WO2004015154A1 - 高温強度に優れたマルテンサイト系酸化物分散強化型鋼およびその製造方法 - Google Patents
高温強度に優れたマルテンサイト系酸化物分散強化型鋼およびその製造方法 Download PDFInfo
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- WO2004015154A1 WO2004015154A1 PCT/JP2003/010081 JP0310081W WO2004015154A1 WO 2004015154 A1 WO2004015154 A1 WO 2004015154A1 JP 0310081 W JP0310081 W JP 0310081W WO 2004015154 A1 WO2004015154 A1 WO 2004015154A1
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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
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1084—Alloys containing non-metals by mechanical alloying (blending, milling)
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0207—Using a mixture of prealloyed powders or a master alloy
- C22C33/0228—Using a mixture of prealloyed powders or a master alloy comprising other non-metallic compounds or more than 5% of graphite
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Definitions
- the present invention relates to a martensite-based oxide dispersion strengthened (ODS) steel excellent in high-temperature strength and a method for producing the same.
- ODS martensite-based oxide dispersion strengthened
- the martensitic oxide dispersion strengthened steel of the present invention can be preferably used as a material for a fast breeder reactor fuel cladding tube, a first wall material for a fusion reactor, a material for thermal power generation, and the like, which require excellent high-temperature strength and creep strength. . Background technology
- Austenitic stainless steel has been used as a component of nuclear reactors, especially fast reactors, which require excellent high-temperature strength and neutron irradiation resistance.However, irradiation resistance such as swelling resistance is limited. . On the other hand, although martensitic stainless steel has excellent irradiation resistance, it has the disadvantage of low high-temperature strength.
- a martensitic oxide dispersion strengthened steel was developed as a material having both irradiation resistance characteristics and high-temperature strength characteristics, and Ti was added to this steel to finely disperse the oxide dispersed particles.
- a structure in which oxide particles are finely divided and uniformly and densely dispersed is obtained, and as a result, a martensitic oxide dispersion-strengthened steel in which excellent high-temperature strength is developed, and The purpose was to provide a manufacturing method.
- the present inventors have excess oxygen content EX 0 in oxide dispersion strengthened martensitic steel (minus the amount of oxygen in Y 2 0 3 from the amount of oxygen in steel) has a close relationship with the high-temperature strength Focusing on this fact, they have found that by adjusting the amount of excess oxygen in the steel to a certain range, the high-temperature strength can be surely improved, and the present invention has been completed.
- the martensitic oxide dispersion-strengthened steel excellent in high-temperature strength of the present invention has a C content of 0.05 to 0.25%, a Cr of 8.0 to 12.0%, There 0. 1 ⁇ 4.
- 0%, T i is 0. 1 ⁇ 1.
- 0%, Y 2 0 3 is 0.1 to 0.5%, the balance being F e and inevitable impurities Upsilon 2 0 3 particles
- the amount of Ti in the steel is adjusted within the range of 0.1 to 1.0% so that the excess oxygen amount E ⁇ in the steel falls within a predetermined range.
- the dispersed Y 2 0 3 particles can be fine densified, resulting in that Do is possible to improve high-temperature short-time strength and high temperature for a long time strength of the steel.
- the present invention is by treating the mechanical alloying element powders or alloy powders and Y 2 ⁇ 3 powder in A r atmosphere, C is 0. 0 5 ⁇ 0. 2 5%, C r is 8. 0 ⁇ :. L 2. 0%, W is 0. 1 ⁇ 4 0%, T i is 0.:!. ⁇ 1. 0% , Y 2 ⁇ 3 is 0.1 to 0 5%, with the remainder being F a process for the preparation of e and oxide dispersion strengthened martensitic steel unavoidable impurities or Ranaru Y 2 ⁇ 3 particles are dispersed, the purity 9 9.9 9 9 9% or more of a r gas as the a r atmosphere By using, the excess oxygen amount E x ⁇ in the steel
- the invention further elemental powder or alloy powder and Y 2 0 3 powder A r Kiri ⁇
- C is 0.05-0.25%
- Cr is 8.0-12.0%
- W is 0.1-4.0%
- 1 ⁇ is 0.. 1 to 1.
- martensite-based oxide dispersion balance are dispersed F e and inevitable impurities or Ranaru Y 2 ⁇ 3 particles
- the amount of excess oxygen ⁇ X ⁇ in the steel is reduced by reducing the stirring energy during mechanical alloying treatment and suppressing oxygen entrapment during stirring.
- the present invention is by treating the mechanical alloying elemental powders or alloy powders and Upsilon 2 0 3 powder to A r atmosphere, C is 0. 0 5 ⁇ 0. 2 5%, C r is 8. 0 to 12.0%, W is 0.1 to 4.0%, T i is 0.1 to 1.0%, Y 2 O 3 is 0.1 to 0.5%, the balance is Fe and a method for producing the inevitable consists not of pure product Y 2 ⁇ 3 martensite-based particles are dispersed oxide dispersion strengthening type steel, a metal Upsilon powder or F e 2 Y powder in place of the Upsilon 2 0 3 powder The amount of excess oxygen in the steel ⁇ ⁇ ⁇ ⁇ ⁇
- FIG. 1 is a graph showing the results of a 700 ° C. creep rupture test of each trial material.
- Fig. 2 is a graph showing the results of the tensile test at 700 and 800 ° C for the test materials MM11, T5, and MM13.
- b) is the tensile strength.
- Fig. 3 shows the experimental materials MM11, T14, MM13, It is a transmission electron microscope photograph of T3.
- Figure 4 shows transmission electron micrographs of the test materials Nos. 4 and 5 with 0.5% added.
- Fig. 5 is a graph showing the relationship between the Ti content and the excess oxygen amount E x ⁇ of each test material, where the hatched portion indicates that the oxide dispersed particles can be refined EX ⁇ ⁇ 0.46 XT i Is the region that satisfies
- Figure 6 is a graph showing the relationship between the target excess oxygen content of each trial material and the measured value.
- Figure 7 is a graph showing the results of a 700 ° C high temperature creep rupture test of each prototype material.
- A shows the creep rupture test results, and
- B shows the dependence of the 1000 hour rupture stress on the excess oxygen content. Shown respectively.
- Figure 8 is a graph showing the T i ⁇ X (E x ⁇ / T i atomic ratio) dependence of the results of the 700 ° C high-temperature creep test of each prototype material, where (a) is the estimate for 100 hours. (B) shows the T i Ox dependence of the breaking strength, and (b) shows the T i Ox dependence of the tensile strength.
- FIG. 9 is a graph plotting the relationship between the Ti addition amount and the excess oxygen amount EX 0 of each trial material.
- Cr is an important element for ensuring corrosion resistance, and if it is less than 8.0%, the deterioration of corrosion resistance becomes remarkable. If it exceeds 12.0%, the toughness and ductility may be reduced. For this reason, the Cr content is set to 8.0 to 12.0%.
- C is considered to be a stable tissue when the Cr content is 8.0-12.0%.
- This martensite structure is obtained by normalizing at 1000 to 115 ° C + tempering heat treatment at 700 to 800 ° C.
- more carbides C content is increased (M 23 C 6, M 6 C , etc.) often becomes a high temperature strength is precipitation amount is increased, processability is deteriorated and large amount containing from 0.2 5%. For this reason, the C content is set to 0.05 to 0.25%.
- W is an important element that forms a solid solution in the alloy and improves the high-temperature strength, and is added in an amount of 0.1% or more. If the W content is increased, the creep rupture strength is improved by the solid solution strengthening action, carbide (M 23 C 6 , M 6 C, etc.) precipitation strengthening action, and intermetallic compound precipitation strengthening action. If it exceeds, the amount of ⁇ ferrite increases and the strength also decreases. For this reason, the W content is 0.1 to 4.0%.
- T i plays an important role in the dispersion strengthening of Y 2 0 3, by reacting with Upsilon 2 0 3 to form a Y 2 T i 2 0 7 or the composite oxide of Y 2 T I_ ⁇ 5, acid Has the function of refining the oxide particles. This effect tends to be saturated when the Ti content exceeds 1.0%, and when the Ti content is less than 0.1%, the miniaturization effect is small. For this reason, the Ti content is 0.1-1.0%.
- Y 2 0 3 is Ru important additive der to improve the high-temperature strength by dispersion strengthening.
- the content is less than 0.1%, the effect of dispersion strengthening is small and the strength is low.
- the content exceeds 0.5%, curing is remarkable and a problem occurs in workability. For this reason, the content of Upsilon 2 ⁇ 3 and 0.1 to 0.5%.
- oxide dispersion strengthened martensitic steel of the invention may be incorporated so that the target composition and the components described above with elemental powders or alloy powders and Upsilon 2 0 3 powder, the powder mixture Alloying process in which a high-energy attritor is charged and stirred in an Ar atmosphere (mechanical After alloying, the obtained alloyed powder is filled into soft iron capsules, degassed, sealed, heated to 115 ° C, and hot-extruded to solidify the alloyed powder.
- the method can be adopted.
- Ar gas purity in the Ar atmosphere at the time of mechanical alloying treatment is usually 99.9%, but when such high purity Ar gas is used.
- mixing of oxygen into steel is inevitable, albeit slightly.
- the use of ultrapure Ar gas having a purity of 99.999% or more can reduce the incorporation of oxygen into steel, and as a result, Can be adjusted so that the amount of excess oxygen in a given range falls within a predetermined range.
- the agitation energy in the attritor is reduced and oxygen entrapment during agitation is suppressed.
- This also allows the amount of excess oxygen in the steel to be reduced, and can be adjusted to fall within a predetermined range.
- Specific measures to reduce the stirring energy include lowering the rotation speed of the stirring device (agitator) installed inside the attritor, or using a pin attached to the stirring device. For example, it is possible to shorten the length.
- Table 1 summarizes the target composition, compositional characteristics, and production conditions of the martensitic oxide dispersion strengthened steel prototype.
- MM 1 1, MM 1 3, T 1 4 and E 5 as the composition is a basic composition, T 3 is MM 1 3, T 1 unstable oxide 4 basic composition of (F e 2 03)
- T4 is a sample with intentionally increased excess oxygen
- T4 is a sample with increased Ti added to the basic composition of MM13, T14
- T5 is an unstable oxide (F e 2 0 3 ) was added to increase the amount of excess oxygen and to increase the amount of Ti added.
- the “stirring energy” in the manufacturing conditions (mechanical alloying treatment conditions) in Table 1 refers to the pin of a stirrer installed inside the agitator for stirring the raw material powder during the mechanical alloying treatment.
- "Stirring energy: large” indicates that a pin of normal length was used, and "stirring energy :: small” indicates that a pin shorter than usual was used. That is, even if the rotation speed of the stirrer is the same, when the pin is short, the amount of oxygen involved during stirring is reduced because the stirring energy of the pin having the normal length is small. Only the MM 11 in Table 1 used a stirrer with short pins and low stirring energy, but used a stirrer with high stirring energy in all other cases having pins of normal length.
- T14, T3, ⁇ 4, ⁇ 5, ⁇ 5 of the hot-extruded rods obtained above were normalized (1500 ° CX lhr ⁇ air-cooled) + tempered (800 ° CX A final heat treatment consisting of 1 hr ⁇ air cooling) was performed to finish the rod.
- MM11 and MM13 are processed into a tube and then subjected to a final heat treatment consisting of normalizing (1500 ° CX 1 hr ⁇ air cooling) + tempering (800 ° CX lhr ⁇ air cooling). did.
- the pipe making process was performed by first cold rolling + softening heat treatment-second cold rolling + softening heat treatment-third cold rolling + softening heat treatment ⁇ fourth cold rolling + final heat treatment.
- the bar specimens (T14, ⁇ 3, ⁇ 4, ⁇ 5, ⁇ 5) thus obtained were subjected to a creep rupture test at 700 ° C for the tubular specimens (MM11, MM13).
- the results are shown in the graph of FIG.
- the rod-shaped test pieces (T14, ⁇ 3, ⁇ 4, ⁇ 5, ⁇ 5) were subjected to a test with a gauge section of 6 mm in diameter ⁇ 3 Omm in length. From this graph, it can be seen that the creep rupture strength of each of the test materials MM11, T4, ⁇ 5 and ⁇ 5 is superior to the other test materials. Since the martensitic oxide dispersion-strengthened steel has an isotropic structure and has no anisotropy in strength, it is possible to compare a tubular specimen with a rod-shaped specimen.
- the arrow in the graph of Fig. 1 indicates that the rupture time has not yet broken after the elapse of the test time, and that the rupture time can be extended.
- the graph of Fig. 2 shows the results of tensile strength tests performed on the test materials MM13, MM11, and T5 at test temperatures of 700 ° C and 800 ° C.
- MM11 and MM13 tubular test pieces similar to those used in the cleave rupture test were used.
- the circumferential strength is important, so the diameter is 6.9111111 and the wall thickness is 0.4 mm (MM 13) or the diameter.
- a gage part was provided in the circumferential direction of a 8.5 mm X wall thickness 0.5 mm (MM 11) tubular test piece, and a circumferential tensile strength test (ring tensile strength test) was performed.
- the length of the gauge part was 2 mm and the width was 1.5 mm. Since T5 is a round bar material, a gauge portion having a diameter of 6 mm and a length of 30 mm was provided, and an axial tensile strength test was performed. Since the martensitic oxide dispersion strengthened steel has an isotropic structure and has no anisotropy in strength, the results of the tensile strength test of MM13 and MM11 and the tensile strength test of T5 Can be compared directly. The strain rate was set between 0.1% / min and 0.1% / min according to JISZ2241.
- the prototypes of MM11 and T5 are superior in both 0.2% resistance to heat and tensile strength as compared with the prototypes of the basic composition of MM13.
- Fig. 3 shows the results of transmission electron microscopy observations of each of the test materials that had been subjected to heat treatment (150 ° C x 1 hr) as a final heat treatment on the hot-extruded rod obtained above. This is shown in Fig. 4 (a trial material with 0.5% Ti added) and Fig. 4 (a trial material with 0.5% Ti added).
- the trial material of MM 11 has a finer density of Y 2 ⁇ 3 particles, and in FIG. 4, ⁇ 4 and ⁇ In each of the cases (5), ( 2) and ( 3) particles have been finely densified.
- T 3 test material of basic composition T i content 0.2 1%; excess oxygen content 0.1 4 7> 0.46 XT i
- T5 trial material Ti content 0.46%; excess oxygen 0.16 7 ⁇ 0.46 XT i
- the excess oxygen content can be reduced to less than 0.46 XT i%
- the dispersed Y 2 ⁇ 3 particles can be made finer and denser than T 3, and creep rupture Strength can also be improved.
- the martensitic oxide dispersion-strengthened steel whose Ti content in the steel was adjusted so that the excess oxygen content ⁇ 0.46 XT i within the range of 0.1 to 0.5%, It can be seen that the Y 2 ⁇ 3 particles are finely densified and have excellent high-temperature strength.
- the MM13 trial material with basic composition (excess oxygen content 0.13 7> 0.46 XT i) and MM11 trial material with the same composition (excess oxygen content 0.07 x 0.46 XT i)
- MM 1 1 test material is, MM 1 3 can fine densified dispersion Y 2 ⁇ 3 particles as compared with the test material, it is possible to improve the cleaved breaking strength and tensile strength.
- Table 3 summarizes the target composition and target excess oxygen content of the prototype materials. E5 and T3 in Table 3 are the same as the trial materials in Table 1.
- E 5 is a standard material of the base composition with the addition of Upsilon 2 0 3 powder, and the target excess oxygen content 0.08% and.
- Y l, ⁇ 2, ⁇ 3 is obtained by adding a metal Upsilon powder instead of Upsilon 2 0 3 powder. That, Y 1 is by adding a metal ⁇ powder, and the target excess oxygen content is 0% without the addition of unstable oxide (F e 2 0 3).
- Y 2 and Y 3 is a metal Y powder F e 2 ⁇ 3 powder powder were added respectively 0.1 5% Oyobi 0.2 9% with the target excess oxygen content their respective 0.0 5% And 0.09%.
- T 3 is increased excess oxygen content by addition of F e 2 0 3 powder to the base composition of E 5, E 7.
- the trial materials Yl, ⁇ 2, ⁇ 3, and ⁇ 7 are all hot-extruded rods according to the same manufacturing method and manufacturing conditions as MM13 described above, and the final heat treatment is furnace cooling heat treatment (1050 ° 1111: ⁇ 600 (30 ° C / hr)) or normalizing (105 ° CXlhr-air cooling) + tempering (780 ° CXlhr ⁇ air cooling) Heat treatment was performed.
- Table 4 summarizes the results of component analysis of each prototype material.
- Figure 6 is a graph showing the relationship between the target excess oxygen content of each trial material and the measured value.
- the target excess oxygen content is, F e 2 ⁇ 3 powder and Y 2 ⁇ 3 powder other oxygen written Chi lifting from about 0.04% to the raw material powder, about 0.04 in the mechanical alloying treatment %, With a total of 0.08% oxygen contamination.
- the amount of impurity oxygen in the raw material powder (Fe, Cr, W, T i) and the amount of oxygen mixed in the mechanical alloying process are the same as those of the raw material powder and the chemical components after the mechanical alloying process. It is a value obtained by measurement by the melting method.
- the target value and the measured value of the excess oxygen content is also almost coincide with a low amount of less than 1% 0.
- Y 2 0 3 is formed by the combined addition of the metal Y and F e 2 ⁇ 3, 0 It can be seen that the excess oxygen can be controlled in a low range of 1% or less.
- Figure 7 shows the results of a 700 ° C high-temperature creep test of each test material, (a) shows the results of the creep rupture test, and (b) shows the dependence of the 1000-hour rupture stress on the excess oxygen content. It is a graph shown.
- the high-temperature creep strength peaked in test materials E5 and E7 where the excess oxygen content was around 0.08%, and the strength tended to decrease around 0.08%. From this fact, it is effective to adjust the excess oxygen amount at a low level near 0.08% in order to improve the high-temperature strength.
- Figure 8 shows the T i Ox (E ⁇ / T i atomic ratio) dependence of the results of the 700 ° C high-temperature creep test of each test material, and (a) shows the T i of the estimated breaking stress for 1000 hours.
- (B) is a graph showing the Ti Ox dependency of the tensile strength. From these graphs, T i Ox is 0.65 to 1.4. It can be seen that the creep strength and the tensile strength peak in the range (shaded area).
- Figure 9 is a graph plotting the relationship between the amount of Ti added and the amount of excess oxygen Ex ⁇ in each trial material.
- the creep strength peaks [0.65 XTi (atomic%) ⁇
- the range of ⁇ ⁇ (atomic%)-1.4 XT i (atomic%)] is indicated by oblique lines.
- the above relationship expressed in atomic% is converted to mass%, it is expressed as [0.22 X Ti (mass%) x E xO (mass%) ⁇ 0.464 X Ti (mass%)].
- T i forms a Y 2 0 3 powder and composite oxide
- T i added amount exceeds 0% 1.
- the excess oxygen amount is set to [0.22 XT i (mass%) ⁇ EXO (mass%) ⁇ 0.464 XT i ( Mass%)], that is, within the hatched range in the graph of FIG. 9, a martensitic oxide dispersion-strengthened steel excellent in high-temperature strength can be manufactured.
- the Ti content is adjusted so that the excess oxygen amount falls within a predetermined range by focusing on the excess oxygen amount in the steel, or during the manufacturing process.
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Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
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EP03784584A EP1528112B1 (en) | 2002-08-08 | 2003-08-07 | Dispersed oxide reinforced martensitic steel excellent in high temperature strength and method for production thereof |
US10/502,257 US7037464B2 (en) | 2002-08-08 | 2003-08-07 | Dispersed oxide reinforced martensitic steel excellent in high temperature strength and method for production thereof |
DE60329395T DE60329395D1 (de) | 2002-08-08 | 2003-08-07 | Mit dispergiertem oxid verstärkter martensitischer stahl mit hervorragender hochtemperaturfestigkeit und herstellungsverfahren dafür |
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JP2002231780 | 2002-08-08 | ||
JP2002-231780 | 2002-08-08 | ||
JP2003276554A JP4413549B2 (ja) | 2002-08-08 | 2003-07-18 | 高温強度に優れたマルテンサイト系酸化物分散強化型鋼の製造方法 |
JP2003-276554 | 2003-07-18 |
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WO2004015154A1 true WO2004015154A1 (ja) | 2004-02-19 |
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US (1) | US7037464B2 (ja) |
EP (1) | EP1528112B1 (ja) |
JP (1) | JP4413549B2 (ja) |
CN (1) | CN100357469C (ja) |
DE (1) | DE60329395D1 (ja) |
WO (1) | WO2004015154A1 (ja) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN1316049C (zh) * | 2005-04-04 | 2007-05-16 | 北京科技大学 | 一种用化学浸润法制造氧化物弥散强化铁素体型合金的方法 |
CN108950357A (zh) * | 2018-07-27 | 2018-12-07 | 中南大学 | 一种多尺度多相弥散强化铁基合金及其制备和表征方法 |
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Publication number | Priority date | Publication date | Assignee | Title |
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JP3753248B2 (ja) * | 2003-09-01 | 2006-03-08 | 核燃料サイクル開発機構 | 残留α粒を有する高温強度に優れたマルテンサイト系酸化物分散強化型鋼の製造方法 |
AT8975U1 (de) * | 2006-02-27 | 2007-03-15 | Plansee Se | Poröser körper |
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US9303295B2 (en) * | 2012-12-28 | 2016-04-05 | Terrapower, Llc | Iron-based composition for fuel element |
US10157687B2 (en) | 2012-12-28 | 2018-12-18 | Terrapower, Llc | Iron-based composition for fuel element |
JP6270197B2 (ja) * | 2013-06-13 | 2018-01-31 | 国立研究開発法人日本原子力研究開発機構 | 酸化物分散強化型焼き戻しマルテンサイト鋼の製造方法 |
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CN113215480B (zh) * | 2021-04-29 | 2021-12-14 | 西安建筑科技大学 | 一种多尺度粒子强化低活化钢及其制备方法 |
CN113462949B (zh) * | 2021-07-20 | 2022-01-07 | 天津大学 | 一种基于粉末冶金工艺制备弥散氧化物强化型钢的方法 |
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Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4963200A (en) * | 1988-04-25 | 1990-10-16 | Doryokuro Kakunenryo Kaihatsu Jigyodan | Dispersion strengthened ferritic steel for high temperature structural use |
EP0949346A1 (fr) * | 1998-04-07 | 1999-10-13 | Commissariat A L'energie Atomique | Procédé de fabrication d'un alliage ferritique-martensitique renforce par dispersion d'oxydes |
Family Cites Families (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5209772A (en) * | 1986-08-18 | 1993-05-11 | Inco Alloys International, Inc. | Dispersion strengthened alloy |
US5167728A (en) * | 1991-04-24 | 1992-12-01 | Inco Alloys International, Inc. | Controlled grain size for ods iron-base alloys |
JPH0518897A (ja) | 1991-07-15 | 1993-01-26 | Fuji Electric Co Ltd | コバルト合金の組成分析方法 |
DE69314438T2 (de) * | 1992-11-30 | 1998-05-14 | Sumitomo Electric Industries | Niedrig legierter Sinterstahl und Verfahren zu dessen Herstellung |
SE9602835D0 (sv) * | 1996-07-22 | 1996-07-22 | Hoeganaes Ab | Process for the preparation of an iron-based powder |
JP4975916B2 (ja) * | 2001-09-21 | 2012-07-11 | 株式会社日立製作所 | 高靭性高強度フェライト鋼とその製法 |
-
2003
- 2003-07-18 JP JP2003276554A patent/JP4413549B2/ja not_active Expired - Fee Related
- 2003-08-07 US US10/502,257 patent/US7037464B2/en not_active Expired - Lifetime
- 2003-08-07 DE DE60329395T patent/DE60329395D1/de not_active Expired - Lifetime
- 2003-08-07 CN CNB038055724A patent/CN100357469C/zh not_active Expired - Fee Related
- 2003-08-07 EP EP03784584A patent/EP1528112B1/en not_active Expired - Fee Related
- 2003-08-07 WO PCT/JP2003/010081 patent/WO2004015154A1/ja active Application Filing
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4963200A (en) * | 1988-04-25 | 1990-10-16 | Doryokuro Kakunenryo Kaihatsu Jigyodan | Dispersion strengthened ferritic steel for high temperature structural use |
EP0949346A1 (fr) * | 1998-04-07 | 1999-10-13 | Commissariat A L'energie Atomique | Procédé de fabrication d'un alliage ferritique-martensitique renforce par dispersion d'oxydes |
Non-Patent Citations (1)
Title |
---|
See also references of EP1528112A4 * |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN1316049C (zh) * | 2005-04-04 | 2007-05-16 | 北京科技大学 | 一种用化学浸润法制造氧化物弥散强化铁素体型合金的方法 |
CN108950357A (zh) * | 2018-07-27 | 2018-12-07 | 中南大学 | 一种多尺度多相弥散强化铁基合金及其制备和表征方法 |
Also Published As
Publication number | Publication date |
---|---|
DE60329395D1 (de) | 2009-11-05 |
JP4413549B2 (ja) | 2010-02-10 |
EP1528112B1 (en) | 2009-09-23 |
EP1528112A1 (en) | 2005-05-04 |
EP1528112A4 (en) | 2006-09-13 |
US7037464B2 (en) | 2006-05-02 |
JP2004084071A (ja) | 2004-03-18 |
US20050084405A1 (en) | 2005-04-21 |
CN100357469C (zh) | 2007-12-26 |
CN1639369A (zh) | 2005-07-13 |
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