WO2021141099A1 - オーステナイト系ステンレス鋼材 - Google Patents
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- WO2021141099A1 WO2021141099A1 PCT/JP2021/000422 JP2021000422W WO2021141099A1 WO 2021141099 A1 WO2021141099 A1 WO 2021141099A1 JP 2021000422 W JP2021000422 W JP 2021000422W WO 2021141099 A1 WO2021141099 A1 WO 2021141099A1
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- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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Definitions
- the present invention relates to an austenite-based stainless steel material.
- Austenitic stainless steel is one of the metal materials used in the above-mentioned related equipment from the viewpoint of manufacturing cost, strength, and corrosion resistance. Therefore, in order to suppress hydrogen embrittlement, austenitic stainless steel having improved hydrogen embrittlement resistance has been developed.
- Patent Documents 1 and 2 disclose austenitic stainless steel having excellent hydrogen embrittlement resistance at low temperatures.
- the austenitic stainless steels disclosed in Patent Documents 1 and 2 have improved hydrogen embrittlement resistance by adjusting the chemical composition to a predetermined amount.
- the austenitic stainless steel used as a material may be required to have not only hydrogen gas embrittlement resistance but also weldability.
- Patent Document 3 discloses an austenitic stainless steel for hydrogen having excellent weldability.
- hydrogen resistance is enhanced by containing a certain amount of Ni, Cu, etc., and the content of S, P, Ca, Al, etc., which affects weldability, is adjusted. .. This improves the weldability and hydrogen resistance of the steel.
- diffusion bonding may be used instead of welding. This is because when joining by welding, a large change in shape is involved, but when joining by diffusion joining, the shape change can be suppressed. In welding, the material is melted, re-solidified, and joined, whereas in diffusion bonding, pressure is applied at a temperature below the melting point to the extent that plastic deformation does not occur as much as possible, and the diffusion of atoms between interfaces is used. , To join. Therefore, diffusion bonding is suitable for manufacturing an apparatus that requires dimensional accuracy and the like.
- the austenitic stainless steels disclosed in Patent Documents 1 to 3 do not mention diffusion bonding. Therefore, when the stainless steel is joined by diffusion bonding, an appropriate bonding strength may not be obtained, and good diffusion bonding resistance may not be obtained.
- An object of the present invention is to solve the above-mentioned problems and to provide an austenite-based stainless steel material having excellent hydrogen gas embrittlement resistance and diffusion bonding property.
- the present invention has been made to solve the above problems, and the following austenite-based stainless steel materials are the gist of the present invention.
- An austenite-based stainless steel material having a passivation film on its surface The chemical composition is mass%, C: 0.10% or less, Si: 1.0% or less, Mn: 8.0 to 10.0%, P: 0.030% or less, S: 0.0030% or less, Cr: 15.0 to 18.0%, Ni: 7.0-9.0%, N: 0.15 to 0.25%, Al: 0.005 to 0.20%, Ca: 0.0005-0.01%, Cu: less than 1.0%, Mo: less than 1.0%, B: 0 to 0.0050%, Nb: 0 to 0.50%, Ti: 0 to 0.50%, V: 0 to 0.50%, W: 0 to 0.50%, Zr: 0 to 0.50%, Co: 0 to 0.50%, Mg: 0 to 0.005%, Ga: 0-0.010%, Hf: 0 to 0.10%, REM: 0 to 0.10%, Remaining: Fe and impurities, An austenite-based stainless steel material having an f-
- each element symbol in the above formula (i) represents the content (mass%) of each element contained in the steel, and if it is not contained, it is set to zero.
- the chemical composition is mass%.
- an austenite-based stainless steel material having excellent hydrogen gas embrittlement resistance and diffusion bondability can be obtained.
- the present inventor examined austenitic stainless steels having good hydrogen gas embrittlement resistance and diffusion bonding properties, and obtained the following findings (a) to (d).
- (B) Cu is effective in suppressing a local increase in dislocation density and forming a uniform processed structure of an austenite phase. Therefore, it is an effective element for suppressing hydrogen gas embrittlement.
- Cu which has a relatively low melting point, is concentrated at the diffusion interface in a high temperature, non-oxidizing atmosphere at the time of joining, and easily melts. At this time, it is considered that a liquid film is formed at the interface and the bonding at the interface is hindered.
- Diffusion bonding is a method of bonding by utilizing the diffusion of atoms near the diffusion interface.
- non-metal inclusions such as oxides and sulfides interfere with interfacial contact, making it difficult to join. This is because if the non-metal inclusions are present near the interface, they need to be broken, dispersed and reduced for bonding.
- Stainless steel improves corrosion resistance by forming a Passivation film rich in Cr on the surface. Since this passive film serves as a bonding interface, stable reduction of Cr oxide is required even in a low oxygen environment, which affects the diffusion bonding property.
- Suitable for diffusion bonding is a passivation film in which Mn and Fe, which are easily reduced in the non-oxidizing atmosphere at the time of diffusion bonding, are concentrated. Therefore, it is desirable to control the composition of the passivation film by controlling the chemical composition and the production conditions.
- the present invention has been made based on the above findings, and the austenite-based stainless steel material according to the present invention has a passivation film on the surface.
- the austenite-based stainless steel material according to the present invention has a passivation film on the surface.
- C 0.10% or less C is an element effective for stabilizing the austenite phase and also contributes to the improvement of hydrogen gas embrittlement resistance.
- the excessive content of C promotes the precipitation of Cr-based carbides at the bonding interface and the precipitation at the grain boundaries, and lowers the diffusion bonding property and the corrosion resistance. Therefore, the C content is set to 0.10% or less.
- the C content is preferably 0.08% or less, and more preferably 0.07% or less.
- the C content is preferably 0.01% or more.
- the C content is preferably 0.03% or more, more preferably 0.04% or more.
- Si 1.0% or less Si has a deoxidizing effect, but if the Si content is excessive, it forms an oxide at the bonding interface, thereby lowering the surface cleanliness and lowering the diffusion bonding property. .. Therefore, the Si content is set to 1.0% or less.
- the Si content is preferably 0.8% or less, more preferably 0.7% or less, and even more preferably 0.6% or less.
- the Si content is preferably 0.1% or more, more preferably 0.2% or more, and further preferably 0.3% or more.
- Mn 8.0 to 10.0%
- Mn is an element effective for stabilizing the austenite phase and contributes to the improvement of hydrogen gas embrittlement resistance. It is also an element that is concentrated in the passivation film and is effective in improving diffusion bondability. Therefore, the Mn content is set to 8.0% or more.
- the Mn content is preferably 8.5% or more, and more preferably 9.0% or more.
- the Mn content is set to 10.0% or less.
- P 0.030% or less
- P is an element contained in steel as an impurity, which may form non-metal inclusions and reduce diffusion bondability. Therefore, the P content is set to 0.030% or less.
- the P content is preferably 0.025% or less, more preferably 0.015% or less. However, excessive reduction of P content increases raw material and manufacturing costs. Therefore, the P content is preferably 0.005% or more.
- S 0.0030% or less
- S is an element contained in steel as an impurity, which forms non-metal inclusions and lowers diffusion bondability. Therefore, the S content is set to 0.0030% or less.
- the S content is preferably 0.0020% or less, more preferably 0.0010% or less. However, if the S content is excessively reduced, the manufacturing cost increases. In addition to this, hot workability is reduced. Therefore, the S content is preferably 0.0001% or more.
- Cr 15.0 to 18.0% Cr is an element contained in stainless steel in a certain amount, and has an effect of improving corrosion resistance, particularly weather resistance. Therefore, the Cr content is set to 15.0% or more. However, Cr is a ferrite forming element. Therefore, if Cr is excessively contained, the austenite phase is destabilized and the hydrogen gas embrittlement resistance is lowered. Further, excess Cr is concentrated in the passive film, which lowers the diffusion bondability. Therefore, the Cr content is set to 18.0% or less. The Cr content is preferably 17.0% or less, more preferably 16.0% or less.
- Ni 7.0-9.0%
- Ni is an element necessary for ensuring hydrogen gas embrittlement resistance. Therefore, the Ni content is set to 7.0% or more. However, if an excessive amount of Ni is contained, the manufacturing cost increases. Further, as the recrystallization temperature rises, the diffusion bondability decreases. Therefore, the Ni content is set to 9.0% or less.
- the Ni content is preferably 8.5% or less, and more preferably 8.0% or less.
- N 0.15 to 0.25%
- N is an element effective for improving the embrittlement resistance of hydrogen gas. Therefore, the N content is set to 0.15% or more.
- the N content is preferably 0.17% or more.
- the N content is set to 0.25% or less.
- the N content is preferably 0.22% or less, and more preferably 0.20% or less.
- Al 0.005 to 0.20%
- Al is an element having a deoxidizing effect and is an element necessary for reducing O in steel.
- the austenite-based stainless steel material according to the present invention it is desirable to reduce the O content to 0.003% or less from the viewpoint of diffusion bondability.
- the Al content is set to 0.005% or more in order to exert the deoxidizing effect.
- the Al content is preferably 0.010% or more, and more preferably 0.020% or more.
- the Al content is set to 0.20% or less.
- the Al content is preferably 0.10% or less, more preferably 0.05% or less, and even more preferably 0.04% or less.
- Ca 0.0005-0.01% Like Al, Ca also has a deoxidizing effect and has an effect of reducing O in steel. In addition, sulfide is formed in steel to immobilize S. By forming the non-metal inclusions in the steel in this way, it has the effect of reducing the non-metal inclusions at the diffusion interface and improving the diffusion bondability. Therefore, the Ca content is set to 0.0005% or more.
- the Ca content is preferably 0.001% or more, and more preferably 0.002% or more.
- the Ca content is set to 0.01% or less.
- the Ca content is preferably 0.005% or less.
- Cu Less than 1.0% Cu is effective in suppressing a local increase in dislocation density and forming a uniform processed structure of an austenite phase. Therefore, it is an effective element for suppressing hydrogen gas embrittlement.
- the diffusion bondability may be lowered.
- Cu which has a relatively low melting point, is concentrated at the diffusion interface in a high temperature, non-oxidizing atmosphere at the time of joining, and easily melts. At this time, it is considered that a liquid film is formed at the interface and the bonding at the interface is hindered. Therefore, the Cu content is set to less than 1.0%.
- the Cu content is preferably 0.5% or less, more preferably 0.3% or less, and even more preferably less than 0.05%.
- the Cu content is preferably 0.01% or more.
- Mo Less than 1.0% Mo is an element mixed from raw materials such as scrap, but if it is contained in excess, the formation of a ⁇ ferrite phase is promoted and the hydrogen gas embrittlement resistance is lowered. Therefore, the Mo content is set to less than 1.0%.
- the Mo content is preferably 0.5% or less.
- the Mo content is preferably 0.01% or more.
- one or more selected from B, Nb, Ti, V, W, Zr, Co, Mg, Ga, Hf, and REM may be further contained in the range shown below. The reasons for limiting each element will be described.
- B 0 to 0.0050%
- the grain boundaries are strengthened and the crystal grains of the steel material are made finer.
- the movement of grain boundaries at the time of diffusion bonding is promoted, which has the effect of indirectly improving the diffusion bonding property. It also has the effect of improving manufacturability. Therefore, it may be contained as needed.
- the B content is set to 0.0050% or less.
- the B content is preferably 0.0030% or less.
- the B content is preferably 0.0002% or more.
- Nb 0 to 0.50% Nb forms carbides or carbonitrides to make the crystal grains of the steel material finer. As a result, the movement of grain boundaries during diffusion bonding is promoted, which indirectly has the effect of improving diffusion bonding. Therefore, it may be contained as needed. However, if Nb is excessively contained, the recrystallization temperature is raised and the diffusion bondability is lowered. Therefore, the Nb content is set to 0.50% or less. The Nb content is preferably 0.30% or less. On the other hand, in order to obtain the above effect, the Nb content is preferably 0.01% or more.
- Ti immobilizes C and N in the steel, forms non-metal inclusions in the steel, and reduces non-metal inclusions at the diffusion interface. As a result, Ti has the effect of improving the diffusion bondability. Therefore, it may be contained as needed. However, when Ti is excessively contained, the effect of forming non-metal inclusions in steel is saturated, and non-metal inclusions are also formed at the diffusion interface. Therefore, the Ti content is set to 0.50% or less. The Ti content is preferably 0.30% or less. On the other hand, in order to obtain the above effect, the Ti content is preferably 0.01% or more.
- V 0 to 0.50%
- V has the effect of improving the strength by being solid-solved or precipitated as a carbonitride in the steel. Therefore, it may be contained as needed. However, if V is excessively contained, the carbonitride is excessively formed, which lowers the diffusion bondability and the manufacturability during hot working. Therefore, the V content is set to 0.50% or less.
- the V content is preferably 0.30% or less.
- the V content is preferably 0.01% or more.
- W 0 to 0.50% W has the effect of improving strength and corrosion resistance. Therefore, it may be contained as needed. However, if W is contained in excess, the manufacturing cost increases. Therefore, the W content is set to 0.50% or less.
- the W content is preferably 0.30% or less. On the other hand, in order to obtain the above effect, the W content is preferably 0.001% or more.
- Zr 0 to 0.50%
- Zr has a deoxidizing effect and has an effect of improving diffusion bondability by forming an oxide. It also has the effect of improving corrosion resistance. Therefore, it may be contained as needed. However, excessive Zr content reduces toughness and workability. Therefore, the Zr content is set to 0.50% or less.
- the Zr content is preferably 0.30% or less.
- the Zr content is preferably 0.01% or more.
- Co 0 to 0.50%
- Co has the effect of improving corrosion resistance and stabilizing the austenite phase. Therefore, it may be contained as needed. However, excessive Co content reduces toughness and workability. Therefore, the Co content is set to 0.50% or less.
- the Co content is preferably 0.30% or less.
- the Co content is preferably 0.01% or more.
- Mg 0 to 0.005% Since Mg has a deoxidizing effect, it forms an oxide with O in steel. Then, at the diffusion interface, it has the effect of reducing non-metal inclusions such as oxides and improving the diffusion bondability. It also has the effect of improving hot workability. Therefore, it may be contained as needed. However, when Mg is excessively contained, the effect of forming oxides in steel is saturated, and oxides are also formed at the diffusion interface. In addition, the manufacturing cost increases and the hot workability decreases. Therefore, the Mg content is set to 0.005% or less. The Mg content is preferably 0.003% or less. On the other hand, in order to obtain the above effect, the Mg content is preferably 0.0001% or more.
- Ga 0 to 0.010% Ga has the effect of improving hot workability. Therefore, it may be contained if necessary. However, if Ga is contained in an excessive amount, the manufacturability is lowered. Therefore, the Ga content is set to 0.010% or less. The Ga content is preferably 0.008% or less. On the other hand, in order to obtain the above effect, the Ga content is preferably 0.001% or more.
- Hf 0 to 0.10% Hf has the effect of improving the strength and the hydrogen gas embrittlement resistance.
- the crystal grains are made finer, it indirectly contributes to the improvement of diffusion bondability. Therefore, it may be contained if necessary. However, if Hf is excessively contained, the workability is lowered. Therefore, the Hf content is set to 0.10% or less.
- the Hf content is preferably 0.005% or less.
- the content of Hf is preferably 0.01% or more.
- REM 0 to 0.10% Since REM has a deoxidizing effect, it forms an oxide with O in steel. Then, at the diffusion interface, it has the effect of reducing non-metal inclusions such as oxides and improving the diffusion bondability. It also has the effect of improving hot workability and corrosion resistance. Therefore, it may be contained as needed. However, when REM is excessively contained, the effect of forming oxides in steel is saturated, and oxides are also formed at the diffusion interface. In addition, the manufacturing cost increases and the hot workability decreases. Therefore, the REM content is set to 0.10% or less. The REM content is preferably 0.05% or less. On the other hand, in order to obtain the above effect, the REM content is preferably 0.01% or more.
- REM refers to a total of 17 elements of Sc, Y and lanthanoid, and the above REM content means the total content of these elements.
- the balance is Fe and impurities.
- the impurity is a component mixed by various factors of raw materials such as ore and scrap, and various factors in the manufacturing process when the steel material is industrially manufactured, and is allowed as long as it does not adversely affect the present invention. Means things.
- the f-number calculated below is defined as an index indicating the stability of the austenite phase. Specifically, the f value calculated by the following equation (i) is set to more than 29.5 and less than 32.5.
- each element symbol in the above formula (i) represents the content (mass%) of each element contained in the steel, and if it is not contained, it is set to zero.
- the f value is set to exceed 29.5.
- the f value is set to less than 32.5.
- the f value is preferably in the range of 30.0 or more and 31.5 or less.
- the austenite-based stainless steel material according to the present invention has a passivation film.
- the formation state of the passive film affects the diffusion bondability. This is because the portion where the passivation film comes into contact becomes a diffusion interface that is substantially bonded. Diffusion bonding is performed at a high temperature and in a non-oxidizing atmosphere.
- the passivation film is an oxide and is reduced in a non-oxidizing atmosphere to expose the metal surface, so that atoms are diffused at the bonding interface and the bonding proceeds. Cr oxide is difficult to reduce and stable in a low oxygen environment.
- each element symbol in the above formula (ii) represents the cation fraction (atomic%) of each element contained in the passive film, and if it is not contained, it is set to zero.
- the middle value of Eq. (Ii) is preferably 4.5 or more, more preferably 4.7 or more, further preferably 5.0 or more, and 5.5 or more. Is extremely preferable.
- the middle value of equation (ii) is 9.0 or more, the manufacturability and corrosion resistance deteriorate. Therefore, the middle value of Eq. (Ii) is preferably less than 9.0, more preferably 8.5 or less, and even more preferably 8.0 or less.
- the cation fraction of each element in the passive film can be measured by the following procedure. Specifically, the measurement is performed using an X-ray photoelectron spectrometer (also referred to as "XPS").
- the X-ray source is AlK ⁇ ray
- the incident X-ray energy is 1486.6 eV
- the X-ray detection angle is 90 °.
- the existence state of each element can be confirmed by detecting the spectrum near the binding energy.
- the integrated intensity of each spectrum can be measured and converted into cation ions excluding the elements C, O, and N to obtain the cation fraction of each element.
- the passivation film in the steel material in the present invention means an oxide film up to 0.01 ⁇ m in the plate thickness (thickness) direction from the surface (rolled surface or processed surface). Further, the cation fraction of the passivation film may be measured by using the rolled surface or the processed surface above and below the plate thickness direction as the surface, and measuring the passivation film formed on either surface in the plate thickness direction from the surface.
- the shape of the austenite-based stainless steel material according to the present invention is not particularly limited, but for example, a steel plate, particularly a thin plate, is preferable. Further, it may have a steel pipe shape. In the case of a thin plate, the plate thickness is preferably about 0.5 to 5.0 mm, and in the case of a steel pipe shape, the wall thickness is preferably about 1.0 to 6.0 mm.
- the austenite-based stainless steel material according to the present invention is preferably used for hydrogen equipment, and is suitable for, for example, hydrogen production equipment, heat exchangers, hydrogen storage tanks, and pressure vessels.
- the austenite-based stainless steel material according to the present invention can be stably manufactured by the manufacturing method described below.
- the shape of the steel material will be described as a steel plate for the sake of simplicity.
- Steel adjusted to the above-mentioned chemical composition is melted and cast by a conventional method to obtain a steel piece to be subjected to hot rolling.
- the chemical composition by containing an arbitrary element that has the effect of refining the crystal, for example, Nb, B, etc., a metal structure having a fine particle size is formed, and grain boundary movement during diffusion bonding is promoted. Therefore, the diffusion bonding resistance is likely to be improved.
- hot rolling is performed by a conventional method.
- the conditions for hot rolling are not particularly limited, but usually, the heating temperature of the steel piece is preferably in the range of 1150 to 1270 ° C., and the rolling reduction is in the range of 60.0 to 99.5%. preferable.
- cold rolling is performed.
- Cold rolling is preferably carried out in the range of a reduction ratio of 40 to 90%, and is preferably a cold-rolled steel sheet (cold-worked material).
- annealing is performed at 900 to 1150 ° C. for 1 second to 10 minutes at an isothermal temperature, and the metal structure of the cold-rolled steel sheet is preferably an austenite structure.
- a descaling treatment as exemplified by pickling. Cold rolling, annealing, and descaling may be repeated a plurality of times.
- the descaling treatment in order to obtain a passivation film satisfying the equation (ii), it is preferable to carry out the treatment by the salt method described later and the high-pressure water spray.
- the steel material in a mixed salt composed of sodium hydroxide, sodium sulfate and the like.
- the mixed salt (hereinafter, also referred to as “salt”) at this time is preferably heated to 450 to 550 ° C. and melted in a melting tank. That is, the immersion temperature in the salt is preferably in the range of 450 to 550 ° C.
- the immersion time at this time is preferably 5 to 10 seconds.
- the immersion temperature in the salt described above is less than 450 ° C., it may be difficult to sufficiently remove the oxide containing Cr. Therefore, the immersion temperature is preferably 450 ° C. or higher. In order to promote the reaction between the steel sheet and the scale, the immersion temperature is preferably more than 500 ° C. On the other hand, when the immersion temperature exceeds 550 ° C., discoloration and salt residue are likely to occur on the surface of the steel sheet. Therefore, the immersion temperature is preferably 550 ° C. or lower.
- the immersion time in the salt is less than 5 seconds, it may be difficult to sufficiently remove the oxide containing Cr. Therefore, considering the reactivity with the scale, the immersion time is preferably 5 seconds or more. On the other hand, if the immersion time is too long, discoloration and salt residue are likely to occur on the surface of the steel sheet. Therefore, the immersion time is preferably 10 seconds or less.
- the pressure of the spray may be about 1 MPa (10 kgf / cm 2 ), and the spray irradiation time may be 60 seconds or less.
- the reason for the above process is due to the following mechanism. Immediately below the Cr-concentrated passivation film and the surface, there are regions where the Cr concentration is lower than the composition of the base metal and Mn and Fe are relatively concentrated. Therefore, the passivation film and the surface where Cr is concentrated are scraped off by polishing to expose the regions where Mn and Fe are concentrated. After that, it is preferable that these elements are naturally oxidized in the atmosphere to form a passivation film in which Mn and Fe are concentrated.
- polishing is performed in a range of up to 10 ⁇ m from the surface in the vertical direction of the plate thickness.
- the polishing method is preferably mechanical polishing, but for example, polishing may be performed using polishing paper, a polishing grindstone, or the like. Moreover, you may use a solid abrasive. If necessary, electrolytic polishing may be performed.
- the surface roughness at this time is preferably adjusted so that Ra is 0.3 ⁇ m or less. Ra is more preferably 0.1 ⁇ m or less.
- the surface roughness may be measured using a contact type surface roughness measuring machine or the like. After that, it is preferable to form a passivation film in which Mn and Fe are concentrated.
- polishing is preferably performed after water spraying, but even if the surface of the steel is ground in advance before cold rolling. Good. If the surface is ground before cold rolling, it may or may not be polished after water spraying. Further, the surface of the steel may be ground before cold rolling, and further polished after water spraying. In this case, the value of the middle value in Eq. (Ii) can be further increased. When grinding the surface of steel before cold rolling, it is preferable to grind the range from the surface to 10 to 20 ⁇ m in the vertical direction of the plate thickness.
- the austenite-based stainless steel material according to the present invention is used, for example, in a hydrogen production apparatus.
- the hydrogen production apparatus is manufactured by the following procedure. Specifically, a hydrogen flow path is created by etching a thin plate of an austenite-based stainless steel material according to the present invention. Subsequently, a plurality of the above thin plates are laminated and diffusion bonded. Diffusion bonding is preferably performed at a high temperature and in a non-oxidizing atmosphere. Specifically, it is desirable to carry out the operation in an inert gas atmosphere such as Ar or N 2, or in a non-oxidizing atmosphere containing a part of the inert gas. It is preferably performed in a temperature range of 900 to 1200 ° C. and a degree of vacuum of 10 -1 to 10 -3 Pa.
- the bonding method may be solid-phase diffusion bonding or liquid-phase diffusion bonding.
- the steel plate is immersed in the melting tank for 5 seconds, and then the spray pressure is 1 MPa (10 kgf / cm 2 ).
- the irradiation time was set to 30 seconds, and high-pressure water spray was performed.
- polishing with a grindstone was performed from the front and back surfaces to 10 ⁇ m in the vertical direction of the plate thickness to obtain a mirror finish.
- the surface of the steel sheet was ground by 10 ⁇ m before cold rolling.
- a passivation film was then formed in the atmosphere.
- the cation fractions of Mn, Fe and Cr in the obtained passive film were measured by the following procedure. Specifically, XPS was used, and in the measurement, the X-ray source was AlK ⁇ rays, the incident X-ray energy was 1486.8 eV, and the X-ray detection angle was 90 °. As a result, the existence state of each element was confirmed by detecting the spectrum near the binding energy.
- the cation fraction of each element was calculated by measuring the integrated intensity of each spectrum described above and converting it into cation ions excluding the elements C, O, and N.
- Hydrogen embrittlement resistance evaluation value ⁇ (tensile breaking strength in 70 MPa hydrogen or breaking elongation) / (tensile breaking strength in 0.1 MPa nitrogen or breaking elongation) ⁇ ⁇ 100 (%) ... (a) When the hydrogen embrittlement resistance evaluation value of the tensile breaking strength calculated from the above formula is 95% or more and the hydrogen embrittlement resistance evaluation value of the tensile elongation at break is 80 to 90%, it is considered that the hydrogen embrittlement resistance is good. , ⁇ .
- the hydrogen embrittlement resistance evaluation value of tensile breaking strength is 95% or more and the hydrogen embrittlement resistance evaluation value of tensile breaking elongation is more than 90%, it is considered that the hydrogen embrittlement resistance is further excellent. Described. On the other hand, when the hydrogen embrittlement resistance evaluation value is less than the above value, it is described as x because the hydrogen embrittlement resistance is poor.
- Diffusion bondability evaluation value (total length of unjoined portion / total length of bonded interface) x 100 (%) ... (b) Then, when the diffusion bondability evaluation value is 30% or less, it is judged that the diffusion bondability is good, and it is marked with ⁇ . Further, when the diffusion bondability evaluation value is less than 10%, it is judged that the diffusion bondability is further good, and it is described by ⁇ . On the other hand, when the diffusion bondability evaluation value is more than 30%, it is judged that the diffusion bondability is poor, and it is marked with x. The results are summarized in Table 2 below.
- the test No. that does not satisfy the provisions of the present invention. In 15 to 21, at least one of hydrogen gas embrittlement resistance and diffusion bonding property was poor. No. In No. 15, the Cu content did not satisfy the provisions of the present invention, so that the diffusion bondability was lowered. No. In No. 16, since the Al content was excessive, it is considered that the Al oxide was not reduced at the diffusion interface and remained as it was, so that the diffusion bondability was deteriorated.
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Abstract
Description
化学組成が、質量%で、
C:0.10%以下、
Si:1.0%以下、
Mn:8.0~10.0%、
P:0.030%以下、
S:0.0030%以下、
Cr:15.0~18.0%、
Ni:7.0~9.0%、
N:0.15~0.25%、
Al:0.005~0.20%、
Ca:0.0005~0.01%、
Cu:1.0%未満、
Mo:1.0%未満、
B:0~0.0050%、
Nb:0~0.50%、
Ti:0~0.50%、
V:0~0.50%、
W:0~0.50%、
Zr:0~0.50%、
Co:0~0.50%、
Mg:0~0.005%、
Ga:0~0.010%、
Hf:0~0.10%、
REM:0~0.10%、
残部:Feおよび不純物であり、
下記(i)式で算出されるf値が、29.5超32.5未満である、オーステナイト系ステンレス鋼材。
f値=Ni+0.72Cr+0.88Mo+1.11Mn-0.27Si+0.53Cu+12.93C+7.55N ・・・(i)
但し、上記(i)式中の各元素記号は、鋼中に含まれる各元素の含有量(質量%)を表し、含有されない場合はゼロとする。
B:0.0002~0.050%、
Nb:0.01~0.50%、
Ti:0.01~0.50%、
V:0.01~0.50%、
W:0.001~0.50%、
Zr:0.01~0.50%、
Co:0.01~0.50%、
Mg:0.0001~0.005%、
Ga:0.001~0.010%、
Hf:0.01~0.10%、および
REM:0.01~0.10%、
から選択される一種以上を含有する、上記(1)に記載のオーステナイト系ステンレス鋼材。
4.5≦(Mn+Fe)/Cr<9.0 ・・・(ii)
但し、上記(ii)式中の各元素記号は、前記不働態皮膜中に含まれる各元素のカチオン分率(原子%)を表し、含有されない場合はゼロとする。
各元素の限定理由は下記のとおりである。なお、以下の説明において、特段の記載が無い場合、含有量についての「%」は、「質量%」を意味する。また、後述する化学組成は、鋼材全体の平均の化学組成である。
Cは、オーステナイト相の安定化に有効な元素であり、耐水素ガス脆化性の向上にも寄与する。しかしながら、過剰なCの含有は、Cr系炭化物が接合界面での析出および粒界での析出を助長し、拡散接合性と耐食性とを低下させる。このため、C含有量は、0.10%以下とする。C含有量は、0.08%以下とするのが好ましく、0.07%以下とするのがより好ましい。一方、上記効果を得るためには、C含有量は、0.01%以上とするのが好ましい。また、f値を高め、耐水素ガス脆化性を維持したい場合は、C含有量は、0.03%以上とするのが好ましく、0.04%以上とするのがより好ましい。
Siは、脱酸効果を有するが、Si含有量が過剰であると、接合界面において酸化物を形成することで、表面清浄性を低下させ、拡散接合性を低下させる。このため、Si含有量は、1.0%以下とする。Si含有量は、0.8%以下とするのが好ましく、0.7%以下とするのがより好ましく、0.6%以下とするのがさらに好ましい。一方、上記効果を得るためには、Si含有量は、0.1%以上とするのが好ましく、0.2%以上とするのがより好ましく、0.3%以上とするのがさらに好ましい。
Mnは、オーステナイト相の安定化に有効な元素であり、耐水素ガス脆化性の向上に寄与する。また、不働態皮膜中に濃化して拡散接合性の向上にも有効な元素である。このため、Mn含有量は8.0%以上とする。Mn含有量は、8.5%以上とするのが好ましく、9.0%以上とするのがより好ましい。しかしながら、Mnを過剰に含有させると、水素脆化感受性の高いε相の生成を助長し、耐水素ガス脆化性を低下させる。このため、Mn含有量は、10.0%以下とする。
Pは、不純物として鋼に含有される元素であり、非金属介在物を形成させ、拡散接合性を低下させる場合がある。このため、P含有量は、0.030%以下とする。P含有量は、0.025%以下とするのが好ましく、0.015%以下とするのがより好ましい。しかしながら、P含有量を過剰に低減すると、原料および製造コストが増加する。このため、P含有量は、0.005%以上とするのが好ましい。
Sは、不純物として鋼に含有される元素であり、非金属介在物を形成させ、拡散接合性を低下させる。このため、S含有量は、0.0030%以下とする。S含有量は、0.0020%以下とするのが好ましく、0.0010%以下とするのがより好ましい。しかしながら、S含有量を過剰に低減すると、製造コストが増加する。また、これに加え、熱間加工性が低下する。このため、S含有量は、0.0001%以上とするのが好ましい。
Crは、ステンレス鋼において一定量含有させる元素であり、耐食性、特に耐候性を向上させる効果を有する。このため、Cr含有量は、15.0%以上とする。しかしながら、Crはフェライト形成元素である。このため、Crを過剰に含有させると、オーステナイト相を不安定化させ、耐水素ガス脆化性を低下させる。さらに、過剰なCrが不働態皮膜中へ濃化し、拡散接合性を低下させる。このため、Cr含有量は、18.0%以下とする。Cr含有量は、17.0%以下とするのが好ましく、16.0%以下とするのがより好ましい。
Niは、Mnとともに、耐水素ガス脆化性を確保するために必要な元素である。このため、Ni含有量は、7.0%以上とする。しかしながら、過剰にNiを含有させると、製造コストが増加する。また、再結晶温度が上昇することで、拡散接合性が低下する。このため、Ni含有量は、9.0%以下とする。Ni含有量は、8.5%以下とするのが好ましく、8.0%以下とするのがより好ましい。
Nは、MnおよびNiと同様に、耐水素ガス脆化性の向上に有効な元素である。このため、N含有量は、0.15%以上とする。N含有量は、0.17%以上とするのが好ましい。しかしながら、Nを過剰に含有させると、溶製時のブローホール等、内部欠陥が発生する場合があり、製造性を低下させる。このため、N含有量は、0.25%以下とする。N含有量は、0.22%以下とするのが好ましく、0.20%以下とするのがより好ましい。
Alは、脱酸効果を有する元素であり、鋼中のOを低減するために必要な元素である。本発明に係るオーステナイト系ステンレス鋼材においては、拡散接合性の観点から、O含有量は、0.003%以下にまで低減するのが望ましい。このように、脱酸効果により酸化物系の非金属介在物を低減することができるため、Alを含有させることで、拡散接合性を向上させることができる。したがって、Al含有量は、脱酸効果を発揮させるため、0.005%以上とする。Al含有量は、0.010%以上とするのが好ましく、0.020%以上とするのがより好ましい。しかしながら、Alを過剰に含有させると、鋼中での酸化物の形成効果が飽和し、拡散界面においても還元されにくい酸化物が形成する。この結果、耐拡散接合性が低下する。このため、Al含有量は、0.20%以下とする。Al含有量は、0.10%以下とするのが好ましく、0.05%以下とするのがより好ましく、0.04%以下とするのがさらに好ましい。
Caも、Alと同様に、脱酸効果を有し、鋼中でOを低減させる効果を有する。また、鋼中で、硫化物を形成し、Sを固定化する。このように、鋼中で非金属介在物を形成させることで、拡散界面における非金属介在物を低減し、拡散接合性を向上させる効果を有する。このため、Ca含有量は、0.0005%以上とする。Ca含有量は、0.001%以上とするのが好ましく、0.002%以上とするのがより好ましい。しかしながら、Caを過剰に含有させると、鋼中での酸化物の形成効果が飽和し、拡散界面においても還元されにくい酸化物が形成する。この結果、耐拡散接合性が低下する。このため、Ca含有量は、0.01%以下とする。Ca含有量は、0.005%以下とするのが好ましい。
Cuは、局所的な転位密度の上昇を抑制して均一なオーステナイト相の加工組織を形成するのに有効である。このため、水素ガス脆化を抑制するのに有効な元素である。しかしながら、Cuを過度に含有させた場合、拡散接合性が低下する場合もある。融点が比較的低いCuは、接合時の高温、無酸化雰囲気において、拡散界面に濃化し、溶融しやすくなる。この際、界面に液膜を形成し、界面での接合を阻害すると考えられるからである。このため、Cu含有量は、1.0%未満とする。Cu含有量は、0.5%以下とするのが好ましく、0.3%以下とするのがより好ましく、0.05%未満とするのがさらに好ましい。しかしながら、Cu含有量を過剰に低減すると、溶解原料の制約を招き、製造コストが増加する。さらに、熱間加工性も低下する。このため、Cu含有量は、0.01%以上とするのが好ましい。
Moは、スクラップ等の原料から混入する元素であるが、過剰に含有させると、δフェライト相の生成を促進させ、耐水素ガス脆化性を低下させる。このため、Mo含有量は、1.0%未満とする。Mo含有量は、0.5%以下とするのが好ましい。一方、Mo含有量を過剰に低減すると、溶解原料の制約を招き、製造コストが増加する。このため、Mo含有量は、0.01%以上とするのが好ましい。
Bは、結晶粒界への偏析により、粒界強化とともに鋼材の結晶粒を微細にする。この結果、拡散接合時の粒界移動が促進されるため、間接的に拡散接合性を向上させる効果を有する。また、製造性を向上させる効果も有する。このため、必要に応じて含有させてもよい。しかしながら、Bを過剰に含有させると、再結晶温度を上昇させることで、拡散接合性が低下する。このため、B含有量は、0.0050%以下とする。B含有量は、0.0030%以下とするのが好ましい。一方、上記効果を得るためには、B含有量は、0.0002%以上とするのが好ましい。
Nbは、炭化物または炭窒化物を形成し、鋼材の結晶粒を微細にする。この結果、拡散接合時の粒界移動が促進されるため、間接的に、拡散接合性を向上させる効果を有する。このため、必要に応じて含有させてもよい。しかしながら、Nbを過剰に含有させると、再結晶温度を上昇させることで、拡散接合性が低下する。このため、Nb含有量は、0.50%以下とする。Nb含有量は、0.30%以下とするのが好ましい。一方、上記効果を得るためには、Nb含有量は、0.01%以上とするのが好ましい。
Tiは、鋼中にC、Nを固定化し、鋼中で非金属介在物を形成させ、拡散界面において非金属介在物を低減させる。この結果、Tiは、拡散接合性を向上させる効果を有する。このため、必要に応じて含有させてもよい。しかしながら、Tiを過剰に含有させると、鋼中での非金属介在物の形成効果が飽和し、拡散界面においても非金属介在物が形成する。このため、Ti含有量は、0.50%以下とする。Ti含有量は、0.30%以下とするのが好ましい。一方、上記効果を得るためには、Ti含有量は、0.01%以上とするのが好ましい。
Vは、鋼中に固溶または炭窒化物として析出し、強度を向上させる効果を有する。このため、必要に応じて含有させてもよい。しかしながら、Vを過剰に含有させると、炭窒化物が過剰に形成し、拡散接合性および熱間加工時の製造性を低下させる。このため、V含有量は、0.50%以下とする。V含有量は、0.30%以下とするのが好ましい。一方、上記効果を得るためには、V含有量は、0.01%以上とするのが好ましい。
Wは、強度および耐食性を向上させる効果を有する。このため、必要に応じて含有させてもよい。しかしながら、Wを過剰に含有させると、製造コストが増加する。このため、W含有量は、0.50%以下とする。W含有量は、0.30%以下とするのが好ましい。一方、上記効果を得るためには、W含有量は、0.001%以上とするのが好ましい。
Zrは、脱酸効果を有し、酸化物を形成することで、拡散接合性を向上させる効果を有する。また、耐食性を向上させる効果を有する。このため、必要に応じて含有させてもよい。しかしながら、Zrを過剰に含有させると、靭性および加工性が低下する。このため、Zr含有量は、0.50%以下とする。Zr含有量は、0.30%以下とするのが好ましい。一方、上記効果を得るためには、Zr含有量は、0.01%以上とするのが好ましい。
Coは、耐食性を向上させ、オーステナイト相を安定化させる効果を有する。このため、必要に応じて含有させてもよい。しかしながら、Coを過剰に含有させると、靱性および加工性が低下する。このため、Co含有量は、0.50%以下とする。Co含有量は、0.30%以下とするのが好ましい。一方、上記効果を得るためには、Co含有量は、0.01%以上とするのが好ましい。
Mgは、脱酸効果を有するため、鋼中でOとの酸化物を形成する。そして、拡散界面において、酸化物といった非金属介在物を低減させ、拡散接合性を向上させる効果を有する。また、熱間加工性を向上させる効果も有する。このため、必要に応じて含有させてもよい。しかしながら、Mgを過剰に含有させると、鋼中での酸化物の形成効果が飽和し、拡散界面においても酸化物が形成する。また、製造コストが増加し、熱間加工性が低下する。このため、Mg含有量は、0.005%以下とする。Mg含有量は、0.003%以下とするのが好ましい。一方、上記効果を得るためには、Mg含有量は、0.0001%以上とするのが好ましい。
Gaは、熱間加工性を向上させる効果を有する。このため、必要に応じて、含有させてもよい。しかしながら、Gaを過剰に含有させると、製造性を低下させる。このため、Ga含有量は、0.010%以下とする。Ga含有量は、0.008%以下とするのが好ましい。一方、上記効果を得るためには、Ga含有量は、0.001%以上とするのが好ましい。
Hfは、強度を向上させ、耐水素ガス脆化性を向上させる効果を有する。また、結晶粒を微細化させるため、間接的に拡散接合性の向上にも寄与する。このため、必要に応じて、含有させてもよい。しかしながら、Hfを過剰に含有させると、加工性が低下する。このため、Hf含有量は、0.10%以下とする。Hf含有量は、0.005%以下とするのが好ましい。一方、上記効果を得るためには、Hfが含有量は、0.01%以上とするのが好ましい。
REMは、脱酸効果を有するため、鋼中でOとの酸化物を形成する。そして、拡散界面において、酸化物といった非金属介在物を低減させ、拡散接合性を向上させる効果を有する。また、熱間加工性および耐食性を向上させる効果も有する。このため、必要に応じて含有させてもよい。しかしながら、REMを過剰に含有させると、鋼中での酸化物の形成効果が飽和し、拡散界面においても酸化物が形成する。また、製造コストが増加し、熱間加工性が低下する。このため、REM含有量は、0.10%以下とする。REM含有量は、0.05%以下とするのが好ましい。一方、上記効果を得るためには、REM含有量は、0.01%以上とするのが好ましい。
本発明に係るオーステナイト系ステンレス鋼材では、オーステナイト相の安定性を示す指標として、以下に算出されるf値を規定する。具体的には、下記(i)式で算出されるf値を、29.5超32.5未満とする。
但し、上記(i)式中の各元素記号は、鋼中に含まれる各元素の含有量(質量%)を表し、含有されない場合はゼロとする。
本発明に係るオーステナイト系ステンレス鋼材は、不働態皮膜を有する。上述したように、不働態皮膜の形成状況は、拡散接合性に影響を及ぼす。これは、不働態皮膜が接触する部分が、実質的に接合される拡散界面となるからである。拡散接合は、高温、無酸化雰囲気で行われる。ここで、不働態皮膜は酸化物であり無酸化雰囲気下で還元されて金属表面が露出することで、接合界面において原子の拡散が生じて、接合が進む。Cr酸化物は低酸素環境下で還元し難く安定である。このため、上述した温度、低酸素環境下において、還元されやすい、Mn、およびFe酸化物の比率が高い不働態皮膜を形成していることが好ましい。したがって、不働態皮膜中における化学組成のカチオン分率が、下記(ii)式を満足するのが好ましい。
但し、上記(ii)式中の各元素記号は、不働態皮膜中に含まれる各元素のカチオン分率(原子%)を表し、含有されない場合はゼロとする。
本発明に係るオーステナイト系ステンレス鋼材の形状は特に限定しないが、例えば、鋼板、特に薄板であるのが好ましい。また、鋼管形状としてもよい。薄板の場合は、板厚0.5~5.0mm程度であるのが好ましく、鋼管形状の場合は肉厚1.0~6.0mm程度であるのが好ましい。そして、本発明に係るオーステナイト系ステンレス鋼材の用途は、水素用機器に用いられるのが好ましく、例えば、水素製造装置、熱交換器、水素貯蔵用タンク、圧力容器に好適である。
本発明に係るオーステナイト系ステンレス鋼材は、以下に記載の製造方法により安定して製造することができる。
得られた不働態皮膜中のMn、FeおよびCrのカチオン分率は以下の手順で測定した。具体的には、XPSを用い、測定においては、X線源は、AlKα線とし、入射X線エネルギーは1486.8eVとし、X線の検出角度は90°とした。これにより、結合エネルギー付近におけるスペクトルの検出により、各元素の存在状態を確認した。各元素のカチオン分率は、上述の各スペクトルの積分強度を測定し、C、O、Nの元素を除くカチオンイオン換算で算出した。
耐水素ガス脆化性については、得られた鋼板について平行部の幅4±0.03mm、長さ20mm±0.01mmの板状の引張試験片を採取した。続いて、上記引張試験片を-40℃、70MPa水素中および0.1MPa窒素中において歪速度5×10-5/sの低歪引張試験(以下、単に「SSRT試験」と記載する。)を行った。SSRT試験の評価で引張破断強さと引張破断伸びを測定した。耐水素ガス脆化性は、耐水素脆性評価値を用いて評価した。耐水素脆性評価値は以下の式に基づいて、算出することができる。
上記式から算出された引張破断強さの耐水素脆性評価値が95%以上かつ引張破断伸びの耐水素脆性評価値が80~90%の場合を、良好な耐水素ガス脆化性を有するとして、〇と記載した。同様に、引張破断強さの耐水素脆性評価値が95%以上かつ引張破断伸びの耐水素脆性評価値が90%超である場合を、さらに耐水素ガス脆化性が優れているとして◎と記載した。一方、耐水素脆性評価値が上記数値に満たない場合を耐水素ガス脆化性が不良であるとして、×と記載した。
拡散接合性については、得られた鋼板について、50mm角形状の板を3枚作製した。上記板同士を積層し、真空度1.3×10-2~1.0×10-3Paの真空中で、300℃/hで1150℃へ昇温後、接触面圧が500g/mm2でホットプレスによる加圧状態を3h保持し、拡散接合を行った。得られた接合体について、接合界面が観察できるように組織観察を行い、接合界面の合計長さに対する未接合部の長さの割合を、百分率(以下「拡散接合性評価値」と記載する。)で算出した。算出式は、以下のとおりである。
そして、拡散接合性評価値が30%以下である場合を拡散接合性が良好であると判断し、○で記載した。また、拡散接合性評価値が10%未満である場合を、さらに拡散接合性が良好であると判断し、◎で記載した。一方、拡散接合性評価値が30%超である場合を拡散接合性が不良であると判断し、×と記載した。以下、結果をまとめて表2に示す。
Claims (5)
- 表面に不働態皮膜を有するオーステナイト系ステンレス鋼材であって、
化学組成が、質量%で、
C:0.10%以下、
Si:1.0%以下、
Mn:8.0~10.0%、
P:0.030%以下、
S:0.0030%以下、
Cr:15.0~18.0%、
Ni:7.0~9.0%、
N:0.15~0.25%、
Al:0.005~0.20%、
Ca:0.0005~0.01%、
Cu:1.0%未満、
Mo:1.0%未満、
B:0~0.0050%、
Nb:0~0.50%、
Ti:0~0.50%、
V:0~0.50%、
W:0~0.50%、
Zr:0~0.50%、
Co:0~0.50%、
Mg:0~0.005%、
Ga:0~0.010%、
Hf:0~0.10%、
REM:0~0.10%、
残部:Feおよび不純物であり、
下記(i)式で算出されるf値が、29.5超32.5未満である、オーステナイト系ステンレス鋼材。
f値=Ni+0.72Cr+0.88Mo+1.11Mn-0.27Si+0.53Cu+12.93C+7.55N ・・・(i)
但し、上記(i)式中の各元素記号は、鋼中に含まれる各元素の含有量(質量%)を表し、含有されない場合はゼロとする。 - 前記化学組成が、質量%で、
B:0.0002~0.0050%、
Nb:0.01~0.50%、
Ti:0.01~0.50%、
V:0.01~0.50%、
W:0.001~0.50%、
Zr:0.01~0.50%、
Co:0.01~0.50%、
Mg:0.0001~0.005%、
Ga:0.001~0.010%、
Hf:0.01~0.10%、および
REM:0.01~0.10%、
から選択される一種以上を含有する、請求項1に記載のオーステナイト系ステンレス鋼材。 - 前記不働態皮膜中における化学組成のカチオン分率が、下記(ii)式を満足する、請求項1または2に記載のオーステナイト系ステンレス鋼材。
4.5≦(Mn+Fe)/Cr<9.0 ・・・(ii)
但し、上記(ii)式中の各元素記号は、前記不働態皮膜中に含まれる各元素のカチオン分率(原子%)を表し、含有されない場合はゼロとする。 - 鋼材形状が薄板である、請求項1~3のいずれか1項に記載のオーステナイト系ステンレス鋼材。
- 水素製造装置に用いられる、請求項1~4のいずれか1項に記載のオーステナイト系ステンレス鋼材。
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JP2003041349A (ja) * | 2001-08-01 | 2003-02-13 | Nisshin Steel Co Ltd | 電気抵抗材料 |
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EP4089186A1 (en) | 2022-11-16 |
TW202132585A (zh) | 2021-09-01 |
JP7270777B2 (ja) | 2023-05-10 |
US20230047414A1 (en) | 2023-02-16 |
KR20220124234A (ko) | 2022-09-13 |
CN114929919A (zh) | 2022-08-19 |
TWI757044B (zh) | 2022-03-01 |
EP4089186A4 (en) | 2023-06-28 |
JPWO2021141099A1 (ja) | 2021-07-15 |
CN114929919B (zh) | 2023-05-05 |
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