KR100622746B1 - Method for manufacturing of turbin housing for automobile - Google Patents
Method for manufacturing of turbin housing for automobile Download PDFInfo
- Publication number
- KR100622746B1 KR100622746B1 KR1020040089945A KR20040089945A KR100622746B1 KR 100622746 B1 KR100622746 B1 KR 100622746B1 KR 1020040089945 A KR1020040089945 A KR 1020040089945A KR 20040089945 A KR20040089945 A KR 20040089945A KR 100622746 B1 KR100622746 B1 KR 100622746B1
- Authority
- KR
- South Korea
- Prior art keywords
- weight
- manufacturing
- turbine housing
- present
- silicon
- Prior art date
Links
Images
Classifications
-
- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01D—NON-POSITIVE DISPLACEMENT MACHINES OR ENGINES, e.g. STEAM TURBINES
- F01D25/00—Component parts, details, or accessories, not provided for in, or of interest apart from, other groups
- F01D25/28—Supporting or mounting arrangements, e.g. for turbine casing
Abstract
본 발명은 자동차용 터빈 하우징의 제조방법에 관한 것으로서, 터빈 하우징을 제조하기 위한 오스테나이트계 구상흑연 주철을 노말라이징 열처리를 한 다음, 규화물 생성을 억제하여 인성을 향상시킬 수 있도록 제어 냉각을 적용하고, 실리콘 및 마그네슘의 함량을 제하여 불순물로 인한 결함 발생을 억제하는 자동차용 터빈 하우징의 제조방법에 관한 것이다.The present invention relates to a method for manufacturing a turbine housing for an automobile, the austenitic nodular cast iron for manufacturing a turbine housing is subjected to normalized heat treatment, and then controlled cooling is applied to improve the toughness by suppressing silicide generation and The present invention relates to a method for manufacturing a turbine housing for automobiles by suppressing defects caused by impurities by reducing the content of silicon and magnesium.
상기의 목적을 달성하기 위하여 본 발명은, 철(Fe)을 주재로 하고 여기에 니켈(Ni) 34 ~ 38중량%, 실리콘(Si) 4.8 ~ 5.3중량%, 마그네슘(Mg) 0.03 ~ 0.07중량%, 탄소(C) 2.0중량% 이하, 몰리브덴(Mo) 0.2 ~ 0.6중량%, 크롬(Cr) 1.6 ~ 2.2중량%를 함유하되 900 ~ 940℃의 온도로 3 ~ 5시간 동안, 노말라이징 열처리를 한 다음, 서서히 480 ~ 520℃까지는 로냉하고, 나머지는 공랭처리하는 자동차용 터빈 하우징의 제조방법을 제공하고자 한다. In order to achieve the above object, the present invention is based on iron (Fe), which is 34 to 38% by weight of nickel (Ni), 4.8 to 5.3% by weight of silicon (Si), 0.03 to 0.07% by weight of magnesium (Mg) , Carbon (C) 2.0% by weight or less, molybdenum (Mo) 0.2 to 0.6% by weight, chromium (Cr) containing 1.6 to 2.2% by weight at the temperature of 900 ~ 940 ℃ for 3 to 5 hours, the normalized heat treatment Next, to slowly provide a method of manufacturing a turbine housing for the car to be cooled to 480 ~ 520 ℃ slowly, the remaining air-cooled.
자동차, 터빈 하우징, 제조방법Automotive, Turbine Housing, Manufacturing Method
Description
도 1은 본 발명에 따른 자동차용 터빈 하우징 합금의 열처리 후, 충격시험 결과를 나타내는 그래프,1 is a graph showing the impact test results after the heat treatment of the automotive turbine housing alloy according to the present invention,
도 2a 및 도 2b는 본 발명에 따른 자동차용 터빈 하우징 합금의 미세조직을 나타내는 비교예 및 실시예이다. 2A and 2B are comparative examples and examples showing a microstructure of an automotive turbine housing alloy according to the present invention.
본 발명은 자동차용 터빈 하우징의 제조방법에 관한 것으로서, 더욱 상세하게는 터빈 하우징을 제조하기 위한 오스테나이트계 구상흑연 주철을 노말라이징 열처리를 한 다음, 규화물 생성을 억제하여 인성을 향상시킬 수 있도록 제어 냉각을 적용하고, 실리콘 및 마그네슘의 함량을 제하여 불순물로 인한 결함 발생을 억제하는 자동차용 터빈 하우징의 제조방법에 관한 것이다.The present invention relates to a method for manufacturing a turbine housing for an automobile, and more particularly, to normalize heat treatment of austenitic nodular cast iron for manufacturing a turbine housing, and then to control the silicide generation to improve toughness. The present invention relates to a method for manufacturing a turbine housing for an automobile in which cooling is applied and content of silicon and magnesium is suppressed to suppress defects caused by impurities.
일반적으로, 자동차의 터빈 하우징은 고온에서 장시간 노출되는 부품이므로 고온 강도 및 크립 강도가 우수한 재질이 요구되는 바, 종래에는 실리콘 함유량이 높은 페라이트계 구상흑연주철이 많이 사용되었지만 최근들어 자동차의 출력 향상 등으로 배기가스 온도가 상승하게 되므로 종래의 페라이트계 구상흑연 주철재로는 그 사용에 한계가 있다.In general, since a turbine housing of an automobile is a component exposed to a long time at a high temperature, a material having excellent high temperature strength and creep strength is required. In the past, ferrite-based nodular cast iron having a high silicon content was used, but in recent years, the output of an automobile has been improved. As the exhaust gas temperature increases, the use of the conventional ferritic spheroidal graphite cast iron material is limited.
이에, 니켈 함유량이 높은 오스테나이트계 구상흑연 주철재가 개발 및 사용되고 있다.Accordingly, austenitic spherical graphite cast iron materials having a high nickel content have been developed and used.
이러한 오스테나이트계 구상흑연 주철재는 니켈(Ni) 함유량이 34 ~ 38중량%이고 ,실리콘(Si) 함유량이 5.0 ~ 6.0중량% 정도로서, 기존 페라이트계 구상흑연 주철재보다 가격이 훨씬 비싸고, 기본적으로 크롬(Cr) 1.6 ~ 2.2중량%, 몰리브덴(Mo) 0.2 ~ 0.6중량% 등이 함유되어 있어 인성이 낮은 문제점이 있다. The austenitic nodular cast iron material has a nickel (Ni) content of 34 to 38% by weight, and a silicon (Si) content of about 5.0 to 6.0% by weight, much more expensive than the existing ferritic nodular graphite cast iron material, and basically Since chromium (Cr) 1.6 to 2.2% by weight, molybdenum (Mo) 0.2 to 0.6% by weight is contained, there is a problem of low toughness.
이러한 문제를 해결하기 위하여 노말라이징 열처리를 실시하는 바, 상기 노말라이징 열처리는 터빈 하우징의 강도를 저하시켜 인성을 향상시키는 효과가 있으나, 오스테나이트계 구상흑연 주철재의 경우, 이러한 노말라이징 열처리는 냉각시의 규화물 생성으로 인하여 충격특성의 개선이 어려운 문제점이 있으며, 또한 첨가된 실리콘은 구상화제인 마그네슘과 반응하여 마그네슘 실리케이트와 같은 불순물에 의한 결함 등이 발생하여 엔진 동작 중에 내부균열로 인한 엔진의 파손 등이 일어나는 문제점이 있다. In order to solve this problem, the normalizing heat treatment is performed. The normalizing heat treatment lowers the strength of the turbine housing, thereby improving toughness. Impairment of the impact characteristics is difficult due to the formation of silicides in the city, and the added silicon reacts with magnesium, a spheroidizing agent, to cause defects due to impurities such as magnesium silicate, resulting in engine damage due to internal cracking during engine operation. There is a problem that occurs.
따라서, 본 발명은 상기와 같은 문제점을 해결하기 위해 발명한 것으로서, 철을 주재로 하고, 여기에 니켈(Ni), 실리콘(Si), 마그네슘(Mg), 탄소(C), 몰리브덴(Mo) 그리고, 크롬(Cr)을 적절히 함유시킨 자동차의 멤버용 소재 조성물과, 이러한 조성물의 소재를 노말라이징 열처리를 실시하는 자동차용 터빈 하우징의 제조방법을 개발한다.Therefore, the present invention has been invented to solve the above problems, based on iron, nickel (Ni), silicon (Si), magnesium (Mg), carbon (C), molybdenum (Mo) and And a method for manufacturing a member material composition for automobiles containing appropriately chromium (Cr) and a turbine housing for automobiles which is subjected to normalizing heat treatment of the material of such compositions.
즉, 본 발명의 주된 목적은 철(Fe)을 주재로 하고 여기에 니켈(Ni) 34 ~ 38중량%, 실리콘(Si) 4.8 ~ 5.3중량%, 마그네슘(Mg) 0.03 ~ 0.07중량%, 탄소(C) 2.0중량% 이하, 몰리브덴(Mo) 0.2 ~ 0.6중량%, 크롬(Cr) 1.6 ~ 2.2중량%를 함유되어 있는 것을 특징으로 하는 자동차용 터빈 하우징의 소재 조성물과, 이러한 조성물의 소재를, 규화물 생성 억제를 통해 인성을 향상시키고, 실리콘 및 마그네슘 첨가로 인한 불순물에 의한 결함 생성을 억제할 수 있는 자동차용 터빈 하우징의 제조방법을 제공하는데 그 목적이 있다.
That is, the main object of the present invention is based on iron (Fe), which is 34 to 38% by weight of nickel (Ni), 4.8 to 5.3% by weight of silicon (Si), 0.03 to 0.07% by weight of magnesium (Mg), carbon ( C) 2.0% by weight or less, molybdenum (Mo) 0.2 to 0.6% by weight, chromium (Cr) 1.6 to 2.2% by weight of the material composition of the automotive turbine housing, and the material of such a composition It is an object of the present invention to provide a method of manufacturing a turbine housing for an automobile that can improve toughness through suppression of production and suppress generation of defects caused by impurities due to addition of silicon and magnesium.
이하, 상기와 같은 목적을 달성하기 위한 본 발명의 특징에 대해 설명하면 다음과 같다. Hereinafter, the features of the present invention for achieving the above object are as follows.
본 발명에 따른 자동차용 터빈 하우징의 제조방법은, 철(Fe)을 주재로 하고 여기에 니켈(Ni) 34 ~ 38중량%, 실리콘(Si) 4.8 ~ 5.3중량%, 마그네슘(Mg) 0.03 ~ 0.07중량%, 탄소(C) 2.0중량% 이하, 몰리브덴(Mo) 0.2 ~ 0.6중량%, 크롬(Cr) 1.6 ~ 2.2중량%로 이루어진 구상흑연주철을 노말라이징 열처리를 한 다음, 서서히 480 ~ 520℃까지는 로냉하고, 나머지는 공랭처리하여 제조하며, 특히 상기 노말라이징 열 처리는, 온도 900 ~ 940℃, 시간은 3 ~ 5시간으로 설정한 것을 특징으로 한다. In the method of manufacturing a turbine housing for automobiles according to the present invention, iron (Fe) is mainly used, and nickel (Ni) 34 to 38% by weight, silicon (Si) 4.8 to 5.3% by weight, magnesium (Mg) 0.03 to 0.07 Spheroidal graphite cast iron composed of weight%, 2.0% by weight or less of carbon (C), 0.2 to 0.6% by weight of molybdenum (Mo), and 1.6 to 2.2% by weight of chromium (Cr) is subjected to normal heat treatment, and then gradually to 480 to 520 ° C. It is quenched and the remainder is air-cooled, and the normalizing heat treatment is characterized in that the temperature is set to 900 to 940 ° C and the time is set to 3 to 5 hours.
이하, 첨부도면을 참조하여 본 발명의 구성에 대해 상세하게 설명하면 다음과 같다. Hereinafter, the configuration of the present invention with reference to the accompanying drawings in detail.
도 1은 본 발명에 따른 자동차용 터빈 하우징 합금의 열처리 후, 충격시험 결과를 나타내는 그래프이며, 도 2a 및 도 2b는 본 발명에 따른 자동차용 터빈 하우징 합금의 미세조직을 나타내는 비교예 및 실시예이다. 1 is a graph showing the impact test results after the heat treatment of the automotive turbine housing alloy according to the present invention, Figures 2a and 2b are comparative examples and examples showing the microstructure of the automotive turbine housing alloy according to the present invention. .
본 발명은 고온 강도 및 크립 특성이 우수한 자동차용 터빈 하우징의 제조방법에 있어서, 오스테나이트계 구상흑연주철(Austenitic Ductile Cast Iron)에 관한 것으로서, 철(Fe)을 주재로 하고 여기에 니켈(Ni) 34 ~ 38중량%, 실리콘(Si) 4.8 ~ 5.3중량%, 마그네슘(Mg) 0.03 ~ 0.07중량%, 탄소(C) 2.0중량% 이하, 몰리브덴(Mo) 0.2 ~ 0.6중량%, 크롬(Cr) 1.6 ~ 2.2중량%를 함유하되 900 ~ 940℃의 온도로 3 ~ 5시간 동안, 노말라이징 열처리를 한 다음, 서서히 480 ~ 520℃까지는 로냉하고, 나머지는 공랭처리하게 된다.BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an austenitic ductile cast iron (Austenitic Ductile Cast Iron) in a method of manufacturing an automotive turbine housing having excellent high temperature strength and creep characteristics. 34 to 38% by weight, silicon (Si) 4.8 to 5.3%, magnesium (Mg) 0.03 to 0.07%, carbon (C) 2.0% or less, molybdenum (Mo) 0.2 to 0.6%, chromium (Cr) 1.6 It contains ~ 2.2% by weight, but the normalizing heat treatment for 3 to 5 hours at a temperature of 900 ~ 940 ℃, then slowly cooled to 480 ~ 520 ℃, the rest is air-cooled.
여기서, 상기 오스테나이트계 구상흑연주철은 고온 내 크립 특성이 우수하여 자동차 터빈 하우징 등과 같은 고온에서 주로 사용되는 재질로서, 상기 니켈(Ni)은 그 함유량이 많을수록 고온 내 크립 특성이 향상되는 바, 그 함유량이 38중량%를 초과하면 가격 상승으로 인해 바람직하지 않으며, 34중량% 미만일 경우, 고온 강도성 확보 및 열팽창 계수의 저하 등과 같은 장점을 발휘하지 못하는 문제점이 있어 바람직하지 않다. Here, the austenitic spheroidal graphite cast iron is a material that is mainly used at high temperatures such as automobile turbine housings because of excellent creep resistance at high temperatures, and the nickel (Ni) is improved in creep resistance at high temperatures as its content increases. If the content exceeds 38% by weight, it is not preferable due to the increase in price, and if the content is less than 34% by weight, there is a problem in that it does not exhibit advantages such as securing high-temperature strength and lowering of the thermal expansion coefficient.
실리콘(Si)은 열팽창계수를 저하시켜 치수 안정 및 열피로 특성을 향상시키 는 조성물로서, 그 함유량이 5.3을 초과하면 마그네슘 실리케이트 불순물로 인한 결함이 발생하여 바람직하지 않으며, 4.8중량% 미만이면 열팽창 계수가 높아 치수 안정 및 열피로 특성이 불안정하여 바람직하지 않다. Silicon (Si) is a composition that lowers the coefficient of thermal expansion and improves the dimensional stability and thermal fatigue characteristics. If the content exceeds 5.3, defects due to magnesium silicate impurities occur, which is not preferable, and the coefficient of thermal expansion is less than 4.8 wt%. It is not preferable because of high dimensional stability and thermal fatigue characteristics.
따라서, 니켈 함유량을 34 ~ 38중량%로 하고, 실리콘 함유량을 4.8 ~ 5.3중량%로 한다.Therefore, nickel content is 34-38 weight% and silicon content is 4.8-5.3 weight%.
이때, 고온 강도 및 크립 특성을 향상시키기 위해 몰리브덴(Mo)과 크롬(Cr)을 추가적으로 첨가시킨다. At this time, molybdenum (Mo) and chromium (Cr) are further added to improve high temperature strength and creep characteristics.
추가적으로 첨가되는 몰리브덴(Mo) 및 크롬(Cr) 함유량은 각각 0.2 ~ 0.6중량%, 1.6 ~ 2.2중량%가 적합하다. Additional molybdenum (Mo) and chromium (Cr) content is preferably 0.2 to 0.6% by weight and 1.6 to 2.2% by weight, respectively.
왜냐하면, 이 범위보다 미만인 경우, 고온 내 크립 특성이 부족하고, 상기 범위를 초과할 경우 Mo2C, (Fe, Cr)3C 등의 탄화물의 분산석출로 인한 취성의 증대 및 탄소 고갈에 따른 유동성저하, 수축결함 발생 등으로 바람직하지 않기 때문이다.If less than this range, the creep resistance at high temperature is insufficient, and if it exceeds the above range, the brittleness due to dispersion precipitation of carbides such as Mo 2 C, (Fe, Cr) 3 C, and fluidity due to carbon depletion It is because it is unpreferable because of a fall, shrinkage defects, etc.
이와 더불어 마그네슘(Mg) 함유량은 0.03 ~ 0.07중량%가 적합하다. In addition, the magnesium (Mg) content is appropriately 0.03 to 0.07% by weight.
왜냐하면, 마그네슘 함유량이 0.03중량%미만일 경우, 흑연의 구상화가 안되고, 0.07중량%를 초과할 경우, 불순물에 의한 결함이 발생하기 때문이다. This is because when the magnesium content is less than 0.03% by weight, the graphite is not spheroidized, and when the magnesium content is more than 0.07% by weight, defects due to impurities are generated.
또한, 탄소(C)의 함유량은 2.0중량% 이상이 적합한데, 그 이유는 탄소 함유량이 이 범위보다 높을 경우에는 초정 흑연이 생성되고, 이 범위보다 낮을 경우에는 유동성 저하 및 경도상승으로 인한 가공성이 떨어져 바람직하지 않기 때문이다. In addition, the content of carbon (C) is preferably 2.0% by weight or more, because if the carbon content is higher than this range, primary graphite is formed, and if it is lower than this range, workability due to fluidity decrease and hardness increase is obtained. Because apart is not desirable.
한편, 오스테나이트에 고용되어 있는 실리콘(Si)은 탄소(C)가 급냉되면 규화물이 생성되어 인성이 저하되는 문제점이 있어 이를 해결하기 위하여 초기 480 ~ 520℃까지는 로냉으로 냉각을 느리게 진행하게 된다.On the other hand, silicon (Si) dissolved in austenite has a problem that silicide is formed when carbon (C) is quenched and the toughness is lowered. Thus, in order to solve the problem, the cooling is slowly performed by quenching up to 480 to 520 ° C.
이와 같이 로냉을 통해 충분히 확산을 통하여 페라이트 기지에 고용되어 페라이트를 강화 시킨다. 그 이후 온도에서는 공냉을 통하여 냉각과정을 단축시킨다.In this way, through the cooling to the ferrite base through sufficient diffusion to strengthen the ferrite. After that, the cooling process is shortened by air cooling.
한편, 표 1은 비교예 및 실시예의 화학성분의 함량을 나타내는 것으로서, 도 1은 기존의 열처리 방법 및 본 발명에 따른 열처리 방법에 의거하여 충격시험을 실시한 결과를 나타내었다.On the other hand, Table 1 shows the contents of the chemical components of Comparative Examples and Examples, Figure 1 shows the results of the impact test based on the conventional heat treatment method and the heat treatment method according to the present invention.
이를 통해 본 발명에 따른 자동차용 터빈 하우징의 제조방법을 적용시 충격 특성이 향상됨을 확인할 수 있었다.Through this, it was confirmed that the impact characteristics are improved when applying the manufacturing method of the automotive turbine housing according to the present invention.
또한, 상기 비교예와 실시예의 합금의 미세조직을 관찰한 결과, 비교예에서 발생되었던 불순물로 인한 결함이 개선된 것을 실시예를 통해 알 수 있었다.In addition, as a result of observing the microstructure of the alloy of the comparative example and the embodiment, it can be seen through the examples that the defects due to impurities generated in the comparative example is improved.
상술한 바와 같이, 본 발명에 따른 자동차용 터빈 하우징의 제조방법에 의하 면, 다음과 같은 효과가 있다.As described above, according to the manufacturing method of the automotive turbine housing according to the present invention, there are the following effects.
1) 열처리를 통해 규화물 생성에 의한 충격 특성 저하를 방지하여 인성을 향상시킴으로써, 내구성을 확보한다.1) The durability is ensured by improving the toughness by preventing the impact property deterioration by the silicide generation through heat treatment.
2) 합금 원소의 제한된 첨가를 통해 불순물에 의한 결함 발생을 억제하는 효과가 있다. 2) There is an effect of suppressing defects caused by impurities through limited addition of alloying elements.
Claims (2)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020040089945A KR100622746B1 (en) | 2004-11-05 | 2004-11-05 | Method for manufacturing of turbin housing for automobile |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020040089945A KR100622746B1 (en) | 2004-11-05 | 2004-11-05 | Method for manufacturing of turbin housing for automobile |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| KR20060040375A KR20060040375A (en) | 2006-05-10 |
| KR100622746B1 true KR100622746B1 (en) | 2006-09-19 |
Family
ID=37147358
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| KR1020040089945A KR100622746B1 (en) | 2004-11-05 | 2004-11-05 | Method for manufacturing of turbin housing for automobile |
Country Status (1)
| Country | Link |
|---|---|
| KR (1) | KR100622746B1 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101949311B (en) * | 2009-11-18 | 2013-06-05 | 西峡县众德汽车部件有限公司 | Turbocharger shell and preparation method thereof |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06228713A (en) * | 1993-02-03 | 1994-08-16 | Hitachi Metals Ltd | Austenitic heat resistant cast steel excellent in strength at high temperature and machinability and exhaust system parts using same |
| KR19990088161A (en) * | 1998-05-12 | 1999-12-27 | 레비스 스테픈 이 | Heat treated, spray formed superalloy articles and method of making the same |
| KR20040007212A (en) * | 2000-02-29 | 2004-01-24 | 제너럴 일렉트릭 캄파니 | Nickel base superalloys and turbine components fabricated therefrom |
| JP2004107724A (en) | 2002-07-25 | 2004-04-08 | Toyota Central Res & Dev Lab Inc | Cast alloy for turbine wheel superior in high-temperature property, and casting therefor |
-
2004
- 2004-11-05 KR KR1020040089945A patent/KR100622746B1/en not_active IP Right Cessation
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06228713A (en) * | 1993-02-03 | 1994-08-16 | Hitachi Metals Ltd | Austenitic heat resistant cast steel excellent in strength at high temperature and machinability and exhaust system parts using same |
| KR19990088161A (en) * | 1998-05-12 | 1999-12-27 | 레비스 스테픈 이 | Heat treated, spray formed superalloy articles and method of making the same |
| KR20040007212A (en) * | 2000-02-29 | 2004-01-24 | 제너럴 일렉트릭 캄파니 | Nickel base superalloys and turbine components fabricated therefrom |
| JP2004107724A (en) | 2002-07-25 | 2004-04-08 | Toyota Central Res & Dev Lab Inc | Cast alloy for turbine wheel superior in high-temperature property, and casting therefor |
Also Published As
| Publication number | Publication date |
|---|---|
| KR20060040375A (en) | 2006-05-10 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| KR100856659B1 (en) | Heat and corrosion resistant cast stainless steels with improved high temperature strength and ductility | |
| JP3936849B2 (en) | Ferrite-based spheroidal graphite cast iron and exhaust system parts using the same | |
| WO2010070949A1 (en) | Spheroidal graphite cast iron | |
| US8540932B2 (en) | Ferritic spheroidal graphite cast iron | |
| WO2016052750A1 (en) | Austenitic heat-resistant cast steel having excellent thermal fatigue characteristics, and exhaust system component comprising same | |
| US20080092995A1 (en) | High-silicon ferritic heat-resistant cast iron having high-temperature strength and high oxidation resistance | |
| KR100435324B1 (en) | Cast iron with improved oxidation resistance at high temperature | |
| KR100622746B1 (en) | Method for manufacturing of turbin housing for automobile | |
| KR20130130490A (en) | Ferritic spheroidal cast iron for exhaust system | |
| JP3296509B2 (en) | Tough high carbon cementite alloy cast iron | |
| KR101676243B1 (en) | Heat resistant cast steel having superior high temperature strength and oxidation resistant | |
| KR101438825B1 (en) | Ferritic nodular cast iron | |
| JP2018154863A (en) | Spheroidal graphite cast iron and exhaust component | |
| KR20150028904A (en) | Heat resistant cast iron having excellent wear resistance at high temperature | |
| KR20190035746A (en) | Ferritic steel for turbochargers | |
| JPS6233744A (en) | Heat-resistant cast steel | |
| WO2018008674A1 (en) | Martensitic stainless steel for fuel injection member and fuel injection member using same | |
| KR20100007090A (en) | Ferritic nodular cast iron | |
| KR20050096228A (en) | Composition of turbin housing for automobile | |
| JPH0524977B2 (en) | ||
| JPH0359967B2 (en) | ||
| CN112853207A (en) | Heat-resistant steel for turbocharger component and smelting method thereof | |
| KR20130136335A (en) | Austenitic heat resisting cast steel for exhaust system | |
| WO2009002013A1 (en) | Cast iron for turbine housing/exhaust manifold | |
| KR20090025667A (en) | Method for manufacturing high strength ferritic cast steel parts |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A201 | Request for examination | ||
| E902 | Notification of reason for refusal | ||
| E701 | Decision to grant or registration of patent right | ||
| GRNT | Written decision to grant | ||
| LAPS | Lapse due to unpaid annual fee |