpensive integration on existing devices. State of the art perovskite-silicon tandem solar cells achieved record efficiencies of 23.6% for monolithically integrated cells, and 26.4% for mechanically stacked configuration. Attempts to make perovskite-perovskite tandem solar cells have also been tried with record efficiencies of 18.5%, but these rely largely on the development of more efficient and more stable low-end-gap perovskite absorbers (1.1 to 1.3eV). The PCE figures are expected to grow significantly with a deeper understanding of the materials.
All these aspects make the development of perovskites for tandem devices an active field of research.
In order to achieve higher band-gap solar devices, compositional tuning of the solar cells has been tried by the Materials Science & Engineering group led by Mike McGehee. His students, Bush et al. describe their result in their paper: “Compositional Engineering for Efficient Wide Band-Gap Perovskites with Improved Stability to Photo-induced Phase Segregation”.
They explore various compositions of hybrid perovskites of the form FA1-xCsxPb(I1-yBry)3. They investigate the performance of solar cells as well as the photo-stability by varying the composition between formamidinium (FA) and caesium (Cs) in the perovskite A-site and between iodide and bromide on the X-site. With that, they show that increasing the concentration in caesium into the solid-solution thin film results in higher VOC and greater photo-stability, as it raises the bandgap. This can be compared with the previously known raise of bromide, that yields higher band-gap, with a fewer photo-stability and VOC.
That article might be particularly important in the development of high-efficiency perovskite tandem solar cells, as the authors identify stable compositions with high band-gap (1.68 to 1.75eV), that demonstrate high device efficiencies.
Variation of those A-site cation changes the band-gap. Prasanna et al. proposed an interpretation in their JACS paper: “Band-gap Tuning via Lattice Contraction and Octahedral Tilting in Perovskite Materials for Photovoltaics”. By exploring both lead and tin on the B-site, they allow different octahedral sizes, as the length of the metal-halide bond changes. In this paper, they show that the use of a smaller A-site cation can distort the perovskite lattice in two different ways: either by tilting the BX₆ octahedra (pictured on the right) or by contracting the lattice isotropically (depicted on the left). The first effect yields to a change of the metal-halide orbital overlap, that varies the band-gap. The second results in a relative contraction that increases the orbital overlap, thus cutting down the band-gap.
Those two strategies can be achieved with partial substitution of the large FA cation with the smaller Cs. With lead halide perovskites, this results in octahedral tilting but with tin-based materials to lattice contraction, due to the smaller size of the tin.
Hence the authors provide a framework to tune the band-gap as well as the valence and conduction band positions by controlling the A-site cation composition.
In order to achieve high efficiency perovskite-based tandem solar cells, it is necessary to adjust the band-gap of the top cells. As shown in this post, this can be improved through control of the cation composition, resulting in higher band-gaps. These results will, for sure, be needed for future high-efficiency solar panels.
The cover picture is from Michigan Engineering on Flickr. Scheme from Prasanna et al.
Some months ago, I had conversations with some researchers to propose them a graduate project proposal that could be done within the scope of a PhD. I have been admitted at the University of Manchester to carry out this project under the supervision of Prof Sir Andre K. Geim and Prof Irina V. Grigorieva. I have decided to publish this proposal here, as it may give ideas to other students.
In the past five years, metal halide perovskites have drawn huge excitement from the photovoltaics research community because of their high power conversion efficiency. The 2D-structured perovskite demonstrate promising stability properties [Wang 2017], large carrier mobility [Brenner 2016], strong light absorption, superb photo- and electro-luminescence [Stranks 2017, Dou 2015] and strong quantum confinement effects. These properties have enabled LEDs [Yuan 2016, Friend 2017], lasers and photodetectors [Li 2017] powered with perovskite materials.
In the realm of 2D materials, the use of stacked layers, forming so-called van der Waals heterostructures, has empowered in-band structure engineering [Geim 2013] to create tunnel junctions with unparalleled performances. To date, the best materials for building such heterostructures have been graphene, frequently achieving superior performances for surface science, endowing it with favourable electronic, optical, thermal and mechanical properties [Novoselov 2016].
This proposal aims to create heterostructures based on layered 2D perovskite with graphene sheets. This challenge has been addressed with thin film perovskites and has shown excellent FET performance but poor stability in ambient conditions [Cheng 2015]. Here, two dimensional perovskite may be a promising alternative for enhanced stability and attractive electronic and optical properties [Yang 2016]. Moreover, 2D perovskite can be bound to graphene sheets by various techniques as I present in this research proposal.
I propose to investigate various bonding strategies between 2D perovskite layers and graphene sheets to create stacks and assess their properties. Various synthetic methods as well various bond types may be explored: van der Waals, ionic, covalent and hydrogen bonds [Liu 2012].
The question to be addressed is: to what extend does the nature of the bonding between graphene sheets and 2D perovskite layers influence the optoelectronic properties of the stack?
Graphene and perovskite space groups are different therefore stacking the two materials in a heterostructure will induce lattice strain. However, interface modelling studies [Guo 2017] showed that this kind of heterostructure can be stable.
Van der Waals heterostructures will be manufactured via physical deposition under vacuum. Ionic heterostructures will be developed by doping the graphene structure to make it more or less electroattractive. Hydrogen and covalent bonding will involve structure modification, enabled by the 2D perovskite where the crystallographic structure is not influenced by the cation [Weidman 2016]. Thus both the excitonic energy and the bandgap will stay unchanged. However, it may require the modification of graphene via grafting organic cations molecules on its surface.
Van der Waals heterostructures of graphene and perovskite have been theorised [Guo 2017]. It has been predicted that the electronic structure of both 2D halide perovskite and graphene will be preserved after stacking. To my knowledge, there has never been any attempt to carry out the practical experiment.
With grafting methods, I anticipate that recombination rates may be reduced by transferring charge carriers from the perovskite to the graphene layers. This may lead to higher efficiency solar cells. Finally, I anticipate that the different binding approaches will tune the position of the Fermi level by modifying the interface between the two layers. The orbital overlapping may be altered, as well as the electronic configuration at the interface.
Characterisation of the manufactured materials would be carried out with X-Ray Diffraction techniques, as well as observations with Scanning and Transmission Electron Microscopy. The optoelectronic properties would be explored via photoluminescence spectroscopy; charge transport with microwave conductivity measurements; surface states with transient absorption spectroscopy; and the band structure with Compton and Raman scattering.
The first year of the PhD would be dedicated to exploring the property range through methodical testing, with the aim of identifying the most efficient process for keeping the heterojunction stable. During the two following years, I would focus on the optoelectronic properties of the manufactured materials. The various bonding investigations would be carried out simultaneously in order to be able to compare results.
I believe that combining two outstanding materials may lead to unparalleled results. Covalent bonding will affect the graphene conjugation system, therefore compromising some of its properties. I suppose that non-covalent interactions may preserve all of its electronic properties. The afforded assembly with two-dimensional perovskite structures may certainly give rise to a new class of layered semiconductors, as the assembly with the bulk perovskite counterparts already gave astonishing performances [Cheng 2015].
I am convinced that the perovskite is a class of materials that has the potential to impact the future of modern civilisation. My investigations may lead to meaningful industrial opportunities with great impact on energy saving and energy collection.
You may have realised that there were two shortcomings in this proposal. How would you manage to fix it?
The cover picture is from Charles van Meter on Flickr.
When we think of the long term future for perovskite solar cells, there are basically two strategies. The first is to enhance their efficiency by making tandem solar cells. The second is to create flexible devices with roll to roll technologies, as industrials currently do with organic solar cells. This latter strategy has an enormous potential, but shows an important issue: to be scalable, we absolutely need enhanced stability, especially at the interface between the electrodes and the active layer. One way to enhance this stablity is to use carbon nanotubes (CNTs).
To present CNTs for solar cell applications, let me introduce Dr Severin N. Habisreutinger (@sevnhabis) who, during and after his Ph.D. at the University of Oxford, worked extensively with carbon nanotubes for perovskite applications. He has now ben awarded the Director’s fellowship at the National Renewable Energy Laboratory (NREL) in Golden, Colorado, for investigating the nature of CNT-perovskite interface.
To imagine a (single-wall) carbon nanotube think of a sheet of paper being rolled up such that it forms a tube. If you replace the sheet of paper with a monoatomic sheet of carbon atoms (known as graphene) you get a carbon nanotube. Commonly the diameter is around one nanometer (4-5 orders of magnitude smaller than the diameter of a single strand of hair). CNTs exhibit several very interesting properties. On one hand, their mechanical strength make it one of the strongest materials we know. In addition they are chemically quite resilient, which means they do not readily form strong chemical bonds with other materials. This is important, in particular, at interfaces with very reactive materials. And finally, the property which makes them particularly interesting for photovoltaic application is their extraordinary charge-transport characteristics, above all the high charge carrier mobility. This means that a charge carrier can travel a long distance through a CNT before it is lost when it recombines with a charge carrier of the opposite polarity. The basic idea how to exploit this particular property is to use CNTs at the interface with an absorber material in which light generates charge carriers. These photogenerated carriers can then be rapidly transferred away from the interface through the CNTs which act like high-speed channels for those charges moving them away from a region, namely the illuminated absorber, in which they can readily recombine and would thus be lost.
A challenge for using CNTs is the fact that they have the tendency to form bundles, which makes it more difficult to process them out of solution and it negates some of their excellent electronic properties. A strategy which successfully overcomes this challenge is wrapping individual CNTs with conjugated polymers, known from organic electronics.
With this approach, CNT thin films can be used in photovoltaic applications, such as perovskite solar cells, for example as hole-selective layers. As opposed to conventional solar cells, charge separation in a perovskite device does not rely on an internal electric field, instead charge selective contacts introduce a driving force for electrons on one side, and holes on the other side.
For CNTs, the mechanism leading to the collection of holes is a good alignment of the valence band of the CNTs and the HOMO of the perovskite active layer. Another aspect is their ability to block the electrons. The combination of these characteristics makes them a good hole-transport layer. Severin explains:
Actually, the exact underlying mechanism is still a bit contested, but we know that when CNTs are in contact with ambient oxygen, they become more p-type therefore there is a higher concentration of holes available in the carbon nanotubes. That makes them an interesting hole-transporting material which is the main aspect most recent publications are currently looking at.
However, in some conditions, he explains, PCBM can be used to dope the material and make it more n-type:
I think there is a lot of potential in using CNTs both as anode and cathode with the active layer sandwiched in between. Looking forward, I would imagine that quite a few researchers will look into using CNTs in such a capacity, but for now we still need to answer a range of questions.
Specifically for the use in perovskite devices, we would like to know: what exactly happens at the interface in terms of charge transfer kinetics? Do the metallic-type CNTs have a positive or a negative effect? What about hybrid layers comprising CNTs? We expect that the answers will lead to interesting new concepts and ideally to more stable and more efficient contacts.
Large-scale use of CNTs in this capacity still needs a lot of work to be done to better understand the interface interactions. Guess what? That is exactly what Severin is looking at. Therefore we expect a deeper understanding leading to higher quality charge selective layers and more stable solar cells.
Our discussion evolved to more futuristic ideas, such as direct inclusion of CNTs into the perovskite absorber. The basic idea is to extract photogenerated charges even more directly thus further reducing recombination losses. At the moment, it seems hard to tell whether this would be beneficial since the charge transport in perovskite is already remarkably good. But we imagined grafting carbon nanotubes on perovskite crystals to avoid surface recombination. In fact, this concept of a heterojunction is essential for organic solar cells because the electron diffusion length is limited, and one needs to provide a direct conducting path between the active layer and the CNT electrode. As mentioned above, this is less of a concern for the perovskite bulk. However, it could also be an approach to avoid recombination at grain boundaries, if CNTs were to penetrate a perovskite film. There is one interesting study, Severin mentioned, by Prof Horváth and co-workers from EPFL who tried some interesting in that direction. In fact, they grew a perovskite single crystal around carbon nanotubes, achieving a vertical protogenic inclusion of CNTs into a MAPbBr₃ single-crystal.
We also talked about using graphene layers:
In general, if you have a pristine graphene layer, it will have better charge transport characteristics than a CNT film. There is a common issue with the charge transfer between individual carbon nanotubes within a conductive film. The inter-tube junctions create obstacles for the charge-carriers often due to the formation of Schottky barriers, limiting the transport of charges on a macro-scale. That is not present in pristine graphene. However, there is still a big challenge for graphene: fabricating it large scale. One interesting way to implement graphene nonetheless is to make a hybrid layer of graphene flakes and CNTs. This way we could use the excellent electrode properties of graphene in combination with the charge selectivity of CNTs.
Thus, we might expect synergistic effects from the combination of both graphene and CNTs. That may be the kind of idea to explore in the future, especially combined with other nanostructured materials.
The cover photo is from NASA Goddard Space Flight Center on Flickr.
Degradation of perovskite has been a well-developed topic on this blog. Actually, it represents one of the greatest challenges to address. Scientists try to tackle the degradation issues from many approach angles. Here I showcase two articles I’ve read in the past months about how the lattice evolves and how it leads to cell degradation: “Effects of Small Polar Molecules on Degradation Processes of Perovskite Solar Cells”, from Prof. Chun-Sing Lee et al. and “Study on degradation mechanism of perovskite solar cell and their recovering effect by introducing CH₃NH₃I layers” from Prof Masanori Ozaki et al. I find important links between those two articles, that is actually what I wanted to present.
As we all know, degradation of perovskite materials can be caused by humidity, oxygen, light, or heat. After being exposed to humidity, the perovskite’s colour changes, making it a perfect moisture sensitive material. In this very interesting article, Prof. Eugene A. Katz and co-workers found that the decomposition of perovskite is induced by illumination in the presence of water. In fact, concentrated sunlight experiments have shown that light triggers degradation and the mechanism depends highly on the temperature and the composition of the materials.
Water has been considered as the main cause of the instability of the perovskite, causing hydrolysis reactions that degrade the solar cells. Prof. Aron Walsh and co-workers have shown in 2014 that upon illumination and heating, hydrated MAPI (methylammonium lead triiodide) perovskite phases, such as MAPbI₃.H2O and MA₄PbI₆.2H₂O are formed and are followed by the release of a gas phase, composed of MAI. Those hydrated phases present no optoelectronic properties, therefore, this effect is considered responsible for the degradation along which the cell proceeds.
Prof. Nam-Gyu Park and co-workers reported last year that mobile MA⁺ ions appear in the perovskite film during degradation. Here Prof. Lee’s article is of particular importance. It appears that polar molecules, such as MA⁺ or H₂O are closely related to the degradation processes. Knowing that there are mobile MA⁺ ions in the perovskite film during degradation, the authors investigated the degradation processes of MAPI perovskite solar cells with different PbI₂/MAI ratios. They show with X-ray diffraction that the perovskite lattice is expanded by incorporation of water molecules. This mechanism is followed by a crystal breakage, in which MA⁺ and I⁻ ions are released. Those ions diffuse to form PbI₂ crystals.
The formed lead iodide crystals do not present electronic properties thus they are blocking the conducting channels. Hence the ion diffusion coefficient is lowered with the formation of those crystals. Later on, the scientists have demonstrated that the adsorption of water leads to a decrease in the Jsc along with a bulk degradation that accompanies an ion diffusion process. It becomes important when putting in relation with Prof. Ozaki’s article.
In this interesting article, MAPI perovskite materials are evaluated before and after degradation due to moisture and sunlight. It has been reported that during degradation, the crystalline structure changed with peaks assigned to planes of hexagonal PbI₂ and orthorhombic I₂. Simultaneously, the colour of the perovskite changed, indicating its degradation. Because they observed such a phenomenon, Ozaki et al. tried to add MAI layers on top of the perovskite. They have shown that with this layer addition, the MAPI solar-cell performance recovered. The hypothesis developed is that PbI₂ formed with the degradation allows recrystallization of perovskite after introducing MAI layers.
Thus, with the assumption that evaporated MAI cannot be recycled, the authors tried to add it directly to the surface. That allows the cell to be “refurbished”. This article shows an example of what can be done with MAI to reverse the degradation process. This could have many derived applications in the future.
Those two examples show how scientists have been able to understand, in a very basic way, how degradation happens. These understandings have led them to ideas of better, more stable and more efficient cells. That was to say that the perovskite field is rapidly evolving and we will rapidly have a better understanding of the degradation processes that will allow us to develop more stable and more efficient solar cells.
The cover photo has been taken from Swansea University on Flickr
The properties of crystalline semiconductors, and particularly those giving rise to the photoelectric effect, are mainly due to the presence of defects inside a crystalline lattice. Two weeks ago, at the annual Perovskite Solar Cells and Optoelectronics Conference (#PSCO17) in Oxford, one of the main topic developed was the exceptional defect tolerance found in the perovskites and the doping allowed by it. I contacted Prof. Aron Walsh, from the Department of Materials at Imperial College London (United Kingdom) that published recently a an interesting commentary in Nature Materials: ‘Instilling defect tolerance in new compounds’ and presented new results at the conference.
There are different type of defects in crystalline semiconductors: interruptions (crystallographic defects) or foreign atoms in the lattice (impurities). Those interruptions can be present in the form of point defects, including atomic vacancies, interstitials or anti-site substitutions, and higher dimensional defects like dislocations, grain boundaries or precipitates. Defects are formed in the lattice because there are thermodynamically favourable: their equilibrium concentration depends highly on their formation energy.
All of these defects will have different impact on the electronic and optoelectronic structures. Defects with energy levels inside the bandgap will induce electron or hole trapping. In other cases, defects can imply electron or hole emission: one hole and electron can be captured by a recombination centre. To sum it up, defects in a crystalline lattice produce recombination or emission centres that are at the heart of the optoelectronic properties of a lattice.
Due to these defects, semiconductors create unintentional n- or p-type doping, leading to the formation of p-n junctions. Also, from Fermi level pinning by defect states, unfavourable band alignment can be created that limit the voltage of solar cells.
Perovskites are also crystalline semiconductors. For this reason, defects exist and are active within the lattice. Their implications are not negligible and contribute significantly to many properties like carrier recombination. Also, in some cases, the presence of defects seems to have no major implication on recombination that leads to astonishing performance of perovskite solar cells. Prof. Aron Walsh explains this defect tolerance:
Practically speaking, in halide perovskite we expect many point defects to be present, but they do not destroy the performance of solar cells. In optoelectronic devices, it is essential to avoid non-radiative processes that convert electronic to thermal energy via defects. These events lower efficiency and can trigger device breakdown. It turns out that many of the low energy point defects in halide perovskite are “inert”, which is one of the reasons for the materials success. In other technologies such as kesterite (Cu₂ZnSnS₄) solar cells, non-radiative recombination is high, limiting the solar cell efficiencies to below 15%. Such defect intolerance is common in many materials that have been studied for solar cells (e.g. SnS, Cu₂O, FeS₂), which is why the unusual behaviour of halide perovskites is so important to understand.
I think that understanding the reason leading to such properties will lead to ways to enhance not only the properties of perovskites, but also the properties of other semiconductors. That is one of the reasons why research with perovskite is of high importance.
There are other properties that are in relation with the presence of defects. The mobile ions issue, which was previously discussed on this blog, is said to be due to the defect properties within perovskite structures. The presence of halogen interstitial or vacancy within the structure plays a major role: it has been observed that under light exposure, iodide and bromide species migrate along the cell, creating iodide- and bromide-rich domains, that act as recombination centres. Many scientist think that improving the crystal quality would lower the separation in halogen-rich domains. Personally, I think that a better understanding of the defect tolerance will allow us to develop better materials, that will not present hysteresis cycles lowering the performance of the cell.
In typical crystalline semiconductors, defects are very important for the reason they allow the doping of the structure. Doping means that a given material can be tuned to be a better electron- or hole-acceptor, due to the presence of charged defects. Therefore, the question arises as to whether the perovskite materials can be tuned or not. That is a real question. Aron has an enticing opinion on it:
In principle, doping of perovskite is simple: partial substitution of Pb²⁺ by a metal with a higher charge could generate excess electrons, while replacing it by a singly charged metal could generate excess holes. The challenge is achieving this without forming other defects that compensate the charge.
He explains the process in a clear and precise manner in his latest publication, even which there are now limitations. Working with these limitations, and trying to overcome these are a challenge most of the scientists in the perovskite community are working on.
If one manages to dope perovskite with tangible results, these could lead to the creation of p-n junction and therefore to field-effect transistors made with perovskite. The perspective of Prof. Walsh is very interesting at this point:
It will be possible once we would have understood how to control defect concentrations and transport. The current generation of perovskite solar cells are based on a p-i-n architecture, where the perovskite layer is intrinsic (i) with low carrier concentrations. Alternative p-n junctions would enable lower cost perovskite devices with fewer layers of materials, and potentially higher efficiency comparable to the best silicon solar cells. If realised, this would be a major breakthrough in the field.
Thus, the challenge to address is of great importance. I am sure we will understand in the year ahead the main reasons why perovskite are defect-tolerant, and will find solutions to create p-n junctions that will improve both the quality, the performance of solar cells, but also will allow us to create new electronic devices based on perovskites that will revolutionise the semiconductor industry.
The cover photo and the figure have been drawn by James M. Ball and Prof. Annamaria Petrozza in Nature.