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Home > Sustainability > Energy > Morocco Launches 305 MW Noor Atlas Solar Program as ONEE and MASEN Sign Power Agreements Morocco Launches 305 MW Noor Atlas Solar Program as ONEE and MASEN Sign Power Agreements Casablanca – Morocco’s Office National de l’Électricité et de l’Eau Potable (ONEE) and the Moroccan Agency for Sustainable Energy (MASEN) have signed electricity purchase agreements linked to the Noor Atlas photovoltaic solar program while simultaneously announcing the launch of construction works for the project. The agreements cover the development, financing, construction, and operation of the Noor Atlas program, a large-scale solar initiative designed to expand Morocco’s renewable energy capacity across several regions of the country. The project includes the construction of six photovoltaic power plants with a combined installed capacity of 305 megawatts. The facilities will be built in Ain Béni Mathar in the province of Jerada, Boudnib in the province of Errachidia, Bouanane in the province of Figuig, Enjil in the province of Boulemane, Tata in the province of Tata, and Tan-Tan in the province of Tan-Tan. Masen will oversee the operation and maintenance of the plants under an engineering, procurement, and construction framework. The agency and the national utility described the initiative as a major project aimed at strengthening renewable electricity production in several regions of Morocco. Financing for the Noor Atlas program combines concessional and commercial funding. Germany’s development bank KfW and the European Investment Bank are providing concessional financing, while Bank of Africa is contributing commercial financing for the project. Construction of the solar plants will be carried out by consortiums bringing together Moroccan and European companies. Read also: IEA: Global Electricity Demand to Grow 3.6% Yearly as Renewables, Nuclear Reach 50% by 2030 According to the announcement, this approach is intended to support skills transfer while also strengthening the national industrial ecosystem. The participation of local companies is also expected to contribute to job creation in the regions hosting the plants. The project is scheduled to begin delivering electricity starting in July 2027 once the different sites are completed and connected to the national grid. Once operational, the Noor Atlas facilities are expected to supply renewable electricity while improving the quality of energy services at the regional level. The plants will also contribute to lowering greenhouse gas emissions by increasing the share of renewable energy in Morocco’s electricity mix. The announcement comes as Morocco continues expanding its solar capacity as part of its broader energy transition strategy. Solar infrastructure has become a central pillar of the country’s approach to diversifying electricity production and reducing reliance on conventional energy sources. Through the Noor Atlas program, the national electricity utility and Masen reaffirm their complementary roles in advancing Morocco’s renewable energy agenda. Both institutions said the project reflects their ongoing coordination in implementing the country’s strategy for sustainable energy development and supporting the transition toward cleaner electricity production across the country. Copyright 2026 Morocco World News. All rights reserved. Morocco World News is not responsible for the content of external sites. Read about our approach to external linking. Login to your account below
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A vast migrant labour force is helping India meet its ambitious renewable energy goals, drawn by promises of good wages and perks. But many say they are forced to ‘escape’ without pay A month into his new job at the world’s largest renewable energy park in Gujarat’s Rann of Kutch, Anawar Alam was planning his escape. Hired along with 17 others who had travelled with him to work on the construction of a solar project, Alam had hoped that the promised pay and perks would support his family back home on the farm in Bihar. But within two weeks he was having second thoughts. “Nothing really prepared us for where we would be working or the fact that it was so far from the nearest village. The work was strenuous, the shifts were 12 hours, and we were living in makeshift tents,” says Alam. “It was incredibly hot, and the contractor kept yelling at us for not working longer or harder, threatening us by saying that he would kill us and no one would even know we had disappeared. But the bigger problem was that he was not paying us on time or in full.” Alam is one of thousands of young migrant workers who are signing up to work in the remote, salty marshland of Kutch district. Drawn largely from the hinterlands of Jharkhand, Bihar and Uttar Pradesh, they arrive in their hundreds to work on the construction of solar projects, encouraged by contractors who promise good wages, facilities and steady employment. However, for many of the men, mostly in their 20s, the job is short-lived, as they say a complex chain of subcontracting results in long delays in payment, harsh living conditions with little access to power, clean drinking water and other amenities. Workers say that as a result, most return home after a few months, losing wages and opportunities in a sector that is seen as key to creating green jobs. “There have been a few complaints, and we have immediately taken action,” says a senior official at the labour department of Bhuj city in Kutch, who requested anonymity. “We encourage workers to report wage theft and other issues. But not many come forward given that most are migrant workers.” Migrant workers are often not familiar with the place they migrate to work and are unaware of complaint procedures. In addition, language can be a barrier and if they have returned to their home states, they may be unable to travel back and forth to pursue their case. Alam, 22, and his co-workers say they raised complaints with the company’s on-site engineers. When there was no response, he asked his father to send him 30,000 rupees (£250). He then made a series of trips out of the heavily guarded facility with his co-workers, who had travelled with him and also wanted to leave, temporarily housing them in Khavda village. Once all the men were out, he hid in a vehicle leaving the energy park, rejoined the others and returned home. “Not only did I not earn anything, but I also ended up borrowing money from my father to escape,” says Alam. In 2023, India had an estimated 1.02m renewable energy jobs, with hydropower taking the lion’s share, employing 453,000 people, according to the International Renewable Energy Agency’s (Irena) annual review 2024. By 2030, India aims to train and up-skill more than 300,000 workersto support the installation, maintenance and operation of solar infrastructure across the country, including planned large solar parks and rooftop installations. While the solar power systems are being built by some of India’s largest companies, there is little or no accountability, as most hire recruitment agencies, who in turn hire labour contractors, rights campaigners say. Besides the energy park at Khavda, a number of other solar projects are being built by a largely migrant workforce as they race to meet India’s renewable energy goal of 500GW from non-fossil fuel sources by 2030. “This vast labour force coming to construct renewable energy projects is not recognised as ‘solar labour’ but just as general construction workers,” says Anuj (who did not want to give his surname) a research fellow at the Centre for Energy, Environment and People (Ceep), a nonprofit that works on energy justice for communities. “It is a completely unregulated sector from a labour point of view. There is a new and complex network of solar contractors, engineers and workers developing. The sector is new but those running it are coming from old systems, bringing with them exploitative labour practices.” Arpit Sharma, CEO of the Skill Council for Green Jobs under India’s Ministry of Skill Development and Entrepreneurship, says: “At present, these jobs attract a lot of migrant workers, but the space is not regulated. We are recommending that it is done soon so that these jobs become more sustainable for workers.” Officials declined to comment on whether labour issues had affected completion dates, with most stating that “delays could be attributed to many factors and labour was just one of them”. Khavda is the last village on the road from Bhuj to the Rann of Kutch. En route, one road leads to the ancient city of Dholavira, a Unesco world heritage site that is home to one of the two largest Harappan civilisation sites in India. It connects to the “road to heaven”, a scenic highway that attracts thousands of tourists. The other road out of Khavda leads to the Border Security Force post in Kotada, the last outpost beyond which lies the Rann of Kutch and the renewable energy park. The park is a hybrid project combining solar and wind power generation with a planned capacity of 30GW. When completed in 2028, it is expected to power about 18m homes and offset 58m tonnes of CO2 emissions annually. Six developers have been allotted land on the site to develop renewable energy, including the National Thermal Power Corporation (NTPC), Gujarat Industries Power Company and Adani Green Energy. Spread over 72,400 hectares (180,000 acres), the project is under various stages of construction, with each developer bringing its own engineers and workers on site. Labour contractors say delays in clearing bills affects wages being paid on time. They say their contracts give little leeway, with 10% of the payment from the energy companies being held for a year after completion of work as surety, and money being released in phases that don’t coincide with worker’s paydays. Many have refused to supply labour to the Khavda project, citing lack of amenities for workers, the heavy financial burden on contractors and harsh working conditions. Sumer Singh, 30, who runs a small recruitment company, says: “Earlier, companies built labour colonies for the workers to stay on site but it proved too expensive for them. So now the labour contractor must help them rent homes in nearby villages or provide makeshift accommodation on site. “For small contractors, these are prohibitive costs.” Many contractors say they are held accountable by workers in case of delays or other concerns not being addressed quickly enough. “If one worker has a problem and packs up his bags to return home, everyone from that group goes back,” says a contractor at Kotada. The Gujarat Power Corporation, which oversees the energy park, and Solar Energy Corporation of India did not respond to repeated requests for comment. Open vehicles carrying workers and supplies from Khavda start arriving at Kotada border post early in the morning. Long queues snake along the road leading to document verification windows for all men and materials entering the park, a 30-minute drive further into the Rann. “For the hundreds that arrive here every day, there are hundreds who leave also,” says Jesanguhai Ranabhai, the sarpanch [village head] of Khavda. Sikander Kumar, a worker from Godda district, Jharkhand, arrived with 25 others to work for 900 rupees a day, more than his small patch of land was yielding back home. “The work was not bad, the food was OK, though we would have frequent issues getting clean drinking water,” he says. “There was no power supply to where we were staying, and we were not being paid full salaries. We migrated so far from home for money and if we don’t get it, what is the point?” Kumar and his group left after two months, walking more than 12 miles (20km) to find transport to take them to the station to catch a train home. Their return trip was funded by their families. Now Kumar must pay some of the workers who left their villages on his assurance for their losses. “I have to pay back 40,000 rupees and, more importantly, rebuild trust with them,” he says. Similarly, Alam was summoned by his village council and asked to pay workers he had convinced to go along with him. Alam sold part of his family land to raise 200,000 rupees (£1,700), and now works as a tailor. “We thought we would earn more in solar, save and improve our lives. The opposite happened,” Alam says. “We lost on all fronts. “Now we are back home and there is no way to complain or follow up on the wages we lost and the additional money we spent for our return. All our calls are going unanswered.” Anuradha Nagaraj is an independent journalist and co-founder of the Migration Story where a version of this story first appeared
Tata Power is set to build India’s largest solar wafers and ingots plant with a 10 GW capacity. This move completes their manufacturing chain for solar products. The company is exploring government financial support for this significant project. Tata Power is also considering entering nuclear power generation as India expands its nuclear capacity.
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Connecting business research with policy, practice and public debate Connecting business research with policy, practice and public debate 0 comments | 3 shares Estimated reading time: 5 minutes Connecting business research with policy, practice and public debate 0 comments | 3 shares Estimated reading time: 5 minutes Australian households have embraced solar power. But when homeowners upgrade, they wrongly assume that their old panels will no longer work. So most are removed and sent to landfill, undermining the environmental benefits of reusable energy. Ishika Chhillar, Sukhbir Sandhu, Subhadarsini Parida and Peter Majweski show how reusing panels could cut waste and make solar power more accessible. Australia has long been a global leader in solar energy. With one of the highest rates of rooftop solar installations, solar power has become a central part of the nation’s energy transition and shift toward sustainability. More than four million Australian homes (around 39 per cent of households) now have panels on their roofs. But while Australians have focused on generating clean energy, a new challenge is emerging: what to do with all the end-of-life solar panels being pulled off roofs. Solar panels typically last 25 to 30 years. But many are replaced earlier, often because homeowners upgrade to newer and more efficient models. That means the first big wave of solar waste – installed about 16 years ago in the early 2010s – is arriving earlier than expected. The Australian Energy Council estimates that Australia will produce about 280,000 tonnes of solar panel waste by the end of 2025. And that number is rising quickly. An estimated 685,000 tonnes of panels will have to be retired by 2030. Although many Australians assume old solar panels are useless, most can still generate power for years. Most discarded solar panels in Australia are currently sent to landfills or partial recycling facilities. While recycling is better than disposal, it is often not economically viable. In practice, recycling mainly recovers materials such as aluminium frames and glass, while other components such as plastics, silicon and toxic trace metals like lead, still end up in landfill. If Australia continues with a “take, make, dispose” approach to solar technology it will waste valuable resources and lose the climate benefits that clean energy was meant to provide. Recycling alone does not solve the solar waste issue. Reusing old panels must be part of the solution. While the scale of the waste problem is daunting, it also presents an opportunity. Reuse offers a way to extend the life of solar panels before they are shredded for materials. Reusing still-functional panels can defer the waste problem, buying time for recycling systems to expand and for panels to reach true end-of-life. It also extracts more value and energy from each manufactured panel, reducing the need for new materials and lowering environmental impact. Despite these benefits, reuse has barely begun. Europe has policies requiring manufacturers to take back old panels for reuse or recycling. But Australia has no equivalent regulations yet. A national product stewardship scheme for solar panels is in development, but not yet operational. Several major barriers stand in the way before reuse can become mainstream. If reusing solar panels makes so much sense, why are Australians not doing it already? Our research highlights that the main issue is economics. The price of new solar panels has dropped sharply and government rebates make them even cheaper. When new systems are affordable, more efficient and backed by warranties, there is little incentive to buy second-hand. Testing, transporting and reinstalling used panels adds additional costs. Another barrier is the lack of national standards. Australia has no official certification process to prove that solar panels are safe. Without a national framework, installers do not know who is liable if something goes wrong and consumers cannot tell whether a used panel is reliable. Currently, there is no simple way to check the age, condition or power output of a second-hand panel, so for most people, reusing them feels risky. Our research elaborates that a trusted certification system could change that. Much like certified pre-owned cars, reused panels could be tested, graded and sold with a clear record of their performance and remaining lifespan. A simple rating label (such as Gold, Silver, or Bronze) could signal quality at a glance, giving buyers and installers confidence that the panels meet safety and performance standards. Digital tracking could strengthen this trust further. A QR code or “digital passport” on each panel could show its model, age, test results and installation history. Having that information easily accessible would make used panels feel far less uncertain and much more like verified, dependable products. But for reuse to really take off, certification alone will not be enough. The government needs to back any scheme with supportive policies and incentives, such as rebates for certified reused panels or funding for regional testing hubs. The federal government’s upcoming product stewardship scheme for solar photovoltaic systems is a welcome step, but it will need to include reuse alongside recycling. Certified reused panels could make solar energy more affordable for schools, community centres or households that cannot afford new systems. Demonstration projects could show that reuse is safe, cost-effective and good for the environment. Australia’s solar success story does not have to end with a landfill full of old panels. With the right framework in place, the looming waste crisis can become an opportunity. Certification, traceability, supportive policies and community awareness could help Australia build a second-life solar industry that creates jobs, reduces waste, and keeps clean energy truly sustainable. Reuse is the next step in making renewable energy genuinely circular. This article gives the views of the author, not the position of LSE Business Review or the London School of Economics. You are agreeing with our comment policy when you leave a comment. Image credit: Elias Bitar provided by Shutterstock. Ishika Chhillar is a PhD candidate at Adelaide University's Centre for Workplace Excellence. Her research focuses on developing a certification framework for the reuse of solar photovoltaic panels. Her research involves qualitative research, including interviews with stakeholders across industry, government, academia and consumers, to identify enablers, barriers and opportunities in the transition from recycling toward reuse. Her work highlights how certification can build trust, reduce risk perceptions and foster market confidence in contested industries. Sukhbir Sandhu is the Executive Director of the Centre for Workplace Excellence at Adelaide University. Her research focuses on social and environmental sustainability, examining how organisations respond to external sustainability pressures and implement internal strategic change. She has published widely in leading journals and received multiple international awards for research impact, leadership, and teaching excellence. Subha Parida is a researcher at Adelaide University whose work examines sustainability across individual, organisational and stakeholder behaviours shaping the future of work, with a focus on the social and governance dimensions of ESG in the built environment. She has held research leadership roles at Curtin and Edith Cowan universities and works closely with government, industry and community organisations. Her research has been recognised with early career awards for teaching and research excellence. Peter Majewski is an industry expert affiliated with Equals International and a former Research Professor at the University of South Australia’s Future Industries Institute. He holds a PhD in Mineralogy from Leibniz University of Hannover and has extensive experience in materials science, renewable energy and product stewardship. He has published over 180 journal articles and has held senior leadership and governance roles across academia and industry focused on sustainable technologies. Your email address will not be published.Required fields are marked *
We use cookies to improve your experience and for marketing. Read our cookie policy or manage cookies. According to a report from PV-Tech, French energy company TotalEnergies has started pilot commissioning for the initial generating unit of a large solar installation in Iraq’s Basra region. The first unit, with a capacity of 61 megawatts, is being brought online and will be increased incrementally to its full 250-megawatt output. This unit will feed power into the national grid using specific transmission lines, based on technical plans developed by the project’s teams. The solar farm is described as the largest of its kind in Iraq and is composed of four separate 250-megawatt units. The entire facility extends over nine kilometers and will utilize two million solar panels across all four units. A senior official noted that initiating trial operations for this first unit represents a significant achievement for the company and the Iraqi Ministry, emphasizing the project’s role in broadening the country’s energy sources, especially in Basra where power needs are growing quickly. The project was first announced several years ago and represents the second one-gigawatt solar plant TotalEnergies is constructing in Iraq. It involves a substantial investment that also covers new gas infrastructure and seawater treatment facilities. The solar initiative requires building 132-kilovolt transmission lines over a total distance of 180 kilometers, erecting a new substation, and upgrading two existing substations managed by the ministry. TotalEnergies will also be responsible for operating and maintaining the solar farm for a quarter of a century. The electricity generated will be delivered to three secondary substations. The plant is being developed in collaboration with Iraq’s Ministry of Oil. Another state-owned energy company joined the venture as a minority partner more recently, while a separate Saudi energy firm was confirmed to be providing development assistance. Iraq has broader ambitions for solar power, having announced a target for significant photovoltaic capacity by the end of the decade. The national investment authority has started issuing licenses for these projects, with a large portion of the planned capacity already approved by the government and processes ongoing to allocate the remainder. Making Data-Driven Decisions to Grow Your Business A Quick Overview of Market Performance Understanding the Current State of The Market and its Prospects Finding New Products to Diversify Your Business Choosing the Best Countries to Establish Your Sustainable Supply Chain Choosing the Best Countries to Boost Your Export The Latest Trends and Insights into The Industry The Largest Import Supplying Countries The Largest Destinations for Exports The Largest Producers on The Market and Their Profiles
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A paid subscription is required for full access. As of March 2023, Gujarat was the leading state in India in terms of rooftop solar capacity installed. The state had a capacity of almost *** gigawatts as of that date. Maharashtra followed with a solar rooftop capacity of roughly *** gigawatts. In total, India’s rooftop solar capacity amounted to approximately *** gigawatts as of March 2023.
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Massac County farmer Clint Smith points out his property as he talks with a SB Energy representative on Tuesday, Feb. 24, during a scheduled public hearing. Smith’s property adjoins a portion of the proposed SB Energy Shawnee Energy Project. The solar farm encompassing 5,150 acres is to be located on the Massac-Johnson line. With the hearing’s informal setting not to the liking of a contingent of those attending, a more formal hearing is being rescheduled. Some 50 to 75 Massac County residents attended a public hearing held Tuesday, Feb. 24, concerning the Shawnee Energy Project by SB Energy. While representatives were on hand to discuss the project informally with attendees, many objected to its being held at the Metropolis Elks Lodge and not a more formal setting. It is being rescheduled for sometime in April. The land makeup of the proposed SB Energy Shawnee Energy Project is shown in blue on a poster set up during the Feb. 24 public hearing. In Massac County, the project involves land owned by the three farms of West, Mathis and Main.
For The Sun ttemple@metropolisplanet.com Massac County farmer Clint Smith points out his property as he talks with a SB Energy representative on Tuesday, Feb. 24, during a scheduled public hearing. Smith’s property adjoins a portion of the proposed SB Energy Shawnee Energy Project. The solar farm encompassing 5,150 acres is to be located on the Massac-Johnson line. With the hearing’s informal setting not to the liking of a contingent of those attending, a more formal hearing is being rescheduled. Some 50 to 75 Massac County residents attended a public hearing held Tuesday, Feb. 24, concerning the Shawnee Energy Project by SB Energy. While representatives were on hand to discuss the project informally with attendees, many objected to its being held at the Metropolis Elks Lodge and not a more formal setting. It is being rescheduled for sometime in April. The land makeup of the proposed SB Energy Shawnee Energy Project is shown in blue on a poster set up during the Feb. 24 public hearing. In Massac County, the project involves land owned by the three farms of West, Mathis and Main. MASSAC COUNTY — What residents thought would be a formal meeting providing information on an upcoming solar farm project and what those project representatives planned to be a more informal setting collided last week. The pubic hearing, which is required by the Massac County solar ordinance, was Tuesday, Feb. 24, at the Metropolis Elks Lodge. Javascript is required for you to be able to read premium content. Please enable it in your browser settings. Your comment has been submitted.
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With all members present, including District 2 Magistrate Shawna Coldiron and District 3 Magistrate Roger Humphrey both attending via Zoom, Judge/Executive Chuck Dills called the Grant County Fiscal Court to order on March 3. Agenda items included appointments, ordinance readings and advertising bids along with Ethics Commission meeting information and Farmers’ Market Produce Stand request. Re-appointments Court unanimously approved the following re-appointments: · Teddy Beckham, E911 Service Fee Appeals Board, retroactive to Feb. 2 and expiring Dec. 31, 2032 · Billy Points, E911 Service Fee Appeals Board, retroactive to Feb. 2 and expiring Dec. 31, 2032 · Lester “Lum” Edwards, E911 Service Fee Appeals Board, retroactive to Feb. 2 and expiring Dec. 31, 2032 · Candace Hammonds Faulkner, Tax Appeals Board, retroactive to Feb. 2 and expiring Dec. 31, 2032 · Fred Scheffler, 109 Board, retroactive to Feb. 2 and expiring Dec. 31, 2032 Ordinances · Second Reading: Ordinances numbers 001-2026-0293 and 002-2026-0294 received their first readings. Both deal with putting “Solar Energy Systems” regulations in place. Ordinance 0293 is an amendment to the ordinance intended to change “the zoning ordinance by adding … the inclusion of Solar Energy Systems to the list of Conditional Uses within and Industrial Two (I-2) Zone. Ordinance 0294 is an amendment to the ordinance intended to “change the zoning ordinance by adding … the inclusion of Solar Energy System Regulations to Article 15 Performance Standards for Industrial Zones…” It adds “solar energy system to Industrial 2 zone” and adds “pertains to regulation for” those systems. · First Reading: Ordinance numbers 003-2026-0295, Solar Energy Data Storage Center Amendment, and 0004-2026-0296, Data Storage Center Amendment, adding Industrial-2 Industrial Zone. Dills previously explained both Solar Farms and Data Storage Center ordinances are “proactive” actions so the County will have standards in place should any entity want to site solar farms in the County. · First Reading: Ordinance Number 0004-2026-0296, Troy and Tammy Pendleton Zone Change for a 5.9 acre site with existing house. The ordinance changes zoning from A-1 to R-1A (residential one agriculture), separating one acre with the house from remaining 4.9 acres to build another house. Dills noted all ordinances are available in the Judge/Executive’s Office in the old courthouse. Miscellaneous · Court unanimously approved Dills to sign contract agreement approving Matthew Dunaway as an electrical inspector for Grant County, effective March 3. Dills said the Court maintains three electrical engineers approved to work in the County. He said Larry Wright, one of the current approved electricians, has moved to semi-retirement and will not being available as a full-time inspector for the County. Dills said Dunaway is “highly recommended” and is class three certified electrician. · A proposed interfund transfer from the General Fund to the Jail Fund for $30,000 was withdrawn by County Treasurer Peggy Updike as funds were received. · Sheriff Dennis Switzer provided his monthly report: 953 calls for service were received. The Sherffi’s Office opened 26 investigations, made 43 arrests, investigated 23 collisions, issued 96 citations, served 222 civil/criminal summons, completed 233 auto inspections, traveled 5,187 miles on fugitive transports and worked 62.5 hours of court security. Switzer said two court security officers are in the hiring process. · Court approved advertising for bid for the Grant County Road Department materials and supplies for Fiscal Year 2026-2027. Dills said this is the “time of year we are beginning to prepare for budget” and this is part of the process. · Dills had added an agenda item to allow him to sign a contract with “Civil Con Incorporated” for replacement of Ford’s Mill Road bridge. The company is a “licensed consulting engineering” firm that will provide plans for the bridge as well as assist the county in obtaining funding from the state to replace the bridge. Court approved this unanimously. · Dills noted the County Ethics Board met Feb. 23 and “reviewed all the current elected officials, all the individuals that [are] running for public office.” No violations were found. · Dills said Grant County Farmers’ Market has again asked to use property by the Whippy Dip. They submitted their request along with proof of insurance. He has approved that request. The next meeting of the Grant County Fiscal Court is scheduled for Tuesday, March 17, 2026 at 6 p.m. at the Courthouse, 101 North Main Street Williamstown. For more information on the meeting, call (859) 823-7561. Your comment has been submitted.
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A file photo of a California Highway Patrol vehicle. A truck transporting a shipment of solar panels caught fire Friday on a San Diego highway near the neighborhoods of Normal Heights and Kensington, according to the California Highway Patrol. The panel fire erupted around 7 a.m. Friday on southbound Interstate 15 just north of Adams Avenue, according to the CHP communications. Stream San Diego News for free, 24/7, wherever you are with NBC 7. 🔥Car Fire🔥 UPDATE: 3/6/26 @ 7:40 AM
I-15 SB, north of Adam’s Ave., everything has been moved to the right shoulder.
All lanes are open. CHP communications said that fire was seen coming from the truck’s engine, with “huge flames and lots of smoke.” As of 8 a.m., all lanes have reopened on southbound I-15 north of Adams, the CHP said. No injuries were immediately reported.
Thank you for visiting nature.com. You are using a browser version with limited support for CSS. To obtain the best experience, we recommend you use a more up to date browser (or turn off compatibility mode in Internet Explorer). In the meantime, to ensure continued support, we are displaying the site without styles and JavaScript. Advertisement Nature Communicationsvolume 16, Article number: 4148 (2025) Cite this article 13k Accesses 55 Citations 39 Altmetric Metrics details The interfacial contact between NiOx and self-assembled monolayers (SAMs) in wide-bandgap (WBG) subcells limits the efficiency and stability of all-perovskite tandem solar cells (TSCs). The strongly acidic phosphoric acid (PA) anchors in common PA-SAMs corrode reactive NiOx, undermining device stability. Moreover, SAM aggregation leads to interfacial losses and significant open-circuit voltage (VOC) deficits. Here, we introduce boric acid (BA) as a milder anchoring group that chemisorbs onto NiOx via strong –({{rm{BO}}}_2{mbox{-}}) –Ni coordination. A benzothiophene-fused head group enhances interfacial bonding through S–Ni orbital interactions, yielding higher binding energy than PA-SAMs. This design also promotes homogeneous SAM formation without aggregation. Resultantly, the WBG cell exhibits an improved PCE to 20.1%. When integrated with narrow bandgap (NBG) subcell, the two-terminal (2T) TSCs achieve an ameliorative PCE of 28.5% and maintain 90% of the initial PCE after maximum power point tracking (MPP) under 1 sun illumination for 500 h. All-perovskite tandem solar cells (TSCs), consisting of a wide-bandgap (WBG, 1.7–1.8 eV) top cell paring with a narrow bandgap (NBG, 1.2–1.3 eV) bottom cell, have been presented as a promising approach to breaking the Shockley-Queisser (SQ) limits of single-junction perovskite solar cells (PSCs)1,2,3. With the rapid advancements of subcells and interconnection layers, TSCs have reached certified power conversion efficiency (PCE) of 30.1%, demonstrating the great potential to be commercialized as cost-effective photovoltaic (PV) technology4,5. Whereas, photovoltaic efficiency and stability of all-perovskite TSCs are both severely limited by the suboptimal interfacial contacts between NiOx and self-assembled monolayers (SAMs) in WBG subcell. Though SAMs directly coating on transparent conductive oxides (TCO, including ITO or FTO) substrates demonstrates a universal way for the development of single-junction inverted PSCs6,7, NiOx/SAM combination has been generally utilized as a hole-transporting layer (HTL) in WBG cells and TSCs8,9,10,11. This might be due to the commonly observed wrinkle morphological features of the buried WBG perovskite with much higher roughness than that of 1.55 eV bandgap perovskite (low content of Cs and Br). Therefore, NiOx is required to prevent current leakage between perovskite/ITO or FTO electrodes, as a single SAM layer is too thin to avoid shunting. While, due to the higher reactivity of NiOx than ITO and FTO12,13, the strong acidic phosphoric acid (PA) anchor in the widely employed PA-functionalized SAMs would corrode NiOx, which is detrimental to the long-term stability of solar cell devices. Additionally, the easy agglomeration of the commonly used PA-functionalized SAM leads to unsatisfied surface coverage and some weakly anchored SAMs through OH···O=P hydrogen bonding. Such loosely bonded sites are prone to be desorbed by strong polar solvents such as DMF14, resulting in a random redeposition at the perovskite bottom layer. It not only leads to nonradiative recombination and substantial VOC deficit15,16,17,18, but also severely limits the operational stability of PSCs. Besides, WBG perovskite with a high Br content (40%) suffers from an inhomogeneous nucleation-crystallization process, characterized by a markedly rapid crystallization rate for Br-rich perovskite. This phenomenon may stem from the different coordination strength between FA-DMSO and PbI2/PbBr2-DMSO adducts19,20,21. Consequently, nonuniform I-rich and Br-rich regions are formed, which further lead to trap-assisted nonradiative recombination centers. Such inferior film morphologies are also susceptible to phase segregation under continuous illumination, compromising the operational stability of WBG cells22,23. Previous studies have shown that SAMs could play multiple roles in the performance of PSCs, that is strengthening the bridging bonds between SAM and metal oxide substrates (ITO, FTO, NiOx), and simultaneously regulating the crystallization of WBG perovskite films24,25,26,27. A commonly employed strategy to address issues related to SAM wettability and agglomeration in inverted PSCs with a bandgap of 1.55 eV is the co-assembly of SAM with small molecules on ITO or FTO. This approach improves surface coverage and morphology of the buried perovskite layer10,14,15,25,26,27,28. It is important to note that while PA-based SAMs have been widely used to modify the surface of ITO or FTO29,30, they do not necessarily fit on NiOx substrate, considering the higher reactivity of NiOx than ITO/FTO. This can cause corrosion at the interface, leading to stability issues13, particularly when upscaling device fabrication, where TCO substrates necessitate rinsing in SAM solution for the anchoring process3. Herein, in this work, the acidic-weakened boric acid functionalized SAM (BA-SAM) with various fused cores are reported to anchor onto the NiOx surface. Density functional theory (DFT) calculations and X-ray photoelectron spectroscopy (XPS) analysis reveal strong coordination between –({{rm{BO}}}_2{mbox{-}}) and Ni. The design of benzothiophene fused core as the functional head group strengthened the interfacial bonding through an additional orbital-pair contribution from S-Ni interaction, resulting in a higher binding energy (−6.73 eV) than that of PA-SAM (−6.14 eV) on NiOx. Such interaction between the fused head core and NiOx surface further benefits the homogeneous formation of BA-functionalized SAM on the NiOx surface without aggregation. These expect to improve the surface coverage and enhance the interfacial stability of the WBG subcell. Additionally, we elucidate a π-cation interaction between benzothiophene fused core and FA+ cation through a combination of theoretical and experimental analysis, which engenders a balanced crystallization rate of I-rich and Br-rich perovskite phases. The resulting WBG perovskite film presents a homogeneous I/Br distribution and mitigated phase segregation under continuous illumination aging. By further mixing BA-SAM with a small amount of the commonly utilized Me-4PACz (at a molar ratio of 4:1, BA-SAM: Me-4PACz), the WBG cell shows a substantial improvement in PCE from 18.9% (control device based on Me-4PACz) to 20.1%, with VOC of 1.30 V, JSC of 18.2 mA cm−2 and FF of 84.8%. Integrating with the NBG subcell, the 2T TSCs achieve an ameliorative PCE of 28.5%, along with notable operational stability by retaining 90% of the initial PCE after maximum power point tracking (MPP) under 1 sun illumination for 500 h. To dig into the adsorption mechanism of different SAMs on NiOx surface, DFT calculations including the electron localization function (ELF) were performed on Me-4PACz/NiOx, Me-4BACz (substituting PA with BA)/NiOx, S-BA/NiOx and O-BA/NiOx, N-BA/NiOx models (Supplementary Fig. 1 and Fig. 1a–d). Noted that S-BA, O-BA, and N-BA are BA-functionalized SAMs with benzothiophene, pyridine, and benzofuran cores, respectively. Firstly, we analyze the adsorption mechanism of BA on NiOx by comparing Me-4PACz/NiOx and Me-4BACz /NiOx models, as shown in Supplementary Fig. 1f, g. Figure 1b demonstrates an obvious symmetry breaking and deformation between –({{rm{BO}}}_2{mbox{-}}) and Ni, suggestive of orbital overlapping of O-Ni bonding. The differential charge density mapping in Supplementary Fig. 1m exhibits charge transfer between –({{rm{BO}}}_2{mbox{-}}) and Ni as well. This is further confirmed by the Crystal Occupied Hamilton Population (COHP) calculation. Illustrated by Fig. 1e, the interactions between Ni 3d-O 2p contribute to the formation of the bonding state, while the anti-bonding state originates from Ni 4s-O 2s2p and Ni 3d-O 2p. The efficient anchoring could be attributed to the high Lewis acidity of NiOx, which facilitates a dominate coordination process. In contrast, on less Lewis acidic ITO substrates, the adsorption mechanism of SAM involves heterocondensation first, primarily affected by pKa of the tailoring group6. Such orbital-pair contribution compensates for the relatively weak acidity of the BA group, generating a comparable binding energy of Me-4BACz (−5.58 eV) than that of Me-4PACz (−6.14 eV) (Supplementary Table 1). The results are consistent with the previous report on BA-based SAM31. ELF images absorbed by (a) Me-4PACz, (b) S-BA, (c) O-BA, (d) N-BA on the NiOx surface were obtained by DFT calculation. COHP analysis of (e) O-Ni and (f) S-Ni bonding between S-BA and NiOx surfaces. (g) The Ni 2p3/2) XPS spectra of the NiOx film with SAMs (Me−4PACz, S-BA-SAM, O-BA-SAM and N-BA-SAM). KPFM images of (h) the NiOx/Me-4PACz original film and (i) the film after DMF washing and (j) the film after 6 h of light; (k) the NiOx/S-BA-SAM original film and (l) the film after DMF washing and (m) the film after 6 h of light. CPD distributions of (n) NiOx/Me-4PACz and (o) NiOx/S-BA-SAM. To further study the effects of fused rings on the adsorption, ELF images of S-BA/NiOx were plotted. From Fig. 1b, a symmetry breaking and deformation between S (from S-BA) and Ni (from NiOx) is unveiled, illustrating a charge transfer between the S atom and NiOx. Similarly, from Fig. 1f, the COHP shows a bonding state from Ni 4s-S 3p and an anti-bonding state from Ni 3d4s-S 3p. This interaction, which is absent in Me-4PACz/NiOx, further contributes to strengthening the bonding between the S-BA and NiOx surface. As a result, the S-BA shows stronger anchoring than Me-4PACz on the NiOx surface, with a more negative binding energy of −6.73 eV. Comparatively, O-BA and N-BA show less negative binding energies of −6.67 and −6.25 eV, respectively. These results confirm the robust anchoring of S-BA on NiOx. On top of that, as oxygen vacancies are also active sites for SAM adsorption14, the adsorption models of different SAMs on oxygen-deficient NiOx surfaces were also calculated. From the results in Supplementary Fig. 2, the binding energies can be summarized in Supplementary Table 2. It is seen that S-BA also shows a more negative binding energy of −6.53 eV than the Me-4PACz analog (−6.34 eV), confirming the preferred adsorption of S-BA on oxygen-deficient NiOx. Hole conducting characteristics of the above BA-tailed SAMs were then investigated by quantum chemical calculations. From the frontier molecular orbitals in Supplementary Fig. 3, it is observed that the electron-rich carbazole dominates both HOMO and LUMO levels in Me-4PACz and Me-4BACz, delivering high-lying LUMO levels of −0.92 eV and −0.76 eV, respectively. The high excited state energy of carbazole under illumination makes it susceptible to chemical reactions. It would lead to light-induced degradation, which is disadvantageous to interfacial contacts and charge transfer between SAM and NiOx32. Contrastingly, Supplementary Fig. 3 shows a high level of delocalization of HOMO and LUMO levels near the S atom and anchoring group. Such delocalization is even more intense in the mixed S-BA and Me-4PACz system (denoted as S-BA-SAM), as shown in Supplementary Fig. 3, which is favorable for electron/charge delocalization and transport, as well as a more stable LUMO level (S-BA-SAM: −1.45 eV vs. Me-4PACz −0.92 eV). The results are consistent with the experimental findings that mixing S-BA with a small content of Me-4PACz (at a molar ratio of 4:1, BA-SAM: Me-4PACz) benefits the hole-transporting process, in terms of achieving larger conductivity, higher hole mobility, and improved photovoltaic efficiency, which will be discussed in the later context. Therefore, in the following experimental studies, the mixed BA-functionalized SAM with Me-4PACz were characterized in comparison with Me-4PACz. Noted that DFT calculations were again adopted to study the bonding configurations of mixed SAM, in an attempt to unveil the anchoring competition process between BA- and PA-tailed molecules in the mixed SAM system. ELF diagram of S-BA-SAM in Supplementary Fig. 4 shows the deformation of Ni upon its interaction with O and S, evidencing the chemical interactions of Ni-O and Ni-S. This supports that S-BA remains binding to NiOx through the original three-site anchors (two covalent B-O bonds and one S-Ni interaction), even under the coexistence of Me-4PACz. Similar results are also observed in the oxygen-deficient NiOx system (Supplementary Fig. 5). Therefore, it is proved that Me-4PACz would not cause the desorption of BA-based SAM. The anchoring strength of SAMs on NiOx was then evaluated using XPS measurements, with key parameters summarized in Supplementary Table 3. Firstly, it is noted that the construction of monolayer SAM in PSC devices is actually an ideal case. Han et al. pointed out that highly efficient PSCs require a deposited SAM thicker (~6 nm) than one monolayer, because the deposition of perovskite layer (DMF solvent) would wash away some SAM molecules. On top of this, most studies in high-impact journals did not incorporate a post-cleaning treatment in their experimental procedures3,8,27,33,34,35. Even when post-treatment was mentioned36,37, it involved spin-casting ethanol onto the SAM film, instead of rinse. As the former would just wash away some molecules on the top layer, while the latter leads to the formation of exact “monolayer”, which is not good for device performance. Following this spin-coating cleaning treatment, the NiOx/SAM films were post-cleaned with ethanol through spin-casting before test. As shown in Fig. 1g, the XPS spectra of NiOx/Me-4PACz film exhibit Ni 2p3/2 peaks at 855.9 and 854.1 eV, corresponding to Ni3+ and Ni2+, respectively. With the co-SAM strategy by S-BA-SAM and O-BA-SAM, Ni 2p3/2 spectra shift downward by 0.4 eV and 0.2 eV, respectively, while that of NiOx/N-BA-SAM shows negligible shifts. The significant downward shifts in NiOx/S-BA-SAM are illuminative of facilitated charge transfer between NiOx and S-BA-SAM, suggesting an increased anchoring strength of S-BA-SAM on NiOx38,39. This enhanced interfacial bonding is further supported by a reduction in the Ni3+ ratio, from 79.6% in NiOx/Me-4PACz film to 78.5% with S-BA-SAM and 79.1% with O-BA-SAM. It reflects an improved surface chemical environment, which benefits the long-term stability of the buried interface39. The corrosion effects of the SAM on NiOx were then studied, which could result from two processes. First, the solution deposition process of SAM onto NiOx exposes the NiOx to an acidic environment, leading to a corrosive reaction of NiOx + 2H+ → nNi2+ + (1-n)Ni3+ + H2O. To quantify the leaching of Ni2+ and Ni3+ ions, ITO/NiOx substrates were immersed in S-BA-SAM or Me-4PACz solution for 5 h, followed by detection of the Ni ion concertation using Inductively Coupled Plasma Optical Emission Spectrometer (ICP-OES). As shown in Supplementary Fig. 6, the concentration of Ni ions in S-BA-SAM solution (29 μg/L) is significantly lower than that in Me-4PACz solution (87 μg/L), confirming the suppressed corrosion of NiOx by less acidic BA-functionalized SAM. Second, it is unveiled from Fourier transform infrared (FTIR) spectroscopy (Supplementary Fig. 7) that considerable amount of PA-tails fail to bind to NiOx through P-O-Ni covalent bonds (with strong P-OH signal existed), suggesting a substantial presence of phosphoric acid groups on the NiOx surface. aligning with other published reports40. XPS analysis further quantifies the number of covalent bonds in S-BA-SAM/NiOx and Me-4PACz/NiOx films. As illustrated in Supplementary Fig. 8a, b, Me-4PACz/NiOx exhibits a low P-O-Ni to P-O-H ratio of only 27%, supporting the presence of significant acid groups on the surface. Contrastingly, the S-BA-SAM/NiOx shows notably higher B-O-Ni to B-O-H ratio of 47%. This might be attributed to the easier aggregation of Me-4PACz, which will be elaborated upon later. The presence of -POOH on the surface can corrode the NiOx substrate, particularly under thermal or light accelerated aging, which is again studied by ICP-OES. To obtain measurable results, 8 pieces of 2 cm × 2 cm Me-4PACz/NiOx substrates were aged under light illumination for 40 h, followed by immersion in ethanol solvent for 20 min to wash out the leached Ni ions. As shown in Supplementary Fig. 9, a considerable amount of Ni ions (32 ug/L) was detected, verifying the corrosive reaction. In contrast, the S-BA-SAM/NiOx substrates aged under the same condition show negligible content of Ni ions, suggesting enhanced interfacial stability. The corrosive effects of –POOH on NiOx in thin film states were further analyzed by XPS spectra, where the peak area ratio of hydroxide and lattice O atoms (Ni-O) in O 1s core was determined14. As shown in Supplementary Fig. 10, the ratio of hydroxide and lattice O atoms in the NiOx/Me-4PACz film after light aging increases significantly from 82% to 122%, suggesting the increment of unbonded –OH and decrement in covalent Ni-O on NiOx surface. The results indicate deteriorated interfacial contact with significant desorption of Me-4PACz from the NiOx surface, which could be due to corrosive effects of unanchored –POOH on NiOx in thin film states. Aging tests on ITO/Me-4PACz samples were also conducted to have a comparison with those on NiOx substrate. From XPS spectra shown Supplementary Fig. 11, ITO/Me-4PACz shows slightly increased peak area ratio of hydroxide and lattice O atoms from 84% to 102% after 5 h light aging, further suggesting the higher reactivity of NiOx than ITO and the urgency of using weak-acid anchors. Using the BA-based SAM, the ratio in the NiOx/S-BA-SAM shows marginal changes (from 68% to 63%) under light aging, suggesting the less-acidic BA-SAM helps maintain the integrity of the interfacial contact. The influence of post-cleaning step and residual SAM molecules on the corrosion process were then analyzed by XPS measurements on NiOx/SAMs before and after ethanol washing. The XPS analysis (Supplementary Figs. 12, 13 and Supplementary Table 4) reveals a higher surface coverage for the unwashed sample (1.22 × 10−2) compared to the washed ones (1.02 × 10−2), indicating that a portion of residual molecules was removed from the top surface. Noted that even with the cleaning step (ethanol spin-casting rather than rinsing), a film thicker than a monolayer is formed, which is recognized to be critical for the fabrication of highly efficient PSCs3,8,14,27,33,34. After 5-h light aging, the unwashed ITO/NiOx/Me-4PACz exhibits a comparable increment (from 96% to 145%) in the peak area ratio of hydroxide to lattice O atoms relative to the washed ones (from 82% to 122%), as shown in Supplementary Fig. 14. This suggests that the additional unbonded –POH groups on the top surface have a limited impact on the interfacial stability, implying that the molecules near the buried interface play a more significant role in the corrosion process. A similar trend was also observed in ITO/NiOx/S-BA-SAM films as well (Supplementary Fig. 15). This finding aligns with our observation of similar device stabilities for PSCs with or without washing step. Another critical issue raised by the traditional Me-4PACz is its tendency to aggregate or crystallize during solution deposition, driven by strong van der Waals interactions, particularly π-π interactions. This has also been testified by molecular dynamic (MD) calculations in Supplementary Fig. 16, which shows the formation of Me-4PACz dimers, trimers, and tetramers aggregations. The molecular aggregation would lead to unsatisfied surface coverage and some weakly anchored SAMs through OH···O=P hydrogen bonding. Such loosely bonded sites could be desorbed by strong polar solvents such as DMF14, resulting in random redeposition at the perovskite bottom layer. It expects to severely limit the operational stability of PSCs. S-BA-SAM, on the other side, shows homogeneous distribution without aggregation, which might be due to the strong interaction between the benzothiophene on S-BA and NiOx, as well as the less π-π interactions through benzothiophene, as illustrated by the MD calculations in Supplementary Fig. 16b. Correspondingly, the resistance of two acid-functionalized SAMs to DMF was thus tested. The NiOx/SAM samples rinsed in DMF solvent for different periods were prepared, which were subsequently measured by XPS. Samples are not exposed to ambient air at any time. Robustness of SAM (S-BA-SA and Me-4PACz) on the NiOx surface upon DMF washing could be determined by the coverage factor, which was calculated as the core level area of C1s in SAMs molecule normalized to the NiOx 3p3/2 core level area in XPS41. From the C 1s and Ni 2p3/2 XPS spectra in Supplementary Figs. 17–22, surface coverage could be summarized in Supplementary Fig. 23 and Supplementary Tables 5, 6. S-BA-SAM shows significantly higher coverage factors under a variety of DMF washing volumes (0–1200 μL) than those of Me-4PACz, evidencing a decreased desorption of S-BA-SAM from NiOx during the deposition process of perovskite film. The less corrosive effect, together with improved robustness of S-BA-SAM on NiOx, is expected to improve the interfacial contact and its long-term stability. Subsequently, the structural and electronic properties of NiOx/SAM were assessed before and after light aging and DMF washing. As shown in Supplementary Fig. 24, the Raman peak at 793 cm−1 belongs to the B–O bond42. Other peaks near 1000–1400 cm−1 (C–H and C–C stretching vibrations in the methyl segment) and 1600 cm−1 (C–C stretching in benzothiophene) confirm the presence of benzothiophene43,44. As shown in Supplementary Fig. 24a–c, the characteristic Raman peaks of the sample show minor changes after DMF washing and illumination for 12 h. While in the NiOx/Me-4PACz system, the intensity is greatly reduced, indicating that BA-functionalized SAM possesses higher structural stability. Similarly, the surface potential changes of NiOx/SAM layers were inspected by Kelvin probe force microscopy (KPFM). As shown in Fig. 1h–o, the contact potential difference (CPD) distribution for S-BA-SAM is narrower than that of the control sample, indicative of the homogeneous formation of S-BA-SAM on NiOx substrate. Additionally, mixed SAM strategy shifts the CPD peak from −791 mV (control) to less negative values of −697 mV, −741 mV, and −742 mV for S-BA-SAM, O-BA-SAM and N-BA-SAM, respectively. This suggests a reduction in the work function of the NiOx/SAM layer, as described by the equation CPD = (Φtip–Φsample)/e45. This effect might be ascribed to the less electronegative BA-tail for lowering the p-type characteristics of the surface. The results are consistent with the energy level alignment extracted from ultraviolet photo-electron spectroscopy (UPS) measurements, as illustrated in Supplementary Figs. 25–28. Moreover, the control film (NiOx/Me-4PACz) shows a substantial CPD shift of 167 mV (from −791 mV to −642 mV) upon DMF washing, illustrating a weak adsorption of Me-4PACz on NiOx due to molecular aggregation. Conversely, NiOx/S-BA-SAM shows negligible CPD shift before and after washing, concealing stronger bonding interactions. As a result, light aging (continuous illumination for 6 h) imposes a minimal impact on the surface potential variations of the NiOx/S-BA-SAM layer. In addition to that, conductivities of NiOx/SAMs were further measured. From Supplementary Fig. 29, NiOx/S-BA-SAM film shows larger conductivity (3.84 × 10−3 S m−1) than that of NiOx/Me-4PACz (3.16 × 10−3 S m−1), indicative of improved hole conducting ability. Its conductivity remains almost constant before and after illumination, while NiOx/Me-4PACz shows a significant reduction to 1.91 × 10−3 S m−1 after 12 h of illumination. The above results demonstrate enhanced structural and electronic stability of S-BA-SAM. FTIR spectra of FAI, FAI + SAM, and SAM were recorded to dig into the π-cation interactions between FA+ cation and SAM. From Fig. 2a and Supplementary Fig. 30, it is seen that the skeletal vibration of FA+46, shifts from 1716.1 cm−1 to 1721 cm−1, 1723.5 cm−1, 1716.1 cm−1 and 1718.0 cm−1, respectively, for Me-4PACz, S-BA-SAM, O-BA-SAM and N-BA-SAM. The shifts of FTIR peaks to higher wavenumbers could be explained by the electron-withdrawing effects of the fused rings. Benzothiophene fused ring, with the strongest electron capture ability, imparts the large force constant to the FA+ cation (benzothiophene > pyridine > benzofuran)47, resulting in the highest vibrational frequency. Therefore, the energy required for the transition from the ground state to the first excited state (i.e., the highest vibrational frequency) is greatest for the FAI/S-BA-SAM sample. The results testify the strong π-cation interactions between FA+ and S-BA-SAM. (a) FTIR of FAI, FAI + Me-4PACz and FAI + S-BA-SAM. In situ PL spectroscopy of perovskite film during spin-coating with (b) Me-4PACz and (c) S-BA-SAM modification. (d) Peak position variations of Me-4PACz and S-BA-SAM modified perovskite during spin coating. (e) PL intensity variations of Me-4PACz and S-BA-SAM modified perovskite during spin coating. Such interactions tend to slow the crystallization rate of both FAI/PbI2 and FAI/PbBr2, thereby inducing a homogeneous formation of I-rich and Br-rich regions. To verify this, in-situ UV-Vis absorption spectroscopy and photoluminescence (PL) measurements were performed, enabling real-time monitoring of perovskite nucleation and crystallization during spin-coating and thermal annealing, as depicted in Fig. 2b, c and Supplementary Fig. 31. From the 2D pseudo-color plots (Fig. 2b, c), the PL peak positions and intensities over time provide critical insights. Clear PL signals are detected immediately upon antisolvent dripping at ~24 s, indicative of the onset of perovskite nucleation. As shown in Fig. 2d, PL signals in both films initially appear at short wavelengths (630–640 nm) and then redshift to ~660–670 nm over 24–26 s. This reflects that the nucleation of the Br-rich region occurs first in the WBG perovskite film, followed by I− diffusion into the Br-rich nuclei, realizing the mixed I/Br nucleation process48. Notably, S-BA-SAM treatment accelerates the nucleation of the I-rich component, as highlighted by the red-dotted circle at ~25 s. It delivers heterogeneous nucleation of mixed I/Br halide perovskite, stabilizing the WBG perovskite phase during spin-coating (~25–50 s). Contrastingly, the control WBG film deposited on Me-4PACz presents an uncontrollable nucleation manner with spontaneous phase segregation of the I-rich region and Br-rich region. This engenders nonradiative recombination and poor light stability of WBG perovskite film, negatively affecting both photovoltaic efficiency and operational stability of the subcell devices48. Additionally, it can be seen from Fig. 2e that the PL intensity of S-BA-SAM is higher than that of Me-4PACz. In situ UV-Vis absorption spectra during spin-coating (Supplementary Fig. 31a, b) align well with the in situ PL spectra (Supplementary Fig. 31c, d). Specifically, S-BA-SAM treated perovskite film shows a rapid absorption band-edge expansion upon antisolvent dripping, suggesting a fast and homogenous nucleation of I/Br mixed halides. The rapid nucleation further gives rise to densely formed perovskite nuclei in the target film, which could be reflected by the significantly higher absorbance in S-BA-SAM treated perovskite film than that of the control ones. The PL spectroscopy of both Me-4PACz and S-BA-SAM treated perovskite films during thermal annealing are shown in Supplementary Fig. 32. It is seen that the S-BA-SAM treated sample shows a gradual PL intensity increment during the first 4 s, while that of the control sample instantly reaches the highest value. It suggests a slower crystal growth of perovskite, which assists in the formation of higher-quality perovskite film49. The attenuated PL intensity in both samples could be explained by the unavoidable film degradation under intense incident light excitation. Since the crystallization process typically begins at the air/liquid surface, a faster Br-rich region crystallization rate over the I-rich one leads to a nonuniform vertical distribution of Br and I, with a large amount of Br frozen near the film surface50,51,52. This is evidenced by the time-of-flight secondary ion mass spectrometry (TOF-SIMS) analysis of the whole devices. As shown in Supplementary Fig. 33a, b, the mixed SAM strategy results in a lower Br/I ratio in the target film than that in the control film, further illustrating a homogeneous distribution of halide components. To study whether the crystallization changes were caused by the wettability of the buried layer, contact angles of perovskite precursors on NiOx/SAM were measured. Presented by Supplementary Fig. 34, the Me-4PACz film exhibits a mean contact angle of 86.3°, whereas the S-BA and S-BA-SAM film demonstrate slightly lower but comparable contact angles of 68.3°, and 72.3°, respectively. The slight decrement might be due to the homogeneous distribution of SAM without aggregation (as evidenced by MD calculation and KPFM results). While the core group of S-BA (benzothiophene) is still hydrophobic, both pure S-BA and its mixture with Me-4PACz (S-BA-SAM) do not show a significant reduction in contact angle values. As a result, we conclude that the primary influence of buried SAM on perovskite crystallization arises from the π-cation interactions between benzothiophene and FA+. The chemical environment of the WBG perovskite surfaces was subsequently studied by XPS measurements. Illustrated in Supplementary Fig. 35a, Pb 4f5/2 and Pb 4f7/2 peaks shift downward from 143.2 and 138.4 eV (Me-4PACz) to 143.0 and 138.2 eV for S-BA-SAM, suggestive of a reduction in undercoordinated Pb2+. While those peaks show marginal shifts for O-BA-SAM and upshift to 143.4 and 138.6 eV for N-BA-SAM. This might be attributed to the more balanced crystallization of Br/I halide in S-BA-SAM treated film, which effectively suppresses the phase segregation, particularly at the film surface (as evidenced by the TOF-SIMS result). As phase segregation typically induces tensile strains in perovskite lattices or grains, which degrades the film surface and exposes undercoordinated Pb2+. Improved crystallization, as seen in the S-BA-SAM treated perovskite film, could stabilize the perovskite lattice and strengthen the N-H···I hydrogen bonds. This is evidenced by the downshift in the I 3d XPS spectra of S-BA-SAM treated perovskite film, as illustrated in Supplementary Fig. 35b. Effects of the modulated crystallization kinetics on the top and bottom surface morphologies were directly assessed by scanning electron microscopy (SEM) images. Among the top-surface morphologies of WBG perovskite on different SAMs illustrated in Fig. 3a, b and Supplementary Fig. 36, the S-BA-SAM-based target film demonstrates the largest and most compact grains without unreacted PbI2 regions or pinholes. Similarly, the buried interface of S-BA-SAM/perovskite film shows greatly improved morphology compared with the control film, with markedly enlarged grain size and the elimination of numerous nanovoids (Fig. 3c, d). Such features render improved resilience of perovskite films to light illumination. Contrary to the severe degradation of the control film, the target films show negligible morphological changes (Fig. 3e–h). SEM images of the top surface of perovskite films on (a) Me-4PACz and (b) S-BA-SAM; SEM images of the buried interface morphology of perovskite films on (c) Me-4PACz and (d) S-BA-SAM; SEM images of the top surface of perovskite films on (e) Me-4PACz and (f) S-BA-SAM after 6-h light aging; SEM images of the buried interface morphology of perovskite films on (g) Me-4PACz and (h) S-BA-SAM after 6-h light aging. GIWAXS of perovskite films with (i) Me-4PACz and (j) S-BA-SAM modification with a variety of incident angles (α) 0.2°–1.0°. (k) Ratio of (100) to (110) diffraction peak intensities of perovskite films with Me-4PACz and S-BA-SAM modification with a variety of incident angles (α) 0.2°–1.0°. (l) Integrated azimuth angle at 14.24° (100) from GIWAXS pattern in Supplementary Figs. 37 and 38 (α = 0.2°). To scrutinize the crystallographic orientation from the surface to the bulk film along the vertical direction, grazing incident wide-angle X-ray scattering (GIWAXS) with a variety of incident angles 0.2°–1.0° were illustrated in Supplementary Figs. 37, 38 and Fig. 3i–k. From Fig. 3i, the control film on top of Me-4PACz exhibits a noticeable splitting of the diffraction peaks from the (200) lattice plane (~28.9°), which might be ascribed to the lattice distortion caused by residual stresses. Such a phenomenon disappears in the target film based on S-BA-SAM (Fig. 3j). Additionally, the target film shows an overall increased intensity ratio of the (100) and (110) diffraction peaks (I(100)/I(110)), as illustrated in Fig. 3k. It suggests that the mixed SAM strategy assists a preferred orientation of the (100) lattice plane throughout the entire film, which would benefit charge carrier transport across the perovskite lattices. Whereas, I(100)/I(110) values are significantly lower on both the top surface and the bottom layer in the control film. The reduced top-surface value might be due to uncontrolled Br/I halide crystallization kinetics, while the low value at the bottom layer might result from poor surface coverage of SAM and nanovoids formed at the buried interface. Additionally, azimuthal integration analysis of the (100) peak at q = 1 Å (Fig. 3l) verifies that the target film exhibits enhanced orientation, with stronger diffraction signals at azimuthal angles of 120° and 160°. This preferential growth direction likely enhances film performance by reducing defect state density, leading to a more ordered crystalline structure and improved film quality. These are further confirmed by the lower trap densities (1.73 × 1016 cm−3 vs. 1.63 × 1016 cm−3) and enhanced carrier transport mobilities (7.92 × 10−5 cm−2 V−1 s−1 vs. 6.47 × 10−5 cm−2 V−1 s−1) extracted from the IV characteristics in Supplementary Fig. 39. Presented by the GIWAXS patterns and the azimuth profiles of O-BA-SAM, and N-BA-SAM modified perovskite film in Supplementary Fig. 40, it is seen that they both have fewer effects on perovskite morphology compared to S-BA-SAM. As severe phase segregation in WBG perovskite would cause local lattice mismatch (between the I-rich and Br-rich regions) and the subsequent residual tensile stresses53,54, the residual stresses within the perovskite films were then quantitatively analyzed using depth-resolved grazing incident X-ray diffraction (GIXRD) patterns. The stress (σ) was calculated based on the following equation ({{rm{sigma }}}=frac{-{{rm{E}}}}{2(1+{v})}frac{{{rm{pi }}}}{180^circ },cot {{rm{theta }}}frac{partial (2{{rm{theta }}})}{partial {sin }^{2}Psi ,})55, where E and v respectively represent Young’s modulus and Poisson’s ratio of the perovskite film. From the 2θ-sin2Ψ plots (Supplementary Fig. 41) derived from the GIXRD patterns in Supplementary Fig. 42, the tensile stresses were determined to be 25, 22, 20, and 16 MPa for the control, O-BA-SAM, N-BA-SAM and S-BA-SAM treated WBG perovskite films, respectively. The released tensile stress could be accredited to the controllable crystallization of Br/I halide, as previously discussed, eliminating the lattice mismatch issues. It is in turn illustrates higher intrinsic perovskite film stability. The surface potential of both buried and top perovskite films on different NiOx/SAM substrates was further investigated by KPFM measurements, as illustrated in Fig. 4a–d and Supplementary Figs. 43–45. As summarized in Fig. 4e, the CPD of buried interfaces on mixed SAMs shifts upward by 91, 80, and 75 mV for S-BA-SAM, O-BA-SAM, and N-BA-SAM, respectively, as compared to that of the control film on Me-4PACz. The less negative CPD values are suggestive of more p-type characteristics of the buried interface properties, which is beneficial for hole conduction from perovskite to NiOx/SAM HTL. Meanwhile, the narrower CPD distribution for the perovskite films treated with S-BA-SAM (full-width at half maximum FWHM of 25 mV), O-BA-SAM (FWHM of 26 mV), and N-BA-SAM (FWHM of 32 mV) compared to the control film (FWHM of 35 mV) implies improved film homogeneity. Similarly, in Supplementary Figs. 43–45, KPFM of the top surfaces reveals comparable CPD peaks of 114, 96, 87, and 149 mV for the Me-4PACz, S-BA-SAM, O-BA-SAM, and N-BA-SAM based perovskite films, respectively. These values are consistent with the Fermi level of perovskite extracted from UPS measurements (shown in Fig. 4f). The NiOx/S-BA-SAM system demonstrates a well-matched highest occupied molecular orbital (HOMO) level with the perovskite layer (Fig. 4f), minimizing interfacial energy losses. Notably, S-BA-SAM-based perovskite film shows much narrower FWHM than those of others, further indicating enhanced film uniformity. Under continuous light illumination aging for 6 h, the control film exhibits a broadening of CPD distributions and a significant shift to less positive values (from 114 mV to 75 mV), which might signify the formation of higher work function PbI2 regions (5.9 eV). This reflects the degradation of control WBG perovskite into I-rich and Br-rich regions. In contrast, the film on NiOx/S-BA-SAM substrate shows only minor changes in surface potential characteristics after light aging (Supplementary Fig. 44c), evidencing suppressed photo-induced phase segregation. KPFM images of the perovskite buried interface modified by (a) Me-4PACz, (b) S-BA-SAM, (c) O-BA-SAM, (d) N-BA-SAM. (e) CPD distribution histogram of the perovskite buried interface modified by Me-4PACz, S-BA-SAM, O-BA-SAM, N-BA-SAM. (f) Energy level diagrams of the SAM (Me-4PACz, S-BA-SAM, O-BA-SAM, N-BA-SAM)/perovskite. PL mapping of the bottom surface of perovskite films on Me-4PACz (g) before and (h) after 5-h light aging; PL mapping of the bottom surface of perovskite films on S-BA-SAM (i) before and (j) after 5-h light aging; PL mapping of the top surface of perovskite films on Me-4PACz (k) before and (l) after 5-h light aging, PL mapping of the top surface of perovskite films on S-BA-SAM (m) before and (n) after 5-h light aging. Steady-state and time-resolved photoluminescence (PL and TRPL) measurements were conducted on the four WBG perovskite films. As shown in the PL spectra (Supplementary Fig. 46), the PL quenching increases with mixed SAM substrates, following the trending of incremented electron capture effects of the fused ring (i.e., benzothiophene > pyridine > benzofuran), which suggests a reduction in trap-assisted nonradiative recombination losses. Consistently, bi-exponentially fitting of the TRPL spectra (Supplementary Fig. 46b, c) gives remarkably elongated carrier recombination lifetime from 26.1 (control) to 483.9, 247.2, and 238.72 ns, respectively, for S-BA-SAM, O-BA-SAM, and N-BA-SAM, in line with the PL spectra. Fitting details are shown in Supplementary Table 7. The reduced defects and recombination could be attributed to the homogeneous crystallization of Br/I regions, suppressing the formation of narrow bandgap recombination sites. Light stability of the WBG perovskite on different NiOx/SAM substrates was subsequently assessed. As shown in the evolution of the PL spectra under continuous light illumination (Supplementary Fig. 47), the corresponding 2D pseudo-color images are plotted in Supplementary Fig. 48. It is evident that the PL spectrum of the control film exhibits significant redshifts during the first 90 min of illumination, indicating the onset of phase segregation. This suggests that photo-generated charge carriers tend to migrate to low-energy I-rich regions followed by being quenched. Upon extended illumination for 5 h, additional shoulders appear around ~760–810 nm, manifesting severe phase segregation of the I/Br mixed halides into distinct Br-rich and I-rich regions. Contrastingly, the WBG perovskite on NiOx/S-BA-SAM displays only a marginal redshift without the appearance of lower-energy PL shoulders, evidencing the significantly suppressed phase segregation and enhanced light stability of the target film56. Photoluminescent properties of the perovskite films at the microscopic scale were examined using confocal PL mapping, before and after light illumination. Both top and buried surfaces were analyzed. Comparing PL mapping images of the fresh perovskite films (bottom interface) in Fig. 4g–j, the target film on NiOx/S-BA-SAM exhibits an overall enhancement in PL intensity across a 5 μm×5 μm area, whereas the control film exhibits obvious inhomogeneity with “wrinkle” morphologies (Supplementary Fig. 49). The ameliorated buried interfacial photoluminescent characteristics could be attributed to the strong anchoring of S-BA-SAM on NiOx and a complete surface coverage, which promotes homogeneous crystallization of Br/I halides. After 5 h of continuous light illumination, the buried interface undergoes severe degradation, with coarsened film morphology (Supplementary Fig. 49) and reduced PL intensities (Fig. 4h). Contrastingly, the target buried film retains its intact film morphology and uniform PL intensity distribution, as illustrated in Fig. 4i, j and Supplementary Fig. 49. Similarly, the top surface of perovskite film on NiOx/S-BA-SAM substrate also demonstrates preferable photoluminescent properties and light stability over those of the control film, as shown in Fig. 4k–n and Supplementary Fig. 50. Motivated by the balanced Br/I halide crystallization, enhanced HTL/perovskite interfacial stability, and improved optoelectronic properties of perovskite films achieved through the mixed SAM strategy, single-junction WBG PSCs were fabricated using the device architecture of NiOx/SAM or mixed SAM/ WBG/C60/ALD SnO2/Ag, as shown by the inset of Fig. 5a. J-V characteristics of these cells were recorded under simulated 1 sun illumination at an intensity of 100 mW/cm2 (AM 1.5 spectrum). The optimal molar ratio of BA-SAMs mixed with Me-4PACz was determined to be 4:1 (BA-SAM: Me-4PACz), as illustrated in Supplementary Fig. 51. Figure 5a compares the J-V characteristics of the champion devices of control and mixed SAM-based WBG PSCs. From the photovoltaic parameters summarized in Supplementary Table 8, S-BA-SAM based device shows remarkably enhanced PCE from 18.9% to 20.1%, along with improvements in VOC from 1.28 V to 1.30 V, JSC from 18.1 to 18.2 mA cm−2 and FF from 82.08% to 84.8%, compared to those of the control device. As seen in Supplementary Table 9, the N-BA-SAM and O-BA-SAM modified devices show progressively increased PCE over that of the control device, in line with the electron capture effect of the boron acid-SAMs. Noted that PSCs based on pure S-BA show relatively lower PCE of 19.0% than that of mixed S-BA-SAM based ones, with VOC of 1.28 V, JSC of 18.1 mA cm−2 and FF of 82.1% (Supplementary Fig. 52 and Supplementary Table 10). This could be explained by the previous quantum chemical calculations that a mixture of S-BA and Me-4PACz affords a higher degree of charge delocalization in frontier orbitals than pure S-BA, facilitating hole transport. The assumptions are also testified by the conductivity (Supplementary Fig. 29) and mobility measurements (Supplementary Fig. 39). The steady-state PCE output (SPO) tracking results (Fig. 5b and Supplementary Fig. 53) show steady-state PCEs of 17.9%, and 19.3%, 18.7%, and 18.2% for the control, S-BA-SAM, O-BA-SAM, N-BA-SAM based devices, respectively, corroborating the reliability of the J-V characteristics. Integration of the external quantum efficiency (EQE) spectra of the PSCs (Fig. 5c) yields JSC values of 17.3 mA cm−2 and 17.7 mA cm−2 for the control and target devices, respectively, aligning well with the J-V results. Figure 5d, e demonstrates the statistical performance of 20 individual cells for both PSCs, detailed parameters were in Supplementary Tables 11 and 12, which shows preferable reproducibility of the photovoltaic parameters (VOC, PCE) of the target devices over those of control ones, likely due to improved homogeneity and reduced defects in the polycrystalline film. (a) J-V characteristics of champion devices based on Me-4PACz and S-BA-BA-SAM. (b) SPO of champion devices based on Me-4PACz and S-BA-SAM. (c) EQE spectra of champion devices based on Me-4PACz and S-BA-SAM. Statistical (d) PCE and (e) VOC of the device based on Me-4PACz and S-BA-SAM. (f) PLQY and QFLS or iVOC values of perovskite film based on Me-4PACz and S-BA-SAM. (g) VOC versus light intensity of perovskite film based on Me-4PACz and S-BA-SAM. (h) Mott–Schottky plots of devices based on Me-4PACz and S-BA-SAM. (i) Nyquist plots of devices based on Me-4PACz and S-BA-SAM. (j) Recombination lifetime of the devices extracted from the middle-frequency region of the Nyquist plots of devices based on Me-4PACz and S-BA-SAM. (k) MPP tracking of encapsulated control and target devices under 1 sun illumination. In order to gain deeper insight into the significant VOC and FF enhancement with mixed S-BA-SAM strategy, charge carrier transport and recombination dynamics in the devices were systematically studied. The nonradiative recombination at interfacial contacts and corresponding energy losses were firstly assessed by photoluminescence quantum yield (PLQY) of perovskite and HTL/perovskite films. It is seen from Fig. 5f and Supplementary Fig. 54 that PLQY of the control perovskite film increases from 0.238% to 0.255%, 0.248%, and 0.243% with S-BA-SAM, O-BA-SAM, N-BA-SAM modification, consistent with the PL results. While, in contact with NiOx/Me-4PACz HTL, the PLQY value of the control film substantially reduces to 0.150%, suggesting the remarkable nonradiative recombination and energy losses at the HTL/perovskite interface. This could be ascribed to the numerous voids and defects formed at the buried interface as proved in previous context. By refining the buried contacts, PLQY incremented to 0.247%, 0.223%, and 0.200% for the target NiOx/S-BA-SAM, O-BA-SAM, and N-BA-SAM /perovskite film. Furthermore, in Fig. 5f, we estimate the quasi-Fermi level splitting (QFLS) and implied open circuit voltage (iVOC) (QFLS = e × iVOC), e is the elementary charge)24,57. The QFLS of the Me-4PACz/PVK sample decreases significantly to 1.296 eV compared to 1.322 eV of pure perovskite, while the QFLS of S-BA-SAM/WBG sample reduces slightly from 1.326 to 1.322 eV. It could be attributed to the improved energy level arrangement and passivated surface defects of perovskite with S-BA-SAM treatment, which minimizes non-radiative recombination losses at the interface. The carrier recombination process under light illuminations was further evaluated by light intensity (Plight) dependent VOC. From Fig. 5g and Supplementary Fig. 55, slopes of VOC dependence on light intensity (Plight) of the control, O-BA-SAM modified devices, N-BA-SAM modified devices, and target devices are determined to be 1.01, 1.44, 1.45, and 1.48 kT/q, respectively, indicative of a suppressed trap-assisted recombination in the target device. The Mott-Schottky characteristics of the PSCs were also studied. From Fig. 5h, the mixed SAM treatment notably increments the built-in potential (Vbi) of the device from 1.07 V for the control device to 1.22 V for the target device. It arises from the reduced trap-assisted recombination and suppressed interfacial energy losses, conforming to the improved VOC of S-BA-SAM-based PSCs. Additionally, based on the equation (frac{{{{rm{dC}}}}^{-2}}{{{rm{dV}}}}=frac{2}{{{{rm{A}}}}^{2}{{{rm{q}}}{{rm{varepsilon }}}{{rm{varepsilon }}}}_{0}{{{rm{N}}}}_{{{rm{t}}}}})58, charge carrier density (Nt) decreases from 3.8 × 1014 cm−3 to 2.9 × 1014 cm−3 with S-BA-SAM modification, manifesting accelerated charge transport thus lower charge accumulation at the HTL/perovskite interface. Electrochemical impedance spectroscopy (EIS) of the devices under external voltages of 0.0–0.9 V were further measured59. EIS spectra (0.9 V) of the control and target PSCs are compared in Fig. 5i, which shows higher recombination resistance of the target device (7158 Ω) over that of the control one (2463 Ω). Based on the EIS spectra under different external biases (Supplementary Fig. 56), the carrier recombination lifetimes of the perovskite films are extracted and compared in Fig. 5j and Supplementary Fig. 57. The mixed SAM treatment delivers an overall prolonged carrier recombination lifetimes than those of the control ones. These results further evince the reduced probability for non-radiative recombination in the target device. Effects of the buried layer modification on the operational stability of the WBG PSCs were investigated by tracking the maximum power point (MPP) under continuous 1 sun illumination. All the devices for testing were encapsulated. As demonstrated in Fig. 5k, the control device experiences rapid degradation to only 56% of the initial PCE after 750 h illumination. This is likely due to the combined effects of the weak interfacial contacts at NiOx/SAM and the phase segregation within the WBG perovskite film. Contrastingly, the target WBG device exhibits drastically enhanced resilience to light illumination, with 91% of the initial PCE retained after 750 h aging (under ISOS-L-1 protocol). The thermal effect has also been taken into consideration by conducting tests under ISOS-L-2 protocol (1sun MPP tracking under 85 °C). As illustrated by Supplementary Fig. 58a, the WBG subcell retains 86% of the initial PCE after 200 h MPP tracking, while that of the control device drops to 63% of the initial PCE. The stronger resilience under both light and thermal stresses could be accredited to improved homogeneity of co-SAM distribution and their robust anchoring on NiOx, ameliorating the interfacial stability. Suppressed phase segregation of WBG film also contributes to the enhanced stability. The configuration of the TSCs is ITO/NiOx /SAM or Mixed SAM /WBG perovskite/C60 /SnO2 /Au/PEDOT: PSS/NBG perovskite/C60/BCP/Ag (Fig. 6a). Cross-sectional SEM image of the tandem device is presented in Fig. 6b, which shows the thickness of the WBG and NBG perovskite films to be ~1100 and ~400 nm, respectively. The monolithic 2T all-perovskite TSCs were further fabricated by integrating the WBG perovskite as the top subcell (described above) with 1.25 eV NBG perovskite as the bottom subcell (see Methods for details). As illustrated in Fig. 6c, the NBG PSCs show PCE of 22.2%, with VOC of 0.85 V, JSC of 32.9 mA cm−2 and FF of 79.8%. With S-BA-SAM modification on NiOx, the champion device achieves an ameliorative PCE of 28.5%, with VOC of 2.15 V, JSC of 16.0 mA cm−2 and FF of 83.0% (Fig. 6c), and PCE was stabilized at 28.0% (Fig. 6d). While the control device exhibits a much inferior PCE of 26.1%. Integrated from EQE spectra, the bottom NBG and top WBG subcells show well-matched integrated JSC of 16.0 and 16.2 mA cm−2 (Fig. 6e), respectively, in good agreement with the JSC values obtained from J-V characteristics. A total of 43 all-perovskite TSCs were fabricated (in Fig. 6f), demonstrating the preferable reproducibility of the target device. Furthermore, accredited to the significantly improved light and thermal stability of WBG subcells, the target TSC devices also demonstrate notably elongated operational stability than that of the control device, with only10% degradation in PCE after 500 h tracking under ISOS-L-1 protocol and 20% decrement in PCE after 150 h aging under ISOS-L-2 protocol (Fig. 6g and Supplementary Fig. 58b). (a) The device architecture of 2-T tandem solar cells. (b) Cross-sectional SEM images of the devices. (c) J–V characteristics of three different devices: single-junction NBG PSC, single-junction WBG PSC, and tandem solar cells. (d) SPO of the champion 2-T TSCs based on Me-4PACz and S-BA-SAM under working conditions with 100 mW cm−2 irradiation. (e) EQE spectra of TSCs. (f) Statistic histogram of PCE. (g) MPP tracking of encapsulated control and target devices under 1 sun illumination. In summary, we have demonstrated that buried interface engineering by using a mixed SAM (S-BA-SAM: Me-4PACz = 4:1, molar ratio) has a substantial impact on the performance of WBG subcells and TSCs. By exploring the interaction between the BA anchoring group of BA-SAM and NiOx, as well as the interaction between conjugation π cores of BA-SAM and FA+ cation, we successfully improve the interfacial contact between HTL/perovskite and suppress the notorious phase segregation in WBG perovskite film. As a result, significant improvements in key parameters such as VOC and FF were achieved, delivering a meliorative PCE of 20.1% for the WBG subcell and 28.5% for all-perovskite TSCs. Both modified devices demonstrate significantly improved light and thermal stabilities compared to the control ones. Overall, our research into buried interface engineering provides valuable insights for further advancements and optimization in the field of perovskite photovoltaics. Formamidinium iodide (FAI, 99.99%), methylammonium chloride (MACl 99.99%), lead (II) iodide (PbI2 99.9%), cesium iodide (CsI), lead bromide (PbBr2), lead (II) chloride (PbCl2 99.9%), nickel oxide (NiOx) and patterned ITO substrates were purchased from Advanced Election Technology CO., Ltd.. Isopropanol (IPA, 99.9%), chlorobenzene (CB, 99.9%), N, N-dimethyl formamide (DMF, 99.8%), diethyl ether (DE), and dimethyl sulfoxide (DMSO, 99.7%) were obtained from Beijing J&K Scientific Ltd.. Tin (II) fluorine (SnF2,99%) and ammonium thiocyanate (NH4SCN, 99.9%) and lead (II) thiocyanate (Pb(SCN)2, 99.9%) and 4-Dibenzothienyl boronic acid (S-BA) were purchased from Sigma-Aldrich. PEDOT: PSS (CLEVIOS P VP AI 4083) was purchased from Heraeus. Methylammonium iodide (MAI), cesium iodide (CsI), lead bromide (PbBr2), and ethanediamine dihydroiodide (EDAI)2 were supplied from Xi’an Polymer Light Technology Corporation. 4-(Dibenzofuranyl) boronic acid (O-BA) was purchased from Macklin and 9H-Carbazol-1-yl) boronic acid (N-BA) was purchased from Bide pharm. Dissolve 221.3 mg PbI2, 264.2 mg PbBr2, 165.1 mg FAI, 6.67 mg PbCl2, 62.4 mg CsI, and 1.62 mg MACl in 1 mL DMF and DMSO (DMF: DMSO = 4:1, v/v) mixed solution to prepare of (1.2 M) perovskite precursors. Finally, the solution was prepared by filtering the solution with 0.22 μm polytetrafluoroethylene (PTFE) membrane. Dissolve 507.10 mg PbI2, 409.77 mg SnI2, 224.56 mg FAI, 104.92 mg MAI, 57.16 mg CsI, 17.23 mg SnF2 and 3.14 mg NH4SCN in 1 mL DMF and DMSO (DMF: DMSO = 3:1, v/v) mixed solution to prepare (2.2 M) perovskite precursors. Finally, the solution was prepared by filtering the solution with 0.22 μm polytetrafluoroethylene (PTFE) membrane. First, the patterned ITO substrates were ultrasonic cleaned with detergent, deionized water, acetone, and isopropyl alcohol successively for 30 min, then dried with N2 and treated with plasma for 5 min. A layer of NiOx nanocrystals (10 mg ml−1 in H2O) was first coated on an ITO substrate spinning at 1500 rpm for 30 s and then annealed at 150 °C in air for 10 min. After cooling, the substrate is immediately transferred to a N2-filled glove box. Next, a self-assembled monolayer Me-4PACz or mixed SAM (0.5 mg ml−1 ethanol) was spinning on NiOx substrate at 3000 rpm for 30 s. The WBG perovskite film is deposited using a two-step spin-coating process: 500 rpm for 2 s and 4000 rpm for 60 s, and in a second spin-coating step, DE is dripped onto the spinning substrate at 25 s. The substrate is then transferred to a hot plate and heated at 100 °C for 10 min. After cooling to room temperature, the substrate is transferred to the evaporation system and a 25 nm C60 film is subsequently deposited. A layer of ALD SnO2 with a thickness of 20 nm was deposited on the C60 film, and then 100 nm Ag was deposited by thermal evaporation. In the all-perovskite tandem solar cell, NiOx solution, SAM solution and perovskite solution were spin-coated in sequence, and then 25 nm of C60 was deposited by thermal evaporation. A layer of ALD SnO2 with a thickness of 20 nm was deposited on the C60 film, and then 1 nm Au was deposited by thermal evaporation. Then took out the glovebox and spin-coated the PEDOT layer at 4000 rpm for 30 s and annealed in air at 120 °C for 20 min. The film is then transferred to an N2 atmosphere glove box for further spin coating. The prepared NBG precursor solution was spin-coated in a two-step process: 1000 rpm for 10 s, 4000 rpm for 40 s, drops of anti-solvent (CB) in 30 s, and then annealed at 100 °C for 10 min in the glove box. Then, the EDAI2 (IPA with a concentration of 1.0 mg ml−1) layer was spin-coated at 4000 rpm for 20 s, then annealed at 100 °C for 1 min, and then sequentially deposited 25 nm C60, 6 nm BCP, and 100 nm Ag by thermal evaporation. All the calculations are performed in the framework of the density functional theory with the projector-augmented plane-wave method, as implemented in the Vienna ab initio simulation package60. The generalized gradient approximation proposed by Perdew, Burke, and Ernzerhof is selected for the exchange-correlation potential61. The long-range van der Waals interaction is described by the DFT-D3 approach62. The plane wave cut-off energy of 400 eV is adopted, the energy convergence accuracy is set to 1 × 10−5 eV/atom, and the force acting on each atom is not greater than 0.1 eV/Å. The Brillouin zone is integrated using a 2 × 1 × 1 k-point grid. All quantum chemical calculations are performed using Gaussian09. For the initial structure, use the B3LYP density functional with the 6-311 G basis set. The NiOx model was optimized geometrically through density functional theory (DFT) calculations performed with the CP2K63. package, utilizing a mixed Gaussian and plane wave (GPW) basis set. The calculations incorporated the Perdew-Burke-Ernzerhof (PBE) exchange-correlation functional, DFT-D3 dispersion corrections, and dipole corrections64 necessary for periodic boundary conditions along the direction perpendicular to the surface. The valence electron wave functions were expanded in a double-ζ Gaussian basis set with polarization functions (DZVP)65. An energy cutoff of 400 Ry was applied for the electron density expansion in the GPW method. Molecular dynamics (MD) simulations were conducted using the GROMACS (version 2021.6) simulation package with the General Amber Force Field (GAFF2)66. RESP charges were calculated using the Multiwfn program67. The molecules were positioned atop the NiOx surface, modeled using a universal force field encompassing the entire periodic table. Following thousands of steps of energy minimization, a 10 ns equilibration was performed at 300 K with position restraints applied to the NiOx surface. The production runs were extended for an additional 10 ns under the NVT ensemble, with snapshots recorded every 1 ps. Temperature control at 300 K was achieved using the Nose-Hoover thermostat. A non-bonded interaction cutoff of 1.0 nm was implemented, and the Particle Mesh Ewald (PME) method with a Fourier spacing of 0.1 nm was applied to handle long-range electrostatic interactions68. The Newport Oriel sol3A 450 W solar simulator was used to test the current density versus voltage (J–V) curves and stabilized power output (SPO) under AM 1.5 G. For J-V scanning of all cells, we place aperture masking masks in front of the solar cells to ensure an effective area of 0.06 cm2. A J-V scan was performed on the WBG perovskite solar cell with a scan rate of 0.1 V s−1 and a delay time of 50 ms. The forward scanning range is −0.2 ~ 1.4 V, and the reverse scanning range is 1.4 ~ −0.2 V. A J-V scan was performed on the Sn-Pb perovskite solar cell with a scan rate of 0.1 V s−1 and a delay time of 50 ms. The forward scanning range is −0.1 ~ 1.0 V, and the reverse scanning range is 1.0 ~ −0.1 V. A J-V scan was performed on the all-perovskite tandem solar cell with a scan rate of 0.1 V s−1 and a delay time of 50 ms. The forward scan is −0.2 ~ 2.2 V, and the reverse scan is 2.2 ~ −0.2 V. The area of the solar cell under test is 0.0116 cm2. The solar cell quantum efficiency test system (Elli Technology Taiwan) was used to measure the EQE spectra of devices. The Mott Schottky curves and the impedance spectroscopy (IS) were determined with the Chenhua CHI760E electrochemical workstation. EQE measurements were measured by applying external voltage/current sources through the PSCs with a REPS measurement instrument (Enlitech). Operational stability tests of WBG/tandem solar cells were performed at maximum power point (MPP) in N2 environment under AM1.5 xenon lamp illumination (100 mW cm−2, without UV filter). The polarizer is made of ZnSe, which limits the low-end spectral range to around 650 cm−1. In these experiments, a different background is required for each polarization position used. For example, if you are going to collect spectra at 0° and 90°, corresponding background spectra are required at 0° and 90°. The spectral resolution was set to 4 cm−1, the aperture was set to 4 mm and spectra were acquired by averaging 256 scans. The X-ray photoelectron spectroscopy (XPS) was performed by a multifunctional photoelectron spectrometer (Axis Ultra DLD, Kratos) under ultrahigh vacuum (3.0 ×10−8 Torr) with a non-monochromatic He-I excitation (21.22 eV). The in-situ dynamic absorption spectrum is measured by the multi-spectral analysis equipment proposed by spectral microvision. Through the combination of the spinning instrument, LED lamp, spectrometer (ATP2002), sample table, and the display screen of the spinning instrument, the test material is evenly coated on the glass substrate on the sample platform, the instrument parameters are set, and the LED light source is irradiated vertically on the sample through the optical fiber. The transmission spectrum was detected by the spectrometer, the spectral resolution reached 0.01 nm, and the time resolution reached 1 ms. The nucleation and crystallization process of perovskites were analyzed by spectral data, and the morphological characteristics of the films were detected and revealed in real-time. The Time-of-Flight Secondary Ion Mass Spectrometry (TOF-SIMS) analysis was performed using a dual-beam approach. Primary ion bombardment was carried out using Bismuth (Bi3+) ions at an energy of 30 keV and a current of 45 degrees per nanoampere. Secondary ion detection was facilitated by Cesium (Cs+) ions at an energy of 1 keV and a current of 80 nanoamps, with the secondary ion beam aligned at 45 degrees to the primary ion path. Additionally, a flood gun was employed to neutralize the charge on the sample surface, ensuring accurate mass resolution and ion yield. PLQY measurements were characterized by a system with an integrating sphere and an excitation wavelength of 365 nm. The fixed light intensity of 100 mW cm−2 was used for the PLQY measurements. The perovskite bottom interface was characterized with XPS, SEM, KPFM, QFSL, PL Mapping, and the thin film preparation procedure was shown in Supplementary Fig. 59. Further information on research design is available in the Nature Portfolio Reporting Summary linked to this article. 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ArticleADSCAS Google Scholar Download references Z.G. acknowledges the funding support from the National Science Fund for Distinguished Young Scholars (21925506), the National Natural Science Foundation of China (2243000169, U21A20331, 81903743, and 22275004); C.L. acknowledges the funding support from the National Natural Science Foundation of China (2279151), and Zhejiang Province “Leading Goose” Plan (2024C01091). These authors contributed equally: Jingnan Wang, Boxin Jiao, Ruijia Tian. Zhejiang Provincial Engineering Research Center of Energy Optoelectronic Materials and Devices, Ningbo Institute of Materials Technology & Engineering, Chinese Academy of Sciences, Ningbo, 315201, China Jingnan Wang, Ruijia Tian, Kexuan Sun, Yuanyuan Meng, Yang Bai, Xiaoyi Lu, Bin Han, Ming Yang, Yaohua Wang, Shujing Zhou, Haibin Pan, Zhenhuan Song, Chuanxiao Xiao, Chang Liu & Ziyi Ge School of Materials Science and Chemical Engineering Ningbo University, Ningbo, 315211, China Jingnan Wang Center of Materials Science and Optoelectronics Engineering University of Chinese Academy of Sciences, 100049, Beijing, China Jingnan Wang, Chang Liu & Ziyi Ge State Key Laboratory of Power System, Department of Electrical Engineering, Tsinghua University, 100084, Beijing, China Boxin Jiao Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar C.L. conceived the idea and guided the work. J.W., R.T., Y.M., and Y.B. designed the experiments, fabricated the perovskite films and devices, and analyzed measured results. B.J. calculated adsorption energy, electron localization function, differential charge density, quantum chemical, and molecular dynamics. Y.M., C.X., X.L., B.H., Y.W., M.Y., H.P., Z.S., and S.Z. helped the characterizations; K.S. calculated the adsorption energy; Z.G., C.L., and R.T. helped to revise the manuscript. All authors discussed the results and commented on the manuscript. Correspondence to Chang Liu or Ziyi Ge. The authors declare no competing interests. Nature Communications thanks Liyuan Han, and the other, anonymous, reviewer(s) for their contribution to the peer review of this work. A peer review file is available. Publisher’s note Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations. 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To view a copy of this licence, visit http://creativecommons.org/licenses/by-nc-nd/4.0/. Reprints and permissions Wang, J., Jiao, B., Tian, R. et al. Less-acidic boric acid-functionalized self-assembled monolayer for mitigating NiOx corrosion for efficient all-perovskite tandem solar cells. Nat Commun16, 4148 (2025). https://doi.org/10.1038/s41467-025-59515-6 Download citation Received: Accepted: Published: Version of record: DOI: https://doi.org/10.1038/s41467-025-59515-6 Anyone you share the following link with will be able to read this content: Sorry, a shareable link is not currently available for this article.
Thank you for visiting nature.com. You are using a browser version with limited support for CSS. To obtain the best experience, we recommend you use a more up to date browser (or turn off compatibility mode in Internet Explorer). In the meantime, to ensure continued support, we are displaying the site without styles and JavaScript. Advertisement View from… Asia Pacific Solar Research Conference 2025 Nature Photonicsvolume 20, pages 252–253 (2026)Cite this article Amidst rapid performance improvements and industrial scaling of perovskite–silicon solar cells, researchers wait with bated breath for the outcome of reliable long-term testing. The latest updates, especially from China, were reported in Brisbane, Australia at the recent APSRC conference. This is a preview of subscription content, access via your institution Access Nature and 54 other Nature Portfolio journals Get Nature+, our best-value online-access subscription $32.99 / 30 days cancel any time Subscribe to this journal Receive 12 print issues and online access $259.00 per year only $21.58 per issue Buy this article USD 39.95 Prices may be subject to local taxes which are calculated during checkout David Pile David Pile Nature Photonics https://www.nature.com/nphoton/ David Pile Search author on:PubMedGoogle Scholar Correspondence to David Pile. Reprints and permissions Pile, D. Perovskite–silicon solar cells put to test. Nat. Photon.20, 252–253 (2026). https://doi.org/10.1038/s41566-026-01871-w Download citation Published: Version of record: Issue date: DOI: https://doi.org/10.1038/s41566-026-01871-w Anyone you share the following link with will be able to read this content: Sorry, a shareable link is not currently available for this article.
US companies SolSource Solutions and TriBeam Financial have launched a prepaid residential solar and storage financing product designed to unlock federal tax credits of up to 40%. Image: Pexels From pv magazine USA SolSource Solutions and TriBeam Financial have announced the launch of Propel, a residential solar and storage financing product. The platform integrates third-party ownership (TPO) structures with a point-of-sale loan system to fund upfront energy agreement payments. The product utilizes a prepaid power purchase agreement or lease model. Homeowners pay the total contract value at the start of the term, often using a loan originated through the TriBeam platform. The structure provides a fixed monthly payment and removes the annual price escalators common in traditional solar leases. Under the contract homeowners can also exercise an option to purchase the solar and battery system starting in the sixth year of operation. The program includes a strategic hardware partnership with Enphase Energy. Enphase will act as the exclusive provider for microinverters and battery systems. The use of Enphase hardware allows the projects to meet domestic content requirements under the Inflation Reduction Act, which can increase the Investment Tax Credit by 10%. Enphase also provides operations and maintenance through its Enphase Care service, while design and proposals are handled via the Solargraf tool. Greentech Renewables will manage national distribution and logistics for installers using the Propel platform. TriBeam Financial provides the technology layer for the product through Concert Finance. The system is designed to connect sales channels directly to capital providers to reduce overhead costs and eliminate hidden fees in the lending process. To lead the national expansion, SolSource appointed Chris Couture as CEO. Couture previously served as vice president and head of customer financing at Enphase Energy and held leadership roles at SunPower Corp. The company is backed by Hudson Sustainable Group. Hudson has managed more than $13 billion in capital across sustainable energy assets since 2007. This content is protected by copyright and may not be reused. If you want to cooperate with us and would like to reuse some of our content, please contact: editors@pv-magazine.com. More articles from Ryan Kennedy Please be mindful of our community standards. Your email address will not be published.Required fields are marked *
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Cloudy skies. High 78F. Winds SSE at 10 to 20 mph.. Thunderstorms this evening followed by occasional showers overnight. Gusty winds and small hail are possible. Low near 65F. Winds S at 5 to 10 mph. Chance of rain 70%. Updated: March 7, 2026 @ 4:56 am Wetlands pictured on a 4,500-acre lot near Stockton north of Interstate -65 and east of Highway 59 (Photo via Baldwin County MLS) Reporter Wetlands pictured on a 4,500-acre lot near Stockton north of Interstate -65 and east of Highway 59 (Photo via Baldwin County MLS) Just days after the Baldwin County Commission greenlit Stockton residents to gather enough signatures to bring forth a vote on whether the community will be brought into county zoning laws, organizers have already surpassed the required figure. As of 4 p.m. on Friday, the Friends of Tensaw River have gathered more than 124 signatures from residents within county’s Zone 3, which lies between I-65 and Old Gainey Road in north Baldwin County and includes Stockton. Javascript is required for you to be able to read premium content. Please enable it in your browser settings. You can contact Grant McLaughlin by email at grant@lagniappemobile.com or by phone at 972-571-2335 Local economic development officials were not involved in bringing solar farms to Stockton, according to the head of an agency tasked with rec… Two solar farms proposed for 4,500 acres in Stockton off Highway 65 drew the ire of more than 200 Baldwin County residents and area advocates … Nashville-based developer Silicon Ranch has launched a dedicated website aimed at addressing community concerns around its $300 million solar … As Stockton residents mobilized against a large-scale solar facility to their south, public records obtained by Lagniappe reveal a second sola… Richard Cox, the Republican challenger for the District 1 commission seat, is pushing back on the Baldwin County Commission’s claim it is powe… Following the announcement of a large-scale utility solar facility on a 4,500-acre tract in Stockton, Lagniappe held a call with the leadershi… Michael Tabb is not an opponent of green energy. As a “generational Mobilian,” former Davidson High School student, and 14-year veteran of the… Recent news of a massive solar facility to support data centers in Montgomery caught Stockton residents off guard. Lagniappe spoke with local property owners, community leaders and officials about the development. According to land records and state regulatory filings, more than 4,500-acre tract of timberland in Stockton is set to become home to two large-scale solar fields tied directly to Meta Platforms’ expanding Montgomery data center campus. Meta Platforms has now upped the ante at its Montgomery data centers to $2.44 billion — a total energy burden that translates to two massive s… Reporter {{description}} Email notifications are only sent once a day, and only if there are new matching items. Your comment has been submitted.
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Thank you for visiting nature.com. You are using a browser version with limited support for CSS. To obtain the best experience, we recommend you use a more up to date browser (or turn off compatibility mode in Internet Explorer). In the meantime, to ensure continued support, we are displaying the site without styles and JavaScript. Advertisement npj Space Explorationhas APC waivers available that can be allocated upon acceptance on an ad-hoc basis. For additional information, contact the Journal Publisher, Jialiang Cai. npj Space Explorationvolume 2, Article number: 12 (2026) Cite this article The Moon exhibits extreme environmental characteristics such as prolonged day-night cycle, large temperature fluctuations, high vacuum, and intense radiation, significantly limiting the applicability of traditional building thermal engineering and energy design methods in this environment. These environmental characteristics pose severe challenges to the thermal performance of lunar base buildings and the stability and safety of their energy systems. Therefore, this paper explores the key technical challenges and primary solutions in the construction of energy systems for long-term lunar habitats. It proposes that by advancing research on precise prediction technologies for building and equipment loads in lunar bases, key technologies for efficient energy storage and photovoltaic power generation, as well as the construction and optimization of multi-energy synergistic energy systems for lunar bases, the autonomy and reliability of lunar energy systems can be enhanced, thereby ensuring the sustained operation of future lunar bases. With the increasing demands of human space exploration and resource utilization, the establishment of long-term lunar bases has become a key objective in international space strategy and technological development. Since 2020, the launch of NASA’s Artemis Program1 and China’s International Lunar Research Station (ILRS)2 has marked the transition of human lunar activities from short-term exploration to long-term habitation. Energy supply is the fundamental prerequisite for the long-term, stable operation of lunar bases. Sufficient and stable energy assurance is critical to the successful construction and sustainable operation of lunar bases, directly affecting the safety of astronauts and the success or failure of space missions. To ensure the safe survival of personnel in the extreme lunar environment and the reliable operation of various equipment, lunar bases must develop life support systems and energy supply systems with high reliability and stability. However, the lunar environment is characterized by a series of extreme conditions, including a prolonged day-night cycle, large temperature fluctuations, high vacuum, and intense radiation. The Moon has a rotational period of ~27.3 Earth days, with lunar day and night each lasting about 14 Earth days3, resulting in an extreme temporal rhythm of “hot and illuminated days” and “cold and dark nights.” In addition, variations in the lunar surface temperature are jointly influenced by solar radiation and internal lunar heat. Owing to the Moon’s extremely low thermal inertia, the daytime surface temperature is dominated by absorbed incident solar radiation. The absence of an atmosphere capable of retaining heat leads to an exceptionally large diurnal temperature variation: surface temperatures reach ~400 K during the lunar day, while in permanently shadowed regions and during the lunar night, temperatures drop to about 90 K4, Fig. 1 illustrates the zonal mean bolometric temperatures of the lunar. Zonal mean bolometric temperatures22. Meanwhile, due to the lack of both an atmosphere and a global magnetic field, the lunar surface is directly exposed to solar radiation and cosmic rays. This high-energy particle radiation environment not only threatens the health of astronauts but also leads to the performance degradation of solar panels, functional failures of electronic devices, and material aging within the energy system. Furthermore, the absence of an atmosphere also results in the global average solar irradiance on the Moon being significantly higher than that on Earth. At lunar noon, a surface oriented normal to the Sun can receive nearly the full solar irradiance of about 1361 W/m², whereas even under optimal conditions on Earth, the peak surface irradiance is only around 1000 W/m2. Figure 2 presents the solar illumination conditions at different latitudes in the northern lunar hemisphere, showing that solar irradiance during the lunar daytime gradually decreases with increasing latitude. Solar illumination conditions at different latitudes in the northern lunar hemisphere23. The strong coupling of extreme lunar environmental factors including prolonged day-night cycle, large temperature fluctuations, high vacuum, and intense radiation poses severe challenges to the thermal performance of lunar buildings and to the stability and safety of their energy systems. Under such conditions, conventional building thermal theories and energy system design methods developed for terrestrial environments become fundamentally inapplicable. This coupled effect not only imposes far more stringent technical requirements on the performance and reliability of key energy-system components operating in extreme environments, but also compels lunar energy systems to achieve precise energy supply-demand matching and transient balance over an ultra-wide dynamic operating range. Consequently, the core objective of research on lunar base energy systems lies in developing accurate thermal modeling and high-efficiency energy system design strategies for lunar base buildings under multiple extreme physical constraints so as to enable dynamic coordination across energy generation, storage, and conversion processes, and ultimately ensure long-term energy self-sufficiency of the lunar base. This paper focuses on the major technical challenges currently confronting the development of lunar energy systems. These challenges include accurate load prediction technologies for buildings and equipment operating under high vacuum and large temperature fluctuations for lunar environments; high-energy-density energy storage technologies capable of supporting the prolonged day-night cycle; efficient energy storage and power generation technologies operable across extremely wide temperature ranges; as well as multi-energy coupled and integrated energy supply systems with intelligent control capabilities. Based on an in-depth analysis of these key issues, this paper further provides relevant research insights, aiming to offer a logically structured, systematically comprehensive, and technically well-defined reference framework for the construction of stable, sustainable, and closed-loop energy systems for future lunar bases. Under high vacuum conditions, the calculation of heating and cooling loads for lunar base buildings faces theoretical and engineering challenges that are fundamentally different from those encountered in earth buildings. Due to the near absence of an atmosphere on the Moon, convective heat transfer which dominates traditional building thermal analysis on Earth becomes largely inoperative in the lunar environment. As a result, heat exchange between buildings and the external environment relies primarily on thermal radiation and heat conduction, rendering conventional building load calculation methods and empirical models difficult to apply directly. Meanwhile, the prolonged lunar day-night cycle, coupled with intense solar irradiation during the daytime and the extremely low deep-space thermal background at night, subjects building envelopes to extreme and highly non-stationary thermal boundary conditions. Consequently, heating and cooling loads exhibit pronounced temporal fluctuations across multiple time scales, placing stringent demands on dynamic thermal load modeling and energy balance analysis. Under high vacuum conditions, the external surfaces of buildings must simultaneously account for direct solar radiation, reflected radiation from the lunar surface, and radiative heat dissipation to space environment5 (as illustrated in Fig. 3), making the accurate characterization of radiative boundary conditions one of the core challenges in load calculation. Radiation exchange at the lunar surface5. Therefore, heating and cooling load prediction for lunar base buildings in high vacuum and large temperature fluctuations environments constitutes a multiphysics coupling problem that integrates unsteady radiative heat transfer with dynamic internal and external disturbances. This challenge underscores the urgent need to develop dedicated theoretical models and computational approaches specifically tailored to the unique environmental characteristics of the lunar surface. In addition, the stable and continuous supply of electricity and thermal energy is essential for life-support systems within a lunar base, including air treatment, oxygen supply, temperature and humidity regulation, lighting, and communications. During the lunar night, extremely low ambient temperatures and substantial heat losses significantly increase the thermal load demand of the base. Meanwhile, the power consumption of scientific instruments, remote sensing equipment, and other facilities may exhibit regular diurnal variations driven by the lunar day-night environment. High-power operational activities are typically conducted during the lunar daytime, while power demand is reduced to a minimum during the lunar night to alleviate overall energy consumption. More critically, in load forecasting, it is essential to strictly distinguish and couple two distinct categories of temperature control objectives: the temperature range required to sustain human life and that required for the normal operation of equipment. Crew habitats must maintain temperature and humidity within an extremely narrow physiological comfort zone (e.g., ~293–297 K), imposing stringent demands on the precision and stability of the air conditioning system. In contrast, many scientific instruments and devices may be designed to operate over a much wider temperature range and could even leverage the extreme cold of the lunar night to achieve certain observational goals, such as infrared astronomy. Therefore, load forecasting techniques must be capable of decoupling and dynamically coordinating these two vastly different thermal demands, while conducting a detailed analysis of the energy consumption characteristics and operational modes of both life support systems and various types of equipment. Such detailed load prediction provides a fundamental basis for accurate energy system design and optimal energy management under extreme lunar environmental conditions. At the early stage of lunar base development, energy systems are primarily based on a solar photovoltaic-battery architecture6. For the photovoltaic power system reliant on solar energy, within the 14-day lunar daytime, it must not only meet the energy consumption of the base during the day but also accumulate sufficient energy to support full-load operation throughout the subsequent 14-day lunar night. Therefore, the energy storage system becomes the core hub of the energy supply. Currently, lithium-ion battery packs are universally employed as energy storage devices across various spacecraft in orbit. Their maximum installed capacity has reached 21 kWh, with a specific energy averaging 150 Wh/kg, and the longest operational lifespan can extend to 15 years7. For a lunar scientific research station, a simplistic “photovoltaic + electrochemical battery” configuration leads to an exponential increase in the required energy storage capacity. Existing studies indicate that under such an architecture, the mass of the energy storage subsystem can account for ~80–90% of the total mass of the entire energy system8; Taking a building with a volume of 54 m³ as an example, the cumulative thermal load during the lunar night is estimated to be about 3400 kWh. Assuming the use of lithium-ion batteries with a maximum energy density of 300 Wh/kg, the mass of the energy storage system required solely to meet lunar-night heating demand would exceed 11 t9. However, in lunar exploration missions, launch vehicle payload constraints on mass and volume are extremely stringent. Excessive energy storage mass would dramatically increase launch costs and technical complexity10. Consequently, under the combined constraints of extreme day-night cycles and harsh environmental conditions, achieving an effective balance among storage capacity, system mass, and energy efficiency remains one of the most critical challenges facing the development of lunar energy systems. In addition, compared with electrical energy storage, thermal energy storage schemes utilizing in-situ lunar resources may offer superior economic efficiency and practical feasibility. During the lunar daytime, solar thermal energy can be collected by solar collectors and stored within lunar regolith based thermal storage media, which can subsequently be utilized for space heating during the lunar night. Currently, various heat collection and storage schemes have been proposed, such as the in-situ energy supply system proposed by Li et al.11, which combines solar heat collection with lunar soil sintering for heat storage. During the lunar night, the heat supply power can reach 7.0 kW, and the energy efficiency is about 48%. Hu et al.12 designed a spherical lunar soil heat storage system, and after optimizing the stacking method, the energy storage density reached 0.25 kWh/kg. Further increasing the thermal storage temperature will give the thermal storage system the potential to generate electricity. Fleith et al.13 proposed that a thermal power generation system based on lunar regolith thermal storage can provide a minimum power output of 36 W within 66 h and has application potential in some polar regions of the moon. However, due to the extremely high-vacuum lunar environment, the thermal energy storage density and heat exchange efficiency of thermal energy storage systems are relatively low, and it is still difficult to support long-term energy demand during the lunar night. It is necessary to further improve the thermal storage density and heating capacity, extend the heating time, and explore integrated energy supply system solutions based on thermal storage. The extremely wide temperature range for the lunar, spanning ~90–400 K, poses severe challenges to the operation of core equipment in lunar energy systems. For battery systems, low temperatures can lead to increased electrolyte viscosity and decreased ion migration rate, significantly reducing charge and discharge efficiency and even causing a sudden drop in capacity; high temperatures can accelerate the decomposition of electrolyte and the aging of electrode materials, shortening battery cycle life14. Under the extreme thermal cycling conditions of the lunar environment, existing battery technologies can only ensure effective energy storage and release through integrated strategies, including advanced battery management systems, active thermal control measures such as heating and insulation, and optimized thermal resistance design15. In addition, for photovoltaic systems, elevated temperatures significantly reduce the open-circuit voltage and conversion efficiency of solar cells16, while under low-temperature conditions, variations in semiconductor carrier transport characteristics introduce increased uncertainty in output performance17. Prolonged exposure to severe thermal cycling further induces thermal expansion mismatch and thermomechanical fatigue in solar cells and encapsulation structures, accelerating interfacial degradation and failure, and thereby substantially compromising system reliability18. Therefore, the development of energy storage materials capable of operating across a wide temperature range, together with robust thermal management design for key energy subsystems such as photovoltaic system and energy storage units, constitutes a critical technological challenge that must be addressed for future lunar energy systems. With the continuous improvement and phased development of the functions of the lunar base, the energy structure of photovoltaic + electrochemical battery can no longer meet the energy needs of the lunar base. Existing studies have pointed out through parameterized analysis that although the photovoltaic + electrochemical battery mode is feasible, its quality and cost are unacceptable if it is not coupled with other systems19. The lunar base has diverse missions and a complex implementation environment, requiring the adoption of suitable energy forms based on different mission requirements and environmental characteristics. Therefore, future lunar bases must develop multi-energy coupled integrated supply systems. The core of this concept lies in achieving the coordinated production, storage, conversion, and distribution of multiple forms of energy (such as electrical, thermal, and chemical energy) to facilitate effective dispatching and complementarity among various energy sources, thereby meeting energy demands at different stages. Technically, the lunar energy supply system will feature multi-energy combined power generation, conversion, transmission, and networking of various energy substances such as electricity, heat, hydrogen, oxygen, and water20. However, its structural design is complex, and its operation and control are challenging. However, this complex system structure presents unprecedented challenges to its operational control, which precisely highlights the lack of intelligent control technology. The capabilities of lunar energy control systems remain inadequate in functions such as power generation forecasting, load forecasting, intelligent dispatching, and fault self-diagnosis21. It also lacks a real-time response mechanism for dynamic states such as day-night transitions, lunar dust obstruction, sudden temperature changes, and battery life degradation, resulting in low system utilization, poor energy efficiency, low reliability, and high redundancy. To ensure the smooth conduct of human lunar exploration activities and the safety of astronauts, the composition and structure of the energy system must be extremely complex. It is necessary to comprehensively improve the autonomous control, management, fault diagnosis, and response capabilities of the energy system, conduct real-time status monitoring, performance prediction, and autonomous decision-making, enhance the reconfigurability and maintainability of the energy system, and ensure high reliability and high safety. Facing the high vacuum and large temperature fluctuations for lunar environments, accurate prediction of building and equipment loads is crucial to ensuring precise matching of energy supply and demand for lunar bases. To address this issue, this paper proposes developing an unsteady heat transfer mechanism model suitable for lunar building envelopes based on high-precision lunar surface thermal environment data. By analyzing a database of typical lunar load scenarios, an accurate prediction technology for lunar base building and equipment loads can be constructed. First, it is necessary to integrate lunar orbiter data and theoretical models to establish a spatiotemporal distribution database of direct solar radiation, lunar albedo, and temperature at different latitudes and terrains, forming a standard thermal boundary condition dataset for lunar base site selection thermal environment analysis. Second, it is necessary to establish a set of thermal property parameters applicable to lunar soil, lunar dust, multilayer composite materials, and phase change materials under ultra-high vacuum and wide temperature ranges and develop a thermal mechanism model for lunar base envelope to solve unsteady-state heat conduction and radiation boundary value problems. Subsequently, through analysis and simulation, the power time-varying laws of life support systems and scientific research equipment in lunar day/night modes will be quantified, and a typical lunar load scenario library will be established. Finally, a lunar building load calculation model integrating “high-precision database of lunar surface thermal environment – unsteady-state heat transfer mechanism model of envelope – typical lunar load scenario library – load generation” will be formed, as outlined in Fig. 4. This model thus provides a reliable data foundation and simulation tools for energy system capacity planning, topology design, and operation strategy optimization of lunar bases, achieving key technological breakthroughs in energy self-sufficiency and safe operation of the base. Main research contents of accurate prediction technology for lunar base building and equipment load. Under the long-term operation conditions of a lunar base, the energy system must achieve continuous, stable, and efficient energy supply under extremely prolonged day-night cycle, large temperature fluctuations, and strict mass and volume constraints. Therefore, a systematic breakthrough in efficient energy storage and power generation technologies is required. Regarding this key technological issue, this paper proposes researching in-situ resource thermal storage technology based on lunar in-situ resources, developing high-energy-density wide-temperature-range energy storage technology and extreme wide-temperature-range photovoltaic power generation performance and temperature control technology, forming a multi-form energy storage synergistic lunar energy architecture, as illustrated in Fig. 5. Main research contents of key technologies for efficient energy storage and photovoltaic power generation in the extreme lunar environment. First, thermal energy storage technologies based on lunar in-situ resource utilization are introduced, with a focus on exploring the feasibility of using lunar regolith and its sintered products as thermal storage media. The thermophysical properties, cyclic stability, and structural integration strategies of regolith-based thermal storage materials are systematically investigated. On this basis, a “solar thermal collection-lunar regolith thermal storage-night time heat release” heating scheme is developed to decouple the high-proportion thermal load of lunar bases from electrical energy storage systems, thereby substantially reducing the required capacity of battery storage. Second, in response to the extreme environmental characteristics of the lunar, including prolonged day-night cycle and large temperature fluctuations, this study investigates high-energy-density, wide-temperature-range energy storage technologies capable of supporting ultra-long-timescale, cross-period energy regulation under extreme thermal conditions. The research focuses on overcoming the limitations of traditional lithium-ion batteries in terms of specific energy, system mass ratio, and operation in low-temperature environments. It investigates the adaptability and thermal management system design of high-specific-energy storage technologies such as regenerative fuel cells, high-energy-density lithium-ion batteries, lithium-sulfur batteries, solid-state batteries, and metal-air batteries in the long-term, high-temperature-varying lunar environment. Finally, a coupled thermo-photoelectric model of photovoltaic modules is developed by comprehensively accounting for solar irradiance, radiative heat dissipation, and structural heat conduction. On this basis, the steady-state operating temperature and output characteristics of photovoltaic modules under different diurnal conditions are predicted, enabling a systematic evaluation of the underlying mechanisms through which temperature variations affect photovoltaic conversion efficiency and operational stability. The results provide quantitative guidance for optimizing photovoltaic module structures and array configuration parameters. Furthermore, integrated photovoltaic-thermal system configurations are investigated. By incorporating thermal energy storage technologies based on lunar in situ resources, active regulation of photovoltaic module temperature is achieved, thereby mitigating the adverse effects of extreme thermal cycling on power generation efficiency and service life. This approach significantly enhances the long-term reliability and energy utilization efficiency of photovoltaic power generation systems operating in the lunar environment. Ultimately, by integrating lunar in situ thermal energy storage, high-energy-density energy storage technologies with wide operating temperature ranges, and photovoltaic-thermal synergistic power generation systems, a comprehensive technical framework is established for the efficient energy acquisition, cross-period storage, and stable utilization of lunar base energy systems. This integrated approach enables a lightweight and highly reliable energy architecture, tailored to the extreme environmental conditions of future lunar bases. To meet the long-term, continuous, and multi-mission operational requirements of future lunar bases, research on lunar energy systems must urgently evolve from single-mode energy supply schemes toward integrated energy systems characterized by multi-energy collaboration, system-level optimization, and intelligent operation. As a first step, a multi-source complementary lunar energy system architecture is established. This paper proposes a lunar energy system framework that enables synergistic conversion and cascade utilization of multiple energy and material carriers including solar energy, electricity, thermal energy, hydrogen, oxygen, and water to solve the problem of continuous energy supply during the lunar night, as shown in Fig. 6. Conceptual design of the lunar base energy system. This system comprehensively considers various energy forms, including solar photovoltaic, solar thermal collectors, regenerative fuel cells, high-energy-density wide-temperature-range energy storage, and in-situ resource thermal storage. The system’s energy inputs include solar energy during the lunar day, lunar water, Earth replenishment water, and lunar soil. It is particularly worth noting that the hydrogen and oxygen within the system are not primary energy sources in themselves, but rather “energy carriers” that store electrical energy in the form of chemical energy through the process of water electrolysis. During the lunar day, solar energy is generated by photovoltaic power generation to provide basic electricity for equipment and hydrogen production at the lunar base, with surplus electricity stored in batteries to power the lunar base during the lunar night. During the lunar day, solar thermal collectors collect solar heat and store it in lunar soil thermal storage, providing heat to the lunar base during the lunar night. During the lunar day, an electrolyzer uses photovoltaic power to electrolyze lunar water or Earth replenishment water to produce hydrogen and oxygen, which are then stored in a storage tank. During the lunar night, hydrogen and oxygen are used to generate electricity via fuel cells, producing water. The heat generated by the fuel cells is recovered as waste heat, providing a heat source for the system’s stable operation in low-temperature environments. Regarding the sourcing of key equipment and resources, differentiated considerations should be applied based on the developmental phase of the lunar base. In the initial construction phase, due to the immaturity of in-situ resource utilization technologies, core equipment with high safety requirements—such as hydrogen and oxygen storage tanks, electrolyzers, and fuel cell stacks—must be directly transported from Earth. As the base expands and technologies mature, in-situ resource utilization strategies can be progressively introduced. On one hand, the exploration and extraction of lunar polar water ice can reduce reliance on Earth resupply and lower long-term operational costs. On the other hand, research into the feasibility of manufacturing non-pressurized or low-pressure storage tanks using lunar regolith through techniques such as 3D printing can further enhance the system’s material self-sufficiency. Secondly, research will be conducted on optimization methods for lunar energy system configuration. Considering different base sizes, mission phases, and deployment environments, and based on lunar base building and equipment load prediction technologies, multi-objective optimization and parametric analysis will be used to seek the optimal balance between energy system quality, reliability, energy efficiency, and cost. Then, the coupling mechanism and operation control strategies of multi-energy systems will be studied, with a focus on breakthroughs in energy dispatching under long-cycle, large temperature difference, and strong load fluctuation conditions to achieve stable system operation. Finally, intelligent and autonomous energy management technologies will be introduced to develop a smart energy management system that integrates accurate forecasting, intelligent scheduling, and self-diagnosis. This system will optimize and adjust energy flow in real time, improving energy utilization efficiency, operational stability, and fault tolerance. Through this research, a safe, efficient, and scalable theoretical and technological framework for lunar base energy systems will be gradually established, providing reliable support for long-term manned lunar habitation and space exploration missions. The grand vision of 21st-century space exploration has humanity’s gaze firmly focused on the lunar, steadily progressing towards the goal of establishing a long-term, sustainable habitat there. Achieving this goal depends on overcoming two crucial and interconnected challenges: to ensure a continuous and stable energy supply and to construct a safe and habitable artificial environment. In this context, all lunar surface activities must rely on a highly autonomous, reliable, and intelligent energy system. This paper starts with the environmental challenges faced by the energy system of the lunar base and suggests that subsequent research should focus on technologies for accurate prediction of the load of buildings and equipment on the lunar base, key technologies for efficient energy storage and photovoltaic power generation, and technologies for the construction and optimization of multi-energy collaborative energy systems on the lunar base. These researches aim to solve the design problems of thermal and efficient energy systems on the lunar base under multiple extreme physical constraints such as prolonged day–night cycle, large temperature fluctuations, high vacuum, and intense radiation, and ensure energy self-sufficiency for long-term personnel stays on the base. Despite existing technological bottlenecks and risks, this work provides a systematic and clear reference framework for the design of lunar base energy systems. 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Parametric study of a lunar base power systems. Energies4, 14 (2021). Google Scholar Williams, J. P., Paige, D. A., Greenhagen, B. T. & Sefton-Nash, E. The global surface temperatures of the Moon as measured by the Diviner Lunar Radiometer Experiment. Icarus283, 300–325 (2017). ArticleADS Google Scholar Kramm, G. et al. On the solar climate of the moon and the resulting surface temperature distribution. Natural Sci.14, 009 (2022). Article Google Scholar Download references The authors gratefully acknowledge the technical support and insightful discussions from colleagues at the Chinese Academy of Building Research and CSSC Systems Engineering Research Institute. The study was sponsored by the National Natural Science Foundation of China (52578149). Chinese Academy of Building Research, Beijing, China Ji Li, Wei Xu, Huiyu Xue, Jing Yuan & Tongtao Wei Jianke EET Co. Ltd, Beijing, China Ji Li, Wei Xu, Huiyu Xue, Jing Yuan & Tongtao Wei CSSC Systems Engineering Research Institute, Beijing, China Jie Yang Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Search author on:PubMedGoogle Scholar Ji Li: conceptualization, writing–original draft, writing–review&editing, project administration. Wei Xu: writing–review&editing, supervision, formal analysis (focus on environmental constraints and load analysis). Jie Yang: writing–review&editing, investigation, formal analysis (focus on energy storage and power generation technologies). Huiyu Xue: writing–review&editing, investigation, resources. Jing Yuan: writing–review&editing, investigation, visualization. Tongtao Wei: writing–review&editing, validation. All authors have read and approved the final version of the manuscript. Correspondence to Ji Li. J.L., as the Editorial Board Member of npj Space Exploration, was not involved in the journal’s review of, or decisions related to, this manuscript. The other authors declare that they have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper. Publisher’s note Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations. Open Access This article is licensed under a Creative Commons Attribution-NonCommercial-NoDerivatives 4.0 International License, which permits any non-commercial use, sharing, distribution and reproduction in any medium or format, as long as you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons licence, and indicate if you modified the licensed material. You do not have permission under this licence to share adapted material derived from this article or parts of it. The images or other third party material in this article are included in the article’s Creative Commons licence, unless indicated otherwise in a credit line to the material. If material is not included in the article’s Creative Commons licence and your intended use is not permitted by statutory regulation or exceeds the permitted use, you will need to obtain permission directly from the copyright holder. To view a copy of this licence, visit http://creativecommons.org/licenses/by-nc-nd/4.0/. Reprints and permissions Li, J., Xu, W., Yang, J. et al. Key technological challenges and systemic solutions for lunar base energy systems designed for long-term deployment needs. npj Space Explor.2, 12 (2026). https://doi.org/10.1038/s44453-026-00030-3 Download citation Published: Version of record: DOI: https://doi.org/10.1038/s44453-026-00030-3 Anyone you share the following link with will be able to read this content: Sorry, a shareable link is not currently available for this article.
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Once again this holiday season The Day will continue its long-running tradition of publishing its Make a Difference series. The daily series highlights our neighbors who area social service agencies say need our help this holiday season.
Select Page Posted by Jan Wondra | Mar 6, 2026 HB26-1007 would save Coloradans money on their energy bills by expanding access to cost-saving solar The Colorado House on Thursday passed legislation to remove barriers to plug-in solar panels to save Coloradans money on their utility bills. HB26-1007 would establish safety standards for plug-in solar and meter collars and ensure that utilities accommodate their use to help Coloradans take advantage of cost-saving solar. “With the passage of this bill, we’re closer than ever before to make safe, plug-in solar options available to Coloradans,” said Rep. Lesley Smith (D-Boulder). “Our bill removes unnecessary barriers and establishes safety standards to make plug-in solar a reality for more Coloradans. Traditional solar rooftop solar panels aren’t an option for most renters, and this makes it easier for Coloradans to lower their utility bills by generating their own clean, reliable energy.” HB26-1007 passed the House by a vote of 48-16. This bill expands access to renewable energy technology by making it easier for those living in apartments or shared spaces to benefit from cost-saving solar. HB26-1007 establishes protective guardrails on the types of plug-in solar products that can be used. Under this bill, all plug-in solar devices installed must meet the UL 3700 product safety standard. Plug-in solar is common in Europe. For example, in Germany, approximately four million households have installed plug-in solar. If passed, Colorado would join Utah in becoming early adopters of safe, reliable, plug-in solar in the United States. Plug-in solar, also referred to as balcony solar, can be plugged into a home electrical outlet and is more affordable than traditional rooftop solar. It consists of one to four solar panels plus an inverter and optional battery and is designed for simple, safe installation. Plug-in solar can be used to power household appliances and offer Coloradans’ alternative, reliable energy sources. “Plug-in solar panels are a safe and helpful tool for saving Coloradans money on their utility bills,” said Rep. Rebekah Stewart, D-Lakewood. “Our bill outlines necessary safety standards for plug-in solar devices and meter collars so more Coloradans can take advantage of this renewable energy source. Many renters are interested in solar, and this bill makes it easier for them to give solar a shot at an affordable price point and without unnecessary barriers.” To streamline solar installation, HB26-1007 encourages the use of meter collars. Meter collars are devices installed between an electric meter socket and a utility billing meter to provide immediate interconnection of customer-owned solar devices to the grid. Meter collars eliminate the need for a costly electrical panel upgrade, saving Coloradans money and time on solar installation. This bill outlines a safe, consistent and repeatable solar installation process with minimal disruption and short installation times to benefit Coloradans. Featured image: Plug-in-solar panels are the latest green energy trend. Image courtesy of USA Solar. Share: Publisher/Managing EditorWith criss-crossing careers in global marketing and advertising, product management, and journalism, Wondra has found leading business entities from Western Union North America Money Transfer to the Arrow Electronics Global Marketing team to be fertile strategic ground before returning to her journalistic roots; first launching theCorridor.biz for the Villager Media Group, before launching Ark Valley Voice. As the winner of several Colorado Press Association Awards and Publisher/Managing Editor, she leads an enthusiastic team of journalists who believe strongly that “Truth should have a voice.” In order to approve your comments, we must have a full name, working email address and your City and State.
US solar manufacturer Silfab Solar has disputed some reports of chemical spillages at its manufacturing facility in Fort Mill, South Carolina. Earlier today PV Tech reported that there were a chemical spill and a chemical leak at Silfab’s manufacturing facility in Fort Mill, South Carolina this week, prompting an investigation from the South Carolina Department of Environmental Services (SCDEP) and pushing the local school district to close a nearby school for two days. The reports said that hundreds of gallons of potassium hydroxide were spilled earlier this week and another spillage of hydrofluoric acid occurred yesterday. Get Premium Subscription In a statement delivered to the press this morning in South Carolina, Silfab director of operations Greg Basden said: “We are extremely committed to operating safe facilities. It’s unfortunate that significant amounts of misinformation have been put in the public domain. It is our responsibility to set the record straight.” He said that the first chemical spill comprised the “accidental release of approximately 300 gallons of water containing small amounts of potassium hydroxide.” He said that the company reported “worst case” conditions in its initial report to authorities, which led to an initial estimate of over 1,500 gallons before being revised down to 300 gallons. “At no time during this event were any employees or the public put at risk,” Basden said. Regarding the second leak of hydrofluoric acid, Basden said: “At the end of last week … we recognised a very small drip occurring at the base of the tank.” He said Silfab communicated with the vendor of the tank and reduced the leak to “roughly one drop an hour”. “We followed state and federal protocols and procedures to alert authorities,” he said, claiming that there was no need to raise alarm in the second incident. Silfab “strongly disputes the classification of this brief drip as a ‘leak’ or a ‘major incident’”, Basden said, adding that it was “unfortunate” that the school district chose to cancel classes for two days. Based on its discussions with SCDEP and other authorities, Basden said: “We anticipate starting back up operations tonight at 6:30.” Speaking before the release of Basden’s statement, state representative David Martin, who pushed for an investigation into Silfab alongside senator Michael Johnson, said: “I don’t really trust what I’m being told from Silfab … and that’s exactly why SCDES has been investigating them over the last few days, to find out exactly what the truth is.” In an official statement released earlier today, Silfab Solar said: “Regarding the letter Silfab Solar received from the South Carolina Department of Environmental Services, the Silfab technical response team is addressing the issue in coordination with DES and local officials. On Thursday afternoon, Silfab made the decision to voluntarily pause operations for the remainder of the day as well as the Friday day shift. “Silfab confirms that there is no health risk to employees, the community or the environment, and there is no threat to public safety as relayed in an earlier statement made by the York County Office of Emergency Management.” The Fort Mill manufacturing facility has faced significant local opposition over recent years. The plant’s inauguration date was previously delayed due to local opposition and concerns over risks to the nearby school and students. That school has been closed for the last two days.
Solar Power World By Billy Ludt | Qcells announced in a press release today that the company has resumed solar panel assembly at its facility in Cartersville, Georgia, following customs clearance delays. The factory plans to advance from solar panel assembly and integrate ingot, wafer and cell production this year at an annual capacity of 3.3 GW, according to a company spokesperson. Qcells Dalton, Georgia, manufacturing facility. “We are proud to be back to work manufacturing the American-made energy the country needs right now,” said Marta Stoepker, head of communications at Qcells. “Like any company, hurdles have and will occur, which requires us to adapt and be nimble, but our overall goal remains the same — to build a complete American solar supply chain. To achieve this, we are excited to welcome hundreds of new, talented people into our workforce as we finalize our one-of-a-kind factory in Cartersville, Georgia. By the end of 2026, we’ll have nearly 4,000 people manufacturing panels and components that America hasn’t made in a very long time.” In November, Qcells furloughed 1,000 employees from its two Georgia plants — about one-third of the company’s workforce – and laid off 300 people because U.S Customs and Border Protection (CBP) was increasingly detaining its imported solar cells and other module components. Stoepker said Qcells was able to bring back every furloughed employee. Products were being stopped at the border under the Uyghur Forced Labor Prevention Act, which prevented Chinese goods manufactured using forced labor from entering the United States. Qcells is headquartered in South Korea, and has claimed it uses no Chinese components in its solar modules, but CBP started detaining Qcell products last summer. The Cartersville plant started operating in April 2025, joining Qcells’ 5.1-GW factory in Dalton, which opened in 2019. State Rep. Kasey Carpenter (R-Dalton) is hosting a press conference highlighting Qcells investments in Georgia on Tuesday at 2:30 p.m. (EDT) at the State Capitol. Billy Ludt is managing editor of Solar Power World and currently covers topics on mounting, inverters, installation and operations.
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