text:
Home > Responsibility > Assets > Cerro San Pedro
At Cerro San Pedro, we strive to achieve a zero-accident workplace through a strict Health and Safety program that applies to all operational staff, both contractors and employees. As a result of our commitment to accident prevention, our mine is one of the safest in Mexico.
We maintain a close relationship with the residents of the Municipality of Cerro de San Pedro, which comprises thirteen communities and three ejidos (communally-owned land holdings) within the project's sphere of influence. We provide the communities with access to medical and dental services and support the local educational system with contributions of computer equipment, educational software and Internet connectivity to classrooms. We provide transportation to and from children's homes to their schools. We also contribute to the preservation of local heritage and culture, and have provided financial support for the restoration of the church of San Nicholas and the altar dedicated to the Virgen de Guadalupe, and construction of a new rectory for the church.
Our contributions have been recognized in our accreditation as a Socially Responsible Company (Empresa Socialmente Reponsable - ESR) by the internationally-recognized non-profit Mexican Centre for Philanthropy (Centro Mexicano para la Filantropía - CEMEFI).
Cerro San Pedro has been awarded with the prestigious "Level 3 Safe Company" by the Ministry for Labor. The award honors those working places which have implemented a labor system of safety and health management, thus promoting the voluntary compliance of regulations in the referred fields, a constant improvement in the prevention of accidents and illness and the decrease of accidents and occupational illness. This award will be granted for a 3-year period, subject to revalidation and has been granted to only 8 mining companies in Mexico. Cerro San Pedro has also earned ISO 9001:2008 Certification in Minerals for metallurgical benefit processes recognizes that control standards are in place upon internal benchmarks, and ISO14001:2004 certification in recognition that the Cerro San Pedro mine is in good standing and operates in compliance with all laws, regulations and an environmental management system internationally certified.
At Cerro San Pedro, we take our environmental responsibilities seriously. Our environmental management system has achieved ISO 14001:2004 status. In this semi-arid region, we have made significant investments in improving our mineral recovery processes to reduce our water consumption. Domestic wastewater is treated and re-used and rainwater is collected and used in processing. Water flows through a closed circuit with no discharges of wastewater. The only water loss is due to the leach pile retention and the high levels of evaporation in this region.
Our Integrated Management System specifies procedures for responsible waste management, applying Mexican classification standards for hazardous, special handling and solid waste and sanitary waste water.
We integrate reclamation into every phase of mining, and maintain a botanical nursery that has produced over 135,000 plants of various indigenous species for ongoing reclamation work. Our annual reforestation goal is 44 hectares, and we have reforested more than 360 hectares of land outside the mine site.
CSR Award Statement
Safety is a core value at New Gold and our people are of paramount importance to us. We are committed to making sure that each of our employees returns home safely at the end of every shift. Our focus on employee safety is reflected in mine-specific assessments and process-oriented action plans that seek to identify and correct unique safety challenges through education and training. We believe focusing on prevention is the best way to eliminate any accidents or injuries and we remain vigilant in our efforts to lead the mining industry through continuous improvement to our health and safety practices.
The Cerro San Pedro mine also received special recognition from the Orica company for its social responsibility and leading role in the application of advanced explosives practices in operating the open pit mine which sits adjacent to the historic town of Cerro San Pedro.


text:
Dhakalive
Backpage
12 September, 2018 00:00 00 AM
Nepal: PM Oli continues to disappoint
Dr. S.Chandrasekharan
In his disappointment over Oli's style and content of governance, one Analyst has pointed out perhaps rightly that- with six months out of power, former PM Deuba's misrule and bad Governance are fading in public memory with the performance of K.P.Oli's government Oli is being accused of: Inability to manage Federalism Curbing freedom of NGOs, of curtailing civil liberties and press freedom Hesitancy in expediting a National Integrity Policy to regulate NGOs.
Of tolerating Non-Performing Ministers and Ministries Weak governance in spite of a two third majority. Of centralising all powers and seen to be coming up as "Rising Despot" in the region. Not filling up the potholes in Trivandrum! ( frivolous one and blaming the poor PM appears to be ridiculous)
Slow progress in institutionalising "federalism" with serious shortage of staff at the Provincial and Local levels. Performance of Local bodies despite being given full powers and funds is to say the least is dismal. Delay and avoidable controversy in choosing the Chief Justice Failure to fulfill his commitments for constitutional amendments. Producing a citizenship law which is stricter than the previous citizenship charter thus making no progress in this long pending issue that affects a large number of the population in the south. Heavy taxation at both the central and provincial levels sometimes going to 300 percent from previous years with no corresponding benefit to show for the Public.
Commitment of over 95 percent of aid for the last fiscal year from Chinese sources, thus leading the country into a possible "Debt Trap" with the Chinese. Failure to take quick remedial action in disputes that are surfacing between the Centre and the provinces and this may lead to serious confrontation if not checked in time.
Hurried introduction on Aug 17 the laws relating to Civil and Criminal Codes. Above all, lack of progress in bringing the peace process to an end with the victims of the civil war still not getting justice.
The list could go on. But what baffles everyone is why Oli in spite of being assured of a five-year term and a two third majority is not being decisive and is seen to be dilly dallying on a simle issue like the appointment of Chief Justice?
Some point out that Oli is facing two challenges internally – the one being his own health and two the attitude of his coalition partner- the Maoists who are pushing for irregular orders for all the atrocities committed during the civil war. Dahal being a wily character, Oli has to constantly see behind his back as to what Dahal is doing.
On Constitutional amendments, Oli continues to parrot his earlier statement that he is ready to amend the constitution "in accordance with the needs of the country and the people." He said this as recently as 19th August in a rally at Janakpur and added that he is committed to a constitutional amendment. Yet no move towards any amendment is being seen and poor Upendra Yadav who joined the government on this commitment continues to face embarrassment in Terai.
On the introduction of new civil and criminal codes, the country was using the outdated Muliki Ain codes first enacted by the Rana regime in 1854. Certainly there will be flaws in the new laws, but that can be corrected. But the people appear to be in a great hurry. They were up in arms on some issues like the one on Doctors who threatened a state wide strike! But the issue was not in implementing the new codes but in taking time to respond to some of the shortcomings in the codes that agitated the affected parties. The Government did deem it necessary to explain to the public on the new laws that have an impact on their day to day life! Nepal held parliamentary elections in November and December but the formation of the new government had been delayed because the Election Commission declined to declare the final results until the election of the upper house of parliament, which was held last week.
"He has already received the appointment letter from the president," Bhandari's spokesman, Kul Prasad Chudal, told Reuters.
Oli is to take the oath of office later on Thursday, Chudal said.Nepal has been embroiled in political instability since a decade-long Maoist conflict ended in 2006 and the monarchy was abolished two years later. Oli is the 26th prime minister since protests led to the establishment of a parliamentary democracy in 1990.
Oli has said he will promote peace, stability and development in one of the world's poorest countries where revolving-door coalitions have sapped business confidence, curbed growth, spurred corruption and slowed reconstruction after a 2015 earthquake that killed 9,000 people.
The new government will be faced with an economy plagued by dwindling exports, manufacturing and remittances.
Party officials said Maoist chief Prachanda will take over from Oli as prime minister before his five year term expired under a power sharing deal. Again, Federalism is a new concept that would take some time for the three tiers of government to coordinate and perform. One third of all the posts in the local and provincial levels are yet to be fulfilled and the process will take sometime to recruit, train and make them understand their roles and perform. Simple things like national holidays should be coordinated. For example, the holiday declared by the Provincial government in Province 2 was not obeyed by the Federal Rashtriya Bank and the Interior Minister of the Province had to go personally to the bank to lock it up. Such ugly incidents should have been avoided. In the matter of taxation, the people are being burdened by overlapping taxes at al the three levels and taxes have doubled and tripled. The people are justifiably angry and there is need to immediately regulate the taxation procedure and clear demarcation of the powers at all the three levels of the Government. Some have begun to think that Federalism is a "Poisoned Chalice."
Some of the criticisms against the PM are not fair like the one of Trivandrum roads being full of potholes. The one instance of stopping of a former Maoist child soldier going to a Conference in Bangkok is being used to declare that the Government is authoritarian! But the Government should have clarified why the individual Lenin Bista was not allowed to board the flight.
In a conference of legal experts, one of the participants said "We are in a state of crisis. The current government of Oli is increasingly showing tendencies of an authoritarian and totalitarian State!" This statement is harsh and one should look around and see what is authoritarianism. One does not have to look far beyond the Maldives where a tyrant President is using all the tools of government to stay in power and to get elected again by sending every possible candidate to jail or to exile!
But Oli should do some things immediately that should indicate that he means business. This is not a complete list. First, is that justice should be done to the victims of the decade long civil war immediately. He has a problem in that some of the perpetrators are part of the Government or part of the newly formed party. He would still have a working majority even if the Maoists withdraw. He should show some bold steps.
Next, go for the Constitutional amendments and do justice to Terai. One is sick of hearing that the Constitution was approved by ninety percent of the people's representatives and so is sacrosanct. This means nothing to one third of the population in Terai who continue to remain in an adversarial situation.
In his disappointment over Olis style and content of governance, one Analyst has pointed out perhaps rightly that- with six months out of power, former PM Deubas misrule and bad Governance are fading in public memory with the performance of K.P.Olis government Oli is being accused of: Inability to manage Federalism Curbing freedom of NGOs, of curtailing civil liberties and press freedom Hesitancy in expediting a National Integrity Policy to regulate NGOs. Of tolerating Non-Performing Ministers and Ministries Weak governance in spite of a two third majority. Of centralising all powers and seen to be coming up as Rising Despot in the region. Not filling up the potholes in Trivandrum! ( frivolous one and blaming the poor PM appears to be ridiculous) Slow progress in institutionalising federalism with serious shortage of staff at the Provincial and Local levels. Performance of Local bodies despite being given full powers and funds is to say the least is dismal. Delay and avoidable controversy in choosing the Chief Justice Failure to fulfill his commitments for constitutional amendments. Producing a citizenship law which is stricter than the previous citizenship charter thus making no progress in this long pending issue that affects a large number of the population in the south. Heavy taxation at both the central and provincial levels sometimes going to 300 percent from previous years with no corresponding benefit to show for the Public. Commitment of over 95 percent of aid for the last fiscal year from Chinese sources, thus leading the country into a possible Debt Trap with the Chinese. Failure to take quick remedial action in disputes that are surfacing between the Centre and the provinces and this may lead to serious confrontation if not checked in time. Hurried introduction on Aug 17 the laws relating to Civil and Criminal Codes. Above all, lack of progress in bringing the peace process to an end with the victims of the civil war still not getting justice. The list could go on. But what baffles everyone is why Oli in spite of being assured of a five-year term and a two third majority is not being decisive and is seen to be dilly dallying on a simle issue like the appointment of Chief Justice? Some point out that Oli is facing two challenges internally the one being his own health and two the attitude of his coalition partner- the Maoists who are pushing for irregular orders for all the atrocities committed during the civil war. Dahal being a wily character, Oli has to constantly see behind his back as to what Dahal is doing. On Constitutional amendments, Oli continues to parrot his earlier statement that he is ready to amend the constitution in accordance with the needs of the country and the people. He said this as recently as 19th August in a rally at Janakpur and added that he is committed to a constitutional amendment. Yet no move towards any amendment is being seen and poor Upendra Yadav who joined the government on this commitment continues to face embarrassment in Terai. On the introduction of new civil and criminal codes, the country was using the outdated Muliki Ain codes first enacted by the Rana regime in 1854. Certainly there will be flaws in the new laws, but that can be corrected. But the people appear to be in a great hurry. They were up in arms on some issues like the one on Doctors who threatened a state wide strike! But the issue was not in implementing the new codes but in taking time to respond to some of the shortcomings in the codes that agitated the affected parties. The Government did deem it necessary to explain to the public on the new laws that have an impact on their day to day life! Nepal held parliamentary elections in November and December but the formation of the new government had been delayed because the Election Commission declined to declare the final results until the election of the upper house of parliament, which was held last week. He has already received the appointment letter from the president, Bhandaris spokesman, Kul Prasad Chudal, told Reuters. Oli is to take the oath of office later on Thursday, Chudal said.Nepal has been embroiled in political instability since a decade-long Maoist conflict ended in 2006 and the monarchy was abolished two years later. Oli is the 26th prime minister since protests led to the establishment of a parliamentary democracy in 1990. Oli has said he will promote peace, stability and development in one of the worlds poorest countries where revolving-door coalitions have sapped business confidence, curbed growth, spurred corruption and slowed reconstruction after a 2015 earthquake that killed 9,000 people. The new government will be faced with an economy plagued by dwindling exports, manufacturing and remittances. Party officials said Maoist chief Prachanda will take over from Oli as prime minister before his five year term expired under a power sharing deal. Again, Federalism is a new concept that would take some time for the three tiers of government to coordinate and perform. One third of all the posts in the local and provincial levels are yet to be fulfilled and the process will take sometime to recruit, train and make them understand their roles and perform. Simple things like national holidays should be coordinated. For example, the holiday declared by the Provincial government in Province 2 was not obeyed by the Federal Rashtriya Bank and the Interior Minister of the Province had to go personally to the bank to lock it up. Such ugly incidents should have been avoided. In the matter of taxation, the people are being burdened by overlapping taxes at al the three levels and taxes have doubled and tripled. The people are justifiably angry and there is need to immediately regulate the taxation procedure and clear demarcation of the powers at all the three levels of the Government. Some have begun to think that Federalism is a Poisoned Chalice. Some of the criticisms against the PM are not fair like the one of Trivandrum roads being full of potholes. The one instance of stopping of a former Maoist child soldier going to a Conference in Bangkok is being used to declare that the Government is authoritarian! But the Government should have clarified why the individual Lenin Bista was not allowed to board the flight. In a conference of legal experts, one of the participants said We are in a state of crisis. The current government of Oli is increasingly showing tendencies of an authoritarian and totalitarian State! This statement is harsh and one should look around and see what is authoritarianism. One does not have to look far beyond the Maldives where a tyrant President is using all the tools of government to stay in power and to get elected again by sending every possible candidate to jail or to exile! But Oli should do some things immediately that should indicate that he means business. This is not a complete list. First, is that justice should be done to the victims of the decade long civil war immediately. He has a problem in that some of the perpetrators are part of the Government or part of the newly formed party. He would still have a working majority even if the Maoists withdraw. He should show some bold steps. Next, go for the Constitutional amendments and do justice to Terai. One is sick of hearing that the Constitution was approved by ninety percent of the peoples representatives and so is sacrosanct. This means nothing to one third of the population in Terai who continue to remain in an adversarial situation. Eurasia Review
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redpajama_set_name: RedPajamaCommonCrawl


text:
How to Become a Content Marketing Expert For Your Blog/Business
by Soh Ying Qi | Mar 17, 2019 | Articles, Digital Marketing, Featured, Inspiration | 0 comments
In this digital age, it has never been more important to ensure the strength of your content. Faced with consumers' increasing need for speed, good content marketing is crucial to helping you make the most of their valuable attention—and hopefully translate it into increased support and sales for your brand.
Fortunately, today's digital resources have made it easier than ever to get started with content marketing. Here, we'll provide a brief introduction to this endlessly fascinating form of marketing, and throw in some of our best tips and tricks to help you get off the ground.
Put simply, content marketing is the practice of creating and distributing content to engage—and retain—a key audience for your work. It goes without saying that truly effective content is clear, relevant and consistently caters to the audience's needs and wants. However, the question of how to create it (and the best way to publish it) is something only you can answer.
Content marketing is not new: businesses have been promoting their work in print media, such as brochures and newspapers, for generations. But the unstoppable rise of digital platforms such as social media has revolutionised the form. Now, it is easier (and cheaper!) than ever to release your content into the cybersphere—but the issue of making sure that it's actually seen by the audience you're targeting remains just as tricky.
What is the Purpose of Content Marketing?
Contrary to its name, the main goal of content marketing is not to make a sale, although it can definitely boost your chances of success. Rather, it is something called a "pull strategy": meant to rein consumers in right when they're in search of your products and services, to spark their interest in your brand, products and services. Because before you dive into a hard sell, you need to capture your audience's attention—and convince them why your brand is the best choice.
What Types of Content Marketing Are There?
By far one of the most popular forms, social media has rapidly established itself as the newest and most exciting frontier of content production. It is a broad term that encompasses a veritable cornucopia of platforms, suiting a variety of content needs. Some of the most popular digital channels include:
The world's most popular social network currently has 2.27 billion monthly active users, and that staggering figure is projected to continue rising. Its ubiquity among content creators and business owners alike is explained by its massive reach as well as its impressive range of features, such as multimedia support and customer feedback channels. Best of all, its free e-learning courses offer courses and advertising tools to help you start off right.
Once a modest photo-sharing app, this hugely popular platform has become a social media juggernaut, commanding 1 billion monthly active users. With a whopping 62% of its user base between the ages of 18 and 34, Instagram is especially useful for reaching out to that ever-elusive youth demographic. But even if you're an absolute novice at filtering photos and writing captions, you'll catch up in no time with free courses on sites like Facebook Blueprint and Skillshare
Though this medium is certainly nothing new, the rebirth of video on some of today's most popular digital channels, like YouTube and Instagram, means that it remains one of the best ways to capture—and retain—your audience's attention. While it is true that this form of content can be one of the hardest (and most expensive) to produce, you can also expect some of the highest returns known to the field of content marketing. And with a little guidance from YouTube Creator Academy, you'll be on track to growing your audience exponentially.
Traditional media has continued to endure into the 21st century, and that includes some of its most well-established formats. Articles as a medium have made a new home for themselves in the cybersphere, known for their versatility and ease of access. Whether you're setting up a blog for your business or contributing to a trade magazine, you'll pick up all you need to know on free sites like Coursera and Udemy.
Another holdover from the age of print media, graphics—in their various forms—remain as effective as ever. Whether it's editing photos of your inventory or creating infographics about your industry and business, there's never been a better time to learn how to create eye-catching graphics. And with a couple of courses on Canva and Alison, you'll be designing like a pro in no time.
How is it Done?
Armed with some basic knowledge of content marketing strategies and a few key questions, you too can become a content marketing expert. Here are six essential steps in crafting an effective marketing strategy for your business.
Understand Your Content Needs
So you know you need fresh, original content to put your brand out there. But you don't know exactly what kind, how much, or how to create it. Where do you even begin?
A good place to start is to consider your target audience. As a content creator, you should always be thinking from the perspective of those who'll consume it: what do they look for in a piece of content? Which platforms do they use most frequently? How much content is too much, and how frequent is too frequent? Once you've figured out the best way to get your content to reach the people you want, you've already won half the battle.
Clarify Your Purpose and Goals
Defining the kind of content you want to produce is also crucial to any content marketing strategy. Each piece of content usually has both a primary and secondary purpose; as a business owner or brand strategist, the secondary purpose of your content will almost always be persuasive in nature, to get audiences to support your products and services. That leaves your primary purpose open to your imagination.
Your content might be primarily informative, like an explanatory article on different styles of wedding dresses that also serves as an advertisement for your boutique. Or it could be mostly instructive, like a series of cake recipes that recommends the use of your top-of-the-line mixers. Whatever strategy you choose, make sure it's in line with the ultimate aim of your approach to content marketing: are you looking to simply raise awareness of your brand, or do you want to go a step further?
Choose the Right Distribution Channel
With a plethora of free, user-friendly platforms at your fingertips, it can be tempting to publish your content on every one to reach the biggest consumer base possible. But it's much more advisable to pick two or three platforms that are tailored to your specific needs and aims. Still, trying to choose from such a large range of platforms can be overwhelming.
Source: Wikimedia
When making your choice, keep in mind that certain channels are better suited to certain industries or audiences. For example, a travel agency looking to promote its services among young people might focus on a service like Instagram to play up the spectacular sights that customers can expect to see. It all comes down to who you want to reach, and which platform makes your content look most appealing.
Be Familiar with Your Target Audience
Of course, you mustn't forget to familiarise yourself with the key characteristics of your target demographic. (You wouldn't want to advertise palliative care services for the elderly using avocado memes!) One way to do this is by breaking it down into smaller groups, and coming up with unique traits for each of these communities. For example, consumers in the broad category of "youth" share certain attributes in terms of what they value in their content, but further segregating them by gender or interests might help you better tailor your content marketing strategy to specific groups.
Review Responses to Your Strategy
Content marketing doesn't occur in a vacuum: once you release your content into the world, it's always a good idea to take audience feedback into account. What do they like about your current approach? What did they respond negatively to? Are there ways you can improve audience engagement or increase the number of impressions?
Luckily, there's an array of tools available to measure your content metrics, both within the platforms themselves (like YouTube Studio and Facebook admin pages) and outside of them. Content marketing is all about audience receptivity, so make sure you're doing everything you can to enhance consumers' experience. The more accepting they are of your message, the more likely it is that you'll be able to convert them into customers later.
Stay Up to Date with the Latest Trends
Given the dynamic, ever-changing nature of social media, what you do after publishing your content is just as important as creating it in the first place. Keep yourself abreast of the latest content marketing trends across the globe and in your region, and make sure you're up to date on the most recent happenings taking place on your chosen platform. If it's something you can take advantage of, like a popular hashtag or brand-new fad, you can use it to boost your visibility.
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text:
\subsection*{Table of contents entry}
in functional oxides are promising for applications},
but their fabrication and use, essentially limited to SrTiO$_3$-based heterostructures,
are hampered by the need of growing complex oxide over-layers
thicker than 2~nm using evolved techniques.
This work shows that thermal deposition of a monolayer of an elementary reducing agent
suffices to create 2DESs in numerous oxides.

\textbf{Keyword}: 2DES in oxide surfaces and interfaces.\\

\begin{figure}[h]
    \begin{center}
        \includegraphics[clip, width=15cm]{Figure-TOC-Al-STO.pdf}
    \end{center}
\end{figure}

\pagebreak

A critical challenge of modern materials science
is to tailor novel states of matter
suitable for future applications beyond semiconductor technology.
Two-dimensional electron systems (2DESs)
in multi-functional oxides~\cite{Ohtomo2004}
can show metal-to-insulator transitions~\cite{Thiel2006},
superconductivity~\cite{Reyren2007,Caviglia2008},
magnetism~\cite{Brinkman2007,Li2011,Bert2011},
or spin-polarized states~\cite{Caviglia2010,BenShalom2010,Santander-Syro2014},
and are thus an active field of current research~\cite{Takagi2010,Mannhart2010,Hwang2012}.
However, the fabrication of 2DESs in oxide heterostructures, like LaAlO$_3$/SrTiO$_3$,
requires growing a layer of binary (\emph{e.g.} Al$_2$O$_3$)
or ternary (\emph{e.g.} LaAlO$_3$) oxides
with a ``critical thickness'' of at least 20~\AA~using evolved deposition techniques,
such as pulsed laser deposition~\cite{Ohtomo2004,Nakagawa2006,Takagi2010,Mannhart2010,
Hwang2012,Chen2011,Lee2012,Delahaye2012}.
Thus, the reproducibility of their properties
depends crucially on the growth parameters, while their fabrication
is complex, expensive, and unsuitable for mass production.
Moreover, the existence of a critical thickness of 20~\AA~for the onset of conductivity
severely limits the control of the 2DES's properties,
hampering tunneling spectroscopy studies or applications
that rely on charge or spin injection~\cite{Lesne2014}.
Similarly, the realization of 2DESs at the surface of SrTiO$_3$ or other oxides
requires the use of intense UV or X-ray synchrotron radiation,
to desorb oxygen from the surface~\cite{Santander-Syro2011,Meevasana2011,
Santander-Syro2012,King2012,Bareille2014,Roedel2014,Walker2014,Roedel2015}.
Thus, these 2DESs can be only manipulated and studied in ultra-high vacuum (UHV),
to preserve the vacancies from re-oxidation,
and are obviously not suited for experiments or applications at ambient conditions.

Here we demonstrate a new,
wholly general, extremely simple and cost-effective method
to generate 2DESs in functional oxides.
We use thermal evaporation from a Knudsen cell
to deposit, at room temperature in UHV, an atomically-thin layer
of an elementary reducing agent, such as pure aluminum,
on the oxide surface.
Due to an efficient redox reaction, the Al film pumps oxygen from the substrate,
oxidizes into insulating AlO$_x$, and forms a pristine, homogeneous 2DES
in the first atomic planes of the underlying oxide.
The principle of redox reactions induced by metals
at the surface of oxides is well documented~\cite{Fu2005,Fu2007}.
However, the simple idea of using a pure, elementary reducing agent
to create a 2DES at a metal-oxide interface was not explored so far.
This overcomes the complexity of growing an oxide thin film,
the requirement of a critical thickness of insulating capping layer
to create the 2DES in UHV,
and the necessity, in the case of surfaces,
of strong synchrotron radiation to desorb oxygen.
As a novel application, we extend this method to generate
a 2D metallic state at the surface of the room-temperature ferroelectric BaTiO$_3$.
Such hitherto unobserved coexistence of ferroelectricity
and 2D conductivity in the same material is promising for functional devices
using ferroelectric resistive switching~\cite{Kim2013,Tra2013}.
This new, simpler and cheaper, fabrication route for 2DESs is thus adaptable
to numerous oxides, given that oxygen vacancies are
shallow donors in these materials, resulting in itinerant
electrons.
Moreover, this technique is scalable to industrial production,
and ideally suited for applications that rely on charge or spin injection
and for the realization of mesoscopic devices.

\begin{figure*}
    \begin{center}
        \includegraphics[clip, width=16cm]{STO-Al-Capping-arXiv-Fig1.pdf}
    \end{center}
    \caption{\label{fig:STO001} \footnotesize
        (a,~b) ARPES energy-momentum intensity maps measured
        at the Al(2\AA)/SrTiO$_3$(001) interface prepared \emph{in-situ},
        using respectively $47$~eV linear vertical (LV)
        and $90$~eV linear horizontal (LH) photons.

        (c,~d) Corresponding Fermi surface maps.

        Data at $h\nu = 47$~eV were measured around the $\Gamma_{102}$ point,
        while data at $h\nu = 90$~eV were measured around $\Gamma_{103}$.

        (e,~f) Fermi surface maps measured at the Al/SrTiO$_3$(111)
        and Al/TiO$_2$(001) anatase interfaces prepared \emph{in-situ}.

        Unless specified otherwise, all spectra in this and remaining figures
        were measured at $T = 8$~K.

        }
      }
\end{figure*}

The existence of a 2DES at the interface between the oxidized Al layer and SrTiO$_3$(001),
SrTiO$_3$(111) and anatase-TiO$_2$(001)
is evidenced by our angle-resolved photoemission spectroscopy (ARPES) data
presented in \textbf{Figure}~\ref{fig:STO001}
--see the \textcolor{blue}{Supporting Information} for details about the surface preparation,
Al deposition, and ARPES measurements.
For simplicity, and to recall that we are simply depositing pure Al
(\emph{not aluminum oxide}) on top of the oxide surfaces,
all throughout this paper we note the resulting oxidized Al capping layer simply as ``Al",
specifying in parenthesis the evaporated thickness.
The energy-momentum and Fermi surface maps formed by the $t_{2g}$ orbitals,
shown in Figure~\ref{fig:STO001}, agree with previous ARPES studies
at the reduced surface of these materials~\cite{Santander-Syro2011,Meevasana2011,Plumb2014,
Roedel2014,Walker2014,Roedel2015},
demonstrating that in both cases the same 2DESs are observed.

Note that, instead of the local creation of oxygen vacancies using an intense UV beam,
the evaporated Al reduces the whole surface homogeneously.
As a consequence, the data quality, evidenced by the line widths,
is also much better than in previous studies.
Thus, as shown in Figure~\ref{fig:STO001}(a), a kink and change in intensity
in the dispersion of the light bands at $E \approx -30$~meV,
attributed to electron-phonon coupling~\cite{King2014},
can be very clearly distinguished.

The Fermi-surface areas and, hence, the charge carrier densities
of the 2DESs at the Al/SrTiO$_3$(111) and Al/TiO$_2$(001) interfaces
are about $1.3$ and $2$ times larger than their counterparts
at the surfaces reduced by photons,
probably due to a higher and more homogeneous concentration of oxygen vacancies.

\begin{figure}
    \begin{center}
        \includegraphics[clip, width=8.5cm]{STO-Al-Capping-arXiv-Fig2.pdf}
    \end{center}
    \caption{\label{fig:Al2p} \footnotesize
        (a) Angle-integrated spectra of the Al 2p peak of the Al/SrTiO$_3$(001)
        Al/TiO$_2$ anatase and Al/BaTiO$_3$(001) interfaces
        measured at a photon energy of $h\nu=100$~eV.
        The curves in different colors correspond to different thicknesses
        of Al (red 2\AA, black 4\AA, blue 6\AA).

        The peak shape of the Al 2p peak indicates if the Al layer is oxidized or metallic.

        The dashed black curve corresponds to a fully oxidized Al layer,
        obtained after annealing the sample with $4$~\AA~Al capping at 250$^{\circ}$C in UHV.

        (b) Momentum distribution curves (MDCs) at $E_F$,
        along the Fermi-surface cut schematized in the inset,
        measured at the Al/SrTiO$_3$(001) interface at $hv=47$~eV
        for different Al thicknesses. Peaks in the MDCs correspond to the Fermi momenta,
        where the MDC cuts the Fermi surface.

        The decrease in intensity of the MDCs for increasing Al thickness
		is merely due to increasing damping of the photoemission signal.

		(c) MDCs integrated over $E_F \pm 5$~meV for increasing UV exposure times
		on the Al/SrTiO$_3$(001) interface and the bare STO surface
		measured under identical conditions.
		The similarity of the two MDCs at the interface is in strong contrast
		to the evolution under light irradiation of the MDCs at the bare surface.
        }
      }
\end{figure}

To understand the redox reaction at the Al/oxide interface,
we probed the oxidation state of Al by measuring the Al-$2p$ core levels,
whose binding energies are very different for metallic and oxidized Al.
As shown in \textbf{Figure}~\ref{fig:Al2p}(a), the two contributions can be distinguished
in the Al(6\AA)/STO spectrum (blue curve), with the metallic component
around $72.5$~eV binding energy and the oxidized part around $75$~eV binding energy.
In contrast, the metallic Al component decreases for a thinner 4\AA~film (black curve),
and the deposition of only 2\AA~of pure Al results in a nearly fully oxidized
film of Al (red curves).
In other words, \emph{an ultra-thin layer of 2\AA~of pure Al is sufficient
to pump the oxygen from the surface region of all the oxides studied in this work}.
The spatial distribution of the oxygen vacancies close to the interface
is discussed in the Supporting Information.
Note that the oxidation of the metallic Al results in an increased layer thickness:
as the mass density of Al is $2.7$~g/cm$^3$ and the one of amorphous Al$_2$O$_3$
is about $4$~g/cm$^3$, the deposition of 2\AA~of Al
yields an oxidized Al film of 2.5\AA.

To determine if the thickness of the Al-layer has an influence
on the electron density of the 2DES, we turn to the momentum distribution curves (MDCs)
at the Fermi level as shown in Figure~\ref{fig:Al2p}(b).
As can be seen in Figure~\ref{fig:Al2p}(b), the Fermi momenta
are essentially the same, within $0.01$~\AA$^{-1}$
for the 2\AA~(red MDC), 4\AA~(black) and 6\AA~(blue) thick Al films.
As the 2D density of electrons depends solely on the Fermi momenta,
it is clear that this electron density already saturates at an Al film thickness of 2\AA.
Thus, our method overcomes the necessity of a ``critical thickness'' of capping layer
to generate a 2DES in UHV.

Previous studies on the bare surface of SrTiO$_3$ prepared \textit{in-situ}
showed that synchrotron UV-irradiation was necessary to create the oxygen vacancies
responsible for the 2DES~\cite{Meevasana2011,Plumb2014,Walker2014,Roedel2015}.
This is again demonstrated in the lower panel of Figure~\ref{fig:Al2p}(c),
which shows the evolution with time of the MDC at $E_{F}$
upon UV-irradiation on a bare SrTiO$_3$(001) surface.
While the 2DES is absent at $t=0$h (black MDC),
its carrier density increases up to saturation upon UV irradiation (blue and red MDCs),
as denoted by the increase of $k_F$ for increasing exposure times.

Contrary to the bare surface, there is \emph{no measurable influence}
of the UV irradiation on the electronic structure of the Al/SrTiO$_3$ system,
neither on the charge carrier density nor on the line-shapes or spectral weight of the 2DES,
as demonstrated in the top panel of Figure~\ref{fig:Al2p}(c):
the MDCs at $E_F$ show a stable subband structure and a maximum electron density
from the very beginning of the measurements.
This indicates that the oxygen vacancy concentration and distribution,
due the redox reaction at the interface between Al and SrTiO$_3$,
is already saturated and stable upon irradiation.

As demonstrated in the \textcolor{blue}{Supporting Information},
the 2DES at the interface of oxidized Al/SrTiO$_3$ is stable also at room temperature,
while the deposition of an Al film of 10\AA~or more on SrTiO$_3$
minimizes the re-oxidation of vacancies in air.

\begin{figure*}
    \begin{center}
        \includegraphics[clip, width=16cm]{STO-Al-Capping-arXiv-Fig3.pdf}
    \end{center}
    \caption{\label{fig:BTO001} \footnotesize

        (a)~AFM topography and corresponding PFM phase signal
        measured on a $30$~nm-thick BaTiO$_3/$Nb:SrTiO$_3$ film.
        No ferroelectric domains could be detected in the as-grown film,
        while such domains can be written, as shown in (b),
        with $+6$~V on the AFM tip in the outer square ($4 \times 4$~$\mu$m$^2$)
        and $-6$~V in the inner square ($2 \times 2$~$\mu$m$^2$).

        (c,~d) ARPES energy-momentum intensity maps
        at the Al(2\AA)/BaTiO$_3$ interface prepared \emph{in-situ},
        using respectively $47$~eV LV and $80$~eV LH photons,
        the latter being close to $\Gamma_{103}$.

        (e)~Second energy-derivative (negative values) of the ARPES map in (d).

        Vertical dashed red lines in (c)-(e) are the Brillouin-zone edges.

        The red curve in (e) is a cosine fit to the heavy band.

        (f,~g)~Spectral weight integrated over $E_F \pm 30$~meV
        at the Al(2\AA)/BaTiO$_3$ interface
        using $80$~eV LV and $47$~eV LV photons, respectively.

        (h)~Capacitance-voltage curve on the Al(2\AA)/BaTiO$_3$ interface
        measured previously by ARPES, showing the butterfly shape
        characteristic of a ferroelectric hysteresis.
        A Pd circular pad and the Nb:STO substrate were used
        as top and bottom electrodes, respectively.

        Note that, due to the voltage drop through the thin alumina layer,
        the voltages $V_{c}^{+}$ and $V_{c}^{-}$ required to reverse the polarization
        are rather high. Thus, it was not possible to perform a polarization reversal in PFM mode.

        }
      }
\end{figure*}
We now show that the deposition of an ultra-thin Al film
can also be used to create a 2DES at the surface
of the room-temperature ferroelectric BaTiO$_3$ (BTO),
thus constituting a new type of confined metallic state
on a truly room-temperature functional oxide.
Our BTO samples are (001)-oriented thin films (thickness $30$~nm)
epitaxially grown on SrTiO$_3$(001)
--see \textcolor{blue}{Supporting Information} for details
about thin-film growth, piezo-response force microscopy (PFM),
and capacitance-voltage (C-V) measurements.
In contrast to the bulk crystals, which
usually exhibit ferroelectric-domain stripes of period $\sim 50 - 200$~nm,
even down to $100$~nm scale thicknesses~\cite{Schilling2006},
the $30$~nm-thick BTO films deposited on Nb:STO show a single domain state,
with the ferroelectric polarization aligned along the $[001]$ axis, due to the in-plane
compressive strain induced by the epitaxial growth~\cite{Pertsev1998,Choi2004,Chen2013}.

The absence of ferroelectric domains and the local reversibility
of the polarization are demonstrated in \textbf{Figures}~\ref{fig:BTO001}(a,~b)
by the simultaneous atomic force microscopy (AFM) and PFM images
of a BaTiO$_3/$Nb:SrTiO$_3$ thin film.

The energy-momentum ARPES intensity maps of Figures~\ref{fig:BTO001}(c-e)
prove the formation of metallic itinerant states at the surface of the BTO(001) thin-film
after deposition of 2~\AA~of Al.
The resulting 2DES is constituted of a light ($d_{xy}$-like) and a heavy ($d_{xz/yz}$-like)
electron pocket around $\Gamma$, best observed in Figures~\ref{fig:BTO001}(c,~d)
with LV and LH polarizations, respectively.
Such light-polarization-dependent selection rules are typical for $t_{2g}$-like
states observed at the surface
of other titanates, such as SrTiO$_3$ and anatase~\cite{Santander-Syro2011,Roedel2015}.
In the case of BaTiO$_3$, the light band forms a strong peak of spectral weight
whose intensity is cut-off at $E_F$
--see Figure~\ref{fig:BTO001}(c).
Although we cannot observe a dispersive feature within this peak of intensity,
its binding energy indicates that the conduction band bottom
is filled up with itinerant electrons.
The heavy band, on the other hand, presents a clear dispersion
--see Figures~\ref{fig:BTO001}(d,~e).
A tight-binding fit of this band, red curve in Figure~\ref{fig:BTO001}(e),
yields a band bottom of $-115$~meV at $\Gamma$, a band top of $-35$~meV at the zone edge,
and an effective mass near $\Gamma$ of approximately $12 m_e$.

Figures~\ref{fig:BTO001}(f,~g) show that the spectral weight at $E_F$
is composed of a central disc formed by the light electron pocket,
best seen in Figure~\ref{fig:BTO001}(g),
and two orthogonal Fermi-surface strips spanning the entire Brillouin zone,
formed by the heavy bands.
These last correspond to the elliptical Fermi sheets observed at the surface
of SrTiO$_3$(001), as in Figure~\ref{fig:STO001}(d), but in the case
of BaTiO$_3$(001) they extend beyond the zone boundary,
thus forming open Fermi sheets.
From Figure~\ref{fig:BTO001}(g), the distribution of spectral weight at $E_F$
for the circular Fermi surface spans a Fermi momentum
$k_F \approx 0.15 \pm 0.02$~\AA$^{-1}$.
The Fermi strips can be approximated as rectangles
of long and short sides $k_{l} = 2 \times \pi / a$
(with $a = 4$~\AA~the size of the square unit cell at the BTO surface)
and $k_{s} = 0.15 \pm 0.02$~\AA$^{-1}$.
From the total area $A_F$ enclosed by all the Fermi surfaces,
the density of carriers of the 2DES at the BaTiO$_3$(001) surface is
$n_{2D}^{\text{BTO(001)}} = A_F/(2\pi^2)
\approx (2.8 \pm 0.4) \times 10^{14}$~cm$^{-2}$,
which is comparable to the density of states at the SrTiO$_3$
or anatase-TiO$_2$ surfaces.
The \textcolor{blue}{Supporting Information} presents additional data
showing the Fermi momenta extracted from fits to the spectra,
and the photon-energy dependence of the electronic structure.

Finally, Figure~\ref{fig:BTO001}(h) shows a measurement of the capacitance-voltage curve
on the \emph{same} Al(2\AA)/BaTiO$_3$ interface that was measured by ARPES.
The ``butterfly'' shape, with a difference of about $0.5$~V
between the two coercive voltages,
demonstrates that the BTO film is still ferroelectric after deposition of the Al layer
and ARPES measurements, thus keeping its functional behavior.

A 2DES at the surface of BaTiO$_3$ is in essence an intrinsic metal/ferroelectric interface.
Polarization switching of the bulk material, for instance by strain,
could allow a direct gating of the 2DES,
while a sufficiently thick capping alumina layer protects it
against re-oxidation at ambient conditions,
and can be even used to draw metallic nano-circuits of intrinsic ferroelectric tunnel junctions.
Thus, this system provides a realistic platform for the realization of non-volatile memories
using ferroelectric resistive switching~\cite{Kim2013,Tra2013}
or for ultra-sensitive strain or pressure detectors.

In conclusion, the method we present here for realizing 2DESs in oxides
has the advantages of simplicity and versatility
--for instance, it can be readily implemented in many UHV setups,
allowing future investigations of 2DESs
in complex oxides using non-synchrotron based spectroscopic techniques,
like tunneling or Raman spectroscopies.
This method is also pertinent for the study of transport phenomena
in mesoscopic oxide devices.
Indeed, STO has emerged as an exciting nano-electronics device platform~\cite{Goswami2015},
owing to the existence of superconductivity, spin-orbit interaction and magnetism
which are controllable with a gate voltage.
Our work opens up new possibilities to explore these questions
by making a class range of transition-metal oxide 2DESs suitable for transport,
including the surfaces which are candidates for hosting
topological electronic states~\cite{Bareille2014,Roedel2014}.
Furthermore, the stability of the 2DES in ambient conditions
can be achieved through a sufficiently thick layer of oxidized Al.
This opens the possibility to integrate TMO 2DESs
into functional devices without the need of evolved deposition techniques.

\subsection*{Experimental Section}
The ARPES measurements were conducted at the CASSIOPEE beamline
of Synchrotron SOLEIL (France).
We used linearly polarized photons in the energy range $30-110$~eV and
a hemispherical electron analyzer with vertical slits.
The angular and energy resolutions were $0.25^{\circ}$ and 15~meV.
The mean diameter of the incident photon beam was smaller than 100~$\upmu$m.
The samples were cooled down to $T=8$~K before measuring.
Unless specified otherwise, all data were taken at that temperature.
The results have been reproduced on more than 10 samples for SrTiO$_3$(001),
and on at least two samples for other surface orientations and for TiO$_2$ anatase,
and on 3 thin films of BaTiO$3$/SrTiO$_3$(001).
All through this paper, reciprocal-space directions $\langle hkl \rangle$ and planes $(hkl)$
are defined in the conventional cell of each material (cubic for SrTiO$_3$,
simple tetragonal for anatase and BaTiO$_3$).
The indices $h$, $k$, and $l$ of $\Gamma_{hkl}$ correspond to
the reciprocal lattice vectors of the cubic unit cell (SrTiO$_3$ and BaTiO$_3$)
or body-centered tetragonal unit cell (anatase).

Additional details on the sample and surface preparation, the Al deposition conditions,
and the piezo-response force microscopy and capacitance-voltage measurements
can be found in the \textcolor{blue}{Supporting Information}.

\subsection*{Acknowledgements}
We thank illuminating discussions with M.~Gabay and M.~J.~Rozenberg,
and V. Pillard for help with the sample preparation.
This work is supported by public grants
from the French National Research Agency (ANR), project LACUNES No ANR-13-BS04-0006-01,
and the ``Laboratoire d'Excellence Physique Atomes Lumi\`ere Mati\`ere''
(LabEx PALM project ELECTROX) overseen by the ANR as part of the
``Investissements d'Avenir'' program (reference: ANR-10-LABX-0039).
T.~C.~R. acknowledges funding from the RTRA--Triangle de la Physique (project PEGASOS).
A.F.S.-S. thanks support from the Institut Universitaire de France.

\section*{Supporting Information}

\subsection*{Sample and surface preparation and Al deposition}
The non-doped, polished crystals of SrTiO$_3$ were supplied by CrysTec~GmbH,
the anatase crystals by SurfaceNet GmbH.
To prepare the SrTiO$_3$ surfaces, the samples were ultrasonically agitated
in deionized water, subsequently etched in buffered HF and annealed at 950$^{\circ}$C
for three hours in oxygen flow. This results in Ti-terminated (001) or (111)
surfaces with terraces of width $50$~to~$200$~nm separated by steps,
as verified by atomic-force microscopy (AFM) in contact mode (data not shown here).

The BTO 300\AA-thick films were prepared by Laser-MBE using a sintered BTO target.
A Kr-F excimer laser was used for the deposition.
The substrate, which was etched prior to the deposition to obtain a TiO$_2$ terminating layer,
was glued to the heater with silver paste.
The growth of the film, monitored by reflection high-energy electron diffraction (RHEED),
was carried out at 650 $^{\circ}$C in 5x10$^{-4}$ mbar oxygen pressure with 0.1 \% ozone.
RHEED oscillations were used to measure the deposited thickness.
At the end of the deposition, the films were cooled down in 6x10$^{-3}$ mbar oxygen pressure,
always with 0.1\% ozone.

To clean the surfaces in UHV, the SrTiO$_3$ samples were annealed at a temperature
$T=550-650$~$^\circ$C for $t=10-90$~min at pressures lower than $p < 2\times10^{-8}$~mbar.
The anatase crystals were prepared by Ar$^{+}$ sputtering ($U=1$~kV, $t=10$~min)
and annealing cycles ($T=550-600$~$^\circ$C, $t=30$~min,)
similar to the procedure described by Setvin~\textit{et al.}~\cite{Setvin2014a}.
The surface of the BaTiO$_3$ thin films was cleaned by annealing the samples
at temperatures $T = 500-550^{\circ}$~C for $5 - 30$~min.
One of the samples was Ar$^+$ sputtered ($U = 500$~V, $t = 10$~min) prior to the UHV annealing,
without noticeable changes in the ARPES data.

The surface quality and the possible existence of surface reconstructions
was probed by low-energy electron diffraction (data not shown here).
The SrTiO$_3$(001) and BaTiO$_3$(001) surfaces are unreconstructed,
whereas the (111) surface shows a $3 \times 3$ reconstruction,
and the anatase (001) surface shows a two-domain $1\times4$ reconstruction.

To create a local, high concentration of oxygen vacancies in the surface region
of SrTiO$_3$, TiO$_2$ anatase, or BaTiO$3$, amorphous Al-films with thicknesses
between $d=2-10$~\AA~were deposited on the prepared surface of the crystals.
Aluminium was evaporated from a Knudsen cell using an alumina crucible.
The growth rate was approximately $0.3$~\AA~/min, corresponding to a temperature of
about 925$^{\circ}$C of the crucible. The Al-flux was calibrated
prior to the evaporation using a quartz microbalance. The cleanliness of the
deposit was checked by evaporating a thin Al-film on a Cu substrate
where no oxidation could be detected by Auger spectroscopy.
The temperature of the crystals ranged between $T=25-100$~$^\circ$C
during the Al deposition.

\subsection*{Piezo-response force microscopy and capacitance-voltage measurements}
For the PFM measurements, a probing signal of $2$~V$_{\textrm{pp}}$
at a frequency of 25~kHz was applied to a Co/Cr coated cantilever
with $\sim 5$~N/m force constant. A lower probing signal of $0.5$~V$_{\textrm{pp}}$
was also used with no change on the observed phase images
such as the ones shown in Figure~3(a) of the main text.
In order to assess the ferroelectric character of the BTO film measured by ARPES,
$300$~$\mu$m-diameter Pd electrodes ($200$~nm thickness) were deposited
through a shadow mask on top of the Al oxide (AlO$_x$) layer.
The C-V measurements were performed using a LCR meter with a $30$~mV$_{\textrm{pp}}$
AC amplitude at $10$~kHz, while a source-meter allowed for the DC biasing with $0.1$~V steps
of $500$~ms duration.
The C-V curve, Figure~3(h) of the main text, shows the characteristic butterfly shape
of a ferroelectric material.
Note that due to the ultra-thin AlO$_x$ layer,
the required voltages to reverse the polarization ($V_c$) are rather high
and shifted towards the positive voltage side,
indicating an internal upward electric field in the BTO layer.
For these reasons it was not possible to achieve a polarization reversal
in PFM configuration on this sample.

\subsection*{Homogeneity of the 2DES}
\begin{figure}
    \begin{center}
        \includegraphics[clip, width=5cm]{STO001_homo.pdf}
    \end{center}
    \caption{\label{fig:STO001_homo} \footnotesize
        (a) Momentum distribution curves integrated over $E_F \pm 5$~meV
        for the Al/SrTiO$_3$(001) interface prepared \emph{in-situ},
        measured at different positions (see inset) separated by at least
        2~mm from each other -or over 100 times the size of the UV spot.
        Each spectrum was obtained within minutes on a part of the sample
        that had not been illuminated before.
        The Fermi momenta, given by the MDC peak positions,
        are independent of the position in the sample,
        demonstrating the homogeneity of the 2DES
        at the Al/SrTiO$_3$(001).
        }
      }
\end{figure}

Previous studies of the 2DES at the surface of SrTiO$_3$
were conducted on fractured~\cite{Santander-Syro2011, Meevasana2011}
or \emph{in-situ} prepared surfaces~\cite{Plumb2014, Roedel2014}.
The fracturing process results in locally ordered surfaces~\cite{Guisinger2009},
while the \emph{in-situ} preparation results in an ordered surface.
The fracturing process or intense UV light irradiation at low temperature
(spot size $\approx 100\times100\upmu$m) create a local, high concentration of oxygen vacancies
in the surface region of SrTiO$_3$ whose electrons (partly) dope the 2DES.

In contrast to such spatial inhomogeneity of the 2DES
in fractured or UV irradiated bare SrTiO$_3$,
the fact that we cannot observe any changes induced by the synchrotron light
at the Al/SrTiO$_3$ interface (Figure~2(c) of the main text)
suggests that the underlying SrTiO$_3$ surface is reduced homogeneously.
This is explicitly shown in \textbf{Figure~}\ref{fig:STO001_homo},
which presents the momentum distribution curves at $E_F$
measured at five different positions on the Al(2\AA)/SrTiO$_3$ interface.
We observe that the Fermi momenta, given by the MDC peaks, are independent of the measurement point,
demonstrating the homogeneity of the interfacial 2DES over distances of several millimeters.

\subsection*{Temperature dependence of the electronic structure of the 2DES
			at the Al/SrTiO$_3$(001) interface}
\begin{figure*}
    \begin{center}
        \includegraphics[clip, width=16cm]{STO001_temp.pdf}
    \end{center}
    \caption{\label{fig:STO001_temp} \footnotesize
        (a) Energy-momentum map measured at the Al(2~\AA)/SrTiO$_3$(001)
        interface prepared \emph{in-situ} at different temperatures
        $T=$21~K, 172~K and 303~K. Data were collected around the $\Gamma_{102}$ point
        using LV photons at $h\nu = 47$~eV.

        (b) Energy and momentum distribution curves along $k_{<010>}=0$
        and the Fermi level of the $E-k$ maps in (a).

        }
      }
\end{figure*}

\textbf{Figure~}\ref{fig:STO001_temp}(a) shows the energy-momentum maps at the Al/SrTiO$_3$ interface
measured respectively at 21~K, 172~K, and 303~K,
under the same conditions as the $E-k$ map in Figure~1(a) of the main text.
The dispersions of the two light bands of $d_{xy}$-character
are still clearly visible at $T=172$~K although the line widths are increased
due to thermal broadening.
At $T=300$~K, the line widths are too large to identify the individual bands,
although the left branch of the outer band
is still visible close to the Fermi level $E_F$.
Nevertheless, the spectral weight at the Fermi level
demonstrates the existence and stability of the 2DES at room temperature.
To compare the energy-momentum maps more directly, Figure~\ref{fig:STO001_temp}(b)
shows the energy distribution curves at $k_{<010>}=0$
and the momentum distribution curves at Fermi level $E_F$.
As can be seen from the value of the Fermi momenta $k_F$ of the peaks in the MDCs
as well as the binding energies of the peaks in the energy distribution curves (EDCs),
the charge carrier density decreases slightly when temperature increases.
We checked (not shown) that these results are reproducible upon thermal cycling.

\subsection*{Effect of exposure to ambient conditions}
\begin{figure*}
    \begin{center}
        \includegraphics[clip, width=16cm]{STO001_high_energy_V2.pdf}
    \end{center}
    \caption{\label{fig:high_hv} \footnotesize
        (a) Fermi surface map measured in three neighboring Brillioun zones
        at $h\nu=459.5$~eV on the Al(10\AA)/SrTiO$_3$(001)
        interface prepared \emph{in-situ} and subsequently exposed to air
        for $t=20$~min. The red dashed circles and ellipses illustrate the Fermi surface
        shown in Figures~1(c,~d) of the main text.
        The thick red lines correspond to the borders of the bulk Brillioun zones.
		%
		(b) Angle-integrated spectrum of the Al 2p peak of the Al(10\AA)/SrTiO$_3$(001)
		interface measured at $h\nu=458.4$~eV.
		Due to the exposure to air, the Al film is completely oxidized
		--compare to Figure~2 of the main text.
        %
        (c) Energy distribution curves
        integrated around $\Gamma$ measured at the Al(10\AA)/SrTiO$_3$(001)
        and Al(2\AA)/SrTiO$_3$(001) interfaces.
        To facilitate the comparison, a momentum-independent background,
        due to spectral weight from the in-gap state, was removed
        from the EDC of the Al(2\AA)/SrTiO$_3$(001) data.
        }
      }
\end{figure*}

In principle, the thicker the oxidized Al film the better the passivation
of the surface against re-oxidation in ambient air pressure.
For amorphous Al$_2$O$_3$ films grown by atomic layer deposition on the surface of SrTiO$_3$(001),
a film thickness of $\geq 1.2$~nm is sufficient to create a stable 2DES
at the Al$_2$O$_3$/SrTiO$_3$ interface~\cite{Lee2012}.
Note that this value is identical to the thickness of the natural oxidized layer
at the surface of aluminum ($1.24$~nm)~\cite{Cai2011}.
Hence, this thickness is sufficient to prevent oxygen diffusion
through a homogenous Al$_2$O$_3$ capping layer.\\
In our case, the probing depth of the high-resolution ARPES measurements,
such as the ones shown in the main text,
is limited by the mean free path of electrons which is $\sim 5$~\AA~at kinetic energies
of $E_{kin}=20-100$~eV.
To increase the probing depth and probe the 2DES at buried interfaces,
\emph{e.g.} LaAlO$_3$/SrTiO$_3$, soft x-ray angle-resolved resonant photoelectron spectroscopy
was applied previously~\cite{Berner2013}.
Thus, to test the stability of the 2DES, we exposed an Al(10~\AA)/SrTiO$_3$ sample
to ambient conditions for about 30 minutes,
and conducted soft x-ray resonant ARPES ($hv$=459.5~eV) at low temperatures.
Note that $1$~nm of Al corresponds to about $1.25$~nm of Al$_2$O$_3$
which is close to the ``critical'' passivation thickness mentioned above.

As can be seen from the Fermi surface in \textbf{Figure~}\ref{fig:high_hv}(a), the 2DES
at the Al(10~\AA)/SrTiO$_3$ interface
still exists after the exposure to air.
For comparison,
the red dashed circles and ellipses represent the Fermi surfaces
measured at the ultra-thin Al(2~\AA)/SrTiO$_3$ interface
--see Figures~1(c,~d) of the main text.
Note that the 10~\AA~Al layer was completely oxidized
after exposure to air, as demonstrated by the peak shape of the Al-2p peak
in Figure~\ref{fig:high_hv}(b).
The data quality in these soft-X-ray ARPES measurements
is lower compared to UV-measurements
as the surface is not pristine anymore after exposure to air,
the 2DES is buried below a thick oxidized Al film,
the photoemission cross section of the valence states is much smaller
at higher photon energies, and the total energy resolution
at $hv = 459.5$~eV is about 80~meV, compared to 15~meV at $h\nu=47$~eV.
However, it is clear that the Fermi surface, and hence the charge-carrier density,
are comparable between the Al(10\AA)/SrTiO$_3$ sample exposed to air
and the pristine Al(2\AA)/SrTiO$_3$.

Figure~\ref{fig:high_hv}(c) compares the momentum-integrated band structure around $\Gamma$
for the two different interfaces,
confirming that their electronic structures are comparable.
Thus, these results demonstrate that the oxidized Al/SrTiO$_3$ interface
effectively passivates the 2DES on SrTiO$_3$.

In order to adapt the method of creation of 2DES at the Al/oxide interface to
transport measurements, and to be certain that the oxidized Al layer completely
blocks oxygen diffusion, a capping layer thickness above the ``critical'' passivation value
of $\sim 1.2$ nm is necessary.
At the same time, the capping layer suitable for transport should be insulating
without contributions of metallic Al.
Several possibilities should be explored in future studies:
optimization of growth parameters (\emph{e.g.} applying an oxygen partial pressure~\cite{Cai2011}
during deposition after the first 2~\AA~of Al and/or a slight increase of the temperature
to oxidize Al thicknesses greater than 2~\AA)
or deposition of another type of insulating capping layer after the deposition of 2~\AA~of Al.

\subsection*{Subband dispersions at the Al(2\AA)/anatase interface}

\begin{figure}
    \begin{center}
        \includegraphics[clip, width=8cm]{Al_TiO2_001_EK.pdf}
    \end{center}
    \caption{\label{fig:Al_TiO2_001_EK} \footnotesize
        Energy-momentum intensity map measured at the Al(2~\AA)/a-TiO$_2$(001)
        interface prepared \emph{in-situ}.

        The data was recorded at $T=8$~K
        using LV photons at $h\nu = 47$~eV around the $\Gamma_{102}$ point.
        }
      }
\end{figure}

\textbf{Figure~}\ref{fig:Al_TiO2_001_EK} presents the ARPES energy-momentum intensity map
at the Al(2\AA)/a-TiO$_2$(001) interface. The two subbands form the circular
Fermi surfaces shown in Figure~1(f) of the main text.
As mentioned there, these Fermi surfaces are almost twice larger
than their counterparts at the surface of anatase reduced by photons~\cite{Roedel2015}.
In agreement with this observation, the two subbands
at the Al(2\AA)/a-TiO$_2$(001) interface disperse down to larger binding energies:
approximately $-100$~meV and $-230$~meV for the upper and lower subbands, respectively,
while at the bare, reduced anatase surface they disperse only down to about
$-60$~meV and $-170$~meV~\cite{Roedel2015}.

\subsection*{Oxygen vacancy distribution at the Al(2\AA)/anatase interface}
\begin{figure*}
  \begin{center}
   	  \includegraphics[clip, width=16cm]{TiO2-XPS-Ovacs.pdf}
  \end{center}
  \caption{\label{fig:TiO2_XPS_Ovacs} \footnotesize{

    (a)	XPS at the Ti-$2p$ core level of Al(2\AA)/a-TiO$_2$~$(001)$ as a function of emission angle
    	using $h\nu = 1150$~eV photons. At this photon energy, the universal
    	inelastic mean free path of electrons emitted from the Ti-$2p$ peak
    	is $\lambda[E_{kin}(\textrm{Ti-}2p)] = 1.4$~nm~\cite{Seah1979}.

  	  	The red markers and corresponding error bars indicate the peak positions and uncertainties
  	  	for the different Ti oxidation state ($4+$, $3+$, and $2+$).

  	(b) XPS at the Ti-$3p$ core level of anatase $(001)$ at normal emission
  		as a function of photon energy. The inelastic mean free path of electrons
  		emitted from the Ti-$3p$ peak at different photon energies
  		is specified in the inset table.

  		The XPS intensity in panels (a) and (b) is normalized to the Ti$^{4+}$ peak.

  	(c)	Ratio of intensities, from panel (a), between the Ti$^{2+}$~$+$~Ti$^{3+}$ shoulder
  		and the Ti$^{4+}$ peak as a function of the electron ejection angle.
  		The dashed curve is the best fit to the data assuming a step-like distribution of vacancies
  		over $9 \pm 3$~\AA~below the surface, as schematized in panel~(d).

  	(d)	Model used for the distribution of the different Ti oxidation states
  		due to oxygen vacancies beneath the AlO$_x$/anatase interface:
  		blue line for Ti$^{2+}$~$+$~Ti$^{3+}$, red line for Ti$^{4+}$. The double arrow
  		indicates the error bar in the determination of the vacancy depth distribution.

  		}
  	}
\end{figure*}

The redox reaction creates oxygen vacancies at the Al(2\AA)/oxide interface.
The spatial distribution of these electron donors results in the creation of a potential well
confining the electrons and forming the 2DES.
To determine the distribution of vacancies,
we measured the Ti-$2p$ and Ti-$3p$ core levels of anatase $(001)$
using X-ray photoemission at $h\nu = 1150$~eV as a function of the electron emission angle,
and at normal emission as a function of the X-ray photon energy,
and fitted the peaks using either Voigt or Lorentzian line shapes together with a Shirley background.
As can be seen in \textbf{Figures~S}\ref{fig:TiO2_XPS_Ovacs}(a,~b),
the core levels are composed of several peaks (red markers)
corresponding to Ti ions of different oxidation state ($4+$, $3+$, and $2+$)
due to the presence of oxygen vacancies.
We observe that the fraction of Ti-$4^{+}$ of stoichiometric, insulating TiO$_2$
increases for larger electron escape depths, as evidenced
by the angle and photon energy dependencies in Figures~S\ref{fig:TiO2_XPS_Ovacs}(a,~b).
By contrats, the Ti-$3^{+}$ and Ti-$2^{+}$ components,
associated to free carriers and oxygen vacancies,
become increasingly important for smaller escape depths and thus, closer to the interface.\\
To obtain the concentration profile $c(z, Ti^{x+})$ of the $Ti^{x+}$ species
along the confinement direction $z$ perpendicular to the surface,
we calculate the total area of the corresponding core level peak by:
\begin{align*}
 a(Ti) \propto \int dz \sum_{x=2,3,4} c(z, Ti^{x+}) \exp\left(-\frac{d(z)}{\lambda(E_{kin})}\right),
\end{align*}
where $d(z)$ is the distance travelled by a photo-emitted electron inside matter
(\emph{i.e.}, anatase~$+$~AlO$_x$ layer), which depends on the emission angle,
and $\lambda$ the inelastic mean free path for electrons photo-emitted with kinetic energy $E_{kin}$. \\
Figure~\ref{fig:TiO2_XPS_Ovacs}(c) shows the ratio $[a(Ti^{2+})+a(Ti^{3+})]/a(Ti^{4+})$
as a function of the electron emission angle.
The error bars indicate the variation of this ratio
using different line shapes and backgrounds to fit the various Ti peaks.
We then fit the observed changes in such peak area ratio using a Heavyside function
for the concentration profile of oxygen vacancies, as shown in Figure~\ref{fig:TiO2_XPS_Ovacs}(d).
The result of the fit, shown by the dashed curve in Figure~\ref{fig:TiO2_XPS_Ovacs}(c),
yields a depth of $9 \pm 3$~\AA~for the vacancy-rich layer below the surface,
and a fraction of $(62 \pm 15)$\% of Ti ions with oxidation states $3+$ or $2+$.

\subsection*{In-plane and out-of-plane Fermi surfaces of the 2DES in BaTiO$_3$}

\begin{figure*}
    \begin{center}
        \includegraphics[clip, width=16cm]{BTO-Al-capping-KFs-HeavyBands.pdf}
    \end{center}
    \caption{\label{fig:BTO_KFs_Heavy} \footnotesize

        (a,~b)~Fermi surface maps (spectral weight integrated over $E_F \pm 5$~meV)
        at the the Al(2\AA)/BaTiO$_3$ interface
        using $80$~eV LV and LH photons, respectively.
        Data were collected around the $\Gamma_{103}$ Brillouin zone.
        The open red circles show the Fermi momenta obtained from Lorentzian fits
        to the MDCs at $E_F$. The red squares show the Brillouin-zone edges.

        (c)~MDC integrated over $E_F \pm 10$~meV
        along the left edge of the $\Gamma_{103}$ Brillouin zone,
        corresponding to a cut along the light blue arrows in panel (a).
        The blue dashed curves are Lorentzian peaks, and the black curve
        is the resulting total fit.

        }
      }
\end{figure*}

\textbf{Figures~S}\ref{fig:BTO_KFs_Heavy}(a,~b) show the Fermi-surface strips formed by the heavy bands
of the 2DES at the surface of BaTiO$_3$ (Al(2\AA)/BTO/Nb:STO interface).
The data were taken on the same Brillouin zone using mutually orthogonal photon polarizations,
which due to photoemission selection rules enhance either the Fermi strip parallel
to $k_{<010>}$ or the Fermi strip parallel to $k_{<100>}$.
The open red circles show the Fermi momenta obtained from Lorentzian fits to the MDCs
at $E_F$.  Figure~\ref{fig:BTO_KFs_Heavy}(c) shows one of such MDCs,
corresponding to a cut at the left edge of the
$\Gamma_{103}$ Brillouin zone (light blue arrows).
This MDC clearly shows a double-peak structure, corresponding to the two Fermi sheets
of the Fermi strip, which is thus open at the Brillouin-zone edge.
This is in agreement with the fact that the heavy bands running along the
$k_{<010>}$ and $k_{<010>}$ directions do not cross $E_F$,
as shown in Figures~3(d,~e) of the main text.
From these MDC fits, the average distance between opposite Fermi momenta
along the short side of the Fermi strips is $k_{s} \approx 0.15 \pm 0.02$~\AA$^{-1}$.

\begin{figure*}
    \begin{center}
        \includegraphics[clip, width=16cm]{BTO-Al-capping-hv-dependence.pdf}
    \end{center}
    \caption{\label{fig:BTO_hv_dep_d2} \footnotesize

        (a)~Raw Fermi surface map at the the Al(2\AA)/BaTiO$_3$ interface
		in the $k_{\langle 001 \rangle}$~--~$k_{\langle 010 \rangle}$ plane,
		acquired by varying the photon energy in 1~eV steps
		between $h\nu_1 = 30$~eV and $h\nu_2 = 100$~eV using LH photons.

		To calculate the momentum perpendicular to the
		surface, we use a free-electron final-state approximation,
		and set the inner potential to $V_0=12$~eV.

		The spectral weight was integrated over $[E_F - 30, E_F + 5]$~meV.

        The red square shows the edges of the $\Gamma_{003}$ bulk Brillouin zone.

        The blue and green arcs show the spherical-cap cuts
		in 3D reciprocal space obtained with $h\nu = 80$~eV and $h\nu = 47$~eV,
		respectively, corresponding to the data presented in Figure~3 of the main text.

        (b)~Second derivative (negative values only) of the Fermi surface map in (a).

        The yellow and purple dashed curves are guides to the eye showing, respectively,
        the non-dispersive Fermi surface of the light $d_{xy}$-like states,
        and the dispersive Fermi surface of the heavy $d_{xz/yz}$-like states.

        }
      }
\end{figure*}

Finally, \textbf{Figures~S}\ref{fig:BTO_hv_dep_d2}(a,~b) show the out-of-plane Fermi-surface map
of the 2DES at the surface of BaTiO$_3$,
obtained from the photon-energy dependence of the electronic structure
measured over more than an entire bulk Brillouin zone.
The inner cylinder, yellow dashed lines in Figure~\ref{fig:BTO_hv_dep_d2}(b),
is associated to the light $d_{xy}$-like band
forming the Fermi circle in the plane.  As its Fermi surface does not disperse along
the confinement direction, it corresponds to a 2D-like state.
The data also show a large ellipse dispersing along $k_{<001>}$,
hence presenting a 3D-like character, best seen in the lower part of the $\Gamma_{003}$
Brillouin zone, purple dashed lines in Figure~\ref{fig:BTO_hv_dep_d2}(b).
This Fermi sheet is associated to the heavy bands forming the Fermi strips in the plane.
Of course, such 3D-like behavior cannot correspond to a true bulk state,
as the redox reaction occurs only at the interface region.
Note also that the 3D carrier density resulting from such a state would be huge,
comparable to that of good metals, while the bulk BTO film is still insulating.
Instead, such 2D-3D dichotomy between different states forming the 2DES in BaTiO$_3$,
also observed for the 2DES at the surface of SrTiO$_3$~\cite{Plumb2014},
can be qualitatively understood as arising from confinement itself.
In the bulk, by cubic symmetry, the $t_{2g}$ bands are expected to form
3 identical mutually orthogonal Fermi surfaces similar to prolate ellipsoids
along the main crystallographic axes
--or open quasi-cylinders, when the band filling is such that the ellipsoids'
long axis extends beyond the zone boundary.
Confinement along $z$ will result, by Heisenberg's principle,
in ``de-confinement'', or elongation, of the ellipsoids along $k_z$.
When the confinement length becomes $\lesssim a$ (one unit cell),
the ellipsoid stretches over $k_z \gtrsim 2\pi/a$ (one Brillouin zone),
and the out-of-plane Fermi surface becomes a cylinder.

Thus, in the case of the 2DES at the surface of BaTiO$_3$,
we see from Figure~\ref{fig:BTO_KFs_Heavy}
that the Fermi-surface strip formed by $d_{xz/yz}$-like states
has an in-plane Fermi momentum $k_F = k_s/2 = 0.075$~\AA$^{-1}$,
while from Figure~\ref{fig:BTO_hv_dep_d2} its out-of-plane Fermi momentum
is approximately 0.4~\AA$^{-1}$.
Hence, there is an elongation along $k_z$ of the $d_{xz/yz}$ ellipsoids
due to confinement.
Similarly, as noted before, the in-plane circular Fermi surface,
formed by $d_{xy}$-like states, forms a cylinder along the out-of-plane direction.
We then conclude that the planar $d_{xy}$-like states are more tightly confined
to the surface, while the non-planar $d_{xz/yz}$-like states extend over multiple
unit cells towards the bulk. This situation is wholly similar to the case
of the 2DES at the surface of SrTiO$_3$~\cite{Plumb2014}, and simply reflects the
fact that the confinement potential is wedge-shaped,
such that electrons with a large effective mass along $k_z$ ($d_{xy}$ states)
are more confined than electrons with a small effective mass along $k_z$
($d_{xz/yz}$ states)~\cite{Santander-Syro2011,Plumb2014}.

redpajama_set_name: RedPajamaArXiv


Hotel Verde, Cape Town Airport was the first hotel in Africa to offer carbon-neutral accommodation and conferencing.
Lifts use regenerative braking on "light" travel cycles, saving 30% of the energy it would normally use. Guests can generate power for the building by taking the stairs up and taking the lift down.
Food waste composted or fed to our worm farm and goes back into the ecosystem.
Verdinos are our in-house currency, rewarding you for being involved in our hotel's sustainability and making green choices. One Verdino is equivalent to R5.
The natural vegetation adjacent to Hotel Verde Cape Town is Cape lowland freshwater wetlands. Before we intervened, the wetland was slowly degrading. Passers-by carelessly discarded refuse, and businesses and contractors dumped rubble from building work and renovations.
The wetland now boasts more than 100 types of indigenous and endemic, water-wise vegetation, an ecotrail, eco-pool, outdoor gym and two beehives, housing over 60 000 Cape honey bees.
In an environmental impact assessment, we identified some of the flora and fauna found in the wetland area since the restoration process. These include vlei grass (Paspalum vaginatum), buffalo grass (Strenotaphrum secundatum) and waterbiesie (Pycreus nitidus).
After the City of Cape Town and Airports Company of South Africa (ACSA) placed their remote plots into the caring hands of our team, the two plots were joined. They are now maintained, cleaned, landscaped and beautified on an ongoing basis. The area is a green lung in the Airport Industrial precinct for all passers-by or hotel guests to enjoy.
We cultivate our own garden using the fertile soil of the hotel's restored wetland. In that little piece of protected land, our gardeners grow organic vegetables such as tomatoes, artichokes and spinach, destined for the kitchen along with the aquaponics herbs and lettuces.
We use a vertical aquaponics system that maintains 475 plants, such as lettuce, herbs, spinach, leeks, peppers, tomato and spring onions. Tilapias (edible fish) can be found in the water tanks at the base of the system. They feed on the algae growing in the tanks, as well as small amounts of additional food. The nutrients of their waste, once broken down by a bio-filter, feeds the plants.
We harvest and regrow our plants on a constant basis, replanting every three-and-a-half months. The aquaponics system allows for virtually emission-free, cost-effective sustainable food production at a high density and saves water when compared with traditional planting methods.
The roof garden above the reception area features a number of indigenous and non-invasive plants reflecting the area's biodiversity, while also being energy efficient. The vegetative roof acts as a thermal barrier – cooling the reception below and reducing the need for air-conditioning.


I've been hearing so much about the Stringdusters as of recently. They seem to be a musician's band. When I speak to bluegrass musicians about other bluegrass bands on the scene, it's almost a sure thing that the Infamous String Dusters will be the topic of conversation. Enjoy this recent show from Asheville, NC on November 16th, 2010.


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WASHINGTON, DC – Today, President Barack Obama announced his intent to appoint the following individuals to key Administration posts:
David Benton – Member, Arctic Research Commission
Phyliss J. Anderson – Member, National Advisory Council on Indian Education
Mandy Broaddus – Member, National Advisory Council on Indian Education
Dahkota Kicking Bear Brown – Member, National Advisory Council on Indian Education
Joely Proudfit – Member, National Advisory Council on Indian Education
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Keith T. Parker – Member, National Infrastructure Advisory Council
President Obama said, "I am honored that these talented individuals have decided to serve our country. They bring their years of experience and expertise to this Administration, and I look forward to working with them."
President Obama announced his intent to appoint the following individuals to key Administration posts:
David Benton, Appointee for Member, Arctic Research Commission
David Benton is a marine resource consultant. From 2004 to 2010, he served as Executive Director of the Marine Conservation Alliance. From 2000 to 2003, he served as the Chair of the North Pacific Management Council. He has held a number of positions in the State of Alaska government from 1987 to 2000, including Deputy Commissioner of the Alaska Department of Fish and Game from 1994 to 2000. Mr. Benton was appointed to be a United States Commissioner on the U.S.-Canada Pacific Salmon Commission in 1995 and also serves on the North Pacific Research Board. Mr. Benton volunteers as President of the Alaska Lighthouse Association and is involved in restoring Point Retreat Lighthouse on Admiralty Island. Mr. Benton received a B.A. from the University of California, Santa Cruz.
Phyliss J. Anderson, Appointee for Member, National Advisory Council on Indian Education
Phyliss J. Anderson is Tribal Chief of the Mississippi Band of Choctaw Indians and is the Chief Executive Officer of the Tribal Government, a position she has held since 2011. Previously, she was Tribal Council Representative for the Red Water Community from 2003 to 2011 and Director of the Tribe's Department of Natural Resources from 1984 to 2003. Ms. Anderson chairs the boards of the Choctaw Resort Development Enterprise, Chahta Enterprises, the Choctaw Residential Center Enterprise, and the Choctaw Shopping Center Enterprise. She is a member of the boards of United South and Eastern Tribes, Inc., the National Congress of American Indians, Choctaw Missions, and the Mississippi Arts and Entertainment Advisory Board. Ms. Anderson received an A.A. from East Central Community College.
Mandy Broaddus, Appointee for Member, National Advisory Council on Indian Education
Mandy Broaddus serves as Director of Indian Education at the Montana Office of Public Instruction, a position she has held since 2009. She held other roles at the Montana Office of Public Instruction, including School Transformation Director from 2011 to 2013 and Indian Education Specialist from 2005 to 2009. From 2002 to 2005, Ms. Broaddus worked as a Principal and Dean of Students in Frazer, Montana. She taught at Fort Peck Community College in 1999, 2001, and 2005. Ms. Broaddus also served as a Teaching Assistant at the University of Montana from 2001 to 2002, the University of Colorado from 2000 to 2001, and the University of California, Los Angeles in 1999. Ms. Broaddus received a B.A. from Pepperdine University and an M.F.A. from the University of Montana.
Dahkota Kicking Bear Brown, Appointee for Member, National Advisory Council on Indian Education
Dahkota Kicking Bear Brown is co-founder of Native Education Raising Dedicated Students (NERDS), an organization of peer to peer youth study groups founded in 2012. After co-founding NERDS, he was named a Champion for Change at the age of 14 in 2013 by the Center for Native American Youth. He is also a Member of the White House Steering Committee for Generation Indigenous, the Center for Native American Youth's Executive Board, and the National Congress of American Indians National Native Youth Cabinet.
Dr. Joely Proudfit, Appointee for Member, National Advisory Council on Indian Education
Dr. Joely Proudfit is an Associate Professor in the Department of American Indian Studies at California State University San Marcos, a position she has held since 2008. She has been Director of the California Indian Culture and Sovereignty Center since 2009 and Department Chair of American Indian Studies since 2015. From 2004 to 2008, Dr. Proudfit was an Associate Professor in the Department of Public Administration and Director of the Tribal Government, Management, and Leadership MPA Program at California State University, Santa Barbara. From 2003 to 2005, she was a Lecturer in the Department of Political Science and International Relations at the University of San Diego and from 1996 to 2004, she was an Associate Professor in the Department of American Indian Studies at San Francisco State University (SFSU). From 1999 to 2000, Dr. Proudfit was Interim Chair of the Department of American Indian Studies at SFSU and from 1998 to 2002, she was Director of American Indian Studies Community Service Learning. She began her career as a Lecturer in the Department of American Indian Studies at California State University, Long Beach. Dr. Proudfit received a B.A. from California State University, Long Beach and an M.A. and Ph.D. from Northern Arizona University.
Robert O. Carr, Appointee for Member, National Infrastructure Advisory Council
Robert O. Carr is Chairman and Chief Executive Officer of Heartland Payment Systems, Inc., a position he has held since 2000. Previously, he served as Chief Executive Officer of HPS, LLC from 1997 to 2000. Prior to that, Mr. Carr was a software consultant and founded Credit Card Software Systems, Inc. in 1987. He began his career at the Bank of Illinois and as a professor at Parkland College in Champaign, Illinois. Mr. Carr received a B.S. and an M.S. from the University of Illinois at Champaign-Urbana.
Keith T. Parker, Appointee for Member, National Infrastructure Advisory Council
Keith T. Parker is General Manager and Chief Executive Officer of the Metropolitan Atlanta Rapid Transit Authority, a position he has held since 2012. Mr. Parker was President and CEO of VIA Metropolitan Transit in San Antonio, Texas, from 2009 to 2012. Prior to that, Mr. Parker was CEO of Charlotte Area Transit System (CATS) from 2007 to 2009, Assistant City Manager for the City of Charlotte, North Carolina from 2004 to 2007, and Chief Operating Officer of CATS from 2000 to 2004. Earlier in his career, he held leadership roles with the Clark County Transit Authority in Vancouver, Washington and the Greater Richmond Transit Company in Richmond, Virginia. Mr. Parker received a B.A. and an M.U.R.P. from Virginia Commonwealth University and an M.B.A. from the University of Richmond.
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