KR20140130590A

KR20140130590A - Ferrite-martensite steel having high impact properties and method thereof

Info

Publication number: KR20140130590A
Application number: KR1020130049037A
Authority: KR
Inventors: 천영범; 김태규; 한창희; 최병권; 김기백; 강석훈; 김대환; 권준현; 노상훈; 정용환; 이동원; 조승연; 안무영; 박이현
Original assignee: 한국원자력연구원; 한국기초과학지원연구원
Priority date: 2013-05-01
Filing date: 2013-05-01
Publication date: 2014-11-11

Abstract

The present invention relates to ferrite-martensite steel with excellent impact properties and a method for manufacturing the same and, more specifically, to ferrite-martensite steel comprising: 0.05-0.12 wt% of carbon (C), 0.03-0.12 wt% of silicon (Si), 0.35-0.50 wt% of manganese (Mn), 8.0-9.5 wt% of chrome (Cr), 1.0-1.7 wt% of tungsten (W), 0.1-0.4 wt% of vanadium (V), 0.04-0.08 wt% of tantalum (Ta), 0.005-0.04 wt% of nitrogen (N), 0.0005-0.006 wt% of boron (B), 0.004-0.03 wt% of titanium (Ti), 0.004-0.015 wt% of zirconium, and the remainder consisting of Fe and inevitable impurities with respect to the total weight percentage. According to the ferrite-martensite steel with excellent impact properties and the method for manufacturing the same, the requirement of reduced activation is satisfied, and tensile properties comparable with the existing reduced activation ferrite-martensite steel are maintained, so the ferrite-martensite steel can be used as a structural material of a fusion reactor requiring impact properties.

Description

TECHNICAL FIELD [0001] The present invention relates to a ferrite-martensitic steel having excellent impact properties and a method of manufacturing the ferrite-

The present invention relates to a ferrite-martensitic steel having excellent impact properties and a method for producing the ferrite-martensitic steel. More particularly, the present invention relates to a ferrite-martensitic steel having excellent low- And a manufacturing method thereof.

Nuclear fuel is a key component of the sodium-cooled high-speed process, which involves the production of energy by nuclear fission, the proliferation of nuclear materials, and the destruction of waste. Therefore, the safety of the nuclear fuel in which radioactive fission products are concentrated is directly related to the safety of the nuclear reactor.

The fuel cladding tube is the most important fuel component directly connected to the safety of the fuel and the reactor because it seals the fuel core and prevents the leakage of the radioactive material. SFR fuel cladding tubes are used under harsh conditions of high temperature and high irradiation. Therefore, a cladding tube having excellent creep resistance at high temperature and maintaining softness while having a low swelling up to a high neutron irradiation dose should be developed. To realize this, it is necessary to develop a new material having high temperature coolant, high temperature / radiation resistance that can withstand high neutron irradiation conditions, and excellent compatibility with liquid sodium.

Recently, ferrite-martensitic steel (FMS) containing high chromium has been attracting attention as a candidate material for the main components of the fourth generation reactor and nuclear fusion reactor, which is excellent in high temperature characteristics.

The high chromium ferrite / martensitic steel containing 8 to 12 wt.% Chromium content is a fast neutron since the 1970s because of its superior thermal properties and resistance to swelling in comparison with austenitic stainless steels (eg SS316, SS304) Has been used as a material for a fuel cladding tube, a wrapper or a duct which is an important component of a fast breeder reactor core using a fuel cell. The HT9 alloy (main component: 12% Cr-1% Mo-0.5% W-0.3% V), which was developed as a high temperature heat resistant material for thermal power plants in the 1960s, In addition, in Europe and Japan, high chromium ferrite / martensitic steel was selected as a cladding at high speed and in-situ irradiation tests were conducted. In recent years, high-chromium ferrite / martensitic steel has been considered as a core component material for use in a highly radioactive environment at a high temperature of 600 ° C or higher and 200 dpa or more in a high-efficiency fourth generation reactor.

The concept of reduced-activation steels was introduced in the mid-1980s when the nuclear fusion reactor material development program began in earnest, and research on low radiated ferrite / martensitic steel (RAFMS) was promoted in earnest. The starting material is the ferrite / martensitic steel of the ASTM Gr.91 alloy (main component: 9% Cr-1% Mo-0.20% V-0.08% Nb) known as the modified 9Cr-1Mo steel. Low radiated ferritic / martensitic steels followed the limitations of alloying elements to reduce the production of long-lived high-level radioactive materials generated by fast neutron irradiation. Namely, the addition of molybdenum, niobium, nickel, copper and nitrogen was strictly restricted in the low radiated ferrite / martensitic steel, and the addition of tungsten and tantalum was proposed instead of these elements. In order to suppress the formation of the δ-ferrite phase, which has a negative effect on the impact characteristics, the alloy which reduces the chromium content to 7 to 9% was preferred, without increasing the amount of α-phase stabilizing elements, carbon or manganese.

In this series of studies, in Japan, the F82H alloy (main component: 8% Cr-2.0% W-0.25% V-0.04% Ta) and JLF- V-0.05% Ta-0.02% Ti) in Europe and EUROFER-97 alloy (main component: 9% Cr-1.1% W-0.20% V-0.12% Ta-0.01% Ti) in Europe, ORNL 9Cr- 2WVTa (main component: 9% Cr-2.0% W-0.25% V-0.07% Ta) was developed.

However, since the structural material of the fusion reactor is used under severe conditions in which high-temperature and high-speed neutrons are irradiated, development of high-chromium ferrite / martensite steel excellent in impact characteristics at high temperature is still required.

SUMMARY OF THE INVENTION The present invention has been made to solve the above-mentioned problems, and an object of the present invention is to provide a ferrite-martensitic steel which improves impact properties while maintaining tensile properties comparable to conventional low activation ferritic- Method.

According to an aspect of the present invention for achieving the above object, the present invention provides a method of manufacturing a semiconductor device, comprising 0.05 to 0.12 wt% of carbon (C), 0.03 to 0.12 wt% of silicon (Si) (V), 0.04 to 0.08 wt.% Of tantalum (Ta), 0.005 wt.% Or less of nitrogen (N), 0.5 to 10 wt.% Of chromium, 8.0 to 9.5 wt.% Of chromium (Cr), 1.0 to 1.7 wt.% Of tungsten (B), 0.004 to 0.03% by weight of titanium (Ti), and 0.004 to 0.015% by weight of zirconium, the balance being Fe and unavoidable impurities, Provide site river.

The present invention also provides a method of manufacturing a semiconductor device comprising 0.05 to 0.12 wt% of carbon (C), 0.03 to 0.12 wt% of silicon (Si), 0.35 to 0.50 wt% of manganese (Mn) (Ti), 0.004 to 0.03 wt.% Of titanium (Ti), and 0.04 to 0.08 wt.% Of tantalum (W), 0.1 to 0.4 wt.% Of vanadium Martensitic steel excellent in impact characteristics including 0.004 to 0.015% by weight of zirconium and the balance of Fe and unavoidable impurities.

On the other hand, the present invention comprises a step (step 1) of preparing an ingot by mixing and dissolving an alloy composition element; Hot rolling the ingot produced in step 1 (step 2); Normalizing the hot-rolled ingot in step 2 and air-cooling the ingot (step 3); And a step (step 4) of tempering the normalized alloy in step 3 and then air-cooling the ferrite-martensitic steel (step 4), thereby providing a ferrite-martensitic steel having excellent impact properties .

Wherein the ingot of step 1 is manufactured using a vacuum induction melting (VIM) method, wherein the hot rolling in step 2 is performed at a temperature of 1100 to 1200 ° C for 0.5 to 2 hours, Rising treatment is carried out at 950 ~ 1050 ℃ for 0.5 ~ 2 hours. The tempering process of step 4 is performed at 700 to 780 ° C for 0.5 to 4 hours.

As described above, the present invention provides a ferrite-martensitic steel and a method of manufacturing the ferrite-martensitic steel which are excellent in low radiative characteristics and impact properties through alloy compositions whose B, Ti and Zr contents are varied.

Accordingly, the present invention satisfies the requirements of low activation and maintains tensile properties comparable to conventional low activation ferritic-martensitic steels, and thus has the effect of being utilized as a fusion structure structure requiring impact characteristics.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS Hereinafter, preferred embodiments of a ferrite-martensitic steel having excellent impact characteristics according to the present invention and a method of manufacturing the same will be described in detail with reference to the accompanying drawings.

Prior to this, terms and words used in the present specification and claims should not be construed as being limited to ordinary or dictionary terms, and the inventor should appropriately define the concept of the term to describe its invention in the best way The present invention should be construed in accordance with the meaning and concept consistent with the technical idea of the present invention.

Therefore, the embodiments described in the present specification and the configurations shown in the drawings are merely the most preferred embodiments of the present invention and are not intended to represent all of the technical ideas of the present invention. Therefore, various equivalents It should be understood that water and variations may be present.

Hereinafter, a ferrite-martensitic steel according to a preferred embodiment of the present invention and a method for producing the same will be described in detail.

The present invention relates to a steel sheet comprising 0.05 to 0.12 wt% of carbon (C), 0.03 to 0.12 wt% of silicon (Si), 0.35 to 0.50 wt% of manganese (Mn), 8.0 to 9.5 wt% of chromium (Cr) (B), 0.0005 to 0.006 wt.% Of boron (B), 0.1 to 0.4 wt.% Of vanadium (V), 0.04 to 0.08 wt.% Of tantalum (Ta), 0.005 to 0.04 wt. 0.004 to 0.03% by weight of Ti) and 0.004 to 0.015% by weight of zirconium, the remainder being Fe and unavoidable impurities.

Hereinafter, the roles and effects of the elements added in the present invention will be described.

(1) carbon (C)

In the high chromium ferrite / martensitic steel according to the present invention, carbon forms a carbide to exhibit a precipitation hardening effect, and a preferred carbon content is 0.05 to 0.12 wt%. If the content of carbon is less than 0.05 wt%, the mechanical strength at room temperature is lowered and the toughness is deteriorated. In particular, Cr equivalent is increased to cause delta ferrite. When the content of carbon is more than 0.12 wt%, a large amount of carbide is produced. There is a problem that the strengthening effect due to the coarse-dea precipitate is easily lost during use.

(2) Silicon (Si)

In the high-chromium ferrite / martensitic steel according to the present invention, silicon serves to improve oxidation resistance and acts as a deoxidizer in steelmaking. The preferable content of silicon is 0.03 to 0.12% by weight. When the content of silicon is less than 0.03% by weight, corrosion resistance is low. When the content of silicon is more than 0.12% by weight, there is a problem of promoting the formation of laves phase which deteriorates toughness.

(3) Manganese (Mn)

In the high chromium ferrite / martensitic steel according to the present invention, manganese has a role of improving the hardenability, and the content of manganese is preferably 0.35-0.50 wt%. If the content of manganese is less than 0.35% by weight, there is a problem in the curing ability, while if the content is more than 0.50% by weight, there is a problem that the impact characteristics are lowered.

(4) Cr (Cr)

In the high chromium ferrite / martensitic steel according to the present invention, chromium is known to increase corrosion resistance and high temperature strength, and the preferable chromium content is 8.0 to 9.5 wt%. If the content of chromium is less than 8.0 wt%, there is a problem that resistance to oxidation and corrosion at high temperatures is lowered. If the content of chromium is more than 9.5 wt%, there is a problem that the impact characteristics are deteriorated.

(5) Tungsten (W)

In the high chromium ferrite / martensitic steel according to the present invention, tungsten is a typical solid solution strengthening alloy element, and the content of tungsten is preferably 1.0 to 1.7 wt%. If the content of tungsten is less than 1.0 wt%, there is a problem in effective employment reinforcement. When the content of tungsten is more than 1.7 wt%, there is a problem that a Laves phase known to deteriorate long-time impact characteristics and toughness is generated.

(6) Vanadium (V)

In the high chromium ferrite / martensitic steel according to the present invention, vanadium is an alloy element showing precipitation hardening, and the content of vanadium is preferably 0.1 to 0.4 wt%. If the content of vanadium is less than 0.1% by weight, the position of precipitates is reduced and the carbides are not uniformly distributed. As a result, coarse carbides are formed to deteriorate impact characteristics. When the content of vanadium exceeds 0.4% by weight, There is a problem that it consumes both carbon and nitrogen and makes it difficult for other types of carbides to be produced during use.

(7) Tantalum (Ta)

In the high-chromium ferrite / martensitic steel according to the present invention, tantalum is included in the niobium precipitate as a low-activation element and plays a role of exhibiting precipitation strengthening effect. In the present invention, the tantalum is preferably added in an amount of 0.04 to 0.08% by weight in order to exhibit excellent mechanical properties. If the tantalum exceeds 0.08% by weight, the tantalum has the same problem as the excessive addition of niobium.

(8) Nitrogen (N)

In the high chromium ferrite / martensitic steel according to the present invention, nitrogen acts to increase the strength by forming nitride or solid solution in an intrusion form, and the preferable nitrogen content is 0.005 to 0.04% by weight. When the content of nitrogen is less than 0.005% by weight, corrosion resistance is lowered. When the content of nitrogen is more than 0.04% by weight, there is a problem that impact properties are rapidly lowered.

(9) Boron (B)

In the high chromium ferrite / martensitic steel according to the present invention, boron segregates at grain boundaries to strengthen the grain boundary to improve high-temperature creep resistance, and the preferable content of boron is 0.0005 to 0.006 wt%. If the content of boron is less than 0.0005 wt%, there is a problem that effective strengthening of the grain boundary can not be obtained. When the content exceeds 0.006 wt%, boron precipitates are formed, which deteriorates impact properties and causes problems in productivity.

(10) Titanium (Ti)

In the high-chromium ferrite / martensitic steel according to the present invention, the specific strength of titanium is less than that of iron, so it is about twice that of iron, and the thermal conductivity and thermal expansion coefficient are small. The preferred content of titanium is 0.004 To 0.03% by weight.

(11) Zirconium (Zr)

In the high chromium ferrite / martensitic steel according to the present invention, phosphorus or zirconium may additionally be added in small amounts in order to improve impact properties. In this case, zirconium is preferably added in an amount of 0.004 to 0.015% by weight, and when it exceeds the above range, the mechanical properties are deteriorated.

In particular, the addition of 0.005-0.2 wt% Zr to a typical 8-10 wt% Cr steel not only improves impact resistance but also relieves the dependence on the amount of tempering of the ductile-brittle transition temperature, And increases the possibility of improving the mechanical properties without deteriorating the impact characteristics. Also, when the amount of Zr added increases, it is possible to form brittle Laves phases such as ZrFe 2 and ZrFe 3, and the addition amount should be limited to 0.2 wt% or less.

In addition, the maximum permissible amounts of elements and impurities to be excluded in the production of the high chromium ferrite / martensitic steel according to the present invention include less than 0.05% of Ni, less than 0.05% of Mo, less than 0.002% of Nb, Cu: less than 0.05%, Al: less than 0.03%, Co: less than 0.01%, Pd: less than 0.05%, Pt: less than 0.05%, and Re: less than 0.005%.

Sb: less than 0.004%, P: less than 0.005%, S: less than 0.005%, O: 0.005% or less, : Less than 0.02%, and H: less than 0.0005%.

The high chromium ferrite / martensitic steel according to the present invention can be produced by a conventional method well known in the art. Preferably, the step of mixing and dissolving the alloying elements to prepare an ingot (Step 1); Hot rolling the ingot produced in step 1 (step 2); Normalizing the hot-rolled ingot in step 2 and air-cooling the ingot (step 3); And a step (step 4) of tempering the normalized alloy in step 3 and then air-cooling the alloy to prepare a high-chromium ferrite / martensitic steel.

Further, after the tempering treatment of step 3 to produce the high chromium ferrite / martensitic steel according to the present invention in a nuclear fuel component of the required type (e. G., A nuclear cladding or duct of a sodium cooling high speed furnace) And then performing the final heat treatment after performing the processing several times repeatedly.

Hereinafter, the production method of the present invention will be described step by step.

First, Step 1 is a step of mixing an alloy composition element and dissolving it to produce an ingot.

The alloying elements include 0.05 to 0.12 wt% of carbon (C), 0.03 to 0.12 wt% of silicon (Si), 0.35 to 0.50 wt% of manganese (Mn), 8.0 to 9.5 wt% of chromium (Cr) (Ti) in an amount of from 0.004 to 0.04% by weight, from 1.0 to 1.7% by weight, from 0.1 to 0.4% by weight of vanadium, from 0.04 to 0.08% by weight of tantalum and from 0.005 to 0.04% by weight of nitrogen, 0.03% by weight or zirconium in an amount of 0.004 to 0.015% by weight, and the balance of Fe and unavoidable impurities.

The ingot may employ a vacuum induction melting (VIM) method.

Specifically, an induction current is applied to the melting chamber in a high vacuum (1 × 10 -5 to 0.5 torr) atmosphere to firstly dissolve the alloy element, and then a deoxidizer such as aluminum or silicon is introduced. Trace elements, especially nitrogen, are charged into the molten metal at the point when the dissolution is almost completed, and samples for component analysis are collected. When the melting is completed, a molten metal is poured into a rectangular parallelepiped mold at 1500 ° C. to perform tapping, and the oxide layer on the surface is mechanically processed to produce an ingot.

Next, Step 2 is a step of hot-rolling the ingot produced in Step 1 above.

The hot-rolled product is used to produce a hot workpiece suitable for hot working. In this case, the hot rolling is preferably performed at a temperature of 1100 to 1200 ° C. for 0.5 to 2 hours. If the temperature is out of the above range, ie below 1100 ° C, the objective of solution annealing can not be attained sufficiently. If the temperature exceeds 1200 ° C, the size of the prior- It is possible to cause a problem of degradation.

Next, Step 3 is a step of normalizing the hot-rolled product in Step 2, followed by air-cooling.

It is preferable that the normalizing treatment is performed for 0.5 to 2 hours in the gamma phase temperature range of 950 to 1050 ° C because the undesirably formed precipitate phase is redissolved in the hot worked product and the cooling temperature is controlled to adjust the size And to control the amount.

Next, Step 4 is a step of tempering the normalized alloy in Step 3 and then air-cooling the alloy to produce a high chromium ferrite / martensitic steel.

The tempering treatment is preferably performed at 700 to 780 ° C for 0.5 to 4 hours in order to finely and uniformly produce a desired stable precipitation phase.

The high-chromium ferrite / martensitic steel according to the present invention can be produced by such a method.

The high chromium ferrite / martensitic steel produced by the above method exhibits excellent impact characteristics as compared with the conventional high chromium ferrite / martensitic steel. Therefore, the fourth generation nuclear reactor, which is used in severe conditions of high temperature and high irradiation, It can be very useful for materials such as nuclear fuel cladding pipes, ducts and wire laps which are main core components of cooling high-speed furnace.

Hereinafter, the present invention will be described in more detail by way of examples. However, the following examples are only illustrative of the present invention, and thus the scope of the present invention is not limited by the following examples.

Example 1 Production of high chromium ferrite / martensitic steel

As the test material, 0.07 wt% of carbon, 0.10 wt% of silicon, 0.4 wt% of manganese, 8.5 wt% of chromium, 1.5 wt% of tungsten, 0.30 wt% of vanadium, 0.05 wt% of tantalum, 0.015 wt% of nitrogen and the balance of iron and other unavoidable impurities Was prepared from a vacuum induction furnace with a 30 kg ingot. The ingot was held at 1150 ° C for 2 hours and hot rolled to a final thickness of 15 mm.

Then, the following heat treatment was carried out.

Specifically, the alloy was subjected to normalizing treatment at 1,050 占 폚 for 1 hour and then air-cooled.

Thereafter, the homogenized alloy was tempered at 750 ° C for 2 hours and air-cooled to produce a high-chromium ferrite / martensitic steel.

&Lt; Example 2 >

As the test material, 0.07 wt% of carbon, 0.10 wt% of silicon, 0.4 wt% of manganese, 8.5 wt% of chromium, 1.5 wt% of tungsten, 0.30 wt% of vanadium, 0.05 wt% of tantalum, 0.015 wt% of nitrogen, 0.005 wt% High-chromium ferrite / martensitic steel was produced in the same manner as in Example 1, except that a test material having a composition including a rare earth element and other unavoidable impurities was used.

&Lt; Example 3 >

As the test material, there were used 0.07 wt% of carbon, 0.10 wt% of silicon, 0.4 wt% of manganese, 8.5 wt% of chromium, 1.5 wt% of tungsten, 0.30 wt% of vanadium, 0.05 wt% of tantalum, 0.015 wt% of nitrogen, 0.005 wt% of boron, High-chromium ferrite / martensitic steel was produced in the same manner as in Example 1, except that a test material having a composition including iron and other unavoidable impurities was used.

As test materials, there were used 0.07 wt% of carbon, 0.10 wt% of silicon, 0.4 wt% of manganese, 8.5 wt% of chromium, 1.5 wt% of tungsten, 0.20 wt% of vanadium, 0.05 wt% of tantalum, 0.015 wt% of nitrogen, 0.005 wt% of boron, High chromium ferrite / martensitic steel was prepared by following the same procedure as in Example 1, except that a test material having a composition of wt.%, Zirconium 0.005 wt.% And balance of iron and other unavoidable impurities was used.

&Lt; Example 5 >

As the test material, 0.07 wt% of carbon, 0.10 wt% of silicon, 0.4 wt% of manganese, 9.0 wt% of chromium, 1.2 wt% of tungsten, 0.20 wt% of vanadium, 0.07 wt% of tantalum, 0.010 wt% of nitrogen and the balance of iron and other unavoidable impurities High-chromium ferrite / martensitic steel was produced in the same manner as in Example 1, except that the test material having the composition of the present invention was used.

&Lt; Example 6 >

As the test material, 0.07 wt% of carbon, 0.10 wt% of silicon, 0.4 wt% of manganese, 9.0 wt% of chromium, 1.2 wt% of tungsten, 0.20 wt% of vanadium, 0.07 wt% of tantalum, 0.010 wt% of nitrogen, 0.010 wt% of titanium, High-chromium ferrite / martensitic steel was produced in the same manner as in Example 1, except that a test material having a composition including a rare earth element and other unavoidable impurities was used.

&Lt; Example 7 >

As the test material, there were used 0.07 wt% of carbon, 0.10 wt% of silicon, 0.4 wt% of manganese, 9.0 wt% of chromium, 1.2 wt% of tungsten, 0.20 wt% of vanadium, 0.07 wt% of tantalum, 0.010 wt% of nitrogen, 0.010 wt% of titanium, High-chromium ferrite / martensitic steel was produced in the same manner as in Example 1, except that a test material having a composition including iron and other unavoidable impurities was used.

&Lt; Example 8 >

As test materials, there were used 0.07 wt% of carbon, 0.10 wt% of silicon, 0.4 wt% of manganese, 9.0 wt% of chromium, 1.2 wt% of tungsten, 0.20 wt% of vanadium, 0.07 wt% of tantalum, 0.010 wt% of nitrogen, 0.020 wt% of titanium, High-chromium ferrite / martensitic steel was produced in the same manner as in Example 1, except that a test material having a composition including iron and other unavoidable impurities was used.

&Lt; Example 9 >

As the test material, 0.10 wt% of carbon, 0.05 wt% of silicon, 0.45 wt% of manganese, 9.0 wt% of chromium, 1.1 wt% of tungsten, 0.20 wt% of vanadium, 0.07 wt% of tantalum, 0.030 wt% of nitrogen, 0.010 wt% of titanium, 0.005 wt% of zirconium High-chromium ferrite / martensitic steel was produced in the same manner as in Example 1, except that a test material having a composition including iron and other unavoidable impurities was used.

&Lt; Example 10 >

As the test material, 0.10 wt% of carbon, 0.05 wt% of silicon, 0.45 wt% of manganese, 9.0 wt% of chromium, 1.1 wt% of tungsten, 0.20 wt% of vanadium, 0.07 wt% of tantalum, 0.030 wt% of nitrogen, 0.001 wt% of boron, High chromium ferrite / martensitic steel was prepared by following the same procedure as in Example 1, except that a test material having a composition of wt.%, Zirconium 0.005 wt.% And balance of iron and other unavoidable impurities was used.

&Lt; Example 11 >

As the test material, 0.10 wt% of carbon, 0.05 wt% of silicon, 0.45 wt% of manganese, 9.0 wt% of chromium, 1.1 wt% of tungsten, 0.20 wt% of vanadium, 0.07 wt% of tantalum, 0.030 wt% of nitrogen, 0.001 wt% of boron, High chromium ferrite / martensitic steel was prepared by following the same procedure as in Example 1, except that a test material having a composition of wt.%, Zirconium 0.01 wt.% And balance of iron and other unavoidable impurities was used.

&Lt; Example 12 >

&Lt; Example 13 >

As the test material, 0.10 wt% of carbon, 0.05 wt% of silicon, 0.45 wt% of manganese, 9.0 wt% of chromium, 1.1 wt% of tungsten, 0.20 wt% of vanadium, 0.07 wt% of tantalum, 0.030 wt% of nitrogen, 0.010 wt% of titanium, High-chromium ferrite / martensitic steel was produced in the same manner as in Example 1, except that a test material having a composition including iron and other unavoidable impurities was used.

&Lt; Example 14 >

0.1% by weight of silicon, 0.45% by weight of manganese, 9.0% by weight of chromium, 1.1% by weight of tungsten, 0.20% by weight of vanadium, 0.07% by weight of tantalum, 0.030% High-chromium ferrite / martensitic steel was produced in the same manner as in Example 1, except that a test material having a composition including iron and other unavoidable impurities was used.

The composition of the high chromium ferrite / martensitic steel prepared in Examples 1 to 14 is summarized in Table 1 below.

<Experimental Example> Characterization of high chromium ferrite / martensitic steel

(1) Measurement of yield strength and tensile strength

In order to measure the properties of the high chromium ferrite / martensitic steel prepared in Examples 1 to 14 and Comparative Examples 1 and 2 at high temperature, the yield strength and tensile strength were measured at 500 ° C. by a tensile test (ASTM E 8M-08) The results are shown in Table 2.

As shown in Table 2, the strength and ductility of the alloys proposed in the present invention were confirmed to be similar to those of Comparative Examples 1 and 2 through tensile properties at room temperature and 500 ° C.

(1) Shock characteristic measurement

The impact properties at high temperature of the high chromium ferrite / martensitic steel prepared according to Examples 1 to 14 and Comparative Examples 1 to 2 were measured and the results are shown in Table 3 below.

As shown in Table 3, from the Charpy impact test carried out using the full-size specimen according to the ASTM E23 standard, the ductile-brittle transition temperature (DBTT) and the upper shock absorption Energy (upper shelf energy, USE) values were obtained. It can be seen that Examples 9 to 14 in which Zr was added show similar or lower DBTT and somewhat higher upper shock absorption energy values than Comparative Examples 1 and 2. [

Accordingly, the high chromium ferrite / martensitic steel according to the present invention exhibits excellent impact properties even at a high temperature of 500 ° C, and thus can be usefully used as a nuclear fuel material used under severe conditions such as high temperature and high irradiation dose.

Although the present invention has been described in detail with reference to the above embodiments, it is needless to say that the present invention is not limited to the above-described embodiments, and various modifications may be made without departing from the spirit of the present invention.

The present invention is applied to the field of structural members for nuclear fusion blanket.

Claims

(C), 0.03 to 0.12 wt% of silicon (Si), 0.35 to 0.50 wt% of manganese (Mn), 8.0 to 9.5 wt% of chromium (Cr), 1.0 wt% of tungsten (W) (Ti) 0.004 to 0.04 wt.%, Tantalum (Ta) 0.04 to 0.08 wt.%, Nitrogen (N) 0.005 to 0.04 wt.%, Boron (B) 0.0005 to 0.006 wt. To 0.03% by weight of zirconium and 0.004 to 0.015% by weight of zirconium, the balance being Fe and unavoidable impurities.

(C), 0.03 to 0.12 wt% of silicon (Si), 0.35 to 0.50 wt% of manganese (Mn), 8.0 to 9.5 wt% of chromium (Cr), 1.0 wt% of tungsten (W) (Ti), 0.004 to 0.03 weight%, and zirconium 0.004 to 0.015 weight%, based on the total weight of the composition. %, And the balance of Fe and unavoidable impurities.

Mixing the alloy composition elements and dissolving them to produce an ingot (step 1);
Hot rolling the ingot produced in step 1 (step 2);
Normalizing the hot-rolled ingot in step 2 and air-cooling the ingot (step 3); And
The method for producing a ferrite-martensitic steel according to any one of claims 1 to 3, wherein the step (3) further comprises a step (4) of tempering the normalized alloy in step (3) A method for producing ferrite-martensitic steel.

The method of claim 3,
Wherein the ingot of step 1 is manufactured using a vacuum induction melting (VIM) method.

4. The method of claim 3, wherein the hot rolling in step 2 is performed at a temperature of 1100 to 1200 占 폚 for 0.5 to 2 hours.

4. The method for producing ferritic-martensitic steel according to claim 3, wherein the normalizing treatment in step 3 is performed at 950 to 1050 DEG C for 0.5 to 2 hours.

4. The method for producing ferritic-martensitic steel according to claim 3, wherein the tempering treatment in step 4 is performed at 700 to 780 DEG C for 0.5 to 4 hours.