EP1361290B1 - Utilisation d'un acier pour cuves chimiques avec excellente résistance à la corrosion par l'acide sulfurique et une résistance à la corrosion par piqûre - Google Patents

Utilisation d'un acier pour cuves chimiques avec excellente résistance à la corrosion par l'acide sulfurique et une résistance à la corrosion par piqûre Download PDF

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EP1361290B1
EP1361290B1 EP03010309A EP03010309A EP1361290B1 EP 1361290 B1 EP1361290 B1 EP 1361290B1 EP 03010309 A EP03010309 A EP 03010309A EP 03010309 A EP03010309 A EP 03010309A EP 1361290 B1 EP1361290 B1 EP 1361290B1
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corrosion resistance
sulfuric acid
stainless steel
corrosion
steel
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EP1361290A1 (fr
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Ryo c/o Nippon Steel Corporation Matsuhashi
Kazuhiro c/o Nippon Steel Corporation Suetsugu
Masaki c/o Nippon Steel Corp. Yawata Works Umeno
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Nippon 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • 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
    • C22C38/18—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
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling

Definitions

  • the present invention with respect to a tank used for storage and transportation of crude sulfuric acid, provides the use of a steel for the tank capable of preventing corrosion caused by crude sulfuric acid that remains stuck to the wall of the tank when crude sulfuric acid is discharged from the tank and preventing, to the utmost, pitting corrosion caused by salt water, such as natural seawater, that is used for cleaning the tank.
  • a carbon steel, a low alloy steel, a stainless steel, an Ni-base alloy and the like have so far been properly selected and used for a tank or a similar container that is used for storage and transportation of crude sulfuric acid, depending on the concentration and/or temperature of sulfuric acid.
  • a stainless steel such as an SUS 304 steel or an SUS 316L steel, which has generally been regarded as a material having good corrosion resistance, has been widely used as a material for a tank because of the broad variety of the cargoes.
  • the stainless steel is a material that is applied to a boiler in a thermal power plant, a flue or a stack. Further, an austenitic stainless steel capable of suppressing corrosion by chlorine ions is disclosed in
  • JP-A-62-247049 for example.
  • the stainless steel is a corrosion resistant material used in a wet-type phosphoric acid manufacturing process.
  • the technologies disclosed in the above documents cannot solve the aforementioned problems that plauge a material for a chemical tanker.
  • JP-A-54-013412 discloses a high corrosion resistance stainless steel with excellent device corrosion resistance.
  • JP-A-02-170946 discloses a stainless steel for chimney, flue and desulfurizing equipment.
  • the present invention provides the use of a stainless steel material capable of avoiding general corrosion (weight loss corrosion) by crude sulfuric acid and pitting corrosion by residual chloride ions, and relates to a stainless steel for a chemical tank, capable of securing the safety of the relevant tank for a long period of time and minimizing the maintenance of the tank.
  • the present inventors applied exposure tests to various kinds of stainless steels in crude sulfuric acid and in salt water, namely in the environments wherein the materials were exposed. That is, each of the stainless steels was once dipped in crude sulfuric acid and in salt water and then exposed in the upper space (hereinafter referred to as a vapor phase space), and the state of corrosion was observed. As a separate test, the general corrosion rates of each of the stainless steels in sulfuric acid solutions having various concentrations were measured and also the pitting corrosion potential (conforming to JIS G0577) of each of the stainless steels in salt water was measured.
  • the present inventors came to specify the alloying components of a stainless steel capable of suppressing, to the utmost, both the general corrosion by sulfuric acid contained in a tank for storage and transportation and the pitting corrosion by salt water, both corrosions having been the problems in the past, and established the present invention.
  • the object of the present invention can be achieved by the features specified in the claims 1 and 2.
  • the feature of the present invention is to regulate a GI value and a PI value on the bases of the combined addition of the five components, Cr, Ni, Mo, Cu and N, for securing corrosion resistance in the environments of sulfuric acid and salt water (satisfying both the sulfuric acid corrosion resistance and the pitting corrosion resistance).
  • the invention is described in more detail in connection with the drawings.
  • Fig. 1 is a graph showing the relation between the sulfuric acid concentrations and the times during which the sulfuric acid is left in the air as it is, the sulfuric acid concentrations being calculated by measuring the change of the weight increase with the passage of time when crude sulfuric acid having a sulfuric acid concentration of 95% is taken out in the glass petri dishes by the precise volume of 0.1, 1 and 10 ml respectively and the dishes are left in the air as they are.
  • the sulfuric acid concentrations drastically drop as the volumes of sulfuric acid decrease.
  • Fig. 2 is a graph showing the relation between the instantaneous corrosion rates of the SUS 316L stainless steel and the times during which the stainless steel is left in the air, as it is, when crude sulfuric acid having a sulfuric acid concentration of 95% is dripped on the surface of the SUS 316L stainless steel at the volume of 0.1 ml and the stainless steel is left in the air, as it is.
  • the maximum corrosion rate appears at the time when about 30 minutes have passed after the stainless steel is left in the air. It is understood that the sulfuric acid concentration at the time is about 50% by referring to Fig. 1.
  • Fig. 3 is a graph showing the relation between the general corrosion rates and the GI values when the comparative steels are immersed in the sulfuric acid aqueous solution of 50% concentration at 40°C. The figure shows that a corrosion rate of not more than 1 mm/y., at which a steel can sufficiently stand actual use, is obtained so long as a GI value is not less than 75.
  • Fig. 4 is a graph showing the relation between the pitting corrosion potentials and the PI values, the pitting corrosion potential being measured in a 3.5%-NaCl solution at 40°C by using a method conforming to the method specified in JIS G0577.
  • any stainless steel having the PI value not less than 23 pitting corrosion is not generated and an oxygen evolution potential caused by the electrolysis of water is observed.
  • Fig. 5 is a graph showing the relation between the GI values and the PI values of the invention steels and the comparative steels.
  • the area that conforms to the present invention is shaded with oblique lines.
  • the invention steels and the comparative steels in Table 1 are shown by the symbols ⁇ and ⁇ respectively.
  • the present inventors studied in detail the corrosion phenomena of stainless steels which corrosion phenomena occurred in the environments of crude sulfuric acid and salt water. That is, each of the stainless steels was once immersed in crude sulfuric acid or in salt water, thereafter pulled out from the solution into the open air, and left as it was for some time, and then the corrosion state of the stainless steel surface was investigated. As a result, it was found that the color of the surface of any stainless steel treated in crude sulfuric acid changed from gray to black and the corrosion proceeded under the discolored surface. Afterward, it was suggested that the phenomenon was based on self-dilution of sulfuric acid (refer to H. Bablik "Iron Age", 123, 879 (1929)).
  • the present inventors investigated the influence of the time during which crude sulfuric acid was left in the air as it was on the sulfuric acid concentration when prescribed volumes of crude sulfuric acid having a sulfuric acid concentration of 95% were taken out in glass petri dishes and the dishes were left in the air as they were.
  • the crude sulfuric acid absorbed water in the air (moisture) and was diluted with the passage of time, and that, in particular, the concentration lowered in a short time as the initial volume of sulfuric acid decreased.
  • the present inventors acquired the knowledge that sulfuric acid in crude sulfuric acid was diluted by absorbing moisture in the air and a stainless steel was corroded by the diluted sulfuric acid. Then, the present inventors found that the sulfuric acid concentration that created the most violent corrosion of a stainless steel was 50% and, on the basis of the finding, carried out the corrosion loss measurement test in a sulfuric acid solution of 50% concentration at 40°C.
  • stainless steels were experimentally produced by using steels containing 18% Cr, 12% Ni, 3% Mo, 1% Cu and 0.1% N as the base steels and by varying the amounts of Cr, Ni, Mo, Cu and N, the dependence of the corrosion rates on the amounts of those alloying elements was clarified by statistically applying the multiple regression analysis to those alloying elements, and, by so doing, the General Corrosion Resistance Index (GI) was established.
  • GI General Corrosion Resistance Index
  • a stainless steel can stand actual use with no problems as long as a corrosion rate is not more than 1 mm/y.
  • the threshold GI value beyond which a corrosion rate was not more than 1 mm/y. was examined from Fig. 3. As a result, it was clarified that general corrosion resistance could sufficiently be secured when a GI value was not less than 75.
  • stainless steels were experimentally produced by using steels containing 18% Cr, 12% Ni, 3% Mo, 1% Cu and 0.1% N as the base steels and by varying the amounts of Cr, Ni, Mo, Cu and N, the dependence of the pitting corrosion potentials (Vc', 100) on the amounts of those alloying elements was clarified by statistically applying the multiple regression analysis to those alloying elements, and, by so doing, the Pitting Corrosion Resistance Index (PI) was established.
  • Vc', 100 the pitting corrosion potentials
  • the present inventors aiming to clarify the components of a stainless steel material appropriate for suppressing the corrosion of the stainless steel to the utmost, studied the influence of the kinds and amounts of alloying components on the general corrosion of a stainless steel in sulfuric acid and a pitting corrosion potential in salt water. As a result of the intensive study, the present inventors specified the appropriate kinds and amounts of alloying components and thus established the present invention.
  • C is required to be contained to some extent from the viewpoint of securing strength, though it is detrimental to the corrosion resistance of a stainless steel.
  • the production cost increases with an ultra-low C amount of less than 0.003%.
  • the C content was determined to be in the range from 0.003 to 0.05%.
  • Si improves corrosion resistance of a stainless steel in a sulfuric acid environment and is also an element effective for securing oxidation resistance.
  • the Si amount was set at not more than 5.0%.
  • Mn is an element able to stabilize austenite and can be added as a substitute for expensive Ni.
  • a Mn amount exceeding 2.0% has no effect on corrosion resistance in salt water, which is one of the subjects of the present invention. Therefore, the Mn amount was set at not more than 2.0% as the upper limit not causing a bad influence on pitting corrosion resistance.
  • S is an element that substantially influences not only corrosion resistance but also hot workability, and the smaller the amount, the better. Therefore, the S amount was set at not more than 0.010%.
  • O like S, is an element that substantially influences hot workability, and the smaller the amount, the better. Therefore, the O amount was limited to not more than 0.0050% that was the amount obtainable in an ordinary steelmaking method of a stainless steel.
  • Cr is a basic component in the present invention and is added in the form of coexistence with Ni, Mo, Cu and N. Cr is required to be added at not less than 18% for securing a good corrosion resistance in sulfuric acid and in salt water even if Mo, N, V and W coexist with Cr. Though corrosion resistance improves as a Cr amount increases, if it exceeds 25%, then the production of a stainless steel becomes somewhat difficult and the cost thereof becomes rather expensive. Therefore, the Cr amount was limited in the range from 18 to 25%.
  • Ni similarly to Cr, Mo, Cu and N, is a basic component in a stainless steel according to the present invention and is necessary for securing corrosion resistance in sulfuric acid.
  • the minimum Ni amount required for securing an austenite phase in a stainless steel according to the present invention is 10%.
  • the upper limit of the Ni amount was determined to be 20% as the largest amount required to maintain an austenite phase at a low cost.
  • Mo similarly to Cr, Ni, Cu and N, is a basic component in a stainless steel according to the present invention and is an element indispensable for securing high corrosion resistance in a sulfuric acid environment and in a salt-water environment.
  • Mo amount is less than 1.0%, corrosion resistance is insufficient.
  • an Mo amount exceeds 4.5% the corrosion resistance improvement effect is saturated and the cost increases.
  • Cu is an element indispensable for obtaining a high corrosion resistance in a sulfuric acid environment and in a salt-water environment while coexisting with Cr, Ni, Mo and N.
  • the effect of the coexistence of Cu with those elements becomes conspicuous when Cu is added by not less than 1.0%.
  • a Cu amount exceeds 3.0%, corrosion resistance is saturated and hot workability is deteriorated. Therefore, the Cu amount was limited in the range from 1.0 to 3.0%.
  • N is added as a basic component in the form of coexistence with Cr, Ni, Mo and Cu.
  • N is a strong austenite forming element and, at the same time, is also an element that hinders the progress of pitting corrosion occurring on a stainless steel.
  • An N amount of not less than 0.05% is necessary for obtaining pitting corrosion resistance stably.
  • W makes a passivation film further stable when it is added in the form of coexistence with Cr, Mo, N and V, and also improves pitting corrosion resistance of a stainless steel in salt water.
  • W is added at not more than 3% according to the specific use in the environment. Further, a W addition of more than 3% deteriorates hot workability remarkably.
  • V makes a passivation film further stable when it is added in the form of coexistence with Cr, Mo, N and W, and also improves pitting corrosion resistance in salt water.
  • V is added at not more than 4% according to the specific use in the environment. The larger the V amount is, the more the corrosion resistance improves. However, when V is added in excess of 4%, the hot workability of a stainless steel deteriorates considerably, it becomes difficult to produce the stainless steel, and the cost increases. Therefore, the upper limit of the V amount was set at 4%.
  • Co further improves general corrosion resistance in sulfuric acid when it is added in the form of coexistence with Cr, Ni, Mo and Cu.
  • Co is added by not more than 2% according to the specific use in the environment. The larger the Co amount is, the more the sulfuric acid corrosion resistance improves. However, when Co is added in excess of 2%, it becomes difficult to produce a stainless steel and, at the same time, the cost increases. Therefore, the upper limit of the Co amount was set at 2%.
  • Ti fixes C and improves corrosion resistance.
  • Ti fixes O by coexisting with Ca, thus suppresses the formation of the oxides of Si and Mn, and, by so doing, improves hot workability and corrosion resistance.
  • Ti is added by not more than 1% according to the specific use in the environment. When a Ti amount exceeds 1%, hot workability deteriorates.
  • Ca or Ce is added usually in the range from 0.001 to 0.03% as a deoxidizing agent or a desulfurizing agent in molten steel. Even though Ca or Ce is added in excess of 0.03%, the deoxidizing effect and the desulfurizing effect are saturated. Furthermore, in relation to S and O, by adding Ca and Ce in combination so that the following expression may be satisfied, O in a low sulfur steel is fixed, the generation of MnS is prevented, and thus hot workability improves remarkably: [ S + O ⁇ ( 0.8 ⁇ Ca ( ppm ) ) ⁇ ( 0.3 ⁇ Ce ( ppm ) ) ] ⁇ 40 ppm .
  • This value represents the percentage of a ⁇ -ferrite amount in a solidification structure. When ⁇ -ferrite appears, it mitigates the segregation of S and O at the portions where intergranular corrosion occurs.
  • a ⁇ -ferrite amount (in volume percent) is in the range from larger than -20% to smaller than 16%, the synergetic effect with the function of the regulation [S + O - (0.8 x Ca (ppm)) - (0.3 x Ce (ppm))] ⁇ 40 ppm is effectuated and hot workability is improved remarkably. Therefore, the ⁇ cal value was limited in the range from -20 to 16.
  • the corrosion rate of the stainless steel is not more than 1 mm/y., at which corrosion rate the stainless steel can stand actual use with no problems.
  • a GI value exceeds 88 the alloy addition effect decreases and, at the same time, the cost in the production of a stainless steel increases substantially and, thus, the stainless steel cannot stand actual use. For that reason, the GI value was limited in the range from 75 to 88.
  • Table 1 shows the comparison between the invention steels and the comparative steels with regard to the chemical compositions, general corrosion resistance and pitting corrosion resistance.
  • Those steels were melted and refined by the electric furnace-AOD method and the electric furnace-VAC method.
  • the resulting molten steels were cast into continuously produced slabs under normal conditions. Thereafter, the slabs were subjected to a soaking treatment in the temperature range from 1,150°C to 1,250°C for a half to one hour. After being subjected to surface conditioning, the slabs were hot rolled into the thickness of 6 mm, heated at a temperature of 1,100°C for a half hour, and thereafter subjected to a solution heat treatment by water quenching. Then the specimens for the sulfuric acid corrosion test and the specimens for the pitting corrosion potential measurement in salt water were cut out from the steel products and the specimens were subjected to the test and the measurement.
  • Fig. 5 shows the result of the relation between the GI values and the PI values with respect to the invention steels and the comparative steels.
  • the area that conforms to the present invention is shaded with oblique lines and the invention steels in Table 1 are shown by the symbols • (the comparative steels by the symbols O).
  • the corrosion test specimens 25 x 25 mm in size and 4 mm in thickness were cut out from the product sheets, the whole surfaces thereof were polished up to the roughness of #400 with wet emery paper, thereafter the specimens were subjected to ultrasonic cleaning in acetone and then dried, the weights of the specimens before subjected to the test treatments were measured precisely using a chemical balance, and after that the specimens were immersed in a solution having a sulfuric acid concentration of 50% for six hours at 40°C. After the elapse of a prescribed time, the specimens were pulled up quickly from the sulfuric acid solution, subjected to water rinse, cleaned of corrosion products, subjected to ultrasonic cleaning in acetone, and dried. Thereafter the weights of the specimens after being subjected to the test treatments were measured, and the corrosion rates were calculated from the weight differences between before and after the test treatments.
  • the measurement was carried out basically by a method conforming to the method described in JIS G0577 except the temperature that was changed to 40°C.
  • the synthetic evaluation was carried out by directly calculating the GI values and the PI values. That is, the specimens satisfying both the expressions 75 ⁇ GI ⁇ 88 and 23 ⁇ PI ⁇ 32 simultaneously were represented by the mark O, and the specimens that do not satisfy either or both of the expressions by the mark X.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
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Claims (2)

  1. Utilisation d'un acier dans un réservoir chimique pour le stockage et le transport d'acide sulfurique brut, l'acier étant excellent concernant la résistance à la corrosion par l'acide sulfurique et à la corrosion par piqûres, où l'acier contient, en masse,
    C : 0,003 à 0,05 %,
    Si : pas plus de 5 %,
    Mn : pas plus de 2 %,
    P : pas plus de 0,03 %,
    S : pas plus de 0,010 %,
    O : pas plus de 0,0050 %,
    Cr : 18 à 25 %,
    Ni : 10 à 20 %,
    Mo : 1,0 à 4,5 %,
    Cu : 1,0 à 3,0%,
    N : 0,05 à 0,3 %, et éventuellement un ou plusieurs parmi
    W : pas plus de 3 %,
    V : pas plus de 4 %,
    Co : pas plus de 2 %,
    Ti : pas plus de 1 %,
    Ca : 0,001 à 0,03 %, et
    Ce : 0,001 à 0,03 %,
    le complément consistant en Fe et en impuretés inévitables ;
    la valeur GI (indice de résistance à la corrosion générale) définie par l'expression suivante est dans la plage de 75 à 88, GI = [ Cr ] + 1 , 6 × [ Ni ] + 6 , 0 × [ Mo ] + 7 , 1 × [ Cu ] ,
    Figure imgb0012
    où les composants pertinents sont exprimés en termes de % en masse ; et
    la valeur PI (indice de résistance à la corrosion par piqûres) définie par l'expression suivante est dans la plage de 23 à 32, PI = [ Cr ] + 1 , 3 × [ Mo ] + 1 , 4 × [ Cu ] + 2 , 2 × [ N ] ,
    Figure imgb0013
     où les composants pertinents sont exprimés en termes de % en masse.
  2. Utilisation d'un acier dans un réservoir chimique pour le stockage et le transport d'acide sulfurique brut selon la revendication 1, où l'acier contient Ca ou Ce ou Ca et Ce à raison de 0,001 à 0,03 % en masse ;
    la valeur δcal définie par l'expression suivante est dans la plage de -20 à 16,
    δcal = 3 x ([Cr] + 1,5 x [Si] + [Mo]) - 2,8 ([Ni] + 0,5 x [Mn] + 30 x [C] + 30 x [N] + 0,5 x [Cu]) - 19,8, où les composants pertinents sont exprimés en termes de % en masse ; et
    la valeur de l'expression [S] + [O] - 0,8 × [Ca] - 0,3 × [Ce] n'est pas supérieure à 40, où les composants pertinents sont exprimés en termes de ppm en masse (1 ppm en masse = 0,0001 % en masse).
EP03010309A 2002-05-10 2003-05-07 Utilisation d'un acier pour cuves chimiques avec excellente résistance à la corrosion par l'acide sulfurique et une résistance à la corrosion par piqûre Expired - Lifetime EP1361290B1 (fr)

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JP2002135883 2002-05-10

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US20060243356A1 (en) 2005-02-02 2006-11-02 Yuusuke Oikawa Austenite-type stainless steel hot-rolling steel material with excellent corrosion resistance, proof-stress, and low-temperature toughness and production method thereof
JP4754362B2 (ja) * 2005-02-02 2011-08-24 新日鐵住金ステンレス株式会社 耐食性、耐力、低温靱性が良好なオーステナイト系ステンレス熱間圧延鋼材およびその製造方法
JP5116265B2 (ja) * 2006-07-13 2013-01-09 新日鐵住金ステンレス株式会社 強度及び延性に優れたオーステナイト系ステンレス圧延鋼板及びその製造方法
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JPS6023185B2 (ja) * 1977-07-02 1985-06-06 新日本製鐵株式会社 耐隙間腐食特性の優れた高耐食オ−ステナイトステンレス鋼
JPH0248614B2 (ja) * 1987-07-15 1990-10-25 Nippon Yakin Kogyo Co Ltd Netsukankakoseinisugurerukotaishokuseioosutenaitosutenresukotosonoseizohoho
JPH068485B2 (ja) * 1988-12-23 1994-02-02 新日本製鐵株式会社 耐食性の優れた煙突・煙道および脱硫装置用高合金ステンレス鋼
JP2774709B2 (ja) * 1991-05-22 1998-07-09 日本冶金工業 株式会社 熱間加工性に優れた耐硫酸露点腐食ステンレス鋼
CN1048760C (zh) * 1995-01-24 2000-01-26 中国科学院金属腐蚀与防护研究所 一种稀硫酸用不锈钢
JP2002241900A (ja) * 1997-08-13 2002-08-28 Sumitomo Metal Ind Ltd 耐硫酸腐食性と加工性に優れたオーステナイト系ステンレス鋼

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EP1361290A1 (fr) 2003-11-12
DE60306981T2 (de) 2007-03-08
ES2263874T3 (es) 2006-12-16
JP3736631B2 (ja) 2006-01-18
KR20030087955A (ko) 2003-11-15
DE60306981D1 (de) 2006-09-07
JP2003328087A (ja) 2003-11-19
KR100545750B1 (ko) 2006-01-24

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