Classifications

• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D6/00—Heat treatment of ferrous alloys
  • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D6/00—Heat treatment of ferrous alloys
  • C21D6/005—Heat treatment of ferrous alloys containing Mn
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
  • C21D8/0226—Hot rolling
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
  • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
  • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D2211/00—Microstructure comprising significant phases
  • C21D2211/001—Austenite
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment

Definitions

• This invention relates to the metallurgy of construction steels comprising, as the basis, iron with the preset ratio of the alloying and impurity elements, and can be used in various branches of industry, more specifically, for the fabrication of high-strength cryogenic welded structures used for the transportation of liquefied gases.
• said known steel contains carbon, chromium, nickel, manganese, nitrogen, silicon, vanadium, copper, molybdenum, cerium, selenium and iron in the following weight ratio (wt.%): carbon 0,01-0,06, chromium 18-22, nickel 15-18, manganese 2-10, nitrogen 0.2-0.5, silicon 0.01-0.45, vanadium 0.1-0.5, copper 0.1-1.5, molybdenum 0.1-2.5, cerium 0.005-0.25, selenium 0.05-0.25, balance iron, wherein if the manganese content is less than 5% the nitrogen content is approx. 0.3 while if the manganese content is greater than 5% the nitrogen content is 0.4-0.5.
• Said known austenitic steel has multiple technical and mechanical properties and the stability of the austenitic structure and can be used for the fabrication of high-load parts of cryogenic machinery and devices.
• Said known austenitic steel has the following disadvantages.
• This steel is not economic due to high concentrations of expensive elements such as nickel (up to 18%) and molybdenum (up to 2.5%).
• the nickel content in this steel is higher than in conventional austenitic stainless steel 19-10.
• manganese and nitrogen are used for the stabilization of the austenitic structure.
• a number of steel compositions having the claimed limits of element contents are not feasible.
• the manganese content in this steel is higher than 5%, the nitrogen content is acceptable at 0.4-0.5%.
• the nitrogen content should be lower than the claimed one, otherwise bubbles will form during the solidification of ingots at nitrogen contents of 0.4-0.5%.
• the prototype of the first subject of this invention is high-strength corrosion resistant non-magnetic steel (RU 2392348 C2, publ. 20.06.2010).
• This steel has the following composition (wt.%): 0.02-0.06 carbon, 0.10-0.60 silicon, 9.5-12.5 manganese, 19.0-21.0 chromium, 4.5-7.5 nickel, 1.2-2.0 molybdenum, 0.08-0.22 vanadium, 0.005-0.010 calcium, 0.005-0.010 sodium, 0.05-0.15 niobium, 0.0005-0.001 magnesium, 0.40-0.60 nitrogen, 0.005-0.01 aluminum, balance iron and impurities, wherein said impurities in this steel are (wt.%) 0.003-0.012 sulfur, 0.004-0.025 phosphorus, 0.0002-0.005 lead, 0.0002-0.005 bismuth, 0.0002-0.005 tin, 0.0002-0.005 arsenic and 0.05-0.2 copper.
• the prototype of the second subject of this invention is a method of thermal deformation processing of the abovementioned high-strength corrosion resistant non-magnetic steel (RU 2392348 C2, publ. 20.06.2010).
• the method of thermal deformation processing of the high-strength corrosion resistant non-magnetic steel comprises ingot heating, ingot deformation to a plate in the 1240-1000 °C temperature range with a total strain rate of 40-94%, air cooling of the plate for surface quality control and cleaning, deformation of the resultant plate in the 1240-1000 °C temperature range, treatment to the final total strain rate of 45 - 65% by 10-14%) at a time to the sheet shape with a thickness of 2.5-3.5 times smaller than the plate thickness, air cooling of the sheet to 1000-950 °C, surface temperature control and final straining in 2-3 runs by 8-12% at a time, followed by rapid cooling at a 10-50 °C/s rate to 100-150 °C at the sheet surface and further air cooling.
• Said known steel is melted in furnaces following a standard technology.
• the steel is subjected to thermal deformation processing in a special mode.
• the thermal deformation processing technology Disadvantages of the thermal deformation processing technology is the excessive detalization of process steps which complicates the implementation and control of the technology and, furthermore, for the recommended pre- straining heating mode and at some element ratios, the structure of the steel during heating to > 1200 °C passes through several phases including 5- ferrite.
• the structure of the steel during heating to > 1200 °C passes through several phases including 5- ferrite.
• the steel has an + ⁇ + (Nb, Cr)N structure. Therefore at the claimed heating temperature according to the patent (1240 °C) it is impossible to obtain a homogeneous ⁇ - structure before rolling and hence no finished austenitic steel will be produced.
• the high strength cryogenic austenitic corrosion resistant weldable construction steel comprises the following elements in the ratios as shown below, wt.%:
• the technical result of the second subject of the claimed invention is a simple industrial implementation of said method, good processability of the steel combined with a relatively low manganese concentration and the possibility of obtaining the required nitrogen concentration during melting at a normal pressure in the existing equipment.
• the method of thermal deformation processing of the high strength cryogenic austenitic corrosion resistant weldable construction steel as per Claim 1 comprises ingot heating, ingot deformation to a workpiece in the 1240-1050 °C temperature range with a total strain rate of at least 50%, air cooling of the workpiece, straining of the resultant plate in the 1 180-1080 °C temperature range with a total compression rate of at least 40% and final straining in 2-3 runs with a total compression rate of 30-80 % in the 1 150-1080 °C temperature range with the finishing rolling temperature of 1050-1080 °C, followed by rapid cooling at a 20-100 °C/s rate to room temperature.
• the advantages of the steel suggested in this invention and its treatment method are as follows.
• the equilibrium structure of the steel in the 1050 - 1300 °C is austenite with fine chromium boride Cr 2 B particles which guarantees the basic austenitic structure and the required combination of properties under actual industrial process conditions.
• the suggested steel also has good economic parameters due to a low nickel content and high workability due to a small number of alloying additions, and at their claimed concentrations the required nitrogen content can be obtained by melting at normal pressure in the existing equipment.
• Carbon contents in the 0.05-0.07% range favors the formation of an austenitic structure in the steel and, jointly with nitrogen provides for the required steel hardening during thermal and thermal deformation processing combined with good corrosion resistance and weldability.
• At higher carbon contents in the steel its corrosion resistance decreases, this being accompanied by increasing susceptibility to intergranular corrosion, susceptibility to brittle fracture and decreasing weldability.
• Chromium, nickel, manganese, molybdenum and copper in the claimed concentration limits at a boron content of 0.005 - 0.015 wt.% and a nitrogen content of 0.30 - 0.38 wt.% at every possible combination of these element compositions in the composition range delimited in this invention provide the finished steel with a stable austenitic structure with a small quantity of fine boron particles, the required mechanical properties, corrosion resistance in acid media and in seawater and suitability for the fabrication of cold-resistant high- strength welded structure used for liquefied gas transportation.
• the required austenitic structure and properties are not achievable, same as the nitrogen concentrations as are required in accordance with this invention.
• an austenitic structure forms but the obtained ⁇ - solid solution has a higher hot plastic deformation strength.
• the claimed concentrations of Cr, Ni, Mn and Mo provide for a high nitrogen solubility in the liquid phase and in the austenite, an das a resultat every possible combination of element concentrations in the composition range claimed in the invention and a nitrogen concentration of 0.30 - 0.38 wt.% the steel crystallized without bubbles or pores in ingots or uninterruptible cast workpieces. At lower nitrogen concentrations the required mechanical properties are not achieved, while at higher nitrogen contents bubbles and pores may form in the ingots.
• Copper makes the steel of this composition more corrosion resistant and at the claimed concentration of other elements increases the higher temperature limit of the ⁇ region.
• the equilibrium steel structure in the 1050 - 1300 °C temperature range is ⁇ + Cr 2 B which guarantees industrial production of an austenite structure and the required combination of properties.
• the corrosion resistance of the steel decreases in acid media and in seawater.
• High copper concentrations are also undesirable due to an increase in the lower temperature limit of the austenite region and the melt and the steel may acquire inhomogeneous chemical composition and properties.
• Aluminum within the claimed concentration limits 0.015 - 0.035 wt.% provides for the required steel deoxidation degree and oxygen content. At lower aluminum concentrations the required steel deoxidation degree is not achieved and chromium oxides may form, while higher aluminum concentrations lead to the formation of high-temperature aluminum nitrides which negatively affect the properties of the steel.
• Silicon within the claimed concentration limits favors efficient steel deoxidation and the removal of nonmetallic inclusions and typically provides for the acceptable equivalent concentration of chromium Cr 3 .
• Cr 3 content increases and ⁇ - ferrites may form in the steel structure.
• steel deoxidation is hindered.
• the presence of these impurities complicates the achievement of the required structure and properties of the steel and reduces the efficiency of nitrogen addition. Therefore nitrogen alloyed steel are usually melted following the pure steel technology.
• the impurity concentration limit required in accordance with this invention i.e. P ⁇ 0.015, S ⁇ 0.0025, Sn ⁇ 0.005, Pb ⁇ 0.005, As ⁇ 0.005 and Bi ⁇ 0.005 in the steel provides for the best steel properties achievable at this composition. At higher impurity concentrations they negatively affect the structure and properties of the steel and the structure formation processes in the steel. Significantly lower impurity concentrations is currently difficultly achievable for technological reasons.
• the steel has a basic austenitic structure and the required combination of mechanical and physical properties. Failure to maintain the required heating temperatures before straining and the onset and completion of the thermal deformation processing operations, compression rate and cooling rate at different process steps the required austenitic steel and the properties claimed in the invention cannot be achieved.
• Embodiments of the Invention Example of steel melting and processing technology follows.
• the ingots were heated at 1250 °C and forged in the 1250-1050 °C temperature range to 70% strain, and then the forged pieces were air cooled and cleaned.
• the forged pieces were heated to 1 180 °C and rolled to a total strain of 60% (to a 10 mm thickness) in the 1 180-1080 °C temperature range in 9 runs with interim heating. After rolling the pieces were air cooled.
• the final rolling was following the high-temperature thermomechanical treatment setup.
• the metal was heated to 1 150 °C and rolled to a sheet with a total strain of 60% (to a 6 mm thickness) in the 1150-1080 °C temperature range with interim heating.
• the final cooling of the rolled pieces was at a 100 °C/s rate in water.
• Then the rolled pieces were cleaned and cut to the required piece sizes.
• the chemical composition of the steels is summarized in Table 1.
• the mechanical properties of the alloys are presented in Table 2.

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• Organic Chemistry (AREA)
• Physics & Mathematics (AREA)
• Thermal Sciences (AREA)
• Crystallography & Structural Chemistry (AREA)
• Heat Treatment Of Steel (AREA)

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• 2017
  • 2017-01-31 RU RU2017103168A patent/RU2657741C1/ru active
  • 2017-09-11 JP JP2019541241A patent/JP2020509225A/ja active Pending
  • 2017-09-11 CN CN201780089165.2A patent/CN110475897B/zh active Active
  • 2017-09-11 EA EA201900398A patent/EA036755B1/ru not_active IP Right Cessation
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