WO2016072244A1 - Matériau en acier inoxydable destiné à la liaison par diffusion - Google Patents

Matériau en acier inoxydable destiné à la liaison par diffusion Download PDF

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WO2016072244A1
WO2016072244A1 PCT/JP2015/079342 JP2015079342W WO2016072244A1 WO 2016072244 A1 WO2016072244 A1 WO 2016072244A1 JP 2015079342 W JP2015079342 W JP 2015079342W WO 2016072244 A1 WO2016072244 A1 WO 2016072244A1
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stainless steel
less
diffusion bonding
phase
steel material
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PCT/JP2015/079342
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English (en)
Japanese (ja)
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淳史 須釜
景岡　一幸
芳明 堀
一成 今川
学 奥
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日新製鋼株式会社
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Priority to SG11201703499XA priority Critical patent/SG11201703499XA/en
Priority to US15/523,882 priority patent/US20170321311A1/en
Priority to EP15857850.0A priority patent/EP3216888B1/fr
Priority to KR1020177015017A priority patent/KR102384698B1/ko
Priority to ES15857850T priority patent/ES2886446T3/es
Priority to CN201580056844.0A priority patent/CN107002189B/zh
Publication of WO2016072244A1 publication Critical patent/WO2016072244A1/fr

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    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • 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
    • C22C38/001—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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to a duplex stainless steel material used for a molded product to be diffusion bonded.
  • Stainless steel diffusion bonding products assembled by diffusion bonding are applied to various uses such as heat exchangers, machine parts, fuel cell parts, household appliance parts, plant parts, decorative component members, and building materials.
  • the diffusion bonding method includes “insert material insertion method” in which an insert material is inserted into the bonding interface and bonded by solid phase diffusion or liquid phase diffusion, and “directly” in which the surfaces of both stainless steel materials are in direct contact with each other. Law ".
  • the insert material insertion method is advantageous in that reliable diffusion bonding can be realized relatively easily.
  • this method since this method uses an insert material, it is disadvantageous compared to the direct method in that the cost increases and the joint portion is formed of a different type of metal from the base material, which may reduce the corrosion resistance. It becomes.
  • the direct method is generally difficult to obtain sufficient bonding strength as compared with the insert material insertion method.
  • this direct method since this direct method has the possibility of being advantageous in terms of reducing manufacturing costs, various methods have been studied. For example, in Patent Document 1, the amount of S in stainless steel is 0.01% by weight or less and diffusion bonding is performed in a non-oxidizing atmosphere at a predetermined temperature to avoid deformation of the material and A technique for improving diffusion bonding is disclosed.
  • Patent Document 2 discloses a method of using a stainless steel foil material having irregularities on the surface by pickling treatment.
  • Patent Document 3 discloses a method in which stainless steel with a suppressed Al content is used as a material to be joined so that an alumina coating that becomes an impediment to diffusion bonding is difficult to form during diffusion bonding.
  • Patent Document 4 discloses a method of promoting diffusion using a stainless steel foil that has been deformed by cold working.
  • Patent Documents 5 and 6 describe ferritic stainless steel for direct diffusion bonding with an optimized component composition.
  • Patent Document 7 a method for manufacturing a diffusion bonded article by the direct method, which can be carried out with a work load equivalent to that of the insert material insertion method without applying heating or high surface pressure.
  • Patent Documents 9 and 10 a method for manufacturing a diffusion bonded article by the direct method, which can be carried out with a work load equivalent to that of the insert material insertion method without applying heating or high surface pressure.
  • Patent Documents 9 and 10 a method for manufacturing a diffusion bonded article by the direct method, which can be carried out with a work load equivalent to that of the insert material insertion method without applying heating or high surface pressure.
  • Patent Documents 9 and 10 a method for manufacturing a diffusion bonded article by the direct method, which can be carried out with a work load equivalent to that of the insert material insertion method without applying heating or high surface pressure.
  • Patent Documents 9 and 10 a method for controlling the surface roughness before joining of the used stainless steel material in order to ensure good joining properties. Therefore, further improvement in bondability is required for stainless steel materials used for diffusion bonding
  • An object of the present invention is to provide a stainless steel material that is not affected by the degree of surface roughness and that is suitable for a diffusion bonding molded product having further improved diffusion bonding properties.
  • the present inventors have controlled the average crystal grain size, ⁇ max amount, and creep elongation before diffusion bonding for a duplex stainless steel material having a duplex structure consisting of at least two of a ferrite phase, a martensite phase, and an austenite phase. As a result, it was found that good diffusion bondability was obtained without being affected by the surface roughness of the steel material, and the present invention was completed as a stainless steel material for diffusion bonding. Specifically, the present invention provides the following.
  • the present invention is a dual-phase stainless steel material in which the metal structure before diffusion bonding has a multi-phase structure composed of at least two of a ferrite phase, a martensite phase, or an austenite phase, and the average of the multi-phase structure
  • the crystal grain size is 20 ⁇ m or less
  • ⁇ max represented by the following formula (a) is 10 to 90
  • the creep elongation is 0.2% or more when a 1.0 MPa load is applied at 1000 ° C. for 0.5 h. It is a stainless steel material for diffusion bonding.
  • ⁇ max 420C-11.5Si + 7Mn + 23Ni-11.5Cr-12Mo + 9Cu-49Ti-47Nb-52Al + 470N + 189 (a) where the element symbol in the above formula (a) means the content (mass%) of each element. To do.
  • the stainless steel material is mass%, C: 0.2% or less, Si: 1.0% or less, Mn: 3.0% or less, P: 0.05% or less, S: 0.03% or less, Ni: 10.0% or less, Cr: 10.0 to 30.0%, N: 0.3% or less, Ti: 0.15% or less, Al: 0.15% or less
  • the balance is the stainless steel material for diffusion bonding according to (1), wherein the balance is made of Fe and inevitable impurities, and the total amount of Ti and Al is 0.15% or less.
  • the stainless steel material further includes, in mass%, Nb: 4.0% or less, Mo: 0.01 to 4.0%, Cu: 0.01 to 3.0%, V: The stainless steel material for diffusion bonding according to (1) or (2) above, comprising one or more of 0.03 to 0.15%.
  • the stainless steel material for diffusion bonding according to any one of the above (1) to (3), wherein the stainless steel material further contains B: 0.0003 to 0.01% by mass%. It is.
  • a duplex stainless steel having a duplex structure composed of at least two of a ferrite phase, a martensite phase, and an austenite phase is obtained by creeping at an average crystal grain size and ⁇ max before diffusion bonding, and at a bonding temperature.
  • a stainless steel material having excellent diffusion bonding properties is provided, and thus a diffusion bonding molded product exhibiting a good bonding interface is provided.
  • a diffusion bonded molded article with improved diffusion bonding properties can be obtained.
  • diffusion bonding by a direct method of stainless steel material is (i) a process in which the unevenness of the joint surface is deformed and brought into close contact, and the joint area of the joined part increases, and (ii) joining at the tight part
  • the process is considered to be completed by three processes: a process in which the surface oxide film of the former steel material disappears and (iii) a process in which the residual gas in the void which is an unjoined part reacts with the base material. ing.
  • the inventors have so far focused on the process of (ii) above to regulate the base material component, the component contained in the passive film, and the surface roughness of the joint surface, and the industrial productivity becomes a bottleneck.
  • the step (ii) is controlled, it may be difficult to ensure industrially stable bondability, and in order to obtain stable bondability in consideration of the step (i).
  • Much research has been conducted on steel materials. As a result, it has been found that when the stainless steel used for diffusion bonding is a dual phase stainless steel having a double phase structure, it is extremely effective to make the crystal grain size before diffusion bonding fine.
  • Multiphase structure Stainless steel is generally classified into austenitic stainless steel, ferritic stainless steel, martensitic stainless steel, and the like based on the metal structure at room temperature.
  • the “multiphase structure” of the present invention has a metal structure composed of at least two of a ferrite phase, a martensite phase, and an austenite phase.
  • the “multi-phase stainless steel material” of the present invention has such a multi-phase structure, and refers to a steel having an austenite + ferrite two-phase structure in the joining temperature range.
  • Such a two-phase stainless steel may include a stainless steel classified as a ferritic stainless steel or a martensitic stainless steel.
  • the stainless steel material used for diffusion bonding has a multiphase structure composed of at least two types of ferrite phase, martensite phase, and austenite phase.
  • Use duplex stainless steel in this stainless steel, in the temperature range where diffusion bonding proceeds, a part of the ferrite phase and the martensite phase is transformed into the austenite phase, and a two-phase structure of austenite phase + ferrite phase is obtained.
  • a fine structure is maintained, and creep deformation estimated to be caused by grain boundary sliding can easily occur.
  • easy deformation is promoted in the concavo-convex portion of the bonding surface, and the bonding area of the bonded portion is increased, thereby enabling diffusion bonding by a direct method at a low temperature and low surface pressure.
  • the duplex stainless steel material of the present invention can be used for both or one of the stainless steel materials that are brought into direct contact and integrated by diffusion bonding.
  • the stainless steel material of the present invention can be applied, other two-phase steel types, austenitic steel types that become austenite single phase in the heating temperature range of diffusion bonding, ferritic steel types that become ferrite single phase Etc. can be applied.
  • the component elements other than Ti and Al are not particularly required from the viewpoint of diffusion bonding properties, and various component compositions can be adopted depending on the application.
  • the present invention targets an austenite + ferrite two-phase structure in the temperature range where diffusion bonding proceeds, it is necessary to employ a steel having a component composition satisfying ⁇ max of 10 to 90 represented by the following formula (a). is there.
  • Specific examples of the component composition range include the following.
  • Nb 4.0% or less
  • Mo 0.01-4.0%
  • Cu 0.01-3.0%
  • V 0.03-0.15%
  • B 0.0003 to 0.01% by mass%.
  • the C improves the strength and hardness of steel by solid solution strengthening.
  • the C content is preferably 0.2% by mass or less, and more preferably 0.08% by mass or less.
  • Si is an element used for deoxidation of steel. On the other hand, if the Si content is excessive, the toughness and workability of steel are reduced. In addition, a strong surface oxide film is formed to inhibit diffusion bonding. Therefore, the Si content is preferably 1.0% by mass or less, and more preferably 0.6% by mass or less.
  • Mn is an element that improves high-temperature oxidation characteristics. On the other hand, if the Mn content is excessive, the steel is work-hardened and the cold workability of the steel is reduced. Therefore, the Mn content is preferably 3.0% by mass or less.
  • the P content is preferably 0.05% by mass or less, and more preferably 0.03% by mass or less.
  • the S content is preferably 0.03% by mass or less.
  • Ni is an austenite-forming element and has the effect of improving the corrosion resistance of steel in a reducing acid environment.
  • the Ni content is excessive, the austenite phase becomes stable and the growth of ferrite crystals cannot be suppressed. Therefore, a stable austenite single phase is formed to suppress the growth of ferrite crystals. Therefore, the Ni content is preferably 10.0% or less.
  • Cr is an element that forms a passive film and imparts corrosion resistance. If the Cr content is less than 30.0% by mass, the effect of imparting corrosion resistance is not sufficient. When it exceeds 10.0 mass%, workability will fall. Therefore, the Cr content is preferably 10.0 to 30.0% by mass.
  • N is an unavoidable impurity and is preferably 0.3% by mass or less in order to deteriorate the cold workability.
  • Ti has an effect of fixing C and N, and is therefore an effective element for improving corrosion resistance and workability.
  • Al is often added as a deoxidizer.
  • Ti and Al are easily oxidizable elements, Ti oxide and Al oxide contained in the oxide film on the surface of the steel material are difficult to be reduced in the heat treatment of vacuum diffusion bonding. Therefore, if these Ti oxides and Al oxides are large, the progress of the process (ii) may be hindered during diffusion bonding, so the Ti content is 0.15% by mass or less, and the Al content is 0.15 mass% or less is preferable, and 0.05 mass% is more preferable.
  • the total content of Ti and Al is preferably 0.15% by mass or less, and more preferably 0.05% by mass or less.
  • Nb is an element that forms carbides or carbonitrides and refines the crystal grains of steel to increase the toughness.
  • the Nb content is preferably 4.0% by mass or less.
  • Mo is an element that has the effect of improving the corrosion resistance without reducing the strength. If the Mo content is excessive, the workability of the steel is reduced, so the Mo content is preferably 0.01 to 4.0% by mass.
  • Cu is an element that is effective in improving the corrosion resistance and has an action of generating a ferrite phase.
  • the Cu content is preferably 0.01 to 3.0% by mass.
  • V is an element that contributes to improving the workability and toughness of steel by fixing solute C as carbide.
  • the V content is preferably 0.03 to 0.15%.
  • B is an element that contributes to improvement of corrosion resistance and workability by fixing N.
  • the B element is contained excessively, the hot workability of the steel is lowered, so the B content is preferably 0.0003 to 0.01%.
  • ⁇ max 420C-11.5Si + 7Mn + 23Ni-11.5Cr-12Mo + 9Cu-49Ti-47Nb-52Al + 470N + 1189 (a) where, in the above equation (a), the element symbols such as C and Si are the contents of each element. (Mass%) is meant.
  • ⁇ max is an index representing the amount (volume%) of the austenite phase that is generated when heated and held at about 1100 ° C.
  • ⁇ max is 100 or more, it can be regarded as a steel type that becomes an austenite single phase.
  • ⁇ max is 0 or less, it can be regarded as a steel type that becomes a ferrite single phase.
  • ⁇ max is 10 to 90, the two phases become austenite + ferrite in the temperature range where diffusion bonding proceeds, and these two phases suppress the growth of crystal grains at high temperatures. Therefore, it is effective for obtaining a fine crystal structure. More preferably, ⁇ max is 50-80.
  • the process (i) can be rapidly advanced. Therefore, the average crystal grain size before bonding is preferably 20 ⁇ m or less, and more preferably 10 ⁇ m or less.
  • the surface of the stainless steel material is preferably smooth, and the surface roughness Ra is preferably 0.3 ⁇ m or less.
  • the stainless steel material of the present invention provides a diffusion bonded product with good bondability by performing vacuum diffusion bonding by a direct method.
  • a specific diffusion bonding treatment for example, in a state of direct contact at a contact surface pressure of 0.1 to 1.0 MPa, a pressure of 1.0 ⁇ 10 ⁇ 2 Pa or less, preferably 1.0 ⁇ 10 ⁇ Diffusion bonding can be advanced by heating and maintaining at 900 to 1100 ° C. in a furnace having a pressure of 3 Pa or less and a dew point of ⁇ 40 ° C. or less.
  • the holding time can be adjusted in the range of 0.5 to 3 h.
  • the stainless steel having the chemical composition shown in Table 1 was melted by 30 kg of vacuum melting, and the obtained steel ingot was forged into a 30 mm thick plate, followed by hot rolling at 1230 ° C. for 2 hours and 3.0 mm. A thick hot-rolled sheet was obtained. Subsequently, annealing, pickling, and cold rolling were performed to obtain a cold-rolled sheet having a thickness of 1.0 mm. Then, the cold-rolled sheet was annealed as described later to produce a cold-rolled sheet, which was used as a test material.
  • Table 1 shows a plurality of steel materials.
  • the metal structure before diffusion bonding is a ferrite + martensite duplex steel ( ⁇ + M phase).
  • the metal structure before diffusion bonding is a ferrite + austenite dual phase steel ( ⁇ + ⁇ phase).
  • the metal structure before diffusion bonding is a ferritic single phase steel ( ⁇ phase).
  • the metal structure before diffusion bonding is an austenitic single phase steel ( ⁇ phase).
  • M-1 steel is martensitic single phase steel (M phase) before diffusion bonding.
  • Each steel plate was obtained by changing the annealing temperature after cold rolling between 900 ° C. and 1200 ° C. to obtain test materials having different average crystal grain sizes.
  • the test material from which surface roughness Ra differs was obtained by changing the finishing process of a cold-rolled annealing board using some steel plates.
  • the average crystal grain size ( ⁇ m) of the steel sheet before diffusion bonding was measured by a quadrature method as shown below.
  • the metal structure of the plate thickness cross section parallel to the cold rolling direction was observed at 1 mm 2 or more continuously, and the number of crystal grains contained in the unit area was calculated using the quadrature method.
  • the average area per crystal grain was calculated
  • Creep elongation was measured by the method shown below.
  • a JIS 13B test piece was cut out from each steel plate, and a hole of ⁇ 5 mm was formed in the center of one gripping part.
  • the test piece was attached to a high-temperature tensile tester so that the test piece was marked with a mark of 50 mm between the marks, so that the grip portion having a hole was positioned downward.
  • the temperature between the gauge points is raised to 1000 ° C., and after soaking for 15 minutes at that temperature, a wire made of SUS310S having a weight calculated so as to apply a stress of 1.0 MPa is attached to the grip portion. Attached to the hole and held for 0.5 h. Thereafter, the SUS310S wire was removed from the test piece, and further cooled to room temperature by air cooling.
  • the length L between the gauge points was measured, and (L-50) / 50 ⁇ 100 was calculated as the creep elongation (%).
  • the jig and the laminate are inserted into a vacuum furnace and evacuated to obtain an initial vacuum of 1.0 ⁇ 10 ⁇ 3 to 1.0 ⁇ 10 ⁇ 4 Pa, and then raised to 1000 ° C. in about 1 h. Warm and hold at that temperature for 2 h. Then, it moved to the cooling chamber and cooled. The said vacuum degree was maintained to 900 degreeC after that, Ar gas was introduce
  • Thickness measurements were made at points. The probe diameter was 1.5 mm. If the measured thickness at a given measurement point indicates the total thickness of the two steel materials, it is assumed that both steel materials are integrated by diffusion of atoms at the interface position of both steel materials corresponding to the measurement point. Can do. On the other hand, when the plate thickness measurement value is different from the total plate thickness of both steel materials, it can be considered that an unjoined portion (defect) exists at the interface position of both steel materials corresponding to the measurement point. When the correspondence between the cross-sectional structure of the laminate after the heat treatment and the measurement results obtained by this measurement method was examined, the number of measurement points at which the measurement results were the total plate thickness of both steel materials was 49 in total.
  • Table 2 shows the average grain size and ⁇ max, surface roughness, creep elongation, and bondability evaluation results after cold rolling annealing of each steel.
  • Examples 1 to 6 of the present invention have a bonding rate of 90% or more, and exhibit good diffusion bonding properties even at a relatively low temperature of 1000 ° C. and a low surface pressure of 0.1 MPa. It was. Inventive Examples 1 to 6 showed good diffusion bonding properties regardless of the degree of the surface roughness Ra, and no influence of the surface roughness was observed. In the multiphase stainless steel material having the configuration of the present invention, the diffusion bondability does not decrease even when the surface roughness is increased, so that it can be understood that the diffusion bondability is not restricted by the surface property of the steel material.
  • Comparative Examples 1 to 10 since the average crystal grain size, ⁇ max, and creep elongation were out of the scope of the present invention, the deformation of the concavo-convex portion of the joint surface in the two-phase high temperature region was small, and The bonding area did not increase. Therefore, most of the joining ratios were slightly poor or poor at less than 80%. Further, regarding the ferrite single phase steels of Comparative Examples 5 to 7 and the austenite single phase steels of Comparative Examples 8 to 9, according to the change in the joining rate due to the surface roughness Ra, Comparative Example 7 and Comparative Example with extremely small surface roughness No. 9 showed a bonding rate of 90% or more.

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  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
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  • Organic Chemistry (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)
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Abstract

La présente invention concerne un matériau d'acier inoxydable se prêtant aux moulages liés par diffusion, dans lequel la capacité de liaison par diffusion a été en outre améliorée sans être altérée par la mesure de la rugosité de surface. La présente invention est un matériau en acier inoxydable destiné à la liaison par diffusion dans lequel la structure métallique, avant liaison par diffusion, présente une structure à plusieurs phases obtenue à partir d'au moins deux parmi une phase de ferrite, une phase de martensite et une phase austénitique : le diamètre moyen du grain cristallin dans la structure à plusieurs phases n'étant pas supérieur à 20 µm ; γmax, représenté par la formule (a), étant compris entre 10 et 90 ; et l'allongement par fluage étant d'au moins 0,2 %, lorsqu'une charge de 1MPa est appliquée à 1 000 °C pendant 0,5 h. γmax = 420 C - 11.5 Si + 7 Mn + 23 Ni - 11.5 Cr - 12 Mo + 9 Cu - 49 Ti - 47 Nb - 52 Al + 470 N + 189 ∙∙∙ formule (a). La notation de l'élément dans la formule (a) représente les teneurs (% en masse) des éléments respectifs.
PCT/JP2015/079342 2014-11-05 2015-10-16 Matériau en acier inoxydable destiné à la liaison par diffusion WO2016072244A1 (fr)

Priority Applications (6)

Application Number Priority Date Filing Date Title
SG11201703499XA SG11201703499XA (en) 2014-11-05 2015-10-16 Stainless steel material for diffusion bonding
US15/523,882 US20170321311A1 (en) 2014-11-05 2015-10-16 Stainless steel material for diffusion bonding
EP15857850.0A EP3216888B1 (fr) 2014-11-05 2015-10-16 Utilisation d'un acier inoxydable à deux phases pour un processus de soudage par diffusion
KR1020177015017A KR102384698B1 (ko) 2014-11-05 2015-10-16 확산 접합용 스테인리스 강재
ES15857850T ES2886446T3 (es) 2014-11-05 2015-10-16 Uso de un material de acero inoxidable de doble fase para la unión por difusión
CN201580056844.0A CN107002189B (zh) 2014-11-05 2015-10-16 扩散接合用不锈钢材料

Applications Claiming Priority (2)

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US20170321311A1 (en) 2017-11-09
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TW201625806A (zh) 2016-07-16
TWI680193B (zh) 2019-12-21
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CN107002189A (zh) 2017-08-01
JP6129140B2 (ja) 2017-05-17
ES2886446T3 (es) 2021-12-20
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