EP2546376B1 - Ferritic stainless steel having excellent corrosion resistance in condensed water environment produced by exhaust gas from hydrocarbon combustion - Google Patents

Ferritic stainless steel having excellent corrosion resistance in condensed water environment produced by exhaust gas from hydrocarbon combustion Download PDF

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Publication number
EP2546376B1
EP2546376B1 EP11753304.2A EP11753304A EP2546376B1 EP 2546376 B1 EP2546376 B1 EP 2546376B1 EP 11753304 A EP11753304 A EP 11753304A EP 2546376 B1 EP2546376 B1 EP 2546376B1
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stainless steel
corrosion
less
corrosion resistance
ferritic stainless
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German (de)
English (en)
French (fr)
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EP2546376A1 (en
EP2546376A4 (en
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Tooru Matsuhashi
Jun Tokunaga
Yuuichi Tamura
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Nippon Steel Stainless Steel Corp
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Nippon Steel and Sumikin Stainless Steel Corp
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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
    • C22C38/02—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

  • This invention relates to ferritic stainless steel excellent in corrosion resistance for use in the structural members of heat exchangers, namely, secondary heat exchangers said to generate low pH condensed water in water heaters operated with LPG or oil as fuel.
  • Heat exchangers are apparatuses for imparting heat produced by burning any of various fuels to a medium, most often water, and are used in various fields ranging from nuclear power plant steam generators to home water heaters.
  • the home gas- and oil-fueled water heaters also have built-in heat exchangers for heating water with the combustion heat.
  • these heat exchangers have conventionally used copper that is easy to process into the fin and other structures and is also excellent in thermal conductivity.
  • water heaters are being required to reduce CO 2 , so that in the interest of further thermal efficiency, a latent heat recovery type water heater was developed that further utilizes the heat of the gas previously exhausted.
  • This water heater has another heat exchanger (secondary heat exchanger) for also utilizing the heat of the exhaust gas from the burned gas or oil after passing through the conventional heat exchanger (primary heat exchanger).
  • the exhaust gas passed through the primary heat exchanger is at about 150 to 200 °C and contains much steam.
  • the secondary heat exchanger improves the total thermal efficiency to 95% or greater by recovering not only the direct heat but also the heat of condensation when the steam becomes water droplets, i.e., the latent heat.
  • An example of the structure of the latent heat recovery type water heater is set out, for example, in Patent Document 1.
  • JP 2006 257 544 discloses a ferritic stainless steel having a good pitting resistance.
  • the condensed water occurring in the secondary heat exchanger arises from within the exhaust gas produced by burning city gas, LPG, oil or other hydrocarbon fuel, it contains nitrate ions and sulfate ions attributable to the gas components and is known to be a weakly acidic aqueous solution of a pH of around 3 or less.
  • the conventionally used copper (corrodes at pH of 6.5 or less) cannot be used with this solution of low pH.
  • Other ordinary steels (corrode at pH of 7 or less) or aluminum (corrodes at pH of about 3) are also susceptible to corrosion.
  • the materials currently selected for the secondary heat exchanger are therefore stainless steels, which are excellent in corrosion resistance in the weakly acidic region, and among ordinary stainless steels, SUS316L (18 Cr - 10 Ni - 2 Mo) austenitic stainless steel, which is especially excellent in corrosion resistance, is mainly adopted because of the priority on corrosion resistance. But while SUS316L satisfies the corrosion resistance required by the structural members of a secondary heat exchanger applied in a latent heat recovery type water heater, the raw material thereof includes large amounts of Ni and Mo, whose price stability is very unstable. Hopes are that the latent heat recovery type water heater will achieve widespread general adoption as a trump card for reducing CO 2 , and additional cost reduction is strongly desired to realize this.
  • SUS316L may sustain the stressed corrosion cracking that is one of the shortcomings of austenitic stainless steels.
  • Patent Documents 1 to 3 In order to resolve such problems occurring when an austenitic stainless steel is applied, attempts have in recent years been made to apply ferritic stainless steels to the secondary heat exchanger components (Patent Documents 1 to 3).
  • Patent Document 1 By applying the ferritic stainless steels SUS436J1L, SUS436L, and SUS444 to a heat exchanger for latent heat recovery, Patent Document 1 obtains a heat exchanger for latent heat recovery that has pipes and fins excellent in thermal conductivity, corrosion resistance and brazeability, and is also relatively low in cost.
  • Patent Document 2 teaches addition of Cr, Mo, Si and Al content as a function of the estimated use temperature.
  • Patent Document 3 prescribes Nb, C and N in a ferritic stainless steel suitable for heat exchanger components subjected to brazing.
  • Patent Document 1 uses the average corrosion depth as an indicator of corrosion resistance, but local pitting corrosion is what mainly occurs in a stainless steel fundamentally excellent in corrosion resistance, and if the pitting corrosion should penetrate through at any location, the steel becomes unusable. On this point, the conditions set out in Patent Document 1 still require improvement, and a study by the present inventors found that even among the ferritic stainless steels taught by Patent Document 1, some were inferior in corrosion resistance particularly when used in a heat exchanger for latent heat recovery.
  • Patent Document 2 has a problem of the steel becoming extremely hard and brittle owing to heavy Al addition, and the temperature assumed by Patent Document 2 is 300 to 1000 °C, so that it defines a material used in an environment of much higher temperature than the latent heat recovery type water heater under consideration. Further, although Patent Document 3 prescribes Nb as a required element for the purpose of preventing crystal grain enlargement during brazing and during heat treatment, it says nothing about corrosion resistance improvement.
  • the object of the present invention is to provide a ferritic stainless steel of low cost and excellent corrosion resistance that can be suitably used in the structural members of a secondary heat exchanger.
  • the present invention is a ferritic stainless steel excellent in corrosion resistance in a secondary heat exchanger environment that was developed by assiduously studying the corrosion environment in such a secondary heat exchanger.
  • the present invention which is given in the claims is a ferritic strainless steel characterized as set out below which is excellent in corrosion resistance in a condensed water environment arising from hydrocarbon combustion exhaust gas.
  • the test tube containing the sample was placed in an 80 °C hot bath and held for 24 hours, and the dried out stainless steel sample was then removed and lightly washed with distilled water, whereafter the operation of again placing the test solution in a washed test tube once more in the foregoing manner, again half-immersing the sample, and holding for 24 hours was repeated 14 times (14 cycles).
  • the reason for setting the hold temperature at 80 °C was that, while the temperature of the exhaust gas is 150 to 200 °C, the temperature declines due to the generation of condensed water and the actual temperature of the structural members is thought to become still lower upon being contacted by the generated condensed water, so a temperature lower than 100 °C that is relatively high was targeted to accelerate corrosion.
  • the test sample after 14 cycles was descaled and then measured for corrosion depth by the focal depth method using a 200x magnification microscope.
  • the depths of five of the pitting corrosion shaped corrosion holes that occurred here were measured in order of diameter from the largest and the largest depth value was defined as the maximum corrosion depth. This means the same as maximum pitting corrosion depth.
  • the 12 steels indicated in Table 1 were used as the tested materials.
  • the reason for maximum corrosion depth becoming small at Si + Cu of 0.5 or less is thought to be as follows.
  • the causes assumed include that while Cu is an element that ordinarily enhances corrosion resistance by lowering dissolution rate of active state, the Cu in the steel elutes once corrosion occurs, so that particularly in an environment rich in nitrate ions acting as an oxidizer like the present test environment, the eluted Cu ions become Cu 2+ oxidizer and promote cathodic reaction, thereby increasing the corrosion rate and enlarging corrosion depth.
  • austenitic stainless steels are higher in MnS and other water-soluble inclusions than ferritic stainless steel, and that is presumed also to be a reason for the high dissolution rate in the present test solution.
  • Cr + Mo + 10Ti in the present case is 22 or greater. Further, Si + Cu is less than 0.2.
  • Cr is the most important element for ensuring the corrosion resistance of a stainless steel, and at least 16% is necessary for stabilizing the ferrite structure. When Cr is increased, corrosion resistance also improves, but workability and productivity are diminished, so the upper limit is made 24%. It is desirably 18.5 to 23% and more desirably 19.0 to 22.0%.
  • Ti is generally a very important element that inhibits intergranular corrosion by fixing C and N and improves workability in the welds of a ferritic stainless steel. In addition, it is an important element from the aspect of corrosion resistance in the corrosion environment under consideration. Although the affinity of Ti for oxygen is very strong, in the present corrosive environment containing nitrate ions, it joins with Cr to form a film on the stainless steel surface, which was found to be very effective for inhibiting occurrence of pitting corrosion. For film-forming and fixing C and N as stabilizing elements, four or more times (C + N) is necessary. However, as excessive addition causes surface defects, its range is made 0.05 to 0.25%. It is more desirably made 0.08 to 0.2%.
  • Mo is effective for passive film repair and is a very effective element for improving corrosion resistance that has a pitting resistance improving effect especially when combined with Cr. Therefore, at least 0.30% of Mo must be included. When Mo is increased, corrosion resistance improves, but workability is decreased, while cost rises, so the upper limit is made 3%. It is more desirably 0.50 to 2.00%.
  • Cu may be contained as an unavoidable impurity at 0.01% or greater when scrap is used as raw material. In the environment concerned, however, Cu is undesirable because it promotes corrosion. As pointed out earlier, this is assumed to be because eluted Cu ions promote cathodic reaction once corrosion starts. Therefore, the less Cu, the more desirable, and the range is made 0.4% or less. It is desirably 0.10% or less.
  • Si is an element unavoidably entrained from the raw material and is generally effective for both corrosion resistance and oxidation resistance, but in the environment under consideration, not only does it act to promote corrosion advance but excessive addition lowers workability and productivity.
  • the upper limit is therefore made 0.4%. It is more desirably less than 0.2%. Moreover, around 0.05% or greater is usually unavoidably contained because extreme reduction increases cost.
  • C has effects of, inter alia, strength-improving and inhibiting crystal grain enlargement in combination with stabilizing elements but degrades intergranular corrosion resistance at weld zone and workability.
  • the upper limit is made 0.030%. It is desirably 0.002 to 0.020% because refining cost is made worse when reduced excessively.
  • N needs to be reduced in content because, like C, it degrades intergranular corrosion resistance and workability, and the upper limit is therefore made 0.030%. However, since excessive reduction makes refining cost worse, it is desirably 0.002 to 0.020%.
  • Mn is an important element as a deoxidation element but when added excessively facilitates generation of MnS that forms corrosion starting points, and also destabilizes the ferrite structure, so the content thereof is made 0.01 to 0.5%. It is more desirably 0.05 to 0.3%.
  • P must be held low because it not only lowers weldability and workability but also facilitates intergranular corrosion. Content thereof is therefore made 0.05% or less. It is more desirably 0.001 to 0.04%.
  • S forms the aforesaid CaS, MnS and other water-soluble inclusions that form corrosion starting points and therefore needs to be reduced. Content is therefore made 0.01% or less. However, it is more desirably 0.0001 to 0.006% because excessive reduction makes cost worse.
  • Al is important as a deoxidation element and also has an effect of refining the structure by controlling the composition of nonmetallic inclusions.
  • the lower limit value is made 0.01% and the upper limit value 0.20%. It is more desirably 0.03% to 0.10%.
  • Nb like Ti, is a very important element in the inhibition of intergranular corrosion at weld zone and improvement of workability by fixing C and N. Nb must therefore be added at 8 times or greater the sum of C and N (C + N). However, the range thereof is made 0.05 to 0.50% because excessive addition lowers workability. It is more desirably 0.1 to 0.3%.
  • Ni, B, and Sn may be added to the stainless steel of the present invention as required in addition to the compositional components set out above, while the presence of one of V and S bis mandatory.
  • Ni inhibits dissolution rate of active state, and since it is very effective for passivation, is added as necessary at 0.3% or greater.
  • the upper limit is made 3% because excessive addition not only lowers workability and destabilizes the ferrite structure but also makes cost worse. It is desirably 0.8 to 1.50%.
  • the lower limit is made 0.0001% and the upper limit 0.003%. It is more desirably 0.0002 to 0.0020%.
  • V improves rust resistance and crevice corrosion resistance, and since excellent workability can also be ensured if V is added while holding down use of Cr and Mo, it can be added as necessary. However, since excessive addition of V lowers workability, and further leads to saturation of the corrosion resistance effect, the lower limit of V is made 0.03% and the upper limit 1.0%. It is more desirably 0.05 to 0.50%.
  • Sn and Sb can also be added as necessary to ensure outflow rust resistance. These elements are important for inhibiting corrosion rate, but as excessive addition makes productivity and cost worse, the range of each is made 0.005 to 1.0%. It is more desirably 0.05 to 0.5%.
  • the steel product of the present invention is a steel that is usable in a heat exchanger and that can be given various forms such as steel sheet, shaped steel, rod, wire, tube and the like, it is produced chiefly as steel sheet.
  • the steel of the composition set out in the aforesaid (1) or (2) is prepared by an ordinary melting-and-refining method using, for example, a converter, electric furnace or the like, conducting vacuum-refining or other secondary refining as required, and casting into a slab by continuous casting or casting into an ingot followed by rolling into a slab.
  • the steel making and casting can be conducted in accordance with ordinary ferritic stainless steel making and casting. After heating, the slab is hot-rolled into a steel product of desired shape.
  • the hot rolling conditions are not particularly restricted and the rolling can be conducted in accordance with the heating and rolling conditions for hot-rolling of an ordinary ferritic stainless steel.
  • the hot-rolled steel sheet can as necessary further be descaled, annealed and thereafter cold rolled into a cold-rolled steel sheet, and further processed into a desired cold-rolled steel sheet by annealing, descaling and the like.
  • the wet and dry cyclic test was the same test as described earlier.
  • test tube containing the sample was placed in an 80 °C bath, and 24 hours later the dried out stainless steel sample was lightly washed with distilled water, whereafter the operation of again placing the test solution in a washed test tube once more, again half-immersing the sample, and holding at an 80 °C for 24 hours was repeated 14 cycles.
  • Expression A) Cr + Mo + 10Ti ⁇ 18
  • Expression B) Si + Cu ⁇ 0.5. It should be noted that the examples that satisfied 20 or greater for Expression A) and less than 0.3 for Expression E) had still smaller maximum corrosion depths, and the invention examples that satisfied 22 or greater for Expression A) and less than 0.2 for Expression B) exhibited outstandingly excellent corrosion resistance results of a maximum corrosion depth of 20 ⁇ m or less.
  • the present invention can be applied as a material for a heat exchanger, particularly a material for the secondary heat exchanger of a latent heat recovery type water heater. Specifically, it can be applied as a material not only for the case and partitions but also for the heat exchanger pipes and the like.
  • the present steel can be similarly provided not only for combustion exhaust gas of a hydrocarbon fuel but broadly for any wet and dry cyclic environment where there is exposure to a solution of low pH containing nitrate ions and sulfate ions.
  • application is to various types of heat exchangers, outdoor external facing materials for acid rain environments, construction materials, roofing materials, outdoor machinery, water and heated water storage tanks, home appliances, bath tubs, kitchen equipment, and other general outdoor and indoor purposes.
EP11753304.2A 2010-03-08 2011-03-01 Ferritic stainless steel having excellent corrosion resistance in condensed water environment produced by exhaust gas from hydrocarbon combustion Active EP2546376B1 (en)

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
PCT/JP2011/055181 WO2011111646A1 (ja) 2010-03-08 2011-03-01 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

Publications (3)

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EP2546376A1 EP2546376A1 (en) 2013-01-16
EP2546376A4 EP2546376A4 (en) 2013-08-07
EP2546376B1 true EP2546376B1 (en) 2015-08-26

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US (1) US20130011294A1 (ja)
EP (1) EP2546376B1 (ja)
JP (1) JP5610796B2 (ja)
KR (1) KR20120112851A (ja)
CN (1) CN102812144B (ja)
WO (1) WO2011111646A1 (ja)

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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
ES2608460T3 (es) * 2011-12-27 2017-04-11 Jfe Steel Corporation Acero inoxidable ferrítico
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
CN104662187A (zh) * 2012-09-25 2015-05-27 杰富意钢铁株式会社 铁素体系不锈钢
CN104769144B (zh) * 2012-10-30 2017-10-10 新日铁住金不锈钢株式会社 耐热性优良的铁素体系不锈钢板
WO2014104424A1 (ko) * 2012-12-24 2014-07-03 주식회사 포스코 내응축수 부식특성, 성형성 및 고온 내산화 특성이 우수한 자동차 배기계용 페라이트계 스테인리스강 및 그 제조방법
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
CN110678566A (zh) * 2017-05-26 2020-01-10 杰富意钢铁株式会社 铁素体系不锈钢
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US20130011294A1 (en) 2013-01-10
CN102812144B (zh) 2016-06-08
KR20120112851A (ko) 2012-10-11
JP2011184731A (ja) 2011-09-22
EP2546376A1 (en) 2013-01-16
JP5610796B2 (ja) 2014-10-22
CN102812144A (zh) 2012-12-05
EP2546376A4 (en) 2013-08-07

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