KR20150100204A - Reduced activation oxide dispersion strengthened steel with excellent tensile and creep strengths and manufacturing method thereof - Google Patents
Reduced activation oxide dispersion strengthened steel with excellent tensile and creep strengths and manufacturing method thereof Download PDFInfo
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- KR20150100204A KR20150100204A KR1020140021714A KR20140021714A KR20150100204A KR 20150100204 A KR20150100204 A KR 20150100204A KR 1020140021714 A KR1020140021714 A KR 1020140021714A KR 20140021714 A KR20140021714 A KR 20140021714A KR 20150100204 A KR20150100204 A KR 20150100204A
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Abstract
Description
More particularly, the present invention relates to a Fe-Cr-W-based low-activation ferrite / martensitic steel as a basic composition, It is possible to increase the amount of addition of titanium (Ti) and zirconium (Zr) as alloying elements and to strengthen the dispersion by the fine dispersion of yttria (Y 2 O 3 ) And a method for producing the same.
Nuclear fusion advanced countries such as the United States, Japan, and Europe, including Korea, are actively developing future fusion systems. Fusion blanket is one of the important components that confine ultra high temperature plasma to convert heat energy and propagate tritium. For this reason, the structural material of the blanket is required to have excellent mechanical properties in an extreme environment of high temperature / high radiation as well as low emissivity.
To this end, a low radiated ferrite / martensitic steel has been developed by replacing the constituent element of the existing heat resistant steel with a low radioactive element and controlling its chemical composition. The blanket structure for the international fusion experiment It will be used as a material. However, in the case of the fusion blanket for commercialization, the high temperature operation of 550-700 ° C and the high radiation superheat operation of 100 dpa or more are assumed, and the conventional low radiated ferrite / martensitic steel has a rapid creep strength at a high temperature of 600 ° C or higher And irradiation embrittlement due to high radiation has been pointed out as a problem in using for a long period of time.
Oxide Dispersion Strengthened (ODS) steel is an alloy that finely disperses oxide particles having excellent thermal stability in a matrix structure to a nanometer scale, and has excellent creep strength at a high temperature compared with conventional ferrite / martensitic steel Recently, it has attracted attention as a material of core structural parts (nuclear fuel cladding tube, duct, wire, seal stopper, etc.) and structural parts for thermal power generation (gas turbine blade, shaft, etc.) of nuclear power system such as sodium cooling high speed furnace. However, since conventional oxide-dispersed steel is developed for application to general industry or nuclear power, there is a problem in that the concept of low radiation is not considered for application as a structural component material of a fusion system.
In order to solve such problems, elements (Mo, Nb, Ni, B and the like) having excellent creep and neutron irradiation resistance and high radioactivity characteristics by neutron irradiation are excluded compared to conventional low activation ferritic / martensitic steel It is necessary to develop a new low-NOx dispersion strengthened steel composed of low-radioactive elements.
Disclosure of Invention Technical Problem [8] The present invention has been made in order to solve the above-mentioned problems in the prior art, and it is an object of the present invention to provide a ferrite / martensitic steel having Fe- (Cr), from 0.5 to 3 wt% of tungsten (W), from 0.5 to 3 wt% of chromium (Cr), and from 0.5 to 3 wt% of chromium (Cr), in order to apply the low- 0.1 to 0.3% by weight of tantalum, 0.01 to 0.1% by weight of tantalum, 0.01 to 0.5% by weight of titanium, 0.01 to 0.2% of zirconium and 0.1 to 0.5% of yttria (Y 2 O 3 ) %, And the remainder comprising iron (Fe) and having excellent tensile and creep strength, and a process for producing the same.
However, the technical problem to be solved by the present invention is not limited to the above-mentioned problems, and other matters not mentioned can be clearly understood by those skilled in the art from the following description.
The present invention relates to a method of manufacturing a semiconductor device, which comprises 0.05 to 0.2 wt% of carbon, 8 to 12 wt% of chromium (Cr), 0.5 to 3 wt% of tungsten (W), 0.1 to 0.3 wt% of vanadium (V) Characterized in that it comprises 0.01 to 0.5% by weight of titanium (Ti), 0.01 to 0.2% by weight of zirconium (Zr), 0.1 to 0.5% by weight of yttria (Y 2 O 3 ) The present invention provides a low activated oxide dispersion strengthened steel having excellent creep strength.
The present invention also provides a process for producing a low activated oxide dispersion strengthened steel comprising the steps of:
(a) a metal powder containing carbon (C), chromium (Cr), tungsten (W), vanadium (V), tantalum (Ta), titanium (Ti), zirconium (Zr) (Y 2 O 3 ) powders and then subjecting them to a mechanical alloying treatment to produce an alloy powder;
(b) charging the canned alloy with the mechanically alloyed alloy powder to perform a degassing treatment;
(c) hot-working the degassed alloy powder to produce an oxide dispersion-strengthened steel;
(d) cold-working the hot-worked oxide-dispersed steel.
The low activated oxide dispersion strengthened steel according to the present invention comprises 0.05 to 0.2 wt% of carbon, 8 to 12 wt% of chromium (Cr), 0.5 to 3 wt% of tungsten (W), 0.1 to 0.3 wt% of vanadium (V) (Ta) 0.01 ~ 0.1 wt.%, titanium (Ti) 0.01 ~ 0.5% by weight, zirconium (Zr) 0.01 ~ 0.2 wt%, yttria (Y 2 O 3) 0.1 ~ 0.5 wt%, and the balance portion of iron (Fe) (Blanket, divertor, etc.) materials for nuclear fusion reactors, and furthermore, core structural parts (fuel cladding, ducts, wires, A sealing cap, etc.).
1 is a flow chart schematically showing a method of manufacturing a low-activation-oxidation-dispersion-strengthened steel of the present invention.
2 is a diagram showing the results of a tensile test of conventional low-activation ferritic / martensitic steels and low-activation oxide dispersion strengthened steels according to the present invention at room temperature, 500 ° C, and 700 ° C.
3 is a graph showing the creep test results of a conventional low-radiated ferrite / martensite steel and a low-activation oxide dispersion strengthened steel according to the present invention at 550 ° C and 700 ° C.
The present inventors have conducted studies to improve the high temperature strength and creep resistance of a low radiated ferrite / martensitic steel used as a core material for a fusion reactor core. As a result, Ti), zirconium (Zr) increases the amount and yttria (Y 2 O 3) in the case of adding, Y-Ti-O and Y-Zr-O-based ultra-fine compound oxide the by conventional low radioactive ferrite formation / Martensitic steel, it was confirmed that the tensile and creep strengths were improved, and the present invention was completed on the basis thereof.
Hereinafter, the present invention will be described in detail.
The present invention relates to a method of manufacturing a semiconductor device, which comprises 0.05 to 0.2 wt% of carbon, 8 to 12 wt% of chromium (Cr), 0.5 to 3 wt% of tungsten (W), 0.1 to 0.3 wt% of vanadium (V) Characterized in that it comprises 0.01 to 0.5% by weight of titanium (Ti), 0.01 to 0.2% by weight of zirconium (Zr), 0.1 to 0.5% by weight of yttria (Y 2 O 3 ) The present invention provides a low activated oxide dispersion strengthened steel having improved creep strength.
When the content of chromium (Cr) is less than 8% by weight, corrosion resistance is deteriorated. When it exceeds 12% by weight, a martensite phase is difficult to be formed. By weight is preferable.
When the content of yttria (Y 2 O 3 ) is less than 0.1% by weight, the dispersion strengthening effect is insignificant. When the content is more than 0.5% by weight, the effect of strengthening dispersion due to the residual dispersion particles is increased, , Yttria (Y 2 O 3 ) is preferably from 0.1 to 0.5% by weight, more preferably from 0.3 to 0.4% by weight.
Tungsten (W) is a solid solution strengthening element added for high temperature strength. The content of tungsten (W) is preferably 0.5 to 3 wt%, and when the amount is less than 0.5 wt%, the effect of solid solution strengthening is insignificant, If it exceeds 3% by weight, there is a problem that the workability is lowered.
Vanadium (V) is a precipitation strengthening element that forms fine MX precipitates and is an element that improves high temperature tensile strength and creep resistance. When the content of vanadium (V) is less than 0.1% by weight, the effect is insignificant. When the content of vanadium (V) is more than 0.3% by weight, a brittle delta ferrite phase is formed.
Tantalum (Ta) is also a precipitation strengthening element that forms fine MX precipitates, which is an element that improves tensile strength and impact properties by refining prior austenite grain. When the content of tantalum (Ta) is less than 0.01% by weight, the effect is insignificant, and when the content exceeds 0.1% by weight, the mechanical properties are deteriorated.
The content of titanium (Ti) is 0.01 to 0.5% by weight are preferred, those of titanium (Ti) is in the heating process, the yttria (Y 2 O 3) and coupled to Y 2 Ti 2 O 7 and Y 2 Y, such as TiO 5 -Ti-O composite oxide is formed to contribute to the high density and fine dispersion of the oxide, whereby the strength can be improved. In the present invention, by increasing the content of titanium (Ti) compared to the conventional low radiated ferrite / martensitic steel, the tensile and creep strength due to refinement of precipitates can be improved.
The content of zirconium (Zr) is preferably from 0.01 to 0.2% by weight. The zirconium (Zr) also binds yttria (Y 2 O 3 ) to form a Y-Zr-O composite oxide, The strength characteristics can be further improved. Zirconium can also be added in the present invention to increase the amount of addition, thereby improving the tensile and creep strength due to refinement of precipitates.
Therefore, the low-activation oxide dispersion strengthened steel of the present invention can be used as a structural component material of a nuclear fusion furnace, as a blanket or as a diverter, and as a structural component material at a sodium cooling high-speed furnace to form a nuclear fuel cladding, a duct, It can be used as a stopper.
As another aspect of the present invention,
There is provided a method for manufacturing a low-activation oxide dispersion strengthened steel excellent in tensile and creep strength, comprising the steps of:
(a) a metal powder containing iron (Fe), carbon (C), chromium (Cr), tungsten (W), vanadium (V), tantalum (Ta), titanium (Ti), and zirconium (Y 2 O 3 ) powders and then subjecting them to a mechanical alloying treatment to produce an alloy powder;
(b) charging the canned alloy with the mechanically alloyed alloy powder to perform a degassing treatment;
(c) hot-working the degassed alloy powder to produce an oxide dispersion-strengthened steel; And
(d) cold-working the hot-worked oxide-dispersed steel.
A flow chart schematically showing the above steps is shown in Fig.
In step (a), a metal containing Fe, C, Cr, W, V, Ta, Ti, and Zr Powder and yttria (Y 2 O 3 ) powder are mixed to form an alloy powder. Wherein the alloy powder comprises 0.05 to 0.2 wt% of carbon, 8 to 12 wt% of chromium (Cr), 0.5 to 3 wt% of tungsten (W), 0.1 to 0.3 wt% of vanadium (V) 0.01 to 0.5% by weight of titanium (Ti), 0.01 to 0.2% by weight of zirconium (Zr), 0.1 to 0.5% by weight of yttria (Y 2 O 3 ), and the balance of iron (Fe). After mixing these metal powders, mechanical alloying powders are prepared using mechanical alloying equipment such as a horizontal ball mill.
In step (b), the mechanical alloying powder produced by step (a) is degassed in vacuum, and more specifically, the mechanical alloying powder produced by step (a) is introduced into a can of carbon steel or stainless steel And then degassed at 400 to 650 ° C and 10 -5 to 10 -3 torr for 1 to 4 hours.
In step (c), the mechanical alloying powder degassed by step (b) is subjected to hot working, and more specifically, in the hot isostatic pressing, hot forging, hot rolling and hot extrusion processes, Steel is manufactured. In this case, the heating temperature is in the range of 850 to 1200 ° C., and the hot isostatic pressing process is maintained for 1 to 4 hours under the pressure of 100 to 200 MPa, and the hot extrusion process is heated for 1 to 4 hours and then hot extruded by pressing to solidify the alloy . Hot rolling is isothermal annealed at a temperature in the range of 950-1200 ℃ for 1-4 hours and rolled at a thickness reduction rate of 70% or more. In the present invention, the hot working step may be applied alone or in combination.
In step (d), the oxide-dispersed tempered steel produced by step (c) may be cold worked, and more specifically, it may be performed alone or in combination in the cold rolling, cold drawing and cold filing processes.
In one embodiment of the present invention, the alloy of the present invention contains 0.05 to 0.2 wt% of carbon, 8 to 12 wt% of chromium (Cr), 0.5 to 3 wt% of tungsten (W), 0.1 to 0.3 wt% of vanadium (V) The balance comprising iron (Fe) in an amount of 0.1 to 0.1 wt%, titanium (Ti) in an amount of 0.01 to 0.5 wt%, zirconium (Zr) in an amount of 0.01 to 0.2 wt%, yttria (Y 2 O 3 ) As a result of comparing the tensile and creep strengths with the conventional low radiated ferrite / martensitic steel after the preparation of the activated carbon dispersion-strengthened steel (see Example 1), it was found that the low- (See Example 2) and a creep strength as well as a significantly lower tensile strength than the low-activation ferrite / martensitic steel of Example 1 (see Example 3).
Hereinafter, preferred embodiments of the present invention will be described in order to facilitate understanding of the present invention. However, the following examples are provided only for the purpose of easier understanding of the present invention, and the present invention is not limited by the following examples.
[ Example ]
Example 1. Manufacture of oxide-dispersed steel
A low radiated ferrite / martensitic steel and oxide-dispersed steel having the composition shown in Table 1 below was prepared.
(Table 1) Chemical composition (wt%) of reference composition and low-activation oxide-dispersed steel, Bal = remainder)
That is, the raw material powder (carbon (C), iron (Fe), chromium (Cr), tungsten (W), vanadium (V), tantalum (Ta), titanium (Ti), and zirconium (Zr) 2 O 3 powder (50 nm or less, purity 99.9%) were mixed according to respective weight ratios, and the mixture was extruded in an ultra-high purity argon (Ar) atmosphere at a rotation speed of 240 rpm for 48 hours using a horizontal ball mill apparatus (ZOZ GmbH, SIMOLOYER CM20) The mechanical alloying powder was prepared by a mechanical alloying method and then filled in a stainless steel can, sealed and degassed at 400-650 ° C. for 3 hours under a vacuum of 10 -4 torr or less.
The prepared powder filled cans were pressurized by hot isostatic pressures at 1150 ℃ and 100 MPa for 3 hours and then heated again at 1150 ℃ for 2 hours and hot rolled at a thickness reduction rate of 70% or more.
Example 2. At room temperature and high temperature The tensile strength Confirm
The yield strength (MPa), the maximum tensile strength (MPa) and the total elongation (%) of the reference alloy and the new alloy prepared in Example 1 were measured at room temperature, 500 ° C and 700 ° C, . Tensile specimens were prepared in accordance with ASTM E8 standards after gauge lengths were taken parallel to the rolling direction of the oxide dispersion strengthened steel. The tensile test was carried out at room temperature, 500 ° C and 700 ° C at a strain rate of 1 x 10 -4 s -1 . The tensile test was performed at least three times for each specimen and temperature, and the average value was calculated and reflected in the results.
As shown in FIG. 2, the conventional low-radiated ferrite / martensite-strong reference alloy has a tensile strength of 650 MPa at room temperature and a tensile strength of about 430 MPa at a high temperature of 500 ° C. On the other hand, the low activated oxide dispersion strengthened steel of the present invention containing Ti and Zr together with Y 2 O 3 exhibited an improved tensile strength of about 85% at room temperature and about 97% at 500 ° C higher temperature than the reference alloy. In addition, tensile strength increased by 102% at a high temperature of 700 ° C. It can be seen that the tensile strength of the low-activation oxide dispersion strengthened steel due to the fine dispersion of the ultrafine composite oxide is further improved as the temperature becomes higher than that of the conventional alloy.
From the above results, it can be seen that the new alloy according to the present invention has about twice the yield strength at room temperature as compared with the conventional low activation ferritic / martensitic steel, and exhibits a remarkably excellent yield strength even at a high temperature of 500 ° C and 700 ° C .
Example 3. Confirm the creep strength of oxide-dispersed steel
The reference alloy and the new alloy prepared in Example 1 were subjected to a creep test at 550 ° C and 700 ° C, and the results are shown in FIG.
As shown in FIG. 3, the conventional low-radiated ferrite / martensite-strong reference alloy is found to break after about 145 hours at 550 DEG C under a stress condition of 240 MPa. On the other hand, the low-energized oxide-dispersed steels with Ti and Zr added with Y 2 O 3 were fractured after 3668 hours at the same conditions and cracked after 2805 hours at higher stresses, indicating a significantly higher creep strength have. At low temperature of 700 ℃, conventional low radiated ferrite / martensite steels took a very short time to break at 120 MPa stress condition, but the low activated oxide dispersion strengthened steels showed excellent creep strength of 3618 hours under the same conditions .
From the above results, it can be seen that the low-activation oxide-dispersed steel according to the present invention has a higher creep strength than the conventional low-activation ferrite / martensitic steel.
It will be understood by those skilled in the art that the foregoing description of the present invention is for illustrative purposes only and that those of ordinary skill in the art can readily understand that various changes and modifications may be made without departing from the spirit or essential characteristics of the present invention. will be. It is therefore to be understood that the above-described embodiments are illustrative in all aspects and not restrictive.
Claims (8)
Characterized in that the structural component material of the sodium-cooled high velocity furnace is a nuclear fuel cladding, a duct, a wire, or a rod.
(a) a metal powder containing iron (Fe), carbon (C), chromium (Cr), tungsten (W), vanadium (V), tantalum (Ta), titanium (Ti), and zirconium (Y 2 O 3 ) powders and then subjecting them to a mechanical alloying treatment to produce an alloy powder;
(b) charging the canned alloy with the mechanically alloyed alloy powder to perform a degassing treatment;
(c) hot-working the degassed alloy powder to produce an oxide dispersion-strengthened steel; And
(d) cold-working the hot-worked oxide-dispersed steel.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111519108A (en) * | 2020-06-09 | 2020-08-11 | 西安建筑科技大学 | Zirconium-reinforced low-activation martensitic steel and preparation method thereof |
| CN111705264A (en) * | 2020-06-24 | 2020-09-25 | 西安建筑科技大学 | Rare earth steel and preparation method thereof |
| KR20200124042A (en) * | 2019-04-23 | 2020-11-02 | 한국원자력연구원 | Ferrite-Martensitic Oxide Dispersion Strengthened Steels |
| CN113851231A (en) * | 2021-08-25 | 2021-12-28 | 中国科学院合肥物质科学研究院 | Method and device for improving tritium value-added rate of fusion reactor |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5326339B2 (en) | 2007-04-25 | 2013-10-30 | 新日鐵住金株式会社 | Ferritic heat-resistant steel and heat-resistant structure with excellent creep characteristics in weld heat-affected zone |
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20200124042A (en) * | 2019-04-23 | 2020-11-02 | 한국원자력연구원 | Ferrite-Martensitic Oxide Dispersion Strengthened Steels |
| CN111519108A (en) * | 2020-06-09 | 2020-08-11 | 西安建筑科技大学 | Zirconium-reinforced low-activation martensitic steel and preparation method thereof |
| CN111705264A (en) * | 2020-06-24 | 2020-09-25 | 西安建筑科技大学 | Rare earth steel and preparation method thereof |
| CN111705264B (en) * | 2020-06-24 | 2021-06-04 | 西安建筑科技大学 | Rare earth steel and preparation method thereof |
| CN113851231A (en) * | 2021-08-25 | 2021-12-28 | 中国科学院合肥物质科学研究院 | Method and device for improving tritium value-added rate of fusion reactor |
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