KR101604598B1 - Ni-based superalloy with excellent oxidization-resistance and creep property and method of manufacturing the same - Google Patents
Ni-based superalloy with excellent oxidization-resistance and creep property and method of manufacturing the same Download PDFInfo
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- KR101604598B1 KR101604598B1 KR1020140164756A KR20140164756A KR101604598B1 KR 101604598 B1 KR101604598 B1 KR 101604598B1 KR 1020140164756 A KR1020140164756 A KR 1020140164756A KR 20140164756 A KR20140164756 A KR 20140164756A KR 101604598 B1 KR101604598 B1 KR 101604598B1
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- base superalloy
- oxidation resistance
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- 229910000601 superalloy Inorganic materials 0.000 title claims abstract description 42
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 13
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 53
- 239000000956 alloy Substances 0.000 claims abstract description 53
- 230000003647 oxidation Effects 0.000 claims abstract description 38
- 238000007254 oxidation reaction Methods 0.000 claims abstract description 38
- 239000011651 chromium Substances 0.000 claims abstract description 37
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 27
- 238000000034 method Methods 0.000 claims abstract description 19
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 17
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 17
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims abstract description 15
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 15
- 239000011733 molybdenum Substances 0.000 claims abstract description 15
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 14
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 14
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims abstract description 14
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 14
- 239000010937 tungsten Substances 0.000 claims abstract description 14
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 239000011572 manganese Substances 0.000 claims description 24
- 238000010438 heat treatment Methods 0.000 claims description 16
- 238000005098 hot rolling Methods 0.000 claims description 13
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 12
- 229910052748 manganese Inorganic materials 0.000 claims description 12
- 238000001816 cooling Methods 0.000 claims description 11
- 230000032683 aging Effects 0.000 claims description 6
- 230000009467 reduction Effects 0.000 claims description 5
- 230000008569 process Effects 0.000 abstract description 11
- 229910052746 lanthanum Inorganic materials 0.000 abstract description 10
- FZLIPJUXYLNCLC-UHFFFAOYSA-N lanthanum atom Chemical compound [La] FZLIPJUXYLNCLC-UHFFFAOYSA-N 0.000 abstract description 10
- 229910052782 aluminium Inorganic materials 0.000 abstract description 9
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 abstract description 9
- 239000000126 substance Substances 0.000 abstract description 6
- 230000001590 oxidative effect Effects 0.000 abstract description 4
- 229910001220 stainless steel Inorganic materials 0.000 abstract description 4
- 229910000753 refractory alloy Inorganic materials 0.000 abstract description 3
- 238000007792 addition Methods 0.000 description 27
- 230000000052 comparative effect Effects 0.000 description 16
- 230000000694 effects Effects 0.000 description 11
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 10
- 229910052710 silicon Inorganic materials 0.000 description 10
- 239000010703 silicon Substances 0.000 description 10
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 8
- 229910052796 boron Inorganic materials 0.000 description 8
- 239000002994 raw material Substances 0.000 description 7
- 238000005728 strengthening Methods 0.000 description 7
- 238000002156 mixing Methods 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- 239000002244 precipitate Substances 0.000 description 4
- 239000000243 solution Substances 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 238000004090 dissolution Methods 0.000 description 3
- 230000001965 increasing effect Effects 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 239000010935 stainless steel Substances 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 230000018109 developmental process Effects 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 230000003993 interaction Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 230000002411 adverse Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000000593 degrading effect Effects 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000001939 inductive effect Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Images
Classifications
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
-
- 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
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
Abstract
A nickel-base superalloy having excellent resistance to oxidation and creep, which is suitable for use as a chemical plant component in an oxidizing and reducing corrosive atmosphere that can not withstand energy plants and stainless steels by control of alloy components and process conditions, and a method for manufacturing the same .
The super refractory alloy having excellent oxidation resistance and creep characteristics according to the present invention is composed of 20 to 26% by weight of chromium (Cr), 13 to 17% by weight of tungsten (W), 1 to 5% by weight of molybdenum (Mo) 0.1 to 1.0% by weight of aluminum (Al), 0.01 to 0.06% by weight of lanthanum (La), 0.01 to 0.20% by weight of carbon (C) By weight and the balance nickel (Ni) and unavoidable impurities.
Description
The present invention relates to a nickel-base superalloy alloy and a method of manufacturing the same, and more particularly, to a nickel-base superalloy for a chemical plant having an oxidizing and reducing corrosive atmosphere which can not withstand an energy plant and stainless steel by controlling alloy components and process conditions Resistant superalloy having excellent oxidation resistance and creep characteristics suitable for use, and a process for producing the same.
Super heat resistant alloys are alloys made primarily for enduring use at high temperatures, and heat resistant steels are alloy steels with good mechanical properties and good corrosion resistance even at high temperatures.
Commercial alloys known to be excellent in oxidation resistance and creep characteristics in the conventionally developed nickel base superalloys are Haynes 230 and Alloy 617 alloys, which can be used for a long time with excellent phase stability up to approximately 650 ° C. In particular, in the case of power plants such as Advanced-Ultra Supercritical (A-USC), the temperature of main steam is expected to rise from 650 ℃ to 700 ~ 760 ℃ for CO2 reduction and energy efficiency. It is difficult to use at a temperature of 700 to 760 DEG C and development of a new alloy excellent in creep characteristics is required.
In addition, the conventional commercial alloy has a problem of not having excellent creep characteristics and excellent oxidation resistance at the same time.
A related prior art is Korean Patent Laid-Open Publication No. 10-1998-022301 (published on Jun. 7, 1998), which discloses a nickel-base superalloy for casting.
It is an object of the present invention to provide a nickel-base superalloy which is excellent in oxidation resistance and creep characteristics suitable for use as a part for chemical plant of an oxidizing and reducing corrosive atmosphere which can not withstand energy plant and stainless steel by controlling alloy component and process condition Alloy and a method of manufacturing the same.
In order to achieve the above object, the nickel-base superalloy according to the present invention is excellent in oxidation resistance and creep characteristics. The nickel-base superalloy has 20 to 26% by weight of chromium (Cr), 13 to 17% by weight of tungsten (W) 0.1 to 1.0% by weight of manganese (Mn), 0.1 to 0.6% by weight of silicon (Si), 0.1 to 1.0% by weight of aluminum (Al) and 0.01 to 0.06% of lanthanum (La) By weight, carbon (C): 0.01 to 0.20% by weight, and the balance nickel (Ni) and unavoidable impurities.
(A) 20 to 26% by weight of chromium (Cr), 13 to 17% by weight of tungsten (W), and the like. 0.1 to 1.0 wt% of molybdenum (Mo), 0.1 to 1.0 wt% of manganese (Mn), 0.1 to 0.6 wt% of silicon (Si), 0.1 to 1.0 wt% of aluminum (Al) ): 0.01 to 0.06% by weight, carbon (C): 0.01 to 0.20% by weight, and the balance nickel (Ni) and unavoidable impurities; (b) hot rolling the mixed and dissolved alloy; (c) heat treating the hot-rolled alloy; And (d) cooling the heat-treated alloy.
A nickel-base superalloy with excellent oxidation resistance and creep characteristics according to the present invention and a method of manufacturing the same are capable of improving the creep characteristics by lowering the content of chromium (Cr) and silicon (Si) By increasing the addition amount and improving the oxidation resistance, oxidation resistance and creep characteristics can be simultaneously improved.
The nickel-base superalloy according to the present invention has excellent oxidation resistance and creep characteristics even at a high temperature of 700 ° C or higher by controlling the alloy components and controlling the process conditions, It is suitable to be used as a part for chemical plant of reducing corrosive atmosphere.
FIG. 1 is a process flow chart showing a method of manufacturing a nickel-base superalloy according to an embodiment of the present invention.
FIG. 2 is a graph showing the creep strain rate over time for the specimens according to Examples 1 to 6 and Comparative Example 2. FIG.
3 is a graph showing the creep characteristic results of the specimens according to Examples 1 to 6 and Comparative Examples 1 and 3.
4 is a graph showing the results of repeated oxidation characteristics for the specimens according to Example 1, Examples 7 to 11 and Comparative Example 2. FIG.
BRIEF DESCRIPTION OF THE DRAWINGS The advantages and features of the present invention, and how to accomplish them, will become apparent by reference to the embodiments described in detail below with reference to the accompanying drawings. It should be understood, however, that the invention is not limited to the disclosed embodiments, but may be embodied in many different forms and should not be construed as being limited to the embodiments set forth herein. Rather, these embodiments are provided so that this disclosure will be thorough and complete, and will fully convey the scope of the invention to those skilled in the art. Is provided to fully convey the scope of the invention to those skilled in the art, and the invention is only defined by the scope of the claims. Like reference numerals refer to like elements throughout the specification.
Hereinafter, a nickel-base superalloy with excellent oxidation resistance and creep characteristics according to a preferred embodiment of the present invention will be described in detail with reference to the accompanying drawings.
Nickel base superalloy
The nickel-base superalloy according to the present invention comprises 20 to 26% by weight of chromium (Cr), 13 to 17% by weight of tungsten (W), 1 to 5% by weight of molybdenum (Mo) (La): 0.01 to 0.06 wt%, carbon (C): 0.01 to 0.20 wt%, and the balance nickel (Ni) and inevitable impurities.
The nickel-base superalloy may further contain 0.001 to 0.015% by weight of boron (B).
The nickel-base superalloy has a Yield strength (YS) of 195 to 300 MPa, a tensile strength (TS) of 420 to 580 MPa and an elongation (El.) Of 35 to 55% at 700 ° C. (YS): 160 to 200 MPa, tensile strength (TS): 235 to 300 MPa and elongation (EL): 48 to 59% at a high temperature condition.
Particularly, in the development of a nickel-base superalloy having excellent oxidation resistance and creep characteristics according to the present invention, it is advantageous to lower the chromium (Cr) content in order to improve creep characteristics, while chromium (Cr) (Cr) addition range in which the creep characteristics and the oxidation resistance can be simultaneously improved. In addition, it has been found that tungsten (W) and molybdenum (Mo) improve the creep characteristics when properly contained, while degrading creep characteristics when contained excessively.
Accordingly, in the present invention, the creep characteristics are improved by lowering the content of chromium (Cr) and silicon (Si), the addition of manganese (Mn) is increased and the oxidation resistance is improved by excluding the addition of Fe, At the same time, we have found out the optimum alloy composition ratio that can be improved.
As a result, the nickel-base superalloy with excellent oxidation resistance and creep characteristics according to the embodiment of the present invention has excellent oxidation resistance and creep characteristics even at a high temperature of 700 ° C or more through control of alloy components and process conditions, It is suitable to be used as parts for chemical plant in oxidizing and reducing corrosive atmosphere which stainless steel can not withstand.
Hereinafter, the role and content of each component contained in the nickel-base superalloy according to the present invention will be described.
Chromium (Cr)
Chromium (Cr) plays a role in improving corrosion resistance and oxidation resistance in super heat resistant alloys, but it can generate carbide or TCP (Topologically Close Packed) phase when added excessively.
Therefore, it is preferable that the chromium (Cr) is added at a content ratio of 20 to 26% by weight based on the total weight of the super refractory alloy according to the present invention. When the content of chromium (Cr) is less than 20% by weight, corrosion resistance may occur. On the other hand, when the content of chromium (Cr) exceeds 26% by weight, the creep characteristics are lowered, and when exposed at a high temperature for a long time, a TCP phase which adversely affects the mechanical properties may be generated.
Tungsten (W)
Tungsten (W) is an element that enhances high temperature strength and creep strength by solid solution strengthening.
The tungsten (W) is preferably added in an amount of 13 to 17% by weight based on the total weight of the super refractory alloy according to the present invention. When the addition amount of tungsten (W) is less than 13% by weight, it may be difficult to exhibit the above effect properly. On the other hand, if the addition amount of tungsten (W) exceeds 17% by weight, the toughness and ductility are lowered and the phase stability is lowered.
Molybdenum (Mo)
Molybdenum (Mo) is a solid solution strengthening element and plays a role in improving the high temperature tensile and creep properties of a super heat resistant alloy. In addition, molybdenum (Mo) bonds with carbon (C) to form M 6 C type carbide in the grain boundary, thereby suppressing grain growth.
The molybdenum (Mo) is preferably added in an amount of 1 to 5% by weight based on the total weight of the nickel-base superalloy according to the present invention. When the addition amount of molybdenum (Mo) is less than 1% by weight, it is difficult to expect the effect of solid solution strengthening because of the small amount of addition of molybdenum (Mo). On the other hand, when the addition amount of molybdenum (Mo) exceeds 5 wt%, the hot workability decreases and a TCP phase tends to be formed.
Manganese (Mn)
Manganese (Mn) serves to improve the oxidation resistance of the alloy.
The manganese (Mn) is preferably added in an amount of 0.1 to 1.0% by weight based on the total weight of the nickel-base superalloy according to the present invention. When the addition amount of manganese (Mn) is less than 0.1 wt%, the effect of improving the creep characteristics may be insufficient because the addition amount is insignificant. On the other hand, when the addition amount of manganese (Mn) exceeds 1.0% by weight, there is a problem that workability and oxidation resistance are lowered.
Silicon (Si)
Silicon (Si) plays a role in improving the oxidation resistance of an alloy like manganese (Mn).
The silicon (Si) is preferably added in an amount of 0.1 to 0.6% by weight based on the total weight of the nickel-base superalloy according to the present invention. When the addition amount of silicon (Si) is less than 0.1% by weight, the addition amount thereof is insignificant, so that it may be difficult to exhibit the oxidation resistance improving effect properly. On the contrary, if the addition amount of silicon (Si) exceeds 0.6 wt%, the oxidation resistance is improved but the creep characteristic is rapidly deteriorated.
Aluminum (Al)
Aluminum (Al) is a constituent element of γ ', which is the main strengthening phase of nickel-base superalloy, and contributes to improvement of oxidation resistance.
The aluminum (Al) is preferably added in an amount of 0.1 to 1.0% by weight based on the total weight of the nickel-base superalloy according to the present invention. When the addition amount of aluminum (Al) is less than 0.1% by weight, it may be difficult to exhibit the above effect properly. On the contrary, when the addition amount of aluminum (Al) exceeds 1.0% by weight, there is a problem that the processability is deteriorated due to excessive precipitation of? 'Phase.
Lanthanum (La)
Lanthanum (La) plays a role in improving oxidation resistance.
The lanthanum La is preferably added in an amount of 0.01 to 0.06% by weight based on the total weight of the nickel-base superalloy according to the present invention. When the addition amount of lanthanum (La) is less than 0.01% by weight, the addition amount of the lanthanum (La) is insignificant, so that it may be difficult to exhibit the above effect properly. On the other hand, when the addition amount of lanthanum (La) exceeds 0.06% by weight, oxidation resistance is deteriorated due to interaction with boron (B).
Carbon (C)
Carbon (C) is combined with tungsten (W), molybdenum (Mo), chromium (Cr) or the like to form carbide of MC, M 6 C or M 23 C 6 type to contribute to grain refinement, Thereby improving grain boundary strength.
The carbon (C) is preferably added in an amount of 0.01 to 0.20% by weight based on the total weight of the nickel-base superalloy according to the present invention. If the addition amount of carbon (C) is less than 0.01% by weight, sufficient carbide is not formed and it is difficult to improve the strength. On the contrary, when the addition amount of carbon (C) is more than 0.20 wt%, too much carbide is formed and the ductility and workability are deteriorated.
Boron (B)
Boron (B) is segregated in grain boundaries to improve grain boundary strength and grain growth to improve creep characteristics.
The boron (B) is preferably added in an amount of 0.001-0.015 wt% of the total weight of the nickel-base superalloy according to the present invention. When the addition amount of boron (B) is less than 0.001% by weight, the effect of improving the creep characteristics is difficult to exhibit properly because the addition amount thereof is insignificant. On the other hand, when the addition amount of boron (B) exceeds 0.015% by weight, there is a problem that the oxidation resistance characteristic is lowered due to interaction with lanthanum (La) improving the oxidation resistance.
Manufacturing method of nickel base superalloy
FIG. 1 is a process flow chart showing a method of manufacturing a nickel-base superalloy according to an embodiment of the present invention.
1, a method of manufacturing a nickel-base superalloy according to an embodiment of the present invention includes a raw material mixing and dissolving step S110, a hot rolling step S120, a heat treatment step S130, and a cooling step S140. .
Raw material mixing and dissolution
In the raw material mixing and dissolution step S110, 20 to 26% by weight of Cr, 13 to 17% by weight of tungsten, 1 to 5% by weight of molybdenum and 1 to 5% 0.1 to 1.0% by weight of aluminum (Al), 0.01 to 0.06% by weight of lanthanum (La), 0.01 to 0.20% by weight of carbon (C) Ni) and unavoidable impurities are mixed and dissolved. At this time, by mixing and dissolving the raw materials in the molten metal, it is possible to produce an alloy in which the raw materials are uniformly mixed with each other.
In this step, the raw material may further contain 0.001 to 0.015% by weight of boron (B).
Hot rolling
In the hot rolling step (S120), the mixed and melted alloy is hot-rolled.
In this case, the hot rolling is preferably performed at a reduction rate of 40 to 80% at 1100 to 1250 ° C. When the hot rolling temperature is less than 1100 ° C, cracking may occur due to hot rolling. On the contrary, when the hot rolling temperature exceeds 1250 占 폚, crystal grains of the alloy are difficult to control due to microstructure control.
In addition, when the reduction ratio of the hot rolling is less than 40%, it is difficult to secure a uniform but fine structure. On the contrary, when the reduction rate of the hot rolling exceeds 80%, the rolling process time becomes longer and the productivity is lowered.
Heat treatment
In the heat treatment step (S130), the hot-rolled alloy is heat-treated.
Such a heat treatment can be subdivided into a step of solution heat treatment of the hot-rolled alloy at 1200 to 1280 ° C and a step of aging the solution-heat-treated alloy at 700 to 850 ° C. The aging treatment step can be selectively carried out according to the composition of the alloy.
That is, it is preferable to perform the solution heat treatment in which the hot-rolled alloy is maintained at 1100 to 1280 ° C for 5 to 180 minutes in a high temperature region, and then aged at 700 to 850 ° C for 4 to 8 hours .
At this time, when the solution heat treatment is performed outside the range of 1100 to 1280 ° C, the precipitates are not completely dissolved and the desired characteristics are not obtained. Here, the solution heat treatment is preferably performed for 5 to 180 minutes in which the homogenization treatment is sufficiently performed in the alloy, that is, to sufficiently dissolve and solidify the carbide and? 'Precipitate phase in the alloy, but no crystal grain growth occurs.
On the other hand, the aging treatment is carried out so as to uniformly distribute the γ 'precipitation phase of the alloy in the matrix and to precipitate carbides in the grain boundaries, thereby inducing sufficient aging so that there is no change in the structure even when exposed at the same aging temperature range It is preferably carried out at 700 to 850 ° C for 4 to 8 hours.
Cooling
In the cooling step (S140), the heat-treated alloy is cooled.
At this time, the cooling can be performed up to room temperature by water cooling or air cooling. The room temperature may be 1 to 40 ° C, but is not limited thereto.
Further, although not shown in the drawings, the method for manufacturing a nickel-base superalloy according to an embodiment of the present invention further includes an additional heat treatment step (not shown) performed after the cooling step S140 .
In the additional heat treatment step, the cooled alloy is further heat treated at 950 to 1100 ° C for 0.5 to 4 hours. As described above, additional heat treatment after the cooling step (S140) has an effect of further strengthening the grain boundary. In this case, as the additional heat treatment is carried out, alloy element components such as solid solution strengthened carbon (C) and chromium (Cr) are precipitated to cause damage to the solid solution strengthening effect, but additional precipitation strengthening effect is further produced. The mechanical properties are changed.
At this time, if the temperature and time for further heat treatment are out of the above range, it is not a stable region of the precipitate, so that generation and growth of precipitates may be disturbed and the desired effect may not be sufficiently exhibited.
The nickel-base superalloy alloy produced in the above-described processes (S110 to S140) is improved in creep characteristics by lowering the content of chromium (Cr) and silicon (Si), increasing the addition amount of manganese (Mn) By improving the oxidation resistance, oxidation resistance and creep characteristics can be improved at the same time.
The nickel-base superalloy according to the present invention has excellent oxidation resistance and creep characteristics even at a high temperature of 700 ° C or higher by controlling the alloy components and controlling the process conditions, It is suitable to be used as a part for chemical plant of reducing corrosive atmosphere.
Example
Hereinafter, the configuration and operation of the present invention will be described in more detail with reference to preferred embodiments of the present invention. It is to be understood, however, that the same is by way of illustration and example only and is not to be construed in a limiting sense.
The contents not described here are sufficiently technically inferior to those skilled in the art, and a description thereof will be omitted.
1. Specimen Manufacturing
Specimens according to Examples 1 to 11 and Comparative Examples 1 to 3 were prepared with the composition shown in Table 1 and the process conditions shown in Table 2.
[Table 1] (unit:% by weight)
[Table 2]
2. Evaluation of mechanical properties
Table 3 shows the results of evaluation of mechanical properties of the specimens according to Examples 1 to 11 and Comparative Examples 1 to 3.
[Table 3]
(YS): 195 to 300 MPa, tensile strength (TS): 420 to 580 MPa and elongation (EL) at 700 ° C for the specimens according to Examples 1 to 11, (YS): 160 to 200 MPa, tensile strength (TS): 235 to 300 MPa and elongation (EL): 48 to 59% at a high temperature of 900 캜 .
It can be seen that the yield strength (YS) and the tensile strength (TS) at 700 ° C and 900 ° C of the specimens of Comparative Examples 1 to 3 are not significantly different from those of Examples 1 to 11. Therefore, it was confirmed that the specimens according to Examples 1 to 11 exhibited similar mechanical properties to the specimens according to Comparative Examples 1 to 3 at high temperature in spite of the fact that cobalt (Co) was not added.
2 is a graph showing the creep strain rates of the specimens according to Examples 1 to 6 and Comparative Example 2 over time.
As shown in FIG. 2, the creep test carried out under the conditions of 900 ° C. and 60 MPa showed that the creep life of Examples 2 to 6 is shorter than that of Comparative Example 2, which is a commercial alloy. On the other hand, in Example 1, the final creep lifetime was 1197 hours, which is about three times that of Comparative Example 2.
3 is a graph showing the creep characteristic results of the specimens according to Examples 1 to 6 and Comparative Examples 1 and 3. The stress graph according to the LMP (Larson-Miller Parameter) shows that the higher the stress in the same LMP, the better the creep characteristics.
As shown in FIG. 3, Examples 2 to 6 showed no creep characteristics superior to Comparative Examples 1 and 3, whereas Example 1 showed clear creep characteristics superior to Comparative Examples 1 and 3.
4 is a graph showing the results of repeated oxidation characteristics for the specimens according to Example 1, Examples 7 to 11, and Comparative Example 2. More specifically, FIG. 4 is a graph showing the results of repeated oxidation of the alloys of Example 1, Examples 7 to 11, Was maintained at 1150 ° C for 15 minutes and then maintained at room temperature for 5 minutes.
As shown in FIG. 4, all of the specimens according to Example 1, Examples 7 to 11, and Comparative Example 2 showed linearly decreasing tendency with time. As a result, it was confirmed that Example 1 and Examples 7 to 11 exhibited oxidation resistance substantially similar to Comparative Example 2 which is a commercial alloy.
Although the preferred embodiments of the present invention have been disclosed for illustrative purposes, those skilled in the art will appreciate that various modifications, additions and substitutions are possible, without departing from the scope and spirit of the invention as disclosed in the accompanying claims. These changes and modifications may be made without departing from the scope of the present invention. Accordingly, the scope of the present invention should be determined by the following claims.
S110: Raw material mixing and dissolution step
S120: Hot rolling step
S130: heat treatment step
S140: cooling step
Claims (9)
The nickel-base superalloy
(YS): 195 to 300 MPa, tensile strength (TS): 420 to 580 MPa and elongation (EL): 35 to 55% Super heat resistant alloy.
The nickel-base superalloy
(YS) of 160 to 200 MPa, a tensile strength (TS) of 235 to 300 MPa and an elongation (EL) of 48 to 59% under a high temperature condition of 900 占 폚. Base heat resistant alloy.
(b) hot rolling the mixed and dissolved alloy;
(c) heat treating the hot-rolled alloy; And
and (d) cooling the heat-treated alloy. The method for manufacturing a superalloy article of a nickel-base superalloy according to claim 1,
In the step (b)
The hot rolling
Resistant alloy at a reduction rate of 40 to 80% at 1100 to 1250 占 폚.
The step (c)
(c-1) subjecting the hot-rolled alloy to a solution heat treatment at 1200 to 1280 占 폚; And
(c-2) aging the solution-heat-treated alloy at 700 to 850 ° C.
After the step (d)
(e) the cooled alloy is subjected to additional heat treatment at 950 to 1100 ° C for 0.5 to 4 hours, thereby producing a nickel-base superalloy having excellent oxidation resistance and creep characteristics.
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020140164756A KR101604598B1 (en) | 2014-11-24 | 2014-11-24 | Ni-based superalloy with excellent oxidization-resistance and creep property and method of manufacturing the same |
| US14/564,686 US20160145729A1 (en) | 2014-11-24 | 2014-12-09 | Ni-BASED SUPERALLOY WITH EXCELLENT OXIDIZATION RESISTANCE AND CREEP PROPERTY AND METHOD OF MANUFACTURING THE SAME |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020140164756A KR101604598B1 (en) | 2014-11-24 | 2014-11-24 | Ni-based superalloy with excellent oxidization-resistance and creep property and method of manufacturing the same |
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| Publication Number | Publication Date |
|---|---|
| KR101604598B1 true KR101604598B1 (en) | 2016-03-21 |
Family
ID=55651094
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| KR1020140164756A KR101604598B1 (en) | 2014-11-24 | 2014-11-24 | Ni-based superalloy with excellent oxidization-resistance and creep property and method of manufacturing the same |
Country Status (2)
| Country | Link |
|---|---|
| US (1) | US20160145729A1 (en) |
| KR (1) | KR101604598B1 (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20190094624A (en) | 2018-02-05 | 2019-08-14 | 창원대학교 산학협력단 | Method of heat treatment of ni-base superalloy containing niobium for excellent interfacial properties of grain boundaries and ni-base superalloy heat-treated thereby |
| WO2019164062A1 (en) * | 2018-02-26 | 2019-08-29 | 한국기계연구원 | Ni-based superalloy for high-temperature fastening member, and manufacturing method therefor |
| KR20190113456A (en) * | 2018-03-28 | 2019-10-08 | 한국기계연구원 | Wrought nickel base superalloys for forging having excellent creep property and method for manufacturing the same |
| KR20200073110A (en) | 2018-12-13 | 2020-06-23 | 부공산업 주식회사 | Chromium base alloy replacing cobalt base with high temperature strength and oxidation resistance at high temperature |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112553505A (en) * | 2020-12-25 | 2021-03-26 | 江苏新核合金科技有限公司 | Nickel-based plate and preparation method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2007018593A1 (en) * | 2005-07-20 | 2007-02-15 | Damascus Steel Casting Company | Nickel-base alloy and articles made therefrom |
| JP2011084812A (en) | 2009-09-15 | 2011-04-28 | Hitachi Ltd | HIGH-STRENGTH Ni-BASED FORGED SUPERALLOY, AND METHOD FOR PRODUCING THE SAME |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5078963A (en) * | 1990-02-14 | 1992-01-07 | Mallen Ted A | Method of preventing fires in engine and exhaust systems using high nickel mallen alloy |
-
2014
- 2014-11-24 KR KR1020140164756A patent/KR101604598B1/en active IP Right Grant
- 2014-12-09 US US14/564,686 patent/US20160145729A1/en not_active Abandoned
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2007018593A1 (en) * | 2005-07-20 | 2007-02-15 | Damascus Steel Casting Company | Nickel-base alloy and articles made therefrom |
| JP2011084812A (en) | 2009-09-15 | 2011-04-28 | Hitachi Ltd | HIGH-STRENGTH Ni-BASED FORGED SUPERALLOY, AND METHOD FOR PRODUCING THE SAME |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20190094624A (en) | 2018-02-05 | 2019-08-14 | 창원대학교 산학협력단 | Method of heat treatment of ni-base superalloy containing niobium for excellent interfacial properties of grain boundaries and ni-base superalloy heat-treated thereby |
| WO2019164062A1 (en) * | 2018-02-26 | 2019-08-29 | 한국기계연구원 | Ni-based superalloy for high-temperature fastening member, and manufacturing method therefor |
| KR20190113456A (en) * | 2018-03-28 | 2019-10-08 | 한국기계연구원 | Wrought nickel base superalloys for forging having excellent creep property and method for manufacturing the same |
| KR102139177B1 (en) * | 2018-03-28 | 2020-07-30 | 한국기계연구원 | Wrought nickel base superalloys for forging having excellent creep property and method for manufacturing the same |
| KR20200073110A (en) | 2018-12-13 | 2020-06-23 | 부공산업 주식회사 | Chromium base alloy replacing cobalt base with high temperature strength and oxidation resistance at high temperature |
Also Published As
| Publication number | Publication date |
|---|---|
| US20160145729A1 (en) | 2016-05-26 |
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