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EP1645650A1 - Duplexedelstahl - Google Patents

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Publication number
EP1645650A1
EP1645650A1 EP04746980A EP04746980A EP1645650A1 EP 1645650 A1 EP1645650 A1 EP 1645650A1 EP 04746980 A EP04746980 A EP 04746980A EP 04746980 A EP04746980 A EP 04746980A EP 1645650 A1 EP1645650 A1 EP 1645650A1
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EP
European Patent Office
Prior art keywords
stainless steel
inclusions
duplex stainless
present
steel
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.)
Withdrawn
Application number
EP04746980A
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English (en)
French (fr)
Other versions
EP1645650A4 (de
Inventor
Kazuhiro Sumitomo Metal Industries Ltd. OGAWA
Tomohiko Sumitomo Metal Industries Ltd. OMURA
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 Corp
Original Assignee
Sumitomo Metal Industries Ltd
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Filing date
Publication date
Application filed by Sumitomo Metal Industries Ltd filed Critical Sumitomo Metal Industries Ltd
Publication of EP1645650A1 publication Critical patent/EP1645650A1/de
Publication of EP1645650A4 publication Critical patent/EP1645650A4/de
Withdrawn legal-status Critical Current

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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
    • 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
    • C22C38/001—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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron

Definitions

  • This invention relates to a duplex stainless steel and particularly to a duplex stainless steel having excellent weldability and pitting resistance.
  • Duplex stainless steels have excellent strength and corrosion resistance and particularly resistance to corrosion in sea water, and they have long been used in a wide range of technical fields of steel pipes for use in heat exchangers and the like. In the past, there have been many proposals for compositions of duplex stainless steels having improved corrosion resistance, strength, workability, and the like.
  • the object of the present invention is to provide a duplex stainless steel having excellent pitting resistance and weldability and particularly a duplex stainless steel having excellent pitting resistance and weldability which does not form intermetallic compounds such as minute sigma phases even in a weld heat affected zone.
  • the present inventors performed various research with the goal of achieving the above described objects and they found the following.
  • a structure which is obtained by rapid heating and rapid cooling in a short length of time such as occur in welding referred to below simply as a "rapid heating/rapid cooling structure"
  • formation of sigma phases is controlled by the formation of sigma phase nuclei and growth of the nuclei.
  • the present inventors found that the formation of sigma phase nuclei is suppressed by addition of around 2% of W, and that under these conditions, it also depends on the amount ofNi and Mo. Ni and Mo are essential elements for guaranteeing ordinary corrosion resistance such as resistance to crevice corrosion and pitting resistance.
  • Equation (1) The metallurgical meaning of Equation (1) is as follows.
  • a sigma phase is an intermetallic compound having a composition in which the ratio of Cr to Fe is approximately 1:1, and in order to form sigma phase nuclei by heating during welding, for example, it is necessary to increase the concentration of Cr.
  • Mo is not necessarily a main constituent element of sigma phases. However, when Mo is present, the activation energy for forming nuclei is reduced, even smaller embryo (the appearance of nuclei) are not eliminated, and stable nuclei are formed. At the sigma phases precipitation temperature, when Ni is present, a ferrite phase becomes unstable. As a result, the driving force of a reaction for transformation of ferrite phase into sigma phase and austenite phase is increased.
  • the left side of Equation (1) is a parameter which describes the relative level of the nucleus forming frequency.
  • the formation of sigma phases can be suppressed to a level which does not affect pitting resistance.
  • sigma phase nuclei is greatly affected by the presence of oxide inclusions in the parent metal.
  • Sigma phases easily precipitate in a low temperature HAZ heated to a temperature of 700 - 1000 °C, which is a temperature range at least 400 °C lower than the melting point of steel.
  • a portion which is heated to just below the melting point of steel will be referred to as a high temperature HAZ, while a HAZ which is heated to a relatively low temperature will be referred to as a low temperature HAZ.
  • the form of an austenite phase does not change in the temperature range of a low temperature HAZ, the formation of sigma phase nuclei is greatly affected by the presence of inclusions in the parent metal. Namely, at the border between inclusions and a steel matrix, the free energy is high, so nuclei having a reduced energy due to precipitation form easily.
  • oxide type inclusions including Al, Mg, or Ca and particularly inclusions including Al have a particularly high surface energy, that coarse inclusions thereof above a certain size are harmful inclusions which promote sigma phase precipitation, and that reducing their density is effective at suppressing precipitation of sigma phases in a HAZ.
  • Figure 1 shows the relationship between the density of coarse inclusions having a major diameter of at least 5 micrometers and containing at least 20 mass % of Al in a HAZ and the temperature for the occurrence of pitting.
  • the number of such alumina type coarse inclusions is at least 20 2 per mm .
  • Equation (1) if the amounts of Mo and Ni are decreased, the formation of sigma phase nuclei in a HAZ is suppressed, and it should be possible to obtain good pitting resistance due to the absence of sigma phases. However, if the amount of Ni is excessively decreased, in a high temperature HAZ which is heated to just below the melting point, the formation of nitrides is promoted. The formation of such nitrides causes pitting in the same manner as with the formation of sigma phases.
  • the driving force for precipitation of nitrides depends upon the solid solubility ofN and the speed of diffusion in the parent metal in a temperature range of at least 500 °C in which N can diffuse in a short period of time.
  • Addition ofNi increases the temperature for the start of precipitation of an austenite phase which precipitates in the course of cooling from a state in which it has been heated to just below the melting point of a purely ferrite phase.
  • Precipitation of austenite phase at a high temperature means that N present in a supersaturated state in a ferrite phase moves towards an austenite phase in which N has a high solid solubility, in a shorter period of time. This also promotes formation of austenite phase, and it effectively contributes to alleviating the degree of supersaturation ofN in ferrite phase, which increases as cooling progresses. As a result, the precipitation of nitrides is suppressed.
  • the left side of Equation (2) is a parameter which describes the relative degree of supersaturation of N in a ferrite phase due to a change in the temperature at which austenite phase forms.
  • this parameter at most -1.6 and suppressing formation of nitrides, the occurrence of pitting caused thereby can be nearly entirely suppressed.
  • PREW is at least 40.
  • a duplex stainless steel according to the present invention exhibits excellent weldability (maintaining pitting resistance without decreasing welding performance) by the overall effect of the above-described plurality of types of alloying elements and by control of the structure.
  • the most significant characteristic resides in the combination of optimum amounts of Ni and Mo and control of coarse alumina type inclusions.
  • C In the same manner as described below with respect to N, C is effective at stabilizing an austenite phase. However, if its content exceeds 0.03%, carbides easily precipitate and corrosion resistance worsens, so it is made at most 0.03%. Preferably it is at most 0.02%.
  • the present invention includes the case in which C is included as an impurity.
  • Si is effective as a deoxidizing component of steel, but it is an element which promotes formation of intermetallic compounds (sigma phases and the like), so in the present invention it is limited to at most 1.0%. Preferably it is at most 0.5%.
  • the present invention includes the case in which Si is present as an impurity.
  • Mn increases hot workability by a desulfurization and deoxidation effect during preparation of a duplex stainless steel. It also has the effect of increasing the solubility ofN. In order to obtain these effects, its content is normally up to 2.0%. However, Mn is an element which decreases corrosion resistance. In the present invention it is limited to at most 1.5%. Preferably it is at most 1.0%. The present invention includes the case in which Mn is contained as an impurity.
  • P is an impurity element which is unavoidably mixed into steel. If its content exceeds 0.040%, corrosion resistance and toughness markedly deteriorate, so its upper limit is made 0.040%.
  • S is an impurity element which is unavoidably mixed into steel and worsens the hot workability of steel.
  • sulfides become the starting points of pitting and worsen pitting resistance.
  • its content is suppressed to at most 0.008%. It is preferably as small as possible at or below this level, and at most 0.005% is particularly preferred.
  • Cr is a fundamental component which is effective for maintaining corrosion resistance. If its content is less than 23.0%, a parent metal having the corrosion resistance of a so-called super duplex stainless steel is not obtained. On the other hand, if the Cr content exceeds 27.0%, precipitation of intermetallic compounds (sigma phases and the like) becomes marked, and this leads to a decrease in hot workability and a worsening of weldability.
  • Mo In the same manner as Cr, Mo contributes to an increase in PREW, and it is a component which is extremely effective at improving corrosion resistance. Particularly in order to increase pitting resistance and resistance to crevice corrosion, its content is made at least 2.0% in the present invention. On the other hand, excessive addition of Mo becomes a cause of embrittlement of a material during manufacture, and in the same manner as Cr, it has a strong effect of facilitating precipitation of intermetallic compounds. Accordingly, the content of Mo is limited to 4.0%.
  • Ni is a component which is essential for stabilizing austenite. However, if its content exceeds 9.0%, due to a decrease in the amount of ferrite, it becomes difficult to guarantee the basic properties of a duplex stainless steel, and it becomes easy for sigma phases and the like to precipitate. On the other hand, if the Ni content is smaller than 5.0%, the amount of ferrite becomes too large, and in the same manner, the properties of a duplex stainless steel are not obtained. In addition, the solid solubility ofN in ferrite is small, so nitrides precipitate and corrosion resistance worsens.
  • Mo and Ni indicate the respective content (in mass %) of these elements.
  • PREW pitting resistance index
  • the contents of Cr, Mo, and N are adjusted so that PREW is at least 35.
  • Cr, Mo, and N are further increased and PREW is made at least 40, so an exceptional resistance to corrosion in sea water is exhibited.
  • An increase in Cr, Mo, and N contributes to a higher strength of steel, so a duplex stainless steel which already has a higher strength than a single-phase ferrite or austenite steel becomes a super duplex stainless steel having an even higher strength.
  • W is an element which increases corrosion resistance and particularly resistance to pitting and crevice corrosion. Above all, it is an element which forms stable oxides which increase corrosion resistance in a low pH environment. Accordingly, greater than 1.5% of W is added. If it is 1.5% or less, it becomes necessary to increase the added amounts of Cr, Mo, N, and the like in order to make PREW at least 40, so the effects of utilizing W decrease. The greater the content of W is, the smaller the contents of Cr and Mo can be made in order to make PREW at least 40, and damage caused by promotion of the formation of sigma phases and the like by these elements can be reduced. A preferred content of W is greater than 2.0%. However, if W is added in excess of 5.0%, an increase in effects commensurate therewith is not observed and costs merely increase accordingly, so its upper limit is made 5.0%.
  • N is a powerful austenite forming element. It is effective for improving the thermal stability and corrosion resistance of a duplex stainless steel. When large amounts of Cr and Mo, which are ferrite forming elements, are added as is the case with the steel of the present invention, at least 0.24% of N is added in order to obtain a suitable balance between ferrite and austenite phases.
  • N also contributes to an increase in PREW, and it increases the corrosion resistance of an alloy in the same manner as Cr, Mo, and W.
  • a duplex stainless steel like the steel of the present invention containing around 25% of Cr ifN is contained in excess of 0.35%, the toughness and corrosion resistance of the steel are worsened due to defects caused by the formation of blow holes or due to the formation of nitrides caused by thermal effects at the time of welding. Therefore, the upper limit on N is made 0.35%.
  • Sol. Al is effective as a deoxidizing agent of steel, but when the amount of N in a steel is high, it precipitates as AlN (aluminum nitride), and it worsens toughness and corrosion resistance. In addition, it forms oxides, and these become sites of formation of nuclei of sigma phases. Accordingly, in the present invention, the Al content expressed as sol. Al is made at most 0.040%. In the present invention, addition of a large amount of Si is avoided, so Al is often used as a deoxidizing agent, but when vacuum melting is carried out, it is not always necessary to add Al.
  • a duplex stainless steel according to the present invention may if necessary include at least one element from the following Groups 1 and 2 in addition to the above-described components.
  • Element Group 1 (Cu, V): At least one of Cu and V can be contained in a duplex stainless steel of the present invention. They have equivalent effects from the standpoint of increasing corrosion resistance and particularly resistance to acids such as sulfuric acid.
  • Cu is particularly effective at improving resistance to acids in a reducing low-pH environment, such as a H 2 SO 4 or hydrogen sulfide environment. In order to obtain this effect, its content is made at least 0.2%. However, addition of a large amount of Cu worsens the hot workability of steel, so its upper limit is made 2.0%.
  • V increases resistance to acids such as sulfuric acid, and particularly when it is added together with W, it also increases resistance to crevice corrosion.
  • acids such as sulfuric acid
  • W sulfuric acid
  • crevice corrosion the amount of ferrite excessively increases, and this leads to a decrease in toughness and corrosion resistance, so its upper limit is made 1.5%.
  • Element Group 2 (B and rare earth elements): Each of these is an element which fixes S or O (oxygen) and increases hot workability.
  • a duplex stainless steel according to the present invention can be in the form of a casting, and it can also be made into a pipe or the like by a powder metallurgy method including forming into a powder, pressing, sintering, and the like.
  • the contents are preferably at most 0.005% for B and at most 0.2% for rare earth elements (primarily La and Ce).
  • the total of the lower limits of B and rare earth elements is preferably at least the sum of S and O as impurities (S + 1 ⁇ 2 O).
  • the number of coarse inclusions which are defined below and particularly coarse alumina inclusions observed in a cross section is limited to at most 10 per mm 2 .
  • coarse inclusions are defined as "inclusions having a major diameter of at least 5 micrometers and containing at least 20% of Al or a total in mass percent of at least 20% of Ca and/or Mg together with Al when Ca and/or Mg is contained in the inclusions.”
  • inclusions including a total in mass percent of at least 20% of Al and Ca and Mg increase deviations of the crystal lattice from that of the parent phase (ferrite phase) and increase the surface energy.
  • such coarse inclusions are referred to as "inclusions containing at least 20 mass % of A1 and having a major diameter of at least 5 micrometers”.
  • Coarse inclusions in a duplex stainless steel according to the present invention are primarily oxide inclusions and particularly alumina inclusions. In the present specification, coarse inclusions will be referred to for convenience as alumina inclusions.
  • the major diameter is less than 5 micrometers, the area of the interface between the parent phase and the inclusions is sufficiently large, so the probability of the interface becoming a site of precipitation of sigma phases becomes small.
  • the major diameter of an inclusion means the length of the longest straight line of the straight lines connecting two different points on the interface between the parent metal and the inclusion 1. These are a1 and a2 in Figures 2(a) and 2(b), respectively.
  • the composition of an oxide type inclusion is determined by finding the content of alloying elements other than O (oxygen) using EDX (energy dispersion x-ray analysis) near the center of the inclusion 1 (b1 and b2 in the examples shown in Figures 2(a) and 2(b), respectively), i.e. near the center of gravity of the cross-sectional shape of the inclusion 1. Accordingly, in this specification, "including at least 20 mass % of Al” means the content of Al(+ Ca + Mg) with respect to all alloying elements other than O.
  • the density of coarse alumina inclusions is limited to at most 10 per mm 2 as described above.
  • Such a duplex stainless steel according to the present invention can be manufactured by carrying out secondary refining by vacuum refining, for example, adjusting the slag basicity at this time to 0.3 - 3.0, for example, and performing adequate stirring of molten steel and refining with slag.
  • inclusions which are formed are primarily alumina inclusions, and when Ca, Mg, and the like are mixed in as impurities, there is the possibility of there being inclusions including Ca and Mg.
  • the reason why the total of (Al + Ca + Mg) for coarse alumina type inclusions, coarse Ca type inclusions, and coarse Mg type inclusions is made at least 20% is in order to guarantee pitting resistance by making it difficult for dissolving out to occur in a corrosive environment.
  • Such Mg and Ca type inclusions are in the form of oxides, and they are combined with alumina type inclusions.
  • the resulting plates were heated to 1250 °C and then rolled to a thickness of 10 mm. A portion of each of the resulting steel plates was cut out, it was mounted in a resin with a cross section perpendicular to the rolled surface facing upwards, and this cross section was polished to a mirror finish. Coarse inclusions were then observed with a SEM at a magnification of 200 times in 5 fields of view, and their size was evaluated.
  • the major diameter of the coarse alumina inclusions was measured in accordance with the definition in Figure 2, the composition of the coarse inclusions near their central portions (b1 and b2 in Figure 2) was analyzed by EPMA, the above-described coarse inclusions were identified, and their density was measured. The density was evaluated based on the average of the number of coarse inclusions per mm 2 in 5 fields of view.
  • the steel plates to be tested were machined to obtain test materials measuring 8 mm thick x 100 mm wide x 200 mm long and having a V-shaped bevel with an internal angle of 30° formed in a long side thereof.
  • a welding rod with an outer diameter of 2 mm prepared from the steel of symbol Al two test materials were abutted against each other, multi-layer welding by TIG welding from one side was carried out using a heat input of 10 kJ/cm (welding condition 1) used for highly corrosion resistance stainless steel which is a higher grade than ordinary stainless steel, or a heat input of 20 kJ/cm (welding condition 2) which does not cause any particular performance problems in welding of ordinary stainless steel to prepare two types of welded joints.
  • a corrosion test piece which measured 3 mm thick, 10 mm wide, and 40 mm long with the 40 mm side extending perpendicular to the welding line and the 3 x 10 mm surface being parallel to the rolled surface was cut from the resulting welded joint, it was immersed for 24 hours in a 10% FeCl 3 • 6H 2 O solution (65 °C), and the occurrence of pitting in the HAZ was evaluated at a magnification of 500.
  • a cross section perpendicular to the welding line and the rolled surface was etched for microscopic examination, image analysis was carried out at a magnification of 500, and the proportion of the area in the HAZ occupied by minute sigma phases was measured. If the proportion of area occupied by sigma phases was 1%, it was determined that there were minute sigma phases.
  • the formation of sigma phases in a weld heat affected zone can be prevented, and the amount of coarse inclusions which are formed can be greatly decreased, so the resulting duplex stainless steel exhibits excellent pitting resistance, and an excellent duplex stainless steel is provided which can be applied to present-day uses.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Heat Treatment Of Steel (AREA)
EP04746980A 2003-06-30 2004-06-29 Duplexedelstahl Withdrawn EP1645650A4 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2003188045 2003-06-30
PCT/JP2004/009511 WO2005001151A1 (ja) 2003-06-30 2004-06-29 二相ステンレス鋼

Publications (2)

Publication Number Publication Date
EP1645650A1 true EP1645650A1 (de) 2006-04-12
EP1645650A4 EP1645650A4 (de) 2007-07-25

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EP04746980A Withdrawn EP1645650A4 (de) 2003-06-30 2004-06-29 Duplexedelstahl

Country Status (9)

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US (1) US20060191605A1 (de)
EP (1) EP1645650A4 (de)
JP (1) JP4265605B2 (de)
KR (1) KR100704201B1 (de)
CN (1) CN100497704C (de)
AU (1) AU2004252373B2 (de)
BR (1) BRPI0412092A (de)
NO (1) NO20056009L (de)
WO (1) WO2005001151A1 (de)

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CN102296249A (zh) * 2011-08-29 2011-12-28 江苏九胜特钢制品有限公司 以钨代钼的双相不锈钢合金材料及其制备方法
CN102296248A (zh) * 2011-08-29 2011-12-28 江苏九胜特钢制品有限公司 一种双相钨不锈钢合金材料及其制备方法
EP2500444A4 (de) * 2009-11-13 2017-10-25 Nippon Steel & Sumitomo Metal Corporation Duplex-edelstahl mit hervorragender alkalibeständigkeit
EP3211107A4 (de) * 2014-10-24 2018-05-09 Nippon Steel & Sumitomo Metal Corporation Zweiphasiger edelstahl und herstellungsverfahren dafür

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CN103602915B (zh) * 2013-11-22 2015-11-18 山东建筑大学 高碳高铬双相不锈钢
CN108048755B (zh) * 2017-11-10 2019-06-28 洛阳双瑞特种装备有限公司 一种用于流体输送的高硬度耐蚀铸造不锈钢
CN110016625B (zh) * 2019-05-15 2021-08-03 丹阳市华龙特钢有限公司 高纯净耐腐蚀合金材料
WO2022085262A1 (ja) 2020-10-23 2022-04-28 日本製鉄株式会社 二相ステンレス鋼溶接継手
CN113337779A (zh) * 2021-05-21 2021-09-03 烟台恒邦合金材料有限公司 一种耐磨耐腐蚀泵用不锈钢材料及其制备方法

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EP2500444A4 (de) * 2009-11-13 2017-10-25 Nippon Steel & Sumitomo Metal Corporation Duplex-edelstahl mit hervorragender alkalibeständigkeit
CN102296249A (zh) * 2011-08-29 2011-12-28 江苏九胜特钢制品有限公司 以钨代钼的双相不锈钢合金材料及其制备方法
CN102296248A (zh) * 2011-08-29 2011-12-28 江苏九胜特钢制品有限公司 一种双相钨不锈钢合金材料及其制备方法
CN102296248B (zh) * 2011-08-29 2013-04-24 江苏九胜特钢制品有限公司 一种双相钨不锈钢合金材料及其制备方法
EP3211107A4 (de) * 2014-10-24 2018-05-09 Nippon Steel & Sumitomo Metal Corporation Zweiphasiger edelstahl und herstellungsverfahren dafür

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JPWO2005001151A1 (ja) 2006-08-10
AU2004252373B2 (en) 2007-02-22
US20060191605A1 (en) 2006-08-31
CN100497704C (zh) 2009-06-10
KR100704201B1 (ko) 2007-04-09
JP4265605B2 (ja) 2009-05-20
BRPI0412092A (pt) 2006-09-05
AU2004252373A1 (en) 2005-01-06
KR20060026898A (ko) 2006-03-24
CN1816640A (zh) 2006-08-09
WO2005001151A1 (ja) 2005-01-06
NO20056009L (no) 2006-01-11

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