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WO2015157169A2 - Alliages de fer coulés à teneur en carbure élevée, à grains fins - Google Patents

Alliages de fer coulés à teneur en carbure élevée, à grains fins Download PDF

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Publication number
WO2015157169A2
WO2015157169A2 PCT/US2015/024508 US2015024508W WO2015157169A2 WO 2015157169 A2 WO2015157169 A2 WO 2015157169A2 US 2015024508 W US2015024508 W US 2015024508W WO 2015157169 A2 WO2015157169 A2 WO 2015157169A2
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Prior art keywords
alloy
article
manufacture
carbide
carbides
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PCT/US2015/024508
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English (en)
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WO2015157169A3 (fr
Inventor
Justin Lee Cheney
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Scoperta, Inc.
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Publication of WO2015157169A2 publication Critical patent/WO2015157169A2/fr
Publication of WO2015157169A3 publication Critical patent/WO2015157169A3/fr

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C37/00—Cast-iron alloys
    • C22C37/06—Cast-iron alloys containing chromium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/24—Selection of soldering or welding materials proper
    • B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
    • B23K35/3053—Fe as the principal constituent
    • B23K35/308—Fe as the principal constituent with Cr as next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/24—Selection of soldering or welding materials proper
    • B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
    • B23K35/3053—Fe as the principal constituent
    • B23K35/308—Fe as the principal constituent with Cr as next major constituent
    • B23K35/3086—Fe as the principal constituent with Cr as next major constituent containing Ni or Mn
    • 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
    • C22C33/08—Making cast-iron alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C37/00—Cast-iron alloys
    • C22C37/06—Cast-iron alloys containing chromium
    • C22C37/08—Cast-iron alloys containing chromium with nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C37/00—Cast-iron alloys
    • C22C37/10—Cast-iron alloys containing aluminium or silicon
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • 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%
    • C22C33/0292—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 more than 5% preformed carbides, nitrides or borides

Definitions

  • the disclosure relates generally to cast iron alloys used in wear-prone environments and which are resistant to wear.
  • the alloy family known as chromium white irons or chromium white cast irons can refer to alloys containing Fe, C, and Cr which can form eutectic chromium carbides.
  • alloys having chromium levels in the range from 15-30 wt. % (or about 15 to about 30 wt. %) and having carbon levels in the range of 1-3 wt. % (or about 1 to about 3 wt. %) can form such chromium white irons.
  • formation of primary chromium carbides is typically avoided which can occur as either Cr or C content is increased.
  • the alloy system can be in the hypoeutectic region of the Fe-C phase field (i.e., the C level is below the eutectic point in the alloy system).
  • Exceeding the C eutectic level in these systems can create Cr 7 C 3 carbide precipitates which are long, rod-like, and can be very embrittling to the material.
  • the addition of chromium can shift the eutectic point to more iron-rich compositions. Therefore, as Cr is added for various benefits (such as corrosion resistance), the amount of carbon which can be added before the alloy enters the hypereutectic regime drops. For example, an Fe-5Cr type alloy has a eutectic point over -4% C while an Fe-25Cr alloy has a eutectic point at around 3.3% C.
  • Chromium white irons are generally very useful for applications where resistance to abrasion is advantageous.
  • the relatively high content of chromium carbides in the micro structure are very hard and thus contribute to the abrasion resistance of the material.
  • the volume fraction of carbides in the alloy can dictate the wear resistance of the material, e.g., increased carbide contents can create increased wear resistance.
  • the carbon beyond the eutectic point can be increased to increase the total carbide fraction. However, this is done at the expense of toughness.
  • computational metallurgy can be used to explore alloy compositional ranges where the total carbide content can be increased without introducing coarse carbide structures known to embrittle the material.
  • the thermodynamic limit for hypoeutectic carbide volume fraction can be 35- 40% (or about 35 - about 40%).
  • This disclosure describes embodiments of alloys which can meet a set of thermodynamic criteria which can exceed the 40% (or about 40%) carbide content limit, but may not introduce the formation of hypereutectic M 7 C 3 , M 23 C 6 or generally any Fe,Cr-rich type carbides.
  • micro structure which can have a very high level, >40% mole fraction (or > about 40% mole fraction) as defined by thermodynamic models, of fine-grained carbides.
  • this new class of materials can be defined as fine-grained high carbide content cast irons.
  • the utility of such a material can be an increased wear resistance, while maintaining similar levels of toughness to hypoeutectic cast irons.
  • an article of manufacture which can contain in at least a portion of its structure a component comprising Fe, Cr, and C in which the total carbide and/or boride content in the micro structure exceeds 40 volume %, and the grain size of all carbides and borides does not exceed 50 micrometers in their longest dimension.
  • the alloy further can further comprise C: 2.5-3.8 wt.%, Cr: 10-28 wt.%, b: 0-5 wt. %, W: 0-9 wt%.
  • the alloy can further comprise Mn: 0-1 wt %, Mo: 0-1 wt%, Si: 0-1%, Ti: 0-0.5%, V: 0-3 wt.%.
  • the alloy further can further comprise C: 2.2-4.02 wt.%, Cr: 12.7-34 wt.%, Nb: 3.8-5 wt. %, W: 4.37-9 wt%.
  • the total carbide and/or boride content can exceed 45 volume %. In some embodiments, the total carbide and/or boride content can exceed 50 volume %.
  • the grain size of all carbides and borides does not exceed 25 micrometers in their longest dimension. In some embodiments, the grain size of all carbides and borides does not exceed 5 micrometers in their longest dimension.
  • the article can be produced via the casting process. In some embodiments, the article can be utilized as a wear resistant component. In some embodiments, the article can be used as a sleeve or layer in pipelines designed to carry abrasive slurries
  • an article of manufacture which can comprise Fe, Cr, and C in which the total carbide and/or boride content in the micro structure exceeds 40 volume %, and the grain size of all carbides and borides does not exceed 50 micrometers in their longest dimension.
  • an article of manufacture which can contain at least a portion of a component comprising Fe, Cr, and C in which the total carbide and/or boride content in the micro structure exceeds 0.4 mole fraction, and the total volume of segregated carbides is less than 0.05 mole fraction, whereas a segregated carbide is defined as Fe or Cr - rich boride or carbide, Fe+Cr >50 wt.%, which is thermodynamically stable at a temperature above the temperature at which austenite is thermodynamically stable.
  • the alloy can further comprise C: 2.5-3.8 wt.%, Cr: 10-28 wt.%, b: 0-5 wt. %, W: 0-9 wt%.
  • the alloy can further comprise Mn: 0-1 wt %, Mo: 0-1 wt%, Si: 0-1%, Ti: 0-0.5%, V: 0-3 wt.%.
  • the alloy can further comprise C: 2.2-4.02 wt.%, Cr: 12.7-34 wt.%, Nb: 3.8-5 wt. %, W: 4.37-9 wt%.
  • the total carbide and/or boride content can exceed 0.45 mole fraction. In some embodiments, the total carbide and/or boride content can exceed 0.50 mole fraction.
  • the article can be produced via the casting process. In some embodiments, the article can be utilized as a wear resistant component. In some embodiments, the article can be used as a sleeve or layer in pipelines designed to carry abrasive slurries
  • Also disclosed herein is a method of forming a component which can contain in at least a portion of its structure a component comprising Fe, Cr, and C in which the total carbide and/or boride content in the micro structure exceeds 40 volume %, and the grain size of all carbides and borides does not exceed 50 micrometers in their longest dimension.
  • the alloy can further comprise C: 2.5-3.8 wt.%, Cr: 10-28 wt.%, Nb: 0-5 wt. %, W: 0-9 wt%.
  • the alloy can further comprise Mn: 0-1 wt %, Mo: 0-1 wt%, Si: 0-1%, Ti: 0-0.5%, V: 0-3 wt.%.
  • the alloy can further comprise C: 2.2-4.02 wt.%, Cr: 12.7-34 wt.%, Nb: 3.8-5 wt. %, W: 4.37-9 wt%.
  • the total carbide and/or boride content can exceed 0.45 mole fraction. In some embodiments, the total carbide and/or boride content can exceed 0.50 mole fraction.
  • the article can be produced via the casting process. In some embodiments, the article can be utilized as a wear resistant component. In some embodiments, the article can be used as a sleeve or layer in pipelines designed to carry abrasive slurries.
  • an article of manufacture comprising an alloy comprising Fe, Cr, and C, wherein a total carbide and boride content in a micro structure of the alloy exceeds 40 volume %, and wherein a grain size of all carbides and borides is less than or equal to 50 micrometers in their longest dimension.
  • the alloy can be an iron based alloy and can comprise C: 2.2-4.02 wt. % and Cr: 10-34 wt. %.
  • the alloy can comprise C: 2.5-3.8 wt.%, Cr: 10-28 wt.%, b: 0-5 wt. %, and W: 0-9 wt. %.
  • the alloy can further comprise Mn: 0-1 wt. %, Mo: 0-1 wt. %, Si: 0-1 wt. %, Ti: 0-0.5 wt. %, and V: 0-3 wt.%.
  • the alloy can comprise C: 2.2-4.02 wt.%. Cr: 12.7-34 wt.%, Nb: 3.8-5 wt. %, and W: 4.37-9 wt. %.
  • the total carbide and boride content can exceed 45 volume %. In some embodiments, the total carbide and boride content can exceed 50 volume %.
  • the grain size of all carbides and borides may not exceed 25 micrometers in their longest dimension. In some embodiments, the grain size of all carbides and borides may not exceed 5 micrometers in their longest dimension.
  • the article of manufacture can comprise a sleeve or layer for use in pipelines designed to carry abrasive slurries. Also disclosed herein are embodiments of a wear resistant component comprising embodiments of the disclosed article of manufacture.
  • an article of manufacture comprising an alloy comprising Fe, Cr, and C, wherein a total carbide and boride content in a micro structure of the alloy exceeds 0.4 mole fraction, and wherein a total volume of segregated carbides is less than 0.05 mole fraction, segregated carbides being defined as Fe or Cr - rich boride or carbide meeting the equation: Fe+Cr >50 wt.%, wherein the segregated carbides are thermodynamically stable at a temperature above a temperature at which austenite of the alloy is thermodynamically stable.
  • the alloy can be an iron based alloy and can comprise C: 2.2-4.02 wt. %, and Cr: 10-34 wt.
  • the alloy can comprise C: 2.5-3.8 wt.%, Cr: 10-28 wt.%, b: 0-5 wt. %, and W: 0-9 wt. %.
  • the alloy can comprise Mn: 0-1 wt. %, Mo: 0-1 wt. %, Si: 0-1 wt. %, Ti: 0-0.5 wt. %, and V: 0-3 wt.%.
  • the alloy can comprise C: 2.2-4.02 wt.%, Cr: 12.7- 34 wt.%, Nb: 3.8-5 wt. %, and W: 4.37-9 wt. %.
  • the total carbide and/or boride content can exceed 0.45 mole fraction. In some embodiments, the total carbide and/or boride content can exceed 0.50 mole fraction.
  • the article of manufacture can comprise a sleeve or layer used in pipelines designed to carry abrasive slurries. Also disclosed herein are embodiments of a wear resistant component which can comprise embodiments of the disclosed article of manufacture.
  • Also disclosed herein are embodiments of a method of forming a component comprising providing an alloy comprising Fe, Cr, and C, wherein a total carbide and boride content in a micro structure of the alloy exceeds 40 volume %. and wherein a grain size of all carbides and borides is less than or equal to 50 micrometers in their longest dimension, and forming a component from the alloy.
  • the alloy can be an iron-based alloy and can comprise C: 2.2-4.02 wt. %, and Cr: 10-34 wt. %.
  • the alloy can comprise C: 2.5-3.8 wt.%, Cr: 10-28 wt.%, Nb: 0-5 wt. %, W: 0-9 wt. %, Mn: 0-1 wt. %, Mo: 0-1 wt. %, Si: 0-1 wt. %, Ti: 0-0.5 wt. %, and V: 0-3 wt.%.
  • the alloy can comprise C: 2.2-4.02 wt.%, Cr: 12.7-34 wt.%, Nb: 3.8-5 wt. %, and W: 4.37-9 wt. %.
  • the total carbide and/or boride content can exceed 0.45 mole fraction. In some embodiments, the total carbide and/or boride content can exceed 0.50 mole fraction.
  • the method can comprise forming the component via a casting process. In some embodiments, the method can comprise forming the component into a sleeve or layer.
  • Figure 1 illustrates a solidification diagram of an embodiment of, in wt. %, Fe: bal, Cr: 25%, C:3.6%.
  • Figure 2 illustrates a solidification diagram of an embodiment of, in weight %, Fe: 17%, C:3.6%, Nb 5%, W 5%.
  • Figures 3A-B illustrate an SEM micrograph of embodiments of alloy X22 at 1,000X magnification ( Figure 3A) and 5,000X magnification ( Figure 3B).
  • Figure 4 illustrates an SEM micrograph of embodiments of alloy X24 at 1,000X magnification.
  • an alloy material such as an alloy containing Fe, C and Cr, having high carbide contents, as well as a method of increasing carbide content in an alloy.
  • the alloy is pushed towards increased amounts of primary, or eutectic, chromium carbide fractions, so embodiments of the disclosed alloys may fall within the group known as chromium white irons.
  • the disclosed alloys can be "iron based," indicating that they have a composition that is predominantly iron, e.g., at least 50 wt. % iron.
  • criteria that can be used for producing a high carbide content alloy. Thermodynamic, micro structural, and compositional criteria could be used to produce such an alloy. In some embodiments, only one of the criterial can be used to form the alloy, and in some embodiments multiple criteria can be used to form the alloy.
  • an alloy can be described fully by thermodynamic models.
  • Two thermodynamic criteria can be used to define fine-grained high carbide content cast irons as are described herein: 1) the maximum mole fraction of the carbide or boride content in the material formed during cooling from a liquid state, and 2) the mole fraction of Fe,Cr-rich type carbides formed prior to the initial formation of the austenitic or ferritic matrix.
  • Fe,Cr-rich type carbides are defined as those where the Fe+Cr weight percent exceeds 50% (or exceeds about 50%).
  • An example solidification diagram is shown in Figure 1 that demonstrates embodiments of the thermodynamic criteria described in this disclosure.
  • FIG. 1 shows an example within the Fe-Cr-C system where the total carbide content in the system may not exceed 40% (or about 40%) without introducing undesirable segregated M 7 C 3 type carbides.
  • Figure 2 shows an example of an alloy system which can possess a high total carbide content (50-55% mole fraction or about 50 to about 55% mole fraction) that may not have any Fe,Cr-rich type carbide phase which forms above the liquidus temperature of the austenite.
  • the alloy shown as an example in Figure 2 can possess the disclosed thermodynamic criteria.
  • the first thermodynamic criterion (the maximum mole fraction of the carbide or boride content in the material formed during cooling from a liquid state) can be used as an indicator for the wear resistance of the material.
  • the criterion will be abbreviated as carbide-max.
  • carbide-max Generally, increased carbide or boride contents can lead to increased wear resistance and can be desirable.
  • the maximum mole fraction of the carbide or boride content can be calculated by evaluating the phase fractions of thermodynamically stable phases as a function of temperature over a range from room temperature to a temperature where the alloy is thermodynamically 100% liquid.
  • the maximum content of carbides or borides at any one temperature is defined as carbide -max.
  • Carbide-max can be the sum of all types of carbide or boride phases at that temperature.
  • the carbide-max can be at least 41% (or at least about 41%) mole fraction.
  • carbide-max can be at least 45% (or at least about 45%) mole fraction.
  • carbide-max can be at least 50% (or at least about 50%) mole fraction.
  • the second thermodynamic criterion (the mole fraction of Fe,Cr-rich type carbides formed prior to the initial formation of the austenitic or ferritic matrix) can be used as an indicator for the toughness of the material.
  • the criterion will be abbreviated as segregated carbide fraction.
  • an increased mole fraction of segregated carbides can decrease the toughness of the material and can be undesirable.
  • the segregated carbide fraction is calculated by 1) identifying the highest temperature at which an iron matrix phase (austenite or ferrite) exists; and 2) calculating the total mole fraction of M 7 C 3 type carbides at 5K higher.
  • the segregated carbide content can be below 5% (or below about 5%).
  • the segregated carbide content can be 0% (or about 0%).
  • thermodynamic criterion can be utilized.
  • This third criterion can be the chromium content in the Fe-based matrix phase, whether austenite or ferrite, at 1300K (or about 1300K). This criterion is thereby designated the matrix chromium content. This value has been selected as it can be similar to the value measured in casting experiments for several candidate alloys.
  • the matrix chromium content can be above 5 weight % (or above about 5 weight %).
  • the matrix chromium content can be above 9 weight % (or above about 9 weight %).
  • the matrix chromium content can be above 12 weight % (or above about 12 weight %).
  • Table 1 contains a list of some, but not all, alloys which can meet the thermodynamic criteria.
  • the alloy can be described by the micro structural features it possesses. Similar to the concepts described as the thermodynamic criteria, it can be advantageous to have a high fraction of carbides (40% volume fraction or higher, or about 40%) volume fraction or higher) to increase hardness and wear resistance.
  • embodiments of the disclosed alloys can have a hardness between 55-70 HRC (or between about 50 and about 70 HRC).
  • the disclosed alloys can have a hardness between 60-65 HRC (or between about 60 and about 65 HRC).
  • the disclosed alloys can have high abrasion resistance as classified by ASTM 65 testing of at least below 0.2 grams lost (or below about 0.2 grams lost).
  • the disclosed alloys can have high abrasion resistance as classified by ASTM 65 testing of at least below 0.15 grams lost (or below about 0.15 grams lost). In some embodiments, the disclosed alloys can have high abrasion resistance as classified by ASTM 65 testing of at least below 0.2 grams lost (or below about 0.2 grams lost). However, it can be also advantageous for these carbides to be relatively fine-grained in order for the structure to maintain a minimum toughness.
  • the measured volume fraction of the carbides or borides in the alloy can exceed 40 volume % (or exceed about 40 volume %). In some embodiments, the measured volume fraction of the carbides can exceed 45 volume % (or exceed about 45 volume %). In some embodiments, the measured volume fraction in the alloy can exceed 50 volume % (or exceed about 50 volume %).
  • the grain size of any carbides and borides present in the micro structure may not exceed 50 micrometers (or exceed about 50 micrometers) in their longest dimension. In some embodiments, the grain of any carbides and borides present in the micro structure may not exceed 25 micrometers (or exceed about 25 micrometers) in their longest dimension. In some embodiments, the grain of any carbides and borides present in the micro structure may not exceed 5 micrometers (or exceed about 5 micrometers) in their longest dimension. In some embodiments, all carbides and borides are below the above listed parameters. In some embodiments, substantially all carbides and borides are below the above listed parameters. In some embodiments, 90%, 95%, 98%, or 99% of all carbides and borides are below the above listed parameters.
  • alloy X22 As shown in Figures 3A-B.
  • the SEM micrograph shows a material with a very high fraction of carbides with a fine-grain size.
  • Two types of carbide dominate the micro structure, niobium carbide (301) and chromium carbide (302).
  • niobium carbide (301)
  • chromium carbide (302)
  • the chromium carbide can become coarse.
  • the chromium carbides remain fine on the order of 10 ⁇ x 1-2 ⁇ in dimension.
  • chromium carbides As previously mentioned, the formation of a high fraction of fine-grained chromium carbides is not an inherent feature of this alloy system as demonstrated by the micrograph shown in Figure 4.
  • the X24 alloy has a relatively similar composition to X22, however the micro structure possesses larger chromium carbides (401) on the order of 50-150 ⁇ known to reduce toughness.
  • This example is provided to illustrate the fact that simple alloying additions of carbide forming elements such as Nb, Ti, W, Mo, V, W, and/or Ta are not sufficient to produce the micro structural features described in this disclosure. Rather, relatively small compositional spaces exist within the greater region defined as cast irons, and computational modeling is the only effective mechanism to effectively identify this space.
  • the disclosed alloys can be iron based alloys having both chromium and carbon in order to form eutectic chromium carbides.
  • chromium can be from 10-34 (or about 10 to about 34) wt. % and carbon can be form 2.2-4.02 (or about 2.2 to about 4.02) wt. %.
  • the alloy can be described by a composition in weight percent comprising the following elemental ranges which can meet certain thermodynamic criteria, and which are can be at least partially based on the compositions presented in Table 1 discussed above:
  • the alloy can be described by a composition in weight percent comprising the following elemental ranges which have been produced and evaluated experimentally, and which are at least partially based on the compositions presented in Table 2 and Table 3 :
  • the alloy can be described by a composition in weight percent comprising the following elemental ranges which have been produced and evaluated experimentally and which can meet certain micro structural criteria, and which are at least partially based on the compositions presented in Table 2 and Table 3 above: 3.
  • the alloy can be described by a composition in weight percent comprising the following elemental ranges as defined through glow discharge spectrometer readings, which have been produced and evaluated experimentally and which can meet certain micro structural criteria, and which are at least partially based on the compositions presented in Table 3 above:
  • the alloy can be described by specific compositions in weight percent comprising the following elements, which have been produced and evaluated experimentally and which can meet certain micro structural criteria, and which are at least partially based on the nominal and measured experimental compositions:
  • the Fe compositions listed above can be the balance of the alloy material. In some embodiments, minor impurities can also be found within the composition.
  • increased carbide content can be advantageous because a high fraction of primary (Nb, Ti, V) carbides can effectively increase the liquidus temperature of an alloy and decreases fluidity, which can improve casting processes.
  • Embodiments of the disclosed alloys can be used in a variety of applications and industries. Some non-limiting examples of applications of use include:
  • Embodiments of the disclosed alloys can be included in the following components and coatings for the following components: wear resistant sleeves and/or wear resistant hardfacing for slurry pipelines, mud pump components including pump housing or impeller or hardfacing for mud pump components, ore feed chute components including chute blocks or hardfacing of chute blocks, separation screens including but not limited to rotary breaker screens, banana screens, shaker screens, liners for autogenous grinding mills and semi-autogenous grinding mills, ground engaging tools and hardfacing for ground engaging tools, wear plate for buckets and dumptruck liners, heel blocks and hardfacing for heel blocks on mining shovels, grader blades and hardfacing for grader blades, stacker reclaimers, siazer crushers, general wear packages for mining components, and other communition components.
  • Embodiments of the disclosed alloys can be included in the following components and coatings for the following components: downhole casing and downhole casing, drill pipe and coatings for drill pipe including hardbanding, mud management components, mud motors, fracking pump sleeves, fracking impellers, fracking blender pumps, stop collars, drill bits and drill bit components, directional drilling equipment and coatings for directional drilling equipment including stabilizers and centralizers, blow out preventers and coatings for blow out preventers and blow out preventer components including the shear rams, oil country tubular goods, and coatings for oil country tubular goods.
  • Embodiments of the disclosed alloys can be included in the following components and coatings for the following components: process vessels and coating for process vessels including steam generation equipment, amine vessels, distillation towers, cyclones, catalytic crackers, general refinery piping, corrosion under insulation protection, sulfur recovery units, convection hoods, sour stripper lines, scrubbers, hydrocarbon drums, and other refinery equipment and vessels.
  • Embodiments of the disclosed alloys can be included in following components and coatings for the following components: rolls used in paper machines including yankee dryers and other dryers, calendar rolls, machine rolls, press rolls, digesters, pulp mixers, pulpers, pumps, boilers, shredders, tissue machines, roll and bale handling machines, doctor blades, evaporators, pulp mills, head boxes, wire parts, press parts, M.G. cylinders, pope reels, winders, vacuum pumps, deflakers, and other pulp and paper equipment,
  • Embodiments of the disclosed alloys can be included in the following components and coatings for the following components: boiler tubes, precipitators, fireboxes, turbines, generators, cooling towers, condensers, chutes and troughs, augers, bag houses, ducts, ID fans, coal piping, and other power generation components.
  • Embodiments of the disclosed alloys can be included in the following components and coatings for the following components: chutes, base cutter blades, troughs, primary fan blades, secondary fan blades, augers, and other agricultural applications.
  • Embodiments of the disclosed alloys can be included in the following components and coatings for the following components: cement chutes, cement piping, bag houses, mixing equipment, and other construction applications
  • Machine element applications Embodiments of the disclosed alloys can be included in the following components and coatings for the following components: shaft journals, paper rolls, gear boxes, drive rollers, impellers, general reclamation and dimensional restoration applications, and other machine element applications
  • Embodiments of the disclosed alloys can be included in the following components and coatings for the following components: cold rolling mills, hot rolling mills, wire rod mills, galvanizing lines, continue pickling lines, continuous casting rolls and other steel mill rolls, and other steel applications.
  • embodiments of the alloys described can be produced and or deposited in a variety of techniques effectively. Some non-limiting examples of processes include:
  • Thermal spray process including those using a wire feedstock such as twin wire arc, spray, high velocity arc spray, combustion spray and those using a powder feedstock such as high velocity oxygen fuel, high velocity air spray, plasma spray, detonation gun spray, and cold spray.
  • Wire feedstock can be in the form of a metal core wire, solid wire, or flux core wire.
  • Powder feedstock can be either a single homogenous alloy or a combination of multiple alloy powder which result in the desired chemistry when melted together.
  • Wire feedstock can be in the form of a metal core wire, solid wire, or flux core wire.
  • Powder feedstock can be either a single homogenous alloy or a combination of multiple alloy powder which result in the desired chemistry when melted together.
  • Casting processes including processes typical to producing cast iron including but not limited to sand casting, permanent mold casting, chill casting, investment casting, lost foam casting, die casting, centrifugal casting, glass casting, slip casting and process typical to producing wrought steel products including continuous casting processes.
  • Post processing techniques including but not limited to rolling, forging, surface treatments such as carburizing, nitriding, carbonitriding, heat treatments including but not limited to austenitizing, normalizing, annealing, stress relieving, tempering, aging, quenching, cryogenic treatments, flame hardening, induction hardening, differential hardening, case hardening, decarburization, machining, grinding, cold working, work hardening, and welding.
  • Conditional language such as “can,” “could,” “might,” or “may,” unless specifically stated otherwise, or otherwise understood within the context as used, is generally intended to convey that certain embodiments include or do not include, certain features, elements, and/or steps. Thus, such conditional language is not generally intended to imply that features, elements, and/or steps are in any way required for one or more embodiments.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Powder Metallurgy (AREA)

Abstract

L'invention concerne des modes de réalisation d'alliages à haute teneur en carbure, à grains fins, et des procédés de fabrication de tels alliages. Les alliages peuvent être déterminés par l'utilisation de critères thermodynamiques, micro-structurels, et de composition en vue de créer un alliage à résistance et ténacité élevées. Dans certains modes de réalisation, les alliages peuvent être utilisés en tant que composant résistant à l'usure.
PCT/US2015/024508 2014-04-07 2015-04-06 Alliages de fer coulés à teneur en carbure élevée, à grains fins WO2015157169A2 (fr)

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Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN105290703A (zh) * 2015-11-04 2016-02-03 北京工业大学 一种用埋弧堆焊和激光熔覆修复磨损热轧辊的方法
CN106801186A (zh) * 2016-12-16 2017-06-06 广西大学 一种抗碱铸铁冷凝器及其制备方法
CN107150175A (zh) * 2017-07-13 2017-09-12 淮阴工学院 损伤齿轮激光实时动态熔覆修复及应力调控系统及方法
CN108004458A (zh) * 2017-12-13 2018-05-08 中钢集团邢台机械轧辊有限公司 一种钨变质处理的改进型高铬铁轧辊
US10100388B2 (en) 2011-12-30 2018-10-16 Scoperta, Inc. Coating compositions
US10105796B2 (en) 2015-09-04 2018-10-23 Scoperta, Inc. Chromium free and low-chromium wear resistant alloys
WO2019056227A1 (fr) * 2017-09-20 2019-03-28 杭州巨星科技股份有限公司 Outil ayant une lame de coupe et son procédé de fabrication
US10329647B2 (en) 2014-12-16 2019-06-25 Scoperta, Inc. Tough and wear resistant ferrous alloys containing multiple hardphases
US10465267B2 (en) 2014-07-24 2019-11-05 Scoperta, Inc. Hardfacing alloys resistant to hot tearing and cracking
US10465269B2 (en) 2014-07-24 2019-11-05 Scoperta, Inc. Impact resistant hardfacing and alloys and methods for making the same

Families Citing this family (23)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
AU2013329190B2 (en) 2012-10-11 2017-09-28 Scoperta, Inc. Non-magnetic metal alloy compositions and applications
CA2931842A1 (fr) 2013-11-26 2015-06-04 Scoperta, Inc. Alliage a rechargement dur resistant a la corrosion
CN106661702B (zh) 2014-06-09 2019-06-04 斯克皮尔塔公司 抗开裂硬面堆焊合金
WO2017044475A1 (fr) 2015-09-08 2017-03-16 Scoperta, Inc. Alliages non magnétiques de formation de carbures forts destinés à la fabrication de poudres
CA3003048C (fr) 2015-11-10 2023-01-03 Scoperta, Inc. Matieres de projection a l'arc a deux fils a oxydation controlee
CN105598395A (zh) * 2016-02-03 2016-05-25 河北海鲲机械设备有限公司 大型叶轮铸造生产方法
EP3433393B1 (fr) * 2016-03-22 2021-10-13 Oerlikon Metco (US) Inc. Revêtement issu de la projection thermique entièrement lisible
CN106378547B (zh) * 2016-11-08 2019-02-19 甘肃酒钢集团西部重工股份有限公司 一种陶瓷耐磨堆焊焊条
CN107164757B (zh) * 2017-04-26 2019-02-01 燕山大学 一种大型柴油机活塞销的修复方法
CN107148815B (zh) * 2017-05-17 2019-12-13 安徽巨泰机械制造有限公司 一种旋耕机用高强耐磨旋耕刀
WO2018231779A1 (fr) * 2017-06-13 2018-12-20 Scoperta, Inc. Alliages non magnétiques à fraction élevée de phase dure
WO2019109138A1 (fr) * 2017-12-04 2019-06-13 Weir Minerals Australia Limited Fontes blanches résilientes et résistantes à la corrosion
JP2022505878A (ja) 2018-10-26 2022-01-14 エリコン メテコ（ユーエス）インコーポレイテッド 耐食性かつ耐摩耗性のニッケル系合金
EP3962693A1 (fr) 2019-05-03 2022-03-09 Oerlikon Metco (US) Inc. Charge d'alimentation pulvérulente destinée au soudage en vrac résistant à l'usure, conçue pour optimiser la facilité de production
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JP7449766B2 (ja) 2020-04-16 2024-03-14 福田金属箔粉工業株式会社 投射材用鉄合金
CN114763609B (zh) * 2021-01-15 2023-10-13 宝山钢铁股份有限公司 一种耐磨轴套涂层及其制备方法
CN115074612B (zh) * 2022-03-04 2023-03-17 中原内配集团股份有限公司 一种铸铁缸套及铸铁缸套制作方法
US12084732B2 (en) * 2022-03-29 2024-09-10 Townley Foundry & Machine Co., Inc. Hypereutectic white iron alloy comprising chromium, boron and nitrogen and cryogenically hardened articles made therefrom
CN116083785A (zh) * 2022-12-27 2023-05-09 安徽华聚新材料有限公司 一种耐磨高铬铸铁及其制备方法

Family Cites Families (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4576653A (en) * 1979-03-23 1986-03-18 Allied Corporation Method of making complex boride particle containing alloys
US4297135A (en) * 1979-11-19 1981-10-27 Marko Materials, Inc. High strength iron, nickel and cobalt base crystalline alloys with ultrafine dispersion of borides and carbides
CH660753A5 (fr) * 1982-07-19 1987-06-15 Giw Ind Inc Procede de refroidissement avec surfusion d'une fonte liquide.
ZA844074B (en) * 1983-05-30 1986-04-30 Vickers Australia Ltd Abrasion resistant materials
GB8403036D0 (en) * 1984-02-04 1984-03-07 Sheepbridge Equipment Ltd Cast iron alloys
JP2857724B2 (ja) * 1991-04-01 1999-02-17 株式会社クボタ 高速度鋼系焼結合金
EP1825013B1 (fr) * 2003-10-27 2012-01-18 Global Tough Alloys Pty Ltd Alliage ameliore resistant a l'usure
US9546412B2 (en) * 2008-04-08 2017-01-17 Federal-Mogul Corporation Powdered metal alloy composition for wear and temperature resistance applications and method of producing same
SE533988C2 (sv) * 2008-10-16 2011-03-22 Uddeholms Ab Stålmaterial och förfarande för framställning därav
US20120160363A1 (en) * 2010-12-28 2012-06-28 Exxonmobil Research And Engineering Company High manganese containing steels for oil, gas and petrochemical applications

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US10465269B2 (en) 2014-07-24 2019-11-05 Scoperta, Inc. Impact resistant hardfacing and alloys and methods for making the same
US10329647B2 (en) 2014-12-16 2019-06-25 Scoperta, Inc. Tough and wear resistant ferrous alloys containing multiple hardphases
US10105796B2 (en) 2015-09-04 2018-10-23 Scoperta, Inc. Chromium free and low-chromium wear resistant alloys
CN105290703A (zh) * 2015-11-04 2016-02-03 北京工业大学 一种用埋弧堆焊和激光熔覆修复磨损热轧辊的方法
CN106801186A (zh) * 2016-12-16 2017-06-06 广西大学 一种抗碱铸铁冷凝器及其制备方法
CN107150175A (zh) * 2017-07-13 2017-09-12 淮阴工学院 损伤齿轮激光实时动态熔覆修复及应力调控系统及方法
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