US20140227124A1 - Iron-based alloy for powder injection molding - Google Patents

Iron-based alloy for powder injection molding Download PDF

Info

Publication number
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
Authority
US
United States
Prior art keywords
powder
injection molding
alloy
ferrous alloy
ferrous
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Abandoned
Application number
US14/349,122
Other languages
English (en)
Inventor
Sung Hak Lee
Byeong-Joo Lee
Jeonghyeon Do
Yang Su Shin
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Academy Industry Foundation of POSTECH
Original Assignee
Academy Industry Foundation of POSTECH
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Academy Industry Foundation of POSTECH filed Critical Academy Industry Foundation of POSTECH
Assigned to POSTECH ACADEMY-INDUSTRY FOUNDATION reassignment POSTECH ACADEMY-INDUSTRY FOUNDATION ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: SHIN, YANG SU, DO, Jeonghyeon, Lee, Byeong-joo, LEE, SUNG HAK
Publication of US20140227124A1 publication Critical patent/US20140227124A1/en
Abandoned legal-status Critical Current

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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • 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
    • 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
    • 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%
    • 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
    • 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
    • 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.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Powder Metallurgy (AREA)
US14/349,122 2011-10-21 2012-04-20 Iron-based alloy for powder injection molding Abandoned US20140227124A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
KR1020110108028A KR101350944B1 (ko) 2011-10-21 2011-10-21 분말사출성형용 철계 합금
KR10-2011-0108028 2011-10-21
PCT/KR2012/003071 WO2013058453A1 (ko) 2011-10-21 2012-04-20 분말사출성형용 철계 합금

Publications (1)

Publication Number Publication Date
US20140227124A1 true US20140227124A1 (en) 2014-08-14

Family

ID=48141076

Family Applications (1)

Application Number Title Priority Date Filing Date
US14/349,122 Abandoned US20140227124A1 (en) 2011-10-21 2012-04-20 Iron-based alloy for powder injection molding

Country Status (6)

Country Link
US (1) US20140227124A1 (ko)
EP (1) EP2770074A4 (ko)
JP (1) JP5819001B2 (ko)
KR (1) KR101350944B1 (ko)
CN (1) CN103890210B (ko)
WO (1) WO2013058453A1 (ko)

Cited By (2)

* Cited by examiner, † Cited by third party
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
US20140105778A1 (en) * 2012-10-15 2014-04-17 Hyundai Motor Company Method of manufacturing control finger using metal powder injection molding

Families Citing this family (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US9115958B2 (en) 2013-03-15 2015-08-25 Leupold & Stevens, Inc. Dual field optical aiming system for projectile weapons
CZ2014865A3 (cs) * 2014-12-05 2016-06-01 Česká zemědělská univerzita v Praze Bimetalický kovový materiál
EP3156155A1 (en) * 2015-10-15 2017-04-19 Höganäs AB (publ) Iron based powders for powder injection molding
JP6735106B2 (ja) * 2016-01-29 2020-08-05 株式会社ダイヤメット 高温耐摩耗性、高温強度に優れるＣｏフリー耐熱焼結材およびその製造方法
KR102130490B1 (ko) * 2018-12-18 2020-07-06 주식회사 엔이피 자동차 조향장치에 사용되는 철계금속부품 제조방법
CN111001813B (zh) * 2019-12-28 2022-02-18 合肥波林新材料股份有限公司 一种高减摩性铁基硫化粉末冶金含油轴承材料及其制备方法和应用
CN111304555B (zh) * 2020-03-31 2022-02-01 广东省科学院新材料研究所 原位内生析出陶瓷颗粒增强Cr-Mn-Ni-C-N奥氏体耐热钢及其制备方法与应用
CN111560555A (zh) * 2020-05-18 2020-08-21 上海红重机械装备有限公司 一种钢结构升降系统制造工艺

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4822415A (en) * 1985-11-22 1989-04-18 Perkin-Elmer Corporation Thermal spray iron alloy powder containing molybdenum, copper and boron
US5643531A (en) * 1989-12-12 1997-07-01 Samsung Heavy Industry Co., Ltd. Ferrous alloy composition and manufacture and coating methods of mechanical products using the same
KR960041395A (ko) * 1995-05-31 1996-12-19 유상부 내식, 내마모성 우수한 철기합금 및 이를 이용한 내식 내마모용 부재의 제조방법
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
CH694401A5 (de) * 1999-05-26 2004-12-31 Basf Ag Nickelarmer, molybdänarmer, biokompatibler, nicht Allergie auslösender, korrosionsbeständiger austenitischer Stahl.
JP3988971B2 (ja) 2000-02-21 2007-10-10 日本ピストンリング株式会社 焼結部材
US20050163645A1 (en) * 2004-01-28 2005-07-28 Borgwarner Inc. Method to make sinter-hardened powder metal parts with complex shapes
KR100650409B1 (ko) * 2004-12-17 2006-11-27 (주)엠티아이지 분말사출성형을 이용한 복잡 형상 재료의 제조방법 및그에 따라 제조된 재료

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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)

* Cited by examiner, † Cited by third party
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
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

Similar Documents

Publication Publication Date Title
US20140227124A1 (en) Iron-based alloy for powder injection molding
CN107686928B (zh) 一种高性能NiCoCrFeMnTi系高熵合金及其制备方法
JP6093405B2 (ja) 窒素含有低ニッケル焼結ステンレス鋼
EP0480495B1 (en) Sintered ferrous-based material
CN105339517A (zh) 用于制造钢成型体的方法
Abenojar et al. Reinforcing 316L stainless steel with intermetallic and carbide particles
WO2005102564A1 (ja) 粉末冶金用混合粉体
KR101736108B1 (ko) 써멧의 주조식 제조방법 및 그에 의해 제조된 써멧
Do et al. Effects of Cr and B contents on volume fraction of (Cr, Fe) 2 B and hardness in Fe-based alloys used for powder injection molding
CN101516549A (zh) 铁基粉末
US20170260609A1 (en) Precipitate strengthened nanostructured ferritic alloy and method of forming
JP5114233B2 (ja) 鉄基焼結合金およびその製造方法
Kumaran et al. A novel and sustainable method to develop non-equiatomic CoCrFeNiMox high entropy alloys via spark plasma sintering using commercial commodity powders and evaluation of its mechanical behaviour
JP4371003B2 (ja) 粉末冶金用合金鋼粉
Pascal et al. Co-sintering and microstructural characterization of steel/cobalt base alloy bimaterials
Huth et al. Diffusion alloying–a new manufacturing method for PM tool steels
Karwan-Baczewska et al. Sintering prealloyed powders Fe-Ni-Cu-Mo modified by boron base on thermodynamic investigations
JPH0347951A (ja) バルブシート用鉄基焼結合金
Huth et al. Powder Manufacturing & Processing: Diffusion Alloying-A New Manufacturing Method for PM Tool Steels
US8636948B2 (en) Methods of preparing high density powder metallurgy parts by iron based infiltration
Kudo et al. Improvement of mechanical properties of injection molded ni-base superalloy compacts
JPH06172804A (ja) 射出成形用鉄系合金粉末
Kim et al. Microstructure and mechanical properties of Cu-based amorphous alloy/copper composites consolidated by spark plasma sintering
Prieto et al. Design and development of a new high entropy alloy by powder metallurgy
JPS60208450A (ja) 鉄系焼結材の製造方法

Legal Events

Date Code Title Description
AS Assignment

Owner name: POSTECH ACADEMY-INDUSTRY FOUNDATION, KOREA, REPUBL

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:LEE, SUNG HAK;LEE, BYEONG-JOO;DO, JEONGHYEON;AND OTHERS;SIGNING DATES FROM 20131230 TO 20140102;REEL/FRAME:032580/0758

STCB Information on status: application discontinuation

Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION