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Physical Processes

Q: What are the main types or variations of Physical Processes?

Physical Processes encompass a wide range of fundamental mechanisms and phenomena, including mechanics, thermodynamics, electromagnetism, optics, acoustics, and more. These different types of Physical Processes cover the fundamental laws and principles that govern the movement, interaction, and conversion of physical quantities like force, energy, and information. Understanding the various manifestations of Physical Processes is crucial for advancing fields such as engineering, materials science, physics, and applied mathematics.

Q: How can Physical Processes research lead to practical applications?

By studying Physical Processes at a deep level, scientists can design more efficient technologies, explain natural phenomena, and push the boundaries of human knowledge. For example, a better understanding of thermodynamics can lead to the development of more energy-efficient systems, while advancements in optics and electromagnetics can enable the creation of novel communication and information technologies. Ultimately, the insights gained from Physical Processes research can have a transformative impact on a wide range of industries and fields.

Q: What are some common challenges researchers face when studying Physical Processes?

One of the key challenges in Physical Processes research is ensuring the reproducibility and accuracy of experiments and protocols. With the vast amount of literature, preprints, and patents available, it can be difficult for researchers to idenfity the most effective and reliable protocols for their specific research goals. This is where PubCompare.ai can be invaluable. The platfom's AI-driven analysis can help researchers quickly screen protocol literature, pinpoint critical insights, and choose the best options for their work, enhancing the reproducibility and accuracy of their Physical Processes research.

Q: How can PubCompare.ai assist researchers in optimizing their Physical Processes research?

PubCompare.ai's leading platform can help optimize research protocols in the critical domain of Physical Processes. The platform allows researchers to screen protocol literature more efficiently and leverage AI to pinpoint critical insights. By identifying the most effective protocols related to Physical Processes for a researcher's specific goals, PubCompare.ai can enable them to choose the best option for enhancing reproducibility and accuracy. The platform's AI-driven analysis can highlight key differences in protocol effectiveness, empowering researchers to make informed decisions that drive their work forward.

Physical Processes are the fundamental mechanisms and phenomena that underlie the behavior and transformations of matter and energy in the physical world.
This broad category encompasses a wide range of topics, including mechanics, thermodynamics, electromagnetism, optics, acoustics, and more.
Researchers studying Physical Processes may investigate the laws and principles that govern the movement, interaction, and conversion of physical quantities like force, energy, and information.
Thier work can lead to advancements in fields such as engineering, materials science, physics, and applied mathematics.
By understanding Physical Processes at a deep level, scientists can design more efficient technologies, explain natural phenomena, and push the boundaries of human knowledge.
PubCompare.ai's leading platform can help optimoze research protocols in this critical domain, enhancing reproducibility and accuracy through AI-driven comparisons of the latest literature, preprints, and patents.

Most cited protocols related to «Physical Processes»

Biochemical Variation Analysis in Protein Sequences

GV and GD calculations in the Align-GVGD program (21 ) are an extension of the Grantham Difference, which takes into account the composition (C), polarity (P) and volume (V) of amino acids (18 (link)). Conceptually, each amino acid can be plotted on a 3D graph, having C, P, V as the three axes, with different weights (18 (link)) applied to each axis. All amino acids at a given position in the MSA then form a cloud of points when plotted. This cloud of points can be enclosed within a box, the coordinates of which are defined by the minimum and maximum values of C, P, V, for the observed amino acids. GV is computed as the Euclidian length of the main diagonal of the box. GV is thus a measure of the amount of observed biochemical variation in a particular position in the alignment. Next, the GD is calculated by plotting a given mutation on the composition-polarity-volume graph, and measuring the Euclidian distance between that mutation and the closest point on the GV box. If the substitution lies within the box, then GD = 0. Otherwise, GD is greater than 0. GD is thus a measure of the biochemical difference between the mutant and the observed variation at that position according to the MSA.
The freely available web-based tool SIFT () (13 (link)) was used with default settings and the MSA obtained by 3D-Coffee as input. SIFT calculates the probabilities of having an amino acid at a specific position relative to the most frequent amino acid at that position. A cutoff for these probabilities is used to classify the mutations as tolerated and non-tolerated.
Mutants were classified according to Dayhoff's substitution matrix. The Dayhoff matrix highlights groups of amino acids with common chemical and physical properties. The following groups derived from the log odds ratio of the 250 PAM matrix were used (22 ): (V,L,I,M), (R,K,H), (D,E,N,Q), (F,Y,W), (C), (A,S,T,G,P). When the mutant and wild-type amino acid fall within a group, the mutation is considered conservative, if they fall into different groups, the mutation is classified as non-conservative.

Mathe E., Olivier M., Kato S., Ishioka C., Hainaut P, & Tavtigian S.V. (2006). Computational approaches for predicting the biological effect of p53 missense mutations: a comparison of three sequence analysis based methods. Nucleic Acids Research, 34(5), 1317-1325.

Publication 2006

Amino Acids Coffee Epistropheus Mutation Physical Processes

FLASHE Study: Recruiting Diverse Participants

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Publication 2017

Adolescent Diet Dietary Supplements Eligibility Determination Ethnicity Females Households Males Malignant Neoplasms Parent Physical Processes Preventive Health Services

DRIM: Exhaustive Motif Identification

The software tool DRIM implements the mHG framework for motif identification in ranked DNA sequences. A flow chart of DRIM is provided in Figure 1. In the rest of this section we describe the details of this implementation.
Exhaustive search of the restricted motif space. Ideally we would like to exhaustively search through the space of all biologically viable motifs and identify those that are significantly enriched at the top of the ranked list. However, this is infeasible in terms of running time (the space of viable TF binding sites includes motifs of size up to 20, i.e., 15²⁰ k-mers). We therefore resort to a simple strategy where the motif search is broken into two stages: first an exhaustive search on a restricted motif space is performed. The “motif seeds” that are identified in the preliminary search are used as a starting point for a heuristic search of larger motifs in the entire motif space. The restricted motif space S used in this study is the union of two subspaces S₁ and S₂: S₁ = {A,C,G,T,R,W,Y,S,N}⁷, where the IUPAC degenerate symbols (i.e., R,Y,W,S,N) are restricted to a maximum degeneracy of 2 and S₂ = {A,C,G,T}³N³⁻²⁵{A,C,G,T}³. The rationale behind the usage of the restricted IUPAC alphabet in S₁ instead of the complete 15 symbol alphabet stems from DNA–TF physical interaction properties and TFBS database statistics as explained in previous work [53 (link)]. S₂ captures motifs that contain a fixed gap (different motifs can have different gap sizes), which is characteristic of some TFs such as Zinc fingers).
mHG enrichment. For each of the motifs in S, we generate a ranked occurrence vector and compute the enrichment in terms of the multidimensional mHG. Due to running time considerations, we restrict the multidimensional mHG to three dimensions. This means that the model assumes each intergenic region contains either 0, 1, or ≥2 copies of a motif. To test whether this assumption is reasonable in the case of true TFBS motifs, we examined the occurrence distribution of TFBS motifs that were experimentally verified in S. cerevisiae (see Figure 9). It can be seen that the assumption holds for the five TFs that were tested since the majority of all intergenic regions contained either zero, one, or two copies of the TFBS. At the end of this stage, only motif seeds with mHG score <10⁻³ are kept. Similar motifs are filtered (as explained in Texts S5 and S6), and the remaining motif seeds are fed into the heuristic search module for expansion, Figure 1iii–1iv.
Motif expansion by heuristic search. The filtered motif seeds are used as starting points for identifying larger motifs that do not reside in the restricted motif space. This is done through an iterative heuristic process that employs simulated annealing. The objective function is to minimize the motif mHG p-value. We tested two different strategies for determining valid moves in the motif space. In the first, we defined a transition from motif M1 to M2 as valid if M1 and M2 are within a predefined Hamming distance D, with all valid moves being equiprobable. Additional bases can also be added to the motif flanks, thus enabling motif expansion. Note that the mHG adaptive cutoff is recalculated at each step. In the second strategy, all the motif occurrences in the target set that are within Hamming distance D are aligned. A consensus motif above IUPAC is extracted and the algorithm attempts a transition to that motif. While the second strategy converges much faster than the first, it is also more prone to converge to local minima (in the final application we use the second strategy with D = 1). At the end of the process, the exact p-value of each of the expanded motifs is computed. To correct for multiple motif testing, the p-value is then multiplied by the motif space size. Only motifs with corrected p-value <10⁻³ are reported.
Optimizations and running time. The DRIM application was implemented in C++. A “blind search” requires ∼100,000 motifs to be checked for enrichment in each run. It is therefore paramount to optimize the above-described procedures to enable a feasible running time. There are two bottlenecks in terms of running time: the motif occurrence vector generation and the mHG computation. We developed several optimization schemes to improve both. In the final configuration, the running time on a list of 6,000 sequences with an average size of 480 bases took ∼3 minutes on a Pentium IV, 2 GHz.

Eden E., Lipson D., Yogev S, & Yakhini Z. (2007). Discovering Motifs in Ranked Lists of DNA Sequences. PLoS Computational Biology, 3(3), e39.

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Publication 2007

Acclimatization Binding Sites Cloning Vectors GPER protein, human Intergenic Region Physical Processes Plant Embryos Stem, Plant Vision Visually Impaired Persons Zinc Fingers

Neonatal Porcine Skin and Skin Simulants for Microneedle Penetration Assessment

Full thickness neonatal porcine skin can be considered a good model for human skin in terms of hair sparseness and physical properties (Meyer, 1996 (link)). It was obtained from stillborn piglets and excised <24.0 h after birth. Full thickness skin (≈0.5 mm) was then stored in aluminium foil at −20.0 °C until further use. Two sections of skin were placed together, with the dermal side contacting each other, such that the stratum corneum surface was exposed at either side, giving a total skin thickness of about 1 mm. This was then utilised for the OCT assessment of MN penetration.
As an alternative to neonatal porcine skin, Parafilm M^® (PF) film and a needle testing polyurethane film were used as skin simulants. A sheet of Parafilm was folded to get an eight-layer film (≈1 mm thickness) and a poly(urethane) needle testing film (Deka^®) was used as received (0.4 mm thickness). The skin/Parafilm^® was then placed onto a sheet of expanded poly(ethylene) for support.
Two insertion methods were carried out: manual and Texture Analyser insertion. For manual insertion, different volunteers were recruited to apply the MN arrays following the same instructions as in the force measurement experiment. The Texture Analyser insertion was performed using a TA.XTPlus Texture Analyser (Stable Micro Systems, Surrey, UK) in compression mode. MN arrays were placed on the surface of the skin/artificial membrane and sticky tape (Office Depot, Boca Raton, USA) was carefully applied on the upper surface without applying force (Fig. 1D). The probe was lowered onto the skin/artificial membrane at a speed of 0.5 mm s⁻¹ until the required force was exerted. Forces were held for 30 s and varied from 10 N to 50 N per array. Once the target force was reached, the probe was moved upwards at a speed of 0.5 mm s⁻¹.

Larrañeta E., Moore J., Vicente-Pérez E.M., González-Vázquez P., Lutton R., Woolfson A.D, & Donnelly R.F. (2014). A proposed model membrane and test method for microneedle insertion studies. International Journal of Pharmaceutics, 472(1-2), 65-73.

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Publication 2014

Aluminum ARID1A protein, human Birth Brown Oculocutaneous Albinism Hair Homo sapiens Infant, Newborn Membranes, Artificial Needles Physical Processes Pigs Poly A Polyethylenes Polyurethanes Skin Skin, Artificial Tissue, Membrane Urethane Voluntary Workers

Longitudinal Modeling of Infant Cortical Growth

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Publication 2013

Brain Cortex, Cerebral Hybrids Infant Kidney Cortex Physical Processes White Matter

Most recents protocols related to «Physical Processes»

Engineered Alginate Production in P. aeruginosa

Not available on PMC !

Example 2

PAO1, the parent strain of PGN5, is a wild-type P. aeruginosa strain that produces relatively small amounts of alginate and exhibits a non-mucoid phenotype; thus, PGN5 is also non-mucoid when cultured (FIG. 3A). In PAO1, the alginate biosynthetic operon, which contains genes required for alginate production, is negatively regulated. Activation of this operon leads to alginate production and a mucoid phenotype. For example, over-expression of mucE, an activator of the alginate biosynthetic pathway, induces a strong mucoid phenotype in the PAO1 strain (e.g., P. aeruginosa strain VE2; FIG. 3B). The plasmid pUCP20-pGm-mucE, which constitutively over-expresses MucE, was used to test whether the genetically-modified PGN5 strain could produce alginate. Indeed, the presence of this plasmid in PGN5 (PGN5+mucE) induced a mucoid phenotype (FIG. 3B). To measure the amount of alginate produced by PGN5+mucE on a cellular level, a standard carbazole assay was performed, which showed that the PGN5+mucE and VE2 (i.e., PAO1+mucE) strains produce comparable amounts of alginate (FIG. 3C; 80-120 g/L wet weight).

To examine whether the alginate produced by PGN5+mucE was similar in composition to alginate produced by VE2, HPLC was performed to compare the M and G content of alginate produced by each strain. The chromatograms obtained from alginate prepared from VE2 and PGN5+mucE were identical (FIG. 3D), and the M:G ratios were comparable to a commercial alginate control (data not shown). To confirm that the physical properties of VE2 and PGN5+mucE alginates were also similar, alginate gels were prepared from alginate produced by each strain and the viscosity and yield stress was measured. The viscosities of VE2 and PGN5+mucE alginate gels were comparable at 73.58 and 72.12 mPa, respectively (FIG. 3E). Similarly, the yield stress of VE2 and PGN5+mucE alginate gels were comparable at 47.34 and 47.16 Pa, respectively (FIG. 3G).

US11873477B2. Bacterial cultures and methods for production of alginate (2024-01-16). Marshall University Research Corporation [US]. Inventors: Hongwei D. Yu [US], Meagan E. Valentine [US], Richard M. Niles [US], Thomas Ryan Withers [US], Brandon D. Kirby [US].

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Patent 2024

Alginate Alginates Anabolism Biological Assay Biosynthetic Pathways carbazole Cells Gels Genes High-Performance Liquid Chromatographies Operon Parent Phenotype Physical Processes Plasmids Pseudomonas aeruginosa Strains Viscosity

Optimizing Secondary Battery Pouch Film Production

Not available on PMC !

Example 1

A secondary battery pouch film is produced, after the drying process temperature of the two-component type solvent-based emulsion having a start temperature of 175° C. to 190° C. is set to 100° C.

A secondary battery pouch film is produced, after the process temperature of the two-component type solvent-based emulsion having a start temperature lowered to 135° C. to 150° C. is set to 100° C.

Example 2

A secondary battery pouch film is produced, after the drying process temperature of the two-component type solvent-based emulsion having a start temperature of 175° C. to 190° C. is set to 120° C.

Example 3

A secondary battery pouch film is produced, after the drying process temperature of the two-component type solvent-based emulsion having a start temperature of 175° C. to 190° C. is set to 135° C.

Example 4

A secondary battery pouch film is produced, after the drying process temperature of the two-component type solvent-based emulsion having a start temperature of 175° C. to 190° C. is set to 150° C.

Example 5

A secondary battery pouch film is produced, after the drying process temperature of the two-component type solvent-based emulsion having a start temperature of 175° C. to 190° C. is set to 165° C.

Example 6

A secondary battery pouch film is produced, after the drying process temperature of the two-component type solvent-based emulsion having a start temperature of 175° C. to 190° C. is set to 180° C.

Example 7

A secondary battery pouch film is produced, after the drying process temperature of the two-component type solvent-based emulsion having a start temperature of 175° C. to 190° C. is set to 200° C.

Example 8

Example 9

Example 10

TABLE 1

Start Drying process

No.temperature (° C.)temperature (° C.)

Comparative Example 1175~190100

Comparative Example 2120

Comparative Example 3135

Comparative Example 4150

Comparative Example 5165

Comparative Example 6180

Comparative Example 7200

Example 1135~150100

Example 2120

Example 3135

Example 4150

Comparative Example 8165

Comparative Example 9180

Comparative Example 10200

Evaluation of Properties

Evaluation of Initial Peel Strength

- (1) An experimental sample is prepared by cutting the secondary battery pouch film to have a size of 1.5 cm by 15 cm in width and length, respectively.
- (2) The metal layer and the sealant layer are peeled off, and the peel strength is measured.

Evaluation of Hydrofluoric Acid Resistance

- (1) After the secondary battery pouch film is cut to have a size of 10 cm by 20 cm, two surfaces on both sides thermally adhered to each other.
- (2) A manufacturing solution (electrolyte+water (10,000 ppm (about 1%) of concentration of water in the solution)) is put inside the secondary battery pouch having the two surfaces adhering to each other, thermal adhering is performed, and a pack is manufactured.
- (3) The pack is stored at a high-temperature condition (85° C.) for 24 hours.
- (4) The electrolyte inside the pack is removed, and the sample is prepared (width 1.5 cm and length 15 cm) in the same manner as in the evaluation of initial peel strength.
- (5) The peel strength between the metal layer and the sealant layer is measured.

Evaluation of Electrolyte Resistance

- (1) An experimental sample is prepared by cutting the secondary battery pouch film to have a size of 1.5 cm by 15 cm in width and length, respectively.
- (2) The prepared sample is impregnated with a standard electrolyte (1.0 M LiPF6(EC/DEC/EMC: 1/1/1)) and is stored at a high temperature condition (85° C.) for 24 hours.
- (3) After the electrolyte is washed off, the metal layer and the sealant layer are peeled off, and the peel strength is measured.

Evaluation of Formability

- (1) A sample is prepared by cutting the produced secondary battery pouch film to have a size of 15 cm by 15 cm.
- (2) The prepared samples are formed by using a test die (size of 3 cm×4 cm) manufactured by Youlchon Chemical, Co., Ltd.
- (3) Evaluation of formability is repeatedly performed by changing the setting of the forming depth and is performed until ten or more samples are not broken.
- (4) A forming depth, in ten or more samples are not broken, is measured.

Evaluation of Penetration Strength

- (1) A sample having a width of 35 mm and a length of 600 mm is produced from the secondary battery pouch film.
- (2) The penetration strength is measured at intervals of about 40 mm in a direction from the outer layer toward the inner layer.
- (3) After the strength is measured ten times, an average value thereof is recorded.

In this case, the higher the formability, a forming process range may be wider during manufacturing of a battery. It is appropriate that the electrolyte resistance strength is equal to or higher than 90% of the initial peel strength, and the hydrofluoric acid resistance strength should be equal to or higher than 5 N/15 mm. Since the electrolyte resistance strength and the hydrofluoric acid resistance strength are much affected by the initial peel strength, it is appropriate that the initial peel strength is equal to or higher than 14 N/15 mm.

Table 2 shows evaluation of physical properties based on the curing start temperature and the drying process temperature.

TABLE 2

Hydrofluoric

DryingInitialElectrolyteacid

StartprocesspeelresistanceresistancePenetration

temperaturetemperaturestrengthstrengthstrengthstrengthFormability

No.(° C.)(° C.)(N/15 mm)(N/15 mm)(N/15 mm)(N)(mm)

Comparative1751002PeelingPeeling18.46.5

Example 1~190

Comparative1202.3PeelingPeeling19.26.6

Example 2

Comparative1352.2PeelingPeeling19.36.6

Example 3

Comparative1506.4PeelingPeeling19.36.5

Example 4

Comparative16514.514.15.824.26.3

Example 5

Comparative18014.814.35.724.66.1

Example 6

Comparative20015.614.85.824.56.1

Example 7

Example 11351009.2 8.13.919.46.8

Example 2~15012012.411.64.320.26.7

Example 313514.614.26.221.86.7

Example 415015.014.36.422.36.8

Comparative16515.114.86.423.86.3

Example 8

Comparative18015.715.16.224.26.1

Example 9

Comparative20016.115.46.524.76.0

Example 10

As known from the above, when an emulsion having a start temperature of 175° C. to 190° C. (Comparative Examples 1, 2, 3, and 4) is applied, the initial peel strength is relatively very low to be 10 N or lower when the drying process temperature is 150° C. or lower. The low initial peel strength resulted in a phenomenon where the sealant layer and the metal layer are completely separated from each other during evaluation of the electrolyte resistance strength and the hydrofluoric acid resistance strength.

When the drying process temperature is 165° C. to 200° C. (Comparative Examples 5, 6, and 7), the initial peel strength, the electrolyte resistance strength, and the hydrofluoric acid resistance strength are all good. However, the penetration strength increased to 24 N or higher. As well, a result that the formability does not reach 6.5 mm is obtained.

When the emulsion having a start temperature lowered to 135° C. to 150° C. is applied, the initial peel strength is 10 N/15 mm or lower only when the drying process temperature is 100° C. (Example 1), and the initial peel strength is 12 N/15 mm or higher in a drying process condition of 120° C. or higher (Examples and Comparative Examples 8 to 10). It is confirmed that a decrease in start temperature improves the adhesiveness even at a low drying process temperature.

However, the hydrofluoric acid resistance strength does not reach 5 N/15 mm in the 120° C. condition (Example 2), and the initial peel strength, the electrolyte resistance strength, and the hydrofluoric acid resistance strength are all good in conditions of 135° C. or higher (Examples 3 and 4 and Comparative Examples 8 to 10).

Similar to Comparative Examples 1 to 7, results of an increase in penetration strength in a condition of 165° C. to 200° C. (Comparative Examples 8, 9, 10) and the result of formability smaller than 6.5 mm is obtained.

The penetration strength increased to 20 N or higher at a condition of 135° C. to 150° C. (Examples 3 and 4), but has the best of the formability of 6.5 mm or more.

Therefore, only in a drying process temperature condition corresponding to the start temperature, all the properties of the initial peel strength, the electrolyte resistance strength, the hydrofluoric acid resistance strength are appropriate. When the drying process temperature is above 150° C., and particularly 165° C. or higher as found in an experiment, the penetration strength of the secondary battery pouch film significantly increases, and thus the formability decreases.

Therefore, in order to appropriately obtain all the physical properties, it is preferable to lower the drying process temperature to 150° C. or below, and to this end, it is preferable to lower the start temperature of the solvent-based emulsion to 150° C. or below.

According to the exemplary embodiments of the invention, when the secondary battery pouch film is manufactured, the primer layer composition that is interposed between the metal layer and the melt-extrusion resin layer or the sealant layer is made of a two-component curing-type organic solvent-based emulsion composition containing acid-modified polypropylene and a curing agent, wherein the curing start temperature and the drying process temperature are adjusted, and thermal lamination is not performed. Thereby, good formability, as well as good initial peel strength, hydrofluoric acid resistance, electrolyte resistance, etc. may be achieved.

The present invention was made under Project ID 20007148 from the Ministry of Trade, Industry and Energy, Korea Evaluation Institute of Industrial Technology under research project “Development of Technology of Materials and Components—Materials and Components Packaging Type”, research title “Performance Evaluation of Medium and Large Size Secondary Battery Pouch and Empirical Research for Application to Demand Companies” granted to Youl Chon Chemical Co., Ltd. For the period 2019 Sep. 1-2021 Feb. 28.

While the present invention has been described with respect to the specific embodiments, it will be apparent to those skilled in the art that various changes and modifications may be made without departing from the spirit and scope of the invention as defined in the following claims.

US11876235B2. Primer layer composition, secondary battery pouch film using the same, and method of manufacturing the same (2024-01-16). Youlchon Chemical Co., Ltd. [KR]. Inventors: Nok Jung Song [KR], Han Chul Park [KR], Hee Sik Han [KR], Ji Min Lee [KR].

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Patent 2024

Acids Adhesiveness Cold Temperature Electrolytes Emulsions Fever Hydrofluoric acid Metals Oligonucleotide Primers Physical Processes Polypropylenes Resins, Plant Solvents Technology Assessment

Synthesis and Characterization of Mn4C Magnetic Material

Not available on PMC !

Example 1

95 g of manganese (purity: 99.95%; purchased from Taewon Scientific Co., Ltd.) and 5 g of high-purity graphite (purity: 99.5%; purchased from Taewon Scientific Co., Ltd.) were placed in a water-cooled copper crucible of an argon plasma arc melting apparatus (manufactured by Labold AG, Germany, Model: vacuum arc melting furnace Model LK6/45), and melted at 2,000 K under an argon atmosphere. The melt was cooled to room temperature at a cooling rate of 10⁴K/min to obtain an alloy ingot. The alloy ingot was crushed to a particle size of 1 mm or less by hand grinding. Thereafter, the obtained powders were magnetically separated using a Nd-based magnet to remove impurities repeatedly, and the Mn₄C magnetic powders were collected. The collected Mn₄C magnetic powders were subjected to X-ray diffraction (XRD) analysis (measurement system: D/MAX-2500 V/PO, Rigaku; measurement condition: Cu—K_α ray) and energy-dispersive X-ray spectroscopy (EDS) using FE-SEM (Field Emission Scanning Electron Microscope, MIRA3 LM).

FIGS. 2(a) and 2 (b) show an X-ray diffraction pattern and an energy-dispersive X-ray spectroscopy graph of the Mn₄C magnetic material produced according to Example 1 of the present disclosure, respectively.

As can be seen in FIG. 2(a), the Mn₄C magnetic material showed diffraction peaks of (111), (200), (220), (311) and (222) crystal planes at 2θ values of 40°, 48°, 69°, 82° and 88°, respectively, in the XRD analysis. Thus, it can be seen that the XRD patterns of the Mn₄C magnetic material produced according to Example 1 are well consistent with the patterns of the cubic perovskite Mn₄C. In addition, the Mn₄C magnetic material shows several very weak diffraction peaks that can correspond to Mn₂₃C₆and Mn. That is, the diffraction peak intensity at 2θ values of 43° and 44°, which correspond to Mn and Mn₂₃C₆impurities, is as very low as about 2.5% of the diffraction intensity of the peak corresponding to the (111) plane. Through this, it can be seen that the powders obtained in Example 1 have high-purity Mn₄C phase. The lattice parameter of the Mn₄C is estimated to be about 3.8682 Å.

FIG. 2(b) shows the results of analyzing the atomic ratio of Mn:C in the powder by EDS. The atomic ratio of Mn:C is 80.62:19.38, which is very close to 4:1 within the experimental uncertainties. Thus, it can be seen that the powder is also confirmed to be Mn₄C.

The M-T curve of the field aligned Mn₄C powder obtained in Example 1 was measured under an applied field of 4 T and at a temperature ranging from 50 K to 400 K. Meanwhile, the M-T curve of the randomly oriented Mn₄C powder was measured under an applied field of 1 T. The Curie temperature of Mn₄C was measured under 10 mT while decreasing temperature from 930 K at a rate of 20 K/min.

FIGS. 3(a) to 3(c) show the M-T curves of the Mn₄C magnetic material, produced according to Example 1 of the present disclosure, under magnetic fields of 4 T, 1 T, and 10 mT, respectively.

FIG. 3 shows magnetization-temperature (M-T) curves indicating the results of measuring the temperature-dependent magnetization intensity of the Mn₄C magnetic material, produced in Example 1, using the vibrating sample magnetometer (VSM) mode of Physical Property Measurement System (PPMS®) (Quantum Design Inc.).

According to the Néel theory, the ferrimagnets that contain nonequivalent substructures of magnetic ions may have a number of unusual forms of M-T curves below the Curie temperature, depending on the distribution of magnetic ions between the substructures and on the relative value of the molecular field coefficients. The anomalous M-T curves of Mn₄C, as shown in FIG. 3(a), can be explained to some extent by the Néel's P-type ferrimagnetism, which appears when the sublattice with smaller moment is thermally disturbed more easily. For Mn₄C with two sublattices of Mn_Iand Mn_II, as shown in FIG. 1, the Mn_Isublattice might have smaller moment.

FIG. 3(a) shows the temperature dependence of magnetization of the Mn₄C magnetic material produced in Example 1. The magnetization of Mn₄C measured at 4.2K is 6.22 Am²/kg (4 T), corresponding to 0.258μ_Bper unit cell. The magnetization of the Mn₄C magnetic material varies little at temperatures below 50 K, and is quite different from that of most magnetic materials, which undergo a magnetization deterioration with increasing temperature due to thermal agitation. Furthermore, the magnetization of the Mn₄C magnetic material increases linearly with increasing temperature at temperatures above 50 K. The linear fitting of the magnetization of Mn₄C at 4 T within the temperature range of 100 K to 400 K can be written as M=0.0072T+5.6788, where M and T are expressed in Am²/kg and K, respectively. Thus, the temperature coefficient of magnetization of Mn₄C is estimated to be about ˜2.99*10⁻⁴μ_B/K per unit cell. The mechanisms of the anomalous thermomagnetic behaviors of Mn₄C may be related to the magnetization competition of the two ferromagnetic sublattices (Mn_Iand Mn_II) as shown in FIG. 1.

FIG. 3(b) shows the M-T curves of the Mn₄C powders at temperatures within the range of 300 K to 930 K under 1 T. The linear magnetization increment stops at 590 K, above which the magnetization of Mn₄C starts to decrease slowly first and then sharply at a temperature of about 860 K. The slow magnetization decrement at temperatures above 590 K is ascribed to the decomposition of Mn₄C, which is proved by further heat-treatment of Mn₄C as described below.

According to one embodiment of the present disclosure, the saturation magnetization of Mn₄C increases linearly with increasing temperature within the range of 50 K to 590 K and remains stable at temperatures below 50 K. The increases in anomalous magnetization of Mn₄C with increasing temperature can be considered in terms of the Néel's P-type ferrimagnetism. At temperatures above 590 K, the Mn₄C decomposes into Mn₂₃C₆and Mn, which are partially oxidized into the manganosite when exposed to air. The remanent magnetization of Mn₄C varies little with temperature. The Curie temperature of Mn₄C is about 870 K. The positive temperature coefficient (about 0.0072 Am²/kgK) of magnetization in Mn₄C is potentially important in controlling the thermodynamics of magnetization in magnetic materials.

The Curie temperature T_eof Mn₄C is measured to be about 870 K, as shown in FIG. 3(c). Therefore, the sharp magnetization decrement of Mn₄C at temperatures above 860 K is ascribed to both the decomposition of Mn₄C and the temperature near the Tc of Mn₄C.

FIG. 4 is a graph showing the magnetic hysteresis loops of the Mn₄C magnetic material, produced according to Example 1 of the present disclosure, at 4.2 K, 200 K and 400 K. The magnetic hysteresis loops were measured by using the PPMS system (Quantum Design) under a magnetic field of 7 T while the temperature was changed from 4 K to 400 K.

As shown in FIG. 4, the positive temperature coefficient of magnetization was further proved by the magnetic hysteresis loops of Mn₄C as shown in FIG. 4. The Mn₄C shows a much higher magnetization at 400 K than that at 4.2 K. Moreover, the remanent magnetization of Mn₄C varies little with temperature and is Δ3.5 Am²/kg within the temperature range of 4.2 K to 400 K. The constant remanent magnetization of Mn₄C within a wide temperature range indicates the high stability of magnetization against thermal agitation. The coercivities of Mn₄C at 4.2 K, 200 K, and 400 K were 75 mT, 43 mT, and 33 mT, respectively.

The magnetic properties of Mn₄C measured are different from the previous theoretical results. A corner Mn_Imoment of 3.85μ_Bantiparallel to three face-centered Mn_IImoments of 1.23μ_Bin Mn₄C was expected at 77 K. The net moment per unit cell was estimated to be 0.16μ_B. In the above experiment, the net moment in pure Mn₄C at 77 K is 0.26μ_B/unit cell, which is much larger than that expected by Takei et al. It was reported that the total magnetic moment of Mn₄C was calculated to be about 1μ_B, which is almost four times larger than the 0.258μ_Bper unit cell measured at 4.2 K, as shown in FIG. 4.

FIG. 5 is an enlarged view of the temperature-dependent XRD patterns of the Mn₄C magnetic material produced according to Example 1 of the present disclosure.

The thermomagnetic behaviors of Mn₄C are related to the variation in the lattice parameters of Mn₄C with temperature. It is known that the distance of near-neighbor manganese atoms plays an important role in the antiferro- or ferro-magnetic configurations of Mn atoms. Ferromagnetic coupling of Mn atoms is possible only when the Mn—Mn distance is large enough. FIG. 5 shows the diffraction peaks of the (111) and (200) planes of Mn₄C at temperatures from 16 K to 300 K. With increasing temperature, both (111) and (200) peaks of Mn₄C shifted to a lower degree at temperatures between 50 K and 300 K, indicating an enlarged distance of Mn—Mn atoms in Mn₄C. No peak shift is obviously observed for Mn₄C at temperatures below 50 K. The distance of nearest-neighbor manganese atoms plays an important role in the antiferro- or ferro-magnetic configurations of Mn atoms and thus has a large effect on the magnetic properties of the compounds.

Thus, it can be seen that the abnormal increase in magnetization of Mn₄C with increasing temperature occurs due to the variation in the lattice parameters of Mn₄C with temperature.

The powder produced in Example 1 was annealed in vacuum for 1 hour at each of 700 K and 923 K, and then subjected to X-ray spectroscopy, and the results thereof are shown in FIG. 6.

The magnetization reduction of Mn₄C at temperatures above 590 K is ascribed to the decomposition of Mn₄C, which is proved by the XRD patterns of the powders after annealing Mn₄C at elevated temperatures. FIG. 6 shows the structural evolution of Mn₄C at elevated temperatures. When Mn₄C is annealed at 700 K, a small fraction of Mn₄C decomposes into a small amount of Mn₂₃C₆and Mn. The presence of manganosite is ascribed to the spontaneous oxidation of the Mn precipitated from Mn₄C when exposed to air after annealing. The fraction of Mn₂₃C₆was enhanced significantly for Mn₄C annealed at 923 K, as shown in FIG. 6.

These results prove that the metastable Mn₄C decomposes into stable Mn₂₃C₆at temperatures above 590 K. The presence of Mn₄C in the powder annealed at 923 K indicates a limited decomposition rate of Mn₄C, from which the Tc of Mn₄C can be measured. Both Mn₂₃C₆and Mn are weak paramagnets at ambient temperature and elevated temperatures. Therefore, the magnetic transition of the Mn₄C magnetic material at 870 K is ascribed to the Curie point of the ferrimagnetic Mn₄C.

The Mn₄C shows a constant magnetization of 0.258μ_Bper unit cell below 50 K and a linear increment of magnetization with increasing temperature within the range of 50 K to 590 K, above which Mn₂₃C₆precipitates from Mn₄C. The anomalous M-T curves of Mn₄C can be considered in terms of the Néel's P-type ferrimagnetism.

US11858820B2. Mn₄C manganese carbide magnetic substance and manufacturing method therefor (2024-01-02). KOREA INSTITUTE OF MATERIALS SCIENCE [KR]. Inventors: Chul Jin Choi [KR], Ping Zhan Si [CN], Ji Hoon Park [KR], Hui Dong Qian [CN].

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Patent 2024

Alloys Argon Atmosphere Biological Evolution Cells Copper Cuboid Bone Debility Energy Dispersive X Ray Spectroscopy Face Fever fluoromethyl 2,2-difluoro-1-(trifluoromethyl)vinyl ether Graphite Ions Magnetic Fields Manganese perovskite Physical Processes Plasma Powder Radiography Scanning Electron Microscopy Spectrum Analysis Vacuum Vision X-Ray Diffraction

Synthesis and Surface Modification of Hydrotalcite Particles

Not available on PMC !

Example 1

In a 2 L stainless steel container, 730 g of aluminum hydroxide powder (commercially available from KANTO CHEMICAL CO., INC., Cica special grade) were added into 1110 mL of 48% sodium hydroxide solution (commercially available from KANTO CHEMICAL CO., INC., Cica special grade), and they were stirred at 124° C. for 1 hour to give a sodium aluminate solution (First Step).

After the sodium aluminate solution was cooled to 80° C., ion exchange water was added into the sodium aluminate solution to achieve a total amount of 1500 mL.

After 96 mL of the sodium aluminate solution were separated into a 1 L stainless steel container, pure water was added into the solution to achieve a total amount of 730 mL (concentration of the sodium aluminate solution: 0.8 mol/L). The solution was stirred with keeping a temperature thereof at 25° C., and the solution was aerated with carbon dioxide in an aeration amount of 0.7 L/min. for 60 minutes to give adjusted aluminum hydroxide slurry (low-crystallinity aluminum compound=pseudo-boehmite) (Second Step).

Separately, 49.5 g of magnesium oxide powder (commercially available from KANTO CHEMICAL CO., INC., special grade) were added to 327 mL of pure water, and they were stirred for 1 hour to give magnesium oxide slurry.

In a 1.5 L stainless steel container, the magnesium oxide slurry and the adjusted aluminum hydroxide slurry were added into 257 mL of pure water, and they were stirred at 55° C. for 90 minutes to cause a first-order reaction. As a result, a reactant containing hydrotalcite nuclear particles was prepared (Third Step).

Then, pure water was added to the reactant to give a solution in a total amount of 1 L. The solution was put into a 2 L autoclave, and a hydrothermal synthesis was performed at 160° C. for 7 hours. As a result, hydrotalcite particles slurry was synthesized (Fourth Step).

To the hydrotalcite particles slurry were added 4.3 g of stearic acid (3 parts by mass with respect to 100 parts by mass of hydrotalcite particles) with keeping a temperature of the hydrotalcite particles slurry at 95° C. to perform a surface treatment on particles (Fifth Step). After the hydrotalcite particles slurry of which particles were surface treated was filtered and washed, a drying treatment was performed at 100° C. to give solid products of hydrotalcite particles. The produced hydrotalcite particles were subjected to an elemental analysis, resulting in that Mg/Al (molar ratio)=2.1.

In accordance with a method of Example 1 described in Japanese Laid-Open Patent Publication No. 2003-048712, hydrotalcite particles were synthesized.

In 150 g/L of NaOH solution in an amount of 3 L were dissolved 90 g of metal aluminum to give a solution. After 399 g of MgO were added to the solution, 174 g of Na₂CO₃were added thereto and they were reacted with each other for 6 hours with stirring at 95° C. As a result, hydrotalcite particles slurry was synthesized.

To the hydrotalcite particles slurry were added 30 g of stearic acid (3 parts by mass with respect to 100 parts by mass of hydrotalcite particles) with keeping a temperature of the hydrotalcite particles slurry at 95° C. to perform a surface treatment on particles. After the hydrotalcite particles slurry of which particles were surface treated was cooled, filtered and washed to give solid matters, a drying treatment was performed on the solid matters at 100° C. to give solid products of hydrotalcite particles.

Example 2

After the sodium aluminate solution was cooled to 80° C., ion exchange water was added into the sodium aluminate solution to achieve a total amount of 1500 mL.

After 96 mL of the sodium aluminate solution were separated into a 1 L stainless steel container, pure water was added into the solution to achieve a total amount of 730 mL (concentration of the sodium aluminate solution: 0.8 mol/L). The solution was stirred with keeping a temperature thereof at 30° C., and the solution was aerated with carbon dioxide in an aeration amount of 0.7 L/min. for 90 minutes to give adjusted aluminum hydroxide slurry (low-crystallinity aluminum compound=pseudo-boehmite) (Second Step).

Solid products of hydrotalcite particles were produced in a same manner as in Comparative Example 1 except that reaction conditions of 95° C. and 6 hours for synthesis of the hydrotalcite particles slurry in Comparative Example 1 were changed to hydrothermal reaction conditions of 170° C. and 6 hours.

Example 3

After the sodium aluminate solution was cooled to 80° C., ion exchange water was added into the sodium aluminate solution to achieve a total amount of 1500 mL.

After 96 mL of the sodium aluminate solution were separated into a 1 L stainless steel container, pure water was added into the solution to achieve a total amount of 730 mL (concentration of the sodium aluminate solution: 0.8 mol/L). The solution was stirred with keeping a temperature thereof at 60° C., and the solution was aerated with carbon dioxide in an aeration amount of 0.7 L/min. for 60 minutes to give adjusted aluminum hydroxide slurry (low-crystallinity aluminum compound=pseudo-boehmite) (Second Step).

In accordance with a method of Example 1 described in Japanese Laid-Open Patent Publication No. 2013-103854, hydrotalcite particles were synthesized.

Into a 5 L container were added 447.3 g of magnesium hydroxide (d50=4.0 μm) and 299.2 g of aluminum hydroxide (d50=8.0 μm), and water was added thereto to achieve a total amount of 3 L. They were stirred for 10 minutes to prepare slurry. The slurry had physical properties of d50=10 μm and d90=75 μm. Then, the slurry was subjected to wet grinding for 18 minutes (residence time) by using Dinomill MULTILAB (wet grinding apparatus) with controlling a slurry temperature during grinding by using a cooling unit so as not to exceed 40° C. As a result, ground slurry had physical properties of d50=1.0 μm, d90=3.5 μm, and slurry viscosity=5000 cP. Then, sodium hydrogen carbonate was added to 2 L of the ground slurry such that an amount of the sodium hydrogen carbonate was ½ mole with respect to 1 mole of the magnesium hydroxide. Water was added thereto to achieve a total amount of 8 L, and they were stirred for 10 minutes to give slurry. Into an autoclave was put 3 L of the slurry, and a hydrothermal reaction was caused at 170° C. for 2 hours. As a result, hydrotalcite particles slurry was synthesized.

To the hydrotalcite particles slum were added 6.8 g of stearic acid (3 parts by mass with respect to 100 parts by mass of hydrotalcite particles) with keeping a temperature of the hydrotalcite particles slurry at 95° C. to perform a surface treatment on particles. After solids were filtered by filtration, the filtrated cake was washed with 9 L of ion exchange water at 35° C. The filtrated cake was further washed with 100 mL of ion exchange water, and a conductance of water used for washing was measured. As a result, the conductance of this water was 50 μS/sm (25° C.). The water-washed cake was dried at 100° C. for 24 hours and was ground to give solid products of hydrotalcite particles.

Example 5

After the sodium aluminate solution was cooled to 80° C., ion exchange water was added into the sodium aluminate solution to achieve a total amount of 1500 mL.

After 192 mL of the sodium aluminate solution were separated into a 1 L stainless steel container, pure water was added into the solution to achieve a total amount of 730 mL (concentration of the sodium aluminate solution: 1.6 mol/L). The solution was stirred with keeping a temperature thereof at 30° C., and the solution was aerated with carbon dioxide in an aeration amount of 0.7 L/min. for 90 minutes to give adjusted aluminum hydroxide slurry (low-crystallinity aluminum compound=pseudo-boehmite) (Second Step).

In accordance with a method of Example 1 described in Japanese Laid-Open Patent Publication No. H06-136179, hydrotalcite particles were synthesized.

To 1 L of water were added 39.17 g of sodium hydroxide and 11.16 g of sodium carbonate with stirring, and they were heated to 40° C. Then, to 500 mL of distilled water were added 61.28 g of magnesium chloride (19.7% as MgO), 37.33 g of aluminum chloride (20.5% as Al₂O₃), and 2.84 g of ammonium chloride (31.5% as NH₃) such that a molar ratio of Mg to Al, Mg/Al, was 2.0 and a molar ratio of NH₃to Al, NH₃/Al, was 0.35. As a result, an aqueous solution A was prepared. The aqueous solution A was gradually poured into a reaction system of the sodium hydroxide and the sodium carbonate. The reaction system after pouring had pH of 10.2. Moreover, a reaction of the reaction system was caused at 90° C. for about 20 hours with stirring to give hydrotalcite particles slurry.

To the hydrotalcite particles slurry were added 1.1 g of stearic acid, and a surface treatment was performed on particles with stirring to give a reacted suspension. The reacted suspension was subjected to filtration and water washing, and then the reacted suspension was subjected to drying at 70° C. The dried suspension was ground by a compact sample mill to give solid products of hydrotalcite particles.

US11873230B2. Hydrotalcite particles, method for producing hydrotalcite particles, resin stabilizer containing hydrotalcite particles, and resin composition containing hydrotalcite particles (2024-01-16). TODA KOGYO CORP. [JP], SAKAI CHEMICAL INDUSTRY CO., LTD. [JP]. Inventors: Koji Kakuya [JP], Atsuko Yasunaga [JP], Nobukatsu Shigi [JP].

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Patent 2024

A-A-1 antibiotic Aluminum Aluminum Chloride aluminum oxide hydroxide Anabolism Bicarbonate, Sodium Carbon dioxide Chloride, Ammonium Filtration hydrotalcite Hydroxide, Aluminum Ion Exchange Japanese Magnesium Chloride Magnesium Hydroxide Molar Oxide, Magnesium Physical Processes Powder Resins, Plant sodium aluminate sodium carbonate Sodium Hydroxide Stainless Steel stearic acid Suby's G solution Viscosity

Viscosity Characterization of Ester Blends in API Group III Base Oil

Not available on PMC !

Example 2

All esters including the CO were blended at 1% by weight into a commercially available isoparaffinic API Group III base oil (NEXBASE 3043) and found to be readily soluble. The base oil technical data from the manufacturer has been provided in Table 2. Dynamic viscosity was characterized from 20-50° C. using an AR 2000 rheometer (TA Instruments) outfitted in a parallel plate (25 mm diameter) configuration at a constant shear rate of 120 s⁻¹and gap distance of 500 μm. Three replicates for each treatment were performed. Kinematic viscosity was then calculated from known densities, and results demonstrated similar values between all ester blends as seen in FIG. 2. FIG. 2 illustrates kinematic viscosity of various ester blends (1% by weight) as a function of temperature. It was thus determined that each lubricant's viscosity would not factor into their respective friction or wear performance. Rather, differences in tribological behavior would be solely dependent on chemical composition.

TABLE 2

Manufacturer reported physical properties for the base oil.

PropertyValueTest Method

Kinematic viscosity (mm²/s)ASTM D-445

40° C.20

100° C.4.3

Viscosity index122ASTM D-2270

Pour Point−18° C.ASTM D-97

Flash Point228° C.ASTM D-92

Density, at 15° C. (g/ml)0.837ASTM D-4052

US11866671B2. Base oil or lubricant additive (2024-01-09). Iowa State University Research Foundation, Inc. [US]. Inventors: George A. Kraus [US], Kyle Podolak [US], Derek Lee White [US], Sriram Sundararajan [US].

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Patent 2024

chemical composition Esters Friction Physical Processes Viscosity Vision

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