WO2025142622A1 - 高圧タンク - Google Patents

高圧タンク Download PDF

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Publication number
WO2025142622A1
WO2025142622A1 PCT/JP2024/044544 JP2024044544W WO2025142622A1 WO 2025142622 A1 WO2025142622 A1 WO 2025142622A1 JP 2024044544 W JP2024044544 W JP 2024044544W WO 2025142622 A1 WO2025142622 A1 WO 2025142622A1
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Prior art keywords
pressure tank
less
hydrogen
tank body
steel
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English (en)
French (fr)
Japanese (ja)
Inventor
拓史 岡野
ヴァナディア イリスカ ユッサラ
奈穂 井上
健一郎 江口
俊夫 高野
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JFE Steel Corp
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JFE Steel Corp
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Priority to JP2025523911A priority Critical patent/JPWO2025142622A1/ja
Publication of WO2025142622A1 publication Critical patent/WO2025142622A1/ja
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    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron

Definitions

  • This disclosure relates to a high-pressure tank for storing high-pressure hydrogen.
  • Hydrogen engines which burn hydrogen as fuel, are environmentally friendly in that they do not emit carbon dioxide ( CO2 ), and their structure can be realized by improving on conventional gasoline engines.
  • CO2 carbon dioxide
  • hydrogen gas used as fuel has the advantage of being highly flammable and having a fast burning speed, it ignites at unexpected times. As a result, hydrogen engines are prone to damage and have durability problems. The dominant factors behind this unstable ignition phenomenon of hydrogen gas have yet to be elucidated.
  • Methane gas ( CH4 ) is also used as an environmentally friendly fuel, and CNG (natural gas) vehicles are well known.
  • CNG natural gas
  • methane gas is slow to ignite and tends to produce unburned methane, which has led to the generation of NOx.
  • NOx As a measure against NOx, lean combustion technology for methane has been developed, but the lean combustion range of methane is narrow, which is an issue.
  • HCNG mixed gas
  • each high-pressure tank in Table 1 was determined by fatigue crack propagation analysis.
  • the fatigue crack propagation analysis was performed in accordance with KHKS0220 (2020).
  • Each high-pressure tank was determined to have reached its life (shown as "OK” in Table 1) or not (shown as "NG” in Table 1) based on whether or not it was broken when subjected to a stress amplitude of 11,250 cycles.
  • the stress amplitude of 11,250 cycles was set in consideration of the number of times that a high-pressure tank generally used as an on-board fuel container is filled with fuel before the vehicle's mileage limit is reached.
  • the life of the high-pressure tank 100 according to embodiment 1 may be a strength of 11,250 cycles or more in the crack propagation analysis, and may also be a strength of 12,000 cycles, 15,000 cycles, 20,000 cycles, 25,000 cycles, or more, and may be a strength of a value between these exemplified values.
  • the high-pressure tank 100 has a long lifespan, the thickness of the tank body 10 tends to increase, resulting in an increase in weight. In this case, there is a risk of reduced fuel efficiency when the high-pressure tank 100 is mounted on a vehicle, so the lifespan of the high-pressure tank 100 should be set to, for example, 50,000 cycles or less.
  • the high-pressure tank in the conventional example was constructed from conventional materials, but because its purpose was to store CNG and the amount of hydrogen in the gas filled was kept to 2% or less, it was not affected by hydrogen embrittlement and was able to ensure the lifespan required for an on-board fuel container. Specifically, the lifespan of the conventional example was 15,784 cycles compared to the criterion of 11,250 stress amplitude cycles.
  • Comparative Example 1 shown in the second column from the left of Table 1 and Comparative Example 3 shown in the fourth column the fuel to be stored is HCNG (mixed gas of natural gas and hydrogen), and the amount of hydrogen in the gas components is 20%.
  • the material constituting the high-pressure tank according to Comparative Example 1 and Comparative Example 3 is a conventional material, for example, SCM435 (chromium molybdenum steel) that has been quenched and tempered as in the conventional example, and has a tensile strength (TS) of 953 MPa, but does not have the characteristics of the steel material used in the high-pressure tank 100 according to the first embodiment.
  • SCM435 chromium molybdenum steel
  • the steel material is hydrogen embrittled due to the influence of the hydrogen contained in the fuel stored therein, and the lifespan is reduced.
  • the high-pressure tank according to Comparative Example 1 has a lifespan of about 1200 to 1300 cycles, and the lifespan as a high-pressure tank mounted on a vehicle could not be ensured.
  • Comparative Example 3 with the conventional material, the life could not be ensured even when the wall thickness t was 10 mm.
  • Comparative Example 2 shown in the third column from the left in Table 1, the fuel to be stored is HCNG (mixed gas of natural gas and hydrogen) like Comparative Example 1.
  • the material constituting the high-pressure tank according to Comparative Example 2 is the same as that of the conventional example, Comparative Example 1, and Comparative Example 3, and is a conventional material, for example, SCM435 (chromium molybdenum steel) that has been quenched and tempered, and has a tensile strength (TS) of 953 MPa, but does not have the characteristics of the steel material used in the high-pressure tank 100 according to the first embodiment.
  • SCM435 chromium molybdenum steel
  • the steel material is hydrogen embrittled due to the influence of hydrogen contained in the fuel stored therein, and the lifespan is reduced.
  • the high-pressure tank according to Comparative Example 2 has a lifespan exceeding the criterion of 11,250 cycles despite being affected by hydrogen embrittlement, and the lifespan as an on-board HCNG high-pressure tank was ensured.
  • the high-pressure tank according to Comparative Example 2 meets the standard for lifespan, it has a thick wall thickness t and weighs 113 kgf, which is twice as much as the conventional example, and it can store less fuel than the high-pressure tanks according to the conventional example, Comparative Example 1, and Comparative Example 3.
  • a high-pressure tank as an on-board fuel tank
  • an increase in the weight of the tank body 10 must be suppressed as much as possible, since it leads to an increase in the weight of the vehicle body.
  • a heavy high-pressure tank 100 such as that of Comparative Example 2 is mounted on an automobile, measures such as reducing the passenger capacity are usually required. For this reason, there are no high-pressure tanks currently in use for storing on-board CNG that are thick.
  • a wall thickness t at least equivalent to that of Comparative Example 2 would be required.
  • Comparative Example 4 shown in the fifth column from the left in Table 1 the wall thickness can be reduced by reducing the outer diameter Do of the tank, which reduces the stress generated.
  • the wall thickness can be reduced by about 3 mm compared to Comparative Example 2.
  • Comparative Example 4 in order to ensure 57 liters, which is the same as the conventional example (the conventional example and Comparative Example 1 in Table 1), a length of 1595 mm is required, and the weight is estimated to be 113 kg. Therefore, as a tank for storing HCNG, the lifespan can be satisfied by simply reducing the outer diameter Do of the high-pressure tank, but the weight cannot be reduced.
  • Examples 2, 3, and 4 of the invention are also high-pressure tanks using the new material, and the life as an on-vehicle HCNG high-pressure tank can be ensured as in Example 1 of the invention.
  • the tank is longer in Example 4, the outer diameter Do of the tank can be reduced, so that the orientation of the tank mounted on the vehicle can be changed from horizontal to vertical, which has the advantage of expanding the freedom of design of the mounting form.
  • Example 1 strength and durability are maintained even when HCNG is stored, and although the weight is increased compared to the conventional example, the weight is reduced by about 40 kgf compared to Comparative Example 2, which uses conventional materials.
  • the high-pressure tank 100 using the new material as in Example 1 of the invention satisfies practical use as an on-board HCNG high-pressure tank.
  • carbides are dispersed in the metal structure, so that hydrogen that has entered the metal structure is trapped within the grains of the metal structure by the carbides, thereby suppressing the effects of hydrogen embrittlement.
  • the carbides present in the metal structure are dispersed in a desired size as precipitates. Therefore, hydrogen that has entered the metal structure is trapped by molybdenum precipitates within the grains of the metal structure, suppressing the effects of hydrogen embrittlement.
  • the molybdenum precipitates are dispersed in the metal structure and trap hydrogen.
  • carbides in the metal structure that are effective as hydrogen traps include TiC (titanium carbide), VC (vanadium carbide), and NbC (niobium carbide).
  • Carbides precipitated in the metal structure are effective as hydrogen traps if they are 100 nm or less, but are preferably 50 nm or less.
  • Figure 3 is an explanatory diagram that shows a schematic representation of the effects of hydrogen on conventional and new materials.
  • Hydrogen atoms that have entered the metal structure of the steel material used in the tank body 10 move within the metal structure along with dislocations in the crystals.
  • the metal structure of steel contains tiny crystal grains, and when high stress is generated, fractures are likely to occur at the boundaries between the crystal grains.
  • hydrogen atoms accumulate at the grain boundaries, the effect of hydrogen on reducing the interatomic cohesive force can cause grain boundary fracture, reducing the fatigue strength of the steel material.
  • Figure 4 is an explanatory diagram that shows the relationship between the stress and the crack propagation speed that occurs in the steel material constituting the tank body 10 according to the first embodiment and the conventional steel material.
  • quasi-cleavage (QC) fracture occurs mainly within the crystal grains up to a certain stress range (horizontal part of the solid line A), and above a certain stress, intergranular (IG) fracture occurs mainly (sloping part of the solid line A).
  • the steel material constituting the tank body 10 according to the first embodiment has a low overall crack propagation speed because carbides are arranged within the crystal grains.
  • hydrogen atoms are trapped within the crystal grains, making it difficult for intergranular fracture to occur, so the region in which quasi-cleavage (QC) fracture is the main fracture mode is expanded, and the stress at which intergranular fracture is the main mode is high.
  • the steel material used in the tank body 10 has a structure in which the main phase is tempered martensite, and molybdenum precipitates are present in the structure.
  • the molybdenum precipitates include precipitates with a diameter of 50 nm or less.
  • the steel material used in the tank body 10 is, for example, the molybdenum steel or martensitic stainless steel shown in the above-mentioned invention example.
  • the grain size number of the prior austenite grains can be adjusted by changing the heating rate, heating temperature, and holding temperature during the quenching process, as well as the number of times the quenching process is performed.
  • the concentration of molybdenum precipitates is adjusted within an appropriate range depending on the size in order to improve hydrogen embrittlement resistance.
  • the molybdenum precipitates are identified by filtration using, for example, the technique described in JP 2010-127791 A and the extraction method described in "Ishida et al., Analysis of the Formation State of Fine Precipitates in Steel, Iron and Steel, Vol. 107, No. 08".
  • a 10 mm square sample taken from a cross section perpendicular to the rolling direction of the steel pipe was electrolyzed in an electrolyte, and the precipitates attached to the steel piece surface were placed in a dispersive aqueous solution and irradiated with ultrasonic waves to extract the precipitates into the aqueous solution.
  • the aqueous solution from which the precipitates were extracted was filtered, the precipitates were separated by size, and the precipitates classified by size were dissolved in a solution, and the Mo concentration was analyzed by ICP to calculate the Mo content of the precipitates of each size.
  • the solution was introduced into plasma to emit an element-specific spectrum, and the concentration of the element in the solution can be obtained from the emission intensity of the light, so that the Mo concentration (mass%) in the precipitates can be calculated.
  • This method allows the Mo content in the entire precipitate to be calculated, and the ratio (mass%) of Mo contained in the precipitates to the Mo contained in the steel can be obtained from this value and the Mo content in the steel.
  • the solution after electrolysis described above was analyzed by ICP in concentration in accordance with the technology described in JP 2009-031269 A to obtain the solid solution concentration of Mo in the steel.
  • the Mo content contained in the precipitates remaining on the filter was analyzed by ICP, and the Mo content contained in the precipitates exceeding 50 nm was analyzed.
  • the proportion (mass%) of Mo contained in precipitates with a diameter of 50 nm or less can be calculated.
  • Mo contained in steel More than 50% of Mo contained in steel is contained in precipitates.
  • the presence of Mo in the steel composition as precipitates improves the hydrogen environment characteristics. If the amount of Mo added to steel is increased and it is dissolved, the effect cannot be expected.
  • the greater the amount of molybdenum precipitates the better the hydrogen trapping ability, and the better it is when 50% or more of Mo contained in steel is contained in precipitates. It is preferable that 60% or more of Mo contained in steel exists in precipitates. However, Mo contained in precipitates may be 50% or less of Mo contained in steel.
  • S 0.005% or less
  • S is an inevitable impurity, and most of it exists as sulfide-based inclusions in steel, which reduces ductility, toughness, and even SSC resistance. Therefore, it is preferable to reduce the S content as much as possible, but it is permissible up to 0.005%. For this reason, the S content is limited to 0.005% or less.
  • the S content is preferably 0.003% or less. The lower the S content, the better, but from the viewpoint of refining costs, the S content is preferably 0.0002% or more.
  • Cu 1.0% or less
  • Cu is an effective element for improving toughness and increasing strength, but if the content is too high, weldability deteriorates. Therefore, when Cu is contained, the Cu content is limited to 1.0% or less.
  • the Cu content may be 0% or more, but it is preferable to contain 0.01% or more in order to obtain the effects of improving toughness and increasing strength.
  • Ca 0.0005-0.005%
  • Ca is an element that combines with S to form CaS and effectively controls the morphology of sulfide-based inclusions, and contributes to improving toughness and hydrogen embrittlement resistance through morphology control of sulfide-based inclusions.
  • the Ca content must be 0.0005% or more.
  • the Ca content exceeds 0.005%, the effect becomes saturated and it is no longer possible to expect an effect commensurate with the content, which is disadvantageous in terms of economy. For this reason, if Ca is contained, the Ca content is limited to the range of 0.0005 to 0.005%.
  • the tank body 10 is made by heating a steel pipe material of the above composition and hot working it to form a seamless steel pipe (seamless steel pipe) into a specified shape. It is preferable that seamless steel pipes for high-pressure hydrogen containers are used for hydrogen containers with a hydrogen pressure of 1 MPa or more, and more preferably 20 MPa or more.
  • Casting speed 2.0 m/min or less
  • the casting speed is preferably 1.5 m/min or less, more preferably 1.0 m/min or less, and even more preferably 0.5 m/min or less.
  • Heating temperature 1050-1350°C If the heating temperature is less than 1050°C, the precipitates in the steel material are not sufficiently dissolved. On the other hand, if the temperature is higher than 1350°C, the crystal grains become coarse, and the precipitates such as TiN precipitated during solidification also become coarse, and the cementite also becomes coarse, so that the toughness of the steel pipe decreases. In addition, if the temperature is higher than 1350°C, a thick scale layer is formed on the surface of the steel pipe material, which causes surface defects during rolling and increases energy loss, which is not preferable from the viewpoint of energy saving. For these reasons, the heating temperature is limited to a temperature range of 1050 to 1350°C. The heating temperature is preferably 1100 to 1300°C.
  • the resulting seamless steel pipe (tank body 10) is subjected to a cooling process in which it is cooled at a rate faster than air cooling until the surface temperature reaches 200°C or below.
  • Cooling treatment after hot rolling Cooling rate: air cooling or more, cooling stop temperature: 200 ° C or less
  • Cooling rate air cooling or more
  • cooling stop temperature 200 ° C or less
  • the shape of the tank body 10 may be formed during or after hot rolling.
  • the tank body 10 is a seamless integrally molded product, the tank body 10 is formed by squeezing both ends of a tubular rolled steel material. Furthermore, removal processing required for the tank body 10 may be performed after hot rolling.
  • Tempering temperature 600 to 740°C
  • the tempering treatment is performed for the purpose of reducing dislocation density, precipitating molybdenum precipitates, and improving toughness and hydrogen embrittlement resistance. If the tempering temperature is less than 600°C, the reduction in dislocations and the precipitation of molybdenum precipitates are insufficient, and therefore excellent hydrogen embrittlement resistance cannot be ensured. On the other hand, if the temperature exceeds 740°C, the structure is significantly softened and the desired high strength cannot be ensured. For this reason, the tempering temperature is limited to a range of 600 to 740°C.
  • the tempering temperature is preferably 640 to 710°C.
  • the average heating rate until the tempering temperature is reached is 0.5°C/min or more Molybdenum precipitates precipitate during the temperature rise process of tempering, and their size increases. Therefore, if the heating rate until the specified temperature in the tempering process is reached is slow, the size of the precipitates becomes too large, and the desired hydrogen embrittlement resistance properties cannot be obtained. Therefore, the average heating rate until the tempering temperature is reached is set to 0.5°C/min or more, preferably 2.0°C/min or more. There is no particular upper limit, but if the heating rate is too fast, unevenness in the temperature distribution occurs, resulting in inhomogeneity in the material structure, so 50°C/min or less is preferable.
  • Holding time at tempering temperature is 10 minutes or more and less than 120 minutes Molybdenum precipitates are most likely to precipitate during tempering. If this time is too short, they will not precipitate sufficiently and the desired hydrogen embrittlement resistance will not be obtained.
  • the holding time at tempering temperature is 10 minutes or more. If the holding time at tempering temperature is too long, the size of the precipitates will become too large, so the holding time is less than 120 minutes. Note that the holding time is a factor in increasing costs in terms of energy, so it is preferably less than 60 minutes.
  • Reheating temperature for quenching Ac3 transformation point or higher and 1000°C or lower
  • the reheating temperature is lower than the Ac3 transformation point, the steel sheet is not heated to the austenite single phase region, and therefore a structure having martensite as the main phase cannot be obtained.
  • the reheating temperature exceeds 1000°C, the crystal grains become coarse and the toughness decreases, and the oxide scale on the surface becomes thick and easily peels off, which causes scratches on the steel sheet surface. Furthermore, the load on the heat treatment furnace becomes excessive, which is also a problem from the viewpoint of energy saving.
  • the reheating temperature for quenching is limited to Ac3 transformation point or higher and 1000°C or lower.
  • the reheating temperature is preferably 950°C or lower.
  • the plate After reheating, the plate is subjected to quenching treatment.
  • the cooling in the quenching treatment is preferably performed by water cooling at an average cooling rate of 2°C/s or more until the temperature at the center of the plate thickness reaches 400°C or less.
  • the cooling in the quenching treatment is performed by rapidly cooling the plate until the surface temperature reaches 200°C or less. It is also preferable that the surface temperature is cooled to 100°C or less.
  • the quenching treatment may be repeated two or more times.
  • Ac3 transformation point (°C) 937-476.5C+56Si-19.7Mn-16.3Cu-4.9Cr-26.6Ni+38.1Mo+124.8V+136.3Ti+198Al+3315B (Here, C, Si, Mn, Cu, Cr, Ni, Mo, V, Ti, Al, B: Content of each element (mass%)) In calculating the Ac3 transformation point, when an element described in the above formula is not contained, the content of the element is set to zero percent.
  • a warm or cold correction process may be performed to correct any shape defects in the tank body 10, if necessary.
  • the tank body 10 may be formed after the quenching and tempering processes.
  • the tank body 10 was not actually molded, but a seamless steel pipe for an actual steel structure was manufactured and its characteristics were evaluated.
  • the evaluation results of the steel types shown as examples of the invention in the remarks column of Table 3 below can be applied regardless of the shape of the tank body 10, whether it is a seamless steel pipe, or the shape of the finished product, which is different.
  • Table 2 shows the composition of steel Nos. 1 to 14.
  • Table 3 also shows the tempering conditions, size and number of molybdenum precipitates, and relative reduction of area (RRA) for each of Nos. 1 to 14.
  • Billet having the composition shown in steel type No. 1 to 14 in Table 2 was produced at a casting speed of 0.6 m/min, and the billet was heated to 1250°C and expanded to obtain a seamless steel pipe.
  • This seamless steel pipe corresponds to the example shown in steel material No. 1 to 14 in Table 3.
  • billet having the composition of steel type No. 5 in Table 2 was produced at a casting speed of 1.8 m/min, and the billet was heated to 1250°C and expanded to obtain a seamless steel pipe.
  • This seamless steel pipe corresponds to the example shown in steel material No. 15 to 17 in Table 3.
  • Hydrogen embrittlement resistance was evaluated from the relative reduction of area (RRA) of the test piece after a slow strain rate tensile test in hydrogen gas.
  • RRA relative reduction of area
  • the steel undergoes plastic deformation, reducing the area of the fracture surface, and therefore the reduction of area ⁇ air becomes large.
  • the elongation of the steel decreases, so the material breaks before it can be reduced, and the area of the fracture surface remains large. Therefore, the reduction of area ⁇ H of the fracture surface after the test in hydrogen becomes smaller, unlike in air. Hydrogen embrittlement resistance was evaluated from this reduction in reduction of area.
  • RRA Relative aperture
  • the method for measuring molybdenum precipitates in steel is as follows. Molybdenum precipitates were identified by an extraction method in which the steel was electrolyzed and the precipitates obtained were filtered. A 10 mm square sample taken from a cross section perpendicular to the rolling direction of a seamless steel pipe (cross section perpendicular to the tube axis direction: C cross section) was dissolved in a 10% AA-based electrolyte by constant current electrolysis, and the steel piece was placed in a 0.05 wt% sodium hexametaphosphate aqueous solution and irradiated with ultrasonic waves to extract the precipitates. The solution was filtered through a filter with a filter diameter of 50 nm to obtain precipitates of 50 nm or less.
  • Precipitates of 50 nm or less that passed through the filter and precipitates of more than 50 nm on the filter were heated and white smoked with sulfuric acid, perchloric acid, and nitric acid, and then dissolved in hydrochloric acid.
  • the precipitate solution and the electrolyte containing the dissolved solids were then analyzed for concentration by ICP, and the Mo concentration, amount of Mo, and dissolved Mo concentration contained in the precipitates of each size were calculated.
  • the high-pressure tank 100 described above may also include combinations of the features shown in Supplementary Notes 1 to 13 below. These combinations are described below.
  • a high-pressure tank that stores a mixed gas containing natural gas and hydrogen, the mixed gas containing more than 2% hydrogen by volume, inside a tank body,
  • the tank body includes: A cylindrical portion extending in a first direction; a dome portion connected to both ends of the cylindrical portion in the first direction,
  • the steel material constituting the tank body is Tensile strength TS: 850 MPa or more;
  • the steel has a structure in which tempered martensite accounts for 95% or more in area ratio, and carbides having a size of 100 nm or less are scattered as precipitates in the metal structure. In crack propagation analysis, it has a strength of more than 11,250 cycles.
  • High pressure tank [Appendix 2] 2.
  • High pressure tank. [Appendix 3] 3. The high-pressure tank according to claim 1 or 2, The wall thickness t of the cylindrical portion is Satisfying 8mm ⁇ t; High pressure tank. [Appendix 4] A high-pressure tank according to any one of appendix 1 to 3, The cylindrical portion and the dome portion are integrally formed. High pressure tank.
  • the high-pressure tank according to claim 9 The steel material constituting the tank body is In mass percent, Si: 0.05-2.00%, Mn: 0.30 to 1.5%, P: 0.015% or less, S: 0.005% or less, Al: 0.005-0.15%, N: 0.006% or less, Cr: more than 0.2% but not more than 1.7%, Nb: 0.001-0.02%, B: 0.0003 to 0.0030%, O: 0.0030% or less, Ti: 0.003 to 0.025%; The balance is Fe and unavoidable impurities. High pressure tank. [Appendix 11] 11.
  • the high-pressure tank according to claim 10 The steel material constituting the tank body is In addition to the above composition, further, in mass%, V: 0.3% or less, Cu: 1.0% or less, Ni: 2.0% or less, W: 3.0% or less. High pressure tank.
  • Appendix 12 12. The high-pressure tank according to claim 10 or 11, The steel material constituting the tank body is In addition to the above composition, further, in mass%, H: 0.0010% or less; High pressure tank.
  • a high-pressure tank according to any one of appendixes 10 to 12 The steel material constituting the tank body is In addition to the above composition, further, in mass%, Ca: 0.0005-0.005% Contains High pressure tank.
  • Tank body 11 Cylindrical portion 12: Dome portion 12a: Dome portion 12b: Dome portion 13: Cap 14: Supply device 90: Space 100: High-pressure tank

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PCT/JP2024/044544 2023-12-27 2024-12-17 高圧タンク Pending WO2025142622A1 (ja)

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2026053866A1 (ja) * 2024-09-04 2026-03-12 Ｊｆｅスチール株式会社 継目無鋼管およびその製造方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2007197776A (ja) * 2006-01-27 2007-08-09 Jfe Steel Kk 耐遅れ破壊特性と耐疲労き裂伝播特性に優れた高強度鋼材およびその製造方法
JP2012036499A (ja) * 2010-07-16 2012-02-23 Jfe Steel Corp 曲げ加工性および低温靱性に優れる高張力鋼板およびその製造方法
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