US20140227124A1 - Iron-based alloy for powder injection molding - Google Patents
Iron-based alloy for powder injection molding Download PDFInfo
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- US20140227124A1 US20140227124A1 US14/349,122 US201214349122A US2014227124A1 US 20140227124 A1 US20140227124 A1 US 20140227124A1 US 201214349122 A US201214349122 A US 201214349122A US 2014227124 A1 US2014227124 A1 US 2014227124A1
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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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/22—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces for producing castings from a slip
- B22F3/225—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces for producing castings from a slip by injection molding
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
- C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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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
- C22C38/18—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
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- 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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
Definitions
- the present invention relates to a ferrous alloy, and more particularly, to a ferrous alloy for powder injection molding.
- Powder injection molding is new powder metallurgy molding technology in which powder metallurgy technology and an injection molding method, which is mass production technology of a precise plastic component, are coupled.
- a PIM process is a process of producing a component by mixing a micro-powder and a polymer binder to be a subject of flow, injecting the powder and the binder into a mold, removing the binder from the mix, and finally sintering only the powder at a high temperature.
- three-dimensional precision components may be made entirely of a powder material such as a metal, a ceramic, a carbide, and an intermetallic compound, and even of a processing resistant material or a material that cannot be cast, because mass production is available with few or no post-processes, so powder injection molding technology is appropriate for economically producing high value components.
- Stainless steel that occupies most of a metal powder injection molding market has a property of strength, hardness, abrasion resistance, and corrosion resistance that a final powder injection molding component requires with a change of chemical composition.
- a stainless steel powder that is used for powder injection molding variously exists as SUS304L, SUS316L, SUS430, and SUS630, and for martensite-based stainless steel powder injection molding, an additional heat treatment process is necessary.
- the present invention has been made in an effort to provide a ferrous alloy having advantages of representing superior hardness, abrasion resistance, and corrosion resistance than those of stainless steel that is used for existing powder injection molding and having a low production cost.
- An exemplary embodiment of the present invention provides a ferrous alloy for powder injection molding including: iron (Fe) at 52.59-78.15 wt %, chromium (Cr) at 16.45-37.34 wt %, boron (B) at 3.42-7.76 wt %, silicon (Si) at 1.64-1.92 wt %, sulfur (S) at 0-0.21 wt %, carbon (C) at 0.16-0.18 wt %, and other inevitable impurities.
- a ratio X Cr /X B of the chromium (Cr) and boron (B) may be 1.0.
- a sum (X Cr +X B ) of a composition of the chromium (Cr) and the boron (B) may be 0.30 to 0.60.
- a sum (X Fe +X Cr +X B ) of a composition of the iron (Fe), the chromium (Cr), and the boron (B) may be 0.9635.
- chromium boride may be distributed in a network form within a ferrite base.
- a volume fraction of the chromium boride (Cr 2 B) may be 51-91%.
- Hardness of the ferrous alloy for powder injection molding may be 600-1600 VHN.
- Another embodiment of the present invention provides a method of injection molding a ferrous powder, the method including: providing powder of the ferrous alloy for powder injection molding; forming a powder mixture by mixing the powder of the ferrous alloy for powder injection molding and a binder; compression molding the powder mixture; removing the binder by heating the powder mixture; and sintering the powder mixture from which the binder is removed.
- the powder mixture may be formed by mixing the powder of the ferrous alloy for powder injection molding, paraffin wax, tungsten carbide balls, and heptanes in a container and rotating the container.
- Ferrous alloys for powder injection molding according to the present invention form hard Cr 2 B boride with different volume fractions, thereby greatly improving hardness and abrasion resistance, compared with a conventionally used stainless steel.
- ferrous alloys for powder injection molding according to the present invention are cheaper in alloy price than a commercial stainless steel by lowering a fraction of an alloy element, and by reducing production cost by lowering a sintering temperature and reducing sintering time, the ferrous alloys are superior in price competitiveness.
- FIG. 1 shows scanning electron microscope (SEM) photographs illustrating a microstructure of a ferrous alloy for powder injection molding according to an exemplary embodiment of the present invention.
- FIG. 2 shows Fe—Cr—B ternary system isothermal phase diagrams of a ferrous alloy that is designed according to an exemplary embodiment of the present invention.
- FIG. 3 shows graphs illustrating calculation results of a precipitation driving force change of Cr 2 B according to each component composition on a constituent element (Fe, Cr, B, Si, S, and C) basis of a basic alloy when designing a ferrous alloy according to an exemplary embodiment of the present invention.
- FIG. 4 shows graphs illustrating a fraction of equilibrium phases existing at 1000° C. according to a ratio of chromium and boron in a ferrous alloy according to an exemplary embodiment of the present invention.
- FIGS. 5 to 7 show graphs illustrating an equilibrium phase fraction according to a temperature of an alloy composition of 9 ferrous alloys that are designed according to an exemplary embodiment of the present invention.
- FIGS. 8 to 10 show SEM photographs of microstructures after ferrous alloys are cast and heated according to an exemplary embodiment of the present invention.
- FIG. 11 illustrates X-ray diffraction analysis results of ferrous alloys according to an exemplary embodiment of the present invention.
- FIG. 12 is a graph illustrating a price of an alloy element according to a property (hardness reference) that is requested for components.
- a ferrous alloy for powder injection molding includes iron (Fe) at 52.59-78.15 wt %, chromium (Cr) at 16.45-37.34 wt %, boron (B) at 3.42-7.76 wt %, silicon (Si) at 1.64-1.92wt %, sulfur (S) at 0-0.21 wt %, carbon (C) at 0.16-0.18 wt %, and other inevitable impurities.
- a microstructure of the ferrous alloy is characterized in that chromium boride (Cr 2 B) is distributed in a network form within a ferrite base. Because a chromium boride (Cr 2 B) phase according to the present invention is very hard, a shape and a fraction distribution state of the precipitated chromium boride phase may have a direct influence on entire hardness and abrasion resistance of a specimen.
- a chromium boride phase of the ferrous alloy forms a network structure, an entire hardness distribution of the specimen is uniform according to a position, and an applied load in an abrasion environment is distributed to be superior in an abrasion resistance property.
- a volume fraction of the chromium boride (Cr 2 B) is 51-91%.
- hardness of the alloy is 600-1600 VHN.
- a high hardness property can be obtained using precipitation of chromium boride, which is a compound of Cr and B of a relatively cheap price.
- a composition ratio of chromium (Cr) and boron (B) is fixed to 1:1, and the sum (the sum of a mole fraction) of a composition ratio of chrome (Cr) and boron (B) may be adjusted to 0.30-0.60.
- the sum of a composition ratio (the sum of a mole fraction) of iron (Fe), chromium (Cr), and boron (B), which are major components, may be fixed to 0.9634.
- the chromium (Cr) is generally an alloy element that is added to increase hardenability of the alloy and to improve corrosion resistance when quickly cooling, and in the present invention, by bonding to boron (B), the chromium (Cr) is an element that adjusts the chromium boride precipitation fraction.
- a precipitation fraction of chromium boride is formed to be 50 vol % or more, and thus hardness of about 600 VHN or more, which is a high hardness request value required in a powder injection molding process, can be obtained.
- a content of boron (B) is determined to be 3.42-7.76 wt % according to such chromium (Cr) content.
- Boron (B) is an element that is added for improving hardenability, and in the present invention, boron (B) is an element that adjusts a chromium boride precipitation fraction by bonding to chromium.
- boron (B) is an element that adjusts a chromium boride precipitation fraction by bonding to chromium.
- a content of boron is 3.42 wt % or more, a precipitation fraction of chromium boride becomes 50 vol % or more, and thus hardness of about 600 VHN or more, which is a high hardness request value required in a powder injection molding process, can be obtained.
- a content of chromium is determined to be 16.45-37.34 wt % according to such content of boron.
- silicone (Si) is an element that performs a function of stabilizing a base with ferrite in a sintering press of a powder injection molding process and improving hardenability through solid solution reinforcement.
- a content of silicone is 1.64 wt % or less, a solid solution reinforcement and ferrite stabilization effect is slight, and when a content of silicone is 1.92 wt % or more, a solid solution reinforcement effect does not increase in proportion thereto, and so content of silicone is limited to 1.64-1.92 wt %.
- sulfur content is controlled to be as low as possible, but by adding sulfur up to a limit at which a sulfide (FeS) is not formed, the present invention attempts to obtain a base and chromium boride stabilization effect. Therefore, it is preferable that an upper limit thereof is set to 0.21 wt %.
- Carbon (C) is an element that can efficiently improve hardenability of an alloy, and in order to satisfy hardness that the present invention desires, carbon (C) at 0.16 wt % or more should be contained, and when carbon (C) at 0.18 wt % or more is added, toughness is deteriorated and thus the content of carbon (C) is limited to 0.16-0.18 wt %.
- a method of injection molding a ferrous powder includes steps of: providing a powder of a ferrous alloy for powder injection molding; forming a powder mixture by mixing the powder of a ferrous alloy for powder injection molding and a binder; compression molding the powder mixture; removing the binder by heating the powder mixture; and sintering the powder mixture from which the binder is removed.
- the powder mixture is formed by mixing a powder of the ferrous alloy for powder injection molding, paraffin wax, tungsten carbide balls, and heptanes in a container and rotating the container.
- Compression molding of the powder mixture may be performed by using a press at a pressure of 100 kgf/cm 2 or more after charging the powder mixture into a mold.
- the binder may be removed by raising the temperature of the compression molded powder mixture up to 500° C. at a heating rate of 2° C./min or more and maintaining the temperature for 1 hour.
- the sintering may be performed by charging the powder mixture from which the binder is removed into a heat treating furnace, heating it to 1175° C. at a heating rate of 3° C./min or more in a hydrogen atmosphere, and maintaining the temperature for 1 hour.
- the present invention provides a ferrous alloy with high hardness and at a low cost for powder injection molding that may represent various properties by forming chromium boride (Cr 2 B) of different volume fractions in a ferrite base by reducing a ratio of an alloy element and changing a ratio of chromium (Cr) and boron (B) based on a Fe-43Cr-5.6B-1.8Si-0.2S-0.17C (wt %) alloy.
- Cr 2 B chromium boride
- a microstructure of alloys according to the present invention may have a structure in which other crystalline particles are distributed in addition to chromium boride (Cr 2 B) and a ferrite base.
- Cr 2 B chromium boride
- Table 1 illustrates a composition of a basic alloy as a reference when designing a ferrous alloy for powder injection molding according to an exemplary embodiment of the present invention.
- Table 2 illustrates a composition of an alloy in which a ferrous alloy for powder injection molding according to an exemplary embodiment of the present invention is designed by thermodynamic calculation.
- a ferrous alloy for powder injection molding was arc melted under an argon (Ar) atmosphere according to a composition of Table 2.
- An alloy that was used for arc melting included high purity Fe (99.9 wt %), Si (99.99 wt %), and C (99 wt %), as well as previously alloyed FeB (99.2 wt %), FeS (98.5 wt %), and FeCr (98.6 wt %) as a pre-alloy, and was turned over 4-5 times and repeatedly melted so as to uniformize a mother alloy component.
- Phases existing within the alloy were analyzed with an X-ray diffraction test method, and a volume fraction of chromium boride (Cr 2 B) was measured by an image analyzer.
- Entire hardness of the alloy was measured under a load of 300 g by a Vickers hardness device.
- a mother alloy ingot was produced.
- the used alloy included high purity Fe (99.9 wt %), Si (99.99 wt %), and C (99 wt %), and previously alloyed FeB (99.2 wt %), FeS (98.5 wt %), and FeCr (98.6 wt %) as a pre-alloy.
- the ingot was again melted at 1550° C. in an argon (Ar) atmosphere, and was produced as a spherical powder through N 2 gas atomization at an injection pressure of 20 bar.
- paraffin wax was used as a binder.
- a ferrous powder with a weight of 97 g and 3 g of a binder were mixed and charged into a high-density polyethylene (HDPE) container having a capacity of 300 ml together with 20 ml of tungsten carbide balls, and heptanes were filled to a volume of 250 ml.
- HDPE high-density polyethylene
- the ferrous powder and the binder were mixed. After a powder mixture was dried at a hot plate at 55° C., the powder mixture was charged into a circular mold with a diameter of 13 mm and compressed and molded using a press at room temperature with a pressure of 100 kgf/cm 2 .
- the temperature of the compact was raised to 500° C. at a heating rate of 2° C./min, and the compact was maintained and degreased at this temperature for 1 hour.
- the compact was charged into a heat treating furnace and a temperature thereof was raised up to 1175° C. at a heating rate of 3° C./min in a hydrogen atmosphere, and the compact was sintered for 1 hour.
- a property determining element of the alloy is determined, and a property (particularly, hardness) of the alloy is closely related to precipitation of chromium boride (Cr 2 B).
- thermodynamic calculation was performed.
- Software that is used for calculation is ThermoCalc, which is a commercial thermodynamic calculation program, and as a thermodynamic database, an upgraded version of TCFE2000 was used.
- FIG. 2 is a Fe—Cr—B ternary system isothermal phase diagram that is formed using the database.
- FIG. 3 illustrates a calculation result of a precipitation driving force change of Cr 2 B according to each component composition on a constituent element (Fe, Cr, B, Si, S, and C) basis of a basic alloy at 1250° C. (pink) and 1000° C. (yellowish green).
- a precipitation driving force is obtained by calculating an amount of a component to adjust in a range from 0 to two times an original amount in a state in which a ratio between other components is fixed.
- the basic alloy When a basic alloy is used for PIM, the basic alloy is sintered for a long time at 1200° C. in a powder injection process, and thus it may be considered that a sintered microstructure has arrived at equilibrium.
- a composition was obtained when the sum (X Fe +X Cr +X B ) of a mole fraction of a major component is maintained at 0.9634 based on a basic alloy of Table 1 as a reference, but values of X Fe and (X Cr +X B ) were adjusted by setting a ratio X Cr /X B of Cr and B to three cases of 1.0 (B ratio increase), 1.6 (basis ratio), and 2.2 (Cr ratio increase).
- FIG. 4 illustrates a fraction of equilibrium phases existing at 1000° C. in the three cases. As the boron ratio increases and as the (X Cr +X B ) value increases, an equilibrium phase fraction of chromium boride (Cr 2 B) increases.
- FIGS. 5 to 7 are graphs illustrating an equilibrium phase fraction according to a temperature of the 9 alloy compositions. Thereby, thermodynamic calculation values of an equilibrium phase fraction of chromium boride (Cr 2 B) at several temperatures may be seen.
- a Cr 2 B fraction is about 43 vol % and the remaining elements are BCC ⁇ -Fe (ferrite) and FCC ⁇ -Fe (austenite).
- BCC ⁇ -Fe ferrite
- FCC ⁇ -Fe austenite
- FIGS. 8 to 10 illustrate SEM microstructures of heat-treated alloys after casting. After heat treatment, because diffusion occurs, a microstructure thereof is considerably different from that of the cast alloy.
- the martensite When martensite is maintained for a long time at a high temperature, the martensite is changed to tempered martensite, i.e., ferrite in which micro-carbides are precipitated, and a form of Cr 2 B is changed from a needle shape or a bar shape to a spherical or oval shape.
- tempered martensite i.e., ferrite in which micro-carbides are precipitated
- a microstructure ( FIG. 9( f )) of an alloy of Exemplary Embodiment 6 having the same composition as an alloy of a reference composition is similar to that of a component that is powder injection molded with the basic alloy powder of FIG. 1 . It may be expected that a microstructure of a heat-treated alloy after casting will be similar to a microstructure of a component having passed through a PIM process after making the alloy into powder.
- FIG. 11 illustrates X-ray diffraction analysis results of heat-treated alloys. Because a peak of ⁇ -Fe (ferrite) and Cr 2 B is represented in all alloys, it can be seen that Cr 2 B is distributed within a ferrite base. A precipitated Cr 2 B fraction was measured and is represented in Table 3, and was compared with a Cr 2 B fraction that is obtained from FIGS. 5 to 7 representing an equilibrium phase fraction.
- Hardness of a cast alloy and a heat-treated alloy was measured and is represented in Table 3. Hardness of a cast alloy and a heat-treated alloy is different in the same chemical composition because a microstructure of a cast alloy that is formed with Cr 2 B and martensite is changed after heat treatment.
- martensite is changed to ferrite after heat treatment, and Cr 2 B arrives in an equilibrium state by a diffusion effect by high temperature heat treatment and thus hardness and a fraction of Cr 2 B increases.
- hardness decreases, and as hardness and a fraction of Cr 2 B increases, hardness increases, while hardness of a cast alloy increases or decreases after heat treatment according to a competition relationship between the two.
- Ferrous alloys that are produced in this research may be variously used for producing a PIM component according to a fraction and hardness of Cr 2 B in consideration of similarity of a microstructure ( FIG. 9( f )) of an alloy of Exemplary Embodiment 6 and a microstructure ( FIG. 1) of a component in which PIM is performed with a basic alloy powder.
- an alloy corresponding thereto for example, alloys of Exemplary Embodiments 1, 5, and 8, may be applied.
- the alloy may have a merit that brittleness decreases and toughness increases, compared with an alloy having high hardness.
- FIG. 12 is a graph illustrating a price of an alloy element according to a property (hardness reference) that is requested for components.
- a price reference of an alloy element was formed based on an LME daily price (based on Jul. 27, 2010).
- a price of an alloy element that is contained in an alloy that is made in this research is lower than that of a basic alloy, and when hardness decreases, an alloy element price also decreases.
- alloy element may be fully used as a replacement.
- an alloy of this research can be fully applied to a PIM component of various conditions and has an excellent property and advantageous economic efficiency.
- hard Cr 2 B adjusts a Cr 2 B fraction from the present invention in which a PIM alloy that is distributed in a ferrite base is designed, an alloy representing various properties may be successfully produced.
- a Cr 2 B fraction and hardness was estimated from a calculation result of a high temperature equilibrium phase fraction by a thermodynamic calculation, and a ferrous alloy having various Cr 2 B fractions and hardness was produced using this.
- these alloys contain much Cr 2 B that is stable at a high temperature and has excellent corrosion resistance, it is expected that these alloys are much superior to an existing stainless steel PIM component in terms of high temperature property, abrasion resistance, and corrosion resistance, as well as room temperature hardness, and thus there is a new possibility that these alloys can be applied to a structural components that require excellent properties.
- an alloy of Exemplary Embodiment 3 represents hardness of 1600 VHN or more, the alloy may be fully applied even to a PIM component of a tungsten carbide alloy as well as stainless steel. While this invention has been described in connection with what is presently considered to be practical exemplary embodiments, it is to be understood that the invention is not limited to the disclosed embodiments, but, on the contrary, is intended to cover various modifications and equivalent arrangements included within the spirit and scope of the appended claims.
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KR10-2011-0108028 | 2011-10-21 | ||
PCT/KR2012/003071 WO2013058453A1 (ko) | 2011-10-21 | 2012-04-20 | 분말사출성형용 철계 합금 |
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EP (1) | EP2770074A4 (ko) |
JP (1) | JP5819001B2 (ko) |
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EP3156155A1 (en) * | 2015-10-15 | 2017-04-19 | Höganäs AB (publ) | Iron based powders for powder injection molding |
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JPH10317009A (ja) * | 1997-05-20 | 1998-12-02 | Sumitomo Metal Mining Co Ltd | ステンレス焼結体の製造方法 |
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KR100650409B1 (ko) * | 2004-12-17 | 2006-11-27 | (주)엠티아이지 | 분말사출성형을 이용한 복잡 형상 재료의 제조방법 및그에 따라 제조된 재료 |
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- 2011-10-21 KR KR1020110108028A patent/KR101350944B1/ko active IP Right Grant
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2012
- 2012-04-20 JP JP2014536968A patent/JP5819001B2/ja not_active Expired - Fee Related
- 2012-04-20 EP EP12841059.4A patent/EP2770074A4/en not_active Withdrawn
- 2012-04-20 WO PCT/KR2012/003071 patent/WO2013058453A1/ko active Application Filing
- 2012-04-20 CN CN201280051137.9A patent/CN103890210B/zh not_active Expired - Fee Related
- 2012-04-20 US US14/349,122 patent/US20140227124A1/en not_active Abandoned
Patent Citations (1)
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US20090297396A1 (en) * | 2006-06-28 | 2009-12-03 | Pohang University Of Science And Technology | Fabrication method of alloy parts by metal injection molding and the alloy parts |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20140041222A1 (en) * | 2012-08-10 | 2014-02-13 | Kia Motors Corporation | Method for manufacturing valve train parts using metal powder injection molding |
US9085028B2 (en) * | 2012-08-10 | 2015-07-21 | Hyundai Motor Company | Method for manufacturing valve train parts using metal powder injection molding |
US20140105778A1 (en) * | 2012-10-15 | 2014-04-17 | Hyundai Motor Company | Method of manufacturing control finger using metal powder injection molding |
US9095905B2 (en) * | 2012-10-15 | 2015-08-04 | Hyundai Motor Company | Method of manufacturing control finger using metal powder injection molding |
Also Published As
Publication number | Publication date |
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EP2770074A4 (en) | 2016-04-20 |
EP2770074A1 (en) | 2014-08-27 |
JP5819001B2 (ja) | 2015-11-18 |
WO2013058453A1 (ko) | 2013-04-25 |
JP2014534344A (ja) | 2014-12-18 |
KR20130043871A (ko) | 2013-05-02 |
CN103890210A (zh) | 2014-06-25 |
KR101350944B1 (ko) | 2014-01-16 |
CN103890210B (zh) | 2016-05-04 |
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