MXPA00005798A - Process components, containers, and pipes suitable for containing and transporting cryogenic temperature fluids - Google Patents

Abstract

Process components (12), containers (15, 11), and pipes are provided that are constructed fromultra-high strengh, low alloy steels containing less than 9 wt.%mickel and having tensile strengths greater than 830 MPa (120 ksi) and DBTTs lower than about -73°C (-100°F).

Description

COMPONENTS CONTAINERS AND PIPES OF ADEQUATE PROCESS FOR CONTAINING AND TRANSPORTING CRYOGENIC TEMPERATURE FLUIDS DESCRIPTION OF THE INVENTION This invention relates to components, containers and process pipes suitable for containing and transporting fluids at cryogenic temperature. More particularly, this invention relates to components, containers and process pipes that are constructed from steel of a low alloy ultra high strength that contains at least 9% by weight of nickel and has a higher tensile strength than 830 MPa (120 ksi) and a DBTT less than approximately -73 ° C (-100 ° F). Different terms are defined in the following specification. For convenience a Glossary of terms is provided herein, immediately followed by the claims. Frequently in the industry, there is a need for process components, containers and pipes that have adequate toughness to process, contain and transport fluids at cryogenic temperatures, i.e., at temperatures below about 40 ° C (-40 ° F). ), i = in fail. It is especially true in the chemical and hydrocarbon processing industries. For example, cryogenic processes are used to achieve the separation of components in hydrocarbon liquids and gases. Cryogenic processes are also used in the separation and storage of fluids such as oxygen and carbon dioxide. Other cryogenic processes used in the industry, for example, include low temperature power generation cycles, refrigeration cycles, and liquefaction cycles. In the generation of low temperature power, the reverse Rankine cycle and its derivatives are typically used to generate power by coating freezing energy available from an ultra low temperature source. In the simplest form of the cycle, a suitable fluid, such as ethylene, is condensed at a temperature, pumping under pressure, vaporized and expanded through a work production turbine coupled to a generator. There is a wide variety of applications in pump shells that are used to move cryogenic liquids in cooling process systems where the temperature can be less than about -73 ° C 100 ° F). Additionally, when the fuel fluids are discharged into a burner system during processing, the fluid pressure is reduced, for example, by passing through a pressure safety valve. This pressure drop results in a concomitant reduction in the temperature of the fluid. If the pressure drop is sufficiently long, the resulting fluid temperature may be sufficiently low that the tenacity of the carbon steels traditionally used in the burner systems is not adequate. Carbon steel can be fractured at cryogenic temperatures. 5 In various industrial applications, fluids are contained and transported at high pressures, that is, as compressed gases. Typically, the containers for storage and transportation of compressed gases are constructed of commercially available standards of 0 carbon steels, or from aluminum, to provide the need for toughness for the fluid transportation containers that are frequently handled, and the walls of the containers must be relatively thick to provide a necessary resistance to contain the highly pressurized compressed gas. Specifically, pressurized gas cylinders are widely used to store and transport gases such as oxygen, nitrogen, acetylene, argon, helium and carbon dioxide, to name a few. Alternatively, the temperature of the fluid can be lowered to produce a saturated liquid, and still subcooled if necessary, so the fluid can be contained and transported as a liquid. The fluids can be liquefied in combinations of pressures and temperatures corresponding to the bubble point conditions for the fluids. Depending on the properties of the fluid, it may be economically advantageous to contain and transport the fluid in a condition at pressurized cryogenic temperature, if the media is available! cost effective to contain and transport the fluid at pressurized cryogenic temperature. Various ways are possible for transporting a fluid at pressurized cryogenic temperature, for example, tank truck, train tank wagons or maritime transport. When the pressurized cryogenic temperature fluids are used by the local distributors in the pressurized cryogenic temperature condition, in addition to the aforementioned storage and transportation containers, an alternative method of transportation is a discharge pipe distribution system, ie , pipes between a central storage area, where a large supply of the cryogenic temperature fluid is being produced | and / or accumulated, for local distributors or users. All these transportation methods require the use | of containers and / or storage pipes constructed from a material having adequate cryogenic temperature tenacity to prevent failure and adequate strength to maintain high fluid pressures. The Ductile to Brittle Transition Temperature (DBTT) delineates the two fracture regimes in structural acills. At temperatures below the DBTT, steel failure tends to occur due to low energy (brittle) crack fracture, while at temperatures above the DBTT, steel failure tends to occur due to high energy ductile fracture . The welded steels used in the construction of process components and containers for the aforementioned cryogenic temperature applications and for other load support, the cryogenic temperature service must have good DBTT 'below the service temperature in the steel base and the HAZ avoiding the failure by the fracture of low energy crack. Nickel-containing steels conventionally used for cryogenic temperature structural applications, for example, steels with nickel contents greater than about 3% by weight, have low DBTTs but also have relatively low tensile strength. Typical and commercially available Ni steels 3.5% by weight, Ni 5.5% by weight and Ni 9% by weight have the DBTT of about -100 ° C (-150 ° F), -155 ° C (-250 ° F) , and -175 ° C (-280 ° F), respectively, and tensile strength 'up to approximately 485 MPa (70 ksi), 620 MPa (90 ksi), and 830 MPa (120 ksi), respectively. To achieve these combinations of strength and toughness, these steels generally undergo expensive processing, for example, double annealing treatment. In the case of applications of cryogenic temperature, the industry currently uses these steels containing commercial nickel due to its good tenacity at low temperatures, but must design around its relatively low tensile strengths. The 5 designs generally require exceeding steel thicknesses for cryogenic temperature applications for load bearing. Therefore the use of nickel-containing steels in applications at cryogenic temperature for load bearing tend to be expensive due to the high cost of the steel combined with the thickness of the steel required. Although some commercially available carbon steels have DBTTs as low as about -46 ° C (-50 ° F), carbon steels are commercially used in the construction of components and commercially available process containers for chemical and hydrocarbon processes do not have adequate tenacity for use under cryogenic temperature conditions. The materials with better tenacity at cryogenic temperature than carbon steel, for example, the acerosi that contain commercial nickel mentioned in the above, (Ni of 3 ^% by weight at Ni 9% by weight) aluminum (Al-5083 or Al-5085), or stainless steel are traditionally used for the commercially available construction process of components and containers that are subject to conditions of cryogenic temperature. Also, the materials ¿^ ¡^^^^^^^^^^^^^^^^^^^^^^^^^^^^ As titanium alloys and specially impregnated epoxy weft glass fiber blends are sometimes used. However, the components, containers and / or process pipes built from! of those materials sometimes have increased wall thicknesses to provide the required strength. This adds weight to the components and containers that must be supported and / or transported, sometimes at the significant cost added to a project. Additionally, these materials tend to be more expensive than standard carbon steels. The added cost for the support and transportation of thick-walled components and containers combined with the increased cost of construction material that tends to decrease the economic attractiveness of the projects. There is a need for the process of components and containers suitable to economically contain, and transport fluids at cryogenic temperature. There is also a need for suitable pipes for economically containing and transporting fluids at cryogenic temperature.1 Accordingly, the main object of the present invention is to provide the process of components and containers suitable for economically containing and transporting fluids at cryogenic temperature and for providing suitable pipes. to economically contain and transporting fluids at cryogenic temperature. Another object of the present invention is to provide the process I of container components and pipes that are constructed from materials having both adequate strength and fracture toughness to contain pressurized cryogenic temperatures. Consistent with the objects set forth in the foregoing of the present invention, the process of the components, containers and pipes are provided to contain and transport fluids at cryogenic temperature. The process of the components, containers and pipes of this invention are constructed from materials comprising an ultra-high strength, the low alloy steel contains less than 9% by weight of nickel, preferably it contains less than about 7% by weight. % by weight of nickel, more preferably contains less than about 5% by weight of nickel and even more preferably contains less than about 3% by weight of nickel. The steel has an ultra high strength, for example, tensile strength (as defined herein) greater than 830 MPa (120 ksi), and a DBTT (as defined herein) less than about -73 ° C (-100 ° F). These new processes of components and containers can be advantageously used, for example, in cryogenic expansion plants for the recovery of natural gas liquids, in the liquefaction and liquefaction processes of liquefied natural gas ("LNG"), in the process of controlled freezing zone i ("CFZ") undertaken by Exxon Production Research Company, in cryogenic refrigeration systems, in low temperature power generation systems, and in cryogenic processes related to the manufacture of ethylene and polyethylene. The use of these new container components and process pipes advantageously reduces the risk of the cold brittle fracture normally associated with conventional carbon steels in cryogenic temperature service. Additionally, these components and process containers can increase the economic attraction of a project. BRIEF DESCRIPTION OF THE DRAWINGS The advantages of the present invention will be better understood by reference to the following detailed description and the attached drawings in which: Figure 1 is a typical process flow diagram illustrating how some of the components of the process of the present invention are used in a de-methanation gas plant; Figure 2 illustrates a sheet for fixed pipe, single pass heat exchanger according to the present invention; Figure 3 illustrates a heat exchanger of aa ^^ M ^^^ St &jag8isßbJ ^^ & j ^^^^^ heat transfer according to the present invention; Figure 4 illustrates an extender of the feed separator according to the present invention; Figure 5 illustrates a burner system according to the present invention; Figure 6 illustrates a network system, distribution of discharge pipe according to the present invention; Figure 7 illustrates a condenser system according to the present invention as used in an inverse Rankine cycle; Figure 8 illustrates a condenser according to the present invention as used in a cascade cooling cycle; Figure 9 illustrates a vaporizer according to the present invention as used in a cascade cooling cycle; Figure 10 illustrates a pumping system according to the present invention; Figure 11 illustrates a process column system according to the present invention; Figure 12 illustrates another process column system according to the present invention; Figure 13A illustrates a depth scheme of critical cracking, to give a cracking length, as a function of fracture toughness CTOD and residual stress; and Figure 13B illustrates the geometry (length and depth) of a cracking. While the invention will be described in relation to its preferred embodiments, it will be understood that the invention is not limited thereto. On the contrary, the invention is intended to cover all alternatives, modifications, and equivalents that may be included within the scope and spirit of the invention, as defined by the appended claims. The present invention relates to the new components, containers and process pipes suitable for processing, containing and transporting fluids at cryogenic temperature; and, in addition, components, containers and process pipes that are constructed from materials comprising a low alloy steel of ultra high strength, which contains less than 9% by weight of nickel and has a tensile strength greater than 830. MPa (120 ksi)? and a DBTT lower than approximately -73 ° C (-100 ° F). Preferably, the ultra high strength low alloy steel has excellent cryogenic temperature toughness both in the bottom plate and in the heat affected zone (HAZ) when welding.

The process of the components, containers and pipes suitable for the processing and containing the fluids at cryogenic temperature is provided, where the process of the components, containers and pipes is constructed from materials comprising an ultra high strength steel, of low alloy which contains less than 9% by weight of nickel and has a tensile strength greater than 830 MPa (120 ksi) and a DBTT less than about -73 ° C (-100 ° F). Preferably, the ultra high strength, low alloy steel contains less than about 7 wt.% Nickel and more preferably contains less than about 5 wt.% Nickel. Preferably the ultra high strength, low alloy steel has a tensile strength greater than about 860 MPa (125 ksi), and more preferably greater than about 900 MPa (130 ksi). Even more preferably, the process of the components, containers and pipes of the invention is constructed from materials comprising an ultra high strength, low alloy steel containing less than about 3% by weight of nickel and having a tensile strength exceeding approximately 1000 MPa (145 ksi) and a DBTT less than approximately -73 ° C (-100 ° F). The five provisional patent applications Copendent North American (the "PLGN Patent Applications"), each entitled "Improved System for Processing, Storing, and Transporting Liquefied Natural Gas", describes containers and tankers for the storage and maritime transportation of pressurized liquefied natural gas (PLNG) at a pressure in the wide range of approximately 1035 kPa (150 psia) to approximately 7590 kPa (1100 psia) and at a temperature in the broad range from -123 ° C (-190 ° F) to, approximately -62 ° C (-80 ° F). The most recent of the PLNG Patent Applications has a priority date of May 14, 1998 and is identified by applicants as File No. 97006P4 and by the United States Patent and Trademark Office ("USPTO") as Application Number 60/085467. The first of the PLNG Patent Applications has a priority date of June 20, 1997 and is identified by the USPTO as Application Number 60/050280. The second of the P &N Patent Applications has a priority date of July 28, 1999 and is identified by the USPTO as Application Number 60/053966. The third of the PLNG Patent Applications has a priority date of December 19, 1997 and is identified by the USPTO as Application Number 60/068226. The fourth of the PLNG Patent Applications has a priority date of March 30, 1998 and is identified by the USPTO as Application Number 60/079904. In addition, the Requests.de PLGN patent describes systems and containers for the processing, storage and transportation of PLNG. Preferably, the PLNG fuel is stored at a pressure of about 1725 kPa (250 psia) 'to about 7590 kPa (1100 psia) and at a temperature of about -112 ° C (-170 ° F) to about -62 ° C (-80 ° F). More preferably, the PLNG fuel is stored at a pressure in the range of about 2415 kPa (350 psia) to about 4830 kPa (700 psia) and at a temperature in the range of about -101 ° C (-150 ° F) to approximately -79 ° C (-110 ° F). Even more preferably, the low ends of the PLNG fuel pressure and temperature ranges are approximately 2760 kPa (400 psi) and approximately -96 ° C (-140 ° F). Hereby, without limitation to this invention, the process of the components, containers and pipes of the invention are preferably used for PLNG processing. The Steel for the Construction Process of the Components, Containers and Pipes Any steel of ultra high strength, low alloy contains less than 9% by weight of nickel and has an adequate tenacity to contain fluids at cryogenic temperature, such as PLNG, in operating conditions, | according to the known principles of the mechanisms | of fracture as described herein, may be used for the construction of the process of the components, containers and pipes of this invention. An exemplary steel for use in the present invention, without thereby limiting the invention, is a low alloy, weldable, low alloy steel containing less than 9 wt.% Nickel and having a higher tensile strength. that 830 MPa (120 ksi) and adequate tenacity to prevent the initiation of a fracture, for example, a case of failure, under operating conditions at cryogenic temperature. Another exemplary steel for use in the present invention, without thereby limiting the invention, is a low alloy, weldable, low alloy steel containing less than about 3% by weight of nickel and having a tensile strength. less than about 1000 MPa (145 ksi) and adequate tenacity to prevent the initiation of a fracture, i.e., a case of failure, under operating conditions at cryogenic temperature. Preferably, these exemplary steels have DBTTs of less than about -73 ° C (-100 ° F). Recent advances in steel made by the technology have made it possible to manufacture ultra high strength, low alloy steels with excellent cryogenic temperature tenacity. For example, three North American patents issued to Koo et al., 5,531,842, 5,545,269, and 5,545,270, describe novel steels and methods for processing these steels to produce steel plates with tensile strength of approximately 830 MPa (120 ksi), 965 MPa. (140 ksi), and greater. The steels and processing methods described herein, have been improved and modified to provide combined steel chemicals and processing for the manufacture of ultra high strength, low alloy steels with excellent toughness at cryogenic temperature in both the steel base, as in the area affected by heat (HAZ) when welding.

These ultra high strength, low alloy steels have also improved toughness over commercially available ultra low strength, low alloy steels. Improved steels are described in the North American provisional patent application entitled "ULTRA-HIGH STRENGTH STEELS WITH EXCELLENT CRYOGENIC TEMPERATURE TOUGHNESS", which has a priority date of December 19, 1997 and is identified by the United States Patent and Trademark Office ("USPTO") as Application 60/068194; in a co-pending provisional US patent application entitled "ULTRA-HIGH STRENGTH AUSAGED STEELS WITH EXCELLENT CRYOGENIC TEMPERATURE TOUGHNESS", which has a priority date of December 19, 1997 and is identified by the USPTO as Application Number 60/068252; and a request for provisional North American provisional patent titled "ULTRA-HIGH STRENGTH DUAL PHASE STEELS WITH EXCELLENT CRYOGENIC TEMPERATURE TOUGHNESS ", which has a priority date of December 19, 1997 and is identified by the USPTO as Application Number 60/068816 (collectively, the" Steel Patent Applications "). in the Steel Patent Applications, and further described in the following examples, are especially suitable for constructing the process of the components, containers, and pipes of this invention in which the steels have the following characteristics, preferably for thicknesses i of steel sheet of approximately 2.2 cm (1 inch) and greater: (i) DBTT less than about -73 ° C (-100 ° F), preferably less than about -107 ° C (-160 ° F), in the base steel and in the welded bead; (ii) tensile strength greater than 830 MPa (120 ksi), preferably greater than about 860 MPa (125 ksi), and more preferably greater than about 900 MPa ( 130 ksi); (iii) superior weldability; (iv) microstructure and properties through substantially uniform thickness; and (v) commercially available ultra high strength, low alloy strength steels with improved toughness over the standard. Even more preferably, these steels have a tensile strength greater than about 930 MPa (135 ksi), or greater than about 965 MPa (140 ksi), or greater than about 1000 MPa (145 ksi). First Exemplary Steel As discussed in the foregoing, the co-pending provisional North American patent application having a priority date of December 19, 1997, entitled "Ultra-High Strength Steels With Excellent Cryogenic Temperature Toughness", and identified by the USPTO as Application No. 60/068194, provides a description of steels suitable for use in the present invention. One method is provided for preparing a steel plate of ultra high strength having a microstructure comprising predominantly remelted granulated fine ribbon martensite, fine granulated tempered lower bainite, or mixtures thereof, wherein the method comprises the steps of (a) ) heating a steel plate to a sufficiently high heated temperature to (i) substantially homogenize the steel plate, (ii) dissolve substantially all the niobium and vanadium carbides and nitrite in the steel plate, and (in) establish austenite grains. fine initial on the steel plate; (b) reducing the steel plate to form the steel plate in one or more hot laminations that pass in a first temperature range in which | the austenite is recrystallized; (c) further reducing the steel plate in one or more hot laminations passing in a second temperature range below approximately temperature Tnr and around approximately the transformation temperature Ar3; (d) tempering the steel plate at a cooling rate of about 10 ° C per second to about 40 ° C per second (18 ° F / sec. -72 ° F / sec.) at a Temper Stop Temperature below about the transformation temperature Ms plus 200 ° C (360 ° F); (e) stop tempering; and (f) tempering the steel plate at a tempered temperature of about 400 ° C (752 ° F) to about the Aci transformation temperature preferably up to, but not including the Aci transformation temperature, over a period of sufficient time to cause precipitation of the hardened particles, that is, one or more of the e-copper, Mo2C, or the niobium and vanadium carbides and carbonitrides. The period of time sufficient to cause the precipitation of the hardened particles depends mainly on the thickness of the steel plate, the chemistry of the steel plate and the tempering temperature, and can be determined by one skilled in the art (See Glossary for predominantly definitions of hardness particles, temperature Tnr, transformation temperatures Ar3, Ms and Aci and Mo2C). To ensure the environment and the tenacity of the cryogenic temperature, the steels according to this first exemplary steel preferably have a With a microstructure comprised of lower bainite of predominantly fine-grained fine granite, tempered granulated fine lath martensite or mixtures thereof, it is preferable to substantially minimize the formation of embrittling constituents such as upper bainite, martensite board and M. As used in the first exemplary steel and in the claims, "predominantly" means at least about 50% volume. More preferably, the microstructure comprises at least about 60 volume% to about 80 volume% of fine fine grained lower bead, tempered fine grained lath martensite, or mixtures thereof. Still more preferably, the microstructure comprises at least about 90 volume% of fine fine-grained lower bainite, tempered fine-grained lath martensite, or mixtures thereof. More preferably, the microstructure comprises substantially 100% fine tempered lath martensite. A steel plate processed in accordance with this first exemplary steel was manufactured in the customary manner and, in one embodiment, comprises iron and the following alloying elements, preferably in the weight ranges indicated in the following Table I: Table I Alloy Element Range (% by weight) carbon (C) 0.04-0.12, more preferably 0.04-0.07 manganese (Mn) 0.5-2.5, more preferably 1.0-1.8 nickel (Ni) 1.0-3.0 more preferably 1.5-2.5 copper (Cu) 0.1-1.5, more preferably 0.5-1.0 molybdenum (Mo) 0.1-0.8, more preferably 0.2-0.5 niobium (Nb) 0.02-0.1, more preferably 0.03-0.05 titanium (Ti) 0.008-0.03, more preferably 0.01- 0.02 aluminum (Al) 0.001-0.5, more preferably 0.005-0.03 nitrogen (N) 0.002-0.005, more preferably 0.002-0.003 Vanadium (V) is sometimes added to steel, preferably up to about 0.10% by weight, and more preferably from about 0.02% by weight to about 0.05% by weight. Chromium (Cr) is sometimes added to steel, preferably up to about 1.0% by weight, and more preferably from about 0.2% by weight to about 0.6% by weight. Silicon (Si) is sometimes added to steel, preferably up to about 0.5% by weight, more preferably from about 0.01% by weight to about 0.5% by weight, and even more preferably 0.05% by weight to about 0.1% by weight . Boron (B) is sometimes added to steel, from ^ * ^ - ^ * ^^ * «* ^^ - > - ^^. ^ -.- 1iTfliMM Mte ??? 1li? 1. ?? 1 ^, l > *, * d *! t * ^ - preferably up to about 0.0020% by weight, and more preferably from about 0.0006% by weight to about 0.0010% by weight. The steel preferably contains at least about 1% by weight of nickel. The nickel content of the steel can be increased by up to about 3% by weight if desired to increase the operation after welding. Every 1% by weight of nickel addition is expected to decrease the DBTT of the steel by approximately 10 ° C (18 ° F). The nickel content is preferably less than 9% by weight, more preferably less than about 6 percent by weight. The nickel content is preferably minimized to minimize the cost of the steel. If the nickel content is increased by up to about 3% by weight, the manganese content can be decreased below about 0.5% by weight below 0.0% by weight. Accordingly, in a broad sense, up to about 2.5% by weight manganese is preferred. Additionally, the residues are preferably substantially minimized in the steel. The content of Phosphorous (P) is preferably less than about 0.01% by weight. The content Sulfur (S) is preferably less than about 0.004% by weight. The content of Oxygen (O) is preferably less than about 0.002% by weight.

In a slightly greater detail, a steel according to this first example of steel is prepared by forming a plate of the desired composition as described herein; heating the plate to a temperature from about 955 ° C to about 1065 ° C (1750 ° F-19500 F); hot rolling the steel plate in one or more steps that provide about 30 percent to about 70 percent reduction in a first temperature range in which the austenite recrystallizes, i.e., up to about the temperature Tnr and further laminar heat the steel plate in one or more steps that provide reduction of about 40 percent to about 80 percent in a second temperature range below approximately the temperature of Tnr and below approximately the transformation temperature Ar3. The heat-laminated steel plate is then tempered at a cooling percentage of about 10 ° C per second to about 40 ° C per second (18 ° F / sec 72 ° F / sec) in an appropriate QST (as defined in Glossary) below approximately the transformation temperature of Ms plus 200 ° C (360 ° F), in which the tempering time is terminated. In one embodiment of this first example of steel, the steel plate is then cooled to air at room temperature. This process is used to produce a microstructure preferably comprising predominantly fine-grained martensite ribbon, lower fine-grained bainite, or mixtures thereof, or, more preferably, substantially comprises 100% fine-grained martensite lath. In this way the martensite directly turned off in steels according to this first steel example has ultra high strength but its toughness can be improved by tempering at a suitable temperature of up to about 400 ° C (752 ° F) at up to about the temperature of the Aci transformation The tempering of steel within this temperature range also leads to the reduction of extinguished tensions which in turn lead to reinforced toughness. While tempering can increase the toughness of steel, it usually leads to substantial loss of strength. In the present invention, the loss of usual resistance of the tempering is compensated for by inducing hardening of the dispersion of the precipitate. The dispersion tenacity of the fine copper precipitates and the mixed carbides and / or carbonitrides are used to optimize the strength and tenacity during tempering of the martensitic structure. The only chemistry of the steels of this first steel example allowed for tempering within the broad range of about 400 ° C to about 650 ° C (750 ° F - 1200 ° F) without any significant loss of resistance as well as off. The plate Steel is preferably tempered at an annealing temperature from about 400 ° C (752 ° F) below the Aci transformation temperature for a period of time sufficient to cause precipitation of the hardened particles (as defined herein). This process facilitates the transformation of the microstructure of the steel plate to the lath of martensite with fine-grained granules, lower bainite of finely grained granules, or the mixture thereof. Again, the sufficient period of time causes the precipitation of the particles that depend mainly on the thickness of the steel plate, the chemistry of the steel plate, and the tempering temperature, and can be determined by an experiment in the art. Second Steel Example As discussed in the above, the co-pending provisional American patent application having a priority date of December 19, 1997, entitled "Ultra-High Strength Ausaged Steels With Excellent Cryogenic Temperature Toughness", and identified by the USPTO as the Application No. 60/068252, provides a description of other steels suitable for use in the present invention. One method is provided for preparing a steel plate of ultra high strength having a micro-laminate microstructure comprising about 2% by volume a - »- ~ * * - - > '* > ~ - ~ - "- ^ n ~ - ^. ^ ia * & ri * ^: ^^^^^ - about 10% by volume of layers of austenite film and slats of approximately 90% by volume to approximately 98% by volume of predominantly fine-grained martensite and fine-grained lower bainite, the method comprises the steps of: (a) heating a steel plate to an annealed temperature sufficiently high to (i) substantially homogenizing the steel plate, ( ii) dissolve substantially all the carbides and niobium and vanadium carbonitrides in the steel plate; and (iii) establish fine initial austenite grains in the steel plate, (b) reduce the steel plate to form the steel plate. in one or more steps of hot rolling in a first temperature range in which the austenite is recrystallized, (c) further reducing the steel plate in one or more steps of hot rolling in a second temperature range below approximately the temperature Tnr and about aproximadame nte the transformation temperature Ar3; (d) temper the steel plate at a cooling rate of about 10 ° C per second to about 40 ° C per second (18 ° F / sec - 72 ° F / sec) at a Temper Stop Temperature (QST) below about the transformation temperature Ms plus 100 ° C (180 ° F) and up to about the transformation temperature Ms; and (e) stop tempering. In one embodiment, the method of this second example of steel also It comprises the step of allowing the steel plate to be cooled to the air at room temperature of the QST. In one embodiment, the method of this second steel example further comprises substantially the step of holding the plate of steel substantially and isothermally in the QST for up to about 5 minutes prior to allowing the steel plate to cool to air at room temperature. In yet another embodiment, the method of this second steel example further comprises the step of slowly cooling the steel plate of the QST at a lower speed of about 1.0 ° C per second (1.8 ° F / sec) by up to about 5 ° C. minutes before allowing the steel plate to cool to room temperature air. In yet another embodiment, the method of this invention further comprises the step of slowly cooling the steel plate of the QST at a lower speed of about 1.0 ° C per second (1.8 ° F / ség) for up to about 5 minutes before allowing that the steel plate chills the air at room temperature. This process facilitates the transformation of the microstructure from the steel plate to approximately 2% by volume to approximately 10% by volume of film layers, austenite and approximately 90% by volume slats to approximately 98% by volume of predominantly martensite. Fine grain and fine grain lower bainite. (See Glossary for definitions of temperature TnL, and of Ar3 and transformation temperatures M =. To ensure the tenacity of the ambient and cryogenic temperature, the slats in the micro-laminated structure preferably comprise predominantly lower bainite or martensite. It is preferable to substantially minimize the formation of fragilizing constituents such as bainite, matched martensite and MA. As used in this second example of steel, and in the claims, "predominantly" means at least about 50 volume percent. The rest of the microstructure can comprise additional fine-grained lower bainite, additional fine-grained martensite lath or ferrite. Most preferably, the microstructure comprises at least about 60 volume percent1 a about 80% by volume of lower bainite or martensite ribbon. Even more preferably, the microstructure comprises at least about 90 volume percent lower bainite or martensite lath. A steel plate processed according to this The second example of steel is manufactured in a customary manner and, in one embodiment, comprises steel and the following alloying elements, preferably in weight ranges indicated in the following Table II: Table II Alloy Element Range (% by weight ) rfß | jglg * íg ^ || ^ g ^? É ^ g * i «^^ Wg¡ Carbon (C) 0.04-0.12, more preferably 0.04-0.07 Manganese (Mn) 0.5-2.5, more preferablyl .0-1.8 Nickel (Ni) 1.0-3.0 more preferably 1.5-2.5 copper (Cu) 0.1-1.0, more preferably 0.2-0.5 Molybdenum (Mo) 0.1-0.8, more preferably 0.2-0.4 Niobium (Nb) 0.02-0.1, more preferably 0.02-0.05 Titanium (Ti) 0.008-0.03, more preferably 0.01-0.02! Aluminum (Al) 0.001-0.5, more preferably 0.005-0.03 Nitrogen (N) 0.002-0.005, more preferably 0.002-0.003 Chromium (Cr) is sometimes added to the steel, preferably up to about 1.0% by weight, and more preferably about 0.2% by weight to about 0.6% by weight. The Silicon (Si) is sometimes added to the steel, preferably up to about 0.5% by weight, more preferably about 0.01% by weight to about 0.5% by weight, and even more preferably 0.05% by weight to about 0.1% by weight. Boron (B) is sometimes added to steel, preferably up to about 0.0020% by weight, and more preferably about 0.0006% by weight to about 0.0010% by weight. The steel preferably contains at least about 1% by weight of nickel. The nickel content of the steel can be increased above about 3% by weight if it is desired to increase the performance after the soldier. Every 1% of the nickel addition is expected to lower the DBTT of the steel by approximately 10 ° C (18 ° F). The nickel content is preferably less than 9% by weight, more preferably less than about 6% by weight. The nickel content is preferably minimized to minimize the cost of the steel. If the nickel content is increased above about 3% by weight, the manganese content can be decreased below about 0.5% by weight below 0.0% by weight. Accordingly, in a broad sense, up to about 2.5% by weight manganese is preferred. Additionally, the residues are preferably substantially minimized in the steel. Content Phosphorous (P) is preferably less than about 0.01% by weight. The content Sulfur (S) is preferably less than about 0.004% by weight. The Oxygen (O) content is preferably less than about 0.002% by weight. In a little greater detail, a steel according to this first example of steel is prepared by forming a plate of the desired composition as described herein; heating the plate to a temperature from about 955 ° C to about 1065 ° C (1750 ° F-19500 F); laminar hot steel plate in one or more steps that SBJKgfc ^ i ^ ± ^ .i ^ ^ provide about 30 percent to about 70 percent reduction in a first temperature range at which the austenite recrystallizes, that is, up to about the temperature Tn? and further laminating the steel plate in heat in one or more steps that provide reduction from about 40 percent to about 80 percent in a second temperature range below about the temperature of Tnr and below. approximately the transformation temperature Ar3. The heat-laminated steel plate is then annealed at a cooling percentage of about 10 ° C per second to about 40 ° C per second (18 ° F / sec 72 ° F / sec) in a suitable QST below about the temperature of transformation over 100 ° C (180 ° F), in which the tempering time is over. In one embodiment of this second steel example, after quenching the steel plate is allowed to be allowed to cool to room temperature air of the QST. In another embodiment of this second steel example, after annealing, the steel plate is maintained substantially and isothermally maintained at the QST for a period of time, preferably up to about 5 minutes, and then cooled to air at room temperature. In yet another embodiment, the steel plate was cooled slowly at a slower rate than cooling to air, i.e. at a rate lower than approximately ,. ^. ^^. ^ ..... . ^^ ^^ .. & ig ga "lMiÉÉ- 8 ^ 1 ° C per second (1.8 ° F / sec), preferably about 5 minutes ha¡sta. In still another embodiment, the steel plate is cooled slowly from the QST at a slower rate than the cooled air, ie, at an even lower rate than about 1 ° C per second (1.8 ° F / sejg), preferably for up to about 5 minutes. In at least one embodiment of this second steel example, the Ms transformation temperature is about 350aC (662 ° F) and, therefore, the Ms transformation temperature plus 100 ° C (180 ° F) is approximately 450 ° C (842 ° F). The steel plate can be maintained substantially isothermal in the QST by any suitable means, as is known from those experiments in the art, such as by placing a thermal blanket on the steel plate. The plate steel can be cooled slowly after annealing. it is terminated by any suitable means, as is known to those skilled in the art, such as by placing an insulating blanket on the steel plate. Third Steel Example 20 As discussed above, the co-pending provisional North American patent application having a priority date of December 19, 1997, entitled "Ultra-High Strength Ausaged Steels With Excellent Cryogenic Temperature Toughness", and identified by the USPTO as; the Application No. 60/068816, provides a description of otjros steels suitable for use in the present invention. One method is provided to prepare a high ultraviolet strength, the double phase steel plate having a microstructure of which comprises about 10% by volume to about 40% by volume of a first phase of substantially 100% by volume (i.e. , substantially pure or "essentially") ferrite, and about 60% by volume to about 90% by volume of a second phase of martensite ribbon predominantly fine-grained and fine-grained lower bainite, or mixtures thereof, wherein the method comprises the steps of: (a) heating a steel plate to an annealed temperature sufficiently high at (i) substantially homogenizing the plate of steel, (ii) dissolve substantially all carbides and carbonitrides of niobium and vanadium in the steel plate and (iii) establish fine initial austenite grains in the steel plate; (b) reducing the steel plate to form the steel plate in one or more steps of hot rolling in a first range of The temperature at which the austenite is recrystallized; (c) further reducing the steel plate in one or more steps of hot rolling in a second temperature range below about the temperature Tpr and about about the transformation temperature Ar ^ ¡; (d) further reduce the steel plate in one or more steps of hot rolled in a third temperature range below about the transformation temperature Ari. (that is, the intercritical temperature range); (e) tempering the steel plate in a cooling range of about 10 ° C per second and about 40 ° C per second (18 ° F / sec - 72 ° F7sec) to a Tempering Delay Temperature (QST) below about the transformation temperature Ms plus 200 ° C (360 ° F) and (f) stop tempering. In another embodiment, of this third steel example, the (QST) preferably below approximately the transformation temperature Ms plus 100CC (180 ° F); and 'more preferably it should be about 350 ° C (662 ° F). In one embodiment of this third example, the steel plate is allowed to cool to air at room temperature after step (f). This process facilitates the transformation of the microstructure of the steel plate to about 10% by volume to about 40% of a first phase of ferrite and about 60% by volume to about 90% by volume of a second phase of martensite ribbon predominantly Fine grain and fine grain lower bainite. (See Glossary for the definitions of the temperature T,? R, and of Ars and Ari transformation temperatures.) To ensure the tenacity of the ambient and cryogenic temperature, the microstructure of the second phase in steels of this third example of steel comprises predominantly fine-grained bottom bamite, fine-grained martensite ribbon. It is preferable to substantially minimize the formation of embrittling constituents such as bainite, matched martensite and MA in the second phase. As used in this third example of steel, and in the claims, "predominantly" means at least about 50 volume percent. The remainder of the second phase microstructure can comprise additional fine-grained lower bainite, additional fine-grained martensite lath or ferrite. Most preferably, the microstructure comprises at least about 60 volume percent to about 80 volume percent of lower bamite or fine gauge martensite ribbon, or mixture thereof. Even more preferably, the microstructure of the second fse comprises at least about 90 volume percent fine-grained lower bainite, fine-grained martensite lath, or mixtures thereof. A steel plate processed according to this third example of steel is manufactured in a customary manner and, in one embodiment, comprises steel and the following alloying elements, preferably in weight ranges indicated in the following Table III: Table III Alloy Element Range (% by weight) Carbon (C) 0.04-0.12, more preferably 0.04-0.07 Manganese (Mn) 0.5-2.5, more preferably 1.0-1.8 Niguel (Ni) 1.0-3.0 more preferably 1.5-2.5 Niobium (Nb) ) 0.02-0.1, more preferably 0.02-0.05 Titanium (Ti) 0.008-0.03, more preferably 0.01-0.02 Aluminum (Al) 0.001-0.5, more preferably 0.005-0.03 Nitrogen (N) 0.002-0.005, more preferably 0.002-0.003 The Chromium (Cr) is sometimes added to steel, preferably up to about 1.0% by weight, and more preferably about 0.2% by weight to about 0.6% by weight. Molybdenum (Mo) is sometimes added to steel, preferably up to about 0.8% by weight, and more preferably about 0.1% by weight to about 0.3% by weight. Silicon (Si) is sometimes added to steel, preferably up to about 0.5% by weight, more preferably about 0.01% by weight to about 0.5% by weight, and even more preferably 0J 05% by weight to about 0.1% by weight . Copper (Cu) is sometimes added to steel, preferably in the range of about 0.1% by weight to about 1.0%, more preferably in the range of about 0.2% to about 0.4% by weight. Boron (B) is sometimes added to steel, - ,, .- ^^,., ^^? * ^^ ... ^ "^ t ^^ aií T ^^^ '^^^ y'i r ^ c ^ i" preferably up to about 0.0020% by weight, and more preferably about 0.0006% by weight to about 0.0010 % by weight The steel preferably contains at least about 1% by weight of nickel The nickel content of the steel can be increased above about 3% by weight if it is desired to increase the performance after welding. Nickel addition is expected to be based on the DBTT of the steel by approximately 10 ° C (18 ° F).

The nickel content is preferably less than 9% by weight, more preferably less than about 6% by weight. The nickel content is preferably minimized to minimize the cost of the steel. If the nickel content is increased above about 3% by weight, the The manganese content can be decreased below about 0.5% by weight below 0.0% by weight. Accordingly, in a broad sense, up to about 2.5% by weight manganese is preferred. Additionally, the residues are preferably substantially minimized in the steel. The content of Phosphorous (P) is preferably less than about 0.01% by weight. The content Sulfur (S) is preferably less than about 0.004% by weight. The content of Oxygen (O) is preferably less than about 0.002 % by weight.

In a little greater detail, a steel according to this first example of steel is prepared by forming a plate of the desired composition as described herein; heating the plate to a temperature from about 5,955 ° C to about 1065 ° C (1750 ° F-1950 ° F); hot rolling the steel plate in one or more steps that provide about 30 percent to about 70 percent reduction in a first temperature range at which the austenite recrystallizes, that is, up to about the temperature Tnr and further heat-laminate the steel plate in one or more passages which provide reduction from about 40 percent to about 80 percent in a second temperature range below about the temperature of TnL and below approximately the transformation temperature Ar3 and the final lamination of the steel plate in one or more steps to provide approximately a reduction of 15 percent to 50 percent in a critical temperature range below 1 of approximately the transformation temperature Ar3 and above of about the transformation temperature of / ?? The heat-laminated steel plate is then quenched at a cooling percentage of about 10 ° C per second to about 40 ° C per second (18 ° F / sec 72 ° F / sec) at a Temper Stop Temperature ( QST) Suitable preferably below approximately transformation temperature of M plus 200 ° C (360 ° F), in which the tempering time is terminated. In another embodiment I of this invention, the QST is preferably below approximately the transformation temperature of Ms plus 5 100 ° C (180 ° F), and more preferably below about 350 ° C (662 ° F). In one embodiment of this third example of steel, the steel plate is allowed to cool to air at room temperature after the quenching is completed. In the steels of example three above, since Ni is an expensive alloying element, the Ni content of the steel is preferably less than about 3.0% by weight, more preferably less than about 2.5% by weight, more preferably less than approximately 2.0% in weight, and even more preferably less than about 1.8% by weight, to substantially minimize the cost of steel. Other steels suitable for use in connection with the present invention are described in other publications describing ultra high strength, low strength steels. alloy containing less than about 1% by weight of nickel, having tensile strengths greater than 830 MPa (120 ksi), and having excellent low temperature toughness. For example, such steels are described in a European Patent Application published on February 5, 1997, and having the International application number Number: PCT / JP96 / 00157, and International publication number WO 96/23909 (08.08.1996 Gazette 1996/36) (such steels preferably have a copper content of 0.1 wt% to 1.2 wt%), and in a request for provisional patent 5 North American pending with a priority date of July 28, 1997, entitled "Ultra-High Strength, Weldable Steels with Excelent Ultra-Low Temperature Toughness", and identified by the USPTO as Application No. 60/053915. For any of the steels mentioned in above, as understood by those skilled in the art, as used herein the "reduction of 'percent in thickness" refers to the percent reduction] in the thickness of the plate or steel plate prior to the referenced reduction. For purposes only of However, without limiting this invention, a steel plate of approximately 25.4 cm (10 inches) the thickness can be reduced approximately 50% (50 percent reduction), in a first temperature range, to a thickness about 12.7 cm (5 inches) then reduced about 80% (80 percent reduction), in a second temperature range, to a thickness of about 2.5 cm (1 inch). Again, for purposes of explanation only, without limiting this invention, a steel plate of approximately 25.4 cm (10 inches) may reduce approximately 30% (30 percent of reduction), in a first temperature range, to a thickness of approximately 17.8 cm (7 inches) then reduced by approximately 80% (an 80 percent reduction), in a second temperature range, to a thickness of approximately 3.6 cm ( 1.4 inches), and then reduced approximately 30% (a 30 percent reduction), in a third temperature range, to a thickness of approximately 2.5 cm (1 inch). As used herein, "plate" means a piece of steel having any dimensions. For any of the steels referred to in the foregoing, as understood by those skilled in the art, the steel plate is preferably annealed by suitable means to raise the temperature of substantially the entire plate, preferably the entire plate, to the desired annealed temperature , for example, by placing the plate in an oven for a period of time. The specific annealing temperature to be used for any steel compositions mentioned in the foregoing can be determined quickly by a person skilled in the art, either by experiment or by calculation using suitable models. Additionally, the temperature of the oven and the necessary annealing time increases the temperature of substantially the entire plate, preferably the entire plate, the desired recycling temperature can be quickly determined by a person skilled in the art by reference to standard industrial publications. For any of the steels mentioned in the foregoing, as understood by those skilled in the art, the temperature which defines the boundary between the range of recpstalization and the range without recrystallization, the temperature of Tnr, depends on the chemistry of the steel , and more particularly, in the annealing temperature before rolling, the concentration of carbon, the concentration of the niobium and the amount of reduction given in the rolling steps. Those skilled in the art can determine this temperature for each steel composition either by experiment or by exemplary calculation. Likewise, the Aci, ri, Ars, and the Ms 5 transformation temperatures mentioned may be determined herein by persons skilled in the art for each steel composition either by experiment or by exemplary calculation. For any of the steels mentioned in the above, as understood by those skilled in the art, except for the annealing temperature, which is applied to substantially the entire plate, the aforementioned subsequent temperatures described in the description of the processing methods of this invention are temperatures measured at the surface of steel. The temperature of the steel surface can be measured by the use of a optical pyrometer, for example, or by any other device suitable for measuring the temperature of the steel surface. The freezing speeds referred to herein are those at the center, or substantially at the center, of the thickness of the plate; and the Tempering Detection Temperature (QST) is the highest, or substantially the highest, temperature reached at the plate surface, after quenching, due to the heat transmitted from the average thickness of the plate . By For example, during the processing of the experimental temperatures of a steel composition according to these examples provided herein, a thermocouple is placed at the center, or substantially in the center, of the thickness of the steel plate to measure the temperature of the center, while the surface temperature is measured by the use of an optical pyrometer. A correlation between the center temperature and the surface temperature is developed by use during the subsequent processing thereof, or substantially the same, the composition of steel, such center temperature can be determined by direct measurement of the surface temperature. Also, the required temperature and flow rate of the quenching fluid to achieve the desired accelerated cooling rate can be determined by one skilled in the art. technique by reference to industry publications standards A person skilled in the art has the requisite knowledge and ability to use the information provided herein to produce the sheets of ultra high strength, low alloy steel having high strength and toughness suitable for use in the construction of the components, containers and pipes of the process of the present invention. Other suitable steels may exist or may be developed from now on. All steels are within the scope of the present invention. A person skilled in the art has the requisite knowledge and ability to use the information provided herein to produce steel plates of ultra high strength, low alloy have modified thicknesses, compared to the thicknesses of the steel plates produced according to the examples provided herein, while still producing steel plates which have adequate high strength and the toughness of Suitable cryogenic temperature for use in the present invention. For example, a person skilled in the art can use the information provided herein to produce a steel plate with a thickness of approximately 2.54 cm (1 inch) and adequate high strength and toughness cryogenic temperature suitable for use in the construction of the components, containers, and pipes of the process of the present invention. Other suitable steels may exist or may be developed from now on. All steels are within the scope of the present invention. When a double-phase steel is used in the construction of the components, containers, and process pipes according to this invention, the double-phase steel is preferably processed in such a way that the period of The time during which the steel is maintained in the intercritical temperature range for the purpose of creating the double phase structure occurs before the accelerated cooling or the tempering step. Preferably the process is such that the double phase structure is formed during the steel cooling between the transformation temperature Ar3 at approximately the Ari transformation temperature. A further preference for the steels used in the construction of the components, containers, and pipes, of the process according to this invention is that the steel has a tensile strength greater than 830 MPa (120 ksi) and; A DBTT of less than about -73 ° C (-100 ° F) in the accelerated cooling finish or tempering step is to finish, without any additional process that requires annealing of the steel such as tempering. More preferably, the tensile strength of the steel in the performance of the tempered or the cooling step is greater than about 860 MPa (125 ksi), and more preferably greater than about 900 MPa (130 ksi). In some applications, a steel has a tensile strength greater than about 930 MPa (135 ksi), or greater than about 965 MPa (140 ksi), or greater than about 1000 MPa (145 ksi), in the performance of the stage Cooling or tempering is preferable. Methods of Union for the Construction of Components, Containers, and Process Pipes To build the components, containers, and pipes of the process of the present invention, a suitable method is required to join the steel plates. Any joining method that will provide seams or seams with adequate strength and tenacity by the present invention, as discussed in the foregoing, is considered to be adequate. Preferably, a suitable welding method to provide fracture toughness and toughness to contain the fluid being contained or transported is used to construct the components, containers, and pipes of the process of the present invention. Such a welding method preferably includes a suitable consumable wire, a suitable consumable gas, a suitable welding process, and a suitable welding process. For example, both gas metal arc welding (GMAW) and the inert gas of Tungsten (TIG) welds, which are well known in the steelmaking industry, can be used to join steel sheets, provided that a suitable consumable wire-gas combination is used. In a first example the welding method, the gas metal arc welding (GMAW) process is used to produce a weld metal chemistry comprising iron and about 0.07% by weight of carbon, about 2.05% by weight of manganese, about 0.32% by weight of silicon, about 2.20% by weight of nickel, about 0.45 'by weight of chromium, about 0.56% by weight of molybdenum, less than about 110 ppm of phosphorus, and less than about 50 ppm of sulfur. The welding is done in a steel, such as any of the steels described in the above, using a protective gas based on argon with less than about 1% by weight of oxygen. The welding heat input is in the range of approximately 0.3 kJ / mm to approximately 1.5 kJ / mm (7.6 kJ / inch to 38 kJ / inch). Welding by this method provides a weld (see Glry) having a tensile strength greater than about 900 MPa (130 ksi), preferably greater than about 930 MPa (135 ksi), more preferably greater than about 965 MPa (140 ksi), and even more preferably at least about 1000 MPa (145 ksi). Furthermore, welding by this method provides a weld metal with DBTT below about -73 ° C (-100 ° F), preferably below about -96 ° C (-140 ° F), more preferably below about 5 -106 ° C (-160 ° F), and even more preferably below about -115 ° C (-175 ° F). In another example of the welding method, the GMAW process is used to produce a weld metal chemistry comprising iron and about 0.10% by weight of Carbon (preferably less than about 0.10% by weight of carbon, more preferably from about 0.07 to about 0.08% by weight of carbon), about 1.60% by weight of manganese, about 0.25% by weight of silicone, about 1.87% by weight nickel weight, about 0.87% by weight of chromium, about 0.51% by weight of molybdenum, less than about 75 ppm of phosphorus, and less than about 100 ppm of sulfur. The welding heat input is in the range of approximately 0.3 kJ / mm to approximately 1.5 kJ / rn (7.6) kJ / inch to 38 kJ / inch) and a preheat of approximately 100 ° C (212 ° F) is used. The weld is made on a steel, such as any of the steels described above, using a protective gas based on argon with less than about 1% by weight oxygen. Welding for this Method is provided a soldier who has a resistance to the tension greater than about 900 MPa (130 ks, i), preferably greater than about 930 MPa (135 ksi), more preferably greater than about 965 MPa (140 ksi), and even more preferably at least about 1000 MPa (145 ksi) ). Furthermore, this method provides welding weld metal a DBTT below about -73 ° C (-100 ° F), preferably below about -96 ° C (-140 ° F), more preferably below about -106 ° C (-160 ° F), and even more preferably below about -115 ° C (-175 ° F). In another example of the welding method, the tungsten inert gas (TIG) welding process is used to produce a weld metal chemistry containing iron and about 0.07 7, by weight of carbon (preferably less than about 0.07 by weight). carbon), about 1.80% by weight of manganese, about 0.20% by weight of silicon, about 4.00% by weight of nickel, about 0.5% by weight of chromium, about 0.40% by weight of molybdenum, about 0.02% by weight of copper about 0.02 wt% aluminum, about 0.010 wt% titanium, about 0.015 wt% zirconium (Zr), less than about 50 ppm phosphorous, and less than about 30 ppm sulfur. The welding heat input is in the range of approximately 0.3 kJ / mm to ^ ^^ ^ ,, ^, -.... ^ ^ Sl ^ to Eis * ^^ about 1.5 kJ / mm (7.6 kJ / inch to 38 kJ / pulgada¡) and prerecocido of about 100 ° C (212 ° F) is used. The welding is done in steel, such as any of the steels described in the above, using a protective gas based on argon with less than about 1% by weight of oxygen. Welding by this method provides a weld having a tensile strength greater than about 900 MPa (130 ksi), preferably greater than about 930 MPa (135 ksi), more preferably greater than about 965 MPa (140 ksi), and further preferably at least about 1000 MPa (145 ksi). In addition, welding by this method provides a welded metal with a DBTT below approximately -73 ° C (-100 ° F), preferably below! about -96 ° C (-140 ° F), more preferably below about -106 ° C (-160 ° F), and even more preferably below about -115 ° C (-175 ° F). Welded metal chemistries similar to those mentioned in the examples can be made using any of the GMAW or TIG welding processes. However, TIG welds are anticipated to have lower impurity content and more highly refined microstructure than GMAW solders, and thus improve the low temperature toughness. A person skilled in the art has the required knowledge and ability to use the information provided herein to weld steel plates ultra high, low alloy to produce joints or seams having suitable high strength and fracture toughness for use in building components, containers, and pipes of the process of this resistance invention. Other suitable joining or welding methods may exist or be developed from now on. All jointing or welding methods are within the scope of the present invention. Construction of Components, Containers, and Pipes Process components, containers, and process piping constructed of materials comprising steel ultra high, low alloy containing less than 9 wt% nickel resistance and have resistance higher voltage that 830 MPa (120 ksi) and DBTTs lower than approximately -73 ° C (-100 ° F) is provided. Preferably ultra high strength steel, low alloy contains less than about 7% by weight of nickel, and more preferably contains less than about 5% by weight nickel. Preferably ultra high strength, low alloy steel has a tensile strength greater than about 860 MPa (125 ksi), and more preferably greater than about 900 MPa (130 ksi). Even more preferably, the ¿G a «< The components, containers, and pipes of the process of this invention of the materials comprising an ultra high strength steel , low alloy containing less than about 3% by weight of nickel and having a tensile strength exceeding approximately 1000 MPa (145 ksi) and a DBTT lower than approximately -73 ° C (-100 ° F). The components, containers, and pipes of the process of this invention are preferably constructed from discrete steel plates of ultra high strength, low alloy with excellent cryogenic temperature toughness. The seams or seams of the components, containers and pipes preferably have approximately the same strength and toughness as steel plates of ultra high strength, alloy. In some cases, one of less resistance than the resistance plate in the order of approximately 5% > to approximately 10% can be justified by the locations of the lowest resistance. Joints or seams with the preferred properties can be made by any suitable joining technique. An exemplary binding technique is described herein, under the heading "Joining Methods for Construction of Process Components, Containers and Pipes." As will be familiar to those skilled in the art. technique, the Charpy V notch test (CVN) can be used for the purpose of fracture toughness assessment and control in the design of the components, containers and pipes of the process for cryogenic temperature fluids of pressurized processing and transportation, particularly through the use of the temperature of the ductile to brittle transition (DBTT). The DBTT delineates two fracture regimes in structural steels. At temperatures below the DBTT, failure in the notch test, of Charpy tends to occur by low energy (brittle) crack fracture, while at temperatures above the DBTT, failure tends to occur by the high energy ductile fracture . The containers that are constructed of the welded steels by the cryogenic temperature service, of cargo transportation, as determined by the Charpy V notch test1, adequately below the service temperature of the structure to avoid brittle failure. Depending on the design, service conditions, and / or company requirements of the applicable classification, the required DBTT temperature change may be from 5 ° C to 30 ° C (9 ° F to 54 ° F) below the operating temperature. As will be familiar to those skilled in the art, the operating conditions taken into consideration in the design of storage containers constructed of welded steel for fluids of pressurized transportation, cryogenic, include, among other things, the pressure and temperature of operation, as well as additional stresses that will probably be imposed on the steel and the soldier (see Glossary). The measurements of standard fracture mechanics, such as (i) the critical strength intensity factor (KIC) which is a measure of flat resistance fracture toughness and (ii) crack point opening displacement (CTOD) that can used to measure the elastic-plastic fracture tenacity, Both of which are familiar to those skilled in the art, can be used to determine the toughness of the steel and weld fracture. Industrial codes generally acceptable for steel structure design, for example, as presented in the BSI publication "Guidance on methods for assensing the acceptability of flaws in welded structures", sometimes referred to as "PD 6493: 1991", can be used to determine acceptable crack sizes for containers based on the toughness of steel fracture and soldier (including HAZ) and the tension imposed on the container. A person skilled in the art can develop a fracture control program to mitigate fracture initiation through (i) the design of the container appropriate to the minimized imposed stress, (ii) the quality control of the fracture. adequate manufacture to minimize defects, (iii) the ^ ate, ttatfc- * J * a ^, UM - "'a ^' '* - ^ -' - ¿^ ^ ^ ^ appropriate control of life cycle pressures and loads applied to the container, and (iv) a inspection program suitable for discovering flaws and defects confidently detected in the container A preferred design philosophy for the system of the present invention is "the leak before failure", as is familiar to those skilled in the art. generally referred to herein as "known principles of fracture mechanics." 10 The following is an example without limitation of the application of these known principles of fracture mechanics in a method for calculating depth of critical failure by a length of failure given by use in a fracture control plan to prevent the initiation of fracture in a pressure vessel, such as a container of the process according to this invention. Figure 13B illustrates a fault 315 fault failure and failure depth 310. PD6493 is used for the values calculated by the fault measurement diagram 300 criticism shown in Figure 13A based on the following design conditions for the pressurized container, such as a container according to this invention: Container diameter: 4.57 m (15 feet) Wall thickness of the container: 25.4 m (1.00 m) pul) Design Pressure: 3445 kPa (500 psi) Acceptable Hoop Resistance: 333 MPa (48.3 ksi) Assumed for the purpose of this example, a surface failure length of 100 mm (4 inches), for example, an axial fault located in the seam weld. 5 Referring now to Figurta 13A, diagram 300 shows the value for critical failure depth as a function of fracture toughness CTOD and residual stress, for residual stress levels of 15, 50 and, 100 percent of performance tension. They can be generated residual stresses due to manufacturing and welding; and PD6493 recommends the use of a residual stress value of 100 percent welding performance tension (including HAZ welding) unless the welds are discharged stresses using techniques such as treatment heat column welding (PWHT) or mechanical stress relief. Based on the fracture toughness CTOD of the steel at the minimum service temperature, container manufacture can be adjusted to reduce stress Residual and an inspection program can be implemented (for the initial inspection and in-service inspection) to detect and measure faults for comparison against the size of the critical failure. In this example, if the steel has a CTOD tenacity of 0.025 mm at the service temperature minimum (as measured using laboratory specimens) "* * &^ '8 ^ vu &tmi *» - - .- ^ - ^ - ^ -j1lffÉÉiJB ^ and the residual stresses are reduced to 15 percent of the steel's yield strength, when the value for the depth of critical failure is approximately 4 mm (see point 320 in Figure 13A) Following similar calculation procedures, as are well known to those skilled in the art, critical failure depths can be determined for various failure lengths as well. as several fault geometries, using this information, a quality control program and inspection program (techniques, detctable failure dimensions, frequency) can be developed to ensure that the flaws detected and remedied before reach the depth of the critical failure or before the application of design loads. Based on published empirical correlations between CVN, K? C and CTOD fracture tensions, CTOD tensions of 0.025 mm generally correlate to a CVN value of about 37 J. This example is not intended to limit this invention in any way. For components, containers and pipes of the The process requiring steel inflection, for example, in a cylindrical shape for a container or in tubular form for a pipe, the steel is preferably bent into the desired shape at room temperature to avoid damaging the cryogenic temperature toughness. excellent of steel. If the steel must be heated to achieve The desired shape after bending, the steel is preferably heated to a temperature no greater than about 600 ° C (1112 ° F) to preserve the beneficial effects of the steel microstructure as described above. Cryogenic Process Components The process components constructed of materials comprising an ultra high strength, low alloy steel containing less than 9% by weight of nickel and have tensile strength greater than 830 MPa (120 ksi) and lower DBTTs that approximately -73 ° C (-100 ° F) are provided. Preferably the high alloy, low alloy strength steel contains less than about 7 wt.% Nickel, and more preferably contains less than about 5 wt.% Nickel. Preferably the ultra high strength, low alloy steel has a tensile strength greater than about 860 MPa (125 ksi), and more preferably greater than about 900 MPa (130 ksi). Even more preferably, the process components of this invention are constructed of materials comprising ultra high strength steel, low alloy containing less than about 3 wt.% Nickel and having a tensile strength exceeding above 1000 MPa. (145 ksi) and DBTT less than about -73 ° C (-100 ° F). Such process components are preferably constructed from the ultra high strength steel, the low alloy with excellent cryogenic temperature toughness described herein. In the cryogenic temperature energy generation cycles, the components of the primary process include, for example, condensers, pump systems, vaporizers, and evaporators. In refrigeration systems, liquefaction systems, and air separation plants, the components of the primary process include, for example, heat exchangers, columns, separator and expansion valves or process turbines. Signal systems are often subjected to cryogenic temperatures, for example, when used in relief systems for ethylene or natural gas in a low temperature separation process. Figure 1 illustrates some of these components that are used in a demethane gas plant and are further discussed in the following. Without thereby limiting this invention, the particular components, constructed in accordance with the present invention, are described in greater detail in the following. Heat Exchangers Heat exchangers, or heat exchanger systems constructed in accordance with this invention, are provided. The components of such heat exchange systems are preferably constructed of ultra high strength, low alloy steels with excellent cryogenic temperature toughness as described herein. Without thereby limiting this invention, the following examples illustrate various types of heat exchange systems according to this invention. For example, Figure 2 illustrates a sheet for fixed pipe, the single pass heat exchanger system 20 includes the heat exchanger body 20a, channel covers 21a and 21b, a pipe sheet 22 (the header of pipe sheet 22 shown in Figure 2), a vent 23, a diverter 24, a drain 25, a pipe inlet 26, a pipe outlet 27, a shell inlet 28, and shell outlet 29. Without limiting therefore this invention, the following example applications illustrate the advantageous utility of the fixed pipe sheet, the single pass heat exchanger system 20 according to the present invention. Example No. 1 of Fixed Tube Plate In a first application example, the fixed tube plate, the single pass heat exchanger system 20 is used as a gas inlet cross exchanger in a cryogenic gas plant with demethanized vapors on the side of the wall and the gas inlet in the tube plate. The gas inlet enters fixed to the tube plate, the pass-through heat exchanger system simple through the tube inlet 26 and exits through the tube outlet 27, while the fluid from the demethanized leaving vapors enters through the inlet 28 of the wall and out through the wall outlet 29. Example No. 2 of Fixed Tube Plate In a second application example, a single-pass heat exchanger system, of fixed tube plate, is used as a secondary kettle in a freezing demetallizer with pre-cooled feed on the tube side and the liquids of the secondary current of the cryogenic column boiling on the side of the body to eliminate methane from the bottoms of the product. The precooled feed enters the single pass heat exchanger system, of fixed pipe plate, through the pipe inlet 26 and exits through the outlet of the pipe 27, while the secondary stream liquids of the column cryogenics enter through the inlet of the body 28 and exit through the outlet of the body 29. Example No. 3 of Fixed Tube Plate In another application example, a single pass heat exchanger system is used. fixed tube, it is used as a secondary kettle in a column; product recovery Ryan Holmes to eliminate methane and C02 of the product funds. A precooled feed enters a heat exchanger system 1 of single passage of pipe plate fi through the inlet of the tube 26 and exits through the outlet of the tube 27, while liquids of the secondary stream of the cryogenic tower enter through the entrance of the body 28 and exit at through the outlet of the body 29. Example No. 4 of Fixed Tube Plate In another application example, a single-pass heat exchanger system 20 was used, fixed as a secondary boiler in a disposal column. of C02 CFZ with a secondary stream of cryogenic liquid on the side of the body and pre-cooled feed gas on the side of the tube to remove methane and other hydrocarbons from the product bottoms rich in C02. The precooled feed enters the single-pass heat exchanger system of fixed pipe plate through the inlet of the pipe 26 and exits through the outlet of the pipe 27, while a secondary stream of cryogenic liquid enters through the pipe. entrance of the body and exits through the exit 29 of the body. In Examples Nos. 1-4, of fixed tube plate, the heat exchanger body 20a, channel covers 21a and 21b, tube plate 22, vent 23, and deflection plates 24 are preferably constructed of steels containing less about 3% by weight of nickel and has adequate strength and fracture toughness to contain the cryogenic temperature fluid that is being processed and more preferably are constructed of steels containing less than about 3% nickel and having strengths to the voltage exceeding approximately 1000 MPa (145 ksi) and DBTT less than approximately -73 ° C (-100 ° F). In addition, the heat exchanger body 20a, channel covers 21a and 21b, tube plate 22, vent 23 and deflection plates 24 are preferably constructed of steels of ultra high strength, low alloy with excellent tenacity at cryogenic temperature as described herein . Other components of the single-pass fixed plate heat exchanger system can also be constructed of ultra high strength, low alloy steels with excellent cryogenic temperature toughness as described herein, or other suitable materials. Figure 3 illustrates a boiler kettle heat exchanger system 30 according to the present invention. In one embodiment, the boiler kettle heat exchanger system 30 includes a boiler kettle body 31, a moldboard 32, a heat exchanger tube 33, a tube side inlet 34, a tube side outlet 35, an inlet to the boiler 36, an outlet of the boiler 37, and a drain 38. Without thereby limiting this invention, the following application examples illustrate the advantageous utility of a heat exchanger system boiler kettle according to the invention. present invention. Example No. 1 Boiler Kettle In a first example, the boiler kettle heat exchanger system 30 is used in a cryogenic gas liquid recovery plant with propane vaporizing at about -40 ° C (-40 ° F) on the boiler and hydrocarbon gas on the side of the pipe. The hydrocarbon gases enter the boiler heat exchanger system 30 through the inlet 34 of the pipe side 10 and exit through the pipe side outlet 35, while the propane enters through the inlet 36. of boiler and goes out through boiler outlet 37. Example No. 2 Boiler Kettle In a second example, boiler kettle heat exchanger system 15 is used in an oil plant without propane grease vaporizing at about -40 ° C (-40 ° F) on the side of the boiler. boiler and oil without fat on the side of the tube. The fat-free oil enters the boiler heat exchanger 30 system through the tube inlet 34 and exits through the tube outlet 35, while the propane enters through the boiler inlet 36 and exits at through boiler outlet 37. Example No. 3 Boiler Kettle 25 In another example, the exchanger system 30 Boiler kettle heat is used in a Ryan Holmes product recovery column with propane vaporizing at approximately -40 ° C (-40 ° F) from the boiler side and highest gas from the product side column of the tube side to condense reflux of the tower. The highest gas from the product recovery column enters the boiler kettle heat exchanger system 30 through the inlet pipe 34 and exits through the outlet pipe 35, while the propane enters through the inlet 36 of the boiler. boiler and goes out through boiler outlet 37. Example No. 4 In another example Kettle boiler, the system 30 mtercambiador kettle reboiler heat is used in a CFZ process with refrigerant vaporizing Exxon side of the boiler and high gas CFZ tower tube side to condense liquid methane to reflow the tower and keep the C0 out of the highest methane product stream. The highest gas from the CFZ tower enters the boiler kettle heat exchanger system 30 through the pipe inlet 34 and exits through the pipe outlet 35, while the coolant enters through the boiler inlet 36 and goes out through boiler outlet 37. The refrigerant preferably comprises propylene or ethylene, as well as a mixture of any or all of the components of the group comprising methane, ethane, propane, butane, and pentane. - '^^ - 6 ^ asto-M t ?? fa ÍHßUÉ Example No. 5 Kettle Caldera In other example, the system 30 reboiler heat exchanger boiler is used as a boiler on a cryogenic demethanizer funds with product the bottoms of the side tower of the boiler and hot inlet gas or hot oil from the side of the tube to remove methane from the bottoms product. The hot inlet gas or hot oil enters the boiler kettle heat exchanger system 30 through the tube inlet 34 and exits through the tube outlet 35, while the bottom product of the tower enters through the boiler entrance 36 and exit through boiler outlet 37. Example No. 6 In another example Kettle boiler, the boiler system 30 heat exchanger boiler is used as a reboiler in a column Ryan Holmes product recovery with fund products boiler side and hot feed gas or hot oil from the side of the tube to remove methane and C02 from the product of the bottoms. The hot feed gas or hot oil enters the boiler kettle heat exchanger system 30 through the tube inlet 34 and exits through the tube outlet 35, while the bottom products enter through the boiler entry 36 and exit through boiler outlet 37.

'^ S ^ S ^ i ítíiíá ^? ^ ^ Ii Tsu íUtlu Example No. 7 In another example Kettle boiler, the boiler system 30 heat exchanger boiler is used in a tower with removal of C02 CFZ liquid funds tower 5 side of the boiler and hot feed gas or hot oil from the side of the tube to remove methane and other hydrocarbons from the liquid bottom stream rich in C02. Hot feed gas or hot oil enters the boiler heat exchanger system 30 through the tube inlet 34 and exits through the tube outlet 35, while the liquids in the bottoms of the tower enter through the boiler inlet 36 and exit through the boiler outlet 37. In Examples nos. 1-7 boiler boiler, the body 31 kettle boiler, the tube 33 heat exchanger, the weir 32, and port connections for the inlet 34 of tube outlet 35 side of the tube inlet 36 of boiler, and outlet 37 boiler preferably constructed of steels containing less than about March 20 wt% nickel and have adequate strength and fracture toughness to contain the cryogenic fluid being processed, and more preferably are constructed from steels containing less than about 3 wt% nickel and have resistances tension that exceed approximately 1000 MPa (146 ksi) and DBTT less than approximately -73 ° C (-100 ° F). In addition, the boiler kettle body 31, the heat exchanger tube 33, weir 32, and port connections for the inlet 34 of the tube side, outlet 35 of the tube side, inlet 36 of the boiler, and boiler outlet 37 they are preferably constructed of ultra high strength, low alloy steels with excellent tenacity at the cryogenic temperature described herein. Other system components 30 heat exchanger boiler can also be constructed from steels of ultra high strength, low alloy with excellent tenacity at the cryogenic temperature described herein, or other suitable materials. The design criteria and method of construction of the heat exchange systems according to this The invention is familiar to those skilled in the art, especially in view of the description provided herein. • Capacitors. Capacitors, or systems of condensation, constructed according to this invention. More particularly, condensation systems are provided, with at least one component constructed according to the invention. The components of such condensation systems are preferably constructed of ultra strength steels high, low alloy with excellent tenacity to the cryogenic temperature described herein. Without limiting this invention, the following examples illustrate various types of condensation systems according to this invention. Condenser Example No. 1 Referring to Figure 1, a condenser according to this invention is used in a gas de-metanization plant 10 in which a gas feed stream is separated into a waste gas and a product stream using a demethanizer column 11. In this particular example, the top of the demethanizer column 11, at a temperature of about -90 ° C (-130 ° F) is condensed in a reflux accumulator (separator) 15 using a condenser system 12 of reflux. The reflux condenser system 12 exchanges heat with the gaseous discharge stream of the expander 13. The reflux condenser system 12 is primarily a heat exchanger system, preferably of the types discussed above. In particular, the reflux condenser system 12 can be a single pass heat exchanger of fixed tube plate (for example, single pass heat exchanger of fixed tube plate, as illustrated in Figure 2 and described above). ). Referring again to Figure 2, the discharge current of the expander 13 enters the system 20 single plate pass heat exchanger of pipe fi x through the tube inlet 26 and exits through the tube outlet 27 while the higher demethanized enters the inlet 28 of the body and exits through the outlet 19 of the body. Condenser Example No. 2 Referring now to Figure 7, a condensation system 760 according to this invention is used in a reverse Rankine cycle to generate power using the cold energy of a cold energy source such as a pressurized liquefied natural gas (PLNG) (see Glossary) or LNG (see Glossary). In this particular example, the force fluid is used in a closed thermodynamic cycle. The force fluid, in gaseous form, expands in the turbine 72 and then is fed as a gas in the condenser system 70. The force fluid leaves the condenser system 70 as a single phase liquid and is pumped by the pump 74 and subsequently evaporated by the vaporizer 76 before returning to the inlet of the turbine 72. The condenser system 70 is primarily an exchanger system of heat, preferably of the types discussed above. In particular, the condenser system 70 may be a single-step, fixed-tube plate heat exchanger (e.g., single-pass heat exchanger system of fixed tube plate, as illustrated in Figure 2 and described above). ). jfc, a¡a¡i5lt¡f «^, rii > ^^ Referring again to Figure 2, in Examples Nos. 1 and 2 of the condenser, the heat exchanger body 20 a, channel covers 21 a and 21 b, tube plate 22, vent 23 and deflection plates 24 are constructed preferably of ultra high strength steels, high alloy containing about 3% by weight of nickel and has adequate strength and fracture toughness by cryogenic temperature to contain the cryogenic fluid being processed, and more preferably are constructed of steels of ultra high strength, low alloy containing less than about 3% by weight of nickel and having tensile strengths exceeding about 1000 MPa (145 ksi) and DBTT less than about -73 ° C (-100 ° F). In addition, heat exchanger body 20a, channel covers 21b, tube extension 22, vent 23 and deflection plates 24 are preferably constructed of ultra high strength, low alloy steels with excellent tenacity at the cryogenic temperature described in FIG. I presented. Other components of the condenser system 70 may also be constructed of ultra low strength alloy steels with excellent tenacity at the cryogenic temperature described herein, or other suitable materials. Condenser Example No. 3 Referring now to Figure 8, a condenser according to this invention is used in a cascade cooling cycle 80 which consists of several stages of compression cycles. The main items of the cascade cooling cycle 80 equipment include the propane compressor 81, the propane condenser 82, the ethylene compressor 83, the ethylene condenser 84, the methane compressor 85, the methane condenser 86, the methane evaporator 87, and 88 expansion valves. Each stage operates at successively lower temperatures by selecting a series of refrigerants with boiling points that span the temperature range required for the complete refrigeration cycle. In this example cascade cycle, the three refrigerants, propane, ethylene and methane can be used in a LNG process with the typical temperatures indicated in Figure 8. In this example, all parts of the methane condenser 86 and the condenser 84 of ethylene are preferably constructed of ultra high strength low alloy steels containing less than about 3% by weight of nickel and having adequate strength and fracture toughness by cryogenic temperature to contain the cryogenic fluid being processed, and more preferably they are constructed of ultra high strength, low alloy steels containing less than about 3 wt.% nickel and having tensile strengths exceeding approximately 1000 MPa (145 ksi) and DBTT less than about -73 ° C (-100 ° F). In addition, all parts of the methane condensate 86 and of the methane condenser 86 and of the ethylene condenser 84 are preferably constructed of steels of ultra high strength, low alloy with excellent tenacity at the cryogenic temperature described herein. Other components of the cascade cooling cycle 80 may also be constructed of ultra high strength, low alloy steels with excellent tenacity at the cryogenic temperature described herein, or other suitable materials. The design criteria and method of construction of the condensation systems according to this invention are familiar to those skilled in the art, especially in view of the description provided herein. Vaporizers / Evaporators Vaporizers / evaporators, or vaporization systems, constructed in accordance with this invention are provided. More particularly, vaporization systems are provided with at least one component constructed in accordance with this invention. The components of such vaporization systems are preferably constructed of steels of ultra high strength, low alloy with excellent tenacity at the cryogenic temperature described in ai? áa ^^ X ^! ^ present. Without thereby limiting this invention, the following examples illustrate various types of vaporization systems according to this invention. Vaporizer Example No. 1 In a first example, a vaporization system according to this invention is used in an inverse Rankine cycle to generate pressurized LNG (as defined herein) or conventional LNG (as defined herein) . In this particular example, a PLNG process stream from a storage and transport vessel is completely vaporized using the vaporizer. The heating means may be the force fluid used in a closed thermodynamic cycle, such as an inverse Rankine cycle, to generate force. Alternatively, the heating medium may consist of a simple fluid used in an open circuit to completely vaporize the PLNG, or various different fluids with successively higher freezing points used to vaporize and successively heat the PLNG at room temperature. In all cases, the vaporizer serves as the heat exchanger function, preferably of the types described in detail herein under the subheading "Heat Exchangers". The mode of application of the vaporizer and the composition and properties of the current or currents processed determine the specific type of exchanger of Lefelifc heat required. As an example, referring again to Figure 2, where a single pass heat exchanger system of fixed pipe plate is used is applicable, a current process, such as PLNG, enters a heat exchanger system 20 single passage of fixed tube plate through the inlet 26 of the tube and exits through the outlet 27 of the tube, while the heating means enters through the body inlet 28 and exits through, the outlet 29 of the body. In this example, the heat exchanger body 20a, channel covers 21a and 21b, pipe extension 22, vent 23 and deflecting plates 24 are preferably constructed of steel containing less than about 3% by weight of nickel and having strength suitable and fracture toughness to contain the cryogenic temperature fluid being processed and more preferably are constructed of steels containing less than about 3% by weight of nickel and having tensile strengths exceeding approximately 1000 MPa (145 ksi) ) and DBTT less than approximately -73 ° (-100 ° F). In addition, the body of the exchanger 20a, channel covers 21a and 21b, fixed tube plate 22, vent 23 and deflection plates 24 are preferably constructed of ultra high strength, low alloy steels with excellent tenacity at the cryogenic temperature described in the present. Other system components 20 exchanger ^ .... "». ^ Jfa ^ fe ^. ^ As ^^ ugly, ^^^ single step heat of fixed tube plate can also be constructed of ultra high strength, low alloy steels with excellent toughness to the cryogenic temperature described herein or other suitable materials. Vaporizer Example No. 2 In another example, a vaporizer according to this invention is used in a cascade cooling cycle which. It consists of several compression cycles in stages, as illustrated by Figure 9. Referring to Figure 9, each of the two compression cycles in stages of the cascade cycle 90 operates at successively lower temperatures by selecting a series of refrigerants with boiling points that cover the temperature range required for the complete refrigeration cycle. The main items of the cycle 90 cascade equipment include propane compressor 92, propane condenser 93, ethylene compressor 94, ethylene condenser 95, ethylene evaporator 96, and expansion valves 97. In this example, the two propane and ethylene refrigerants are used in a LNGP liquefaction process with the typical temperatures indicated. The ethylene evaporator 96 is preferably constructed of steels containing less than 3% by weight of nickel and have adequate strength and fracture toughness to contain the cryogenic temperature fluid that is being ,, M »gz ^. ,,? ^^^ kJí. e < ^ s ^^^^ ?. processing and more preferably is constructed of steels containing less than about 3? by weight of nickel and having a tensile strength exceeding approximately 1000 MPa (145 ksi) and a DBTT less than approximately -73 ° C (-100 ° F). In addition, the ethylene evaporator 96 is preferably constructed of ultra high strength, low alloy steels with excellent tenacity at the cryogenic temperature described herein. Other components of the cascade cycle 90 may also be constructed of steels of ultra high strength, low alloy with excellent tenacity at cryogenic temperature described herein or other suitable materials. The design criteria and method of construction of the vaporization systems according to this invention are familiar to those in the art, especially in view of the description provided herein. Separators Separators, or separator systems (i) constructed of ultra high strength, low alloy steels containing less than about 3% by weight of nickel and (n) having adequate strength and fracture toughness by cryogenic temperature to contain Cryogenic temperature fluids are provided. More particularly, the separation systems, with at least one of the components (i) constructed of resistance steels E * ~. > Maaiig > Ultra high, low alloy containing less than about 3 wt.% Nickel and (ii) having a tensile strength exceeding about 1000 MPa (145 ksi) and a DBTT less than about 73 ° C (-100 ° F) is provided. The components of such separation systems are preferably constructed of steels of ultra high strength, low alloy with excellent tenacity at the cryogenic temperature described herein. Without thereby limiting this invention, the following examples illustrate a separation systems according to this invention. Figure 4 illustrates a separation system 40 according to the present invention. In one embodiment, the separation system 40 includes a container 41, inlet port 42, liquid outlet port 43, gas outlet 44, support edge 45, liquid level control 46, bypass plate 47, carriers 48 of the fog extractor, and isolation of the deviation plate 47 and pressure relief valve 49. In an application example, without however limiting this invention, the separator system 40 according to the present invention is advantageously used as an expander feed separator in a cryogenic gas plant to remove condensed liquids upstream of the expander. In this example, the container 41, the inlet port 42, the liquid outlet port ^ A? Kdá¡m * m ^ & 43, support socket 45, extractor supports 48, and insulating baffle 47 are preferably constructed of steels containing less than about 3% by weight of nickel and having adequate strength and fracture toughness to contain cryogenic temperature fluid that it is being processed, and more preferably they are constructed of steels containing less than about 3% by weight of nickel and having tensile strength exceeding about 1000 MPa (145 ksi) and DBTT less than about minus minus -73 ° C (- 100 ° F). In addition, the container 41, inlet port 42, liquid outlet port 43, support edge 45, supports 48 of the fog extractor, and insulator deviation plate 47 are preferably constructed of ultra high strength, low alloy steels with excellent toughness at cryogenic temperature described herein. Other components of the spacer system 40 may also be constructed of ultra high strength, low alloy steels with excellent tenacity at the cryogenic temperature described herein, or other suitable materials. The design criteria and method of construction of the separation systems according to this invention are familiar to those skilled in the art., especially in view of the description provided herein. Process Columns Process columns, or process column systems, constructed in accordance with this invention are provided. The components of such process column systems are preferably constructed of ultra high strength, low alloy steels with excellent tenacity at the cryogenic temperature described herein. Without thereby limiting this invention, the following examples illustrate various types of process column systems according to this invention. Example No. 1 of Process Column Figure 11 illustrates a process column system according to the present invention. In this embodiment, a dematerizing process column system 110 includes columns 111, spacer belt 112, first inlet 113, second inlet 114, liquid outlet 121, vapor outlet 115, kettle 119, and packing 120. In one application example , without thereby limiting this invention, a process column system 110 according to the present invention is advantageously used as a demethanizer in a cryogenic gas plant to separate the methane from the other condensed hydrocarbons. In this example, column 111, separator belt 112, packing 120 and other internal materials commonly used in such a process column system 110 are preferably constructed from steels containing less than about 3 wt.% Nickel and have strength and fracture toughness suitable for containing the cryogenic temperature fluid being processed, and more preferably constructed of steels containing less than about 3% by weight of nickel and having tensile strengths exceeding approximately 1000 MPa (145 ksi) and DBTT lower than approximately -73 ° C (-100 ° F). In addition, column 111, spacer belt 112, gasket 120, and other internal materials commonly used in such process column systems 110 are preferably constructed of ultra high strength, low alloy steels with excellent tenacity at the cryogenic temperature described herein. . Other components of the process column system 110 may also be constructed of steels of ultra high strength, low alloy with excellent tenacity at the cryogenic temperature described herein, or other suitable materials. Example No. 2 of Process Column Figure 12 illustrates a process column system 125 according to the present invention. In this example, the process column system 125 is advantageously used as a CFZ tower in a CFZ process for the removal of C02 from the methane. In this example, column 126, fusion trays 127 and contact trays 128 are preferably constructed of steels containing less than - á -st i > S ^ m ^ á? ^^^^^ ^ z ^^^^^ j ^^? e-. about 3% by weight of nickel and having adequate strength and fracture toughness to contain the cryogenic temperature fluid that is being processed, and more preferably are constructed of steels containing less than about 3% by weight of nickel and having tensile strength exceeding approximately 1000 MPa (145 ksi) and DBTT less than approximately -73 ° C (-100 ° F). In addition, column 126, melting tray 127, and contact tray 128 are preferably constructed of steels of ultra high strength, low alloy with excellent tenacity at the cryogenic temperature described herein. Other components of the process column system 125 may also be constructed of ultra high strength, low alloy steels with excellent cryogenic temperature toughness described herein or other suitable materials. The design criteria and method of construction of the process columns according to this invention are familiar to those skilled in the art, especially in view of the description provided herein. Pump Systems and Components Pumps or pump systems constructed in accordance with this invention are provided. The components of such pumping systems are preferably constructed from SX? - é ^ ^ t ^ &ij ^ r - ^ eSmfí-mi ^^ iáes ^ steels of ultra high strength, low alloy with excellent tenacity at cryogenic temperature described herein. Without limiting this invention, the following examples illustrate a pump system according to this invention. Referring now to Figure 10, the pumping system 100 is constructed in accordance with this invention. The pumping system 100 is made of substantially cylindrical and plate components. A cryogenic fluid enters the cylindrical fluid inlet 101 from a tube attached to the inlet rim 102. The cryogenic fluid flows into the cylindrical liner 103 to the pump inlet 104 and into the multiple stage pump 105 where it undergoes a increase in -pressure energy. The multi-stage pump 105 and the transmission shaft 106 is supported by a cylindrical support and the pump housing support (not shown in Figure 10). The cryogenic fluid leaves the pumping system 100 through the fluid outlet 108 in a tube attached to the fluid outlet rim 109. An impeller means such as an electric motor (not shown in Figure 10) is mounted and attached to the pumping system 100 through the impeller assembly 211. The mounting of the flange 210 of the impeller is supported by the assembly of the cylindrical case 212. In this example, the pumping system 100 is mounted between the flanges of the pipe (not shown in FIG. ^^ áfeg ^^ Figure 10); but other mounting systems are also applied, such as the pumping system 100 submerged in a tank or container such that the cryogenic liquid enters directly into the fluid inlet 101 without the connecting pipe. Alternatively, the pumping system 100 is installed in another box or "pump can" where the fluid inlet 101 and the fluid outlet 108 are connected to the pump canister, and the pumping system 100 is easily removable, for maintenance or repair. In this example, the pump sleeve 213, the inlet flange 102, the impeller case assembly 212, the impeller flange 210 assembly, the flange mounting 214, the pump end plate 215, and the pump and the support of the box support 217 are all preferably constructed of steels containing less than 9% by weight of nickel and having tensile strengths greater than 830 MPa (120 ksi) and DBTT less than about -73 ° C ( -100 ° F), and more preferably are constructed of steels containing less than about 3% by weight of nickel and having tensile strengths greater than about 1000 MPa (145 ksi) and DBTT less than about -73 ° C ( -100 ° F). In addition, the pump sleeve 213, the inlet flange 102, the impeller case assembly 212, the impeller flange assembly 210, the flange assembly 214, the pump end plate 215, and the pump and support support of the box 217 are built .: ~, tÍ¿ á .i ~ > The present invention is preferably made of steels of ultra high strength, low alloy steels with excellent tenacity at the cryogenic temperature described hereinabove. Other components of the pumping system 100 may also be constructed of steels of ultra high strength low alloy strength with excellent tenacity at the cryogenic temperature described herein, or other suitable materials. The design criteria and method of construction of the components of the pump and the system according to this invention are familiar to those skilled in the art, especially in view of the description provided herein. Burner Systems and Components Burners, or burner systems, constructed in accordance with this invention are provided. The components of such burner systems are preferably constructed of steels of ultra high strength, alloy with excellent tenacity at the cryogenic temperature described herein. Without thereby limiting this invention, the following examples illustrate a burner system according to this invention. Figure 5 illustrates a burner system 50 according to the present invention. In one embodiment, the burner system includes dump valves 56, piping, such as the side pipe 53, collection header pipe 52, and burner pipe 51, and also includes a burner cleaner 54, a chimney or pump 55 of burner, a liquid drain pipe 57, a drain pump 58, a drain valve 59, and auxiliaries (not shown in Figure 5) such as lighters and purge gas. The burner system typically handles combustible fluids that are at cryogenic temperatures due to processing conditions or that cool to cryogenic temperatures upon relieving the burner system, i.e. 10 from a large pressure drop through the relief or valve valves. of download. The burner pipe 51, the collection header pipe 52, the side pipe 53, the burner cleaner 54, and any additional pipes or associated systems that could be exposed to the same cryogenic temperatures as those of the burner system 50 are all preferably constructed of steels containing less than 9% by weight of nickel and having tensile strengths greater than 830 MPa (120 ksi) and DBTT less than about 73 ° C (-100 ° F), and more preferably 20 steels are constructed having less than about 3% by weight of nickel and having tensile strengths greater than about 100 MPa (145 ksi) and DBTT less than about -73 ° C (-100 ° F). In addition, the burner pipe 51, the collection header pipe 52, the side pipe 25 53, the burner cleaner 54, and any pipeline aajgssa ^ w%. & * is < fc ^, a &'W *! - aa -? -; , Ah ^? M ^ 17 or additional associated systems that could be exposed to the same cryogenic temperatures as those of the burner system are preferably constructed of ultra high strength, low alloy steels with excellent tenacity at the cryogenic temperature described herein. Other components of the burner system can also be constructed of ultra high strength, low alloy steels with excellent tenacity at the cryogenic temperature described herein, or other suitable materials. The design criteria and method of construction of the burner components and systems according to this invention are familiar to those skilled in the art, especially in view of the description provided herein. In addition to the other advantages of this invention, as discussed above, a burner system constructed in accordance with this invention has good resistance to vibrations that may occur in burn systems when the relief speeds are high. Cryogenic Temperature Storage Containers Containers constructed of materials comprising an ultra high strength low alloy steel containing less than 9% by weight of nickel and having tensile strengths greater than 830 MPa (120 to? F & m ¥! ® ksá ksi) and DBTT less than approximately -73 ° C (-100 ° F). Preferably the low alloy ultra high strength steel contains less than about 7 wt.% Nickel and more preferably contains less than about 5 wt.% Nickel. Preferably the low alloy ultra high strength steel has a tensile strength greater than about 860 MPa (125 ksi) and more preferably greater than about 900 MPa (130 ksi). Even more preferably, the containers of this invention are constructed of materials comprising an ultra high-strength steel with an alloy containing less than about 3% by weight of nickel and having a tensile strength exceeding approximately 1000 MPa (145 ksi) and a DBTT less than about -73 ° C (-100 ° F). Such containers are preferably constructed of steels of ultra high strength, low alloy with excellent tenacity at the cryogenic temperature described herein. In addition to the other advantages of this invention, as discussed above, ie less total weight with the concomitant savings in transportation, handling, and substructure requirements, the excellent cryogenic temperature toughness of the storage containers of this invention are especially advantageous for cylinders that are frequently handled and transported for fill, such as the Co2 storage cylinders used in the food and beverage industry. Recently have industry plans been announced to make massive sales of CO? at low temperatures to avoid the high pressure of the compressed gas. The storage containers and cylinders according to this invention can be advantageously used to store and transport liquefied C02 under optimum conditions. The design criteria and the method of construction of containers for the storage of fluids at cryogenic temperature according to this invention are familiar to those in the art, especially in view of the description provided herein. Pipes Flow pipe distribution network systems are provided constructed of materials comprising an ultra high strength low alloy steel with less than 9 wt.% Nickel and having tensile strengths greater than 830 MPa (120 ksi) and DBTT less than approximately -73 ° C (-100 ° F). Preferably the low alloy ultra high strength steel contains less than about 7% by weight of nickel and more preferably contains less than about 5% by weight of nickel. Preferably the ultra high strength low alloy steel has a higher tensile strength than about 860 MPa (125 ksi), and more preferably greater than about 900 MPa (130 ksi) even more preferably, the pipes of the flow pipe distribution network system of this invention are constructed of materials comprising an ultra steel high low alloy strength containing less than about 3 wt.% nickel and having a tensile strength exceeding about 1000 MPa (145 ksi) and a DBTT less than about -73 ° C (-100 ° F). Such pipes are preferably constructed of steels of ultra high strength, low alloy with excellent tenacity at the cryogenic temperature described herein. Figure 6 illustrates a pipe network distribution system 60 according to the present invention. In one embodiment, the flow pipe distribution network system 60 includes pipes, such as primary distribution pipe 61, secondary distribution pipe 62, and tertiary distribution pipe 63, and includes main storage vessels 64, and containers 65. storage for final use. The main storage containers 64 and the storage containers 65 for final use are all designed for cryogenic service, ie, proper insulation is provided. Any suitable type of insulation can be used, for example, without thereby limiting this invention, high vacuum insulation, expanded foam, gas filled powders and fibrous materials, eviction powders or multi-stage insulation. The selection of an appropriate insulation depends on the performance requirements, as is familiar to those skilled in the cryogenic engineering art. The main storage containers 64, pipe, such as primary distribution pipe 61, secondary distribution pipe 62 and tertiary distribution pipes 63, and storage container 65 for final use are preferably constructed of steels containing less than 9% by weight of nickel and having tensile strengths greater than 830 MPa (120 ksi) and lower DBTT approximately -73 ° C (-100 ° F) and more They are preferably constructed of steels containing less than about 3% by weight of nickel and having tensile strengths greater than about 1000 MPa (145 ksi) and DBTT less than about -73 ° C (-100 ° F). In addition, the main storage containers 64, pipe, such as primary distribution pipe 61, secondary distribution pipe 62, and tertiary distribution pipe 63, and storage container 65 for final use are preferably constructed of ultra high strength, low alloy steels with excellent tenacity at the cryogenic temperature described in ^! S &^^^^^^^^^ g¡ * faffi ^^^^^ tó & ¡^^^^^^^^ ¡** ^ - ^ «fe ^ ¡^^^^^^^^ jj ^^^^ jjj ^^^^^^ i ^^^^^^ ü present. Other components of the distribution network system 60 may be constructed of ultra high strength, low alloy strength steels with excellent cryogenic temperature toughness described herein or other suitable materials. The ability to distribute fluids that are used in the cryogenic temperature condition through a network distribution pipeline system allows smaller containers in their natural place than would be necessary if the fluid were transported by means of a car. tank or railway. The main advantage is a reduction in storage required due to the fact that there is continuous feeding, rather than periodic delivery, of pressurized fluid at cryogenic temperature. The design criteria and method of construction of pipes for distribution pipeline network systems for cryogenic temperature fluids according to this invention are familiar to those skilled in the art, especially in view of the description provided herein . The process components, containers, and pipes of this invention are advantageously used to contain and transport pressurized fluids at cryogenic temperature or cryogenic temperature fluids at atmospheric pressure. Additionally, the components of the process, Atheikh ^ agaegy ^ liiiah containers, and pipes of this invention are advantageously used to contain and transport pressurized fluids at non-cryogenic temperature. While the above invention has been described in terms of one or more preferred embodiments, it should be understood that other modifications may be made without departing from the scope of the invention, which is set forth in the following claims. . -afaa¿¿ ^ b ^^ f ^^^^ L- ^ u ^^ e ^ Glossary of Terms trans temperature the temperature at which the austenite Aci formation begins to form during the heating temperature of transformation the temperature at which the Ac3 transformation of ferrite to austemta is completed during heating transformation temperature the temperature at which the Ari transformation of the austemta to ferrite or cementite plus of ferpta is completed during the heating temperature of the transformation temperature at which the Ar. austemta begins to transform to ferrite during CFZ heating controlled freezing zone; Conventional LNG Liquefied natural gas at approximately atmospheric pressure and approximately -162 ° C (-260 ° F); cooling speed cooling speed in the center, or substantially in the center, or the thickness of the cryogenic temperature plate any temperature lower than approximately -40 ° C (-40 ° F) CTOD crack tip opening displacement (DBTT) (Temperature delineates the two Ductile Transition regimes to fracture in brittle steels): structural; At DBTT bath temperatures, failure tends to occur by split fracture (break) of the energy, while at temperatures of about DBTT, failure tends to occur due to high-energy ductile fracture; essentially Substantially 100% by volume GMAW: gas metal arc welding Hardened particles one or more of e-copper, Mo2C or the carbides and carbomtrides . - ^.-.- ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^ ^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^^ temperature range of about the micromitric: transformation temperature Aci at about the transformation temperature Ac3 in heating, and from about the transformation temperature Ar3 to about the transformation temperature Ari in cooling; KIC: critical stress intensity factor; KJ: kilo oule; alloy steel a steel containing iron and less than about 10% by weight total alloy additives; MA: martensite-austenite; crack size maximum depth and length of allowed: critical fissure; Mo2C: a form of molybdenum carbide transformation temperature the temperature at which the M transformation from austemta to mertensite starts during cooling; liquefied natural gas liquefied natural gas to a pressurized (PLNG) pressure of about 1035 kPa (150 psia) to about 7590 kPa (1100 psia) and at a temperature of about -123 ° C (-190 ° F) to about -62 ° C (-80 ° F); ppm parts per million predominantly at least about 50 volume percent; tempered cooling accelerated by any means whereby a fluid selected for its tendency to increase the cooling rate of the steel, as opposed to air cooling; Stopping Temperature of the highest, or substantially Temper (QST): the highest, temperature reached on the surface of - < "•. * A« A? «A ^ *» fcSfa the plate, after quenching stops, due to the temperature transmitted from the average thickness of the plate, QST Tempering Stop Temperature, plate: a piece of steel having any tensile strength dimensions in the tensile test, the ratio of the maximum load to the original cross-sectional area; TIG welding: inert gas welding of tungsten; Temperature Tnr: the temperature below which the austemta does not USPTO: United States Patent and Trademark office is recrystallized, and welded a welded joint, which includes: (i) the welded metal, (11) the affected heating zone (HAZ) and (m) the metal base in the "close proximity" of the HAZ The portion of the base metal that is considered within the "close proximity" of the HAZ and therefore a part of the weld, varies depending on the factors known to those skilled in the art. , for example, without limitation ion, the width of the weld, the size of the point to be welded, the number of welds required to make it and the distance between the weld.

Claims (16)

1. CLAIMS 1. A heat exchanger system characterized in that it comprises: (a) a heat exchanger body suitable for containing a fluid at a pressure greater than about 1035 kPa (150 psia) and a temperature less than about -40 ° C (-) 40 ° F), the heat exchanger body being constructed by joining together a plurality of discrete sheets of materials comprising 10 an ultra high strength steel, alloy less than 9% by weight nickel and having a tensile strength greater than 830 MPa (120 ksi) and a DBTT less than about -73 ° C (-100 ° F) ), where the joints between the discrete plates have adequate strength and tenacity in 15 the conditions of pressure and temperature to contain the presupposed fluid; and (b) a plurality of deflection plates.
2. 2. A heat exchanger system characterized in that it comprises: (a) a heat exchanger body suitable for containing liquefied natural gas priced at a pressure of about 1035 kPa (150 psia) to about 7590 kPa (1100 psia) and at a temperature of approximately -123 ° C (-190 ° F) to approximately -62 ° C (-80 ° F), the body 25 heat exchanger being constructed by union together with a plurality of discrete sheets of materials comprising a steel of ultra high strength, low alloy containing at least 9% by weight of nickel and having a tensile strength greater than 830 MPa (120 5 ksi) and a DBTT less than about -73 ° C (-100 ° F), where the joints between the discrete sheets have adequate strength and toughness under pressure and temperature conditions to contain the pressurized liquefied natural gas; and 10 (b) a plurality of deflection plates.
3. 3. A condenser system characterized in that it comprises: (a) a condenser vessel suitable for containing a fluid at a pressure greater than about 15 1035 kPa (150 psia) and a temperature of less than about -40 ° C (-40 ° F), the container container being constructed by joining together a plurality of discrete sheets of materials comprising a steel of ultra high strength, low alloy that contains so At least 9% by weight of nickel and having a tensile strength greater than 830 MPa (120 ksi) and a DBTT less than about -73 ° C (-100 ° F), wherein the joints between the discrete plates have adequate strength and tenacity under pressure and temperature conditions to contain the 25 presupposed fluid; Y (b) heat exchanger means.
4. A vaporizer system characterized in that it comprises: (a) a vapor vessel suitable for containing a fluid at a pressure greater than about 1035 kPa (150 psia) and a temperature less than about -40 ° C (-40 ° F) , the vaporizer vessel being constructed by joining together a plurality of discrete sheets of materials comprising a steel of high ultra strength, with an alloy containing at least 9% by weight of nickel and having a higher tensile strength. that 830 MPa (120 ksi) and a DBTT less than about -73 ° C (-100 ° F), where the joints between the discrete plates have adequate strength and tenacity under the conditions of pressure and temperature to contain the pressurized fluid; and (b) heat exchange media.
5. A spacer system characterized in that it comprises: (a) a separator vessel suitable for containing a fluid at a pressure greater than about 1035 kPa (150 psia) and a temperature less than about -40 ° C (-40 ° F), the separator vessel being constructed by joining together a plurality of discrete sheets of materials comprising a high strength steel, with an alloy containing less than 9% by weight of ¿Ajte Sd É *: At. * a? sSÍk * i a. ^^^^^^^ i ^ gj ^ fetoa ^ Afes ^^ Ag atife nickel and having a tensile strength greater than 830 MPa (120 ksi) and a DBTT less than approximately - 73 ° C (-100 ° F), where the joints between the discrete plates have adequate strength and tenacity under pressure and temperature conditions to contain the pressurized fluid; and (b) at least one isolated deflection plate.
6. 6. A separator system characterized in that it comprises: (a) a separator vessel body suitable for containing a pressurized liquefied natural gas at a pressure of about 1035 kPa (150 psia) to about 7590 kPa (1100 psia) and at a temperature of about -123 ° C X190 ° F) at about -62 ° C (-80 ° F), the separating vessel being constructed by bonding together a plurality of discrete sheets of materials comprising a steel of ultra high strength, with a minor alloy containing at least 9% by weight of nickel and having a tensile strength greater than 830 MPa (120 ksi) and a DBTT less than about -73 ° C (-100 ° F), where the joints between the discrete plates have adequate strength and tenacity under pressure and temperature conditions to contain the pressurized liquefied natural gas; and (b) at least one isolated deflection plate.
7. 7. A process column system characterized because it comprises: (a) a process column suitable for containing a fluid at a pressure greater than approximately 1035 kPa (150 psia) and a temperature less than approximately -40 ° C (-40 ° F), the process column being constructed by joining together a plurality of discrete sheets of materials comprising an ultra high strength, low alloy steel containing less than 9% by weight of nickel and having a tensile strength greater than 830 MPa (120 ksi) and a DBTT less than about -73 ° C (-100 ° F), where the joints between the discrete sheets have adequate strength and tenacity under the conditions of pressure and temperature to contain the pressurized fluid; Y (b) pack.
8. 8. A process column system characterized in that it comprises: (a) a process column suitable for containing liquefied natural gas priced at a pressure of about 1035 kPa (150 psia) to about 7590 kPa (1100 psi) and at a temperature of about -123 ° C (190 ° F) to about -62 ° C (-80 ° F), the process column being constructed by joining together with a plurality of discrete sheets of materials comprising a steel of ultra high strength, ba minor alloy containing less 9% by weight of nickel and having a tensile strength greater than 830 MPa (120 ksi) and a DBTT less than about -73 ° C (-100 ° F), wherein the joints between the Discrete plates have resistance1 and adequate tenacity under pressure and temperature conditions to contain LNG; and (b) pack.
9. 9. A pump system characterized in that it comprises: (a) a pump box suitable for containing a fluid at a pressure greater than about 1035 kPa (150 psia) and a temperature less than about -40 ° C (-40 ° F) , the pump housing being constructed by joining together a plurality of discrete sheets of materials comprising ultra high strength, low alloy steel containing less than 9 wt.% nickel and having a tensile strength greater than 830. MPa (120 ksi) and a DBTT less than about -73 ° C (-100 ° F), where the joints between the discrete plates have adequate strength and tenacity under the conditions of pressure and temperature to contain the pressurized fluid; and (b) a drive coupling.
10. 10. A pump system characterized in that it comprises: (a) a pump box suitable for containing liquefied natural gas at a pressure of approximately 1035 kPa (150 psia) at approximately 7590 kPa (1100 psia) and at a temperature of approximately 123 ° C (190 ° F) at approximately -62 ° C (-80 ° F), the pump housing being constructed by joining together a plurality of discrete sheets of materials comprising a low alloy ultra high strength steel of less than 9%, by weight of nickel and having a tensile strength greater than 830 MPa (120 ksi) and a DBTT less than about - 73 ° C (-100 ° F), where the joints between the discrete plates have adequate strength and tenacity under pressure and temperature conditions to contain the pressurized liquefied natural gas; and (b) an actuator coupling.
11. 11. A burner system characterized in that it comprises: (a) a burner line suitable for containing a fluid at a pressure greater than about 1035 kPa (150 psia) and a temperature less than about -40 ° C (-40 ° F), the burnt line being constructed by joining together a plurality of discrete sheets of materials comprising ultra high strength steel, low alloy containing less than 9 wt.% nickel and having a tensile strength greater than 830 MPa (120 ksi) and a DBTT less than approximately -73 ° C (-100 ° F), where the joints between the discrete plates have adequate strength and tenacity under pressure and temperature conditions to contain pressurized fluid; and (b) a burner cleaner.
12. 12. A burner system characterized in that it comprises: (a) a burner line suitable for containing natural gas at a pressure of about 1035 kPa (150 psia) to about 7590 kPa (1100 psia) and a temperature of about -123 ° C ( -190 ° F) at approximately -62 ° C (-80 ° F), the burn line being constructed by joining together a plurality of discrete sheets of materials comprising an ultra high strength, low alloy steel containing less 9% by weight of nickel and having a tensile strength greater than 830 MPa (120 ksi) and a DBTT less than about -73 ° C (-100 ° F), where the joints between the discrete plates have strength and adequate tenacity in the conditions of pressure and temperature to contain the liquefied natural gas budget; and (b) a burner cleaner.
13. 13. A pipe network distribution system characterized in that it comprises: (a) at least one storage container suitable for containing a fluid at a pressure greater than approximately 1035 kPa (150 psia) and a lower temperature that approximately -40 ° C (-40 ° F), the storage container at least being constructed by joining together a plurality of discrete sheets of materials comprising an ultra high strength, low alloy steel containing less than % by weight of nickel and having a tensile strength greater than 830 MPa (120 ksi) and a DBTT less than about -73 ° C (-100 ° F), where the joints between the discrete sheets have strength and tenacity suitable in the conditions of pressure and temperature to contain the pressurized fluid; and (b) at least one distribution pipe. 1 .
14. A burner flow pipe distribution network system characterized in that it comprises: (a) at least one distribution pipe suitable for containing a fluid at a pressure greater than about 1035 kPa (150 psia) and a temperature less than about -40 ° C (-40 ° F), the distribution pipeline being at least constructed by joining together a plurality of discrete sheets of materials comprising an ultra high strength, low alloy steel containing less than 9% by weight of nickel and having a tensile strength greater than 830 MPa (120 ksi) and a DBTT less than about -73 ° C (-100 ° F), where the joints between the discrete sheets have adequate strength and toughness under the conditions of pressure and 'faith, tf.:, * - liiÉXifir ^^^^ temperature to contain the presupposed fluid; and (b) at least one storage container.
15. 15. A pipe network distribution system characterized in that it comprises: (a) at least one container suitable for containing pressurized liquefied natural gas at a pressure of about 1035 kPa (150 psia) to about 7590 kPa (1100 psia) and at a temperature of about -1230 ° C (-190 ° F) to about -62 ° C (-80 ° C), the storage container being constructed by joining together with a plurality of discrete sheets of materials comprising a steel of ultra high strength, low alloy containing less than 9% by weight of nickel and having a tensile strength greater than 830 MPa (120 ksi) and a DBTT less than about -73 ° C (-100 ° F), wherein the joints between the discrete plates have adequate strength and tenacity under the conditions of pressure and temperature to contain the liquefied natural gas budget; and (b) at least one distribution pipe.
16. 16. A pipe network distribution system characterized in that it comprises: (a) at least one distribution pipe suitable for containing liquefied natural gas at a pressure of approximately 1035 kPa (150 psia) a about 7590 kPa (1100 pass) and at a temperature of about -123 ° C (-190 ° F) to about -62 ° C (-80 ° F), the distribution pipe being constructed by joining together with a plurality of plates discrete materials comprising ultra high strength, low alloy steel containing less than 9% by weight of nickel and having a tensile strength greater than 830 MPa (120 ksi) and a DBTT less than about -73 ° C (-100 ° F), where the joints between the 10 discrete plates have adequate strength and tenacity under pressure and temperature conditions to contain the liquefied natural gas budget; and (b) at least one storage container. i- »a« - * «rtlto *« ~ -?