WO2003069011A1 - Procede de traitement thermique d'une conduite a base d'alliage de nickel - Google Patents
Procede de traitement thermique d'une conduite a base d'alliage de nickel Download PDFInfo
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- WO2003069011A1 WO2003069011A1 PCT/JP2003/001451 JP0301451W WO03069011A1 WO 2003069011 A1 WO2003069011 A1 WO 2003069011A1 JP 0301451 W JP0301451 W JP 0301451W WO 03069011 A1 WO03069011 A1 WO 03069011A1
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- heat treatment
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/058—Alloys based on nickel or cobalt based on nickel with chromium without Mo and W
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- 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
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/10—Oxidising
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/10—Oxidising
- C23C8/16—Oxidising using oxygen-containing compounds, e.g. water, carbon dioxide
-
- 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
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
-
- 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
- C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
Definitions
- the present invention relates to a method for heat-treating an M-base alloy tube, which can be manufactured on an industrial scale at low cost, on an inner surface of the tube, which has an oxide film for suppressing M elution from a base material.
- M-based alloys are used as various materials because they have excellent mechanical properties as well as corrosion resistance.
- materials used as reactor components are M-base alloys, which are highly corrosion-resistant because they are exposed to high-temperature water.
- heat transfer tubes for steam generators in pressurized water reactors (PWRs) are used.
- Alloy 60 (60% Ni-30% Cr-10% Fe, trade name) is used.
- Ni-based alloys have excellent corrosion resistance and a low corrosion rate, but Ni is eluted from the base metal to a small extent over a long period of use to form ions.
- Ni is transported to the reactor core in the process of circulating the reactor water and is irradiated with neutrons near the fuel.
- neutrons near the fuel.
- Co has a very long half-life, so it emits radiation for a long time. Therefore, as the amount of dissolved M increases, the exposure dose to workers who perform periodic inspections increases.
- JP 64 - The 55366 discloses, in an atmosphere of vacuum degree of Ni base alloy heat transfer tube 10 _ 2 ⁇ 10 ⁇ toir, mainly click opening arm oxide was annealed in the temperature range of 400 to 750 ° C There is disclosed a method for forming an oxide film to improve the overall corrosion resistance.
- JP-A-1 one 159 362, the inert gas 10 2-10 - 4 vol. /. How oxygen is mixed, to improve the temperature range in the heat treatment to chromium oxide (Cr 2 0 3) by generating an oxide film mainly comprising resistant grain boundary stress corrosion cracking resistance of 400 to 750 ° C Is disclosed.
- JP-A-2-47249 and JP-A-2-80552 disclose that stainless steel for heater tubes is heated in an inert gas containing a specific amount of oxygen to form a film made of oxide. Discloses a method for suppressing the elution of Co and Co in stainless steel.
- Japanese Patent Application Laid-Open No. 3-153858 discloses an elution-resistant stainless steel in high-temperature water provided with an oxide layer containing more Cr-containing oxides than oxides not containing Cr on the surface.
- Japanese Unexamined Patent Publication No. 4-350180 discloses that ultra-high-purity stainless steel pipes (so-called EP pipes) whose inner surfaces are electrolytically polished are sequentially connected and subjected to solution heat treatment while continuously supplying hydrogen gas to the inside. It allows a method of reducing the emission of gaseous components from the tube surface to produce a passive film to the Cr 2 0 3 and the main body is disclosed. According to this method, a uniform passivation film can be easily formed, but pretreatment for high cleanliness such as electrolytic polishing is required. Therefore, the number of steps is large and the cost is high. Disclosure of the invention
- An object of the present invention is to produce an Ni-based alloy tube with extremely low M elution in a high-temperature water environment for a long time at low cost on an industrial scale without the need for expensive pretreatment such as electrolytic polishing of the inner surface of the tube.
- An object of the present invention is to provide a heat treatment method for an M-base alloy tube that can perform the heat treatment.
- MnCr 2 0 4 has at least including the oxide film of the second layer of the second layer mainly composed of, in the grain size of Cr 2 0 3 of the first layer is 50 to LOOOnm, total thickness of the oxide film 1S0 ⁇ It is a 1500nm tube.
- the gist of the present invention is the following (1) and (2) heat treatment methods for a Ni-based alloy tube.
- % of the component content is% by mass unless otherwise specified.
- a heat treatment method for Ni-base alloy tubes in which the tube to be treated is maintained at 650 to 1200 for 1 to 1200 minutes by a continuous heat treatment furnace, with a dew point within the range of 160 ° C to + 20 ° C.
- At least two gas supply devices for supplying an atmosphere gas composed of hydrogen or a mixed gas of hydrogen and argon are provided on the outlet side of the continuous heat treatment furnace so as to be movable in the traveling direction of the pipe to be treated.
- the front end in the traveling direction is inserted into the pipe to be treated before being charged into the continuous heat treatment furnace.
- the pipe to be treated is charged into the continuous heat treatment furnace while the above-mentioned atmosphere gas is supplied from the side, and after the end of the pipe to be treated reaches the exit side of the continuous heat treatment furnace, the pipe to the inside of the pipe to be treated is introduced.
- a heat treatment method for a Ni-based alloy tube characterized by the following. Hereinafter, this is referred to as a first heat treatment method.
- At least one gas supply device for supplying the atmospheric gas consisting of hydrogen or a mixture gas of hydrogen and argon in the continuous heat treatment furnace.
- the gas supply device is installed movably in the direction, and is provided on the inlet side of the continuous heat treatment furnace, and the gas introduction pipe, which is longer than the pipe to be treated and is disposed so as to penetrate through the continuous heat treatment furnace.
- the pipe to be treated is charged into the continuous heat treatment furnace while supplying the above-mentioned atmospheric gas from the tip side in the traveling direction into the inside of the pipe to be treated before being charged into the continuous heat treatment furnace.
- a heat treatment method for a Ni-based alloy tube characterized by repeating an operation of switching gas supply to supply from a gas supply device provided on an outlet side of a continuous heat treatment furnace.
- this is referred to as a second heat treatment method.
- the M-based alloy tube to be subjected to the heat treatment is preferably a Ni-based alloy of the following (a) or (b).
- M-base alloy tube is cold It is desirable that the steel has been subjected to cold working. This is because cold working makes the inner surface of the Ni-based alloy tube easily diffuse Cr and has the effect of promoting the formation of an oxide film in the subsequent oxide film formation treatment.
- FIG. 1 is a plan view for explaining a first heat treatment method of the present invention.
- FIG. 2 is an enlarged plan view showing a gas introduction pipe and a header used in the first heat treatment method of the present invention.
- FIG. 3 is a plan view for explaining the second heat treatment method of the present invention.
- FIG. 4 is an enlarged plan view showing a gas introduction pipe and a header used in the second heat treatment method of the present invention.
- FIG. 5 is a diagram schematically showing a cross section near the inner surface of a Ni-based alloy tube obtained by the heat treatment method of the present invention.
- FIG. 6 shows the vicinity of the inner surface of the M-base alloy tube obtained by the heat treatment method of the present invention.
- FIG. 1 is a plan view showing an embodiment of the first heat treatment method of the present invention (the inside of the furnace is a plan view of the inside of the furnace).
- A of the figure shows the supply mode of the atmospheric gas to the inside of the tube for the group of tubes la to be treated during the preceding heat treatment and the group of tubes to be treated lb before the subsequent heat treatment.
- B of the figure shows the manner in which the atmosphere gas is supplied to the inside of the pipes for the preceding pipe group la and the subsequent pipe group lb during the heat treatment.
- C of the same figure shows a mode of switching the supply of the atmospheric gas to the inside of the tube with respect to the tube group lb to be processed during the heat treatment.
- a continuous heat treatment furnace (hereinafter simply referred to as a heat treatment furnace) 5 It has a heating zone 5a and a cooling zone 5b.
- the atmosphere in the furnace of the heat treatment furnace 5 is a hydrogen gas atmosphere, and the furnace pressure is set slightly higher than the atmospheric pressure so that the air does not flow into the furnace.
- each of the gas supply devices 4a and 4b is provided so as to be able to advance and retreat in the same direction as the groups of pipes la and lb to be processed, which are transported in the directions indicated by the white arrows.
- the illustrated gas supply devices 4a and 4b are arranged so as to be displaced in a direction perpendicular to the plane of the drawing so as not to interfere with each other.
- the header 2-1 has a tapered nozzle 2a and a gas inlet tube 3-1. The nozzle 2a of the header 2-1 is inserted into the leading end of the preceding tube group la.
- the header 2-1 is connected to the gas supply device 4a.
- the header 2-2 for the succeeding pipe group lb is connected to the gas supply device lb via the gas inlet pipe 3-1. Therefore, in the state shown in FIG. 2, gas does not flow through the gas introduction pipe 3-1.
- atmosphere gas consisting of hydrogen or a mixed gas of hydrogen and argon (hereinafter simply referred to as atmosphere gas) with a dew point in the range of 160 ° C to + 20 ° C is supplied.
- the atmosphere gas is supplied from the gas supply device 4a to the inside of the pipe group la to be processed during the heat treatment, and the header 2-1 is provided to the inside of the pipe group lb before the heat treatment.
- the gas is supplied from the gas supply device 4b via the gas introduction pipe 3-1 attached to the gas supply unit (see (a) in Fig. 1).
- the preceding pipe group la and the subsequent pipe group lb are conveyed in the direction of the white arrow to heat-treat the pipes in both groups (Fig. 1 (b )).
- FIG. 3 is a plan view similar to FIG. 1, illustrating one embodiment of the second heat treatment method of the present invention.
- A of the figure shows the supply mode of the atmospheric gas to the inside of the tube for the preceding group of tubes la to be treated before the heat treatment.
- B of the figure shows a mode of switching the supply of the atmospheric gas to the inside of the tube of the preceding tube group la during the heat treatment.
- C in the same figure shows the manner in which the atmosphere gas is supplied into the tubes of the preceding group of pipes la and the subsequent group of pipes lb during the heat treatment.
- the heat treatment furnace 5 is the same as the furnace shown in FIG. In this method, unlike the case of FIG. 1, one gas supply device 4a and 4b is provided on the inlet side (left side in the figure) and the outlet side (right side in the figure) of the heat treatment furnace 5, respectively. Have been. As in the case of FIG. 1, these gas supply devices 4a and 4b are provided so as to be able to advance and retreat in the same direction as the groups of pipes la and lb to be processed, which are transported in the directions indicated by white arrows.
- FIG. 4 is an enlarged plan view of a part of FIG.
- a protrusion is provided at the center in the longitudinal direction, and a plug 2b-l that can be opened and closed is attached to the right end.
- the tapered nozzle 2a of header 2-1 with 2c-l is inserted.
- a gas is supplied to each pipe from the gas supply device 4a via the gas introduction pipe 3-1.
- a check valve (not shown) that allows only gas flow in the direction of the arrow may be installed inside the left end of the gas inlet pipe 3-1. It is not necessary.
- the same atmosphere gas as described above is supplied from the gas supply device 4a through the gas introduction pipe 3-1 and the header 2-1 closed by the plug 2b-l to the pipe to be treated before the heat treatment. It is supplied to the inside of the tube of group la (see (a) in Fig. 3).
- the tube group la to be treated is transported in the direction of the white arrow and charged into the heat treatment furnace 5 for heat treatment.
- the supply of the atmosphere gas to the inside of the pipe is performed from the inlet side gas supply device 4a.
- the plug 2b-l attached to the right end of the protrusion 2c-l of the header 2-1 is naturally opened.
- the gas supply device 4a on the inlet side is provided for the supply of the atmospheric gas to the inside of the tube of the subsequent tube group to be processed.
- FIG. 3 (c) shows the subsequent pipe group lb receiving the atmosphere gas from the inlet gas supply device 4a and the supply of the atmosphere gas from the outlet gas supply device 4b. This shows an embodiment in which the heat treatment is performed simultaneously on the preceding tube group la to be processed.
- each pipe to be processed constituting the group la (lb, lc) may be used. It is desirable that the above-mentioned joint member has a structure in which the end of the pipe to be treated is fitted inside.
- the set of the header 2 and the gas introduction pipe 3 is used in a circulating manner.
- the atmosphere gas is introduced into the pipe before entering the heat treatment furnace.
- the flow purges the air inside the tube. Therefore, a target oxide film is formed on the inner surface of the tube during the heat treatment.
- the atmospheric gas flows in the pipe in a direction opposite to the direction in which the pipe moves. That is, the residue inside the tube, which has been cleaned but not subjected to the heat treatment, is vaporized in the high temperature part of the heat treatment process and discharged outside the tube.
- the vaporized pipe inner surface residue may move by the gas flow in the pipe, reach a part that has not been heated yet, condense again, and reattach to the pipe inner surface.
- the temperature is raised and then re-vaporized, so that all the gas is finally discharged from the pipe.
- a uniform oxide film having desired performance can be formed on the inner surface of the EP tube without performing prior electrolytic polishing or the like as in the EP tube.
- a heat treatment atmosphere which must be a hydrogen gas or a mixed gas atmosphere of hydrogen and argon. Further, in order to form the above-mentioned oxide film densely, it is necessary to make the above atmosphere contain moisture.
- the amount ranges from 1-60 ° C to +20 ° C when expressed in dew point. Desirable dew point ranges are 130 to 520 ° C in a hydrogen atmosphere containing 0 to 10% by volume of argon, and 150 to 0 ° C in a hydrogen atmosphere containing 10 to 80% by volume of argon.
- Heat treatment time is an important factor that determines the thickness of the film. In less than a minute
- the Cr 0 3 oxide film of the first layer mainly composed of does not become more uniform film thickness 170 nm.
- the first oxide film will be thicker than 1200 nm.
- the total thickness of the oxide film exceeds 1500 nm, and the oxide film is easily peeled off, and the effect of preventing the film from eluting Ni is reduced.
- the pipe to be treated (M-base alloy pipe) be cold worked before the above heat treatment. This is because an oxide film is easily formed on a cold-worked surface and the film becomes dense.
- the working ratio of this cold working is desirably 30% or more. There is no upper limit on the processing rate, but the practical upper limit is 90% that can be achieved with ordinary technology. This cold working is cold drawing and cold rolling.
- a thermal treatment (TT) treatment may be performed.
- This treatment is effective in increasing the corrosion resistance of M-based alloy pipes in high-temperature water, especially stress corrosion cracking resistance.
- Appropriate heat treatment temperature is 650 to 750 ° C and treatment time is 300 to 1200 minutes.
- the oxide film forming process can be replaced with the TT process.
- the base material of the Ni-based alloy tube of the present invention is an alloy containing Ni as a main component.
- Ni As a main component.
- An alloy containing up to 15% and 0 to 0.5% of Ti, with the balance being Ni and impurities is desirable. The reason is as follows.
- C is desirably contained at least 0.01% in order to increase the grain boundary strength of the alloy.
- the content is preferably 0.15% or less. More preferred is 0.01 to 0.06. Most preferred is 0.015 to 0.025%.
- Mn is desirably contained at 0.1 ° / 0 or more in order to form a second layer mainly composed of MnCrO. However, if it exceeds 1.0%, the corrosion resistance of the alloy decreases. A desirable upper limit is 0.50%.
- Cr is an element necessary to form an oxide film that prevents the elution of metals.
- Cr must be contained in an amount of 10% or more. However, if it exceeds 40%, the M content becomes relatively small, so that the corrosion resistance of the alloy decreases. Desirable is 28.5-31.0%.
- Fe is an element that forms a solid solution with Ni and can be used in place of a part of expensive Ni, and is desirably contained at 5% or more. However, if it exceeds 15%, the corrosion resistance of the Ni-based alloy will be impaired. Preferred is 9.0-11.0 ° / 0 .
- Ti is added as necessary since it has the effect of improving the workability of the alloy, but it is desirable to contain 0.1% or more in order to obtain a remarkable effect. However, if it exceeds 0.5%, the cleanliness of the alloy is impaired. A desirable upper limit is 0.40%.
- the other components are substantially M.
- the M content is desirably 45 to 75%, and more desirably 58 to 75%.
- Si is 0.50% or less
- P is 0.030% or less (more preferably 0.015% or less)
- S is 0.015% or less (more preferably 0.003% or less)
- Co is 0.020 ° / 0 or less ( More preferred is 0.014% or less
- Cu is 0.50% or less (more preferred is 0.10% or less)
- N is 0.050% or less
- A1 is 0.40% or less
- B is 0.005% or less
- Mo is 0.2% or less
- b Should be kept below 0.1%.
- FIG. 5 schematically shows a cross section near the inner surface of a Ni-based alloy tube heat-treated by the method of the present invention.
- the oxide film is roughly from the side closer to the base member 7 and the first layer 8 consisting mainly of Cr 2 0 3 that and a second layer 9 of the outer MnCr 2 0 4 and the main body.
- Fig. 6 shows the results of a heat treatment method according to the present invention in which an oxide film was formed on the inner surface of an M-base alloy tube whose base material was an alloy with 29.3% Cr, 9.7% Fe, and the balance M.
- SIMS secondary ion mass spectrometry
- Cr configured high ratio portion of FIG. This is the first layer mainly composed of Cr 2 0 3
- a second layer higher outermost layer of composition ratio of Mn is mainly composed of MnCr 2 0 4.
- These layers also contain oxides such as Mn, Al and Ti, but their amounts are small.
- the oxide film must have a low diffusion rate in the oxide film. It is also necessary to regenerate even if the film is destroyed during the use of the product.
- Such oxidation coating to have a function has a structure as described above, not further, Cr content of the first layer mainly composed of Cr 2 0 3, if the appropriate compactness and thickness .
- the metal elution prevention performance of the oxide film of the conventional Ni-based alloy is low, the low proportion of Cr 2 0 3 oxide skin film, the film thickness of the Cr 2 0 3 is thin, and Cr 2 0 3 Is not dense.
- the Cr concentration in the oxide film of the first layer that affects the amount of M eluted from the M-based alloy in a high-temperature water environment.
- the case where the Cr content in the first layer is 50% or more and the film thickness and denseness are within a predetermined range.
- the higher the Cr content, the greater the effect of preventing elution, so the desirable Cr content is 70% or more.
- the term the Cr content and is the mass% of Cr, which accounts for the total amount of all metal components in the film mainly composed of Cr 2 0 3 is a first layer therein is 100.
- Crystal grain size of the measure of the compactness of the oxide film Cr 2 0 3 is Ru important.
- M is eluted from the base material through the shed 2 0 3 film.
- Ni is moved to spread the grain boundary of Cr 2 0 3.
- the grain size of cr 2 0 3 is smaller than 50 nm, Ri of many crystal grain boundaries, to promote the diffusion of Ni, the elution tends to occur. Therefore, the lower limit of the crystal grain size is 50 nm.
- Cr 2 0 3 oxide film is not uniformly formed on the inner surface of the Ni-based alloy tube, Yabu ⁇ of Cr 2 0 3 film is caused by various reasons. Oxidation when destruction occurs Leaching from the rupture site occurs to a lesser extent than without the coating at all.
- Cause Cr 2 0 3 film is Yabu ⁇ is two broadly divided into the following. The first is the external force applied to the product pipe during manufacture or use. A typical example of external force during manufacturing is bending. External force during use includes vibration. The other is the stress based on the difference in the coefficient of thermal expansion between the base metal and the oxide film.
- the grain size of Cr 2 0 3 requests as follows. That is, a Ni-based alloy tube is dissolved in, for example, a bromethanol solution, and the interface between the base material and the remaining oxide film is magnified 20,000 times by a field emission type secondary electron microscope (FE-SEM). Observe three fields and determine the average value of the minor axis and major axis of each crystal as the diameter of one crystal grain, and calculate the average value. That value is the crystal grain size.
- FE-SEM field emission type secondary electron microscope
- Rukoto used as the oxide film to prevent the Ni elution from the inner surface of M based alloy tube Ru TiO 2, A1 2 0 3 and Cr 2 0 3 der. Both have relatively low solubility in high-temperature water, so forming a dense oxide film is effective in preventing M elution.
- Ru, A1, etc. if a large amount of Ti, A1, etc. is present in the M-base alloy, the amount of intermetallic compounds and inclusions increases, which unfavorably affects the alloy's additive properties and corrosion resistance. Therefore, it cause actively generate an oxide film mainly composed of Cr 2 0 3 on the inner surface of the M base alloy tube in the present invention.
- Elution of M from ⁇ surface of M based alloy tube in high temperature water environments Cr 2 0 3 Is mainly affected by the thickness of the coating.
- the thickness of the active Cr 2 0 3 principal film against M elution prevention is 170 ⁇ 1200mn. At a thickness of less than 170 nm, the film ruptures in a relatively short time and Ni begins to elute. On the other hand, if it exceeds 1200 nm, cracks tend to occur in the film during bending and the like. ⁇ Tsu Te, the thickness of the Cr 2 0 3 principal coating is suitably 170 to 1200 nm.
- the upper limit of the total thickness of the oxide film is set to 1500 nm.
- the minimum value of the total thickness is 180 nm, which is the sum of the desirable lower limit of the thickness of the first layer and the desirable lower limit of the second layer described below.
- the total thickness of the oxide film is the distance (L) from the position where the relative intensity of oxygen (0) is half of the maximum value in Fig. 6 (the position indicated by the broken line in Fig. 6) to the left end of Fig. 6.
- the thickness (L is the thickness of the first layer obtained by subtracting the thickness (L 2 ) of the following second layer from this L.
- the second layer is an oxide film mainly composed of MnCr 2 0 4.
- the MnCr 2 0 4 main layer that generates by Mn contained in the base material from diffusing to the outer layer.
- Mn has lower free energy of oxide formation than Cr and is stable under high oxygen partial pressure. Therefore, Cr 2 0 3 is produced preferentially in the vicinity of the vicinity of the base material, MnCr 2 0 4 is generated in the outer layer. Not become oxide of Mn alone is MnCr 2 0 4 is stable in this environment, and Cr amount is sufficient but whether et. Ni and Fe also have low oxide generation energy, but do not grow on such a layered oxide film due to the slow diffusion rate.
- MnCr 2 O 3 film is protected in use environment by MnCr 2 0 4. Also, MnCr 2 O 4, even if the Cr 2 0 3 film has been Yabu ⁇ for some reason restoration of Cr 2 0 3 film is promoted by exist.
- the film of MnCr 2 0 4 is present in a thickness of about. 10 to 200 nm in order to obtain such an effect Is desirable.
- the Mn content in the base material can positively generate MnCr 2 O 4 .
- excessively increasing Mn adversely affects corrosion resistance and increases manufacturing costs. Therefore, as described above, it is desirable that the Mn content of the base material be 0.1 to 1.0 ° / 0 . Particularly desirable is 0.20 to 0.40%.
- the M-base alloy tube to which the present invention is applied is usually prepared by melting a Ni-base alloy having a predetermined chemical composition into an ingot and then performing a hot working-annealing process, or a hot working-cold working. Manufactured in one annealing step. Further, in order to improve the corrosion resistance of the base material, the above-mentioned TT treatment may be applied.
- the heat treatment method of the present invention may be performed after the above-described annealing, or may be performed together with the annealing. If annealing is also performed, it is not necessary to add a heat treatment step for forming an oxide film in addition to the conventional manufacturing steps, and the manufacturing cost is not increased.
- annealing is also performed, it is not necessary to add a heat treatment step for forming an oxide film in addition to the conventional manufacturing steps, and the manufacturing cost is not increased.
- the TT treatment when the TT treatment is performed after the annealing, this may be performed also as the heat treatment for forming the oxide film.
- both the annealing and the TT treatment may be the treatment for forming an oxide film.
- the ingot is hot forged into a billet, then made into a raw tube by the hot extrusion pipe manufacturing method, and the raw tube is cold-rolled by a cold bilger mill to an outer diameter of 23.0 mm and a wall thickness of 1.4 mm.
- Draw tube for drawing Next, the drawing tube was annealed in a hydrogen atmosphere at 1100 ° C, and then manufactured by a cold drawing method.
- the finished product was a tube with an outer diameter of 16.0imn, a wall thickness of 1.0mm, and a length of 18000mm (section reduction: 50%).
- each tube is washed with an aqueous degreasing solution and rinse water, the inner surface is further washed with acetone, and the two-layer oxide film is formed on the inner surface.
- the samples were subjected to a heat treatment test under the conditions shown in Table 2. Atmospheric gas was supplied into the tube by the method shown in Fig. 3 (21 tubes were treated simultaneously). However, in Test No. 12, the header 2 was arranged on the rear end side of the tube, and the atmosphere gas was supplied in a direction opposite to that of the method of the present invention. In addition, the supply amount of the atmospheric gas was set to 7 Nm 3 Zh in total in 21 cases. table 1
- Specimens were collected from each tube after heat treatment, and the oxide film formed on the inner surface was examined by SIMS analysis.
- the test piece was subjected to a dissolution test as it was to analyze the ion dissolution amount.
- the amount of M ions dissolved in pure water was measured using an autoclave.
- pure water was sealed on the inner surface of the test piece using a Ti lock to prevent the test solution from being contaminated by ions eluted from the jig and the like.
- the test temperature was 320 ° C, and immersed in pure water for 1000 hours.
- the solution was analyzed by high frequency plasma dissolution (dcp) to determine the amount of Ni ions eluted.
- dcp high frequency plasma dissolution
- the M elution amount of Test Nos. 1 to 7 subjected to the heat treatment according to the method of the present invention is extremely small in the range of 0.01 to 0.03 ppm.
- the supply method of the atmosphere gas is the method of the present invention, but any of the test numbers 8 to 11 of the comparative examples in which any of the dew point of the atmosphere gas, the heat treatment temperature and the time is out of the conditions specified in the present invention.
- the elution amount of M was 0.29 to 0.93 ppm.
- the amount of M eluted in Test No. 12 in which the supply direction of the atmospheric gas was reverse to that of the present invention was 0.17 ppm. .
- an oxide film having a two-layer structure that suppresses the elution of M in a high-temperature pure water environment can be reliably and efficiently generated on the inner surface, so that it can be used as a reactor structural member.
- Suitable high quality Ni-based alloy tubes can be provided at low cost.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Heat Treatment Of Articles (AREA)
- Metal Extraction Processes (AREA)
Description
Claims
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
KR1020037013399A KR100567679B1 (ko) | 2002-02-13 | 2003-02-12 | 니켈 베이스 합금관의 열처리 방법 |
EP03703337A EP1475451B1 (en) | 2002-02-13 | 2003-02-12 | METHOD FOR HEAT TREATING Ni BASE ALLOY PIPE |
AU2003207059A AU2003207059A1 (en) | 2002-02-13 | 2003-02-12 | METHOD FOR HEAT TREATING Ni BASE ALLOY PIPE |
US10/681,117 US7037390B2 (en) | 2002-02-13 | 2003-10-09 | Method of heat treatment for Ni-base alloy tube |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
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JP2002-35878 | 2002-02-13 | ||
JP2002035878A JP3960069B2 (ja) | 2002-02-13 | 2002-02-13 | Ni基合金管の熱処理方法 |
Related Child Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US10/681,117 Continuation US7037390B2 (en) | 2002-02-13 | 2003-10-09 | Method of heat treatment for Ni-base alloy tube |
Publications (1)
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WO2003069011A1 true WO2003069011A1 (fr) | 2003-08-21 |
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PCT/JP2003/001451 WO2003069011A1 (fr) | 2002-02-13 | 2003-02-12 | Procede de traitement thermique d'une conduite a base d'alliage de nickel |
Country Status (6)
Country | Link |
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US (1) | US7037390B2 (ja) |
EP (1) | EP1475451B1 (ja) |
JP (1) | JP3960069B2 (ja) |
KR (1) | KR100567679B1 (ja) |
AU (1) | AU2003207059A1 (ja) |
WO (1) | WO2003069011A1 (ja) |
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JP4304499B2 (ja) * | 2004-10-13 | 2009-07-29 | 住友金属工業株式会社 | 原子力プラント用Ni基合金材の製造方法 |
US20100032061A1 (en) * | 2005-02-04 | 2010-02-11 | Hiroyuki Anada | METHOD FOR MANUFACTURING A Ni-BASED ALLOY ARTICLE AND PRODUCT THEREFROM |
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EP2397573B1 (en) * | 2009-02-16 | 2017-09-20 | Nippon Steel & Sumitomo Metal Corporation | Method for producing metal tube |
US10170207B2 (en) | 2013-05-10 | 2019-01-01 | Thorium Power, Inc. | Fuel assembly |
US10192644B2 (en) | 2010-05-11 | 2019-01-29 | Lightbridge Corporation | Fuel assembly |
WO2011143172A1 (en) | 2010-05-11 | 2011-11-17 | Thorium Power, Inc. | Fuel assembly with metal fuel alloy kernel and method of manufacturing thereof |
JP2010270400A (ja) * | 2010-07-21 | 2010-12-02 | Sumitomo Metal Ind Ltd | 原子力プラント用蒸気発生器管 |
KR101589008B1 (ko) | 2010-08-26 | 2016-01-28 | 신닛테츠스미킨 카부시키카이샤 | Cr함유 오스테나이트 합금관 및 그 제조 방법 |
DE102011054718B4 (de) * | 2011-10-21 | 2014-02-13 | Hitachi Power Europe Gmbh | Verfahren zur Erzeugung einer Spannungsverminderung in errichteten Rohrwänden eines Dampferzeugers |
JP5418623B2 (ja) * | 2012-03-13 | 2014-02-19 | 新日鐵住金株式会社 | 管内面皮膜厚さ計測方法および計測装置 |
JP6292311B2 (ja) | 2014-09-29 | 2018-03-14 | 新日鐵住金株式会社 | Ni基合金管 |
US20200087759A1 (en) * | 2016-06-28 | 2020-03-19 | Nippon Steel & Sumitomo Metal Corporation | Austenitic Alloy Material and Austenitic Alloy Pipe |
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- 2003-02-12 AU AU2003207059A patent/AU2003207059A1/en not_active Abandoned
- 2003-02-12 WO PCT/JP2003/001451 patent/WO2003069011A1/ja active Application Filing
- 2003-02-12 EP EP03703337A patent/EP1475451B1/en not_active Expired - Lifetime
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Also Published As
Publication number | Publication date |
---|---|
EP1475451A1 (en) | 2004-11-10 |
US7037390B2 (en) | 2006-05-02 |
JP2003239060A (ja) | 2003-08-27 |
EP1475451B1 (en) | 2012-08-22 |
AU2003207059A1 (en) | 2003-09-04 |
US20040103963A1 (en) | 2004-06-03 |
KR100567679B1 (ko) | 2006-04-04 |
JP3960069B2 (ja) | 2007-08-15 |
KR20030090734A (ko) | 2003-11-28 |
EP1475451A4 (en) | 2010-08-25 |
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