WO2014181385A1 - 耐粒界腐食特性に優れたNi合金クラッド鋼およびその製造方法 - Google Patents
耐粒界腐食特性に優れたNi合金クラッド鋼およびその製造方法 Download PDFInfo
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- 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
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- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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- 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
- B21B1/22—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 for rolling plates, strips, bands or sheets of indefinite length
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- B21B1/38—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 for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack rolling
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- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/013—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium
- B32B15/015—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium the said other metal being copper or nickel or an alloy thereof
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- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
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- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/057—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being less 10%
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- 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
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- 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
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- 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
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- 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
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- 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
- C21D2251/00—Treating composite or clad material
- C21D2251/02—Clad material
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- 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
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- C—CHEMISTRY; METALLURGY
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- 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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
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- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
Definitions
- the present invention relates to a nickel alloy clad steel (nickel-base alloy-clad steel plate) having excellent intergranular corrosion resistance and a method for producing the same.
- High alloy clad steel is a steel material in which two alloys with different properties are bonded together with Ni alloy as the material and low-alloy steel as the base material. Clad steel is obtained by metallographically bonding dissimilar metals, and unlike plating, there is no fear of peeling, and it can have new characteristics that cannot be achieved by a single metal and alloy.
- the clad steel can exhibit the same function as a solid material by selecting a laminated material having a function suitable for the purpose of each use environment. Furthermore, carbon steel and low alloy steel suitable for severe environments such as high toughness and high strength other than corrosion resistance can be applied to the base material of the clad steel.
- clad steel uses less alloying elements than solid wood, can ensure the same rust prevention performance as solid wood, and can ensure the same strength and toughness as carbon steel and low alloy steel. Therefore, there is an advantage that both economy and functionality can be achieved.
- Patent Documents 1 and 2 disclose a manufacturing method that simultaneously achieves corrosion resistance, strength of a base material, and low-temperature toughness without solution treatment.
- Patent Document 3 and Patent Document 4 disclose a method of defining the chemical composition of the clad material and regulating the rolling and cooling conditions to ensure the corrosion resistance of the clad material and the toughness of the base material.
- the present invention adjusts the precipitation state of precipitates in the Ni alloy, limits the amount of Cr existing as precipitates, and adjusts the precipitation amount of carbides to improve the intergranular corrosion resistance.
- An object of the present invention is to improve the intergranular corrosion resistance by adjusting the aspect ratio of the crystal grains of the laminated material that becomes the carbide precipitation sites to finely disperse the carbides on the grain boundaries.
- the clad steel has a problem because it is a composite material. Corrosion resistance of stainless steel and other corrosion resistant materials deteriorates when precipitation of intermetallic compounds, carbides, nitrides, and the like occurs. Therefore, in the case of a solid material, a solution treatment is usually performed after rolling to solidify the precipitate. However, in the case of clad steel, if it is heated and held at such a high temperature that precipitates dissolve, there is a problem that the crystal grains of the low alloy steel as a base material become coarse and the mechanical properties are remarkably deteriorated.
- the inventors have found that when the clad steel is heated and held at such a high temperature that the precipitate is dissolved, the crystal grains of the low-alloy steel of the base material become coarse and the mechanical properties are significantly deteriorated.
- the laminated material of Ni alloy clad steel sheets attention was paid to the fact that precipitates cause deterioration of corrosion resistance, and the relationship between Ni alloy precipitates and corrosion resistance was examined. As a result, it was found that precipitation of intermetallic compounds rarely occurred in the production of Ni alloy clad steel, and the deterioration of corrosion resistance was caused by precipitation of carbides.
- the gist of the present invention is as follows.
- a Ni alloy clad steel excellent in intergranular corrosion resistance characterized in that the Cr content existing as a carbide in the laminated material made of Ni alloy is 0.03% or less by mass%.
- the rolling ratio at 1000 ° C. or more is set to 2 or more and control in a temperature range of 950 ° C. or less.
- Ni alloy clad steel having excellent intergranular corrosion resistance can be obtained.
- MC, M 6 C, M 23 C 6 (M represents a metal element) and the like are precipitated as carbides in the Ni alloy, and as an intermetallic compound, a Laves phase, a ⁇ phase, and a ⁇ ′′ phase There is.
- MC is mainly NbC, and the precipitation of MC does not greatly affect the corrosion resistance.
- the precipitation of intermetallic compounds is slower than the precipitation of carbides and is unlikely to cause corrosion resistance deterioration. Therefore, it is M 6 C and M 23 C 6 that cause the corrosion resistance deterioration of the Ni alloy.
- these M 6 C and M 23 C 6 contain a large amount of Cr and precipitate along the grain boundary of the Ni alloy, which causes sensitization.
- sensitization in Ni alloy arises when a carbide
- the aspect ratio of the crystal grains is increased, the grain boundary length is increased and the carbide precipitation sites are dispersed, so that sensitization is less likely to occur. If the aspect ratio is 1.5 or more, sensitization is unlikely to occur, so the aspect ratio of the crystal grains of the Ni alloy is 1.5 or more.
- the aspect ratio of the crystal grains is related to P, which segregates at the grain boundaries and deteriorates the corrosion resistance in addition to the sensitization in which the low Cr region is preferentially corroded.
- the amount of segregation per unit grain boundary length of S may decrease as the aspect ratio increases.
- C 0.030% or less
- C is an element that should be avoided because it precipitates at the grain boundaries as carbides due to the thermal history of the rolling and heat treatment processes and inhibits corrosion resistance. If the content exceeds 0.030%, precipitation of carbides is promoted, and the corrosion resistance deteriorates due to an increase in the amount of precipitated Cr, so the C content is 0.030% or less. Preferably it is 0.010% or less.
- Si 0.02 to 0.50% Since Si is an element effective for deoxidation during steel making, 0.02% or more is added. However, Si is an element that promotes the precipitation of M 6 C, and if it exceeds 0.50%, the amount of precipitated Cr is increased and sensitization is likely to occur. For this reason, the Si content is in the range of 0.02 to 0.50%. Preferably it is 0.02 to 0.20% of range.
- Mn 0.02 to 0.50% Mn is also an element effective for deoxidation, and 0.02% or more is added. However, if the content exceeds 0.50%, non-metallic inclusions remain, corrosion resistance deteriorates, and hot workability also deteriorates, so the Mn content is in the range of 0.02 to 0.50%. . Preferably it is 0.02 to 0.15% of range.
- P 0.015% or less
- P is an impurity element, and is an element that segregates at grain boundaries and deteriorates corrosion resistance when rolled at 1000 ° C. or more in order to ensure the bonding property of the clad steel plate. Therefore, the P content is 0.015% or less. Preferably it is 0.005% or less.
- S 0.015% or less
- S is an impurity element similar to P, and is an element that segregates at grain boundaries and deteriorates corrosion resistance when rolled at 1000 ° C. or more in order to ensure the bonding property of the clad steel plate. Therefore, the S content is 0.015% or less. Preferably it is 0.001% or less.
- Cr 20.0-23.0%
- Cr is an element that forms a highly protective oxide film on the surface of metal and improves pitting corrosion resistance and intergranular corrosion resistance.
- the Cr content is in the range of 20.0 to 23.0%.
- it is in the range of 21.0 to 22.0%.
- Mo 8.0 to 10.0% Mo improves pitting corrosion resistance and crevice corrosion resistance.
- the combined addition with Ni improves the stress corrosion cracking susceptibility in sour gas environment, so the addition amount with Ni and other alloy elements is taken into account in the range of 8.0 to 10.0%. . Preferably, it is in the range of 9.0 to 10.0%.
- Fe 5.0% or less Fe is an impurity inevitably mixed when ferrochrome, ferromolybdenum or the like is used as a raw material, and if it exceeds 5.0%, the amount of Ni decreases and corrosion resistance decreases.
- the amount of Fe is 5.0% or less. Preferably it is 3.5% or less.
- Al 0.02 to 0.40% Al is added in an amount of 0.02% or more as an element effective for deoxidation. However, if the content exceeds 0.40%, the stress corrosion cracking resistance deteriorates, so the Al content is in the range of 0.02 to 0.40%. Preferably it is 0.02 to 0.20% of range. More preferably, it is in the range of 0.02 to 0.15%.
- Ti 0.10 to 0.40% Since Ti is effective as a C-fixing element, 0.10% or more is added. However, if it is contained in a large amount, it precipitates as an intermetallic compound at the joining interface of the clad steel plate and inhibits the joining property, so the Ti content is set in the range of 0.10 to 0.40%. Preferably it is 0.10 to 0.30% of range.
- Nb + Ta 3.15 to 4.15%
- Nb and Ta are also elements that contribute to the fixation of C. However, if it is contained in a large amount, it precipitates as an intermetallic compound at the joint interface of the clad steel and inhibits the bondability, so the amount of Nb + Ta is set in the range of 3.15 to 4.15%.
- a preferable Nb + Ta amount is in the range of 3.50 to 4.00%.
- Ni is an element that improves corrosion resistance, and remarkably improves stress corrosion cracking resistance in a sour environment.
- the corrosion resistance is further improved by the combined effect of Cr and Mo.
- Inevitable impurities include N, O, V, B, and W. N: 0.01% or less, O: 0.001% or less, V: 0.04% or less, B: 0.0. Even if it is contained within the range of 0005% or less and W: 0.3% or less, it does not affect the corrosion resistance.
- the laminated material of clad steel of the present invention is adjusted to the above-described component range and can be melted by a conventional method or the like.
- the base material of the clad steel is selected depending on the use of the clad steel, etc., but in an application used for pipelines such as carbon steel and natural gas, for example, as a base material, in mass%, C: 0.26% or less, A low alloy steel having Mn: 1.65% or less, P: 0.030% or less, S: 0.030% or less, and Nb + V + Ti: 0.15% or less can be used.
- An assembly slab for clad rolling is prepared by combining these laminated material and base material, and a clad steel plate is obtained by clad rolling.
- the material of the Ni alloy clad steel refers to an assembly slab for clad rolling in which a laminated material and a base material are combined.
- Heating temperature 1050 ° C. or higher and 1200 ° C. or lower Heated to 1050 ° C. or higher in order to sufficiently melt the laminated material during heating.
- heating temperature shall be the range of 1050 degreeC or more and 1200 degrees C or less.
- it is the range of 1050 degreeC or more and 1150 degrees C or less.
- the rolling ratio at 1000 ° C. or higher In order to obtain a sufficient bonding material / base metal interface bonding, the rolling ratio at 1000 ° C. or higher needs to be 2 or higher.
- Ni alloy has a large deformation resistance as compared with low alloy steel, and there is a problem that it is difficult to obtain good jointability when a clad material is manufactured.
- a preferable reduction ratio is 3 or more.
- Control rolling Reduction ratio of 1.5 to 4 at 950 ° C. or less
- Control rolling is based on the premise that finish rolling is finished at 700 ° C. or more, and in order to secure the strength and toughness of the base material, the controlled rolling start temperature is 950 ° C. or less, and the rolling ratio is 1.5 or more and 4 or less.
- the reduction ratio In order to set the crystal grain aspect ratio of the laminated material to 1.5 or more, it is necessary to set the reduction ratio of 950 ° C. or less to 1.5 or more. When the reduction ratio exceeds 4, sufficient reduction in the high temperature range is ensured. It cannot be done and the bondability deteriorates.
- the preferable reduction ratio is 2 or more and 3.5 or less, and the more preferable reduction ratio is 2.5 or more and 3 or less.
- Rolling finishing temperature 700 ° C. or higher
- the rolling finishing temperature is set to 700 ° C. or higher.
- Cooling rate 1 ° C./s or higher
- cooling stop temperature 500 ° C. or lower
- the reason for cooling to 500 ° C. or lower at the cooling rate of 1 ° C./s or higher after rolling is to ensure the strength and toughness of the base material. If the cooling rate in the temperature range from 700 ° C. or higher rolling temperature to 500 ° C. is less than 1 ° C./s, the base material crystal grains are remarkably coarsened and the toughness deteriorates. Further, when the cooling stop temperature is higher than 500 ° C., sufficient strength cannot be obtained. Therefore, cooling is performed to 500 ° C. or lower at a cooling rate of 1 ° C./s or higher after the end of rolling.
- the test method is to immerse the test piece in a boiling 65% nitric acid solution for 48 hours, calculate the corrosion rate (g / m 2 ⁇ h) from the weight change before and after the test, and the same in a new boiling 65% nitric acid solution. Immerse the specimen again. This 48-hour immersion test was repeated five times, and the intergranular corrosion resistance was evaluated from the average value of the five corrosion rates. Evaluation criteria were determined to be good for intergranular corrosion resistance when the value was 0.75 g / m 2 ⁇ h or less.
- the bondability evaluation of the laminated material and the base material was based on the JIS G0601 shear strength test.
- the shear strength test is a method in which the laminated material is peeled from the base material in parallel with the joining surface, and the joining property is evaluated from the maximum shear strength required for the peeling. Evaluation criteria determined that the shearing stress was 300 MPa or more and the bondability was good.
- the toughness of the base material was evaluated by a DWTT test (Drop Weight Tear Test) at -20 ° C.
- a ductile fracture area ratio (Shear Area ratio) of 85% or more is considered to be excellent in the toughness of the base material.
- a laminated material and a base material were prepared using 13 types of laminated material shown in Table 1 (10 types of invention steel, 3 types of comparative steel) and 2 types of base material. Clad steel was produced using this laminated material and base material, and the amount of precipitated Cr and intergranular corrosion resistance were investigated. After heating the clad steel slab using each laminated material at a heating temperature of 1100 ° C., rolling was started, the rolling ratio at 1000 ° C. or higher was 2.5, and the rolling ratio at 950 ° C. or lower was 2.5, and 750 Rolling was terminated at 0 ° C., and accelerated cooling was immediately started at a cooling rate of 5 ° C./s, and accelerated cooling was terminated at 350 ° C. The results are shown in Table 2.
- the laminated material is a laminated material No. 1 shown in Table 1. 1 to 13 Ni alloys were used.
- the chemical composition of the base material is the same as the base material No. Low carbon steel having a component system corresponding to API standard X65 grade shown in AA and BB was used.
- the production methods A to D which are invention examples, all have the reduction ratio, rolling finish temperature, cooling rate, and cooling stop temperature within the scope of the invention.
- the production methods E to H which are comparative examples, any production conditions such as a reduction ratio are out of the scope of the invention.
- test results are shown in Tables 4-1 and 4-2.
- levels 1 to 9 in which the components of the laminated material are within the scope of the invention showed a small amount of precipitated Cr and good intergranular corrosion resistance.
- levels 1 to 5 in which the components of the laminated material and the manufacturing method were within the scope of the invention were all good in corrosion resistance, bondability and base material falling weight characteristics.
- the amount of precipitated Cr exceeds 0.030% of the upper limit value and is inferior in intergranular corrosion resistance.
- E (level 14) the shear strength is low and the bondability is poor.
- F (levels 15 to 17) the production finishing temperature at which the finishing temperature at the rolling finish falls below the lower limit.
- G level 18 and production method no.
- H level 19
- the ductile fracture surface ratio was less than 85% in the DWTT test (falling weight characteristic) at ⁇ 20 ° C., which was inferior to the base material falling weight characteristic.
- Table 5 shows the test results of the aspect ratio.
- the crystal grain aspect ratio was large and the intergranular corrosion resistance was excellent.
- levels 26 to 28 having an aspect ratio of less than the lower limit had a corrosion rate exceeding 0.75 g / m 2 ⁇ hr and were inferior in intergranular corrosion resistance.
- Table 6 shows the results of the amount of precipitated Cr and the aspect ratio. Levels 29 to 32 where the amount of precipitated Cr and the aspect ratio are within the range of the present invention were excellent in the intergranular corrosion resistance. On the other hand, in levels 33 to 35, the amount of precipitated Cr is larger than 0.030, the aspect ratio is less than 1.5, the corrosion rate exceeds 0.75 g / m 2 ⁇ hr, and the intergranular corrosion resistance is inferior. It was.
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Abstract
Description
このような背景から、溶体化処理が不要な耐食性に優れたクラッド鋼の製造方法が検討されている。
本発明の要旨は、以下の通りである。
析出Cr量とは析出物として存在するCr量である。Crは不動態皮膜を形成する元素として一般的に広く知られている。粒界に沿った析出物にNi合金マトリックス中のCrが集まると、析出物周辺部のCr濃度が低くなる。この現象を鋭敏化という。鋭敏化した材料が腐食環境下に置かれると、この低Cr領域が優先的に腐食される。析出Cr量が質量%で0.030%を超えると鋭敏化が進み、結晶粒の脱落が生じる。そのため、析出Cr量は0.030%以下とする。
前述のように、Ni合金における鋭敏化は炭化物が粒界に沿って析出することにより生じる。結晶粒のアスペクト比が大きくなると、粒界長が長くなり、炭化物の析出サイトが分散されるので、鋭敏化が生じにくくなる。アスペクト比が1.5以上であれば鋭敏化が生じにくくなるため、Ni合金の結晶粒のアスペクト比を1.5以上とする。
以下、本発明における合せ材は、炭化物として存在するCr量が質量%で、0.030%以下のNi合金、および/または、合せ材の結晶粒のアスペクト比が1.5以上であるNi合金であれば良い。更に好適な成分組成として以下のように規定した。なお、成分%は、特に記載がない限り質量%を意味する。
Cはクラッド鋼の製造において、圧延および熱処理工程の熱履歴で炭化物として粒界に析出し、耐食性を阻害するため多量の含有は避けるべき元素である。0.030%を超えて含有すると、炭化物の析出が促進され、析出Cr量が増大することで耐食性が劣化するため、C量は0.030%以下とする。好ましくは0.010%以下である。
Siは製鋼時の脱酸に有効な元素のため、0.02%以上添加する。しかし、SiはM6Cの析出を促進する元素であり、0.50%を超えて含有すると、析出Cr量の増大を引き起こし、鋭敏化が生じ易くなる。そのため、Si量は0.02~0.50%の範囲とする。好ましくは0.02~0.20%の範囲である。
Mnも脱酸に有効な元素であり、0.02%以上添加する。しかし、0.50%を超えて含有すると、非金属介在物が残存し、耐食性が劣化し、また熱間加工性も劣化するため、Mn量は0.02~0.50%の範囲とする。好ましくは0.02~0.15%の範囲である。
Pは不純物元素であり、クラッド鋼板の接合性確保のため、1000℃以上で圧延する際に、粒界に偏析し、耐食性を劣化させる元素である。したがって、P量は0.015%以下とする。好ましくは0.005%以下である。
SはPと同様に不純物元素であり、クラッド鋼板の接合性確保のため、1000℃以上で圧延する際に、粒界に偏析し、耐食性を劣化させる元素である。したがって、S量は0.015%以下とする。好ましくは0.001%以下である。
Crは、金属の表面に保護性の高い酸化物皮膜を形成し、耐孔食性や耐粒界腐食特性を向上させる元素である。しかし、Crを過剰に含有すると析出Cr量の増大を引き起こし、鋭敏化を生じ易くなる。従って、Niやその他の合金とのバランスも考え、Cr量は20.0~23.0%の範囲とする。好ましくは、21.0~22.0%の範囲である。
Moは、耐孔食性、耐隙間腐食性を向上させる。また、Niとの複合添加によって、サワーガス環境中での耐応力腐食割れ感受性も改善するため、Niやその他の合金元素との添加量を考慮して8.0~10.0%の範囲とする。好ましくは、9.0~10.0%の範囲である。
Feは、原料としてフェロクロム、フェロモリブデン等を用いた場合、不可避的に混入する不純物であり、5.0%を超えるとNi量が低下して耐食性が低下するため、Fe量は5.0%以下とする。好ましくは3.5%以下である。
Alは脱酸に有効な元素として0.02%以上添加する。しかし、0.40%を超えて含有すると耐応力腐食割れ性が劣化するため、Al量は0.02~0.40%の範囲とする。好ましくは0.02~0.20%の範囲である。より好ましくは、0.02~0.15%の範囲である。
TiはCの固定化元素として有効であるため、0.10%以上添加する。しかし、多量に含有するとクラッド鋼板の接合界面で金属間化合物として析出し、接合性を阻害するため、Ti量は0.10~0.40%の範囲とする。好ましくは0.10~0.30%の範囲である。
Nb、TaもCの固定化に寄与する元素である。しかし、多量に含有するとクラッド鋼の接合界面で金属間化合物として析出し、接合性を阻害するため、Nb+Ta量は3.15~4.15%の範囲とする。好ましいNb+Ta量は3.50~4.00%の範囲である。
上記した合せ材の成分の残部はNiおよび不可避的不純物である。Niは耐食性を向上させる元素であり、特に、サワー環境での耐応力腐食割れ性を著しく改善する。前述したように、CrとMoとの複合添加効果でさらに耐食性は向上する。また、不可避的不純物としては、N、O、V、B、Wが挙げられ、それぞれN:0.01%以下、O:0.001%以下、V:0.04%以下、B:0.0005%以下、W:0.3%以下の範囲内で含有しても耐食性に何ら影響を与えるものではない。
本発明のNi合金クラッド鋼の製造方法について以下に述べる。
加熱時に合せ材を十分溶体化するために1050℃以上に加熱する。しかし、高温に加熱しすぎると合せ材の熱間加工性が劣化し、母材の結晶粒粗大化による靭性劣化を招く。そのため加熱温度は1050℃以上1200℃以下の範囲とする。好ましくは1050℃以上1150℃以下の範囲である。
十分な合せ材/母材界面接合を得るためには、1000℃以上での圧下比が2以上である必要がある。Ni合金は低合金鋼に比較して変形抵抗が大きく、クラッド材を製造する場合、良好な接合性が得られにくいという難点がある。しかし、1000℃以上の高温域ではNi合金と低合金鋼の変形抵抗差は小さくなる。そのため、1000℃以上での圧下比(=(圧延前の板厚)÷(圧延後の板厚))を2以上とすることで良好な合せ材/母材界面の接合強度が得られる。従って、1000℃以上の圧下比を2以上とする。好ましい圧下比は3以上である。
制御圧延は700℃以上で仕上げ圧延を終了することを前提とし、さらに母材の強度、靭性を確保するために、制御圧延開始温度は950℃以下、圧下比は1.5以上4以下とする。合せ材の結晶粒アスペクト比を1.5以上とするには、950℃以下の圧下比を1.5以上とする必要があり、圧下比が4を超えると高温域での十分な圧下を確保出来ず、接合性が劣化する。
圧延仕上げ温度が700℃未満となると、母材の靭性が劣化するため圧延仕上げ温度は700℃以上とする。
圧延終了後に冷却速度1℃/s以上で、500℃以下まで冷却するのは、母材の強度、靭性を担保するためである。700℃以上の圧延終了温度から500℃の温度範囲における冷却速度が1℃/s未満では母材の結晶粒粗大化が著しく、靭性が劣化する。また、冷却停止温度を500℃よりも高温にした場合、十分な強度が得られない。そのため、圧延終了後に冷却速度1℃/s以上で500℃以下まで冷却を行う。
析出物の抽出には10vol.%アセチルアセトン(acetylacetone)-1mass%塩化テトラメチルアンモニウム(tetramethylammonium chloride)-メタノール混合液(methanol mixture 通称10%AA液と呼ぶ)中での電解抽出((Electrolytic extraction)通称SPEED法と呼ぶ)を適用した。ろ過によりフィルター上に捕集した抽出残渣(extraction residue)のXRD(X-ray diffraction)より、析出物の種類を特定した。また、抽出残渣を混酸溶解(混酸成分比 硫酸10ml:硝酸10ml:過塩素酸5ml:水10ml)し、ICP発光分光分析(inductively-coupled plasma emission spectrometry誘導結合プラズマ発光分光分析)することで析出Cr量を求めた。
合せ材の結晶粒アスペクト比はエッチング処理を施した合せ材(L面、 1/4t位置)の組織写真を撮影した後、一定長さの線分を圧延方向と板厚方向にそれぞれ引き、結晶粒の圧延方向長さおよび板厚方向長さの平均値を求め、アスペクト比=(結晶粒の圧延方向長さ)/(結晶粒の板厚方向長さ)として算出した。
合せ材は表1に示す合せ材No.1~13のNi合金を使用した。母材の化学成分は、同じく表1の母材No.AA、BBに示すAPI規格X65グレード相当の成分系を有する低炭素鋼を使用した。
表3において、発明例である製造方法A~Dは圧下比、圧延仕上温度、冷却速度、冷却停止温度が全て発明の範囲内である。一方、比較例である製造方法E~Hは圧下比など、いずれかの製造条件が発明の範囲をはずれている。
Claims (5)
- Ni合金からなる合せ材中に炭化物として存在するCr量が、質量%で、0.030%以下であることを特徴とする耐粒界腐食特性に優れたNi合金クラッド鋼。
- Ni合金からなる合せ材の結晶粒のアスペクト比が1.5以上であることを特徴とする耐粒界腐食特性に優れたNi合金クラッド鋼。
- Ni合金からなる合せ材中に炭化物として存在するCr量が、質量%で、0.030%以下であり、前記合せ材の結晶粒のアスペクト比が1.5以上であることを特徴とする耐粒界腐食特性に優れたNi合金クラッド鋼。
- 合せ材として、さらに、質量%で、C:0.030%以下、Si:0.02~0.50%、Mn:0.02~0.50%、P:0.015%以下、S:0.015%以下、Cr:20.0~23.0%、Mo:8.0~10.0%、Fe:5.0%以下、Al:0.02~0.40%、Ti:0.10~0.40%を含有し、さらに、Nb+Taを3.15~4.15%含有し、残部がNi及び不可避的不純物からなることを特徴とする請求項1乃至3の何れかに記載の耐粒界腐食特性に優れたNi合金クラッド鋼。
- 請求項4に記載のNi合金クラッド鋼の素材を用いて、1050℃以上1200℃以下に加熱後、1000℃以上での圧下比を2以上とし、950℃以下の温度域における制御圧延の圧下比を1.5以上4以下、圧延仕上温度を700℃以上とする熱間圧延を行った後、直ちに冷却速度1℃/s以上、冷却停止温度500℃以下とする加速冷却を行った後に放冷することを特徴とする母材靭性および耐粒界腐食特性に優れたNi合金クラッド鋼の製造方法。
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