[go: up one dir, main page]

WO2011111646A1 - Acier inoxydable ferritique ayant une excellente résistance à la corrosion dans un environnement d'eau de condensation produit par les gaz d'échappement d'une combustion d'hydrocarbures - Google Patents

Acier inoxydable ferritique ayant une excellente résistance à la corrosion dans un environnement d'eau de condensation produit par les gaz d'échappement d'une combustion d'hydrocarbures Download PDF

Info

Publication number
WO2011111646A1
WO2011111646A1 PCT/JP2011/055181 JP2011055181W WO2011111646A1 WO 2011111646 A1 WO2011111646 A1 WO 2011111646A1 JP 2011055181 W JP2011055181 W JP 2011055181W WO 2011111646 A1 WO2011111646 A1 WO 2011111646A1
Authority
WO
WIPO (PCT)
Prior art keywords
stainless steel
corrosion resistance
less
ferritic stainless
corrosion
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP2011/055181
Other languages
English (en)
Japanese (ja)
Inventor
透 松橋
純 徳永
佑一 田村
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Stainless Steel Corp
Original Assignee
Nippon Steel and Sumikin Stainless Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Nippon Steel and Sumikin Stainless Steel Corp filed Critical Nippon Steel and Sumikin Stainless Steel Corp
Priority to CN201180012827.9A priority Critical patent/CN102812144B/zh
Priority to EP11753304.2A priority patent/EP2546376B1/fr
Priority to US13/580,869 priority patent/US20130011294A1/en
Publication of WO2011111646A1 publication Critical patent/WO2011111646A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Images

Classifications

    • 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
    • C22C38/001—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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/50—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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
    • F28F21/00—Constructions of heat-exchange apparatus characterised by the selection of particular materials
    • F28F21/08—Constructions of heat-exchange apparatus characterised by the selection of particular materials of metal
    • F28F21/081—Heat exchange elements made from metals or metal alloys
    • F28F21/082—Heat exchange elements made from metals or metal alloys from steel or ferrous alloys
    • F28F21/083—Heat exchange elements made from metals or metal alloys from steel or ferrous alloys from stainless steel
    • 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

Definitions

  • the present invention relates to a heat exchanger, a hot water heater using LPG or petroleum as a fuel, and a ferritic stainless steel having excellent corrosion resistance used for its members in a secondary heat exchanger that generates low pH condensed water. It is about steel.
  • a heat exchanger is a device that gives heat generated by burning various fuels to a medium centered on water, and is used in various fields from a steam generator for nuclear power generation to a hot water heater in general households.
  • heat exchangers are incorporated in ordinary household gas or oil water heaters in order to convert the combustion heat into hot water.
  • this heat exchanger has been made of copper, which can be easily processed into a fin structure or the like and has excellent thermal conductivity in order to increase thermal efficiency.
  • CO 2 reduction is also required for hot water heaters due to environmental problems in recent years, and a latent heat recovery type hot water heater that further utilizes the heat of conventional exhaust gas has been developed for the purpose of further improving thermal efficiency.
  • This water heater uses another heat exchanger (secondary heat exchanger) to further use the heat of the exhaust gas that burned gas and oil after passing through the conventional heat exchanger (primary heat exchanger).
  • secondary heat exchanger used to further use the heat of the exhaust gas that burned gas and oil after passing through the conventional heat exchanger (primary heat exchanger).
  • primary heat exchanger Since the exhaust gas after passing through the primary heat exchanger is about 150 to 200 ° C. and contains a large amount of water vapor, in the secondary heat exchanger, not only direct heat but also heat of condensation in which water vapor becomes water droplets. In other words, the total heat efficiency is improved to 95% or more by collecting latent heat.
  • Patent Document 1 An example of the structure of this latent heat recovery type water heater is disclosed in Patent Document 1, for example.
  • the condensed water generated in the secondary heat exchanger is generated from exhaust gas in which hydrocarbon-based raw materials such as city gas, LPG, and petroleum are burned.
  • SUS316L satisfies the corrosion resistance necessary for the secondary heat exchanger member applied to the latent heat recovery type water heater
  • the raw material contains a large amount of Ni and Mo, which are very unstable in price stability. Contains.
  • the latent heat recovery type water heater is expected to be widely spread to the general public as a trump card for CO 2 reduction, and further cost reduction is strongly demanded in order to realize this.
  • proposals for alternative materials with lower costs are also expected in SUS316L, which is a secondary heat exchanger material.
  • SUS316L can also corrode in areas such as the coast where sea salt particles are likely to fly, which is one of the factors that hinder the corrosion resistance of stainless steel. Sex cannot be denied.
  • Patent Document 1 uses ferritic stainless steels SUS436J1L, SUS436L, and SUS444 in a heat exchanger for recovering latent heat, thereby having excellent heat conductivity, corrosion resistance, brazing property, and relatively inexpensive pipes and fins. It is said that a heat exchanger for latent heat recovery can be obtained.
  • Patent Document 2 states that as a ferritic stainless steel exhibiting durability in a high-temperature steam environment in a heat exchanger environment, the Cr, Mo, Si, and Al contents are added in relation to the intended use temperature. It is a proposal.
  • patent document 3 has prescribed
  • Patent Document 1 the average corrosion depth was used as an index of corrosion resistance.
  • stainless steel originally excellent in corrosion resistance pitting corrosion is mainly generated, and even in some cases, pitting corrosion is caused. If it penetrates, it cannot be used as a material.
  • the conditions disclosed in Patent Document 1 still require improvement, and according to the study by the present inventors, among the ferritic stainless steels described in Patent Document 1, Some were inferior in corrosion resistance when used in a heat exchanger for latent heat recovery.
  • Patent Document 2 has a problem that the material becomes very hard and brittle because the amount of Al added is large, and the temperature assumed in Patent Document 2 is 300 to 1000 ° C., which is much higher than the latent heat recovery water heater of this time
  • Patent Document 3 uses Nb as an essential element for the purpose of preventing crystal grain coarsening during heat treatment during brazing, but there is no indication of improvement in corrosion resistance.
  • ferritic stainless steel suitable as a secondary heat exchanger member has been sufficiently disclosed.
  • an object of the present invention is to provide a ferritic stainless steel that is inexpensive and excellent in corrosion resistance and can be suitably used as a member for a secondary heat exchanger.
  • the present inventors have evaluated the corrosion resistance of various stainless steels in such an environment.
  • the Cr and Ti contents are large, particularly when they are concentrated on the surface of the passive film.
  • the corrosion resistance in this environment can be improved by reducing Cu and Si.
  • the present invention has developed a ferritic stainless steel having excellent corrosion resistance in the secondary heat exchanger environment as a result of diligent investigation of the corrosive environment in the secondary heat exchanger. That is, the present invention is a ferritic stainless steel excellent in corrosion resistance in a condensed water environment generated from hydrocarbon combustion exhaust gas having the following characteristics.
  • the present invention it is possible to provide a ferritic stainless steel excellent in corrosion resistance in a secondary heat exchanger environment, not an austenitic stainless steel to which a large amount of expensive Ni or Mo is added. Moreover, it becomes possible to exhibit excellent corrosion resistance not only as a water heater but also as a device material used in a condensed water environment of combustion gas using LNG, petroleum or other hydrocarbon as fuel.
  • FIG.1 (a) is the figure which showed the shape of the sample used for the test.
  • FIG.1 (b) is the figure which showed the shape of the sample used for the test.
  • FIG. 2 is a diagram showing the relationship between the maximum corrosion depth after the test and the constituent elements.
  • FIG. 3 is a diagram showing the relationship between the maximum corrosion depth after the test and the constituent elements.
  • FIG. 4 is a diagram showing the results of Examples and Comparative Examples in relation to the maximum corrosion depth after the test and the component elements.
  • ferritic stainless steel that exhibits excellent corrosion resistance as a secondary heat exchanger material of a latent heat recovery type water heater using hydrocarbon fuels such as LNG and petroleum. The following was found.
  • (I) Corrosion depth in repeated wet and dry tests in condensed water generated from combustion exhaust gas is stainless steel satisfying the formula (A): Cr + Mo + 10Ti ⁇ 18 and (B) formula: Si + Cu ⁇ 0.5 among ferritic stainless steels. Steel showed 50 ⁇ m or less.
  • the maximum corrosion depth of the ferritic stainless steel was smaller than that of the austenitic stainless steel showing the same value in the formula (A).
  • compositions which is obtained by simulating a condensed water generated from the LNG in the combustion exhaust gas, Cl - for the ions, a place where there is a fact several ppm, the operation at high beach environment and corrosive environments Assuming the situation, the concentration was set high at an accelerated rate.
  • 1 ml of this test solution 3 is filled in a test tube 1 as shown in FIG. 1A, cut into 1 ⁇ 15 ⁇ 100 mm, and wet-polished with # 600 emery paper on the entire surface. Was soaked in half so that almost half of the longitudinal direction was soaked in the solution (see FIG. 1B).
  • the test tube containing this sample is placed in a warm bath at 80 ° C.
  • the reason why the temperature to be maintained is set to 80 ° C. is that the temperature of the exhaust gas is 150 to 200 ° C., but the temperature is lowered by the generation of condensed water, and the actual member temperature is in contact with the generated condensed water. This is because the temperature is lower than 100 ° C. and a relatively high temperature is aimed at accelerating corrosion.
  • the specimen after 14 cycles was rusted and its corrosion depth was measured by a focusing method using a 200 ⁇ microscope.
  • the depth of five points from the thing with a large hole diameter was measured, and the maximum value was made into the maximum corrosion depth. This has the same meaning as the maximum pitting depth.
  • 12 steel types shown in Table 1 were used for the test material. As a result of this test, when the maximum corrosion depth exceeded 50 ⁇ m, it was determined that it reached the perforation in the long term, and in this case, it was determined that there was no corrosion resistance, and the case where it was 50 ⁇ m or less was corrosion resistance.
  • the maximum corrosion depth is 50 ⁇ m or less in the ferritic stainless steel in which Cr + Mo + 10Ti is 18 or more and Si + Cu ⁇ 0.5. Even when Cr + Mo + 10Ti shows a value of 18 or more, the maximum corrosion depth exceeded 50 ⁇ m when Si + Cu ⁇ 0.5 was not satisfied. On the other hand, even if Cr + Mo + 10Ti shows a value of 18 or more in the austenitic stainless steel, the general corrosion steel does not satisfy Si + Cu ⁇ 0.5, and thus the maximum corrosion depth exceeds 50 ⁇ m.
  • the maximum corrosion depth in the test environment was expressed as an index represented by Cr + Mo + 10Ti as a result.
  • the reason why the maximum corrosion depth is small when Si + Cu is 0.5 or less is considered as follows.
  • Cu is an element that usually increases the corrosion resistance by decreasing the active dissolution rate.
  • nitrate ions that become an oxidizing agent particularly in the test environment are present.
  • the eluted Cu ions become an oxidant of Cu 2+ to accelerate the cathode reaction, thereby increasing the corrosion rate and increasing the corrosion depth.
  • the Si-containing test material was confirmed to precipitate Si oxide mainly at the gas-liquid interface, and corrosion occurred in the vicinity thereof. It was confirmed that This is presumed that crevice corrosion occurred between the precipitate and the specimen, which promoted the corrosion, and further, since Cu 2+ was present in the environment at this time, the corrosion was estimated to be accelerated. Yes. Even in the austenitic stainless steel, even when Cr + Mo + 10Ti is 18 or more, the corrosion depth exceeded 50 ⁇ m. However, in general austenitic stainless steel, Si and Cu are inevitably high due to the steelmaking conditions. This is probably because Si + Cu is almost 0.5 or less.
  • austenitic stainless steel has more water-soluble inclusions such as MnS than ferritic stainless steel, which is presumed to be due to the high dissolution rate in the test solution.
  • Cr + Mo + 10Ti is more preferably 20 or more, and even more preferably 22 or more.
  • Si + Cu is more desirably less than 0.3, and even more desirably less than 0.2.
  • Cr is the most important element for ensuring the corrosion resistance of stainless steel, and at least 16% is necessary to stabilize the ferrite structure. Increasing Cr improves corrosion resistance, but lowers workability and manufacturability, so the upper limit is made 24%.
  • Ti is a very important element that suppresses intergranular corrosion and improves workability by fixing C and N in a welded portion of ferritic stainless steel. Furthermore, in this corrosive environment, it is an important element for corrosion resistance. Ti has a very strong affinity for oxygen, but it has been found that this forms a surface coating of stainless steel with Cr in this corrosive environment containing nitrate ions, and is extremely effective in suppressing pitting corrosion. It is. For film formation and fixation of C and N as stabilizing elements, 4 times or more of (C + N) is required.
  • the range is made 0.05 to 0.25%. More preferably, the content is 0.08 to 0.2%.
  • Mo is effective in repairing the passive film, and is an extremely effective element for improving the corrosion resistance. In particular, Mo is effective in improving the pitting corrosion resistance in combination with Cr. Therefore, it is necessary to contain Mo at least 0.30%. Increasing Mo improves corrosion resistance, but lowers workability and increases cost, so the upper limit is made 3%. More desirably, it is 0.50 to 2.00%.
  • Cu can be contained in an amount of 0.01% or more as an inevitable impurity when scrap is used as a raw material. However, in this environment, Cu is undesirable because it promotes corrosion.
  • the range is made 0.4% or less. More desirably, it is 0.10% or less.
  • Si is an element inevitably mixed from the raw material, and is generally effective in corrosion resistance and oxidation resistance, but not only has an effect of promoting the progress of corrosion in this environment, but also is excessive. Addition reduces processability and manufacturability. Therefore, the upper limit is made 0.4%. More desirably, it is less than 0.2%. Moreover, since extremely reducing causes an increase in cost, it is usually inevitable that the content is about 0.05% or more.
  • C has effects such as improvement in strength and suppression of grain coarsening by a combination with a stabilizing element, but reduces intergranular corrosion resistance and workability of the weld.
  • the content In high-purity ferritic stainless steel, the content must be reduced, so the upper limit was made 0.030%. Since excessive reduction deteriorates the refining cost, it is more preferably 0.002 to 0.020%.
  • N like C, lowers the intergranular corrosion resistance and workability, so its content needs to be reduced, so its upper limit is made 0.030%. However, excessive reduction deteriorates the refining cost, so 0.002 to 0.020% is more desirable.
  • Mn is an important element as a deoxidizing element. However, if added excessively, MnS, which becomes a starting point of corrosion, is easily generated and the ferrite structure is destabilized. 5%. More desirably, it is 0.05 to 0.3%. P not only deteriorates weldability and workability, but also easily causes intergranular corrosion, so P needs to be kept low. Therefore, the content is made 0.05% or less. More desirably, it is 0.001 to 0.04%. Since S produces water-soluble inclusions that serve as starting points for corrosion such as CaS and MnS, it is necessary to reduce S. Therefore, the content is made 0.01% or less.
  • Al is important as a deoxidizing element, and also has an effect of controlling the composition of non-metallic inclusions and refining the structure.
  • the lower limit is set to 0.01% and the upper limit is set to 0.20%. More desirably, it is 0.03% to 0.10%.
  • Nb is an extremely important element for fixing C and N as well as Ti, suppressing intergranular corrosion of the welded portion, and improving workability. For that purpose, it is necessary to add Nb at least 8 times the sum of C and N (C + N).
  • the stainless steel of this invention can add 1 type, or 2 or more types of Ni, B, V, Sn, and Sb other than said composition component as needed. Ni suppresses the active dissolution rate and is very effective in passivating, so 0.3% or more is added as necessary.
  • the upper limit is made 3%. Desirably, it is 0.8 to 1.50%.
  • B is a grain boundary strengthening element effective for improving the secondary work brittleness, and therefore can be added as necessary.
  • the lower limit is made 0.0001% and the upper limit is made 0.003%. More desirably, it is 0.0002 to 0.0020%.
  • V improves the weather resistance and crevice corrosion resistance, and can suppress the use of Cr and Mo, and if V is added to ensure excellent workability, it can be added as necessary.
  • the lower limit of V is 0.03% and the upper limit is 1.0%. More desirably, it is 0.05 to 0.50%. Sn and Sb can also be added as needed to ensure flow rust resistance.
  • the steel material of the present invention is steel that can be used as a heat exchanger, and can be in the form of a steel plate, die steel, bar, wire, tube, etc., but is mainly manufactured as a steel plate.
  • Steel having the composition described in (1) or (2) above is subjected to secondary refining such as vacuum refining using a normal melting method, for example, a converter, an electric furnace, etc. Then, it is made into a steel slab by continuous casting or cast into an ingot and then rolled into a steel slab.
  • Melting and casting can be performed in accordance with normal melting and casting of ferritic stainless steel. After this steel slab is heated, it is hot-rolled to obtain a steel material having a required shape.
  • the conditions relating to hot rolling are not particularly limited, and may be performed according to the heating and rolling conditions of normal ferritic stainless steel.
  • the hot-rolled steel plate is further pickled and annealed as necessary, and then cold-rolled into a cold-rolled steel plate, and further subjected to annealing, pickling, etc. It can be a cold rolled steel sheet.
  • Steel having the chemical composition shown in Table 2 was produced by a conventional method for producing high purity ferritic stainless steel. That is, first, an ingot having a thickness of 40 mm was manufactured after vacuum melting, and this was hot rolled to a thickness of 4 mm. Thereafter, after heat treatment at 900 to 1000 ° C. for 1 minute based on each recrystallization behavior, the scale was ground and removed, and a steel plate having a thickness of 1.0 mm was manufactured by cold rolling. This was heat-treated at 900 to 1000 ° C. for 1 minute based on the respective recrystallization behavior as final annealing, and subjected to the following tests. In the case of austenitic stainless steel, the heat treatment temperature was 1100 ° C.
  • the wet and dry repeated test was the same test as described above.
  • a test tube as shown in FIG. 1 is filled with 10 ml of a test solution, cut into 1 ⁇ 15 ⁇ 100 mm, and various types of stainless steel samples wet-polished with # 600 emery paper are approximately 1 in the longitudinal direction. / 2 was soaked in half so that it was immersed in the solution.
  • the test tube containing the sample is placed in a warm bath at 80 ° C.
  • the maximum corrosion depth of all was 50 ⁇ m or less.
  • the present invention example satisfying 20 or more in the formula A) and less than 0.3 in the formula B) has a smaller maximum corrosion depth, further satisfying 22 or more in the formula A), and B).
  • the example of the present invention satisfying the formula of less than 0.2 showed extremely excellent corrosion resistance with a maximum corrosion depth of 20 ⁇ m or less.
  • the maximum corrosion depth exceeded 50 ⁇ m.
  • the present invention can be applied as a material for a heat exchanger, particularly as a material for a secondary heat exchanger of a latent heat recovery type water heater.
  • the present invention can be applied to any material such as a heat exchanger pipe as well as a case and a partition plate.
  • this material can be similarly provided not only in the combustion exhaust gas of hydrocarbon fuel, but also in an environment where repeated drying and wetting are exposed to a low pH solution containing nitrate ions and sulfate ions.
  • heat exchangers, outdoor exterior materials for acid rain environments, building materials, roofing materials, outdoor equipment, water storage / hot water storage tanks, home appliances, bathtubs, kitchen equipment, and other general outdoor / indoor applications .

Landscapes

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

Abstract

L'invention porte sur un acier inoxydable ferritique ayant une excellente résistance à la corrosion dans un environnement d'eau de condensation produit par un gaz d'échappement de la combustion d'hydrocarbures, ledit environnement d'eau de condensation étant représentée par l'environnement lié à l'utilisation d'une pièce destinée à un échangeur de chaleur secondaire. L'invention porte plus précisément sur un acier inoxydable ferritique qui contient, en % en masse, 0,030 % ou moins de C, 0,030 % ou moins de N, 0,4 % ou moins de Si, 0,01-0,5 % de Mn, 0,05 % ou moins de P, 0,01 % ou moins de S, 16-24 % de Cr, 0,3-3 % de Mo, 0,05-0,25 % de Ti, 0,05-0,50 % de Nb, 0,01-0,2 % d'Al et 0,4 % ou moins de Cu, le reste étant constitué de Fe et des impuretés inévitables. L'acier inoxydable ferritique satisfait à la formule (A) : Cr + Mo + 10Ti ≥ 18 et à la formule (B) : Si + Cu ≤ 0,5.
PCT/JP2011/055181 2010-03-08 2011-03-01 Acier inoxydable ferritique ayant une excellente résistance à la corrosion dans un environnement d'eau de condensation produit par les gaz d'échappement d'une combustion d'hydrocarbures Ceased WO2011111646A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
CN201180012827.9A CN102812144B (zh) 2010-03-08 2011-03-01 由碳氢化合物燃烧排放气体产生的冷凝水环境下的耐蚀性优良的铁素体系不锈钢
EP11753304.2A EP2546376B1 (fr) 2010-03-08 2011-03-01 Acier inoxydable ferritique ayant une excellente résistance à la corrosion dans un environnement d'eau de condensation produit par les gaz d'échappement d'une combustion d'hydrocarbures
US13/580,869 US20130011294A1 (en) 2010-03-08 2011-03-01 Ferritic stainless steel excellent in corrosion resistance in environment of condensed water from hydrocarbon combustion gas

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2010050895A JP5610796B2 (ja) 2010-03-08 2010-03-08 炭化水素燃焼排ガスから発生する凝縮水環境における耐食性に優れるフェライト系ステンレス鋼
JP2010-050895 2010-03-08

Publications (1)

Publication Number Publication Date
WO2011111646A1 true WO2011111646A1 (fr) 2011-09-15

Family

ID=44563448

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2011/055181 Ceased WO2011111646A1 (fr) 2010-03-08 2011-03-01 Acier inoxydable ferritique ayant une excellente résistance à la corrosion dans un environnement d'eau de condensation produit par les gaz d'échappement d'une combustion d'hydrocarbures

Country Status (6)

Country Link
US (1) US20130011294A1 (fr)
EP (1) EP2546376B1 (fr)
JP (1) JP5610796B2 (fr)
KR (1) KR20120112851A (fr)
CN (1) CN102812144B (fr)
WO (1) WO2011111646A1 (fr)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2014050011A1 (fr) * 2012-09-25 2014-04-03 Ｊｆｅスチール株式会社 Acier inoxydable ferritique
EP2799577A4 (fr) * 2011-12-27 2015-07-15 Jfe Steel Corp Acier inoxydable ferritique
EP2915894A4 (fr) * 2012-10-30 2016-10-26 Nippon Steel & Sumikin Sst Feuille d'acier inoxydable ferritique avec une excellente résistance à la chaleur

Families Citing this family (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP6051844B2 (ja) * 2011-12-26 2016-12-27 株式会社ノーリツ 潜熱回収型温水生成用機器およびその製造方法
JP2013204741A (ja) * 2012-03-29 2013-10-07 Nisshin Steel Co Ltd ステンレス鋼管継ぎ手
JP5937867B2 (ja) * 2012-03-29 2016-06-22 新日鐵住金ステンレス株式会社 溶接部の耐食性に優れるフェライト系ステンレス鋼
US10138796B2 (en) 2012-12-24 2018-11-27 Posco Ferritic stainless steel for automotive exhaust system, which have excellent corrosion resistance against condensate, moldability, and high-temperature oxidation resistance, and method for manufacturing same
JP2016102427A (ja) * 2014-11-27 2016-06-02 三井造船株式会社 スクラバ、およびスクラバの製造方法
KR102282218B1 (ko) 2015-01-30 2021-07-26 삼성전자주식회사 3 차원 영상 획득 장치용 결상 광학계 및 이를 포함하는 3 차원 영상 획득 장치
KR101835021B1 (ko) * 2016-09-28 2018-03-09 주식회사 포스코 카본 슬러지 흡착이 저감된 배기계 열교환기용 페라이트계 스테인리스강 및 이의 제조 방법
JP2018115360A (ja) * 2017-01-17 2018-07-26 日新製鋼株式会社 潜熱回収型熱交換器筐体用ステンレス鋼
CN118854188A (zh) 2017-05-26 2024-10-29 杰富意钢铁株式会社 铁素体系不锈钢
CN113227414B (zh) * 2018-12-21 2023-08-11 日铁不锈钢株式会社 耐氢脆性优异的Cr系不锈钢板
KR20230072327A (ko) * 2021-11-17 2023-05-24 주식회사 포스코 내식성 및 자기적 성질이 향상된 페라이트계 스테인리스강 및 그 제조방법
KR20250093776A (ko) * 2023-12-15 2025-06-25 주식회사 포스코 내산용 강판 및 그 제조방법

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06145938A (ja) * 1992-11-04 1994-05-27 Nisshin Steel Co Ltd 排ガス流路部材用フェライト系ステンレス鋼及び製造方法
JPH09279312A (ja) * 1996-04-18 1997-10-28 Nippon Steel Corp 高温特性、耐食性及び加工性に優れたフェライト系ステンレス鋼
JP2001288543A (ja) * 2000-04-04 2001-10-19 Nippon Steel Corp 表面特性及び耐食性に優れたフェライト系ステンレス鋼及びその製造方法
JP2006257544A (ja) * 2005-02-15 2006-09-28 Nippon Steel & Sumikin Stainless Steel Corp 耐すきま腐食性に優れたフェライト系ステンレス鋼
JP2009228036A (ja) * 2008-03-21 2009-10-08 Nisshin Steel Co Ltd 自動車排熱回収装置
JP2010031315A (ja) * 2008-07-28 2010-02-12 Nippon Steel & Sumikin Stainless Steel Corp 加熱後耐食性に優れた自動車排気系部材用省合金型フェライト系ステンレス鋼

Family Cites Families (32)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
SE430904C (sv) * 1980-05-13 1986-07-14 Asea Ab Rostfritt, ferrit-austenitiskt stal framstellt av pulver
JP2739531B2 (ja) * 1991-09-17 1998-04-15 日新製鋼株式会社 溶接部耐食性に優れるフェライト系ステンレス鋼
JP3263426B2 (ja) * 1992-03-26 2002-03-04 日新製鋼株式会社 耐候性に優れたフェライト系ステンレス鋼板及びその製造方法
JP3224694B2 (ja) * 1994-10-07 2001-11-05 新日本製鐵株式会社 耐銹性と加工性に優れたフェライト系ステンレス鋼板
US6136110A (en) * 1994-11-04 2000-10-24 Nippon Steel Corporation Ferritic heat-resistant steel having excellent high temperature strength and process for producing the same
JPH10219406A (ja) * 1997-02-10 1998-08-18 Nisshin Steel Co Ltd 建具用フェライト系ステンレス鋼板
JPH11183083A (ja) * 1997-12-22 1999-07-06 Gastar Corp 熱交換器
JP3769479B2 (ja) * 2000-08-07 2006-04-26 新日鐵住金ステンレス株式会社 プレス成形性に優れた燃料タンク用フェライト系ステンレス鋼板
JP2002106970A (ja) * 2000-09-27 2002-04-10 Toho Gas Co Ltd 潜熱回収用熱交換器及びこれを備えた燃焼機器
JP2002257496A (ja) * 2001-02-27 2002-09-11 Toho Gas Co Ltd 潜熱回収用熱交換器
JP4210097B2 (ja) * 2002-10-15 2009-01-14 日新製鋼株式会社 フェライト系ステンレス鋼製角筒容器
US20060225820A1 (en) * 2005-03-29 2006-10-12 Junichi Hamada Ferritic stainless steel sheet excellent in formability and method for production thereof
JP4312653B2 (ja) * 2004-04-28 2009-08-12 新日鐵住金ステンレス株式会社 耐熱性および加工性に優れたフェライト系ステンレス鋼およびその製造方法
JP2006097908A (ja) * 2004-09-28 2006-04-13 Nisshin Steel Co Ltd 溶接構造貯湯タンク及びその構築方法
JP4498950B2 (ja) * 2005-02-25 2010-07-07 新日鐵住金ステンレス株式会社 加工性に優れた排気部品用フェライト系ステンレス鋼板およびその製造方法
JP2007009290A (ja) * 2005-07-01 2007-01-18 Nisshin Steel Co Ltd 温水容器
JP4850459B2 (ja) * 2005-09-14 2012-01-11 新日鐵住金ステンレス株式会社 耐銹性に優れたフェライト系ステンレス鋼線とその製造方法
JP4732208B2 (ja) * 2006-03-23 2011-07-27 日新製鋼株式会社 シーズヒーター用鋼管およびシーズヒーター
JP5010323B2 (ja) * 2006-04-10 2012-08-29 日新製鋼株式会社 溶接構造温水容器用フェライト系ステンレス鋼および温水容器並びにその製造法
US8470237B2 (en) * 2006-05-09 2013-06-25 Nippon Steel & Sumikin Stainless Steel Corporation Stainless steel excellent in corrosion resistance, ferritic stainless steel excellent in resistance to crevice corrosion and formability, and ferritic stainless steel excellent in resistance to crevice corrosion
JP4767146B2 (ja) * 2006-10-18 2011-09-07 日新製鋼株式会社 高圧力水用ステンレス鋼容器
JP5297630B2 (ja) * 2007-02-26 2013-09-25 新日鐵住金ステンレス株式会社 耐熱性に優れたフェライト系ステンレス鋼板
JP5111910B2 (ja) * 2007-03-23 2013-01-09 新日鐵住金ステンレス株式会社 溶接部加工性および耐すき間腐食性に優れた表面疵の少ないフェライト系ステンレス鋼
CN101652491A (zh) * 2007-03-29 2010-02-17 日新制钢株式会社 焊接结构热水容器用铁素体不锈钢及热水容器
JP4998719B2 (ja) * 2007-05-24 2012-08-15 Ｊｆｅスチール株式会社 打ち抜き加工性に優れる温水器用フェライト系ステンレス鋼板およびその製造方法
KR101253326B1 (ko) * 2007-08-02 2013-04-11 닛폰 스틸 앤드 스미킨 스테인레스 스틸 코포레이션 내식성과 가공성이 우수한 페라이트·오스테나이트계 스테인리스 강 및 그 제조 방법
JP2009097079A (ja) * 2007-09-27 2009-05-07 Nippon Steel & Sumikin Stainless Steel Corp 耐流れさび性に優れるフェライト系ステンレス鋼
JP2009185382A (ja) * 2008-01-09 2009-08-20 Nisshin Steel Co Ltd 溶接隙間酸化皮膜の耐食性に優れるフェライト系ステンレス鋼板
JP2009161836A (ja) * 2008-01-09 2009-07-23 Nisshin Steel Co Ltd 溶接隙間部の耐食性に優れるフェライト系ステンレス鋼板
JP2009167439A (ja) * 2008-01-11 2009-07-30 Nisshin Steel Co Ltd 溶接隙間構造温水容器用フェライト系ステンレス鋼
JP5420292B2 (ja) * 2008-05-12 2014-02-19 日新製鋼株式会社 フェライト系ステンレス鋼
EP2316979A4 (fr) * 2008-07-23 2014-01-22 Nippon Steel & Sumikin Sst Acier inoxydable ferritique destiné à être utilisé pour la production d'un réservoir d'eau-urée

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06145938A (ja) * 1992-11-04 1994-05-27 Nisshin Steel Co Ltd 排ガス流路部材用フェライト系ステンレス鋼及び製造方法
JPH09279312A (ja) * 1996-04-18 1997-10-28 Nippon Steel Corp 高温特性、耐食性及び加工性に優れたフェライト系ステンレス鋼
JP2001288543A (ja) * 2000-04-04 2001-10-19 Nippon Steel Corp 表面特性及び耐食性に優れたフェライト系ステンレス鋼及びその製造方法
JP2006257544A (ja) * 2005-02-15 2006-09-28 Nippon Steel & Sumikin Stainless Steel Corp 耐すきま腐食性に優れたフェライト系ステンレス鋼
JP2009228036A (ja) * 2008-03-21 2009-10-08 Nisshin Steel Co Ltd 自動車排熱回収装置
JP2010031315A (ja) * 2008-07-28 2010-02-12 Nippon Steel & Sumikin Stainless Steel Corp 加熱後耐食性に優れた自動車排気系部材用省合金型フェライト系ステンレス鋼

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP2546376A4 *

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2799577A4 (fr) * 2011-12-27 2015-07-15 Jfe Steel Corp Acier inoxydable ferritique
WO2014050011A1 (fr) * 2012-09-25 2014-04-03 Ｊｆｅスチール株式会社 Acier inoxydable ferritique
JP5534119B1 (ja) * 2012-09-25 2014-06-25 Ｊｆｅスチール株式会社 フェライト系ステンレス鋼
EP2915894A4 (fr) * 2012-10-30 2016-10-26 Nippon Steel & Sumikin Sst Feuille d'acier inoxydable ferritique avec une excellente résistance à la chaleur

Also Published As

Publication number Publication date
EP2546376A4 (fr) 2013-08-07
US20130011294A1 (en) 2013-01-10
EP2546376A1 (fr) 2013-01-16
CN102812144A (zh) 2012-12-05
JP5610796B2 (ja) 2014-10-22
KR20120112851A (ko) 2012-10-11
JP2011184731A (ja) 2011-09-22
CN102812144B (zh) 2016-06-08
EP2546376B1 (fr) 2015-08-26

Similar Documents

Publication Publication Date Title
JP5610796B2 (ja) 炭化水素燃焼排ガスから発生する凝縮水環境における耐食性に優れるフェライト系ステンレス鋼
CN106536777B (zh) 铁素体系不锈钢及其制造方法、以及以铁素体系不锈钢作为构件的热交换器
JP6016331B2 (ja) 耐食性及びろう付け性に優れたオーステナイト系ステンレス鋼
JP6227182B2 (ja) 耐酸露点腐食性に優れた鋼板および排ガス流路構成部材
JP5420292B2 (ja) フェライト系ステンレス鋼
JP5186769B2 (ja) 耐硫酸露点腐食鋼
US9238855B2 (en) Ferrite-based stainless steel for use in components of automobile exhaust system
JP5866378B2 (ja) 冷間割れ性に優れたフェライト系ステンレス鋼熱延鋼板およびその製造方法
JP2013199663A (ja) 耐溶融硝酸塩腐食性に優れたオーステナイト系ステンレス鋼および溶融硝酸塩を蓄熱媒体とする集熱管ならびに蓄熱システム
KR100318529B1 (ko) 내황산부식성과 가공성이 우수한 오스테나이트계 스테인레스강
JP6097693B2 (ja) 耐食性及び加工性に優れるフェライト系ステンレス鋼
CN114599804B (zh) 钢材
JP2010510391A (ja) 硫酸に対する耐食性が優れた鉄鋼及びその製造方法
JP3845366B2 (ja) 溶接熱影響部靭性に優れた耐食鋼
JP7603504B2 (ja) フェライト系ステンレス鋼板
JP7529983B2 (ja) 鋼材
JP3239763B2 (ja) 耐硫酸腐食性に優れたオーステナイト系ステンレス鋼
JP5417764B2 (ja) 熱疲労特性と耐酸化性に優れるフェライト系ステンレス鋼
JPH0534419B2 (fr)
JP4757686B2 (ja) 加工性、溶接性、耐すき間腐食性に優れた貯湯タンク用フェライト系ステンレス鋼
JP7678322B2 (ja) 鋼材
JP5343444B2 (ja) 熱疲労特性、耐酸化性および加工性に優れるフェライト系ステンレス鋼
JP2018115360A (ja) 潜熱回収型熱交換器筐体用ステンレス鋼
JP2025026370A (ja) 鋼材

Legal Events

Date Code Title Description
WWE Wipo information: entry into national phase

Ref document number: 201180012827.9

Country of ref document: CN

121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 11753304

Country of ref document: EP

Kind code of ref document: A1

DPE1 Request for preliminary examination filed after expiration of 19th month from priority date (pct application filed from 20040101)
WWE Wipo information: entry into national phase

Ref document number: 13580869

Country of ref document: US

ENP Entry into the national phase

Ref document number: 20127022791

Country of ref document: KR

Kind code of ref document: A

NENP Non-entry into the national phase

Ref country code: DE

WWE Wipo information: entry into national phase

Ref document number: 2011753304

Country of ref document: EP