FI125105B - Austenitic stainless steel with grain boundary corrosion and method of manufacture - Google Patents

Austenitic stainless steel with grain boundary corrosion and method of manufacture Download PDF

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Publication number
FI125105B
FI125105B FI20136077A FI20136077A FI125105B FI 125105 B FI125105 B FI 125105B FI 20136077 A FI20136077 A FI 20136077A FI 20136077 A FI20136077 A FI 20136077A FI 125105 B FI125105 B FI 125105B
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Prior art keywords
stainless steel
austenitic stainless
heat treatment
grain boundary
plastic deformation
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FI20136077A
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Finnish (fi)
Swedish (sv)
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FI20136077A (en
Inventor
Juho Talonen
Hannu Hänninen
Antti Forsström
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Outokumpu Oy
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Priority to FI20136077A priority Critical patent/FI125105B/en
Priority to PCT/FI2014/050822 priority patent/WO2015063374A1/en
Priority to TW103138169A priority patent/TW201522661A/en
Publication of FI20136077A publication Critical patent/FI20136077A/en
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Publication of FI125105B publication Critical patent/FI125105B/en

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—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
    • C22C38/18—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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese

Description

AUSTENITIC STAINLESS STEEL RESISTANT TO INTERGRANULAR CORROSION AND A METHOD FOR ITS PRODUCTION
This invention relates to an austenitic stainless steel that is resistant to intergranular corrosion caused by a phenomenon called as sensitization. The steel according to the invention differs from conventional austenitic stainless steels in that it is not susceptible to sensitization and intergranular corrosion though it contains high amount of carbon. The invention also relates to a method for producing the austenitic stainless steel.
Due to fluctuating nickel price the stainless steel industry is developing low-nickel and nickel-free alternatives for nickel-containing austenitic stainless steels. In these steels nickel is an important alloying element as it stabilises the austenite phase. Several alloying elements can be utilised to replace nickel, for instance: manganese, copper, nitrogen and carbon. Of these alloying elements manganese, copper and nitrogen are commonly used. Carbon, however, is considered to be an undesired impurity, because it has a tendency to form chromium carbides. Chromium carbides tend to form in particular at the grain boundaries of the steel, which leads to depletion of chromium in these regions. This phenomenon, called as sensitization, occurs if the material is subjected long enough time to temperatures at which the carbides tend to form, typically around 600-900°C. Sensitization may occur, for instance, during welding. Sensitization is harmful, as it can lead to rapid intergranular corrosion attack. In practice, risk of sensitization prevents utilisation of carbon as an alloying element. Instead, in modern stainless steels it is common that the maximum allowed carbon content is less than 0.03 weight %.
A method called as “grain boundary engineering” can be utilised to reduce materials' susceptibility to intergranular corrosion. The grain boundary engineering involves a modification of structure of grain boundaries by thermomechanical treatment including deformation at room temperature and subsequent heat treatment. The grain boundary engineering process may involve a single deformation and a heat treatment, or several such cycles. As the result of the grain boundary engineering process the regular random grain boundaries are replaced by a high fraction of special grain boundaries, referred to as coincidence site lattice (CSL) boundaries. Several patent publications relate to grain boundary engineering of austenitic stainless steels, for instance, US 5817193, JP 2003-253401, EP 2112237 A1.
However, none of these publications relate to utilization of grain boundary engineering in allowing use of carbon as an alloying element stabilising austenite and providing solid solution strengthening. No high carbon containing austenitic stainless steels utilising grain boundary engineering have been disclosed.
The object of the present invention is to prevent drawbacks of the prior art and to produce an austenitic stainless steel having good mechanical properties, low alloying costs and high resistance to intergranular corrosion. The present invention relates also to a production method of such a stainless steel. The essential features of the present invention are enlisted in the appended claims.
The present invention relates to an austenitic stainless steel in the form of a flat or long product, which stainless steel has high strength, low alloying costs and high resistance to intergranular corrosion. Such combination of desired properties is achieved with a manufacturing process according to the invention.
In accordance with the invention the stainless steel is an austenitic stainless steel containing in weight % 0.03 - 0.5 % C, 0.01 - 3 % Si, 0.01 - 20 % Mn, 10 -30 % Cr, 0.01 - 10 % Ni, 0.01 - 3 % Mo, 0.01 - 3 % Cu, 0.03 - 0.5 % N, 0.001 - 0.5 % Nb, 0.001 - 0.5 % Ti, 0.001 - 0.5 % V, the balance of Fe and inevitable impurities.
The stainless steel processed according to the method of the invention is advantageously in the form of a flat or long product such as a plate, a sheet, a strip, a coil, a bar, a rod or a wire.
The stainless steel and its production method according to the invention is based on the utilization of grain boundary engineering for modification of grain boundary structure of the steel. According to invention the grain boundary structure of the stainless steel is modified by at least one thermomechanical processing consisting of at least one plastic deformation stage, preferably for instance cold rolling or tensile straining, and at least one subsequent heat treatment stage. The thermomechanical processing can be repeated several times. After the thermomechanical processing stages the desired fraction of special grain boundaries in the microstructure of the stainless steel is achieved to exceed at least 60%, and preferably at least 80%. The thermomechanical processing in accordance with the invention contains at least one deformation stage and at least one subsequent heat treatment step. The deformation degree in a single deformation stage is at the range of 0.1 - 40 % dependent on the chemical composition of the stainless steel to be treated. The subsequent heat treatment is carried out at the temperature range of 800 -1200°C the time for this treatment being from 1 second to 72 hours depending on the preceding deformation degree and the chemical composition of the stainless steel to be treated. When more than one deformation stage is used, an equal number of the subsequent heat treatment stages is also carried out. If the thermomechanical processing consists of one deformation stage and one heat treatment, the deformation degree is typically rather low, order of 0.1-10% and the subsequent heat treatment is carried out at lower regime of the indicated temperature range and in the upper regime of the indicated time range. If the thermomechanical processing consists of several deformation stages and heat treatments, the deformation degrees during a single deformation stage are typically higher, the heat treatment temperatures higher and the heat treatment durations shorter. The deformation degrees and respectively the heat treatment conditions are the same in two or more thermomechanical processings or the reduction degrees and respectively the heat treatment conditions are different from each other in two or more thermomechanical processings.
The thermochemical processing in accordance with the invention makes possible to utilise carbon as an austenite stabilising and austenite forming element, and to utilise carbon as an alloying element providing solid solution strengthening. Therefore, the stainless steel contains 0.03 - 0.5 % carbon (C), preferably 0.1 - 0.5 % carbon (C). This high content of carbon is beneficial due to two main reasons: carbon improves mechanical properties of the steel, and carbon is also a cost efficient austenite stabilising element that enables lower use of expensive nickel. An additional benefit is that allowing higher carbon content in the stainless steel enables shorter process time for instance in costly argon-oxygen decarburization (AOD) process, and also enables use of carbon-containing ferromanganese as a source of manganese, which is also utilised as a cost-efficient austenite-forming element.
The stainless steel according to the invention is advantageously produced via the conventional stainless steel process route including among others melting in an electric arc furnace, AOD (Argon Oxygen Decarburization) converter treatment and ladle treatment, continuous casting, hot rolling, possibly cold rolling, annealing and pickling. After the conventional processing of the stainless steel to a flat or long product manufactured for instance by hot rolling, cold rolling, drawing, extrusion, forging, the material is thermomechanically processed by deforming and subsequent heat treating according to the invention to modify the grain boundary structure of the stainless steel.
The present invention is described in more details referring to the following drawings, in which
Fig. 1a shows the microstructure of a conventional stainless steel,
Fig. 1b shows the microstructure of a stainless steel according to the invention,
Fig. 2 shows corrosion rate of a conventional stainless steel and the stainless steel according to the invention in a Streicher test in both non-sensitized and sensitized condition,
Fig. 3a shows scanning electron microscope image of the surface of a conventional stainless steel after a Streicher test, and
Fig. 3b shows scanning electron microscope image of the surface of the stainless steel according to the invention after a Streicher test.
The stainless steel of the invention was tested by performing various cold rolling and heat treatment experiments. Examples of microstructures are shown in Fig. 1a for a conventional austenitic stainless steel without any thermomechanical processing and in Fig. 1b for the stainless steel according to the invention after the thermomechanical processing consisting of cold rolling with the reduction degree 1 % and the subsequent heat treatment at the temperature 947°C for 24 hours. The desired special grain boundaries are shown in light gray and random grain boundaries in dark grey in Fig. 1a and in Fig. 1b. In the stainless steel according to the invention the fraction of the desired special grain boundaries is 82% compared to only 38% in the conventional steel.
The intergranular corrosion resistance of the conventional stainless steel and the stainless steel according to the invention are compared in Fig. 2. Fig. 2 presents results of the Streicher test (according to the standard ASTM A262-85 Practice B). In accordance with this corrosion rate test the materials were boiled for 120 hours in an 1 liter Erlenmeyer flask the conditions containing 50 % sulfuric acid and 25 grams of ferric sulfate in order to determine the sensitization effect in the materials. A measure of sensitization effect was weight loss due to the intergranular corrosion, which was determined by measuring weight of samples with 24 hour intervals. In Fig. 2 results are presented for both non-sensitized and sensitized stainless steels. The sensitized test samples were sensitized by a heat treatment at 745°C for 30 min. The stainless steel according to the invention clearly outperformed the conventional stainless steel both in sensitized and non-sensitized conditions. In the sensitized condition the intergranular corrosion attack was so severe in the conventional stainless steel that the sample dissolved entirely before the first weighing of the sample.
Surfaces of the conventional stainless steel (Fig. 3a) and the stainless steel according to the invention (Fig. 3b) after 120 h exposure to Streicher test are shown in Fig. 3a and in Fig. 3b. These samples were not sensitized before the test. Flowever, it can be seen that the conventional stainless steel was clearly attacked at the grain boundaries, whereas no signs of corrosion attack can be seen in the stainless steel thermomechanically processed according to the invention.

Claims (13)

1 Austeniittinen ruostumaton teräs, jolla on korkea raerajakorroosiokestävyys, tunnettu siitä, että hyvää raerajakorroosiokestävyyttä varten ruostumaton teräs, jota prosessoidaan termomekaanisesti omaamaan ruostumattoman teräksen mikrorakenteessa erityisraerajojen (coincidence site lattice) osuudeksi ainakin 60 %, mieluummin ainakin 80 %, sisältää paino-%:na 0.03 - 0.5 % C, 0.01 - 3 % Si, 0.01 - 20 % Mn, 10-30 % Cr, 0.01 - 10 % Ni, 0.01 - 3 % Mo, 0.01 - 3 % Cu, 0.03 - 0.5 % N, 0.001 - 0.5 % Nb, 0.001 - 0.5 % Ti, 0.001 - 0.5 % V, lopun ollessa Fe ja vääjäämättömiä epäpuhtauksia, jossa austeniittisessa ruostumattomassa teräksessä hiiltä käytetään austeniitin muodostumisaineena ja austeniitin stabilointiaineena ja jähmeän liuoksen vahvistusaineena.1 Austenitic stainless steel with high grain boundary corrosion resistance, characterized in that, for good grain boundary corrosion resistance, stainless steel is processed thermomechanically to have a coincidence site lattice of at least 80%, preferably at least 60%, preferably at least 60%, preferably 3% by weight. - 0.5% C, 0.01 - 3% Si, 0.01 - 20% Mn, 10-30% Cr, 0.01 - 10% Ni, 0.01 - 3% Mo, 0.01 - 3% Cu, 0.03 - 0.5% N, 0.001 - 0.5 % Nb, 0.001 - 0.5% Ti, 0.001 - 0.5% V, with the remainder being Fe and unavoidable impurities in which carbon is used in the austenitic stainless steel as an austenite-forming and austenite-stabilizing agent and as a solid solution reinforcement. 2. Patenttivaatimuksen 1 mukainen austeniittinen ruostumaton teräs, tunnettu siitä, että ruostumaton teräs sisältää 0,1 - 0,5 % hiiltä.Austenitic stainless steel according to claim 1, characterized in that the stainless steel contains 0.1 to 0.5% carbon. 3. Patenttivaatimuksen 1 tai 2 mukainen austeniittinen ruostumaton teräs, tunnettu siitä, että ruostumaton teräs on litteän tai pitkän tuotteen muodossa.Austenitic stainless steel according to claim 1 or 2, characterized in that the stainless steel is in the form of a flat or long product. 4. Patenttivaatimuksen 3 mukainen austeniittinen ruostumaton teräs, tunnettu siitä, että ruostumaton teräs on levyn, ohut levyn, nauhan, rullan, tangon, kangen tai langan muodossa.Austenitic stainless steel according to claim 3, characterized in that the stainless steel is in the form of a sheet, a thin sheet, a strip, a roll, a rod, a rod or a wire. 5. Jonkin edellä olevan patenttivaatimuksen 1-4 mukainen austeniittinen ruostumaton teräs, tunnettu siitä, että termomekaaninen prosessointi koostuu ainakin yhdestä plastisen muodonmuutoksen vaiheesta ja ainakin sitä seuraavasta lämpökäsittelyvaiheesta.Austenitic stainless steel according to any one of claims 1 to 4, characterized in that the thermomechanical processing consists of at least one plastic deformation step and at least a subsequent heat treatment step. 6. Menetelmä korkean raerajakorroosiokestävyyden omaavan austeniittisen ruostumattoman teräksen tuottamiseksi, tunnettu siitä, että termomekaaninen prosessointi suoritetaan austeniittiselle ruostumattomalle teräkselle, joka sisältää paino-%:na 0.03 - 0.5 % C, 0.01 - 3 % Si, 0.01 - 20 % Mn, 10-30 % Cr, 0.01 - 10 % Ni, 0.01 - 3 % Mo, 0.01 - 3 % Cu, 0.03 - 0.5 % N, 0.001 - 0.5 % Nb, 0.001 - 0.5 % Ti, 0.001 - 0.5 % V, lopun ollessa Fe ja vääjäämättömiä epäpuhtauksia, litteän tai pitkän tuotteen muodossa aikaansaamaan ruostumattoman teräksen mikrorakenteessa erityisraerajojen (coincidence site lattice) osuudeksi ainakin 60 %, mieluummin ainakin 80 %.6. A process for producing austenitic stainless steel with high grain boundary corrosion resistance, characterized in that the thermomechanical processing is carried out on austenitic stainless steel containing by weight 0.03 to 0.5% C, 0.01 to 3% Si, 0.01 to 20% Mn, 10-30 % Cr, 0.01 - 10% Ni, 0.01 - 3% Mo, 0.01 - 3% Cu, 0.03 - 0.5% N, 0.001 - 0.5% Nb, 0.001 - 0.5% Ti, 0.001 - 0.5% V, the remainder being Fe and inevitable impurities, in the form of a flat or long product, to provide a coincidence site lattice of at least 60%, preferably at least 80%, in the microstructure of the stainless steel. 7. Patenttivaatimuksen 6 mukainen menetelmä, tunnettu siitä, että termomekaaninen prosessointi koostuu ainakin yhdestä plastisen muodonmuutoksen vaiheesta ja ainakin yhdestä sitä seuraavasta lämpökäsittelyvaiheesta.Method according to Claim 6, characterized in that the thermomechanical processing consists of at least one plastic deformation step and at least one subsequent heat treatment step. 8. Patenttivaatimuksen 6 tai 7 mukainen menetelmä, tunnettu siitä, että plastinen muodonmuutosvaihe on kylmävalssausvaihe.Method according to claim 6 or 7, characterized in that the plastic deformation step is a cold rolling step. 9. Patenttivaatimuksen 6 tai 7 mukainen menetelmä, tunnettu siitä, että plastinen muodonmuutosvaihe on vetojännitysvaihe.Method according to claim 6 or 7, characterized in that the plastic deformation step is a tensile stress step. 10. Jonkin edellä olevan patenttivaatimuksen 6-9 mukainen menetelmä, tunnettu siitä, että plastinen muodonmuutosaste on 0,1 - 40 %.Method according to any one of claims 6 to 9, characterized in that the degree of plastic deformation is 0.1 to 40%. 11. Jonkin edellä olevan patenttivaatimuksen 6-10 mukainen menetelmä, tunnettu siitä, että plastista muodonmuutosvaihetta seuraava lämpökäsittelyvaihe suoritetaan lämpötilavälillä 800 - 1200 °C 1 sekunti - 72 tuntia.The method according to any one of claims 6 to 10, characterized in that the heat treatment step following the plastic deformation step is carried out at a temperature between 800 and 1200 ° C for 1 second to 72 hours. 12. Jonkin edellä olevan patenttivaatimuksen 6-11 mukainen menetelmä, tunnettu siitä, että muodonmuutosasteet ja vastaavasti lämpökäsittely-olosuhteet ovat samat kahdessa tai useammassa termomekaanisessa prosessoinnissa.Process according to one of the preceding claims 6 to 11, characterized in that the degree of deformation and, respectively, the heat treatment conditions are the same in two or more thermomechanical processes. 13. Jonkin edellä olevan patenttivaatimuksen 6-11 mukainen menetelmä, tunnettu siitä, että muodonmuutosasteet ja vastaavasti lämpökäsittely-olosuhteet ovat erilaisia toisistaan kahdessa tai useammassa termomekaanisessa prosessoinnissa.Process according to one of the preceding claims 6 to 11, characterized in that the degree of deformation and the heat treatment conditions, respectively, are different in two or more thermomechanical processes.
FI20136077A 2013-11-04 2013-11-04 Austenitic stainless steel with grain boundary corrosion and method of manufacture FI125105B (en)

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FI20136077A FI125105B (en) 2013-11-04 2013-11-04 Austenitic stainless steel with grain boundary corrosion and method of manufacture
PCT/FI2014/050822 WO2015063374A1 (en) 2013-11-04 2014-11-03 Austenitic stainless steel resistant to intergranular corrosion and a method for its production
TW103138169A TW201522661A (en) 2013-11-04 2014-11-04 Austenitic stainless steel resistant to intergranular corrosion and a method for its production

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US11268177B2 (en) * 2015-09-30 2022-03-08 Nippon Steel Corporation Austenitic stainless steel
KR102160735B1 (en) * 2018-08-13 2020-09-28 주식회사 포스코 Austenitic stainless steel with improved strength
CN111334700A (en) * 2018-12-18 2020-06-26 财团法人金属工业研究发展中心 High-nitrogen low-nickel austenitic stainless steel alloy and manufacturing method thereof
CN113025919A (en) * 2019-12-24 2021-06-25 南通耀龙金属制造有限公司 High-strength anti-bending anti-corrosion stainless steel alloy material and preparation method thereof
EP3960881A1 (en) * 2020-09-01 2022-03-02 Outokumpu Oyj Austenitic stainless steel
CN115679225A (en) * 2021-07-28 2023-02-03 叶均蔚 High chromium silicon corrosion resistant steel and use thereof
CN114457288A (en) * 2022-01-20 2022-05-10 山西太钢不锈钢股份有限公司 High-nitrogen austenitic stainless steel and preparation method of middle plate thereof

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JP2009287104A (en) * 2008-05-30 2009-12-10 Hitachi-Ge Nuclear Energy Ltd Thin sheet of austenitic stainless steel and manufacturing method therefor
JP2010275569A (en) * 2009-05-26 2010-12-09 Hitachi-Ge Nuclear Energy Ltd Austenitic stainless steel and method of manufacturing the same
JP2011168819A (en) * 2010-02-17 2011-09-01 Hitachi-Ge Nuclear Energy Ltd Austenitic stainless steel and method for manufacturing the same

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