KR20120044155A - 400hv grade high hardness heat treated rail alloy, and method for manufacturing the same - Google Patents
400hv grade high hardness heat treated rail alloy, and method for manufacturing the same Download PDFInfo
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- KR20120044155A KR20120044155A KR1020100105577A KR20100105577A KR20120044155A KR 20120044155 A KR20120044155 A KR 20120044155A KR 1020100105577 A KR1020100105577 A KR 1020100105577A KR 20100105577 A KR20100105577 A KR 20100105577A KR 20120044155 A KR20120044155 A KR 20120044155A
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/04—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rails
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- 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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- 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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
Description
Embodiments of the present invention relate to a rail, and more particularly, to a 400 (Hv) class high hardness heat treated rail alloy and a method of manufacturing the same.
In general, the material used for railway rails is composed of a pearlite (base) structure, the five major elements of steel, carbon (C), silicon (Si), manganese (Mn), phosphorus (P), sulfur ( It is manufactured through a rolling process using high carbon steel having S) as a basic element.
Although the basic structure of these rail materials is made of pearlite, at the present time of the 21st century, the social demand for the function of the railroad in response to the increase in logistics and the high speed demands the railroad steel with better mechanical properties and safety. .
One embodiment of the present invention provides a 400Hv class high hardness heat-treated rail alloy that can increase the hardness of the rail by delaying the pearlite transformation by adding an alloy such as manganese (Mn), copper (Cu), molybdenum (Mo) do.
One embodiment of the present invention provides a method for producing a 400Hv-class high hardness heat treatment rail alloy, which can produce a high temperature heat treatment rail only by natural air cooling after rolling, without additional heat treatment equipment in the production of high hardness rail.
The problem to be solved by the present invention is not limited to the problem (s) mentioned above, and other object (s) not mentioned will be clearly understood by those skilled in the art from the following description.
400Hv class high hardness heat-treated rail alloy according to an embodiment of the present invention, the weight percent, carbon (C): 0.79 ~ 0.82%, silicon (Si): 0.2? 0.4%, Manganese (Mn): 1.45? 1.55%, phosphorus (P): 0.02% or less, sulfur (S): 0.02% or less, copper (Cu): 0.12 to 0.10%, nickel (Ni): 0.25% or less, chromium (Cr): 0.3% or less, molybdenum (Mo): 0.06 to 0.04%, vanadium (V): 0.06 to 0.04%, aluminum (Al): 0.01% or less, nitrogen (N): 0.008% or less, oxygen (O 2 ): 0.002% or less, and Consisting of the remaining iron (Fe) and other impurities.
The high hardness heat treatment rail alloy preferably has a surface hardness of 400 (Hv) or more.
400Hv class high hardness heat treatment rail alloy according to an embodiment of the present invention is a weight%, carbon (C): 0.79 ~ 0.82%, silicon (Si): 0.2? 0.4%, Manganese (Mn): 1.45? 1.55%, phosphorus (P): 0.02% or less, sulfur (S): 0.02% or less, copper (Cu): 0.12 to 0.10%, nickel (Ni): 0.25% or less, chromium (Cr): 0.3% or less, molybdenum (Mo): 0.06 to 0.04%, vanadium (V): 0.06 to 0.04%, aluminum (Al): 0.01% or less, nitrogen (N): 0.008% or less, oxygen (O 2 ): 0.002% or less, and Heating the rail material consisting of the remaining iron (Fe) and other impurities; Rolling the heated rail material; And naturally air-cooling the rolled rail material.
The heating step may include the step of heating the rail material in the furnace 1250 ~ 1200 degrees.
The rolling step may include rolling to a final rolling end temperature of 1000 ~ 950 degrees.
The natural air cooling step may include a step of naturally air cooling the rail material rolled to a final rolling end temperature of 1000 to 950 degrees from 1000 to 950 degrees to room temperature.
The high hardness heat treatment rail alloy is preferably made of a pearlite structure.
The high hardness heat-treated rail alloy may start the pearlite phase transformation at 625 W 5 degrees when the natural air-cooled and finish the transformation at 550 W 5 degrees.
The high hardness heat treatment rail alloy preferably has a surface hardness of 400 (Hv) or more.
Specific details of other embodiments are included in the detailed description and the accompanying drawings.
Advantages and / or features of the present invention and methods for achieving them will become apparent with reference to the embodiments described below in detail in conjunction with the accompanying drawings. However, the present invention is not limited to the embodiments disclosed below, but may be implemented in various different forms, only the present embodiments to make the disclosure of the present invention complete, and common knowledge in the art to which the present invention pertains. It is provided to fully inform the person having the scope of the invention, which is defined only by the scope of the claims. Like reference numerals refer to like elements throughout.
According to one embodiment of the present invention, by adding an alloy such as manganese (Mn), copper (Cu), molybdenum (Mo), it is possible to delay the pearlite transformation to increase the hardness of the rail.
According to one embodiment of the present invention, after rolling without additional heat treatment facilities in the production of high hardness rail, it is possible to produce a high hardness heat treatment rail only by natural air cooling.
1 is a view showing a continuous cooling curve (CCT) according to the continuous cooling of the rail material, to show that the supercooled structure is generated at a high cooling rate of more than 2 ℃ / s during continuous cooling.
2 is a view showing a continuous cooling curve (CCT) according to the continuous cooling of the rail material, to show that the pearlite structure is generated when cooling at a cooling rate similar to
3 is a manufacturing process diagram illustrating a method for manufacturing a 400Hv class high hardness heat treatment rail alloy according to an embodiment of the present invention.
Hereinafter, the present invention will be described in detail.
As the global high-speed rail market expands, there is a need for hardened rails with improved wear resistance over existing rails. In addition, in order to satisfy the PREMIUM grade rail, a hardness value of 35 mm directly below the surface of the rail head requires at least 380 (Hv).
In order to satisfy the above conditions, the existing heat treatment rails improve hardness through an additional heat treatment process after finishing rolling. However, the heat treatment facility installation site, equipment, time and manpower are wasted in order to undergo the reheating and cooling process.
Therefore, an embodiment of the present invention provides a high hardness heat treatment rail alloy having a surface hardness of 400 (Hv) or more and a manufacturing method thereof by natural cooling alone without undergoing a heat treatment step after rolling.
To this end, the components of the 400Hv class high hardness heat treatment rail alloy of the present invention is by weight, carbon (C): 0.79 ~ 0.82%, silicon (Si): 0.2? 0.4%, Manganese (Mn): 1.45? 1.55%, phosphorus (P): 0.02% or less, sulfur (S): 0.02% or less, copper (Cu): 0.12 to 0.10%, nickel (Ni): 0.25% or less, chromium (Cr): 0.3% or less, molybdenum (Mo): 0.06 to 0.04%, vanadium (V): 0.06 to 0.04%, aluminum (Al): 0.01% or less, nitrogen (N): 0.008% or less, oxygen (O2): 0.002% or less It consists of iron (Fe) and other impurities.
As described above, in the present invention, by adding an alloy such as manganese (Mn), copper (Cu), molybdenum (Mo), the pearlite transformation can be delayed to increase the hardness of the rail.
On the other hand, this invention provides the manufacturing method which can manufacture the high hardness heat-treated rail alloy which has a high hardness physical property by performing natural cooling on the cooling bed after a rolling process of the raw material (the said alloy component) heated by the heating furnace.
To this end, first, a material heated from 1250 to 1200 degrees in a heating furnace is subjected to natural air cooling from 1000 to 950 degrees, which is the final rolling end temperature, to room temperature (15 to 30 degrees) through a rolling process.
At this time, the cooling start temperature is all austenitized state of 1000 ~ 950 degrees. In this state, the pearlite phase transformation starts at about 625 degrees during natural cooling, and the transformation is terminated at around 550 degrees.
As can be seen in Figure 1, due to the perlite transformation delay due to the addition of the alloying component, the supercooled structure is generated at a rapid cooling rate of more than 2 ℃ / s during continuous cooling.
However, when cooled at a cooling rate of 1 ° C / s similar to natural cooling as shown in Figure 2, all the pearlite structure was generated and the hardness was higher than 400 (Hv).
Here, the reason for the air cooling (natural cooling) is to suppress the formation of the bainite and martensite structures, which are supercooled structures without additional heat treatment facilities, and to develop a hard rail having only pearlite structures.
Hereinafter, the composition range of the 400Hv class high hardness heat treatment rail alloy of the present invention will be described in detail.
Steel also contains alloying elements that are artificially added to improve various properties during steelmaking, but also contains trace amounts of residual elements that are mixed in raw materials such as pig iron and scrap iron. The impact cannot be ignored.
Among these residual elements, copper (Cu), nickel (Ni), cobalt (Co), arsenic (As), tungsten (W), molybdenum (Mo), and tin (Sb) are elements that can hardly be removed during steelmaking. It is fixed to steel as a substitution type, and relatively large amount of addition is required in order to change the property of steel.
In addition, elements such as carbon, hydrogen, and nitrogen are elements that can be partially removed in the steelmaking process and are fixed to the steel in an invasive type, and have a great influence on the properties of the steel even in a small amount.
Hereinafter, the composition range of the 400Hv class high hardness heat treatment rail alloy of the present invention will be described in earnest.
The content of carbon (C) is preferably 0.79 to 0.82 wt%.
Carbon is an important element that determines the strength and hardness of the material. If the content is less than 0.79%, the strength and hardness required by the rail of the present invention cannot be obtained. If the content exceeds 0.82%, the martensite structure is easily formed. Therefore, the content of carbon is preferably limited to 0.79 to 0.82%.
The content of silicon (Si) is preferably 0.2 to 0.4% by weight.
Silicon acts as a deoxidizer to remove oxygen during steelmaking. When the content of silicon is less than 0.2%, there is a problem in that a large amount of oxides are generated due to a slight deoxidation effect. When the content of silicon exceeds 0.4%, the strength is improved, but the toughness is deteriorated. Therefore, in the present invention, it is preferable to limit the content of silicon to 0.2 ~ 0.4%.
The content of manganese (Mn) is preferably 1.45 to 1.55 wt%.
Manganese is used as a deoxidizer and a reinforcing element in materials in the steelmaking process, and it combines with sulfur (S) to form manganese emulsion (MnS) to inhibit the formation of iron emulsion (FeS), which causes hot brittleness. In order to improve this effect, it is preferable to contain 1.45% or more.
However, when the content of manganese exceeds 1.55%, segregation is liable to occur, and martensite, which is a local hard tissue, is generated in the segregation portion in the cooling process, which adversely affects the hot workability. Therefore, the content of manganese is preferably limited to 1.45 to 1.55%.
The content of phosphorus (P) is preferably 0.02% by weight or less.
Phosphorus acts to increase the strength of the material, but it is preferable to keep the content as low as possible because it plays a role in causing heat treatment of the material and tempering brittleness of the material used at high temperature. Therefore, in the present invention, it is preferable to limit the content of phosphorus to 0.02% or less.
The content of sulfur (S) is preferably 0.02% by weight or less.
Sulfur acts together with manganese contained in the material to form manganese compounds (MnS), which is a harmful element that impairs impact toughness and harms high temperature strength. Therefore, in the present invention, it is preferable to limit the content of sulfur to 0.02% or less.
The content of copper (Cu) is preferably 0.1 to 0.12% by weight.
Copper is easily incorporated from ores and the like, and the present invention is preferably limited to 0.12% or less. Copper has a solid solution effect due to solid solution in ferrite at room temperature, which slightly increases strength and hardness, but decreases elongation.
In the steel containing copper, hot workability is a problem, especially when it contains more than 0.12%, it causes red brittleness. This is because copper has a lower oxidation rate than iron (Fe) at high temperature, so it is ubiquitous on the steel surface and penetrates into the steel during hot working.
However, this phenomenon can be remarkably improved by addition of nickel (Ni) and molybdenum (Mo). In addition, even if a relatively small amount of copper is contained, the corrosion resistance of the steel is significantly improved in the air and seawater. Coexistence of copper and phosphorus (P) is more effective in improving the corrosion resistance.
In order to achieve this effect, it is desirable to keep the copper content at least 0.1% or more. That is, in the present invention, it is preferable to limit the content of copper to 0.1 ~ 0.12%.
The content of nickel (Ni) is preferably 0.25% by weight or less.
Nickel refines the structure of the steel and strengthens the base because it is well employed in austenite and ferrite. In addition, when coexisted with chromium (Cr) or molybdenum (Mo), it exhibits excellent hardenability and facilitates heat treatment of large steels. Since nickel is an austenite stabilizing element, it forms austenitic stainless steel and heat resistant steel in combination with chromium. Nickel significantly improves the low temperature toughness of steel and does not impair weldability or malleability.
In addition, nickel slows the diffusion of carbon (C) and nitrogen (N), thereby preventing deterioration of heat-resistant steel, and also has characteristics such as expansion rate, stiffness rate, and ceramic rate. In other words, Fe-36% Ni steel has a coefficient of thermal expansion near zero at room temperature, and thus is widely used as an electronic material and a special material. Nickel is thus the most important and common alloying element with chromium.
The content of chromium (Cr) is preferably 0.3% by weight or less.
Chromium is an element that controls strength and toughness and prevents decarburization by lowering carbon activity. However, it is preferable to set the upper limit to 0.3% because increasing the content of chromium promotes the softening characteristics after heat treatment of the steel. That is, in the present invention, it is preferable to limit the content of chromium to 0.3% or less.
The content of molybdenum (Mo) is preferably 0.04 to 0.06% by weight.
Molybdenum is added at 0.04% or more to increase the high temperature strength and to increase the resistance to temper brittleness. However, molybdenum has a problem in that weldability is lowered when its content exceeds 0.06%. Therefore, the content of molybdenum is preferably limited to 0.04 to 0.06%.
The content of vanadium (V) is preferably 0.04 to 0.06% by weight.
Vanadium has a large carbide formation ability, making fine carbides and making the structure of the steel finer, so it is widely used from high tensile steel to various tool steels. The tempering softening resistance is also better than molybdenum (Mo). Vanadium greatly improves the high temperature strength, but V2O5, an oxide, has a high vapor pressure and evaporates at high temperature, so the amount of addition is limited. Therefore, in the present invention, it is preferable to set the content of vanadium to 0.04 to 0.06%.
The content of aluminum (Al) is preferably 0.01% by weight or less.
Aluminum is an element for finely adjusting the deoxidizer and austenite grain size. However, when aluminum is added too much, it is easy to deteriorate casting workability during the solidification of molten steel. Therefore, in the present invention, it is preferable to set the content of aluminum to 0.01% or less.
The content of nitrogen (N) is preferably 0.008% by weight or less.
The amount of nitrogen remaining in the steel varies considerably depending on the raw material, the melting method, and the like. In general, even in the presence of extremely small amounts of nitrogen, the mechanical properties of the steel have a great influence, which increases tensile strength and yield strength and decreases elongation. Therefore, in order to obtain the rail required in the present invention, it is preferable to limit the content of nitrogen to 0.008% or less.
The content of oxygen (O 2) is preferably 0.002% by weight or less.
Since oxygen is hardly dissolved in iron (Fe), it exists mainly in steel as a nonmetallic inclusion. Among the nonmetallic inclusions,
In the high-purity Fe-O alloy, the impact transition temperature increases markedly with increasing oxygen content, but the effect is almost eliminated when a small amount of carbon (C), manganese (Mn), etc. are present in pure iron. When oxygen is contained in a large amount, it becomes a cause of abnormal structure during carburization of steel and at the same time, decreases hardenability and promotes growth of austenite grains by heating. Therefore, in the present invention, it is preferable to set the content of oxygen to 0.002% or less.
Hereinafter will be described in detail with respect to the manufacturing method of 400Hv class high hardness heat treatment rail alloy according to an embodiment of the present invention.
3 is a manufacturing process diagram illustrating a method for manufacturing a 400Hv class high hardness heat treatment rail alloy according to an embodiment of the present invention.
Referring to FIG. 3, in
Here, the rail material is a weight%, carbon (C): 0.79 ~ 0.82%, silicon (Si): 0.2? 0.4%, Manganese (Mn): 1.45? 1.55%, phosphorus (P): 0.02% or less, sulfur (S): 0.02% or less, copper (Cu): 0.12 to 0.10%, nickel (Ni): 0.25% or less, chromium (Cr): 0.3% or less, molybdenum (Mo): 0.06 to 0.04%, vanadium (V): 0.06 to 0.04%, aluminum (Al): 0.01% or less, nitrogen (N): 0.008% or less, oxygen (O2): 0.002% or less It consists of iron (Fe) and other impurities.
Next, in
Next, in
In the natural air cooling, the rail material starts the perlite phase transformation around 625 degrees and ends the transformation around 550 degrees. Accordingly, the whole is made of a pearlite structure, a high hardness heat treatment rail alloy of 440Hv class or more is manufactured.
As described above, in the present invention, by adding an alloy such as manganese (Mn), copper (Cu), molybdenum (Mo), it is possible to increase the hardness of the rail by delaying the pearlite transformation, without additional heat treatment equipment in the production of high hardness rail After rolling, it is possible to produce a hardened heat treated rail only by natural air cooling.
Example
Hereinafter, the configuration and operation of the present invention through the preferred embodiment of the present invention will be described in more detail. 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.
Details that are not described herein will be omitted since those skilled in the art can sufficiently infer technically.
1. Preparation of Hot Rolled Specimens
The hot rolled specimens of Example 1 and Comparative Example 1 were prepared under the composition shown in Table 1 and the process conditions described in Table 2.
In the case of hot-rolled specimens according to Example 1 and Comparative Example 1, ingots having respective compositions were prepared, and the rolled simulation test machine was used to simulate hot-rolling processes such as heating, rolling, cooling (water cooling), tempering, and the like. Charged.
(℃)
(℃)
(℃)
(℃ / s)
(Hv)
2. Evaluation of mechanical properties
Surface hardness test was conducted to evaluate the material of the hot rolled specimens prepared according to Example 1 and Comparative Example 1.
Referring to Table 1 and Table 2, in the case of the hot-rolled specimen prepared according to Example 1, as shown in Table 1, manganese, copper, molybdenum, etc. were added to make a rail material, and the rail material was rolled as shown in Table 2. Then, by performing natural cooling without undergoing a heat treatment process, it was possible to suppress the formation of the subcooled bainite and martensite structure and to produce only the pearlite structure to produce a hardened heat treated rail having a surface hardness of 400 Hv or more.
On the other hand, in the case of the hot-rolled specimen prepared according to Comparative Example 1, unlike the hot-rolled specimen prepared according to Example 1, by performing a heat treatment process separately after rolling to produce a super-cooled bainite and martensite structure, the surface hardness It was significantly lower compared to the hot rolled specimen prepared according to Example 1.
While specific embodiments of the present invention have been described so far, various modifications are possible without departing from the scope of the present invention. Therefore, the scope of the present invention should not be limited to the described embodiments, but should be determined not only by the claims below, but also by the equivalents of the claims.
As described above, the present invention has been described by way of limited embodiments and drawings, but the present invention is not limited to the above-described embodiments, which can be variously modified and modified by those skilled in the art to which the present invention pertains. Modifications are possible. Accordingly, the spirit of the present invention should be understood only by the claims set forth below, and all equivalent or equivalent modifications thereof will belong to the scope of the present invention.
310: heating stage
320: rolling step
330: natural air cooling stage
Claims (9)
The high hardness heat treatment rail alloy
400Hv class high hardness heat-treated rail alloy having a surface hardness of 400 (Hv) or more.
Rolling the heated rail material; And
Naturally air-cooling the rolled rail material
Method for producing a 400Hv-class high hardness heat treatment rail alloy comprising a.
The heating step
Heating the rail material in a furnace at 1250 to 1200 degrees;
Method for producing a 400Hv-class high hardness heat treatment rail alloy comprising a.
The rolling step is
Rolling to the final rolling end temperature of 1000-950 degrees
Method for producing a 400Hv-class high hardness heat treatment rail alloy comprising a.
The natural air cooling step
Naturally air-cooling the rail material rolled to a final rolling end temperature of 1000 to 950 degrees from room temperature to 1000 to 950 degrees
Method for producing a 400Hv-class high hardness heat treatment rail alloy comprising a.
The high hardness heat treatment rail alloy
A method for producing a 400Hv class high hardness heat treated rail alloy comprising a pearlite structure.
The high hardness heat treatment rail alloy
The method of manufacturing a 400Hv-class high-hardness heat treatment rail alloy, characterized in that starting the pearlite phase transformation at 625 ㅁ 5 degrees and terminate the transformation at 550 ㅁ 5 degrees during natural air cooling.
The high hardness heat treatment rail alloy
A method for producing a 400Hv class high hardness heat-treated rail alloy, having a surface hardness of 400 (Hv) or more.
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| KR1020100105577A KR20120044155A (en) | 2010-10-27 | 2010-10-27 | 400hv grade high hardness heat treated rail alloy, and method for manufacturing the same |
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20200081813A (en) * | 2018-12-28 | 2020-07-08 | 현대자동차주식회사 | Iron-based powder for powder metallurgy and method for producing same |
| KR20200081846A (en) * | 2018-12-28 | 2020-07-08 | 현대자동차주식회사 | Iron-based powder for powder metallurgy and method for producing same |
-
2010
- 2010-10-27 KR KR1020100105577A patent/KR20120044155A/en not_active Application Discontinuation
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20200081813A (en) * | 2018-12-28 | 2020-07-08 | 현대자동차주식회사 | Iron-based powder for powder metallurgy and method for producing same |
| KR20200081846A (en) * | 2018-12-28 | 2020-07-08 | 현대자동차주식회사 | Iron-based powder for powder metallurgy and method for producing same |
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