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Presentation at the Society of Petroleum Engineers Workshop: Oil and Gas Technology for a Net-Zero World – Defining Our Grand Challenges for the Next Decade. Provides a high-level overview of point source carbon capture and direct air capture technologies, challenges and cost estimation.
Discontinuous fiber composites have a compelling business case as related to light metals such as aluminum and magnesium machined or die cast components. DFC’s have been in commercial production using carbon fiber/epoxy prepreg for both commercial aircraft and for military applications for a number of years and their usage is expanding into automotive and consumer goods components. Reasons for this include significantly lower cost as compared to continuous fiber composites easier design and understanding of the material by metal traditionalists, higher degree of part complexity with relatively simple and low cost molds when compared to high-pressure die casting, and potential for near zero waste. IACMI’s 10-year goals of reduction in carbon fiber reinforced plastics manufacturing cost by 25%, reduction in their embodied energy by 50%, and recyclability of 95% can all be advanced through robust recycling. With recycling We have shown that a 15% contribution in manufacturing cost reduction is feasible, that a significant reduction in embodied energy (over 90% for the recycled fraction) is achievable, and that when combined with primary pyrolysis recycling, the 95% target can be met. Large-scale application of advanced composites began with the aerospace industry, and CRTC’s location in Washington State provided access to a waste stream of nearly 900 tonnes/year that was going to landfill. As the aerospace industry has automated parts production, their material forms have become significantly easier to recycle, and some evidence of this exists for the future automotive and wind turbine components as well. CRTC decided to focus on re-purposing the carbon fiber/epoxy aerospace scrap streams through materials reformatting and reuse, and not on primary recycling (pyrolysis mainly) as this technology is commercially available. The main reasons for this were that it offers a route to effective use of the most widely available and consistent feedstock called edge-trim, as well as allows creation of complex and low-cost parts using rapid and cost-effective compression molding technologies. The reasons also include leading the way for potential automotive pre-preg recycling as the combination of roughly 85% virgin pre-preg and 15% recycled pre-preg directly supports IACMI’s goals and enables significant part cost reduction and a path to zero-waste composite manufacturing at the OEMs or Tier 1’s. The purpose of the project was to develop equipment and technology to transform continuous fiber pre-preg in roll forms into smaller chip-format DFC feedstock, and to determine impacts on moldability and performance based on lessons learned along the path. The availability of scrap from pre-preg manufacturers was a significant value to the program even though the aerospace pre-preg is designed to be autoclave molded thus has handling, tackiness, and processing factors that are not ideal for DFCs. The scope of the project was to develop a Phase 1 system that could identify and resolve some of the major hurdles, determine where to focus effort on building a commercial-scale Phase 2 system, and develop technology for handling a wide variety of incoming scrap materials to produce the most usable product. A chopping system was developed and reduced to practice via an experimental approach that enabled all forms of scrap coming from the pre-preg manufacturers and some forms of the scrap coming from OEM production lines to be very effectively re-purposed. The systems that were developed were not considered to be production robust but rather identified and resolved some of the major technical hurdles, and demonstrated the path towards effective full-scale commercialization.
The relentless accumulation of anthropogenic greenhouse gases has driven atmospheric carbon dioxide concentrations to approximately 426 ppm, necessitating the aggressive deployment of negative-emission technologies to achieve net zero by 2050. Direct air capture (DAC) offers a scalable, location-independent approach to atmospheric carbon removal; however, it is fundamentally constrained by the significant thermodynamic barriers associated with capturing CO 2 from ultradilute ambient conditions, requiring minimum thermodynamic energy inputs substantially higher than those for postcombustion point sources. This comprehensive review critically examines the technological landscape of DAC, focusing on the interdependent triad of sorbent material design, contactor engineering, and regeneration thermodynamics. We evaluate the fundamental boundaries of adsorption, emphasizing that an optimal adsorption enthalpy and isosteric heat of adsorption must balance the high CO 2 uptake capacity with the energetic penalties of sorbent regeneration. A systematic, comparative analysis of state-of-the-art sorbents is presented, encompassing mesoporous silicas, zeolites, carbon-based materials (CBMs), metal−organic frameworks (MOFs), porous organic polymers (POPs), and polymeric membranes. Special attention is devoted to surface functionalization strategies, particularly amine grafting and impregnation, which transition capture mechanisms from physisorption to chemisorption to enhance selectivity under ambient moisture and low partial pressures. Furthermore, we assess the operational merits of various reactor configurations, including gas−solid, gas−liquid, and membrane contactors, alongside regeneration cycles such as temperature, vacuum, pressure, and moisture swing adsorption. Finally, the review bridges fundamental materials science with industrial application by chronicling the scale-up milestones of pioneering entities and providing a strategic roadmap for advancing DAC technology readiness levels toward global deployment.
Emissions reduction and greenhouse gas removal from the atmosphere are both necessary to achieve net-zero emissions and limit climate change. There is thus a need for improved sorbents for the capture of carbon dioxide from the atmosphere, a process known as direct air capture. In particular, low-cost materials that can be regenerated at low temperatures would overcome the limitations of current technologies. In this work, we introduce a new class of designer sorbent materials known as ‘charged-sorbents’. These materials are prepared through a battery-like charging process that accumulates ions in the pores of low-cost activated carbons, with the inserted ions then serving as sites for carbon dioxide adsorption. We use our charging process to accumulate reactive hydroxide ions in the pores of a carbon electrode, and find that the resulting sorbent material can rapidly capture carbon dioxide from ambient air by means of (bi)carbonate formation. Unlike traditional bulk carbonates, charged-sorbent regeneration can be achieved at low temperatures (90–100 °C) and the sorbent’s conductive nature permits direct Joule heating regeneration using renewable electricity. Given their highly tailorable pore environments and low cost, we anticipate that charged-sorbents will find numerous potential applications in chemical separations, catalysis and beyond.
https://events.usea.org/events/midwest-regional-carbon-conversionutilization-procurement-grant-workshop As the U.S. economy moves toward clean energy and a lower carbon future, the U.S. Department of Energy (DOE) is seeking to partner with states, communities, and industries to support the procurement and development of carbon conversion products. These efforts have been enabled by provisions included in the Bipartisan Infrastructure Law (BIL). As part of the BIL, supporting the Administration’s goal to achieve a carbon-free power sector by 2035 and putting the United States on a path to a net-zero economy by 2050, a new initiative was established within DOE’s Office of Fossil Energy and Carbon Management through its Carbon Conversion/Utilization Program. The new initiative will establish a demonstration grant program to issue grants to eligible entities to procure commercial and industrial products derived from the conversion of anthropogenic carbon oxides and demonstrate a significant net reduction in life cycle greenhouse gas emissions compared to incumbent technologies, processes, and products. DOE-FECM will establish a demonstration grant program within the Carbon Conversion/Utilization Program to support eligible applicants that procure those commercial and industrial products derived from anthropogenic carbon oxides. Therefore, the Carbon Conversion/Utilization Program, with the assistance of the United States Energy Association (USEA), will conduct a series of workshops (both virtual and in-person) with relevant stakeholders, e.g., product manufacturers, eligible entities, or their representative national organizations (e.g., United States Conference of Mayors, etc.) to solicit input and ideas on challenges and opportunities for a potential grant program.
Europe and North America account for 32 % of current carbon emissions. Due to distinct legacy systems, energy infrastructure, socioeconomic development, and energy resource endowment, both regions have different policy and technological pathways to reach net zero by the mid-century. Against this background, our paper examines the results from the net zero emission scenarios for Europe and North America that emerged from the collaboration of the European and American Energy Modeling Forums. Here, in our analysis, we perform an inter-comparison of various integrated assessments and bottom-up energy system models. A clear qualitative consensus emerges on five main points. First, Europe and the United States reach net zero targets with electrification, demand-side reductions, and carbon capture and sequestration technologies. Second, the use of carbon capture and sequestration is more predominant in the United States due to a steeper decarbonization schedule. Third, the buildings sector is the easiest to electrify in both regions. Fourth, the industrial sector is the hardest to electrify in the United States and transportation in Europe. Fifth, in both regions, the transition in the energy mix is driven by the substitution of coal and natural gas with solar and wind, but to a different extent.
A technique is described for the simultaneous in situ measurement of film thickness, refractive index, total normal emissivity, visible-light scattering, and reflectance of contaminant films on a highly reflective liquid-nitrogen cooled, stainless steel substrate. Emissivities and scattering data are obtained for films of water, carbon dioxide, silicone oil, and a number of aromatic and aliphatic hydrocarbons as a function of film thickness between zero and 20 microns. Of the contaminants investigated, water has by far the greatest effect on emissivity, followed by silicone oil, aliphatic hydrocarbons, aromatic hydrocarbons, and carbon dioxide. The emissivity increases more rapidly with film thickness between zero and 2.5 microns than at thicknesses greater than 2.5 microns. Scattering of visible light changes very little below 2 microns thickness but increases rapidly with thickness beyond 2 to 3 microns. The effect of contaminant films on passive radiation coolers is discussed.
Measurements of surface concentrations of carbon in lunar soils and soil breccias provide information on the origin of carbon in the regolith. The reaction C-12 (d, p sub zero) is used to measure 'surface' and 'volume' concentrations in lunar samples. This method has a depth resolution of 1 micron, which permits only a 'surface' and a 'volume' component to be measured. Three of four Apollo 16 double drive tube samples show a surface carbon concentration of about 8 by 10 to the 14th power/sq cm, whereas the fourth sample gave 4 by 10 to the 14th power/sq cm. It can be convincingly shown that the measured concentration does not originate from fluorocarbon or hydrocarbon contaminants. Surface adsorbed layers of CO or CO2 are removed by a sputter cleaning procedure using a 2-MeV F beam. It is shown that the residual C concentration of 8 by 10 to the 14th power/sq cm cannot be further reduced by increased F fluence, and it is therefore concluded that it is truly lunar. If one assumes that the measured surface C concentration is a steady-state concentration determined only by a balance between solar-wind implantation and sputtering, a sputter erosion rate of 0.1 A/yr is obtained. However, it would be more profitable to use an independently derived sputter erosion rate to test the hypothesis of a solar-wind origin of the surface carbon.
In the real-world of political opposition and complex market failures, carbon pricing alone will not achieve deep GHG mitigation targets. Hence, in this study, we search for the most cost-effective “second-best” policies. Focusing on the light-duty vehicle sector in the case of Canada, we compare several policies in terms of effectiveness (regarding 2030 GHG goals) and mitigation costs, namely: (i) a carbon tax; (ii) a vehicle emission standard (or VES); (iii) a zero emissions vehicle (ZEV) mandate, and (iv) combinations of all three at various stringencies. In this effort, we apply the AUtomaker-consumer Model (AUM), which endogenously simulates consumer and automaker decisions and technological change. Comparing individual policies, the regulations are about three times more expensive than the carbon tax. Among “second-best” policies, the VES is cheaper than a ZEV mandate at lower stringencies, but at higher stringencies the two are similarly efficient (both incentivize widespread ZEV deployment). In policy mixes, cost-effectiveness is improved by a carbon tax. Specifically, inclusion of a CDN$100–150/tonne tax can achieve targets while being 30–40% less costly than a regulation alone. We suggest that policymakers implement carbon pricing as stringently as politically feasible (for efficiency), complemented by regulations as needed (for efficacy) to meet GHG targets.
There remains a lack of fundamental understanding in theroleofbackbonerigidityonthe thermomechanical properties of conjugated polymers. Here, we provide the first holistic approach to understand the fundamental influence of backbone rigidity on an n-type naphthalene diimide-based conjugated polymer, denoted by PNDI-Cx, through insertion of a flexible conjugation break spacer (CBS). CBS lengths are varied from fully conjugated with zero alkyl spacer (PNDI-C0) to a seven- carbon alkyl spacer (PNDI-C 7 ), with the CBS engineered into each repeat unit for systematic evaluation. Solution small-angle neutron scattering and oscillatory shear rheometry were employed to provide the first quantitative evidence of CBS influence over conjugated polymer chain rigidity and entanglement molecular weight (M e ), demonstrating a reduction in the Kuhn length from 521 to 36 Å for fully conjugated PNDI-C0 and PNDI-C6, respectively, as well as a nearly consistent Me of ~15 kDa upon the addition of CBS. Thermomechanical properties, such as elastic modulus and glass-transition temperature, were shown to decrease with an increasing length of CBS. An extraordinary ductility, upwards of 400% tensile strain before fracture, was observed for high-molecular-weight PNDI-C4, which we attribute to a high number of entanglements and disruption of crystallization. Furthermore, the deformation mechanism for PNDI-Cx was studied under strain through X-ray diffraction, polarized UV-vis spectroscopy, and atomic force microscopy. Overall, this work sheds light on the important role of backbone rigidity in designing flexible and stretchable conjugated polymers.
Here, we study the effect of quantum vibronic coupling on the electronic properties of carbon allotropes, including molecules and solids, by combining path integral first principles molecular dynamics (FPMD) with a colored noise thermostat. In addition to avoiding several approximations commonly adopted in calculations of electron-phonon coupling, our approach only adds a moderate computational cost to FPMD simulations and hence it is applicable to large supercells, such as those required to describe amorphous solids. We predict the effect of electron-phonon coupling on the fundamental gap of amorphous carbon, and we show that in diamond the zero-phonon renormalization of the band gap is larger than previously reported.
Cd(N2)2(CO2)2 is Cyanogen Chloride-derived structured and crystallizes in the orthorhombic P2_12_12 space group. The structure is zero-dimensional and consists of two cadmium molecules, four carbon dioxide molecules, and four nitrogen molecules.
(N2)2(CO2)4H2 is Cyanogen Chloride-derived structured and crystallizes in the orthorhombic P2_12_12 space group. The structure is zero-dimensional and consists of four ammonia molecules, four carbon dioxide molecules, and two hydrogen molecules.
(NbCO7)2(N2)3(CO2)4(CO)2O2 crystallizes in the monoclinic P2/c space group. The structure is zero-dimensional and consists of twelve ammonia molecules, eight carbon dioxide molecules, four formaldehyde molecules, two hydrogen peroxide molecules, and four NbCO7 clusters. In each NbCO7 cluster, Nb5+ is bonded in a 1-coordinate geometry to six O2- atoms. There are a spread of Nb–O bond distances ranging from 1.74–2.31 Å. C4+ is bonded in a linear geometry to two O2- atoms. There is one shorter (1.17 Å) and one longer (1.18 Å) C–O bond length. There are seven inequivalent O2- sites. In the first O2- site, O2- is bonded in a 1-coordinate geometry to one Nb5+ and one O2- atom. The O–O bond length is 1.41 Å. In the second O2- site, O2- is bonded in a 1-coordinate geometry to one Nb5+ and one O2- atom. In the third O2- site, O2- is bonded in a 1-coordinate geometry to one Nb5+ and one O2- atom. The O–O bond length is 1.40 Å. In the fourth O2- site, O2- is bonded in a single-bond geometry to one C4+ atom. In the fifth O2- site, O2- is bonded in a 1-coordinate geometry to one Nb5+ and one O2- atom. In the sixth O2- site, O2- is bonded in a distorted linear geometry to one Nb5+ and one C4+ atom. In the seventh O2- site, O2- is bonded in a single-bond geometry to one Nb5+ atom.
UO2(N2)2(CO3)3 crystallizes in the monoclinic C2/c space group. The structure is zero-dimensional and consists of sixteen ammonia molecules; twelve carbonic acid molecules; and four pitchblend, uranium(iv) oxide, uranium(iv) dioxide, uranium dioxide molecules.
(VC3O8)2(N2)2(CO2)2O2 crystallizes in the monoclinic P2_1/c space group. The structure is zero-dimensional and consists of eight ammonia molecules, four carbon dioxide molecules, four water molecules, and four VC3O8 clusters. In each VC3O8 cluster, V4+ is bonded in a 2-coordinate geometry to five O2- atoms. There are a spread of V–O bond distances ranging from 1.64–2.40 Å. There are three inequivalent C4+ sites. In the first C4+ site, C4+ is bonded in a linear geometry to two O2- atoms. There is one shorter (1.16 Å) and one longer (1.18 Å) C–O bond length. In the second C4+ site, C4+ is bonded in a linear geometry to two O2- atoms. There is one shorter (1.16 Å) and one longer (1.19 Å) C–O bond length. In the third C4+ site, C4+ is bonded in a linear geometry to two O2- atoms. There is one shorter (1.17 Å) and one longer (1.18 Å) C–O bond length. There are eight inequivalent O2- sites. In the first O2- site, O2- is bonded in a single-bond geometry to one V4+ atom. In the second O2- site, O2- is bonded in a distorted bent 150 degrees geometry to one V4+ and one C4+ atom. In the third O2- site, O2- is bonded in a distorted bent 150 degrees geometry to one V4+ and one C4+ atom. In the fourth O2- site, O2- is bonded in a single-bond geometry to one C4+ atom. In the fifth O2- site, O2- is bonded in a single-bond geometry to one C4+ atom. In the sixth O2- site, O2- is bonded in a distorted bent 150 degrees geometry to one V4+ and one C4+ atom. In the seventh O2- site, O2- is bonded in a single-bond geometry to one C4+ atom. In the eighth O2- site, O2- is bonded in a single-bond geometry to one V4+ atom.
(Cd)2(N2)4(CO2)4H2 is Cyanogen Chloride-derived structured and crystallizes in the orthorhombic Pbcn space group. The structure is zero-dimensional and consists of four cadmium molecules, eight carbon dioxide molecules, four hydrogen molecules, and eight nitrogen molecules.
Since 2015, the U.S. wind installed capacity has grown from 73 to over 120 gigawatts, creating jobs across many sectors and educational levels. The growth of the wind workforce will need to continue to meet the goal of 20% wind by 2030, as well as the Biden administration's goals to reduce greenhouse gas pollution by 2030, reach 100% carbon-free electricity by 2035, and achieve net-zero greenhouse gas emissions no later than 2050. Despite the needed and anticipated growth, there are challenges to meeting this demand. Research has consistently shown that it has been a challenge finding qualified applicants for open wind industry jobs. Between 2012 and 2018, the difficulty of finding qualified applicants increased from 62% to 68% according to industry respondents. In 2017, educational institutions and training programs reported that 67% of their students did not enter the wind energy industry. Research conducted in 2020 showed that 83% of interested workers had some or great difficulty finding job opportunities. In exploring reasons for this gap, the researchers found that challenges were primarily influenced by education, experience, and geography. This difficulty for wind industry employers, educational institutions, and the potential workforce is known as the "wind energy workforce gap." This report further investigates the experience aspect of this gap.