CN103069031A - 具有改善的可机加工性的奥氏体-铁素体不锈钢 - Google Patents
具有改善的可机加工性的奥氏体-铁素体不锈钢 Download PDFInfo
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- CN103069031A CN103069031A CN2011800337876A CN201180033787A CN103069031A CN 103069031 A CN103069031 A CN 103069031A CN 2011800337876 A CN2011800337876 A CN 2011800337876A CN 201180033787 A CN201180033787 A CN 201180033787A CN 103069031 A CN103069031 A CN 103069031A
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- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 238000010273 cold forging Methods 0.000 description 1
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- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
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Classifications
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- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
- C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
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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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/02—Rolling special iron alloys, e.g. stainless steel
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
- B21C1/003—Drawing materials of special alloys so far as the composition of the alloy requires or permits special drawing methods or sequences
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- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
- B21J1/02—Preliminary treatment of metal stock without particular shaping, e.g. salvaging segregated zones, forging or pressing in the rough
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- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
- B22D11/002—Stainless steels
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
- C21D1/60—Aqueous agents
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
- C21D1/613—Gases; Liquefied or solidified normally gaseous material
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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
- 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
- C21D8/0221—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
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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
- C21D8/0263—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
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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
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
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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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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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
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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Abstract
本发明涉及奥氏体-铁素体不锈钢组合物,其组成以重量%计包含的:0.01%≤C≤0.10%;20.0%≤Cr≤24.0%;1.0%≤Ni≤3.0%;0.12%≤N≤0.20%;0.5%≤Mn≤2.0%;1.6%≤Cu≤3.0%;0.05%≤Mo≤1.0%;W≤0.15%;0.05%≤Mo+W/2≤1.0%;0.2%≤Si≤1.5%;Al≤0.05%;V≤0.5%;Nb≤0.5%;Ti≤0.5%;B≤0.003%;Co≤0.5%;REM≤0.1%;Ca≤0.03%;Mg≤0.1%;Se≤0.005%;O≤0.01%;S≤0.030%;P≤0.040%;余量为铁和由生产所致的杂质,并且显微组织由奥氏体和35-65体积%的铁素体组成,该组成还遵守下面的关系式:40≤IF≤65,其中IF=10%Cr+5.1%Mo+1.4%Mn+24.3%Si+35%Nb+71.5%Ti-595.4%C-245.1%N-9.3%Ni-3.3%Cu-99.8,和IRCGCU≥32.0,其中IRCGCU=%Cr+3.3%Mo+2%Cu+16%N+2.6%Ni-0.7%Mn,和0≤IU≤6.0,其中IU=3%Ni+%Cu+%Mn-100%C-25%N-2(%Cr+%Si)-6%Mo+45,以及涉及制造以该钢的板材、带材、卷材、棒材、线材、型材、锻造部件和铸造部件的方法。
Description
本发明涉及奥氏体-铁素体不锈钢,更特别地,涉及旨在制造用于材料生产(化学、石油化学、纸、近海)或能源生产的设备的结构元件的奥氏体-铁素体不锈钢,而不局限于此。
更一般地,在许多应用中可以使用该钢代替4301类型的不锈钢,例如在前述的工业中或在食品和农业中,包括从成型线材(焊接网)、型材(滤器)、钢轴等制成的部件。也可以制备铸造部件和锻造部件。
为此而知道1.4301和1.4307类型的不锈钢种,其在退火状态下的显微组织基本上是奥氏体;在冷锻状态下,它们还可以包含可变比例的加工硬化的马氏体。然而,这些钢包含高的镍添加,其花费通常是非常昂贵的。而且,对于某些应用,这些该钢种从技术观点来看可存在问题,因为它们在退火状态下具有差的拉伸特性,特别在于涉及屈服强度,和低的抗应力腐蚀性。最后,这些奥氏体钢种具有高的热传导系数,这意味着当使用它们作为混凝土结构的钢筋时,它们妨碍良好的热绝缘。
最近,出现了称为1.4162的低合金的奥氏体-铁素体钢种,其包含低的镍含量(少于3%),不包含钼,但包含高的氮含量以补偿这些该钢种的低的镍水平,同时保留所需的奥氏体含量。为了能够添加可高于0.200%的氮含量,需要添加高的锰含量。然而,在这样的氮水平下,观察到在连铸的初轧钢坯中纵向凹陷的形成,其进而在轧制的棒材上产生在某些情况下可成为麻烦的表面缺陷。因此,此类钢种的制造由于该差的可铸性而变得特别棘手。而且,这些钢种具有差的可机加工性。
还知道称为铁素体或铁素体-马氏体的不锈钢种,就热处理所定义的范围而言,其显微组织由铁素体和马氏体组成,例如标准EN10088的1.4017钢种。这些具有通常低于20%的铬含量的钢种,具有强的机械拉伸特性,但是不具有令人满意的抗腐蚀性。
本发明的目的是通过提供具有下列特性而不添加过量的昂贵合金元素例如镍和钼的不锈钢,来克服现有技术的钢和制造方法的缺点:
-良好的可铸性,
-良好的机械性质和特别是在退火或固溶状态下高于400甚至高于450MPa的屈服强度极限,以及在大厚度的板材和棒材上的良好冲击强度,优选地在20℃下高于100J和在-46℃下高于20J,
-高的抗全面腐蚀性,和
-良好的可机加工性。
为此,本发明的首要目的在于奥氏体-铁素体不锈钢,其组成以重量%计包含:
0.01%≤C≤0.10%
20.0%≤Cr≤24.0%
1.0%≤Ni≤3.0%
0.12%≤N≤0.20%
0.5%≤Mn≤2.0%
1.6%≤Cu≤3.0%
0.05%≤Mo≤1.0%
W≤0.15%
0.05%≤Mo+W/2≤1.0%
0.2%≤Si≤1.5%
Al≤0.05%
V≤0.5%
Nb≤0.5%
Ti≤0.5%
B≤0.003%
Co≤0.5%
REM≤0.1%
Ca≤0.03%
Ng≤0.1%
Se≤0.005%
O≤0.01%
S≤0.030%
P≤0.040%
余量为铁和由生产所致的杂质,并且显微组织由奥氏体和35-65体积%的铁素体,优选地35-55体积%的铁素体构成,该组成还遵守下面的关系式:
40≤IF≤65,优选地45≤IF≤55
其中IF=10%Cr+5.1%Mo+1.4%Mn+24.3%Si+35%Nb+71.5%Ti-595.4%C-245.1%N-9.3%Ni-3.3%Cu-99.8
和IRCGCU≥32.0,优选地≥34.0
其中IRCGCU=%Cr+3.3%Mo+2%Cu+16%N+2.6%Ni-0.7%Mn
和0≤IU≤6.0
其中IU=3%Ni+%Cu+%Mn-100%C-25%N-2(%Cr+%Si)-6%Mo+45。
在优选的实施方案中,单独地或组合地,根据本发明的钢具有:
-0.12-0.18重量%的氮含量,
-2.0-2.8重量%的铜含量,
-低于0.5重量%的钼含量,
-低于0.05重量%的碳含量。
本发明的第二个目的在于制造根据本发明的钢的板材、带材或热轧卷材的方法,其中:
-提供具有根据本发明的组成的钢锭或钢板坯,
-在1150-1280℃的温度下,热轧所述钢锭或所述板坯以获得板材、带材或卷材。
在一个特别的实施方案中,制造根据本发明的钢的热轧板材的方法包括在于如下的步骤:
-在1150-1280℃的温度下热轧所述钢锭或所述板坯以获得所谓四辊式(quarto)的板材,然后
-在900-1100℃的温度下进行热处理,和
-通过在空气中淬火使所述板材冷却。
在另一个特别的实施方案中,制造根据本发明的钢的热轧棒材或线材的方法包括在于如下的步骤:
-提供具有根据本发明的组成的连铸钢锭或板坯,
-在1150-1280℃的温度下热轧所述钢锭或所述板坯以获得棒材或线材,使该棒材在空气中冷却,使线材在水中冷却,
-然后,任选地:
-在900-1100℃的温度下进行热处理,和
-通过淬火使所述棒材或所述卷材冷却。
在特别的实施方案中,根据本发明的方法还单独地或组合地包括下列特点:
-在冷却结束时将所述棒材进行冷拉制或将所述线材进行拉丝,
-对根据本发明获得的热轧棒材进行冷成型,
-将根据本发明获得的热轧棒材切割成坯料,然后在1100℃-1280℃下进行所述坯料的锻造。
在阅读仅作为实施例给出的随后描述时,本发明的其他特征和优点将会变得明了。
根据本发明的双相不锈钢包含上面所定义的内容。
该钢种的碳含量为0.01-0.10重量%,和优选地低于0.05重量%。这是因为,该元素的过高含量通过增加焊缝热影响区中碳化铬析出的风险而降低抗局部腐蚀性。
该钢种的铬含量为20.0-24.0重量%,且优选为21.5-24重量%,以便获得良好的抗腐蚀性,其至少与用304或304L类型的该钢种获得的抗腐蚀性相等。
该钢种的镍含量为1.0-3.0重量%,并且优选低于或等于2.8重量%。添加该奥氏体形成元素以便获得良好的抗腐蚀瑕疵形成的特性。添加它还有助于获得在冲击强度和延展性之间的良好折衷。这是因为它具有使冲击强度过渡曲线朝向低温平移的好处,这对于冲击强度性能对其而言为重要的大棒材或厚的四辊式板材的制造是特别有利的。由于其高的价格,将其含量限制于3.0%。
由于在根据本发明的钢中限制了镍含量,已经发现,为了在900℃-1100℃的热处理后获得合适的奥氏体含量,可建议添加非常大量的其他奥氏体形成元素并限制铁素体形成元素的含量。
因此,该钢种的氮含量为0.12-0.20%,且优选为0.12-0.18%,这通常意味着在生产过程中在钢中添加氮。该奥氏体形成元素首先参与铁素体/奥氏体双相钢的获得,其包含适合于在应力下良好的抗腐蚀性的奥氏体比例,也参与高的机械性质的获得。它还使得能够限制焊接区的热影响区中铁素体的形成,这避免了这些区脆化的风险。限制其最大含量,这是因为超过0.16%的氮时,在连铸的初轧钢坯上就开始出现缺陷。这些缺陷由纵向凹陷组成,其进而在轧制棒材上产生表面缺陷,所述缺陷可能在某些情形中成为麻烦。超过0.18%时,则纵向凹陷非常明显并且还观察到与超过氮的最大量有关的气泡,其可以在该钢种的结构中保持在熔体中。
该钢种的锰含量为0.5-2.0重量%,优选为0.5-1.9重量%且更加优选为0.5-1.8重量%。这是奥氏体形成元素,但是仅低于1150℃。在更高的温度下,它在冷却时使奥氏体的形成延迟,导致在焊缝的热影响区中过量铁素体的形成,使它们的冲击强度非常低。另一方面,如果锰在该钢种中以高于2.0%的量存在,那么在该钢种的生产和精炼过程中就引起问题,因为它侵蚀用于盛钢桶的某些耐火材料,因而需要更频繁地更换这些昂贵的元素并因此更频繁地中断该工艺。通常用于组成该钢种的锰铁的添加还包含大量磷以及硒,不希望将其引入钢中,并且其在该钢种的精炼过程中是难以去除的。另一方面,锰通过限制脱碳的可能性而干扰该精炼。它还在该方法的更下游引起问题,这是因为它由于硫化锰MnS和氧化的夹杂物的形成损坏该钢种的抗腐蚀性。优选地将其限制在少于1.9重量%,甚至少于1.8重量%和更加优选地少于1.6重量%,因为试验显示当降低其含量时,可锻性(和更一般地,热变形能力)得到改善。特别地,当含量高于2.0%时,观察到裂纹的形成,使得该钢种不适合于热轧。
奥氏体形成元素铜以1.6-3.0重量%,优选2.0-2.8重量%,甚至2.2-2.8重量%的含量存在。它参与所希望的奥氏体-铁素体双相组织的获得,从而使得能够获得更好的抗全面腐蚀性,而不被迫过高地提高该钢种的氮水平。另一方面,固溶体中的铜改善了在还原性酸环境中的抗腐蚀性。低于1.6%时,为具有所希望的双相组织所需的氮水平开始变得非常大以抑制如上面所描述的连铸的初轧钢坯的表面质量问题。高于3.0%时,开始铜偏析和/或析出的风险,其可以在高于200℃下的延长使用(超过一年)中引起抗局部腐蚀性的下降和冲击强度的下降。
铁素体形成元素钼,是以0.05-1.0重量%,甚至0.05-0.5重量%的含量存在于该钢种中的元素,而钨是任选的元素,其可以以低于0.15重量%的含量添加。然而,由于花费的原因,优选不添加钨,因而将其含量限制在残留0.05重量%。
另一方面,这两种元素的含量是这样的:总和Mo+W/2低于1.0重量%,优选低于0.5重量%,甚至低于0.4重量%,且特别优选地,低于0.3重量%。这是因为,本发明人已发现,通过保持这两种元素以及其总和低于所示值,观察不到任何脆性的金属间析出物,这使得能够特别是通过允许热处理后板材和带材在空气中冷却,使板材或带材的制造方法去束缚。而且,已观察到通过将这些元素控制在要求保护的界限内,改善了该钢种的焊接能力。
铁素体形成元素硅以0.2-1.5重量%,优选低于1.0重量%的含量存在。添加其以确保在生产过程中钢浴的良好去氧化,但是因为在热轧后差质量淬火的情况下∑相形成的风险,其含量受限。
铁素体形成元素铝是任选的元素,其可以以低于0.05重量%和优选地0.005重量%-0.040重量%的含量向该钢种添加,以便获得具有低熔点的铝酸钙夹杂物。限制其最大含量以便避免氮化铝的过度形成。
铁素体形成元素钒是任选的元素,其可以以0.02-0.5重量%且优选地低于0.2重量%的量存在于该钢种中,以便改善钢的抗点蚀腐蚀性。它还可以作为在铬的添加过程中带来的残留元素而存在。
铁素体形成元素铌是任选的元素,其可以以0.001重量%至0.5重量%的量存在于该钢种中。它允许改善该钢种的拉伸强度和通过更好的切屑破裂改善其可机加工性,这得益于细小的NbN类型的氮化铌或NbCrN类型的铌和铬的氮化物(Z相)的形成。限制其含量以限制粗大的镍氮化物的形成。
铁素体形成元素钛是任选的元素,其可以以0.001-0.5重量%的量且优选以0.001-0.3重量%的量存在于该钢种中。它使得改善该钢种的机械强度和通过更好的切屑破裂改善其可机加工性,这得益于细小的钽氮化物的形成。限制其含量以便避免特别是在熔融钢中形成的钛氮化物簇的形成。
硼是任选的元素,其可以以0.0001重量%至0.003重量%的量存在于根据本发明的钢种中,以便改善其热变形性。
奥氏体形成元素钴是任选的元素,其可以以0.02至0.5重量%的量存在于该钢种中。该元素是由原材料带来的残留元素。主要因为维护问题而限制其,可能在核设备中的部件辐射后引起该维护问题。
稀土元素(由REM表示)是任选的元素,其可以以0.1重量%的水平存在于该钢种中。特别将提及铈和镧。限制这些元素的含量,因为它们能够形成不希望的金属间化合物。
在根据本发明的该钢种中还可找到钙,其可为0.0001至0.03重量%,和优选地高于0.0005重量%的量,以便控制氧化物夹杂物的性质和改善可机加工性。限制该元素的含量,因为它易于与硫组合以形成劣化抗腐蚀性的钙硫化物。
可以进行以0.1%的最终含量的量的镁添加以改变硫化物和氧化物的性质。
由于其对于抗腐蚀性的有害影响,优选地将硒保持在少于0.005重量%。该元素通常以锰铁锭的杂质的形式被带入该钢种中。
优选地,将氧含量限制于0.01重量%以便改善其锻造能力和其焊缝的冲击强度。
将硫保持在低于0.030重量%的含量,且优选低于0.003重量%的含量。如在前面已看见的,该元素与锰或钙形成硫化物,其存在对抗腐蚀性是有害的。它被认为是杂质。
将磷保持在低于0.040重量%的含量并认为其是杂质。
组合物的余量由铁和杂质组成。除了上面已经提到的这些,特别还将提及锆、锡、砷、铅或铋。锡可以以低于0.100重量%且优选低于0.030重量%的含量而存在,以避免焊接的问题。砷可以以低于0.030重量%且优选低于0.020重量%的含量存在。铅可以以低于0.002重量%且优选低于0.0010重量%的含量存在。铋可以以低于0.0002重量%且优选低于0.00005重量%的含量存在。锆可以以0.02%的数量存在。
在退火状态下,根据本发明的钢的显微组织由奥氏体和铁素体组成,其优选地是在1050℃下1小时的处理后,以35-65体积%的铁素体和更特别地,45-55体积%的铁素体的比例。
本发明人还已发现下式合适地考量1050℃下铁素体的含量:
IF=10%Cr+5.1%Mo+1.4%Mn+24.3%Si+35%Nb+71.5%Ti-595.4%C-245.1%N-9.3%Ni-3.3%Cu-99.8
因此,为了获得在1050℃下35-65%的铁素体比例,指数IF应当为40-65。
在退火状态下,显微组织不包含对其机械性质有害的其他相,例如∑相和其他金属间相。在冷加工状态下,一部分奥氏体可能已根据有效变形温度和所施加的冷变形的量而转变成马氏体。
另一方面,本发明人已发现,当铬、钼、铜、氮、镍和锰的重量百分比遵守下面的关系式时,所涉及的该钢种具有良好的抗全面腐蚀性:
IRCGU≥32.0,且优选地≥34.0
而IRCGU=%Cr+3.3%Mo+2%Cu+16%N+2.6%Ni-0.7%Mn
最后,本发明人已确定,当镍、铜、锰、碳、氮、铬、硅和钼的重量百分比遵守下面的关系式时,所涉及的该钢种具有良好的可机加工性:
0≤IU≤6.0
而IU=3%Ni+%Cu+%Mn-100%C-25%N-2(%Cr+%Si)-6%Mo+45。
通常,可以以热轧板材(也称为四辊式板材)的形式,也可以以热轧带材的形式,从板坯或钢锭开始,也可以以冷轧带材的形式从热轧带材开始,来生产和制造根据本发明的钢。也可以将它热轧成棒材或线坯或型材或锻件;这些产品可以随后通过锻造而热变形或冷加工为拉制的棒材或型材或拉制的线材。根据本发明的钢还可以通过模制随后进行热处理或没有热处理来制造。
为了获得可能的最好性能,优选地将使用根据本发明的方法,其包含首先提供具有符合本发明的组成的钢锭、板坯或初轧钢坯。
该钢锭、板坯或初轧钢坯通常通过在电炉中熔炼原材料,接着与脱碳一起进行AOD或VOD类型真空重熔来获得。随后可以以钢锭的形式,或通过在无底锭模中连铸以板坯或初轧钢坯的形式来浇铸该钢种。还可以考虑直接以薄板坯的形式,特别是通过在对转的辊之间的连铸来浇铸该钢种。
在提供钢锭或板坯或初轧钢坯后,任选地进行再加热以达到1150-1280℃的温度,但是也可以伴随着浇铸热,在从连铸而来的板坯上直接加工。
在制造板材的情况下,随后热轧该板坯或钢锭以获得通常具有5-100mm的厚度的所谓四辊式板材。在该阶段下通常使用的压下率在3和30%之间变化。随后通过在900-1100℃温度下再加热然后冷却而使该板材经历使在该阶段所形成的析出物恢复成溶体的热处理。
根据本发明的方法要求通过在空气中淬火的冷却,其比用于该钢种类型的通常冷却更容易完成,通常冷却是借助于水的更快冷却。然而,仍可进行在水中的冷却,如果希望这样的话。
在空气中的这种慢冷却特别因为根据本发明的组成而受限的镍和钼含量而成为可能,其不易遭受对于其使用特性有害的金属间相的析出。该冷却可以特别地以0.1-2.7℃/秒的速度来进行。
在热轧结束后,可以对该四辊式板材进行矫直、切头和酸洗,如果希望以这样的状态交付它的话。
还可以在热带材轧机上以3-10mm的厚度轧制该裸钢。
在从钢锭或初轧钢坯制造长产品的情况下,可以在1150-1280℃的温度下,在多架轧钢机上在带槽轧辊中以一次或多次加热进行热轧,以获得棒材或轧制的线材或线坯圈。起始初轧钢坯和最终产品之间的横截面比优选地大于3,以便确保轧制产品的内部健全性。
在已制造了棒材时,通过在空气下的简单展开使其在轧制结束时冷却。
在已制造了轧制线材时,可以通过如下方式使其冷却:通过在离开轧钢机时在水槽中以卷材形式进行淬火,或者通过在传送带上经过850℃-1100℃温度下的固溶炉后,以传送带上按匝展开的形式在水中进行淬火。
可选地,可以在900℃-1100℃在炉中对这些已经在轧制热下处理的棒材或卷材进行进一步的热处理,如果希望完成组织的再结晶和轻微降低拉伸机械性质。
在这些棒材或这些线卷的冷却结束时,可以根据产品的最终用途进行不同的热成形或冷成形处理。因此,在冷却结束时将可以进行棒材的冷拉制或线材的拉制。
还可以将热轧的棒材进行冷成型,或在已将棒材切成坯料和已经锻造它们之后制造部件。
实施例
生产了不同的熔体然后转变成具有不同直径和特征的棒材。
机械性质
根据标准NFEN 10002-1测定了拉伸性质Rp0.2和Rm。依照标准NF EN 10045在不同温度下测定了冲击强度KV。
车削试验
在配备有Kistler测力板、以最大5800rpm运转的28kW的车床RAMO RTN30上进行这些试验。所有试验在干燥下进行。所使用的参考尖端为尖端STELLRAMSP0819 CNMG120408E-4E,认为其对于Duplex不锈钢而言是最佳的。
这些试验使得能够测定该钢种的可机加工性水平的两个特征值:
-表达为m/分钟的车削速度VB15/0.15(VB15/0.15越高,可机加工性越好),
-切屑破碎区ZFC(ZFC越大,可机加工性越好)。
1.VB15/0.15的测定
该测试在于找到对于15分钟的有效机加工产生0.15m侧面磨损的车削速度。在具有涂覆碳化物的尖端的常规车削道次中进行该试验。设置的参数为:
-走刀深度ap=1.5mm
-进刀量f=0.25mm/车削
在这些试验的过程中,通过在×32放大倍数下与照相机连接的光学系统来测量侧面磨损。该测量是磨损区表面与该区的表观长度的比例。在获得0.15mm的侧面磨损前在出现大于0.45mm(是VB值的3倍)的凹槽或发生尖端失效时,认为不可找到VB15/0.15值;在这种情况下,将测定最大速度,对于该最大速度而言既没有0.45mm的侧面磨损,也没有15分钟的尖端失效,并且将指示作为VB15/0.15大于该值的结果。
在本发明的范围内,认为在上面所描述的条件下测量的小于220m/分钟的VB15/0.15值不符合本发明。
2.ZFC的测定
在测定ZFC值之前,需要定义最小切割速度Vcmin。
2.1)Vcmin的评价
Vcmin的测定通过具有以递增速度的车削走刀来进行。以非常低的切割速度Vc(40m/分钟)起动,并且在走刀过程中以规律的方式升高至大于VB15/0.15的速度。力Kc的记录使得能够直接描画曲线Kc=f(Vc)。
切割条件为:
-走刀深度ap=1.5mm
-进刀量f=0.25mm/rev
-在VB15/0.15的条件下由一次车削磨损工具
所获得的曲线在大多数情况下为单调递减函数。Vcmin的值为对应于曲线的拐折。
2.2)ZFC的评价
在与Vcmin的120%相等的速度下,通过改变切割条件来在恒定速度下进行6秒的机加工。如此扫描进刀量表(tableau d′avances)(从0.1mm/rev至0.4mm/rev,每0.05mm/rev的步长)和走刀深度(从0.5mm至4mm,每0.5mm的步长)。
对于56个f-ap组合的每一个,评价获得的切屑,将这些切屑与在“C.O.M.车削”标准ISO 3685中预先定义的切屑形式进行比较。ZFC是合并以f和ap的条件的表区,对于它们,切屑是良好破碎的,通过计数令人满意的组合的数目来量化它。
在本发明的范围内,认为在上面所描述的条件下测量的小于15的ZFC值不符合本发明。
腐蚀性试验
测定了在23℃下,在2摩尔/升的硫酸介质中以μA/cm2表达的临界溶解或活性电流。首先进行随机电势(potent iel d′abandon)测量900秒;随后,以10mV/分钟的速度从-750mV/ECS开始直至+1V/ECS描画出动电势曲线。在如此获得的极化曲线上,临界电流对应于在钝态区之前揭示的最大峰电流。
下面的表总结了所测试的组成和对于所获得的产品的结果与表征。
表1:试验的化学组成
首先发现比较钢种6-8和12显示出在连铸的初轧钢坯上的纵向凹陷的形成,而根据本发明的钢种1至5则没有它们,由此证明了根据本发明的该钢种的良好可铸性。
而且,根据本发明的试验的屈服强度极限明显大于450MPa,与对于例如比较钢种9所观察的不同。
如在-46℃下那样,在20℃下,在大厚度的板材和棒材上的冲击强度值也是同样令人满意的,并且特别地优于例如比较钢种6和7的冲击强度。
就切割速度和切屑破碎区而言,根据本发明的钢种还都呈现出良好的可机加工性。相反,发现比较钢种6和7以及11和12(其IU指数为负的)不呈现出令人满意的切割速度,而比较该钢种10(其IU指数大于6.0)具有不足的切屑破碎区。
根据本发明的钢种的抗全面腐蚀性是非常令人满意的,并且特别地优于比较钢种8的抗全面腐蚀性。
因此发现仅根据本发明的钢种是结合全部所寻求的性能的钢种,即良好的可铸性;在退火状态或固溶下大于400甚至大于450MPa的屈服强度极限;在大厚度的板材和棒材上的良好冲击强度,优选地在20℃下大于100J和在-46℃下大于20J;高的抗全面腐蚀性和良好的可机加工性。
Claims (14)
1.奥氏体-铁素体不锈钢,其组成以重量%计包含:
0.01%≤C≤0.10%
20.0%≤Cr≤24.0%
1.0%≤Ni≤3.0%
0.12%≤N≤0.20%
0.5%≤Mn≤2.0%
1.6%≤Cu≤3.0%
0.05%≤Mo≤1.0%
W≤0.15%
0.05%≤Mo+W/2≤1.0%
0.2%≤Si≤1.5%
Al≤0.05%
V≤0.5%
Nb≤0.5%
Ti≤0.5%
B≤0.003%
Co≤0.5%
REM≤0.1%
Ca≤0.03%
Mg≤0.1%
Se≤0.005%
O≤0.01%
S≤0.030%
P≤0.040%
余量为铁和由生产所致的杂质,并且显微组织由奥氏体和35-65体积%的铁素体组成,该组成还遵守下面的关系式:
40≤IF≤65
而IF=10%Cr+5.1%Mo+1.4%Mn+24.3%Si+35%Nb+71.5%Ti-595.4%C-245.1%N-9.3%Ni-3.3%Cu-99.8
和IRCGCU≥32.0
而IRCGCU=%Cr+3.3%Mo+2%Cu+16%N+2.6%Ni-0.7%Mn
和O≤IU≤6.0
而IU=3%Ni+%Cu+%Mn-100%C-25%N-2(%Cr+%Si)-6%Mo+45。
2.根据权利要求1的钢,其特征还在于,
IRCGU≥34。
3.根据权利要求1或2的钢,其特征还在于,铁素体的比例为35-55体积%。
4.根据权利要求1至3中任一项的钢,其特征还在于,
45≤IF≤55。
5.根据权利要求1至4中任一项的钢,其特征还在于,氮含量为0.12-0.18重量%。
6.根据权利要求1至5中任一项的钢,其特征还在于,铜含量为2.0-2.8重量%。
7.根据权利要求1至6中任一项的钢,其特征还在于,钼含量低于0.5重量%。
8.根据权利要求1至7中任一项的钢,其特征还在于,碳含量低于0.05重量%。
9.制造根据权利要求1至8中任一项的钢的热轧板材、带材或卷材的方法,根据其:
-提供具有根据权利要求1至8中任一项的组成的钢锭或钢板坯,
-在1150-1280℃的温度下热轧所述钢锭或钢板坯以获得板材、带材或卷材。
10.制造根据权利要求9的钢的热轧板材的方法,其中:
-在1150-1280℃的温度下热轧所述钢锭或钢板坯以获得所谓的四辊式板材,然后
-在900至1100℃的温度下进行热处理,和
-通过在空气中淬火使所述板材冷却。
11.制造根据权利要求1至8中任一项的钢的热轧棒材或线材的方法,其中:
-提供具有根据权利要求1至8中任一项的组成的连铸钢锭或初轧钢坯,
-在1150-1280℃的温度下热轧所述钢锭或所述初轧钢坯以获得棒材或线材,使棒材在空气中冷却,而使线材在水中冷却,
然后,任选地:
-在900-1100℃的温度下进行热处理,和
-通过淬火使所述棒材或所述卷材冷却。
12.根据权利要求11的制造方法,其中在冷却结束时将所述棒材进行冷拉制或将所述线材进行拉丝。
13.钢型材的制造方法,其中将通过根据权利要求11的方法获得的热轧棒材进行冷成型。
14.锻造钢部件的制造方法,其中将通过根据权利要求11的方法获得的热轧棒材切割成坯料,然后在1100℃-1280℃进行所述坯料的锻造。
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TWI512115B (zh) * | 2014-11-05 | 2015-12-11 | China Steel Corp | 沃斯田鐵系合金鋼材之製造方法 |
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CN105506510A (zh) * | 2015-12-03 | 2016-04-20 | 浙江腾龙精线有限公司 | 一种不锈钢丝的生产工艺 |
TWI606120B (zh) * | 2016-08-24 | 2017-11-21 | 中國鋼鐵股份有限公司 | 沃斯田鐵系合金鋼材之表面處理方法 |
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CN111057963A (zh) * | 2018-10-17 | 2020-04-24 | 山特维克材料技术公司 | 生产双相不锈钢管的方法 |
CN115430996A (zh) * | 2022-09-20 | 2022-12-06 | 苏州雷格姆海洋石油设备科技有限公司 | 海上fpso关键零部件大型锻造双相不锈钢特殊管件制备方法 |
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WO2012004464A1 (fr) | 2012-01-12 |
EP2591134A1 (fr) | 2013-05-15 |
BR112013000264B1 (pt) | 2018-04-24 |
US20170121789A1 (en) | 2017-05-04 |
SI2591134T1 (sl) | 2015-05-29 |
AU2011275610A1 (en) | 2013-01-24 |
ES2534930T3 (es) | 2015-04-30 |
DK2591134T3 (en) | 2015-04-20 |
CN106119737A (zh) | 2016-11-16 |
WO2012004473A1 (fr) | 2012-01-12 |
CA2804320A1 (en) | 2012-01-12 |
US9587286B2 (en) | 2017-03-07 |
JP5972870B2 (ja) | 2016-08-17 |
BR112013000264A2 (pt) | 2016-05-24 |
US9797025B2 (en) | 2017-10-24 |
JP2013535567A (ja) | 2013-09-12 |
AU2011275610B2 (en) | 2014-06-05 |
KR20130034044A (ko) | 2013-04-04 |
EP2591134B1 (fr) | 2015-01-21 |
CA2804320C (en) | 2015-04-28 |
US20130174948A1 (en) | 2013-07-11 |
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