EP4003935A2

EP4003935A2 - Inorganic material with improved properties

Info

Publication number: EP4003935A2
Application number: EP20750591.8A
Authority: EP
Inventors: Mohammad Hossein EHSAEI; Bernd Spangenberg; Sidon FUTTERKNECHT
Original assignee: Agemos Ag
Current assignee: Agemos Ag
Priority date: 2019-07-23
Filing date: 2020-07-22
Publication date: 2022-06-01
Also published as: WO2021013383A2; US20220274878A1; CN114616217B; AU2020321450A1; CN114616217A; KR20220054304A; MX2022000823A; EP4003928A1; WO2021018694A1; JP2022541063A; US20220267212A1; WO2021013383A3; BR112022001144A2; CA3148234A1; DE102019005107A1

Abstract

Described is a solid body formed with Si, Al, Ca, O and at least one of Na and K, said body exhibiting in the ²⁷Al MAS NMR spectrum a signal additional to the ²⁷Al MAS NMR spectrum of pure calcium aluminate, with a chemical shift sited between that of the main peak of calcium aluminate and the peak next upfield to the main peak of calcium aluminate. Possible uses of the solid body include use as a building material with aggregates, as a coating, as an adhesive for joining two components for sanitary ceramic units, for high-temperature applications, for renovating existing edifices, especially for underwater renovation, for the erection and/or repair of built structures, particularly when high compressive strengths are needed or chemically aggressive conditions arise. It can be produced by bringing waterglass, sodium hydroxide and/or potassium hydroxide, calcium aluminate, one or more aggregates and optionally water, especially sea water, into contact, even at temperatures below 0°C without heating.

Description

Inorganic material with improved properties

The present invention relates to what is claimed in the generic term and thus relates to materials formed with Si, Al, Ca, O and at least one of Na and K.

Materials formed with Si, Al, Ca, O and at least one of Na and K are known.

They include the inorganic materials concrete and ceramics, which have a number of desirable properties, such as high strength and temperature resistance. Although the desired positive properties can often be easily adjusted due to the many years of use of the materials, both conventional concrete and conventional ceramics suffer from problems, in particular, but not only, with regard to the CO2 emissions during manufacture.

Ceramic materials are used in a number of different ways. In addition to ceramics in the classic sense of sanitary ceramics; So sinks, bathtubs, shower trays, toilet bowls, tiles, etc. are also known today technical ceramics that offer advantages due to their resistance to abrasion, high temperatures, chemical attack, etc. Given the wide range of applications, it is not surprising that ceramic materials are sometimes defined as “inorganic, non-metallic, sparingly soluble in water and at least 30% crystalline”, but this definition is not universally accepted and also not in all areas the technique is used in this way.

Nonetheless, what many of the ceramics mentioned have in common is that they are formed from a raw material at room temperature and that their typical material properties are obtained through a temperature treatment at mostly over 800 ° C. Occasionally, the shaping takes place even at an even higher temperature or even via the melt flow with subsequent crystallization.

The production of ceramics therefore requires a lot of energy, which is critical and undesirable for climatic reasons, but also leads to high energy costs in production and, moreover, requires large ovens suitable for large-volume components such as bathtubs and the like.

It would be desirable to provide alternatives for at least some of the above-mentioned applications, especially for those who require a particularly high energy requirement in the manufacture, be it due to the large mass of ceramics to be replaced or large-volume sanitary ceramic elements, be it due to the wide distribution or because of the special resistances required. It is therefore desirable to provide a replacement for at least some ceramic applications.

As for concrete, it is a widely used building material that has been used for a wide variety of different applications for a long time. The concrete and its properties vary according to the application. It may be necessary to use chemically particularly stable types of concrete, for example for port facilities exposed to seawater; Concrete can be used in applications that are particularly subject to dynamic, alternating loads, such as heavy goods traffic routes, railway sleepers, airport taxiways, etc.; strong bending and / or compressive stresses must be encountered in tension bridge construction, in high-rise construction, etc. There may be applications in which a particularly high temperature resistance is desired, for example with so-called magma or volcanic concrete, which is designed to store the heat of hot fluids, or in which the temperature resistance must be guaranteed in the event of fire. Other applications require very low density concrete, such as foamed concrete. There is concrete that should harden faster or slower, flow further or less before hardening, etc.

Since it is possible to adapt concrete recipes based on long experience, concrete types meet the respective requirements by changing the components, choosing suitable additives such as superplasticizers, surfactants, etc. What is common with conventional concrete is that cement is used to manufacture it. The German word cement goes back to the Latin name opus caementitium. Burnt lime (mostly “white lime” without clay-like constituents) and aggregates (quartz, greywacke, sandstone, tuff or broken bricks) are already present in opus caementicium. Even today, cement is still produced by burning, the raw material of modern cement, which still consists mainly of natural raw materials, is ground and mixed in the dry process and then burned, for which continuous processes are used in rotary kilns ver today; the fired material is then cooled and regrinded before use.

However, the use of this type of cement has now met with considerable ecological concerns. According to the publication "Novel binders - The time after the port land cement" by Horst-Michael Ludwig in: Concrete of the future, challenges and opportunities, 14th symposium on building materials and building preservation Karlsruhe Institute of Technology (KIT), March 21, 2018 " The huge amounts of cement that are consumed worldwide (2016: approx. 4 billion tons) and the large amount of energy required to produce it mean that the cement industry is responsible for 5 to 8% of anthropogenic carbon dioxide emissions, even though today it is particularly energy-intensive to produce , traditional port land cement is no longer used in its pure form. The dimension of the problem becomes clear in the article by a comparison with the air traffic that so often appears in the headlines. While at the time of the considerations all air traffic led to CO ₂ emissions of approx. 700 million tons annually, emissions from the cement industry were well over 2 billion tons of CO2 per year.

It is therefore desirable to be able to specify cement-free concrete alternatives for at least some, preferably for many and particularly preferably for all concrete variants.

This is true even though global cement-related C0 ₂ emissions have been reduced through the use of so-called Portland composite cements for over 20 years. Be there Certain components such as blast furnace slag and fly ash are used to manufacture cement from Group CEM II, i.e. cements containing blast furnace slag and limestone powder. CEM II cements containing fly ash have hardly been used in Germany so far. Class CEM III blast furnace elements are already playing a major role and have doubled their market share from around 10% to over 20% in the last 10 years.

In addition, alternative binders are already being discussed by cement experts as alternatives to classic Portland cement, in order to enable further CO2 savings. These include, for example - with the C02 saving potential indicated in brackets -

(A) Reactive Belite-rich Portland cement clinker (9%)

(B) Belite- Ye'elimite-Ferrite clinker (26%)

(C) Highly heated calcium silicate clinker (CCSC) (37%)

(D) Magnesium oxide, made from magnesium silicates (possibly up to 100%)

However, the savings potentials of options A - C are practically unsuccessful, whereas building materials based on option D have not yet been technically sufficiently developed, see the article "Alternative cement clinkers" by Ellis Gärtner and Tongbo Sui in Cement and Concrete Research 114 (2018) 27-39.

Therefore, neither with Portland cement nor with its above-mentioned alternative variants discussed by experts, a CO ₂ neutrality by 2050 can be achieved.

Further alternatives have therefore already been discussed. Alkali-activated cements, so-called geopolymers, which can form binders similar to portland cement from fly ash or blast furnace slag in combination with water glass, are increasingly mentioned as future cement alternatives.

It is assumed that geopolymers form structures consisting of silicon and aluminum tetrahedra, whereby it is assumed that the geopolymerization reaction endothermically new, negatively charged Al (IV) centers (tetrahedrally coordinated) are formed, which are via oxygen atoms are covalently linked to Si centers. This can only be assumed, however, because no defined pure substances are used in geopolymer research, but kaolin, metakaolin, volcanic aluminum silicates, fly ash and blast furnace slag. In [John L. Provis, Jannie SJ van Deventer, Editors Alkali Activated Materials, Springer 2014, p.95] it is pointed out that Al / Si ratios below 1 lead to unstable products and it is recommended that the Si / Al- To put the ratio in the range 1 - 5 in order to obtain usable building materials.

An example of the use of geopolymers can be found in EP 3530631 A1, which specifies a geopolymer foam formulation for a non-flammable, sound-absorbing, heat-insulating geopolymer foam element, which should comprise at least one inorganic binder selected from the group consisting of latent hydraulic binders, pozzolanic binders and mixtures thereof; at least one alkaline activator selected from the group consisting of alkali metal hydroxides, alkali metal carbonates, alkali metal aluminates, alkali metal silicates and mixtures thereof; at least one surfactant selected from the group consisting of anionic surfactants, cationic surfactants, non-ionic surfactants and mixtures thereof; a gas phase and water. The alkaline activator should be selected from alkali metal hydroxides of the formula MOH and alkali metal silicates of the formula m Si0 ₂ · n M2O, where M is the alkali metal, preferably Li, Na, K and mixtures thereof, and the molar ratio m: n <4.0, preferably less than or equal to 3.0, more preferably less than or equal to 2.0, in particular less than or equal to 1.70, and very particularly preferably less than or equal to 1.20. It is stated that the hardening behavior or the setting time of a geopolymer foam formulation can be positively influenced by the addition of cement and that Portland cement, calcium aluminate cement and mixtures thereof are particularly suitable for this purpose; Calcium aluminate cement is particularly preferred with a light color. However, neither an example of a common mixture of calcium aluminate, water, lye and water glass is described, and the calcium aluminate content should be limited to 1-20% by weight. A ratio of silicon to aluminum atoms is also given (Si / Al ratio, which should be between 10: 1 and 1: 1.

Reference is also made to WO 2010 / 121886A1, which describes an allegedly low-shrinkage binder system in which a mixture of alkali-activatable aluminosilicate binders (with aluminosilicate is probably meant "aluminum silicate") and further vegetable fats and / or oils to reduce shrinkage and for hydrophobization in alkali-activatable aluminosilicate binders. Fugenmör tel, leveling compounds or coatings that contain the specified mixture are also described. As an alkali-activatable aluminosilicate binder. Inorganic binder systems are mentioned which are based on reactive, water-insoluble oxides based on, among other things, silicon dioxide in combination with aluminum oxide. As a reactive oxide mix, for example, slag sand flour, metakaolin, slag, fly ash, activated clay or a mixture thereof can be used. The alkaline medium for activating the binder usually consists of aqueous solutions of alkali carbonates, sulfates, fluorides and, in particular, alkali hydroxide and / or soluble waterglass. It is stated that alkali metal or alkaline earth metal hydroxides should preferably be used as activators, the alkali metal hydroxides being preferred because of their high quality. The hardened binders are said to have high mechanical and chemical resistance, are more cost-effective and more stable than cement, and have a more favorable CO2 emissions balance. In one variant, the mixture should contain slag powder, fly ash and / or microsilica as a binding agent, which should contribute to better acid resistance of the binding agent (mixtures), primarily due to their preferably high proportion of aluminate and silicate. The binders mentioned should be amorphous to a high degree and have relatively high and reactive surfaces. This accelerates the setting behavior. The proportion of aluminate (as Al2O3) and silicate (as S1O2) should preferably total more than 50% by weight, particularly preferably more than 60% by weight, based on the total mass of the binder (mixture). Blast furnace slag as a particularly preferred alkali-activatable aluminosilicate binder can be used, preferably in an amount between 5 and 90% by weight, preferably between 5 and 70% by weight, based in each case on the total weight of the mixture. The flour can be used, preferably in the above-mentioned amount, alone or together with puzzolas, microsilica and / or fly ash.

WO 2010/1218861 traces the slight shrinkage of the previously known mass containing "aluminosilicate" back to the formation of calcium silicate hydrate. It is stated that the phases calcium silicate hydrate (CSH) and calcium aluminate hydrate (CAH) in cement have the property of being relatively stable to alkalis, it being stated that a suitable selection of the binders Control the properties of the hardened building materials. It is therefore explicitly not about a chemical reaction of calcium aluminum minat with silicon under basic conditions, but only about hydration, which is well known per se as the physical water absorption of cement.

Regarding the mode of action of cement containing calcium aluminate, it is stated that the alkaline cement acts as an activator when mixed with water, so that setting or hardening begins. It is stated that a 1-component system can thus be provided according to the citation, which can only be activated by adding water for setting and hardening; the alkaline cement thus acts via hydration. It is emphasized that cement is chemically relatively stable to alkalis. According to WO 2010/1218861, cement itself does not need to be present at all; rather, according to WO 2010/1218861, even mixtures that contain no cement are preferred. It is also mentioned that cement is relatively stable to alkalis, i.e. does not react chemically. This shows that WO 2010/1218861 does not regard calcium aluminate as a necessary starting material for a new material.

It should also be mentioned that inorganic polymer binders have been proposed, inter alia, for producing a coating on metallic surfaces using the material, compare DE 10 2005 046 912 A1. It is proposed there that the inorganic polymer binder is a hardening binder which contains 3% -80% thermally activated oxide mixture, 3% -50% alkali hydroxide, up to 50% alkali waterglass and 80% -20% other additives (including water) as components. This publication limits the calcium aluminate content to 0.5-5% by weight, but provides a preferred proportion between 0 to 25% by weight, the particularly preferred proportion by weight between 0 to 15% by weight and the most preferred proportion by weight between 0 to 10% by weight. In addition, a combination of water glass and alkali hydroxide is not described. Rather, with regard to the material for coating metallic substrates and surfaces, DE 102005046912 A1 states that the material is a chemically stable inorganic polymer binder, based on a cold-curing binder and free of calcium compounds. In one example too, calcium aluminate is only mentioned as a further additive in addition to several others and should not make up more than 2%.

However, the use of geopolymers cannot meet all needs. In the case of many previously known geopolymers, for example, the reaction does not take place automatically at room temperature due to the endothermic characteristics. Rather, heat must be supplied to form the negative Al centers. Another objection to the use of geopolymers is that the quantities of water glass required for cement substitution are not available (at least today) and that fly ash and blast furnace slag have long been used as additives for today's Portland cement. The requirement of a heat supply is often undesirable,

As far as the availability of water glass is concerned, the production of water glass could be upscaled, even C0 ₂ -neutral, provided that the electricity required for water glass production was obtained from solar energy. Fly ash, blast furnace slag and blast furnace slag, on the other hand, pose a major problem and will no longer be available in the desired C0 ₂ -free economy.

Conventional concrete not only suffers from the considerable CO2 emissions that occur in connection with the production of the cement required for concrete production, but also aggregates that are used in concrete production are increasingly scarce resources. It must be noted that one tonne of concrete on average only wa contains 150 kg of cement, which is particularly harmful to the climate, whereas the rest consists of sand and gravel, which are also becoming scarce worldwide, compare the article "Technology assessment on the subject of concretes of the future - challenges and opportunities," by Matthias Achternbosch in: Concrete of the future , Challenges and Chances, 14th Symposium on Building Materials and Building Preservation Karlsruhe Institute of Technology (KIT), March 21, 2018 ”, reports.

One of the particularly troublesome types of concrete is that, due to their high viscosity, only particles with a diameter of more than 2 mm can be mixed in without any problems. With grain diameters of less than 150 pm, the particularly round desert sand and fine sand, on the other hand, are unsuitable for many conventional types of concrete, such as P. Albers, H. Offermanns, M. Reisinger, in "Sand as a raw material, crystalline and amorphous", Chemistry in Our Time, 30 (2016), 162-171 reports. In addition, where smaller particles are added, in particular the energy expenditure to distribute the particles sufficiently evenly in a mass that has not yet hardened is very high, both mechanically and energetically. Both the economic and ecological costs increase significantly.

In addition, even where it is still to be used regardless of the climatic problems, concrete does not always meet the requirements despite the long years of developing better and better concrete types; this is particularly true because the temperature stability of concrete is often insufficient. Concrete decomposes from around 600 ° C, which leads to problems in particular in fire protection and tunnel construction; In the event of a fire in a tunnel, temperatures of well over 600 ° C must be expected, see also Ulrich Schneider, “Behavior of concrete at high temperatures”, ISSUE 337 (1982), GERMAN COMMITTEE FOR REINFORCED CONCRETE.

Against this background, it is desirable to be able to provide alternatives to conventional concrete that can be classified as climate-friendly or at least more climate-friendly and that achieve at least some of the desired positive properties of conventional concrete types or even have better properties.

It is therefore desirable, inter alia, but not exclusively, to provide a material that can be used as a concrete substitute, has at least its strength, is superior to this in terms of temperature resistance and C0 ₂ balance and which in particular, if necessary, the use of desert or Fine sand as an aggregate is made possible.

In addition, there are other problems with conventional, commercially available materials that make certain applications difficult or impossible, for example because there are no suitable processing options. For example, it can be desirable to create structures or components using new processes such as 3D printing, which, however, in view of the available processing machines, requires different or at least precisely controllable curing times, viscosities, etc., which is why neither conventional concrete nor conventional ceramics can be processed easily allow.

Here it would be desirable to provide a material that opens up new application or processing possibilities that are not or not readily accessible with conventional materials with comparable final properties, in particular to facilitate easier, more precise, faster and / or less energetically expensive processing to enable or even open up applications in which neither ceramics nor concrete are currently used, for example to replace the now common vitrification of radioactive substances for final or temporary storage.

It would be desirable to at least partially solve at least some of the problems mentioned.

The object of the present invention is to provide something new for commercial application.

The solution to this problem is claimed in an independent form. Preferred embodiments can be found in the dependent claims.

A first basic idea of the invention is thus initially to form a solid with Si, Al, Ca, O and at least one of Na and K, in which the Al-MAS-NMR spectrum of the solid is compared to the Al-MAS -NMR spectrum of calcium aluminate an additional signal is present which has a chemical shift which lies between that of the main peak of calcium aluminate and the peak of calcium aluminate which is closest to the main peak at a higher field.

According to the applicant's understanding, a material with such a spectrum is new because the structure leading to the spectrum itself is novel and the spectrum described is characteristic of the novel material. According to our opinion, the new material can therefore be clearly identified through the spectrum without further ado.

The fact that the solid is formed with Si, Al, Ca, O and at least one of Na and K obviously does not mean that the elements mentioned only need to be present in traces, but rather refers to the fact that essential areas of the solid, for example se a matrix embedding aggregates, with these elements as essential constituents. It will be readily understood that without deviating from the invention, for example, additives can be present that consist of different materials and therefore do not themselves result in the spectrum described.

The Si, Al, Ca, alkali metal and O contained in the material can be provided, for example, by reacting water glass, calcium aluminate, water and alkali hydroxide or alkali hydroxide solution. The use of water glass is not even absolutely necessary. Water glass provides silicon for the solid material, which is able to bind tetrahedrally; but it is also possible to provide the silicon tetrahedra in other ways besides water glass, in particular by nanoparticulate silicon dioxide. Mention should be made of Köstrosol, for example Köstrosol 1540, an aqueous dispersion of synthetic, amorphous, nanoscale SiCE particles. However, for reasons of cost, the use of water glass is clearly preferred as a rule. All types of water glass are suitable per se and generally for the reaction, regardless of the type of alkalization or modulus value. Thus, in particular, the use of water glass of low purity for technical applications is readily possible for the purposes of the present invention.

In the reaction leading to the novel material according to the invention react - activated by OH groups - negatively charged aluminum tetrahedra of calcium aluminate with charge-neutral silicon tetrahedra, which are provided, for example, by the water glass; that the negative charge of the Al tetrahedron in calcium aluminate is caused by Ca ²⁺ ions is compensated, it should be noted. Since the reaction is activated by OH groups, the calcium aluminate does not react with pure water glass solution without a sufficiently strong hydroxide, as provided by NaOH or KOH.

Such a reaction can be identified by the formation of new defined Al-O-Si bonds, which can be clearly seen in the ²⁷ A1-MAS-NMR.

In this respect, numerous references to the interpretation of

27 Al spectra, see, for example, C. Gervais, KJD MacKenzie, ME Smith, “Multiple magnetic field Al solid state NMR study of the calcium aluminates CaAl ₄ 0 ₇ and CaAl _{| 2} 0 _{| y} “in Magn. Reson. Chem. 2001, 39, 23-28; or KJD MacKenzie, IWM Brown, RH Meinhold, “Outstanding Problems in the Kaolinite-Mullite Reaction Sequence Investigated by Si and

27 Al Solid-state Nuclear Magnetic Resonance: I, Metakaolinite ”, J. Am. Ceram. Soc. 68, (1985), 293-297, and by PS Singh, M. Trigg, I. Burgar, T. Bastow, “Geopolymer formation processes at room temperature studied by Si and Al MAS-NMR”, Materials Science and Engineering A 396 (2005) 392-402.

The signals in the range of a chemical shift from 0 to 100 ppm compared to AICI ₃ · 6H ₂ O as the customary external standard to which the chemical shift is based are accordingly assigned as follows

Al (VI) at 11.77 ppm

A1 (V) at 47.19 ppm

Al (IV) at 77.68 ppm (main peak)

Pure calcium aluminate also has these peaks and the peaks can also be seen in the spectra of the material according to the invention, albeit with different intensities, but with approximately the same ppm values. It is characteristic of the material according to the invention that, in addition to the above signals of the starting material calcium aluminate, a new signal appears between the signal assigned to Al (IV) and the signal assigned to A1 (V), even if this may not be completely isolated due to overlapping , separate peak, but as the shoulder of the Al (IV) signal on the side of the higher field.

According to the applicant, this additional signal or the added shoulder in the Al spectrum can be explained by a reaction in which new bonds are formed from Al (IV) via oxygen to Si centers by substituting existing Al (IV) centers will. In this respect, it should be explained in more detail that the reaction taking place according to the applicant's understanding on the filing date is, according to the applicant's understanding, a covalent bond formation between Al and Si tetrahedra and not a hydration reaction.

As mentioned, pure calcium aluminate shows in the Al-MAS-NMR spectrum at 78 ppm a sharp signal which is assigned to the negatively charged Al tetrahedra and a broader signal at 12 ppm which is assigned to six-coordinate Al atoms. If calcined calcium aluminate is mixed with water, it hardens in the course of a conventional hydration reaction, which leads to the complete disappearance of the tetrahedral signal of the aluminum at 78 ppm, because the four-coordinate aluminum before hydration is completely converted into six-coordinate aluminum during hydration around. Therefore During hydration, the signal at 12 ppm increases by the proportion by which the signal at 78 ppm decreases. With an excess of water, the signal at 78 ppm even disappears completely due to hydration.

In the case of the new reaction described here leading to the novel solid, however, this is different. Although water is added, e.g. in the form of water contained in a water glass solution or in the form of make-up water, almost all of the aluminum remains four-fold coordinated. It does not react in the form of hydration to form six-fold coordinated aluminum.

In this respect it is also possible to characterize the new material even more precisely in that the Al-MAS-NMR spectrum of the solid also contains a peak related to the calcium aluminate signal. This is at a chemical shift of 78 ppm, whereby in the ideal case and with good spectrometers it is so strong that it is at least 3s (sigma) above the noise. It should be noted that slight shifts in this peak occur due to noise, for example, so that the maximum of the signal can shift by approximately + -0.5 ppm. The solid formed with Si, Al, Ca, O and at least one of Na and K is thus preferably further described by the fact that a calcium aluminate signal is also present in the Al-MAS-NMR spectrum of the solid, namely in the case of a chemical Shift by 78 ppm, this calcium aluminate signal being at least 3s (sigma) above the noise.

It should be pointed out that the position of the signal, which is around 78 ppm chemical shift, is very stable in terms of frequency, whereas the additional signal can have a varying chemical shift; the position of the maximum of this additional signal thus varies, between about 65-59 ppm. More precisely, the position of the signal maximum varies depending on the proportion of aluminum relative to the proportion of silicon, because the greater the additional signal related to the Al-O-Si bonds, the further away from 65 ppm and the closer to 60 ppm is the Si fraction relative to Al.

The chemical shift will, however, regularly be between 65 ppm and 59 ppm, which is why, taking into account the noise occurring during the measurement, it can reasonably be assumed that additional signals will be generated at a chemical shift between 67 ppm and 57 ppm, preferably between 65 ppm and 59 ppm is found. Accordingly, in a preferred embodiment, it may be preferred to describe the novel solid in more detail such that the chemical shift of the additional signal is between 67 ppm and 57 ppm, in particular between 65 ppm and 59 ppm.

It should be pointed out that, moreover, the additional signal can in any case be regarded as present if it is sufficiently clearly above the noise. In the case of conventional spectra, it is assumed that this is the case when the additional signal is at least 3s (sigma) above the noise. In a preferred embodiment, the additional signal will accordingly be at least 3s (sigma) above the noise. It will also be clear that - apart from noise and possibly a different spectral resolution - the specifically used Al-MAS-NMR spectrometer has no significant effect on the spectrum.

Furthermore, the newly formed, defined Al-O-Si bonds may not only be recognized in an Al-MAS-NMR spectrum based on the additional signal, but these can also be identified by a band in the IR spectrum at around 960 cm ¹ - 910 cm ¹ . The solid body formed with Si, Al, Ca, O and at least one of Na and K can thus preferably be further characterized in that it has a band at approximately 960 cm ¹ - 910 cm ¹ in an IR spectrum.

Although the solid has three spectral properties, namely the band in the IR spectrum around 950 cm, a signal in the Al-MAS-NMR signal at 77.7 ppm corresponding to the aluminum tetrahedra used and an additional signal in the Al-MAS-NMR signal between 67 ppm and 57 ppm, in particular between 65 ppm and 59 ppm, can be identified and described particularly clearly, a characterization referring to all three spectral properties is, however, not absolutely necessary.

Moreover, it will be evident that the person skilled in the art could possibly also describe the solid formed with Si, Al, Ca, O and at least one of Na and K, possibly alternatively and / or additionally, by saying that in the Al-MAS-NMR - Spectrum a signal can be found at 77.7 ppm and an additional signal between 67 ppm and 57 ppm, in particular between 65 ppm and 59 ppm. It may therefore not necessarily be necessary to refer to the higher field of the calcium aluminate peak which is closest to the main peak. Obviously, this also applies to the solid body in its preferred embodiments and the materials formed therewith, for example provided with additives, and the corresponding uses.

On the fact that, due to the newly formed Al bonds during the reaction, less aluminum is available for those bonds that were previously present in the calcium aluminate and contributed to the structure of the pure calcium aluminate spectrum, and thus the calcium aluminate spectrum, to which the new signal is added, modified in this respect, should also be noted. The formation of the new bonds thus changes the relative peak heights found in the spectrum of pure calcium aluminate.

It should also be emphasized once again that the Al-MAS-NMR spectrum of the new material differs significantly from the Al-MAS-NMR spectrum of other materials, in particular the spectra of Roman concrete and modern geopolymers.

Modern geopolymers will typically show in the Al-MAS-NMR signal at most a signal which is at 50 ppm instead of the presently relevant approximately 65 ppm; in the case of the substance present here, the signal is between 59 and 65 ppm; in addition, the spectra of modern geopolymers lack a signal with a shift of 78 ppm.

The signal peak around 78 ppm, which is characteristic of calcium aluminate, is also found neither in the spectrum of tobermorite nor in the spectrum of Roman concrete, see "Unlocking the secrets of Al-tobermorite in Roman seawater concrete" by Marie D. Jackson, Se- jung R. Chae, Sean R. Mulcahy, Cagla Meral, Rae Taylor, Penghui Li, Abdul-Hamid Emwas, Juhyuk Moon, Seyoon Yoon, Gabriele Vola, Hans-Rudolf Wenk, and Paulo JM Monteiro, Cement and Concrete Research, Volume 36, Issue 1, January 2006, Pages 18-29). Fig. 11 comes from this essay.

The lack of a signal peak of 78 ppm chemical shift is explained for Roman concrete by the fact that in the manufacture of Roman concrete the starting materials first have to be converted in such a way that the Al tetrahedron structures associated with the signal peak is associated, are only formed, unlike in the present material, with its Production of inherently starting materials with the required Al tetrahedron structure are available. This also means that the material properties that can be attributed to the -O-Si-O-Al-O bonds to be formed can be controlled particularly well in the novel material and a high level of reproducibility of the desired material properties can be achieved.

It has already been emphasized that the formation of the new bonds that take place in the chemical reaction that forms the solid according to the invention change the signal heights of the various peaks in the Al-MAS-NMR spectrum of calcium aluminate, while at the same time the characteristic, additional signal in the Al-MAS-NMR spectrum. Therefore, not only does the exact chemical shift at which the characteristic, additional signal harbors depend on the ratio of silicon to aluminum, but also the signal heights or the areas that can be assigned to the respective signals in the spectrum change. This is particularly advantageous because it allows the ratio of silicon to aluminum to be determined in a simple manner on the finished material. This, in turn, is of importance because solids according to the invention with different calcium aluminate content can be produced; Certain desirable properties such as compressive strength and chemical resistance are improved if the proportion of - comparatively expensive calcium aluminate - is increased. This makes it possible in particular to check quickly and reliably whether a material corresponds to the agreed compositions.

It turns out that the stoichiometric ratio between the silicon and aluminum tetrahedra can be freely adjusted in a range from 1: 1 to 1:12, even if only mixtures in a ratio of 1/1 to about 1/8 make sense in terms of price are. Particularly large amounts of calcium aluminate in the production of a solid with aggregates do not lead, in particular, to ever increasing compressive strength; rather, the curve “compressive strength versus calcium aluminate proportion” shows a pronounced maximum, so that the additional costs for a particularly high proportion do not bring any advantages, particularly with regard to compressive strength.

In particular for solids that are used as matrix formers or binders in a building material provided with aggregates, the Si / Al ratio is therefore less than 1, but greater than 0.1, in particular less than 1 and greater than 0.105, in particular preferably less than 1 and greater than or equal to 0.125. Since this ratio can be recognized from the Al-MAS-NMR spectrum, it is also preferred if the solid formed with Si, Al, Ca, O and at least one of Na and K for those parts of the solid that are in the Al- MAS-NMR spectrum lead to the calcium aluminate signal and the additional signal, a Si / Al ratio that can be determined based on the signal strengths of the calcium aluminate signal and the additional signal and / or based on the signal areas of the calcium aluminate signal and the additional signal is smaller than 1 and greater than 0.1, in particular less than 1 and / or greater than 0.105 or greater than or equal to 0.125.

Accordingly, in the production of the solid by contacting water glass, sodium and / or potassium hydroxide, calcium aluminate, one or more additives and, if necessary, additional water, it is also particularly preferred if such amounts of water glass and calcium aluminate are used that are in the solid lead to an Si / Al ratio less than or equal to 1, in particular less than 1 and greater than 0.1, preferably less than 1 and greater than 0.105, preferably less than 1 and greater than or equal to 0.125. Incidentally, water glass (or water glass solution), alkali hydroxide and water are preferably first brought into contact and the calcium aluminate is then mixed in. It is clear that this also opens up a control process with which it can be checked spectroscopically whether the agreed proportion of calcium aluminate was used for the production of a solid. Obviously, this is particularly important in view of the currently comparatively high costs of calcium aluminate, although it is intelligently possible to produce an inadequate solid body while adhering to an agreed proportion of calcium aluminate, for example because a reasonable amount of activating alkali is strongly deviated from. In this regard, it should be pointed out, on the one hand, that a selected Si / Al ratio results in not only the proportion of calcium aluminate and water glass but also the required amount of activating lye. On the other hand, it should be pointed out that in principle it is possible to produce a solid with, in particular, an excess of NaOH as the activating lye, but an excess of NaOH of just a few percent can reduce a final strength quite considerably. In view of the comparatively low cost of NaOH, however, deliberate deviations from the required stoichiometric ratios are unlikely.

As far as the stoichiometry is concerned, it should first be pointed out that a mixture of calcium aluminate and pure water glass like commercially available soda water glass with a modulus value of s = 4 (and thus with a Si / Na ⁺ ratio of 2: 1) theoretically results in a Si / Al ratio of 2: 1, but such a mixture will not react because the free base for activation (e.g. NaOH) is missing.

Mixtures are only reactive from a ratio of Si / Al ~ 1. The upper limit of the lye content is set by its viscosity (as an aqueous solution). Solutions of the alkali in water glass with an alkali ion content of more than 1.5, based on the alkali ion content of the water glass, can no longer be mixed with solid calcium aluminate because of their high viscosity.

The lower limit of the realizable mixtures is at a ratio of about Si / Al ~ 1: 8. Higher amounts of calcium aluminate (for ratios between 1/8 and 1/12) can only be mixed homogeneously with undiluted water glass by adding water. However, this results in hydration of the calcium aluminate and not the intended hydration competition reaction of the calcium aluminate, which leads to less stable products.

Therefore, Si / Al ratios only make sense from Si / Al ~ 0.125 (i.e. 1/8).

With regard to the proportion of alkaline solution, it can be shown that the following conditions should be met: When referring to sodium, the ratio of calcium ions of the calcium aluminate to alkali ions from water glass or the activating alkali lye (i.e.

NaOH) in a ratio of 1: 2 or greater; Al and Na should be present in a ratio of at least 1: 1, but the Al / Na ratio can also be greater than 1, which allows a calcium aluminate excess.

The concentration of OH ions used also determines the reaction rate, as does the concentration of the Al tetrahedra; a high concentration of OH ions leads to a faster reaction; the same applies to the concentration of Al tetrahedra. The higher the aluminum tetrahedra and the higher the concentration of NaOH in the mixture, the faster a material-forming mixture cures. The hardening times can be set between several hours and a few minutes or even less, with the longer mentioned hardening times being achieved with an Si / Al ratio close to 1 and the shorter Short waiting times for one at the lower limit of the Si / Al ratios indicated as meaningful.

From the above it follows that the solid can be obtained by bringing a silicon tetrahedron source into contact, in particular water glass, sodium and / or potassium hydroxide, calcium aluminate, one or more additives and, if necessary, additional water.

As far as the silicon tetrahedron source is concerned, reference is made to the use of water glass at other points in the description. First of all, it should be mentioned that the use of water glass is not mandatory. Rather, other silicon tetrahedral sources can also be used, for example silicon dioxide nanoparticles. For cost reasons, however, water glass is the preferred silicon tetrahedron source for many applications. Here, at least at the time of registration, sodium waterglass, which is sometimes also referred to as soda waterglass, is clearly preferred for reasons of cost.

Different water glasses, also different sodium water glasses, differ in terms of several properties.

Water glasses are usually made of sand and Na or K carbonate. They consist of silicates that are readily soluble in water, the negative charge of which is compensated by monovalent counter cations (M ⁺ ). Water glasses are therefore often characterized by their s-value, which indicates the mass ratio S1O2 / M2O (M = alkali metal); the smaller the s-value, the more alkali metals are present. Water glasses with different s-values are available in stores. The s-value of a water glass determines the chemical constitution of the silicate. With an s value of s = 1, the silicate has a negative charge on average. Theoretically, the s-value can drop to 0.25. Water glasses with s values of up to approx. 8 are known. For various experiments on the present invention, for example, water glasses with an s-value of 0.4-5 were used.

Aqueous solutions of water glasses are viscous. Soda water glasses usually lead to a higher viscosity than potash water glasses with the same S1O2 proportion (s-value). For the production of the material according to the invention, tests were successfully carried out with water glass solutions which have a solids content of approx. 22-52% by weight, because these water glass solutions were readily available commercially. These water glass solutions have been found to be useful.

It is possible to use a single type of sodium water glass or a mixture of different sodium water glasses. In addition, a potassium water glass, sometimes also referred to as a potassium water glass, or a mixture of different potassium water glasses can be used. In another embodiment, a mixture of sodium and potassium water glasses or glasses is used, such as a 90:10 to 10:90 mixture. For the production of the inorganic material of the present invention, one or more water glasses can be used in particular. It should be emphasized that in the present application the term “water glass” is also used to simplify reference to mixtures of different water glasses.

Since potassium water glasses and KOH sometimes react significantly faster than sodium water glasses and NaOH, it can be used especially where fast curing times are required, For example, in the case of inorganic superglue or the 3-D printing of very fine structures, it may be advantageous to use potassium material, although this is not only more expensive, but also has to be used in larger amounts by weight due to the higher molecular weight, even with otherwise the same mixing ratio .

In contrast, for particularly inexpensive solids that are required in large quantities, for example as binders to be used in construction, the less expensive sodium water glasses, especially those of technical quality or purity, are preferred.

It should also be mentioned that it is possible to produce a hydrophobic or lipophilic solid by choosing water glasses that contain an organic residue. For example, instead of purely inorganic water glasses, a water glass with a propyl residue, such as Protectosil WS808 from Evonik, can also be used. In tests, octyl-triethoxysilane and Rhodarsil R51T (tripotassium methylsilanetriolate, a methylsiliconate) have also proven to be lipophilic. Inorganic waterglass can be completely replaced if necessary, but lipophilization of the material proves to be consistent in just a few percent. An admixture of 0.5-3% octyltriethoxysilane has led to such a thorough lipophilization of the material that the material can be sanded or drilled without touching the ground or ground joint. Drilling sites lose their water-repellent properties. The functionalization is therefore continuous in the volume, i.e. H. the solid is hydrophobic or lipophilic throughout its volume. Even with the other hydrophobing silicates Rhodarsil R51T and Protektosil WS 808 tested, an admixture in the% range is sufficient for thorough lipophilization. It is to be anticipated that, in addition to the organic, hydrophobicizing siloxanes and silicates used experimentally and explicitly mentioned here, other comparable, commercially available modified silanes can be used.

Therefore, further monosiloxanes, in particular trimethoxy-n-octylsilane, dimethoxymethyl-n-octylsilane or dieethoxymethyl-n-octylsilane, disiloxanes, in particular hexamethyldisiloxane, octamethyltrisiloxane, decamethyltrisiloxane, decamethyltetrasiloxane, and also polydimethylsiliconoxane (such as dimethoxymethyltetrasiliconoxane) and also polydimethylsiliconoxane (such as dimethoxymethyltetrasilicone) and also polydimethylsilicone, in particular, such as dimethoxymethyl-n-octylsilane, and in particular polydimethylsiliconoxane, may also be mentioned e.g. octamethylcyclotetrasiloxane, decamethylcyclopentasiloxane) and also silyl ethers, in particular trimethylsilyl ether (TMS), triethylsilyl ether (TES), tert-butyldimethylsilyl ether (TBDMS), tert-butyldiphenylsilyl ether (TBDPS), silyl triisopropyl ether (TBDPS). The exact choice of the functionalizing organic silane or the functionalizing organic silanes will depend both on the costs and on the specific functionalization of the material that is required in each case. It is also evident that a material that has already been fully functionalized during manufacture has clear advantages over a material that has only been functionalized by a subsequent coating. In the construction sector, for example, this opens up the possibility of providing easy-to-clean surfaces that remain functionalized even in the event of damage.

In a particular embodiment, the solid body according to the invention will thus be a hydrophobic or lipophilic solid, in particular a solid body that is hydrophobic or lipophilic throughout its volume. It will be understood that such a solid can be produced by further providing for a production process which includes bringing a silicon tetrahedron source, sodium and / or potassium hydroxide, calcium aluminate, one or more additives and possibly additional water into contact that silanes that carry organic groups are mixed in or used exclusively are, in particular in a proportion of 0.2 to 5, preferably 1-3% by weight of the binder or matrix former.

As far as the source of the Al tetrahedron is concerned, according to the current understanding of the applicant, only calcium aluminate is suitable.

For example, a commercially available calcium aluminate such as Secar® 71 from Kerneos Inc. or a calcium aluminate from Almatis GmbH such as CA-14 or CA-270 can be used. It should be emphasized that the reaction present here is a covalent bond formation between Al and Si tetrahedra and not a hydration reaction. Unlike a hydration reaction, there is no need to form a solid structure with crystal formation and the calcium aluminate therefore does not necessarily have to be calcined; rather, it is sufficient if Al tetrahedra are present with the counterion calcium. This is a considerable advantage because the calcium aluminate to be reacted can also be produced wet-chemically at room temperature, for example from sodium aluminate and CaCl2 or CaSO4. Such a wet chemical production of the calcium aluminate has a significant positive influence on the overall C0 ₂ balance of the new material.

The new type of solid does not need to be used in its pure form. Rather, it is possible, please include to incorporate other materials, in which case the solid body according to the invention can then function as a matrix material or binder.

During the production of the solid, a mixture which is liquid for at least a short time is typically provided, in which water glass, sodium and / or potassium hydroxide, calcium aluminate and, if appropriate, additional water are brought into contact. This allows fabrics and fleeces to be soaked and thus composite materials, for example fiber mat composite materials such as carbon fiber mat composite materials, to be produced.

It is also easily possible to mix the liquid mixture or a not yet reactive starting liquid used to provide the liquid mixture with additives. If necessary, this can be done by mixing the additives into a starting liquid that is not yet reactive. The fact that only liquids have to be mixed during production and that the viscosity is low had a positive effect here. The fact that only liquids are mixed and, moreover, the viscosity is low, allows fine fractions with very little energy expenditure, i.e. H. an energy consumption significantly below that for the production of UHPC, i.e. current ultra-high-performance concrete types, and at the same time producing very homogeneous mixtures. These very homogeneous mixtures in turn cause minor cracking in the finished material. Because very fine mineral aggregates can be used without a particularly high expenditure of energy, grain compositions can also be used that correspond to an ideal grading curve. In addition, material-forming mixtures readily have self-compacting properties.

There are also a wide variety of aggregates that are suitable for use with the material of the invention. First of all, mineral aggregates may be mentioned, in particular mineral aggregates selected from the group of coarse gravel, sand, quartz powder and / or rock flour.

The mineral aggregates can in particular also be fine sand with an average grain diameter of less than 150 μm, as well as desert sand itself if this has the very round grain shape typical of desert sand, which leads to massive problems with conventional concrete; With conventional cement / concrete, only sharp-edged sand with an average grain size of> 2000 mm can be used, while fine sand and desert sand made from round grains with an average grain size of <150 μm (grain size determined by sieving; weight average) can also be used in the present invention . As in the mixture, unlike in conventional concrete, alkali contaminants do not interfere, even sand contaminated with sea salt can be used if necessary. He therefore mentions the use of sea sand and river sand.

It is also possible to use granules as additives, even if the grain size of the granules falls below 2 mm or at least for a not inconsiderable proportion of the granulate falls below 2 mm. This can be assumed if the proportion of a grain size smaller than or equal to 2 mm is at least 5%, preferably at least 10%, particularly preferably at least 25%. Even such small grain sizes can be mixed in easily and without great expenditure of energy. This makes the use of recycled concrete, recycled brick, recycled road paving, crushed weathered sandstone, crushed perlite, pumice granulate, and / or mixtures thereof as aggregates particularly attractive. As far as recyclates are concerned, it should be particularly emphasized that granules made of material according to the invention, optionally granules of a material according to the invention with added and / or functionalized material, can also be used as an aggregate. This opens up the possibility of an ecologically wanted and economically advantageous material cycle.

Fibers can also be used as aggregates, in particular fibers from the group of rock wool, glass wool, plastic fibers, plastic fibers with OH-functional groups on the surface, inorganic fibers, CNTs, glass fibers, metal fibers, steel fibers, fabric fibers, and / or mixtures thereof. Mention should also be made of the usability of renewable aggregates, in particular wood fibers or other sufficiently stable plant fibers. An admixture of plant fibers is also understood to mean mixing sawdust or sawdust.

These fibers will typically have lengths greater than 0.3 mm, preferably greater than 1 mm, in order to provide the desired mechanical properties to a sufficient extent. At the same time, fibers are preferably shorter than 5 cm, particularly preferably shorter than 1 cm; Fibers that are too long can have a blocking effect during processing, for example in pumping processes, during mixing and the like, which should be avoided; the fibers mentioned can also be embedded as a fabric, the fibers within a fabric then being allowed to be longer than the upper limits mentioned, since here the risk of blocking pumps, mixers, etc. by fibers that are too long is at best low. It should be mentioned that an improvement in the properties can be achieved by the fibers in a manner known per se.

Plastic materials can also be used as additives, in particular plastic materials selected from the group consisting of plastic materials with OH functional groups on the surface, polyurethane, foamed plastic materials and / or plastic recyclates. The preference for plastic materials with OH functional groups on the surface is due to the better integration into the material. This also explains why polyurethane-based plastics are preferred over materials like styrofoam for embedding. The integration into a matrix material with regard to glass fibers, which is facilitated by OH-functional groups on the surface, must also be observed, because these often have a coating that is unfavorable for the integration. It will also insofar it is also assumed that sand is bound into a matrix of material according to the invention through the formation of OH bonds on the surface.

Mention should also be made of the usability of inorganic additives as additives, in particular inorganic additives selected from the group consisting of inorganic pigments, lead oxides, iron oxides, iron phosphate, calcium phosphate, magnesium phosphate, BaSCC, MgSCC, CaSCC, Al ₂ O ₃ , metakaolin, kaolin , Wollastonite. The use of such oxides allows the material to be used for colored and permanently color-fast design objects. In addition, shielding properties against radioactive radiation can, if necessary, be improved by suitable additives, such as additives containing lead. Thus material according to the invention is also particularly suitable to be used instead of the otherwise required glazing of radioactive waste.

The usability of aggregates - and, where desired, their combination - expands the possible applications considerably. In this regard, attention is drawn to the fact that the use of suitable aggregate materials means that at most little, typically no relevant shrinkage occurs during the production of the material. This also extremely reduces crack formation when the material hardens; It should be mentioned, however, that cracking can still occur due to poor material choices; ergo, where cracking is to be avoided, it must be ensured that cracking is reduced by volume-stable additives.

The use of suitable aggregates also makes the material particularly suitable for lightweight construction, since high flexural strengths are achieved even with little filler or matrix material, which then favors the use of thin structures. It should be mentioned that the surcharges are naturally limited for particularly high requirements in terms of fire protection.

Considerable proportions of aggregates can be added; The amounts of the constituents of a solid to which aggregates are added are preferably as follows: a) Water glass: 2.5 - 12.5% by weight (calculated as solid)

b) alkali hydroxide: 0.7 - 7% by weight

c) Water: 6.8-20% by weight

d) Calcium aluminate: 10 - 70% by weight

optional e) additives such as sand: 0 - 80% by weight

where the total amount of a, b, c, d and e) is considered 100%.

It should be mentioned that the large amount of additives that can be added makes a molded body to be produced with the material according to the invention cheaper.

It has already been emphasized that a solid body according to the invention with additives is made easier due to the use of liquids for the starting material.

The material according to the invention can be produced from a medium-viscosity liquid and a powder or, alternatively, from a liquid phase and a high-viscosity suspension. When producing from a medium viscosity liquid and a powder, the medium viscosity liquid can comprise water glass solution and alkali hydroxide, the liquid component having proven to be stable for at least five months, and the powder component comprising calcium aluminate and possibly additives. These can be, for example, in Ratio of 1: 1 to be mixed. If, on the other hand, a liquid phase and a highly viscous suspension are to be used to produce the material, the highly viscous suspension can comprise the water glass solution, calcium aluminate and any additives; Such a suspension has been shown to be stable for about a week, similar to Speis. Long-term stable, aqueous alkali metal hydroxide can be added to this suspension for the reaction. Typically, alkali hydroxide: suspension ratios of 1:20 to 1:50 can be used; processes in which a highly viscous suspension is combined with an alkali hydroxide liquid phase are particularly suitable for 3-D printing. It should be mentioned that where fine sands with a grain diameter of <500 μm are used as aggregate, it has proven advantageous to mix the fine sand with water glass and lye first and then to add the calcium aluminate.

Against this background, it is clear that in a preferred embodiment, the process for the production of a material according to the invention by bringing a silicon tetrahedron source into contact, in particular water glass, sodium and / or potassium hydroxide, calcium aluminate, one or more additives and, optionally, additional water in this way it is stated that sodium or potassium hydroxide is used as an aqueous solution.

As far as the optional addition of water is concerned, it should be emphasized again that the present reaction to form the novel material comprises a covalent bond formation between Al and Si tetrahedra and not a hydration reaction. For this reason alone, water must not be used in excess.

The reactive aluminates that are used to form the material, however, absorb a certain amount of water. The calcium aluminates used in the examples consist of 29% CaO and 71% Al2O3, which corresponds approximately to a 3: 1 mixture of “CA” and “CA ₂ ”, which is why the calcium aluminates used have a molecular formula (CaOjhAkOsF (C4A5) with a molar mass of 734.

These reactive aluminates take up the following maximum amounts of water:

CaO · AI2O3 · 10 H ₂ 0, (CA · 10 H ₂ 0)

CaO · 2A1 ₂ 0 ₃ · 8 H ₂ 0, (CA ₂ - 8 H ₂ 0)

However, these hydrates are not stable and then decompose in a process known as “conversion” to 3 CaO · AI2O3 · 6 H ₂ O, Al (OH) 3 and water.

Theoretically, one mole of the (CaOüiAüOsü used can absorb 38 moles of water, but only stably bind 8 + 7 = 15 moles of water per mole of (Ca0) 4 (Al ₂ 03) 5. This happens, however, as part of a hydration reaction .

With the new binder, on the other hand, it has been experimentally shown that almost exactly 10 moles of water are incorporated per 1 mole of calcium aluminate (C4A5). This suggests that exactly one water molecule per Al center is required in the end product for charge stabilization and corresponds to less water incorporation than with simple hydration of

(Ca0) 4 (Al ₂ 0 ₃ ) 5.

It may therefore be necessary to use an amount of water - albeit a limited one. On the one hand, the viscosity of the reaction solutions is influenced by the amount of water, which is advantageous in order to set a desired viscosity; the viscosity of the reaction solutions can be adjusted by varying the amounts of the starting materials at 20 ° C. in a range of 25-700 mPa. At the same time, the amount of water - like the calcium aluminate content - influences the hardening time, which could be set between 50 seconds and 90 minutes for the mixtures examined here. The ability to adjust the curing times and the viscosity make the material-forming reaction solutions easily suitable for 3-D printing.

Where water is to be added, no distilled or even deionized water is needed; the use of plain tap water is sufficient, but not even mandatory. Since the material according to the invention - unlike conventional concrete, which contains no alkali ions but a high proportion of calcium and silicon - has a molar ratio of alkali cations (usually Na ⁺ and / or K ⁺ ) to calcium that is around 1 : 2, the material-forming reaction is very alkali-tolerant. This makes it possible to use alkali-contaminated water, especially sea or salt water. In one embodiment of a method for producing a material according to the invention by bringing a silicon tetrahedron source into contact, in particular water glass, sodium and / or potassium hydroxide, calcium aluminate, one or more additives and water, it is therefore provided that sea or salt water is added. The alkali tolerance even allows rock salt to be incorporated, as experiments have shown in which stable stones with up to 80% rock salt could be produced.

The material-forming reaction presented here, in which higher-energy Al (IV) -0-Al (IV) bonds are substituted by lower-energy Al (IV) -0-Si bonds, is also advantageous in that it takes place exothermic as a whole . Mixtures for the production of the patented material hardened even at temperatures of -24 ° C, which obviously offers advantages in the conduct of the reaction in particular if the material is to be produced at low temperatures without additional heating measures. This has a significant advantage over conventional concrete in winter construction, which according to the relevant DIN may not be processed at temperatures below 5 ° C.

For the course of the reaction forming the material according to the invention, it should be noted that the calcium aluminate used in the reaction does not react with pure water glass solution without a sufficiently strong activator being present to activate the negatively charged aluminum tetrahedron of the calcium aluminate by OH groups to implement with the silicon tetrahedron provided by water glass. Both NaOH and KOH are suitable as activators, while other, weaker alkalis such. B. LiOH or NH ₄ OH, the basicity can prove to be insufficient to start the reaction at normal Temperatu ren.

A stoichiometrically correct mixture of the reactants is required for complete conversion, since otherwise unreacted starting materials remain, which is undesirable insofar as the stability of the material formed is adversely affected. It is also considered to be advantageous if there is a sufficient amount of water to be incorporated into the material being formed in the mixture.

During the reaction, negatively charged Al tetrahedra react with OH ions in a stoichiometric ratio of at least 1: 1; the ratio between the calcium ions of the calcium aluminate and the alkali ions, e.g. B. Na ⁺ from water glass and from for activation If NaOH is used, it must be 1: 2 or greater, as the alkali ions serve to exchange the Ca ²⁺ ions that carry the equalizing charge for the negative Al tetrahedra in the calcium aluminate. The exchanged calcium ions are completely converted into Ca (OH) 2, which precipitates. The precipitation of the Ca (OH) 2 during the reaction is currently regarded as an important driving force of the reaction, which is why the use of calcium aluminate is essential for the reaction according to the current understanding of the applicant.

While the material formed is no longer stable in water if too little calcium aluminate is used, it is easily possible to use more calcium aluminate than is stoichiometric required to bind the nations through the negatively charged Al tetrahedra. The ratio, AG: Na ⁺ should be at least 1: 1, whereby the desired compressive and flexural strengths and the hardening time can be set via the ratio AG: Na ⁺ or Ca ²⁺ : Na ⁺ . It should be noted in this context that the hardening times also depend on the Si: Al ratio and the amount of water, as can be seen from other parts of the description. It has already been disclosed that the ratio of Si tetrahedra and AG tetrahedra can be freely adjusted in an Si / Al range from 1/12 to 1/1. With the expected use of calcium aluminate and water glass as aluminum tetrahedron source or silicon tetrahedron source, the preselected Si / Af ratio then determines the amount of Ca aluminate to be used as AG tetrahedron source relative to the amount of water glass to be used as Si tetrahedron source.

In view of the overall exothermic, material-forming reaction, it will be clear that a method for producing a material according to the invention by bringing a silicon tetrahedron source into contact, in particular water glass, sodium and / or potassium hydroxide, calcium aluminate, one or more additives and water Certain conditions are preferably carried out at ambient temperatures above 30 ° C, in particular above 35 ° C without cooling measures or without heating measures at temperatures below + 5 ° C, in particular below 0 ° C. However, it must be anticipated that where particularly fast reactions are desired, for example in 3-D printing, a reaction acceleration, i.e. an acceleration of curing, can be achieved by additional heating measures. It should be mentioned in this regard that it has already been shown experimentally to be possible to allow the reaction to proceed at least at +60 ° C.

Regardless of the fact that extremely short hardening times may be achieved for very special applications, possibly through additional heating, it should be emphasized that hardening times are achieved even without such measures, which allow very early stripping of the formwork in molds and also a very early high one Ensure strength. The times until the formwork can be stripped is significantly shorter than with concrete, for example; this can result in very significant cost advantages or quality advantages in view of the likewise very early high strength compared to precast concrete parts.

In this respect, it should be emphasized that the material that can be used as a binder hardens both under water and on foot in a temperature range from -20 ° C to + 80 ° C and without shrinkage, the material according to the invention then proving to be absolutely stable to concentrated aqueous acids and joints and - assuming suitable aggregates - can withstand temperatures of over 1000 ° C without loss of stability; Tests have also been carried out to ensure that the material can be exposed to temperatures of up to 2400 ° C. It can also be assumed that the material is frost-resistant; repeated freeze-thaw cycles did not lead to material damage in first attempts. At the same time, with suitable material mixtures, compressive strengths can be achieved that are about twice as high as with the most powerful concrete types known on the filing date. The flexural strengths also considerably exceed those of concrete. WUR achieved with the material according to the invention in tests, for example, flexural strengths measured according to DIN 1038 of up to 17 N / mm, which corresponds to about three times the flexural strength that can be achieved with conventional concrete.

There are also advantages over concrete in terms of the carbon dioxide balance of up to 75% with the same compressive strength. This is due not only to the low production energy requirement for the raw materials used, but also to the unproblematic integration of even very fine aggregates such as dusts, fine-granular recyclates and desert sands, which is possible due to the high stability can be used with an inert substance content of up to about 80% by weight of the form body mass. The fact that the wide range of aggregates that can be used allows recourse to locally available aggregates and / or to renewable aggregates such as wood, wood shavings or sawdust, which can therefore be transported to a manufacturing site with little energy expenditure, is particularly emphasized.

As can be seen from the above, there are therefore a number of positive properties both in the manufacturing process and in the finished material which, alone or together, make the use particularly attractive for a large number of applications. He mentions positive properties that are technically particularly significant - which are partly obtained independently of the exact composition of the material-forming mixture and partly can be attributed to additives, in particular easily available inexpensive additives and / or additives required in only small quantities These include the rapid hardening, the favorable CCE balance, the worldwide availability of the essential basic raw materials, the consistent colorability, the usability of fine sand in the micrometer range and / or desert sands, the early mechanical stress without a ripening period, the algae stability, the Self-compression, the acid resistance, the chloride resistance, the possibility of obtaining ceramic properties without burning depending on the active ingredient, the ability to adjust different densities, the complete recyclability, the high temperature resistance up to 1000 ° C and above, for example up to 1200 ° C, the usability with 3 -D prints, the consistent hydrophobability, the sometimes even significantly longer service life compared to comparable materials such as concrete, the absence of shrinkage or shrinkage, the ability to achieve high strengths of over 50 megapascals, especially with suitable mixtures of even over 150 megapascals, the Curing not only at room temperature, but especially between + 60 ° C and -25 ° C without heat, curing under water and the absence of cement.

The fact that the material retains its good properties even in contact with organic and vegetable materials opens up applications in the wood sector, e.g. for chipboard as a formaldehyde-free adhesive, for joining wood fiber concrete panels and for producing panels that replace such panels, in wood fire protection, in the replacement of wood concrete and for furniture production.

The fact that the material is not flammable makes it easy to use in fire protection. The material can be used, for example, for fire bars with expanded glass, fire bars for windows or fire protection panels in lightweight construction. The high temperature resistance also makes it suitable for furnace construction. It should also be emphasized that material can easily be used as joint material and tile adhesive due to its good adhesive properties. Another advantage here is the acid resistance of the material, which improves the cleaning options. Due to the chemical resistance, further applications also include the manufacture and / or coating of sewer pipes, industrial pipes and separators.

It also opens up the possibility of embedding color pigments and providing high-quality surfaces, if necessary also providing functionalized high-quality surfaces such as hydrophobic surfaces, possible applications for example in the area of kitchen worktop production, for plaster, acoustic panels, heavy sound insulation, as design concrete and for Interior surfaces of parking garages.

It has already been emphasized that the rapid hardening makes material-forming mixtures also ideally suited as adhesives and as starting materials for 3-D printing.

Since the material is inexpensive, but still offers high resistance, other applications include tunnel linings, the replacement of ceramic hybrids, the provision of embedding compounds in the disposal or use of recycling material, screed replacement, and use as filling compounds, e.g. for bricks or hollow blocks and the manufacture of railway sleepers and other pre-fabricated molded bodies question, with the rapid curing of particular advantage in the area of building materials that can be manufactured quickly under high price pressure.

With regard to the production of prefabricated parts, it should also be emphasized that formwork can easily be removed by using oil as a separating agent on plastic or metal formwork skins, regardless of the low degree of shrinkage, even with conventional formwork, as is also used in concrete production is. It should be mentioned that, for example, in precast factories or on site, the short cycle times made possible by the short curing times when using a given formwork for the repeated production of similar components can, if necessary, be further shortened by, for example, the use of folding formwork; reference is made to WO 2004 / 065087A2 by way of example only.

According to the above, it is clear that a preferred use of the solid according to the invention is to use it as an adhesive for connecting two components and / or for repairing an existing structure, in particular for underwater repairing a structure.

According to the above, it is also evident that another preferred use of the solid according to the invention is to use it as a building material for the construction and / or repair of structures, in particular structures with a required compressive strength of at least 30 N / mm ² , preferably at least 40 N / mm ² , in particular more than 60N / mm ² at at least some of the locations using the solid as a building material and / or at locations exposed to chemically aggressive conditions and / or at locations to be built in the presence of water or are to be repaired, and / or in particular as a matrix former in a solid body provided with aggregates, which is used as a building or repair material for the aforementioned building structure. According to the above, it is further evident that another preferred use of the solid body according to the invention is to use it for the production of a sanitary ceramic element or for the production of one to withstand temperatures above 700 ° C, preferably above 1000 ° C, particularly preferably above 1500 ° C required body. Incidentally, where ceramic surfaces are to be made particularly smooth, it is obviously advantageous not to use any coarse aggregates such as sand that is too coarse. The smooth surfaces that are obtained without the use of sand make the material readily suitable as a ceramic substitute, the functionalizations offering additional advantages and, moreover, the apparently continuous functionalizations being able to offer application advantages over known, only superficial functionalizations. As an application in which a very high temperature stability is desired, the construction of thermal storage systems, in particular thermal high-temperature solar storage systems, should also be mentioned, in which fluid initially heated in solar power plants with strong solar radiation flows through a body of high heat capacity in order to maximize it to heat high temperatures, and in which subsequently, with weak or complete lack of solar radiation, cool res fluid is passed through the bodies heated to high temperatures in order to heat the cool res fluid and then use this heat, for example to generate electrical energy. These bodies of high heat capacity can be created with the material according to the invention.

With regard to the temperature behavior and, in particular, the temperature change behavior, it should also be pointed out that the material according to the invention withstands temperature changes, including very rapid temperature changes, well. For example, material according to the invention could be heated to red heat in a Bunsen burner flame (approx. 1200 ° C) and then abruptly cooled in water without breaking or cracking, even with repeated, frequent temperature changes. The material is accordingly to be regarded as temperature-resistant with temperature changes of more than 100 ° C, preferably more than 200 ° C, particularly preferably more than 500 ° C and very particularly preferably more than 1000 ° C, for both heating and cooling, whereby The heating and / or cooling around the temperature differences mentioned can in particular take place at a rate of temperature change of greater than 100 ° C / min, preferably greater than 200 ° C / min, in particular greater than 500 ° C / min, particularly preferably greater than 1000 ° C / min ; The rate of temperature change is preferably even greater than 1000 ° C./30 seconds, preferably 1000 ° C./15 seconds. It will be evident that this opens up further applications. It was also possible to allow a thermite reaction to take place in a vessel made of the material without the vessel being destroyed. This can be seen as proof of resistance up to over 2000 ° C.

It will also be apparent from the foregoing that another preferred use of the solid body according to the invention is to use it to produce a coating, in particular a corrosion protection coating for metals and / or a coating for water-bearing structures, in particular for sewer pipes and / or with Use areas in sewage treatment plants in contact with clarifying wastewater. A coating that consists of a thin layer of the solid or is built up with it is regarded as claimable and patentable, as is a composition forming such a coating, in particular a multi-component composition forming such a coating. As far as coatings are concerned, they can be made very fine-grained or very smooth on the surface. Experience shows that tactile smooth surfaces are obtained with the material according to the invention, provided that no additives such as sand that is too coarse are used. The fact that a functionalization of the material and thus also a functionalization of the surfaces can be achieved through additives, such as hydrophobization or fipophilization in connection with the use of the material for coatings.

One of the advantages of using it as a coating is its resistance to biogenic sulfuric acid, which often occurs in ducts. Where cement-based concrete is attacked, a seal formed with the material according to the invention can be applied, unless entire components are completely formed with the material according to the invention from the outset. Particular mention should be made of coatings in sewage treatment plants, where a closed-cell material that is extremely smooth and dense and does not require an organic coating is desired.

It should also be mentioned that the coating material can be applied without the use of volatile solvents, which is a considerable advantage, especially when processing in closed rooms, especially since the mixtures are odorless per se. The coating can also be applied to rusty base material without derusting it beforehand, as the material adheres well, seals well and is stress-free. It will also have to be estimated that the material is more stable to C0 ₂ than concrete, because a reaction of CO2 with water could possibly occur inside the material.

The invention is further explained by way of example below with reference to the accompanying drawing, the drawing shows:

Fig. 1: ²⁷ A1-MAS -NMR spectrum of calcium aluminate (Almatis ^® CA- 14)

2: ²⁷ A1-MAS-NMR spectrum of the solid obtained in Example 5

3: ²⁷ A1-MAS-NMR spectrum of the solid obtained in Example 6

4: ²⁷ A1-MAS-NMR spectrum of the solid obtained in Example 7

5: Kinetics of the solid-state formation reaction on the basis of IR spectra; The figure shows the change in the IR absorption spectrum of a mixture of water glass and calcium aluminate that was activated with NaOH:

5 a shows the change in the IR spectra in transmission between 650 and

2000 cm ¹ ,

Fig. 5b shows the absorption between 650 and 1200 cm ¹ . Absorptions above

1300 cm ¹ are caused by water. The conversion of a Si-O-Si bond into an AG-O-Si bond as the dominant bond, which is associated with a shift from 995 to 920-960 cm ¹ , can be clearly seen.

Fig. 6 Compressive strengths achieved for various Si / AG ratios (reaction with

Soda water glass, NaOH, calcium aluminate and various amounts of quartz flour to set identical initial viscosities of the reaction mixture).

Fig. 7 ²⁷ A1-MAS-NMR spectrum (Si-Al ratio 0.875) with the maximum of the

Binding peaks at 59.3 ppm and in the IR at 943 cm ¹ .

Fig. 8 ²⁷ Al -MAS-NMR spectrum (Si-Al ratio 0.625) with the maximum of the

Binding peaks at 59.1 ppm and in IR at 940 cm ¹ .

Fig. 9 ²⁷ Al -MAS-NMR spectrum (Si-Al ratio 0.375) with the maximum of the

Binding peaks at 63.4 ppm and in IR at 943 cm ¹ . Fig. 10 ²⁷ Al -MAS-NMR spectrum (Si-Al ratio 0.125) with the maximum of the binding peak at 65.0 ppm and in the IR at 952 cm ¹ .

Fig. 11 ²⁷ Al -MAS-NMR spectrum of Roman concrete (state of the art)

A number of example samples were first prepared in accordance with the present invention in order to investigate the extent to which different mixing ratios and starting materials affect the compressive strength and density of the material obtained. In addition, further properties such as the color of the material obtained and the ²⁷ Al-MAS -NMR spectra were investigated for a number of samples.

To determine the density, the volume and weight of a rectangular sample body was determined and the density was calculated as weight / volume.

The compressive strength of the samples was measured using a Z250 universal testing machine from Zwick / Roell. For this purpose, the compressive forces (in N) were graphically recorded over the deformation path. The maximum pressure reached was related to the surface (mm) of the sample.

The following measurement parameters could be used to record the NMR spectra Al-MAS-NMR spectroscopy: 4 mm MAS BB / ¹ H probe in a Bruker AVANCE III 400 WB (magnetic field 9.4 T; rotation frequency 9 kHz) with a frequency of 104.3 MHz For

27 Al, a single pulse excitation (1 ps pulse length; round trip delay 0.5 s), and a 1 M aqueous solution of AICI3 · 6H ₂ O as external standard (0 ppm). In the figures, which show NMR spectra, the chemical shift in ppm based on the external standard is plotted on the x-axis and the signal strength in arbitrary units on the y-axis.

The following materials were used for Examples 1 to 9:

Betolin K35: potassium water glass, s = 2.6; Wöllner GmbH, aqueous solution with 35%

Solids content

Betol K5020T: potassium water glass, s = 1.49; Wöllner GmbH, aqueous solution with

48% solids content

Protectosil ^® WS8O8: water glass with propyl residue, s = 0.4; Evonik; 55% solids content

Secar ^® 71: calcium aluminate (AI ₂ O ₃ > 68.5%, CaO> 31.0%), Kerneos Inc.

Almatis ^® CA 14: calcium aluminate (Al2O3 = 71%, CaO = 28%), Almatis GmbH, Frankfurt

Na48 / 50: Sodium water glass, s = 2.6, Wöllner GmbH, aqueous solution with

44.5% solids content

Na50 / 52DS: Sodium water glass, s = 1.54, Wöllner GmbH, aqueous solution with

48% solids content

Na38 / 40: Sodium water glass, s = 3.4, Wöllner GmbH, aqueous solution with

35.8% solids Quartz powder: 1205-SIKRON-Quartz SF800

Compressive strength and density

First of all, the compressive strength and density of material samples were investigated using various examples 1-4

example 1

100 g K35, 100 g K5020T, 36 g WS808, 50 g KOH, 64 g water) were mixed with 600 g Secar ^® 71 and 60 g quartz flour. The mixture could be stirred for five minutes and was solid after 20 minutes. The density of the cured material was 2.13 g / cm, the compressive strength 179 N / mm ² .

Example 2

K35 100 g, 100 g K5020T, 36 g WS808, 50 g KOH, 64 g of water) was mixed with 600 g Almatis ^® CA-14 and mixed 60 g quartz flour. The mixture could be stirred for five minutes and was solid after 20 minutes. The density and compressive strength of the cured material were comparable to those of Example 1.

Example 3

80 g Na 48/50, 20 g Na50 / 52DS, 21 g NaOH, 29 g water were mixed with 350 g Secar ^® 71 and 4.3 g KH2PO4. The density of the cured material was 2.11 g / cm, the compressive strength 132 N / mm ² .

Example 4

80 g Na 48/50, 20 g NA50 / 52DS, 21 g NaOH, 29 g water were mixed with 350 g Almatis ^® CA-14 and 4.3 g KH2PO4 mixed. The density and compressive strength of the cured material were comparable to those of Example 3.

It was therefore found that the compressive strength can be significantly higher than that which can be achieved with concrete on the filing date.

Spectra of the material - 1

Solids according to the invention were then prepared using a number of material mixtures with different ratios of water glass to calcium aluminate and examined spectroscopically. For this purpose, the following water glass-water mixtures were used in Examples 5-7:

WG1: 9.92 g NaOH, dissolved in 20 g water, mixed with 100.2 g Na38 / 40

WG2: 19.98 g NaOH, dissolved in 10 g water, mixed with 100.6 g Na38 / 40

Almatis CA-14 was used as the calcium aluminate.

Example 5

A concrete substitute was made from 40 g Almatis ^® CA-14 and 19.4 g WG1; the mixture was solid and gray in color after 32 minutes. The density was determined to be 2.21 g / cm and the compressive strength to be 101.3 N / mm ² . (Sample Bl) Example 6

A concrete substitute was made from 40 g Almatis ^® CA-14 and 9.48 g WG1; the mixture was solid and white in color after 3-4 minutes. (Sample CI)

Example 7

A concrete replacement was prepared from 40g Almatis ^® CA-14 and 28.86 g WG2; the mixture was solid and gray in color after 20 minutes. The density was determined to be 1.97 g / m 2. (Pro be Dl)

The ²⁷ A1 MAS-NMR spectra from Examples 5-7 are shown in Figures 2-4. Fig. 1 (Pro be A) shows a comparison of the ²⁷ A1 MAS NMR spectrum of Almatis ^® CA-14. This ²⁷ A1 MAS-NMR spectrum shown in Fig. 1 was with a 4 mm MAS BB / 'H probe in a Bruker AVANCE III 400 WB (magnetic field 9.4 T; rotation frequency 9 kHz) with a frequency of 104.3 MHz for Al, a Single pulse excitation (1 ps pulse length; round trip delay 0.5 s), and a 1 M aqueous solution of AICI ₃ · 6H ₂ 0 as an external standard (0 ppm).

In the introduction, reference has already been made to literature on the interpretation of Al spectra. Taking into account the references cited above, the signals in the range from 0 to 100 ppm in FIG. Can be assigned as follows

Al (VI) at 11.77 ppm

A1 (V) at 47.19 ppm

Al (IV) at 77.68 ppm (main peak)

It should be mentioned that when using a different device and / or slightly different measurement conditions the exact appearance of the spectrum could deviate somewhat from FIG. 1; Even then, however, the three characteristic peaks mentioned would be recognizable in the range from 0-100 ppm (with AICI ₃ · 6H ₂ 0 as 0 ppm standard).

The main peak at around 78 ppm is characteristic of calcium aluminate and is not found, for example, in the spectrum of tobermorite or in the spectrum of Roman concrete (see Fig. 11 from "Unlocking the secrets of Al-tobermorite in Roman seawater concrete" by Marie D. Jackson, Sejung R. Chae, Sean R. Mulcahy, Cagla Meral, Rae Taylor, Penghui Fi, Abdul- Hamid Emwas, Juhyuk Moon, Seyoon Yoon, Gabriele Vola, Hans-Rudolf Wenk, and Paulo JM Monteiro, Cement and Concrete Research, Volume 36, Issue 1, January 2006, Pages 18-29).

FIGS. 2-4 show that these three signals of the calcium aluminate can also be seen in the spectra of the material according to the invention with approximately the same chemical shifts in ppm, but with different intensities. It is characteristic of the material according to the invention, as the spectra in FIGS. 2 to 4 show, that in addition to these signals of the starting material calcium aluminate, a new signal appears between the signal assigned to Al (IV) and the signal assigned to A1 (V), even if this may not be seen as a separate peak due to superimposition, but as a shoulder of the Al (IV) signal on the side of the higher field. The additional signal or the added shoulder in the Al spectrum is currently explained in such a way that, during the material-forming reaction, new bonds from Al (IV) via oxygen to Si centers through the substitution of already existing Al (IV) - Centers are formed; In view of this understanding, it is considered important for the presented reaction that high-energy Al (IV) -0-Al (IV) - Bonds are replaced (substituted) by lower-energy Al (IV) -0-Si bonds. Overall, this makes the reaction exothermic, and so it can take place at room temperature.

The material according to the invention can accordingly be described in such a way that it contains the three peaks of calcium aluminate and additionally one in an Al-MAS-NMR spectrum in the range from 0-100 ppm (when using AICI ₃ · 6H ₂ O as an external standard) Signal between the main peak and the peak closest to the higher field, this signal can be present as a shoulder. Of course, as new bonds form, the relative peak heights change compared to those in the spectrum of calcium aluminate.

kinetics

The kinetics of the solid-state formation reaction were then examined using IR spectra; What is shown here is the change over time of the IR absorption spectrum of a mixture of water glass and calcium aluminate according to the invention activated with NaOH. In order to illustrate this change, several spectra recorded in the course of the reaction are superimposed in the figures. The spectra recorded later have the stronger bands.

FIG. 5 a shows the change in the IR spectra in transmission between 650 and 2000 cm ¹ , FIG. 5 b shows the absorption between 650 and 1200 cm ¹ . Absorptions above 1300 cm ¹ are caused by water. The conversion of a Si-O-Si bond into an AG-0-Si bond, which is associated with a shift from 995 to 920-960 cm ¹ , as the dominant bond of the bond, can be clearly seen in FIGS. 5a and 5b. The IR spectrum of the solid material according to the invention accordingly shows a characteristic band around 960-910 cm ¹ . It should be mentioned that conventional geopolymers oscillate between 960 and 1000 cm ¹ at slightly higher wave numbers. It should also be mentioned that two characteristic shifts of the water bands to about 1390 cm ¹ and to a signal between 2800 and 3000 cm ¹ can also be observed in the IR spectrum, see also FIG. 5.

Aggregates of different grain sizes

It was then examined how aggregates of different grain sizes affect density and compressive strength.

Example 8A and B

102 g Na38 / 40, 10 g NaOH, 50 g water and 925 g coarse crushed stone were mixed with 165 g Secar ^® 71 (A) or 165 g Almatis ^® CA14 (B). Density: 2.27 g / cm ³ (A), compressive strength: 40.9 N / mm (A); Density and compressive strength for (B) were comparable.

Example 9A and B

102 g NA38 / 40, 10 g NaOH, 18 g of water were mixed with 325 g desert sand (grain size 120 pm) and 180 g of Secar 71 ^® (A) or 180 g Almatis ^® CA14 (B) are mixed. Density: 2.01 g / cm ³ (A), compressive strength: 37.5 N / mm (A), flexural tensile strength: 7.8 N / mm (A); The density, compressive strength and flexural strength of (B) were comparable.

Carbon dioxide emissions

It was then calculated for various samples produced practically according to the invention what reduction in the CO ₂ emissions during the production of the invention Material compared to concrete can be obtained.

The CCE emissions that are released during the production of concrete cannot be reduced below a fixed limit value, as around 2/3 of the CO2 emissions released during the production of concrete are due to the conversion of CaCCE to CaO. If the emission is calculated with 0.75 tons of CO2 for each ton of cement produced, or 0.354 tons of CO2 for one m of concrete with a compressive strength of 40 N / mm, the CO2 emissions can be compared with those released when using the mixture according to the invention if it is assumed that water glass, NaOH and, to a limited extent, calcium aluminate are produced using solar power generated without emissions.

The values given in the example recipes for the reduction of C0 ₂ emissions refer on the one hand to the C0 ₂ emissions in the production of concrete of the specified quality available today and on the other hand to the C0 ₂ emissions of water glass, NaOH and calcium aluminate Assumes the exclusive use (100%) of solar power in the manufacture of the required raw materials.

Example 10:

6.4 g NaOH + 86 g water glass Na38 / 40 with 36 g calcium aluminate (and 330 g construction sand) is solid after 90 minutes (final hardness: 41 N / mm ² ). The Si / AG ratio is 1/1. (Proportional CO2 emissions, based on concrete: 20%)

Example 11:

14 g NaOH + 86 g water glass Na38 / 40 with 50 g calcium aluminate (and 370 g building sand) is solid after 180 minutes (final hardness: 30 N / mm ² ). The Si / AG ratio is about 3/4 (5.7 / 8). (Proportional C0 ₂ emissions, based on concrete: 24%)

Example 12:

14 g NaOH + 86 g water glass Na38 / 40 with 50 g water and 35 g calcium aluminate (and 680 g building sand) is solid after 24 hours (final hardness: 11 N / mm ² ). The Si / AG ratio is 1/1. (Proportional C0 ₂ emissions, based on concrete: 11%)

Example 13 (maximum value from Fig. 6):

30 g NaOH + 32 g water glass Na38 / 40 and 68 g water glass Na48 / 50 with 70 g water and 370 g calcium aluminate (and 31 g quartz flour) is solid after 12 minutes (final hardness: 155 N / mm). The Si / AG ratio is 1/8. (Proportional C0 ₂ emissions, based on concrete: 100%)

It should be noted in the last example in particular that a very high final strength was achieved there, and the quartz powder, i.e. a very fine aggregate, was incorporated, which typically leads to a considerable amount of mixing energy required in high-performance concrete, which is not comprehensive and in the general considerations was correctly considered. This means that overall considerable amounts of CO2 can be saved.

Lipophilization

It was then examined how the material can be functionalized by using different functionalizing silanes. During the production of the solids, water glass, sodium hydroxide and calcium aluminate and the required amounts of water were brought into contact with the various functionalized silanes and the solids obtained were then examined.

It has been found that the lipophilic compound octyl-triethoxysilane lipophilizes the entire batch when it is mixed with the binder in a range of 0.5-3%. This not only makes the surface water-repellent, but the entire stone. So you can grind or drill without the stone losing its water-repellent properties in the appropriate places.

Even if the water glasses Rhodarsil R51T (tripotassium methylsilane triolate, a methylsiliconate) or Protektosil WS 808 (tripotassium propylsilane triolate, a propylsiliconate) were mixed in between a few% and 100% as a water glass substitute, a consistent fipophilization of the stones was achieved.

Silicon nanoparticles as a source of Si tetrahedra

It was then investigated whether the material according to the invention can also be produced without water glass.

In order to show that a material according to the invention can also be freely produced waterglass, the SiCE nanoparticles (here: Köstrosol 1540) were caused to react with calcium aluminate instead of waterglass. 10 g of Köstrosol, mixed with 3 g of NaOH and 20 g of calcium aluminate, were solid within 3 minutes. SiCE nanoparticles can therefore easily function as a Si tetrahedron source.

Mixtures for fast curing

Various mixtures were used to investigate how the curing time can be shortened.

100 g K42 (Betolin K42 from Woellner), 20 g KOH, 50 g water with 55 g water and 420 g calcium aluminate. The mixture is solid after 90 seconds, with a compressive strength of 123 N / mm ² .

100 g K35 (Betolin K35 from Woellner), 20 g KOH, 50 g water with 55 g water and 425 g calcium aluminate, solid after 8 min, with a compressive strength of 169 N / mm.

Si / Al ratio 0.33: 100 g Na38 / 40 (Betol 38/40 from Woellner), 10 g NaOH, 10 g water, 250 g calcium aluminate, 125 g desert sand, solid after 12 min, with a compressive strength of 162 N / mm ² .

It should be emphasized that mixtures with such rapid curing are already very well suited for 3D printing. Surcharges

Recipes as described in Examples 1-13, various additives were added in order to check whether a good material bond was possible.

In this way it could be confirmed that a good material bond of the mixtures with the following aggregates is obtained: aluminum oxide, quartz powder, blue quartz flour, titanium dioxide, metakaoline, polyfill, Ceratec, Granoflour Röhrig gray, Granoflour yellow, concrete recycling material, fine rubber granulate, coal , Barium sulfate, concrete gravel, red concrete gravel, mica, talc, fireclay, corundum, microsicilica, poraver in various grain sizes, namely 0.06-0.125; 0.25-0.5; 0.5-1.0; 1.0-2.0; Liaver in different grain sizes, namely 0.25-0.5; 0.5-1.0; 1.0-2.0; 2.0-4.0; Wood chips; Gutex wood fiber; Wood chips, expanded clay; Aeroballs; Aeropor 180; Aeroballs 0.5-0.7, Nabalox, Alfa Tab 0-0.5045; Alfa Tab 0-0.6; Wollastonit Tremin 263-100, Lumiten 3108, as well as various types of sand, namely ultra-fine sand, recycling sand 0-2 mm; Desert sand from China, Dubai, Oman, Jordan and Tunisia, quartz sand from Krauchenwies on the Swabian Alb and unscreened sand from a Portuguese sandy beach. It was possible to produce stable solids with all these materi alien, these solids being sufficiently abrasion-resistant for applications to be anticipated without further res.

It was checked whether the different aggregates interfere with one another or whether a good connection can be established through the material according to the invention. For this purpose, layers of material were hardened with an aggregate in a mold and then further layers of material with different aggregates each were brought to harden in order to determine whether a stable material composite was obtained. A first “sandwich” was created with material layers that contained desert sand, aluminum hydroxide and brick recycling material, as well as another “sandwich”, the material layers of which consisted of sliver, wood and concrete gravel as aggregates. These layers of material were found to be stable; H. no separation failure occurred at the layer boundaries.

As far as mineral aggregates are concerned, it was then investigated whether, when using aggregates of very different grain sizes, segregation occurs before curing. For this purpose, a recipe was used that had a long hardness time of over 60 minutes for the material according to the invention. Such a mixture was mixed with mineral additives of different grain sizes, poured into a column mold and placed with this on a vibrating table in order to investigate whether long-lasting vibrations could provoke segregation. It was found that despite the long-lasting rubella no segregation occurred.

As far as wood as aggregate is concerned, wood chips of different types of wood were also combined with one and the same material mixture resulting in the material according to the invention to form a chipboard. In this way, stable chipboard could be produced without the need for heating under pressure. The material mixture resulting from the material according to the invention was thus used as a binder. Wood shavings were used for different samples of both hardwood species and coniferous wood species to check whether one and the same material according to the invention is in principle suitable for connecting different wood shavings to one another, which could be answered in the affirmative. When using the same binder for different types of wood, no differences were found. To check the fire resistance, chipboard panels were then flamed with a Bunsen burner using the material according to the invention. For this purpose, a waterglass mixture of 102g K35, 10g H20, 12g KOH was made up and 74g of this made up mixture was again mixed with 100g calcium aluminate and 60g wood fiber as well as 9.4g R51T and hardened in plate form. It was found that after a flame time, at which conventionally manufactured chipboard panels were already on fire, no damage was observed on the chipboard panels produced with the material according to the invention.

Maximum compressive strength

It was then investigated how the compressive strength can be influenced by varying the ratio of Si / AG ratio for given starting materials.

After it was initially determined that particularly high compressive strengths result when the Si / Al ratio is particularly small, whereas only lower compressive strengths can be achieved when the Si / Al is larger, i.e. less aluminum is used in relation to the silicon, the compressive strength for particularly low Si / Al ratios was investigated. By correspondingly varying the mixing ratios of a material-forming mixture according to the invention, the compressive strength curve in FIG. 6 could be recorded. This shows that if the Si / Al ratios are too low, the compressive strength decreases again, so the use of the expensive calcium aluminate in excess does not result in any advantages in terms of mechanical stability.

Spectra of the material - II

It was then investigated how the variation in the Si / AG ratio affects the 27 Al-MAS-NMR. For this purpose, samples of the material according to the invention with un different mixing ratios of a material-forming mixture according to the invention were produced in such a way that samples with the desired Si / AG ratio result.

Table 1 lists the amounts of NaOH, waterglass Na38 / 40 and calcium aluminate used in each case to produce the samples with the desired Si / AG ratios. In addition to waiting times and compressive strength after five and 21 days for these samples, Table 1 also lists them.

Tab. 1 Data of various mixing approaches with curing times and compressive strengths, measured after 5 and 21 days.

Si / Al NaOH Na38 / 40 Ca-Alumnt curing time N / mm 2

0.125 14.2 g 86 g 286 g 5 min 57 (5 days)

0.156 20 g 100g + 10g H20 268 g 17min 77 (21 days)

0.231 10 g 100g + 10g H20 180 g 20 min 60 (21 days)

0.375 14.2 g 86 g 96 g 100 min 75 (5 days)

0.625 14.2 g 86 g 58 g 140 min 32 (5 days)

0.875 9.1 g 91 g 44 g 50 min 47 (5 days)

The 27 Al-MAS-NMR spectra recorded on these samples are shown in FIGS. 7-10. Please note that the scaling of the X-axis is sometimes slightly different. These spectra show that the new binder or the new solid-state material can not only be identified per se by the Al-MAS-NMR, but that further relevant information can also be obtained from the spectrum. In this context, important conclusions can be drawn from the strengths of the signals at the respective peaks or from the area values of the signals by comparing the strengths or area values of different signals.

The ratio of the area value of the signal is around 65 ppm, i.e. the actual binding signal from the -O-Si-O-Al-O bonds, to the area value of the signal at 78 ppm, i.e. the signal of the -O-Al-O- Bonds, from 0 - if only -O-Al-O bonds are present in the calcium aluminate - to over 10. The value in the upper signal ratio range close to 10 is limited by the recognizability of the at 78 ppm, because for Si / Al- At ratios close to 1 the signal at 78 ppm will be very small and possibly even close to zero, because the calcium aluminate will react almost completely at this Si / Al ratio. However, NMR devices are generally very good today. It is therefore possible with today's NMR devices to set a detection limit of 3s (sigma) for the 78 ppm signal, and despite this strict criterion for a clear recognizability of the 78 ppm signal in a material according to the invention, even if it was generated with a ratio of Si / Al almost equal to 1, at which practically all calcium aluminate should have been converted to still find unreacted calcium aluminate in an amount sufficient for spectral recognition, for example in insufficient through mixed areas.

Against this background, the peak areas for the three signals to be assigned to the calcium aluminate and for the additional signal were determined. If the peak area of the individual signals is normalized to the total area in the spectrum, values as shown in Tab. 2 result. Per se, the observed signals of the calcium aluminate at the values 78 ppm, 47.2 ppm and 11 ppm together with the additional signal should make up 100% of the total area; however, some of the peak area values differ slightly, which can be ascribed to effects such as noise, inaccuracies in the calculation due to the superimposition of curves, etc. Nevertheless, it can be clearly seen that the signal component of the signal increases significantly by 65 ppm with the Si / Al ratio. It should be noted that the signal at 47.2 ppm, which can be assigned to a five-coordinate aluminum, plays no role in the reaction.

Tab. 2 Peak area values in percent of the individual 27 Al signals.

Ratio signal at

Si / Al- 78 ppm 65 ppm 47.2 ppm 11 ppm 65ppm / 78 ppm

0 80.8% 0.0% 6.7% 12.5% 0

0.125 40.1% 17.6% 3.1% 39.2% 0.4

0.156 25.1% 30.6% 3.1% 34.5% 1.2

0.231 2E6% 38.8% 3.1% 36.5% 1.8

0.375 7.40% 49.5% 3.1% 40.0% 6.7

0.625 7.58% 56.2% 3.1% 33.1% 7.4

0.875 11.7% 62.0% 3.1% 23.2% 5.3 In a corresponding way, instead of the area values, the peak heights of the individual signals can also be determined in the Al-MAS-NMR. The corresponding, relative signal levels are listed in Tab. 3, a relative normalization again being carried out. Again, the signal at 47.2 ppm, which can be assigned to a five-coordinate aluminum, plays no role in the reaction.

Tab. 3 peak height values (in percent) of the individual 27 Al signals.

Ratio signal at

Si / Al 78 ppm 65 ppm 47.2 ppm 11 ppm 65ppm / 78 ppm

Ö 80.8% 0.0% 6.7% 12.5% Ö

0.125 40.0% 12.5% 3.5% 44.0% 0.31

0.156 33.9% 25.5% 3.5% 37.1% 0.75

0.231 40.6% 19.8% 3.5% 36.1% 0.49

0.375 15.5% 26.8% 3.5% 54.2% 1.7

0.625 16.8% 40.4% 3.5% 39.3% 2.4

0.875 35.3% 38.6% 3.5% 22.6% 1.1

Exemplary compositions at range limits

Against the background of the experiments, mixtures were then defined which lead to the formation of material with very large or very small Si / Al ratios; for comparison, a reaction mixture was also defined which gives a material with an Si / Al ratio in between. These mixtures are only intended to give examples of reaction mixtures for the range limits, without being themselves limiting. The reaction mixtures of Tab. 4 are proposed as an example. As far as a mixture to achieve a material just below the Si / Al ratio of 12:12 is concerned, it will be understood that the calcium aluminate content is then slightly reduced and the water glass is reduced partly increased.

Tab. 4 Marking out the area boundaries

Si / Al ratio 1:12 8:12 12:12

Calcium aluminate 70.2% 35.0% 26.3%

Water glass (solid) 5.10% 19.9% 22.0%

NaOH (solid) 2.34% 9.10% 4.70%

Water 22.4% 36.0% 47.0%

The proportion of inert substances can be up to 80%. The weight percentage ratios listed above decrease to a maximum of 1/5 of the above values if they are related to the weight of a structural element provided with aggregates. The proportion of calcium aluminate in the total mass required to produce construction elements of a given mass does not fall below the value of 5.26%, even for such a high proportion of inert substances.

With regard to KOH and potassium water glass, the values for lye and water glass are a maximum of a factor of 56/40 = 1.4 higher than those for sodium hydroxide and sodium silicate. The proportion of inert substances can be increased up to 80%. The percentage ratios listed above decrease to a maximum of 1/5 of the above values. Thus, the calcium aluminate content of no mixture falls below the value of 5.26%. Above, among other things, but not exclusively a with Si, Al,

Ca, O and at least one solid formed by Na and K, which in the 27 Al-MAS-NMR spectrum to the Al-MAS-NMR spectrum of calcium aluminate has an additional signal with a chemical shift between that of the main peak of calcium aluminate and the calcium aluminate peak closest to the main peak towards the higher field. The solid is, among other things, as a building material with supplements, as a coating, as an adhesive to connect two components, for sanitary ceramic elements, for high temperature applications, to repair existing structures, in particular for underwater repair, for construction and / or repair can be used by structures, especially when high compressive strengths are required or chemically aggressive conditions occur. It can be produced by bringing water glass, sodium and / or potassium hydroxide, calcium aluminate, one or more additives and optionally additional water, in particular seawater, into contact, even at temperatures below 0 ° C without heating.

Claims

PATENT CLAIMS

1. With Si, Al, Ca, O and at least one of Na and K formed solid, characterized in that in the 27 Al-MAS-NMR spectrum of the solid compared to the

27 Al-MAS-NMR spectrum of calcium aluminate an additional signal is present which has a chemical shift which lies between that of the main peak of calcium aluminate and the peak of calcium aluminate which is closest to the main peak towards the higher field.

2. With Si, Al, Ca, O and at least one solid formed by Na and K according to the preceding claim, characterized in that a calcium aluminate signal is also present in the Al-MAS-NMR spectrum of the solid, namely at one chemical shift of 78 ppm, with the calcium aluminate signal at least 3s (sigma) above the noise.

3. With Si, Al, Ca, O and at least one of Na and K formed solid according to egg nem of the preceding claims, characterized in that the chemical shift of the additional signal between 67 ppm and 57 ppm, in particular between 65 ppm and 59 ppm.

4. With Si, Al, Ca, O and at least one solid body formed from Na and K according to one of the preceding claims, characterized in that the additional signal is at least 3s (sigma) above the noise.

5. With Si, Al, Ca, O and at least one of Na and K formed solid according to one of the preceding claims, in which the Al-MAS-NMR spectrum contains the additional signal and a calcium aluminate signal with a chemical shift of 78 has ppm,

characterized in that

a

for those parts of the solid,

which lead to the calcium aluminate signal and the additional signal in the 27 Al-MAS-NMR spectrum,

based

the signal strengths of the calcium aluminate signal and the additional signal

and or

based

of the signal areas of the calcium aluminate signal and the additional signal

certain

Si / Al ratio

less than 1 and greater than 0.1

preferably less than 1 and greater than 0.105

is particularly preferably less than 1 and greater than or equal to 0.125.

6. With Si, Al, Ca, O and at least one solid formed from Na and K according to one of the preceding claims, characterized in that it has a band at about 960-920 cm ¹ in an IR spectrum.

7. Hydrophobic solid according to one of the preceding claims, in particular throughout the entire volume of hydrophobic solid according to one of the preceding claims.

8. Shaped body with a matrix or a binder made of a solid according to one of the preceding claims, characterized in that the shaped body further comprises at least one material selected from the group of

mineral aggregates,

in particular one selected from the group

Coarse gravel,

Sand,

Desert sand,

Rock salt,

sea salt contaminated sand,

Fine sand with an average grain diameter of <150 pm,

Quartz flour,

and mixtures thereof

Granules,

in particular one selected from the group

Recycled concrete, recycled bricks, recycled pavement, crushed weathered sandstone, crushed perlite, pumice granulate and mixtures thereof,

and / or with a proportion of a grain size smaller than or equal to 2 mm of at least 5%, preferably at least 10%, particularly preferably at least 25%; Fibers,

preferably fibers selected from the group

Rock wool, glass wool, plastic fibers, plastic fibers with OH functional groups on the surface, inorganic fibers, CNTs, glass fibers, metal fibers, steel fibers, fabric fibers, wood fibers, in particular sawdust, wood shavings and / or wood wool and mixtures thereof,

wherein the shaped body is in particular a wood fiber-containing board made with material according to the invention,

and or

with lengths

be larger than 0.3 mm, preferably larger than 1 mm

and or

smaller than 5 cm, preferably smaller than 1 cm;

Plastic materials,

in particular at least one selected from the group

Plastic materials with OH-functional groups on the surface, polyurethane, foamed plastic materials, plastic recyclates; and mixtures thereof.

inorganic additives, preferably selected from the group inorganic pigments, lead oxides, iron oxides, iron phosphate, calcium phosphate, magnesium phosphate, BaSCL, MgSCL, CaSCL, AI2O3, methaolin, kaolin, wollastonite and mixtures thereof.

9. Use of the solid body according to one of the preceding claims as an adhesive for connecting second components and / or for repairing an existing building, in particular for underwater repairing a building.

10. Use of the solid body according to one of claims 1 to 8 as a building material for the construction and / or repair of structures,

in particular structures with a required compressive strength of at least 30 N / mm ² , preferably at least 40 N / mm ² , in particular more than 60 N / mm ² at at least some of the locations using the solid as building material and / or at locations exposed to chemically aggressive conditions and / or in places to be built or repaired in the presence of water,

and / or in particular as a matrix former in a solid body provided with aggregates according to claim 8, which is used as a building material for the aforementioned building structure.

11. Use of the solid body according to one of claims 1 to 8 as a ceramic element, in particular as a sanitary ceramic element and / or as a body suitable for withstanding temperatures above 700 ° C, preferably above 1000 ° C, particularly preferably above half of 1500 ° C .

12. Use of the solid body according to one of claims 1 to 8 as a coating, in particular as a corrosion protection coating for metals and / or as a coating for water-bearing structures, in particular for sewer pipes and / or surfaces in sewage treatment plants in contact with sewage to be clarified.

13. A method for producing a molded body according to claim 8, comprising bringing a silicon tetrahedron source into contact, in particular water glass, sodium and / or potassium hydroxide, calcium aluminate, one or more additives and, optionally, additional water.

14. The method according to the preceding claim, characterized in that sodium or potassium hydroxide is used as the aqueous solution.

15. The method according to any one of the preceding claims, characterized in that such amounts of water glass and calcium aluminate are used that in the solid body by an Si / Al ratio less than or equal to 1, in particular less than 1 and greater than 0.1, preferably less than 1 and greater than 0.105 and / or preferably as determined according to claim 5, lead.

16. The method according to any one of the preceding claims, characterized in that sea or salt water is added.

17. The method according to any one of the preceding claims, characterized in that it without cooling measures at ambient temperatures above 30 ° C, in particular above 35 ° C or without heating measures at temperatures below + 5 ° C, especially below 0 ° C.

18. The method according to any one of the preceding claims, characterized in that silanes which carry organic groups are used exclusively or added to whoever, in particular in a proportion of 0.2-5% by weight of the binder or matrix former.

19. A method for producing a shaped body, in particular a wooden board, comprising bringing a silicon tetrahedron source into contact, in particular water glass, sodium and / or potassium hydroxide, calcium aluminate, optionally additionally water and / or additives, furthermore wood, in particular sawdust, wood flour, Wood chips and / or recycled wood is added.