Claims:WE CLAIM:

1. A method of producing high strength structural steel sheet, the method comprising:
casting a steel slab with composition by weight: Carbon (C) 0.10-0.2%, Manganese (Mn) 0.8-1.6%, Silicon (Si) 0.25–0.5%, Chromium (Cr) 0.15-0.35%, Molybdenum (Mo) 0.05-0.25%, Copper (Cu): 0.1-0.3%, Titanium (Ti) 0.02-0.06%, Sulphur (S) 0.002-0.008%, Nickel (Ni) 0.1-0.25%, phosphorous (P) 0.015-0.025%, and nitrogen (N) 0.004-0.01%;
reheating the steel slab at a temperature ranging from 1100 °C to 1300 °C;
hot rolling the steel slab into a thin sheet in an austenite region with several passes at a finish rolling temperature below a threshold temperature (Tnr); and
cooling the hot rolled thin sheet at a rate of 10-70 °C/s up to a coiling temperature ranging from 430 °C to 500 °C.
2. The method as claimed in claim 1, comprising holding the steel slab for 2-4 hours at a temperature ranging from 1170 °C to 1220 °C.
3. The method as claimed in claim 1, wherein the finish rolling temperature ranges from 810°C to 860 °C.
4. A high strength structural steel sheet comprising:
yield strength ranging from 700 MPa to 800 MPa;
elongation of ranging from 14% to 18%; and
yield to tensile strength ratio ranging from 0.7 to 0.95.
5. The high strength structural steel sheet as claimed in claim 4, wherein the sheet has hardness is greater than 260 HV.
6. The high strength structural steel sheet as claimed in claim 4, wherein the sheet has a mixture of martensite and ferrite not more than 30-50% by weight.
7. The high strength structural steel sheet as claimed in claim 6, wherein the ferrite is less than 40% by weight.
8. The high strength structural steel sheet as claimed in claim 4, wherein the sheet has bainite which in microstructure is 50-70% by weight.
9. The high strength structural steel sheet as claimed in claim 8, wherein the bainite thickness is below a submicron level.
, Description:METHOD OF PRODUCING HIGH STRENGTH STRUCTURAL STEEL SHEET

TECHNICAL FIELD
[0001] The present disclosure, in general, relates to the field of Materials & metallurgy. The disclosure provides a viable economical method to prepare steel having an excellent combination of yield strength and ductility. Said method and the corresponding steel product having excellent mechanical properties is highly suitable for industrial applications, for instance, in load bearing components such as mobile cranes, booms, bridges including lifting & excavation where a combination of high yield strength and elongation is elongation is necessary.
[0002] In particular, the present disclosure related to a method of producing high strength structural steel sheet and a high strength structural steel sheet produced by the said method.

BACKGROUND
[0003] Background description includes information that may be useful in understanding the present invention. It is not an admission that any of the information provided herein is prior art or relevant to the presently claimed invention, or that any publication specifically or implicitly referenced is prior art.
[0004] Structural steels demand high load-bearing capacity and light weighting. For an example reduction in weight are one of the major objectives for mobile crane industries to reduce fuel consumption, light weight and easy handling. Another driver is maintaining a high standard of safety due to high strength. These can be achieved through the development of stronger, tougher and thinner steel
[0005] High yield strength is mainly used for structural applications for an example of mobile crane components, lifting excavation, bridge, shipbuilding, and many other applications. Steels for these applications required higher yield strength to ensure higher load bearing capability and thinner to save weight. The process and product should be economical, highly productive and simple processing. High yield tough and lightweight steel contributes to reducing air pollution also. Light-weight component design is a growing trend nowadays to address the problems of environmental pollution and convenience for handling. Effective light-weight for mobile cranes, lifting components require utilization of steel with high yield strength and good plasticity.
[0006] Developing high yield strength steel through the addition of excess alloying not only become expensive but also create a scarcity of resources, therefore, not desirable as well as economical. Addressing the present scenario, the steel is designed intelligently to achieve a very good combination of tensile properties with cost-effective alloy design.
[0007] Most of the currently available high yield strength steels are produced through the plate rolling mill, which has several drawbacks. This has led to the development of alternative production route to achieve a similar range of properties aiming relevant applications mobile crane components, lifting & excavation, shipbuilding including automotive.
[0008] Various attempts have taken to develop structural steel with very high yield strength with adequate elongation over the years and. Various groups are currently producing, however, in different ways and different technology compared to the current invention.
[0009] One of the leading producers (SSAB of Sweden), produces this kind of steel with yield strength 700 MPa employing quenching and tempering process through plate mill. Many others follow a similar route. The major drawback of developing the product using this route or technology is a low production rate and less economical.
[0010] Various approached have been adopted in the state of the art to develop a high yield strength steel. For, instance, Japanese steel manufacturer JFE has developed a high yield strength steel based on alloy concept, processing condition and microstructure [JP2011225980A].
[0011] US patent 2008/0110592 A1 discloses development 700 MPa yield strength steel through thin slab casting & rolling technology, which is different from the method adopted in the current invention.
[0012] Japanese patent application JP2004052063A reported the development of steel plate approx. 20 mm thick with a tensile strength above 780MPa using hot rolling process.

OBJECTS OF THE DISCLOSURE
[0013] In view of the foregoing limitations inherent in the state of the art, some of the objects of the present disclosure, which at least one embodiment herein satisfy, are listed hereinbelow.
[0014] It is a general object of the present disclosure to propose a hot rolled high yield strength steel strip product which eliminates the disadvantages of prior art.
[0015] It is an object of the present disclosure to propose the development of hot rolled product thickness 5-7mm with yield strength at least 700 MPa strength and elongation 14% to 18%
[0016] It is another object of the present disclosure to propose the development of hot rolled product thickness minimum 5 mm but not more than 7mm with yield ratio 0.8-0.9.
[0017] It is another object of the present disclosure to propose hot rolled very high yield strength steel strip product comprising of microstructural constituent mainly bainite 50-70% and rest mixture of ferrite and martensite by volume.
[0018] It is another object of the present disclosure to propose the steel is made using conventional existing hot rolling mill comprising of soaking, roughening, austenite hot rolling, cooling and subsequent coiling in predetermined temperature preferably between bainite start and martensite start temperature according to composition of the steel followed by air cooling to ambient temperature to achieve properties disclosed herein.
[0019] These and other objects and advantages of the present invention will be apparent to those skilled in the art after a consideration of the following detailed description taken in conjunction with the accompanying drawings in which a preferred form of the present invention is illustrated.

SUMMARY
[0020] This summary is provided to introduce concepts related to a method of producing high strength structural steel sheet and a high strength structural steel sheet produced by the said method. The concepts are further described below in the detailed description. This summary is not intended to identify key features or essential features of the claimed subject matter, nor is it intended to be used to limit the scope of the claimed subject matter.
[0021] In an embodiment, the present disclosure relates to a method of producing high strength structural steel sheet. The method includes casting a steel slab with composition by weight: Carbon (C) 0.10-0.2%, Manganese (Mn) 0.8-1.6%, Silicon (Si) 0.25–0.5%, Chromium (Cr) 0.15-0.35%, Molybdenum (Mo) 0.05-0.25%, Copper (Cu): 0.1-0.3%, Titanium (Ti) 0.02-0.06%, Sulphur (S) 0.002-0.008%, Nickel (Ni) 0.1-0.25%, phosphorous (P) 0.015-0.025%, and nitrogen (N) 0.004-0.01%; reheating the steel slab at a temperature ranging from 1100 °C to 1300 °C; hot rolling the steel slab into a thin sheet in an austenite region with several passes at finish rolling temperature below a threshold temperature (Tnr); and cooling the hot rolled thin sheet at a rate of 10-70 °C/s up to a coiling temperature ranging from 430 °C to 500 °C.
[0022] In an aspect, the method includes holding the steel slab for 2-4 hours at a temperature ranging from 1170 °C to 1220 °C.
[0023] In an aspect, the finish rolling temperature ranges from 810°C to 860 °C.
[0024] In another embodiment, the present disclosure comprises a high strength structural steel sheet comprising yield strength ranging from 700 MPa to 800 MPa; elongation ranging from 14% to 18%; and yield to tensile strength ratio ranging from 0.7 to 0.95.
[0025] In an aspect, the sheet has hardness is greater than 260 HV.
[0026] In an aspect, the sheet has a mixture of martensite and ferrite not more than 30-50% by weight.
[0027] In an aspect, the ferrite is less than 40% by weight.
[0028] In an aspect, the sheet has bainite which in microstructure is 50-70% by weight.
[0029] In an aspect, the bainite thickness is below a submicron level.
[0030] Various objects, features, aspects, and advantages of the inventive subject matter will become more apparent from the following detailed description of preferred embodiments, along with the accompanying drawing figures in which like numerals represent like components.

BRIEF DESCRIPTION OF THE ACCOMPANYING DRAWING
[0031] The illustrated embodiments of the subject matter will be best understood by reference to the drawings, wherein like parts are designated by like numerals throughout. The following description is intended only by way of example, and simply illustrates certain selected embodiments of devices, systems, and methods that are consistent with the subject matter as claimed herein, wherein:
[0032] FIG. 1 illustrates a method of producing high strength structural steel sheet in accordance with an embodiment of the present disclosure
[0033] FIG. 2 illustrates engineering stress-strain plot of the steel developed in accordance with an embodiment of the present disclosure;
[0034] FIG. 3 illustrates an optical microstructure of the steel developed in accordance with an embodiment of the present disclosure;
[0035] FIG. 4 Scanning Electron Microscope microstructure of the developed steel developed in accordance with an embodiment of the present disclosure;
[0036] FIG. 5 EBSD micrograph of the developed steel developed in accordance with an embodiment of the present disclosure; and
[0037] FIG. 6 X-ray diffraction profile of the steel developed in accordance with an embodiment of the present disclosure.

DETAILED DESCRIPTION
[0038] The detailed description of various exemplary embodiments of the disclosure is described herein with reference to the accompanying drawings. It should be noted that the embodiments are described herein in such details as to clearly communicate the disclosure. However, the amount of details provided herein is not intended to limit the anticipated variations of embodiments; on the contrary, the intention is to cover all modifications, equivalents, and alternatives falling within the spirit and scope of the present disclosure as defined by the appended claims.
[0039] It is also to be understood that various arrangements may be devised that, although not explicitly described or shown herein, embody the principles of the present disclosure. Moreover, all statements herein reciting principles, aspects, and embodiments of the present disclosure, as well as specific examples, are intended to encompass equivalents thereof.
[0040] The terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting of example embodiments. As used herein, the singular forms “a”, “an”, and “the” are intended to include the plural forms as well, unless the context clearly indicates otherwise. It will be further understood that the terms “comprises”, “comprising”, “includes”, “consisting” and/or “including” when used herein, specify the presence of stated features, integers, steps, operations, elements and/or components, but do not preclude the presence or addition of one or more other features, integers, steps, operations, elements, components and/or groups thereof.
[0041] It should also be noted that in some alternative implementations, the functions/acts noted may occur out of the order noted in the figures. For example, two figures shown in succession may, in fact, be executed concurrently or may sometimes be executed in the reverse order, depending upon the functionality/acts involved.
[0042] Unless otherwise defined, all terms (including technical and scientific terms) used herein have the same meaning as commonly understood by one of ordinary skill in the art to which example embodiments belong. It will be further understood that terms, e.g., those defined in commonly used dictionaries, should be interpreted as having a meaning that is consistent with their meaning in the context of the relevant art and will not be interpreted in an idealized or overly formal sense unless expressly so defined herein.
[0043] The aim of the present disclosure is to identify suitable processing route/parameters to produce high yield strength steel having good elongation and hardness, weldability for critical structural applications. In addition, the steel must be processed through the existing melting and hot strip rolling mill facilities without additional investment. The alloy and process design is done in such fashion that the steel offers easy casting, hot rolling, good surface quality, weldable, tough and certainly high load bearing capacity including light weighting. Carbon equivalent is maintained below a certain level for better weldability. Some alloying elements restricted below a certain level to achieve good surface quality after hot rolling and achieve good coating performance. The optimum hot rolling parameters, cooling, and coiling are identified to ensure the steel could be produced under conventional mill operating parameters in the same runout table. Light weighting is achieved through thickness reduction. The high yield strength and toughness is achieved through precise process control and introducing a combination of tough and simple phase mixture in the microstructure. The right combination of processing condition and phase mixture offered an excellent combination of yield strength and elongation in the developed steel.
[0044] The aim of the present disclosure is to develop steel possessing superior yield strength and elongation properties. In particular, one of the objectives of the present disclosure is to fabricate very high strength steel having extraordinary yield strength and elongation, formability and weldability wherein said steel must be developed through existing hot rolling mill facilities without making significant/extra investment.
[0045] The present disclosure relates to a method of fabricating high yield strength steel strip with thickness 5- 7mm that comprises preparation of liquid steel to achieve following alloy composition:
C: 0.10-0.2, Mn: 0.8-1.6, Si: 0.3 – 0.6, Cr: 0.15-0.5 , Al:0.01-0.02, Cu: 0.1-0.3, Mo: 0.05 – 0.25, Ti-0.01-0.06 S- 0.008 max, P - 0.025 max, , N- 0.005 max and rest amount Fe
[0046] Description of the primary components constitutes the newly developed hot-rolled steel sheet is described below.
• C: 0.10 - 0.20 wt.%. To achieve the desired strengthening, the proportion of phase fractions amount of carbon content must be adjusted to so that proper strength level can be obtained. Carbon plays an important role to affect coiling temperature as well as mechanical properties. Weldability is also determined by carbon level along with other alloying. Preferable carbon content should be kept below 0.15% to achieve desired strength and elongation and also weldability, therefore, should be restricted below 0.16%.
• Mn: 0.8- 1.6 wt.% Manganese helps to strengthen through solid solution strengthening and improves yield strength which is important from a structural point of view. However, its amount should be 1.0 or more, preferably 1.25 or more, more preferably 1.55% or more. Manganese amount should preferably be less than 1.6% to avoid welding, casting crack and banding.
• Si: 0.3 – 0.6 wt.% Silicon is also a ferrite stabilizer and strengthening element. Silicon suppresses carbide precipitation during bainite transformation during constant temperature holding/coiling and facilitate mechanical properties improvement. The higher amount of silicon addition is not desirable due to varieties of unwanted scale formation during hot rolling and subsequent cooling. Scale formation leads to bad surface and reduces coating / gavanizibility. Hence, Si should be restricted within a certain range as mentioned and more preferably below 0.4wt%.
• P: 0.028% maximum: Phosphorus is considered detrimental in steel. Therefore, should be amount be restricted to 0.028% maximum or preferably 0.02% or less.
• S: 0.014% maximum: Like Phosphorus Sulphur is also considered detrimental. So sulphur content to be kept as low as possible, preferably below 0.014 wt%. More preferably sulphur content should be below 0.01 wt% to minimize the amount of inclusions which is potential sites for premature failure during forming operations.
• N: 0.005 % maximum: Excess nitrogen in steels is also detrimental. Excess nitrogen may lead to hard inclusions such as TiN and AlN which deteriorate formability. Therefore, nitrogen content has to be restricted below 0.005wt%.
• Ti Nb: 0.01-0.1% maximum: Niobium is added to increase the strength of the steel by a various mechanism such as grain refinement, precipitation. Nb addition is also useful to have a larger amount of retained austenite in the microstructure. Nb should be added carefully and optimized to take advantage of an economic advantage as Nb is costly. Therefore, Nb level should be below 0.09% or more preferably, below 0.055%.
• Mo: 0.05-0.3 wt.% maximum: Molybdenum is added to enhance the hardenability in steel, thereby, favors easy formation of bainite. Due to excess hardenability softer ferrite and relatively harder pearlite phase formation could be suppressed during the bainitic reaction. As Mo is costly, therefore, its amount should be restricted below 0.25 wt% to make the steel economical and taking processing advantage during hot rolling.
• Cr: 0.15-0.5 wt% maximum: Chromium acts very much similar manner to Mo, avoids the formation of polygonal ferrite and pearlite. Cr addition is also more economical in the kind of steel being innovated in the present disclosure. However, Cr could be harmful if added excessive amount as Cr form various kind of carbides.
• Ti: 0.05-0.1 wt% maximum: Ti helps to restrict austenite grain growth, thereby, keep the austenite grain finer. In addition, Ti also forms very fine carbonitride in the presence of Nb, V and increase strength. An excess amount of Ti could be harmful as Ti has a tendency to form hard TiN inclusions. Therefore, the amount of Ti should be restricted below 0.1wt% and more preferably, below 0.05 wt%.
[0047] The developed high strength hot rolled steel contains primarily bainite with volume percent 50-70% and remaining mixture of ferrite and martensite (50-30%) at ambient temperature.
[0048] Bainite: The bainite present (50-70 wt%) in the microstructure is essentially very fine with high dislocation density. Therefore, results in higher strength and good ductility combination
[0049] Ferrite: Ferrite is the high-temperature product that helps to achieve strength, ductility, and toughness. The steel is designed in such a manner it contains at least 20% ferrite to achieve desired mechanical properties
[0050] Martensite: The mixture of retained austenite and martensite constituents of the microstructure is also essential from the point of view of the developed steel. Martensite is beneficial for improvement in the strength properties, however, the ductility decreased. To get a beneficial effect microstructure the aim should be to have some amount of austenite in the microstructure.
[0051] In an aspect, the high strength hot rolled steel contains yield strength 700MPa to 800MPa; elongation 14% to 18%; and yield to tensile strength ratio 0.7 to 0.95.
[0052] FIG. 1 illustrates example method 100 of producing high strength structural steel sheet. The order in which the method 100 is described is not intended to be construed as a limitation, and any number of the described method blocks may be combined in any order to implement the method 100, or an alternative method.
[0053] At block 102, the method 100 includes casting a steel slab with composition by weight: Carbon (C) 0.10-0.2%, Manganese (Mn) 0.8-1.6%, Silicon (Si) 0.25–0.5%, Chromium (Cr) 0.15-0.35%, Molybdenum (Mo) 0.05-0.25%, Copper (Cu): 0.1-0.3%, Titanium (Ti) 0.02-0.06%, Sulphur (S) 0.002-0.008%, Nickel (Ni) 0.1-0.25%, phosphorous (P) 0.015-0.025%, and nitrogen (N) 0.004-0.01%.
[0054] At block 104, the method 100 includes reheating the steel slab at a temperature ranging from 1100 °C to 1300 °C.
[0055] At block 106, the method 100 includes hot rolling the steel slab into a thin sheet in an austenite region with several passes at a finish rolling temperature below a threshold temperature (Tnr).
[0056] At block 108, the method 100 includes cooling the hot rolled thin sheet at a rate of 10-70 °C/s up to a coiling temperature ranging from 430 °C to 500 °C.
[0057] In an aspect, the method includes holding the steel slab for 2-4 hours at a temperature ranging from 1170 °C to 1220 °C.
[0058] In an aspect, the finish rolling temperature ranges from 810°C to 860 °C.
[0059] The method adapted according to present disclosure is to develop the steel product with the specified composition consists of following steps: alloy melting or heat making, casting, roughening, hot rolling, cooling and coiling and cooling to ambient temperature. Each and every processing steps involved are detailed below:
[0060] The alloy according to the present disclosure is melted in pilot scale induction melting furnace and subsequently cast in the form ingot or slab. The ingot or slab is homogenized at a temperature above 1100 °C and held for sufficient time according to the thickness and subsequently applied roughening to deform the austenite and break the cast structure and also achieve suitable thickness prior to the hot rolling process. The roughened hot steel is subsequently hot rolled using multiple passes in the austenite to achieve thickness 5 mm to 7 mm with finish rolling temperature keeping in the austenite region lower side and subsequently passed through pilot scale run out table where the steel is subjected to cooling using water to achieve the desired transformation temperature. From the runout table, the steel transferred in an arrangement for coiling where the steel is allowed to stay for sufficient time to achieve transformation. The predetermined temperature is based on the alloy design and kept in between martensite and bainite regime. The coiling simulation is performed either salt bath or similar kind of arrangement at a predetermined temperature above Ms or below Bs and holds for various time periods. The steel samples are then transferred to air and allowed to cool to ambient temperature. Specimens for microstructure and mechanical properties are taken from the hot rolled sheet. Microstructural characterization is carried out using an optical, scanning electron microscope and electron backscatter diffraction (EBSD). Mechanical properties are evaluated by Vickers hardness method and tensile tests are performed as per ASTM standard using 50 mm gauge length. X-Ray diffraction is employed to confirm the microstructural constituents.
[0061] Tensile testing is performed to assess the performance of the developed steel. As an example, the stress-strain plot of the disclosed one of the steels is depicted in FIG. 2, which shows the steel has superior yield strength with good elongation. The yield strength and elongation obtained in the range 725-780MPa and elongation 15-19% in full-scale ASTM sample [Table2]. The optical micrograph as shown in FIG. 3 confirms that the developed steel has a mixture of bainite and ferrite with little martensite. The scanning electron micrograph further confirmed [FIG.4] the presence of the above phases. The SEM examination also ensured the structure is very fine and bainite plate thickness well below submicron size. EBSD examination again ensured the presence of both bainite and ferrite structure in the microstructure [FIG. 5]. Electron backscatter diffraction (EBSD) also confirms the absence any retained austenite in the structure. The fineness of bainite determines the strength and toughness of the steel. The thickness of bainitic plates is found below submicron size. X-ray diffraction carried is out on the developed steel showed presence diffraction peaks from body center cubic (BCC) indicated by abcc as shown in FIG. 6. Hardly any signals for austenite could be observed from the XRD profile. This confirms that the new steel developed has mainly the bcc structure comprising mainly bainite structure along with ferrite and martensite. Examples: of the exact steel compositions along with corresponding properties:
Composition 1 2 3
C 0.17 0.16 0.15
Mn 1.25 1.29 1.2
Si 0.36 0.36 0.35
Cr 0.21 0.22 0.2
Mo 0.09 0.09 0.1
Al 0.02 0.02 0.02
Ti 0.03 0.03 0.03
Cu 0.12 0.17 0.15
Ni 0.17 0.13 0.15
P 0.02 0.01 0.02
S 0.01 0 0.01
N 0.01 0 0.01
YS (Mpa) 776 773 725
TS (Mpa) 884 830 820
TEL (%) 17 17 16

[0062] The above results confirm the interesting combination of properties of the presently developed hot rolled steel products including yield strength between 725-775 MPa with total elongation (TEL) 14-19% and hardness 265-275 Vickers.
[0063] Thus, with the method of the present subject matter, a high strength structural steel sheet is obtained and said steel comprising yield strength ranging from 700 MPa to 800 MPa; elongation ranging from 14% to 18%; and yield to tensile strength ratio ranging from 0.7 to 0.95.
[0064] In an aspect, the sheet has hardness is greater than 260 HV.
[0065] In an aspect, the sheet has a mixture of martensite and ferrite not more than 30-50% by weight.
[0066] In an aspect, the ferrite is less than 40% by weight.
[0067] In an aspect, the sheet has bainite which in microstructure is 50-70% by weight.
[0068] In an aspect, the bainite thickness is below a submicron level.

TECHNICAL ADVANTAGES
[0069] The present disclosure provides steel that has excellent yield strength with good tensile ductility as well as high yield ratio, therefore, attractive for structural applications such as a mobile crane, automotive, machinery application and several other areas where a good combination of yield strength and elongation is required
[0070] The present disclosure provides steel that has kind of microstructure, therefore, expected to be useful for application where toughness, load bearing capability and light weighting is essential
[0071] The present disclosure proposes judicious alloying with the help of thermodynamic calculation will favor processing of the steel in existing conventional hot strip mill setup without investing additional capital investment
[0072] The present disclosure provides an innovative alloy design which ensures easy process control after hot rolling.
[0073] The present disclosure provides an intelligent alloy design which is also expected to minimize surface related issues such as coating and the like.
[0074] The present disclosure provides economic alloying selection which is also beneficial for good and easy castability and weldability.
[0075] The developed steel with the present disclosure is adopted different, i.e., hot strip process route, which not only offers the better product as developed here but also improve productivity and economical. Therefore, the present disclosure is very much unique and different as the steel has been developed in different route using hot strip mill and coiling, which eliminates or overcome the drawbacks of the plate mill.
[0076] Steel with similar level of yield strength has been developed through hot strip mill other manufacturers, however, the processing and microstructure introduced in the product is different from the present disclosure.
[0077] Thus, the present disclosure provides a method of producing steel with high yield strength and good and good elongation. Said method comprises melting, casting, hot rolling and coiling of steel. The composition described herein to obtain the steel product with excellent mechanical properties. The stated process is highly productive, simple, viable, economical and is highly suitable for industrial applications including load-bearing applications where a combination of very high yield strength with good elongation is necessary.
[0078] Furthermore, those skilled in the art can appreciate that the terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting of the present disclosure. It will be appreciated that several of the above-disclosed and other features and functions, or alternatives thereof, may be combined into other systems or applications. Various presently unforeseen or unanticipated alternatives, modifications, variations, or improvements therein may subsequently be made by those skilled in the art without departing from the scope of the present disclosure as encompassed by the following claims.
[0079] The claims, as originally presented and as they may be amended, encompass variations, alternatives, modifications, improvements, equivalents, and substantial equivalents of the embodiments and teachings disclosed herein, including those that are presently unforeseen or unappreciated, and that, for example, may arise from applicants/patentees and others.
[0080] While the foregoing describes various embodiments of the present disclosure, other and further embodiments of the present disclosure may be devised without departing from the basic scope thereof. The scope of the present disclosure is determined by the claims that follow. The present disclosure is not limited to the described embodiments, versions or examples, which are included to enable a person having ordinary skill in the art to make and use the invention when combined with information and knowledge available to the person having ordinary skill in the art.