WO2017006843A1 - Métal pour tôles et son procédé de fabrication - Google Patents

Métal pour tôles et son procédé de fabrication Download PDF

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Publication number
WO2017006843A1
WO2017006843A1 PCT/JP2016/069541 JP2016069541W WO2017006843A1 WO 2017006843 A1 WO2017006843 A1 WO 2017006843A1 JP 2016069541 W JP2016069541 W JP 2016069541W WO 2017006843 A1 WO2017006843 A1 WO 2017006843A1
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hardness
thin plate
rolling
heat resistance
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PCT/JP2016/069541
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English (en)
Japanese (ja)
Inventor
木村　謙
文崇 市川
正美 澤田
慎一 寺岡
雄一 福村
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新日鐵住金株式会社
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Priority to JP2016568083A priority Critical patent/JP6160787B2/ja
Publication of WO2017006843A1 publication Critical patent/WO2017006843A1/fr

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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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • 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
    • C22C38/40—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

Definitions

  • the present invention relates to a thin plate and a manufacturing method thereof.
  • a gasket used as a sealing material for automobile exhaust gas is required to have high strength.
  • a metal gasket such as stainless steel is processed into a predetermined gasket shape by molding (cutting or punching), drilling, overhanging, bending, etc., using a thin plate of about 0.1 to 0.3 mm as a raw material. .
  • Ni-based alloys such as Inconel 718 may be used.
  • Ni-based alloys are excellent in heat resistance, there is a problem that the alloy cost is high because Ni is contained in excess of 50%, and a cheaper heat-resistant alloy for gaskets is desired.
  • SUS301 or the like is known as an austenitic stainless steel conventionally used as an exhaust manifold gasket.
  • SUS301 is a material that uses processing-induced martensite to increase the strength. However, when exposed to a high temperature of 500 ° C. or higher, the material has a large softening allowance.
  • SUH660 using precipitation strengthening by an intermetallic compound containing Ni, Ti, and Al is known.
  • SUH660 has higher strength at high temperatures than SUS301.
  • a temperature in the vicinity of 700 ° C. where a Ni-based alloy is used there is a problem that a decrease in strength, so-called “sagging” occurs.
  • Patent Document 1 discloses an austenitic stainless steel in which the intermetallic compound species is controlled and the heat resistance is improved by defining the ratio of Ti and Al.
  • Patent Document 2 discloses heat-resistant stainless steel having Ni: 10 to 50% and a total addition amount of Ti, Al, and Nb of 3.0 to 7.0 wt%.
  • Patent Document 3 discloses a technique that defines the amount of elements contained in IVa group and Va group.
  • Patent Document 4 there is a technology that considers the balance between cold workability and high temperature strength by defining Ni: Mn ratio and Ti / Al ratio with Ni: 15 to less than 20% for the purpose of reducing the cost of SUH660. It is disclosed.
  • JP-A-4-48051 JP 2000-109955 A Japanese Patent Laid-Open No. 7-109539 JP 2012-212385 A
  • Patent Document 1 Although the technology of Patent Document 1 has higher heat resistance than SUH660, it has a large sag during use at 700 ° C. as described above, and cannot be said to have sufficient heat resistance.
  • Patent Document 2 and Patent Document 3 are high in heat resistance, they are technologies related to the production of a rod and wire, and these technologies exhibit sufficient heat resistance when manufacturing a gasket plate. I could't. Moreover, the workability to the gasket shape after manufacturing a thin plate was not considered, and the description which suggests an improvement in workability was not recognized.
  • the technique of Patent Document 4 has a problem that heat resistance is not sufficient when used at 700 ° C.
  • an object of the present invention is to provide a thin plate that achieves both heat resistance and workability as a thin plate by defining steel components, hardness, and manufacturing method.
  • a thin plate having a hardness of 400 HV or more and a change in hardness after holding at 700 ° C. for 400 hours is 80 HV or less.
  • the composition contains one or more of B: 0.0002 to 0.01%, Ca: 0.0002 to 0.002%, and Mg: 0.0002 to 0.002% by mass%.
  • a thin plate having excellent workability and heat resistance can be provided by defining the steel components and the production conditions.
  • ⁇ C 0.002 to 0.10%> C produces carbide and acts as a strengthening phase. If the amount of C is excessively reduced, the cost in the steelmaking stage increases, so the content is made 0.002% or more. In addition, it is preferable to set it as 0.005% or more from a viewpoint of stable manufacturability. Further, when the content of C is high, deterioration of workability and sensitization (embrittlement) due to Cr carbide precipitation are caused. For this reason, it is 0.10% or less. In the case of performing molding with a high degree of processing, the content is preferably 0.030% or less, and more preferably 0.020% or less.
  • Si may be used as a deoxidizing element or may be positively added to improve oxidation resistance. Since extremely low Si causes an increase in cost, its content is set to 0.02% or more. From the viewpoint of deoxidation, it is preferably 0.05% or more. Moreover, since addition of a large amount causes the workability fall by hardening of a material, the content is good to set to 3.0% or less. In addition, when the degree of processing is severe, it is preferably 1.0% or less.
  • Mn may also be used as a deoxidizing element like Si. Since excessive reduction of Mn causes an increase in cost, its content is set to 0.02% or more. In addition, it is preferable to set it as 0.05% or more from the point of refining cost, More preferably, it is 0.07% or more. In addition, since a large amount of Mn causes hardening of the material, its content is set to 2.0% or less. From the viewpoint of oxidation resistance and stable productivity, it is preferably 1.5% or less.
  • P is an impurity. Although it may mix as an impurity element from a raw material, the content is so preferable that it is small. When P is present in a large amount, workability is deteriorated, so the content is limited to less than 0.050%. In addition, it is preferable to set it as 0.035% or less from a viewpoint of suppression of workability deterioration.
  • the lower limit of the P content need not be determined, but excessive reduction leads to an increase in raw material and steelmaking costs. From this point, the P content may be 0.005% or more, and further 0.010%. It is good also as above.
  • S is an impurity. In some cases, it is mixed as an impurity element from the raw material. It is an element that degrades hot workability and corrosion resistance, and the lower the content, the better. Therefore, it is limited to less than 0.010%. Moreover, since corrosion resistance is so favorable that the content is low, Preferably it is less than 0.0030%. More preferably, it is less than 0.0010%. On the other hand, excessive reduction leads to an increase in the refining cost, so it may be 0.0002% or more.
  • ⁇ Cr: 12.0 to 30.0%> Cr is an extremely important element in securing corrosion resistance and heat resistance. In order to acquire this effect, it is preferable to make it contain 12.0% or more. In addition, from a viewpoint of corrosion resistance and heat resistance, the content is preferably 14.0% or more. On the other hand, addition of a large amount causes toughness deterioration during production, so the content is made 30.0% or less. In consideration of manufacturing stability, the content is preferably 28.0% or less. More preferably, it is 26.5% or less.
  • Ni is an extremely important element for producing an intermetallic compound which is a precipitation strengthening phase and ensuring corrosion resistance and heat resistance.
  • the workability of the thin plate is greatly affected. Since processing cracks occur when the amount of Ni is small, the content is preferably more than 30.0%. In addition, it is preferable to set it as 37.5% or more from a manufacturing stability and a heat resistant viewpoint. On the other hand, addition of a large amount leads to an increase in alloy cost and decreases the workability of the thin plate, so the content is made less than 50.0%. In consideration of manufacturing stability (prevention of hot work cracking), the content is preferably 46.0% or less.
  • N may reduce workability due to the formation of nitrides
  • N is preferably low, and its content is 0.020% or less.
  • the degree of processing is severe, it is desirable to make it less than 0.010%.
  • the content is made 0.0005% or more.
  • Al is an element constituting an intermetallic compound and contributes to improvement in heat resistance. Therefore, in order to obtain this effect, 0.002% or more is preferably contained. In order to utilize also as a deoxidation element, it is preferable to set it as 0.005% or more. On the other hand, the addition of a large amount not only deteriorates the hot workability during production, but also produces precipitates that do not become a strengthening phase, so the content is made 5.0% or less. Considering the stability of manufacturability, it is desirable to make it less than 3.5%.
  • Ti is an element constituting an intermetallic compound that is a strengthening phase.
  • Ti is added in combination with Nb to enhance heat resistance and ensure heat resistance that can withstand use at 700 ° C.
  • it is preferable to contain more than 3.0%, More preferably, it is 3.5% or more, More preferably, it is 4.0%.
  • the addition of a large amount reduces the hot workability and the forming workability after manufacturing the thin plate, so the content is made less than 7.5%. Considering stable manufacturability, it is preferably less than 5.5%.
  • Nb is an element effective for improving heat resistance, and is contained in an amount exceeding 0.5%.
  • the combined addition with Ti has an effect of extremely improving heat resistance.
  • the effect of suppressing sag after use at high temperatures is great.
  • the addition of a large amount generates cracks during hot rolling and cold rolling and lowers the tensile elongation at break, so the content is made less than 4.0%. Considering the yield at the time of manufacture, less than 3.0% is desirable.
  • the following elements are not essential additive elements, but one or more may be selected and added.
  • Mo and W are effective for improving heat resistance.
  • the addition of these elements is thought to increase the strength of the precipitated phase in addition to strengthening the parent phase at high temperatures. In order to acquire this effect, it is preferable to contain 0.02% or more of any element. For the purpose of strengthening in a wide temperature range, 0.5% or more is preferably added. Moreover, since addition of a large amount induces cracks during production, the respective contents are set to 4.0% or less. Preferably it is 3.0% or less. Moreover, there is no problem even if both elements are added together.
  • Impurity means a component mixed due to raw materials such as ore and scrap and other factors when industrially producing steel materials.
  • each content is preferably 0.0002% or more. Preferably it is 0.0005% or more. Addition of a large amount not only reduces hot workability, but also tends to cause casting cracks, nozzle clogging, etc., so the contents are 0.01% or less for B and 0.002 for Ca and Mg, respectively. % Or less.
  • the thin plate of the present invention satisfies the following characteristics.
  • “thin plate” in the present invention indicates that the plate thickness is 0.3 mm or less.
  • predetermined cold rolling is performed. This condition will be described later.
  • the crystal grain size is 20.0 ⁇ m or more. If the crystal grain size is less than 20.0 ⁇ m, the amount of change in hardness after holding at 700 ° C. for 400 hours becomes large, so this was made the lower limit.
  • the upper limit is not particularly required from the viewpoint of heat resistance, but if it is too large, cracking during cold rolling tends to occur or cracking may occur during processing into a gasket shape. The following is preferable. Further, by satisfying this range, it is possible to satisfy an elongation value of 1.0% or more necessary for processing into a gasket shape after cold processing. In order to satisfy this crystal grain size, the heat treatment temperature and the cold rolling rate are important.
  • ⁇ Cross section hardness is 400HV or more>
  • the cross-sectional hardness is Vickers hardness and the lower limit is 400 HV.
  • the Vickers hardness is measured with a load of 4.903N (HV0.5) by a method based on JIS Z 2244. Measure 5 or more points in the range of 1/4 to 3/4 of the plate thickness, and take the average value as the representative value.
  • HV0.5 4.903N
  • the hardness is adjusted by cold rolling described later. In general, it is possible to increase the hardness to a certain extent only by increasing the degree of cold rolling, but as will be described later, in order to ensure the hardness after holding at 700 ° C., the components and It is necessary to adjust the hardness by combining manufacturing methods.
  • ⁇ Hardness change after holding at 700 ° C. for 400 hours is 80 HV or less>
  • the amount of change in hardness after holding at 700 ° C. for 400 hours is an index indicating heat resistance in the present invention.
  • the gas temperature increases during high-speed driving, and the gasket is exposed to a temperature near 700 ° C. for a long time.
  • the settling is large, and the strength (hardness) after use at 700 ° C. is greatly reduced.
  • “amount of change in hardness when held at 700 ° C. for 400 hours” is used as an index indicating a sag during use at 700 ° C.
  • the reason why the holding time is limited to 400 hours is that the decrease in hardness when held at 700 ° C. may change in hardness after 200 to 300 hours have elapsed, and the amount of change is small after 400 hours. This is because the hardness tends to gradually decrease with the passage of time.
  • the amount of change exceeds 80 HV after about 1000 to 1500 hours, although it depends on the chemical composition and the temper rolling ratio. Even if the composition is the same, as will be described later, when the heat treatment conditions, cold rolling conditions, and temper rolling conditions specified by the present invention are not satisfied, the hardness rapidly increases when the temperature is maintained at 700 ° C. May rise or fall. Therefore, the conditions of 700 ° C. and 400 hours were selected.
  • SUS301 cold rolled material has a hardness of 400 HV or more, but the room temperature hardness after holding at 700 ° C. for 400 hours is lower than 200 HV. That is, the hardness change amount is 200 HV or more.
  • the amount of change in hardness after holding at 700 ° C. for 400 hours is 80 HV or less. If it exceeds 80 HV, strength reduction during traveling increases, leading to fuel efficiency reduction due to deformation of members, generation of abnormal noise, and the like. The smaller the change in hardness, the smaller the settling, so 50HV or less is preferable.
  • the hardness may increase after holding for 400 hours due to precipitation during holding at 700 ° C.
  • the hardness change amount which is a value obtained by subtracting the cross-sectional hardness after holding at 700 ° C. for 400 hours from the cross-sectional hardness takes a negative value, there is no problem if it is 80 HV or less as described above.
  • the hardness is measured with a load of 4.903N (HV0.5) in accordance with JIS Z 2244, measured at 5 points or more in the range of 1/4 to 3/4 of the plate thickness, and representative with an average value. Value.
  • the metal structure and composition such as initial strength and crystal grain size, it is possible to suppress sag during use at 700 ° C. Since sag is due to tissue softening (metal structure change), a low sag rate indicates that there is little change in metal structure when held at 700 ° C.
  • the inventors measured the hardness after adding various heat histories to the thin plate within the scope of the present invention, and further examined the difference from the hardness after holding at 700 ° C. for 400 hours, all of which are 80 HV or less. I have confirmed that. That is, if a material actually used (including a material whose previous thermal history is unknown) is subjected to heat treatment at 700 ° C. for 400 hours and the hardness change before and after is 80 HV or less, the characteristics of the present invention are obtained. Will be satisfied.
  • the hardness, amount, ease of coarsening, degree of lattice mismatch with the parent phase, density, and the like are important control factors.
  • Addition amount of elements (Ti, Nb, Al, Ni) constituting intermetallic compounds, heat treatment conditions, cold rolling conditions, and temper rolling conditions affect the hardness, precipitation amount, and coarseness of precipitates. Effect. It is important to sufficiently dissolve the precipitates that contribute to strengthening by the heat treatment process before the final cold rolling, and by regulating the subsequent cooling rate, the precipitation before the cold rolling is suppressed and the final control is performed. It is considered that the strain introduced by quality rolling (cold rolling) affects the number of precipitation sites (precipitation density) and the diffusion rate (easiness of coarsening) of each atom in the metal.
  • the thin plate of the present invention comprises the following steps (A) to (F) and is produced by repeating the following steps (C) to (E) twice or more.
  • Step of melting an ingot having a predetermined composition First, an ingot having a predetermined composition is melted by casting. Casting may be either continuous casting or ingot casting.
  • the temperature is set to less than 1100 ° C.
  • the temperature is preferably less than 1080 ° C. Holding at this temperature for a long time is not preferable because crystal grain coarsening occurs, but a certain amount of holding may be performed to stabilize the material.
  • the holding time is preferably 300 s or less.
  • the average cooling rate of 900 ° C. to 600 ° C. is applied to the cold-rolled plate subjected to the above step (C). Is cooled at 30 ° C./s or more.
  • the cooling rate is slow, precipitation occurs during cooling, and sufficient workability cannot be obtained after cold rolling. Therefore, it is necessary to increase the cooling rate.
  • the average cooling rate in this temperature range is set to 30 ° C./s or more.
  • the average cooling rate is a value obtained by dividing the temperature difference between 900 ° C. and 600 ° C. (300 ° C.) by the time required to reach 600 ° C. from 900 ° C.
  • the upper limit value of the average cooling rate does not need to be determined in particular, but it is not realistic because a special cooling device (function) exceeding 200 ° C./s is required in consideration of the current facility capacity. As long as the cooling rate is satisfied, there is no problem as long as the cooling method is satisfied. However, in consideration of existing facilities, a method of forcibly blowing a gas such as air, Ar, mist, water or the like is desirable.
  • Step of cold rolling at a rolling rate of 10 to 60% Subsequent to the above heat treatment and cooling, cold rolling at a rolling rate of 10 to 60% is further performed and the temper rolling rate performed after the final annealing is taken into consideration Finish to the finished thickness.
  • the rolling rate is less than 10%, productivity is deteriorated and abnormal grain growth is likely to occur.
  • the cold rolling rate exceeding 60%, a rolling material becomes hard and it becomes easy to generate
  • (F) Step of temper rolling at a rolling rate of 10 to 60% The temper rolling step is necessary to increase the dislocation density and ensure high hardness of the material.
  • the precipitation density of the intermetallic compound at the time of use is increased.
  • cold rolling can achieve both an increase in initial strength and an increase in strength during use (effective precipitation strengthening).
  • the cold rolling rate is less than 10%, the initial strength is low and the sealing property is inferior.
  • the cold rolling rate exceeds 60%, the crystal grain size becomes small, and therefore the hardness decrease after holding at 700 ° C. becomes large.
  • the preferable reduction rate of cold rolling which makes 60% an upper limit is 20% or more and 55% or less.
  • steps (C) to (E) are repeated twice or more to finally produce a thin plate having a thickness of 0.3 mm or less after the step (F). If the steps (C) to (E) are less than twice, the increase or decrease in hardness at the time of holding becomes remarkable, so the number of times is set twice or more.
  • the present invention is a technique for controlling the strength (hardness) and workability of a thin plate within a specific range by defining the composition and manufacturing conditions. It has been conventionally known that Ni, Ti, Nb, Al and the like constitute an intermetallic compound, and that the heat resistance is improved when the amount of these added is large. On the other hand, in order to ensure the workability of a thin plate in applications such as gaskets in the Ti, Nb, and Al amount ranges as in the present invention and to prevent a decrease in hardness during use, an optimal Ni, Ti, Nb, and Al range The existence of is a new finding.
  • the precipitate can be sufficiently dissolved by repeating cold rolling-annealing-cooling twice or more.
  • temper rolling in addition to increasing the material strength, the dislocations introduced by cold rolling are used as precipitation nuclei when maintained at 700 ° C., thereby dispersing the precipitation.
  • a sample was prepared by the following process.
  • A A 30 kg steel ingot having the composition (% by mass) shown in Table 1 was melted.
  • B The obtained steel ingot was made into a hot rolled sheet having a thickness of 5.0 mm by forging and hot rolling.
  • C Holding was performed at a predetermined temperature.
  • D The cooling rate from 900 ° C. to 600 ° C. was cooled at a predetermined cooling rate.
  • E Cold rolling was performed at a predetermined rolling rate.
  • F Temper rolling was performed at a predetermined rolling rate.
  • the cross-sectional hardness was measured at room temperature by measuring the Vickers hardness (HV0.5) at the central portion of the cross-sectional thickness by a method according to JIS Z 2244. The average value measured 5 times was used.
  • the crystal grain size was calculated from the cross-sectional structure.
  • Tensile elongation was measured by a method based on JIS Z 2241 using a JIS No. 13 B tensile test piece.
  • the elongation value in the tensile test is 1.0% or more, molding into a gasket shape is possible. Therefore, a material having an elongation value of 1.0% or more was regarded as an acceptable level of formability.
  • the heat resistance was judged by the cross-sectional hardness after holding at 700 ° C. for 400 hours.
  • an average value (HV0.5) measured five times by a method according to JIS Z 2244 was used.
  • the alloy thin plate obtained using the steel type having a composition deviating from the composition of the present invention, and the alloy thin plate produced based on the production condition deviating from the production condition of the production method of the present invention are: Any of the cross-sectional hardness, tensile elongation, and heat resistance did not satisfy the predetermined characteristics.
  • variations in sheet thickness and cracks occurred in the subsequent cold rolling.
  • a crack occurred during the molding of the gasket.
  • good characteristics were obtained regardless of the pre-heat treatment conditions.
  • Steel grade no. Nos. 15 and 16 are compositions that satisfy Patent Document 3, but they do not exhibit good characteristics unless they satisfy the manufacturing method and structure as in the present invention.
  • a thin plate excellent in workability and heat resistance can be obtained, and can be used in all industrial fields.
  • the thin plate of the present invention can be applied to members used at high temperatures in addition to gaskets used as sealing materials for automobile exhaust systems.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
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  • Metallurgy (AREA)
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  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

L'invention concerne un métal pour tôles dont la composition, en termes de % en masse, comprend : de 0,002 à 0,10 % de C, de 0,02 à 3,0 % de Si, de 0,02 à 2,0 % de Mn, moins de 0,050 % de P, moins de 0,010 % de S, de 12,0 à 30,0 % de Cr, plus de 30,0 % et moins de 50,0 % de Ni, de 0,0005 à 0 020 % de N, de 0,002 à 5,0 % de Al, plus de 3,0 % et moins de 7,5 % de Ti, plus de 0,5 % et moins de 4,0 % de Nb, de 0 à 4,0 % de Mo, de 0 à 4,0 % de P, de 0 à 0,01 % de B, de 0 à 0,002 % de Ca, et de 0 à 0,002 % Mg, le reste étant du fer et des impuretés inévitables, la taille des grains cristallins du métal pour tôles étant de 20,0 µm ou plus, la dureté en section transversale de celui-ci étant de 400 HV ou plus, et la variation de la dureté de celui-ci après rétention pendant 400 heures à 700 °C étant de 80 HV ou moins. Ce métal pour tôles présente d'excellentes caractéristiques d'aptitude au façonnage et de résistance à la chaleur.
PCT/JP2016/069541 2015-07-03 2016-06-30 Métal pour tôles et son procédé de fabrication WO2017006843A1 (fr)

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Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2018188686A (ja) * 2017-04-28 2018-11-29 新日鐵住金株式会社 耐熱部材用合金原板、耐熱部材用合金板、およびエンジンの排気系部材用のガスケット
JP2019002048A (ja) * 2017-06-15 2019-01-10 日立金属株式会社 耐熱板材
JP2020041195A (ja) * 2018-09-12 2020-03-19 日鉄ステンレス株式会社 メタルガスケット中間製品およびメタルガスケットの製造方法
WO2022123812A1 (fr) * 2020-12-10 2022-06-16 日立金属株式会社 Procédé de fabrication d'une bande d'acier inoxydable austénitique

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JPH07332035A (ja) * 1994-06-15 1995-12-19 Daido Steel Co Ltd 排気バルブ用合金
JP2000109955A (ja) * 1998-10-05 2000-04-18 Sumitomo Electric Ind Ltd 耐熱ステンレス鋼
JP2005002451A (ja) * 2003-06-13 2005-01-06 Daido Steel Co Ltd 耐熱ばね用Ｆｅ−Ｎｉ−Ｃｒ基合金および耐熱ばねの製造方法
JP2013227644A (ja) * 2012-03-28 2013-11-07 Nippon Steel & Sumitomo Metal Corp オーステナイト系耐熱合金
WO2016043199A1 (fr) * 2014-09-19 2016-03-24 新日鐵住金株式会社 Tôle d'acier inoxydable austénitique

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH07332035A (ja) * 1994-06-15 1995-12-19 Daido Steel Co Ltd 排気バルブ用合金
JP2000109955A (ja) * 1998-10-05 2000-04-18 Sumitomo Electric Ind Ltd 耐熱ステンレス鋼
JP2005002451A (ja) * 2003-06-13 2005-01-06 Daido Steel Co Ltd 耐熱ばね用Ｆｅ−Ｎｉ−Ｃｒ基合金および耐熱ばねの製造方法
JP2013227644A (ja) * 2012-03-28 2013-11-07 Nippon Steel & Sumitomo Metal Corp オーステナイト系耐熱合金
WO2016043199A1 (fr) * 2014-09-19 2016-03-24 新日鐵住金株式会社 Tôle d'acier inoxydable austénitique

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2018188686A (ja) * 2017-04-28 2018-11-29 新日鐵住金株式会社 耐熱部材用合金原板、耐熱部材用合金板、およびエンジンの排気系部材用のガスケット
JP2019002048A (ja) * 2017-06-15 2019-01-10 日立金属株式会社 耐熱板材
JP2020041195A (ja) * 2018-09-12 2020-03-19 日鉄ステンレス株式会社 メタルガスケット中間製品およびメタルガスケットの製造方法
JP7090514B2 (ja) 2018-09-12 2022-06-24 日鉄ステンレス株式会社 メタルガスケット中間製品およびメタルガスケットの製造方法
WO2022123812A1 (fr) * 2020-12-10 2022-06-16 日立金属株式会社 Procédé de fabrication d'une bande d'acier inoxydable austénitique

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