Claims:
WE CLAIM:
1. A method of manufacturing cold-rolled steel strip, the method comprising:
casting an ingot comprising in weight % 0.15 - 0.25 carbon, 4 - 7 manganese, 0.1 - 1 silicon, up to 0.02 titanium, 0.1 - 1 aluminum, maximum up to 0.01 sulphur, maximum up to 0.03 phosphorous and up to 0.01 nitrogen, maximum up to 0.0005 hydrogen the balance being iron and impurities.;
anti-flaking heat treatment at 650-700 °C for 12-24 hours;
reheating the ingot up to 1200 °C for homogenization;
hot rolling the steel ingot producing a hot steel strip, finish rolling is being done at a temperature (T1), wherein T1 is A3 + 50 (°C) to A3 + 70 (°C), A3 being the temperature at which the transformation of austenite to ferrite starts at equilibrium;
cooling the hot steel strip to room temperature;
cold rolling the hot steel strip up to a deformation of 70-80 %; and
annealing the hot steel strip at T3, where (A3 – 50 °C) > T3 > (A3 - 100 °C), for 1 - 2 hours and quenching to room temperature.
2. The method as claimed in claim 1, wherein manganese content is present in the range of 4.0 - 6.0 wt. %.
3. The method as claimed in claim 1, wherein the inter-critical annealing time is 1 - 2 hours.
4. The method as claimed in claim1, wherein the extent of cold deformation is 70 – 80 %.
5. A high-toughness cold-rolled steel strip comprising,
0.15 - 0.25 carbon, 4 - 7 manganese, 0.1 - 1 silicon, up to 0.02 titanium, 0.1 - 1 aluminum, max up to 0.01 sulphur, maximum up to 0.03 phosphorous and up to 0.01 nitrogen, maximum up to 0.0005 hydrogen, the balance being iron and impurities (all in wt %);
microstructure of 65 – 75 % ferrite and 25 - 35 % austenite, and
a toughness = 40 GPa%.
6. The high-toughness cold-rolled steel strip as claimed in claim 5, wherein ultimate tensile strength (UTS) of the strip is in the range of 1000-1200 MPa
7. The high-toughness cold-rolled steel strip as claimed in claim 5, wherein total elongation of the strip is the range of 38-45 %.
8. The high-toughness cold-rolled steel strip as claimed in claim 5, wherein manganese content varies in the range of 4 - 6 weight %.
9. The high-toughness cold-rolled steel strip as claimed in claim 5, wherein manganese content of the second phase austenite is 8-10 wt. %.
10. The process as claimed in claim 5, wherein manganese content is present in the range of 4.0 - 6.0 wt. %.
, Description:COLD-ROLLED STEEL STRIP AND METHOD FOR MANUCTURING THE SAME

TECHNICAL FIELD
[0001] The present disclosure, in general, relates to the field of a cold rolled steel strip and, in particular, relates to a cold-rolled steel strip and a method for manufacturing the same.

BACKGROUND
[0002] 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.
[0003] In the mid and late 20th century, steels with less than 350 MPa was deemed sufficient for usage in a range of automotive applications. But with evolution, vehicles became more and more advanced in terms of performance, crash worthiness, and environment friendliness. This lead to development of multiple generations of high strength steels, which meant the tensile strength was increasing more and more at the same time there was also a decrease in the ductility which affected the formability of the steel.
[0004] In the past decades, the automobile industry has been keen on reducing the carbon footprint along with increasing the passenger safety which lead to greater usage of dual phase steel, bainitic steel, complex phase steel, martensitic steel, and the like. These steels were primarily ferritic base and possessed better mechanical properties when compared with their predecessors. But the strength and ductility combination was still not as desired by the ever evolving automotive industry. Hence, the next generation advanced high strength steel mainly comprising TRIP (transformation induced plasticity) and TWIP (twinning induced plasticity) steel were developed to mitigate the pertaining issues of formability. However heavy alloying and production issues of TWIP steels limited its usage, further TWIP and TRIP steels are austenitic base which made them prone to issues pertaining to hydrogen embrittlement. The stringent requirements of the automotive industry could be met by the third generation advanced high strength steel, a result of unique combination of alloy processing coupled with microstructure engineering.
[0005] Recent developments in manufacturing aforementioned grade though quench and partitioning (Q&P) route has been attempted. The microstructure of Q&P steel consists of retained austenite (RA) along with bainite or martensite. These steels have tensile strength in excess of 1000 MPa along with good ductility which is attribute the presence of RA in the microstructure.
[0006] Research has already been put into development of high strength and high plasticity steels, light weight ferritic steels, wear resistance steels through hot rolling as well as cold rolling routes (CN103103438A, KR20140030969A, CN104694829A) with Manganese content of 4-15 wt.% steels with high strength and elongation have been already produced but they often contain high amount of alloying elements like Aluminium (Al) in excess of 8 wt.%, as disclosed in KR20140030969A and CN102304664A. High amount of Molybdenum (Mo), Chromium (Cr), Copper (Cu) and Nickle (Ni) have been added to achieve a strength levels in excess of 800 MPa with excellent ductility, as disclosed in CN104651734A, CN104630641A, and CN108546812A. However, such inventions often require a higher alloying addition which renders the product cost in effective. Moreover, complex and long post processing treatments in excess of 24 hours (as disclosed in CN108546812A) would limit the product usage. Other Cold rolled steel with deformation up to 65-70 % has already been produced but again high amount of alloying makes it cost ineffective (as disclosed in CN104694816A). Though there have been developments with lower alloying content, a complex processing makes it less energy efficient (as discussed in CN103695765A).
[0007] There have been several attempts in making medium manganese steel, most attempts are in a smaller weight scale. And possibilities of micro cracking in the material arises when thicker sections are made owing to generation of residual stresses. Steels with ultimate tensile strength (UTS) in excess of 1000 MPa and elongation more than 40 % have been made but the scale, the amount of alloy added, and the complexity of the process makes it less attractive for the steel industry.
[0008] Accordingly, there is a need for a technically viable and economically attractive way of developing cold rolled medium Mn steel grade in a large scale without aforementioned limitations.

OBJECTS OF THE DISCLOSURE
[0009] 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.
[0010] It is a general object of the present disclosure to propose a steel within the genre of third generation AHSS with toughness of minimum 40 GPa%.
[0011] It is an object of the present disclosure to propose a steel with toughness of minimum 40 GPa% which has maximum 8.25 % by Wt. alloying content and shorter processing time.
[0012] It is an object of the present disclosure to develop steel with toughness of minimum 40 GPa% which has maximum 7% by weight of Manganese, preferably less than 6%.
[0013] It is another object of the present disclosure to propose a cold-rolled steel strip having a minimum toughness of 40 GPa%, which possesses a microstructure consisting of ferrite and second phase (Retained Austenite) and the retained austenite is in the form of globules, and has a manganese concentration of not less than 9 % by weight.
[0014] It is another object of the present disclosure to propose a cold-rolled steel strip which has undergone an anti-flaking heat treatment cycle of no less than 24 hours.
[0015] It is another object of the present disclosure to propose a cold-rolled steel strip having a minimum toughness of 40 GPa%, which is adaptable to automotive industry in particular for manufacturing components where high strength and high ductility is required.
[0016] 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
[0017] This summary is provided to introduce concepts related to a cold-rolled steel strip and a method for manufacturing the same. 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.
[0018] In an embodiment, the present disclosure relates to a method of manufacturing a cold-rolled steel strip. The method includes casting an ingot comprising in weight % 0.15 - 0.25 carbon, 4 - 7 manganese, 0.1 - 1 silicon, up to 0.02 titanium, 0.1 - 1 aluminum, maximum up to 0.01 sulphur, maximum up to 0.03 phosphorous and up to 0.01 nitrogen, maximum up to 0.0005 hydrogen the balance being iron and impurities; anti-flaking heat treatment at 650 °C for 12-24 hours; reheating the ingot up to 1200 °C for homogenization; hot rolling the steel ingot producing a hot steel strip, finish rolling is being done at a temperature (T1), wherein T1 is A3 + 50 (°C) to A3 + 70 (°C), A3 being the temperature at which the transformation of austenite to ferrite starts at equilibrium; cooling the hot steel strip to room temperature; cold rolling the hot steel strip up to a deformation of 70-80 %; and annealing the hot steel strip at T3, where (A3 – 50 °C) > T3 > (A3 - 100 °C), for 1 - 2 hours and quenching to room temperature.
[0019] In an aspect, the anti-flaking heat treatment pertains to soaking the steel at a temperature of 650-700 °C for a long duration. The duration of soaking can vary from 12-24 hour. The anti-flaking heat treatment ensures the hydrogen trapped in the steel after solidification to defuse out. Also, the presence of hydrogen often causes cracking during subsequent processing.
[0020] In an aspect, the manganese content is present in the range of 4.0 - 6.0 wt. %.
[0021] In an aspect, the inter-critical annealing time is 1 - 2 hours.
[0022] In an aspect, the extent of cold deformation is 70 – 80 %.
[0023] In another embodiment, the present disclosure further relates to a high-toughness cold-rolled steel strip comprising 0.15 - 0.25 carbon, 4 - 7 manganese, 0.1 - 1 silicon, up to 0.02 titanium, 0.1 - 1 aluminum, max up to 0.01 sulphur, maximum up to 0.03 phosphorous and up to 0.01 nitrogen, maximum up to 0.0005 hydrogen, the balance being iron and impurities (all in wt %); microstructure of 65 – 75 % ferrite and 25 - 35 % austenite, and a toughness = 40 GPa%.
[0024] In an aspect, ultimate tensile strength (UTS) of the strip is in the range of 1000-1200 MPa.
[0025] In an aspect, total elongation of the strip is the range of 38-45 %.
[0026] In an aspect, manganese content varies in the range of 4 - 6 weight %.
[0027] In an aspect, manganese content of the second phase austenite is 8-10 wt. %.
[0028] In an aspect, manganese content present in the range of 4.0 - 6.0 wt. %.
[0029] 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
[0030] 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:
[0031] FIG. 1 illustrates variation of strength and elongation for different advanced high strength steel;
[0032] FIG. 2 illustrates a method a method of manufacturing a cold-rolled steel strip, in accordance with an embodiment of the present disclosure;
[0033] FIG. 3A illustrates a microstructure of steel 1 after processing in accordance with an embodiment of the present disclosure;
[0034] FIG. 3B illustrates a microstructure of steel 2 processed in a condition not suitable for attaining a final microstructure;
[0035] FIG. 4 illustrates cracks present in the steel 2 with high hydrogen content along the rolling direction; and
[0036] FIG. 5 illustrates X-ray diffraction of steel 1, showing presence of retained austenite, after processing in accordance with an embodiment of the present disclosure.

DETAILED DESCRIPTION
[0037] 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.
[0038] 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.
[0039] 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.
[0040] 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.
[0041] 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.
[0042] Embodiments explained herein pertain to a cold rolled steel strip with a tensile strength of at least 1000 MPa and ductility at least 40 %. This cold rolled steel strip can be employed widely as auto components requiring high strength along with ductility.
[0043] The cold rolled steel strip having a minimum toughness of 40 GPa%, according to the present disclosure contains in weight percent 0.15 - 0.25 % of carbon, 4 – 7 % of manganese - preferably 4 - 6 %, 0.1 - 1 % of silicon, up to 0.02 % of titanium, 0.1 - 1 % of aluminum, maximum up to 0.01 % of sulphur, maximum up to 0.03 % of phosphorous and up to 0.01 % of nitrogen, the balance being iron and impurities. The cold-rolled steel strip with a minimum toughness of 40 GPa% according to the present disclosure has a microstructure comprising 65-75% of ferrite and 25-35% of retained austenite wherein the ferrite is in the granular form so as the austenite.
[0044] The present disclosure relates to a cold rolled dual phase steel strip which has a specific alloying composition and is manufactured with a precise control of the rolling and cooling parameters in order to produce the target microstructure, such that a minimum toughness of 40 GPa%, is achieved.
[0045] In accordance with an embodiment, the chemical composition constituting the cold rolled steel strip produced according to the present disclosure are described below:
1. Alloying additions:
[0046] The addition of each alloying element and the limitations imposed on each element are essential for achieving the target microstructure and properties.
• Carbon (C): 0.15 - 0.25%: Carbon is one of the most effective and economical strengthening elements. Carbon readily partitions during the intermediate heat treatment in austenite thereby stabilizing it. Carbon is the component which reduces the Ms temperature to the maximum extent. However, in order to avoid weldability issues and excess stabilization of austenite, the carbon content has to be restricted to less than 0.25%.
• Manganese (Mn): 4.0 - 7.0%: Manganese not only imparts solid solution strengthening to the ferrite but it also lowers the austenite to ferrite transformation temperature thereby refining the ferrite grain size. Mn helps in lowering the stacking fault energy of austenite. Manganese beyond 6% by Wt. will reduce the austenite to ferrite transformation kinetics and make it sluggish thus affecting the processing time and hence, Manganese is preferred to be less than 6%.
• Silicon (Si): 0.1 - 1 %: Silicon like Manganese is a very efficient solid solution strengthening element. Silicon restricts the formation of carbides thereby enriching the austenite with carbon. Silicon helps in enhancing the ferrite to austenite transformation kinetics which otherwise gets sluggish due to addition of manganese. However, additions of Silicon should be restricted to less than 1 % in order to prevent excessive formation of surface scales.
• Phosphorus (P): 0.03% maximum: Phosphorus content should be restricted to 0.03% maximum as higher phosphorus levels can lead to reduction in toughness and weldability due to segregation of P into grain boundaries.
• Sulphur (S): 0.01% maximum: The Sulphur content has to be limited otherwise it results in a very high inclusion level that deteriorates formability.
• Nitrogen (N): 0.01% maximum: Reducing nitrogen levels positively affects ageing stability and toughness in the heat-affected zone of the weld seam, as well as resistance to inter-crystalline stress-corrosion cracking.
• Aluminium (Al): 0.1 - 1 %: Aluminium is used as a deoxidizer and killing of steel. It limits growth of austenite grains. Al along with Si helps in enhancing the ferrite transformation kinetics. Al content should be restricted to 1.0 % maximum as higher aluminium levels can lead to issues during coating.
• Titanium (Ti): 0.05% maximum: Titanium improves strength by limiting austenite grain size. Titanium forms carbides and nitrides which are stable at high temperature.
2. Microstructure:
[0047] In order to achieve the required mechanical properties, the concept of TWIP/TRIP steel is used in conjunction with possible strengthening mechanisms. As stated above, the strengthening contribution from solid solution elements is restricted. In view of the above, the only way by which the target strength can be achieved is by modifying the microstructure and hence a microstructure consisting of second phase (retained austenite) and ferrite as matrix was targeted in the present disclosure. The required amount of strength comes from the solid solution strengthened ferrite due to additions of Si and Mn along with grain refinement and the ductility increases due to the presence of retained austenite which transforms to a’-martensite by TRIP or to e-martensite by TWIP. Formation of twins in the microstructure results in refinement of the grains which results in higher strength as well as elongation, hence precise control of the microstructure is essential for achieving the final strength.
[0048] According to an embodiment of the present disclosure, a new processing route is described to develop a cold rolled ferrite and austenite dual phase steel whose composition is shown in Table 1:

Table 1: Chemical composition of two alloys developed at medium scale plant. The weight of each heat is approximately 2.5 tonnes.
Sl.No. Chemical composition (wt. %)
C Mn Si Al N S P H
Steel 1 0.196 5.16 0.82 0.36 0.0081 0.004 0.007 0.0005
Steel 2 0.224 5.09 0.85 0.42 0.0083 0.004 0.005 0.0032

[0049] FIG. 2 illustrates a method of manufacturing a cold-rolled steel strip, in accordance with an embodiment of the present disclosure, in accordance with an embodiment of the present disclosure. The order in which the method 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, or an alternative method.
[0050] The method of manufacturing a cold-rolled steel strip according to the present disclosure consists of a casting step followed by a forging step, anti-flaking heat treatment, hot rolling step, a controlled cooling step, acid bath pickling, a cold rolling step and an inter-critical annealing step using a steel material which satisfies the composition as shown in Table 1. The various processing steps are described in their respective order below:
[0051] In an aspect, a cold rolled strip of the composition as shown in Table 1 was used for the carrying out final heat treatments which will ensure the required properties being achieved. The processing schedules were designed keeping in mind the final objective to develop a microstructure with 25 - 35 % second phase (retained austenite) along with 65-75 % ferrite in order to develop a steel which has high toughness (greater than 40 GPa%). All the processing parameters were tuned keeping the target to fulfil such objective.
[0052] The process flow of the method involved in the present disclosure comprises of method steps 100 – 110. As per step 100, the steel is produced through air induction melting where in the ferro alloys to be added were pre-heated to a temperature of 150 °C, so that the moisture is driven out which often results in high hydrogen content in the steel.
[0053] As mentioned in step 101, the molten metal is bottom poured into moulds already preheated at 500 °C, as soon as the metal pouring was completed, extended hot tops are put on the moulds so as to avoid any sort of pipe formation due to metal shrinkage during solidification.
[0054] In step 102 the cast ingots are hot transferred and charged into a furnace already at 650-700 °C for about 12-24 hours, the temperature of the furnace is gradually increased to 1200 °C and maintained at the mentioned temperature for 4 hours to homogenize the composition within the ingot. This will ensure in minimization of manganese segregation within the ingot.
[0055] As per step 103, the ingots are hot forged to break the cast dendritic structure and then air cooled to room temperature.
[0056] Post forging, in step 104, the forged ingots are subjected to anti-flaking heat treatment for a duration of 24 hours at 650 °C and gradually furnace cooled to room temperature. The anti-flaking heat treatment pertains to soaking the steel at a temperature of 650-700 °C for a long duration, the duration of soaking can vary from 12-24 hour. The anti-flaking heat-treatment ensures the hydrogen trapped in the steel after solidification to defuse out. Presence of hydrogen often causes cracking during subsequent processing.
[0057] Step 105 involves a non-destructive testing by means of ultra sound, which ensures no abnormality within the material prior to the hot rolling process.
[0058] At step 106, the forged steel ingot is then again homogenized at 1200 °C for 3 hours prior to rolling in order to ensure a completely austenitic structure so that the rolling loads are less.
[0059] In step 107, the ingot is finish rolled at a temperature of T1 where (A3 + 50 °C) < T1 < (A3 + 70 °C). A3 being the temperature at which the austenite just starts to transform into ferrite. After the finish rolling, maximum 10-15 °C drop in the temperature is allowed to air cool to T2, where 50 °C < T2 < 28 °C.
[0060] The next step 108 is pickling the hot rolled strip in an acid bath comprising of hydrochloric acid and water in the ratio 1:1. This step 108 ensures no residual scale post hot rolling is present on the strip which may create defects during cold rolling.
[0061] In step 109, cold rolling of the aforementioned steel was done to the extent of 70-80 %. The final thickness of the steel strip after step 109 is between 1.4 to 1.8 mm.
[0062] Finally, the step 110 is annealing the cold rolled strips at a temperature T3 such that (A3 – 50 °C) > T3 > (A3 - 100 °C) for 1 – 2 hours after which the strip was quenched to room temperature.
[0063] Thus, the first quenching step to T2 after rolling is to ensure a completely martensitic microstructure. Being martensite, the structure has high defect density which ensures a faster partitioning of substitutional alloying elements while annealing in the inter-critical region. The annealing of the rolled strip at temperature T3 for 1 – 2 hours ensures enrichment of austenite with carbon and manganese, so to get it retained at room temperature. And, the extent of enrichment of carbon and manganese in the heat treated steel affects the stacking fault energy of austenite which in turn affects the desired mechanical properties.

Examples
[0064] Two heats as per the composition of present disclosure are cast in the laboratory. Both heats are hot forged, hot-rolled and cold rolled according to the present disclosure. The process flow followed in the present disclosure is shown in FIG. 2. However, the inter-critical annealing for both samples was different. For Steel 1, the inter-critical annealing was done in accordance with the present present disclosure, whereas for Steel 2, a lower annealing temperature and a lesser duration of holding is used. The duration of annealing for both steels as well as their mechanical properties is listed in Table 2:

Table 2. Mechanical properties and annealing duration of two alloys
Steel YS
MPa UTS
MPa %
Elongation Second phase (%) Toughness
GPa% Annealing Duration
(hours)
Steel 1 817 1016 43 28 43.6 1.5
Steel 2 840 1030 34 <20 35 0.75

[0065] The microstructures of the two steels are shown in FIGS. 3A and 3B. Moreover, it can be seen that in steel 2 (FIG. 3B), there is a very high amount of hydron, which lead to cracking of the material post processing, the cracks in the material can be seen in FIG. 4. Hence, it is clear from the mechanical properties and the microstructures achieved that the target properties cannot be achieved when the annealing duration and temperature do not conform to the processing parameters of the present disclosure.
[0066] An x-ray diffraction study is also performed to ascertain the amount of retained austenite in the microstructure and the amount of the second phase in steel 1 is in the range of 25-35%. The x-ray profile of steel 1 is shown in FIG. 5 which clearly shows presence of retained austenite. In an aspect, the austenite is stabilized by substitutional and interstitial atoms like carbon and manganese.
[0067] The subject matter as per the present disclosure provides a method of manufacturing a high toughness cold-rolled steel strip with a minimum toughness of at least 40 GPa%. The manufactured steel strip comprises of 65-75 % ferrite and 25-35% retained austenite and can be used to manufacture automotive components which will weigh less and will have higher crash resistance than the components made from existing grades of steel. Components like front bumper beam, side impact bar, engine cradle are some of the examples of the automotive components.
[0068] Each of the appended claims defines a separate invention, which for infringement purposes is recognized as including equivalents to the various elements or limitations specified in the claims. Depending on the context, all references below to the "invention" may in some cases refer to certain specific embodiments only. In other cases, it will be recognized that references to the "invention" will refer to subject matter recited in one or more, but not necessarily all, of the claims.
[0069] Groupings of alternative elements or embodiments of the invention disclosed herein are not to be construed as limitations. Each group member can be referred to and claimed individually or in any combination with other members of the group or other elements found herein. One or more members of a group can be included in, or deleted from, a group for reasons of convenience and/or patentability. When any such inclusion or deletion occurs, the specification is herein deemed to contain the group as modified thus fulfilling the written description of all groups used in the appended claims.
[0070] 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.
[0071] 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.
[0072] 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.