EP1721999A1 - Corrosion and wear resistant alloy - Google Patents

Corrosion and wear resistant alloy Download PDF

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Publication number
EP1721999A1
EP1721999A1 EP06252443A EP06252443A EP1721999A1 EP 1721999 A1 EP1721999 A1 EP 1721999A1 EP 06252443 A EP06252443 A EP 06252443A EP 06252443 A EP06252443 A EP 06252443A EP 1721999 A1 EP1721999 A1 EP 1721999A1
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Prior art keywords
alloy
corrosion
chromium
wear
vanadium
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EP06252443A
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German (de)
English (en)
French (fr)
Inventor
Alojz Kajinic
Andrzej L. Wojcieszynski
Maria K. Sawford
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Crucible Materials Corp
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Crucible Materials Corp
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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%
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
    • 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
    • C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.7% by weight of carbon

Definitions

  • the invention relates to powder metallurgy corrosion and wear resistant tool steel alloy article, manufactured by hot isostatic compaction of nitrogen atomized, prealloyed high-chromium, high-vanadium, high-niobium powder particles.
  • the alloy of the article of the invention is characterized by very high wear and corrosion resistance, making it in particular useful as a material from which to make components for advanced bearing designs as well as machinery parts exposed to severe abrasive wear and corrosion conditions such as those, among many others, in the plastic injection molding industry and the food industry.
  • the trend in the industry is to keep increasing processing parameters (e.g., temperature and pressure), which in turn imposes ever-increasing demands on the alloys and their ability to successfully withstand corrosion attack and wear of the materials being processed.
  • the corrosiveness and abrasiveness of those materials are constantly increasing.
  • the wear resistance of tool steels depends on the amount, the type, and the size distribution of primary carbides, as well as the overall hardness.
  • V-rich and V-Nb-rich MC primary carbides possess the highest hardness.
  • the corrosion resistance of tool steels depends primarily on the amount of "free” chromium in the matrix, i.e., the amount of chromium that is not “tied up” into carbides.
  • through-hardening tool steel must contain at least about 12 wt. % "free” chromium in the martensitic matrix after heat treatment.
  • corrosion and wear resistant tool steels must also contain a relatively high level of carbon for heat treatment response. As chromium has a high affinity for carbon with which it forms chromium-rich carbides, a corrosion and wear resistant tool steel must contain excess chromium.
  • tool steels The corrosion resistance of tool steels is further improved by the presence of molybdenum in the martensitic matrix.
  • Some tool steels that contain about 10 wt. % "free" chromium in the martensitic matrix are corrosion resistant because they also contain a sufficient amount of "free" molybdenum.
  • An example is Crucible 154 CM grade, which is based on the Fe-1.05C-14Cr-4Mo system.
  • the tool steel In order to withstand the stresses imposed during operation, the tool steel must also possess sufficient mechanical properties, such as hardness, bend fracture strength, and toughness. In addition, the tool steel must possess sufficient hot workability, as well as machinability and grindability, to ensure that parts with the required shape and dimensions can be manufactured. In general, the higher the volume fraction of primary carbides, the higher the wear resistance of the tool steel, and the lower its toughness and hot workability.
  • the corrosion and wear resistant martensitic tool steels currently used include grades such as CPM S90V, M390, Elmax, Anval 10V-12, HTM X235, for example.
  • the overall chromium content of some of these alloys is as high as 20 wt. % (e.g., M390)
  • the corrosion resistance is not necessarily as high as one might expect.
  • a large amount of chromium which is a strong carbide former, is pulled out of the matrix and tied up into chromium-rich carbides. This tied up chromium does not contribute toward the corrosion resistance.
  • niobium is used as well in order to further increase the amount of MC primary carbides, and in turn decrease the amount of chromium-rich primary carbides, due to the fact that niobium has even a higher affinity toward carbon than vanadium.
  • a primary object of the invention is to provide wear and corrosion resistant, high chromium, high vanadium, high niobium, powder metallurgy tool steel article with significantly improved corrosion and wear resistance.
  • the alloy article of the invention possesses a unique combination of corrosion and wear properties that are achieved by balancing its overall chemical composition as well as selecting an appropriate heat treatment.
  • the major alloying elements used in the alloy of the invention are ferrite stabilizers. High amounts of these ferrite stabilizers can lead to the presence of ferrite in the heat-treated microstructure. It has been discovered, however, that the presence of about 2 wt. % cobalt in the ,alloying system of the invention is a necessary and sufficient measure to eliminate ferrite in the heat-treated microstructure.
  • the alloy of the invention is to be preferably hot isostatically pressed at the temperature of 2150°F ( ⁇ 25°F) and the pressure of at least 14.5 ksi.
  • a corrosion and wear resistant article produced by hot isostatic compaction of nitrogen gas atomized prealloyed powder particles within the following composition limits, in weight percent, carbon, 2.0 to 3.5, preferably 2.7 to 3.0; silicon 1.0 max.; chromium 12.0 to 16.0, preferably 13.5 to 14.5; molybdenum 2.0 to 5.0 preferably 3.0 to 4.0; vanadium 6.0 to 11.0, preferably 8.5 to 9.5; niobium 2.0 to 6.0, preferably 3.0 to 4.0; cobalt 1.5 to 5.0, preferably 2.0 to 3.0; nitrogen 0.05 to 0.30, preferably 0.10 to 0.20; and balance iron and incidental impurities.
  • C max 0.6 + 0.099 ⁇ % Cr ⁇ 11 + 0.063 ⁇ % Mo + 0.177 ⁇ % V + 0.13 ⁇ % Nb ⁇ 0.85 ⁇ % N
  • Figure 1 shows a vertical section of the Fe-C-Cr-Mo-V-Nb-N system at 14 wt % Cr, 3.5 wt % Mo, 9 wt % V, 3.5 wt % Nb, and 0.13 wt % N;
  • Figure 2 is a vertical section of the Fe-C-Cr-Mo-V-Nb-Co-N system at 14 wt % Cr, 3.5 wt % Mo, 9 wt % V, 3.5 wt % Nb, 2 wt % Co, and 0.13 wt % N;
  • Figure 3 shows the etched microstructure (magnification of 1500X) of the alloy of the invention (04-099) hardened from 2150°F in oil and tempered at 975°F for 2h+2h+2h;
  • Figure 4 shows the etched microstructure (magnification of 1500X) of the hardened alloy (04-100) with no cobalt present.
  • Table 1 gives the chemical compositions that were examined experimentally and that led to the alloy of the article of the invention that achieves an improved combination of corrosion and wear resistant properties.
  • the reported alloys 03-192 through 04-099 are alloys in accordance with the invention.
  • compositions were prepared using the Crucible Particle Metallurgy (CPM) technology. Prealloyed tool steel grades of the various reported chemical compositions were melted in a nitrogen atmosphere, atomized by nitrogen gas, and hot-isostatically-pressed (HIP) at the temperature of 2150°F and the pressure of 14.5 ksi for four hours.
  • CPM Crucible Particle Metallurgy
  • Carbon is present in an amount of at least 2.0 %, while the maximum content of carbon may amount to 3.5 %, and preferably in the range of 2.7-3.0 %. It is important to carefully control the amount of carbon in order to obtain a desired combination of corrosion and wear resistance, as well as to avoid forming either ferrite or unduly large amounts of retained austenite during heat treatment.
  • the carbon in the articles of the invention may preferably be balanced with the chromium, molybdenum, vanadium, and nitrogen contents of the alloy of the invention according to the following formulae:
  • C min 0.4 + 0.099 ⁇ % Cr ⁇ 11 + 0.063 ⁇ % Mo + 0.177 ⁇ % V + 0.13 ⁇ % Nb ⁇ 0.85 ⁇ % N
  • C max 0.6 + 0.099 ⁇ % Cr ⁇ 11 + 0.063 ⁇ % Mo + 0.177 ⁇ % V + 0.13 ⁇ % Nb ⁇ 0.85 ⁇ % N
  • Nitrogen is present in an amount of 0.05-0.30 %, and preferably in the range of 0.10-0.20 %.
  • the effects of nitrogen in the alloy of the invention are rather similar to those of carbon.
  • nitrogen forms carbonitrides with vanadium, niobium, tungsten, and molybdenum. Unlike carbon, nitrogen improves the corrosion resistance of the alloy of the invention when dissolved in the martensitic matrix.
  • Silicon may be present in an amount of up to 1 %, and preferably up to 0.5 %. Silicon functions to deoxidize the prealloyed materials during the melting phase of the gas-atomization process. In addition, silicon improves the tempering response. Excessive amounts of silicon are undesirable, however, as it decreases toughness and promotes the formation of ferrite in the microstructure.
  • Manganese may be present in an amount of up to 1 %, and preferably up to 0.5%. Manganese functions to control the negative effects of sulfur on hot workability. This is achieved through the precipitation of manganese sulfide. In addition, manganese improves hardenability and increases the solubility of nitrogen in the liquid prealloyed materials during the melting phase of the gas-atomization process. Excessive amounts of manganese are undesirable, however, as it can lead to the formation of unduly large amounts of retained austenite during the heat treatment.
  • Chromium is present in an amount of 12.0-16.0 %, and preferably in the range of 13.5-14.5 %.
  • the main purpose of chromium is to increase the corrosion resistance, and, to a lesser degree, to increase hardenability and secondary-hardening response.
  • Molybdenum is present in an amount of 2.0-5.0 %, and preferably in the range of 3.0-4.0 %. Like chromium, molybdenum increases the corrosion resistance, hardenability, and secondary-hardening response of the alloy of the invention. Excessive amounts of molybdenum, however, reduce hot workability.
  • Vanadium is present in an amount of 6.0-11.0 %, and preferably in the range of 8.5-9.5 %. Vanadium is critically important for increasing wear resistance. This is achieved through the formation of vanadium-rich MC type primary carbonitrides.
  • niobium-vanadium-rich MC primary carbides contain a smaller amount of chromium compared to vanadium-rich MC primary carbides. This in turn increases the amount of "free" chromium in the matrix, which in turn increases the corrosion resistance.
  • Thermo-Calc software coupled with TCFE3 steel thermodynamic database, was used to model two alloys that have the equivalent amount of vanadium; one with niobium (Fe-2.8C-14Cr-3.5Mo-9V-3.5Nb-2Co-0.13N) and the other one without niobium (Fe-2.8C-14Cr-3.5Mo-11V-2Co-0.13N).
  • the two alloys have the same vanadium equivalency (11 % V).
  • Thermodynamic calculations were performed for the following two austenitization temperatures: 2050°F and 2150°F. The results are given in Tables 2 and 3.
  • the amount of "free" chromium in the matrix is higher in the alloy that contains niobium. Based on thermodynamic calculations, it has been discovered that the presence of niobium decreases the solubility of chromium in MC primary carbides (see Table 3), which in turn results in a higher level of "free" chromium in the matrix.
  • Cobalt is present in an amount of 1.5-5.0 %, and preferably in the range of 2.0-3.0 % in order to prevent the undesirable presence of ferrite ( ⁇ ) in the heat-treated microstructure of the alloy of the invention.
  • Figure 3 shows the microstructure of an alloy of the invention (alloy number 04-099).
  • the alloy was hardened from 2150°F in oil and tempered at 975°F for 2h+2h+2h. After etching with Vilella's reagent for 90 seconds, the total volume of primary carbides was measured to be 21.7 percent, the standard deviation being 0.7 percent.
  • thermodynamics calculations performed on the Fe-2.8C-14Cr-3.5Mo-9V-3.5Nb-0.13N alloy indicated the presence of ferrite ( ⁇ ) when the alloy is austenitized at a temperature that is below 2156°F (see Figure 1).
  • the first set of compositions examined experimentally was centered around the Fe-C-17Cr-2.5Mo-2.5W-3.5Nb-5Co-0.2N system (alloys 02-354 through 02-359; see Table 1).
  • the problem with this alloying system was retained austenite that was difficult to transform into martensite even after sub-zero treatments.
  • the second set of compositions examined experimentally was centered around the Fe-C-14Cr-3Mo-8V-3Nb-2Co-N system (alloys 03-192 through 03-195 and 03-199 through 03-201).
  • the levels of carbon balance tested ranged from -0.20 to +0.20, and were calculated using the following formula:
  • C bal % C ⁇ 0.4 + 0.099 ⁇ % Cr ⁇ 11 + 0.063 ⁇ % Mo + 0.177 ⁇ % V + 0.13 ⁇ % Nb ⁇ 0.85 ⁇ % N
  • the amount of carbon present in the steel has the most profound effect on the properties of any corrosion and wear resistant tool steel grade.
  • the amount of carbon has a direct effect on the hardness, the wear resistance, and the corrosion resistance of wear and corrosion resistant tool steel.
  • the carbon balances were targeted to be close to zero ( ⁇ 0.2%).
  • the alloys that are based on the Fe-C-14Cr-3Mo-8V-3Nb-2CoN system exhibited better hardness response, better corrosion resistance, and marginally better wear characteristics when compared to other corrosion and wear resistant martensitic tool steels.
  • the matrix of the heat treated alloy that contains no cobalt has some ferrite present (see Figure 4), which resulted in poor heat-treat response for the alloy (less than 54 HRC).
  • the other two alloys of the third set that contain about 2 wt. pct. of cobalt (04-098 and 04-099) developed desired heat-treated responses (62.5 HRC and 63.5 HRC, respectively) as well as microstructures that consist of V-Nb-rich MC and Cr-rich M 7 C 3 primary carbides in the matrix of tempered martensite.
  • the pitting resistance equivalent number (PRE) is useful for evaluating the resistance of an austenitic stainless steels to pitting and crevice corrosion.
  • the PRE is calculated using the following equation: Cr + 3.3 Mo + 0.5 W + 16 N
  • the PRE is calculated using the bulk chemical composition.
  • the alloys disclosed herein contain high amounts of primary carbides that deplete the matrix of some of the necessary elements needed for corrosion resistance. Therefore, the PRE of these alloys was calculated using an estimated matrix composition as determined by Thermo-Calc software (see Table 6). The alloys are listed by increasing PRE values.
  • the invention alloy (04-099) Based on the matrix composition, the invention alloy (04-099) has the highest PRE even though it does not have the highest matrix chromium content.
  • the PRE of this alloy (04-099) is even higher than those alloys with higher bulk chromium contents such as MPL-1, X235, M390 and Elmax. Since the matrix chromium content of these alloys is similar, the high PRE of the invention alloy is due to its high contents of chromium and molybdenum in the matrix. This is because 30-47.5% of the chromium in the high chromium alloys is used in the formation of the primary carbides in these materials.
  • chromium in the invention alloy Only about 2.5% of the chromium in the invention alloy is used in the formation of the primary carbides thereby keeping most of the chromium in the matrix to aide in corrosion resistance. More chromium is present in the matrix in the invention alloy due to the presence of niobium and vanadium which preferentially form more stable MC type carbides compared to the M 7 C 3 type (chromium rich) carbides.
  • the wear and corrosion resistant alloys are given different heat treatments. If corrosion resistance is of utmost concern, the alloy is typically tempered at or below 750°F, which allows more of the chromium to stay in the matrix by minimizing the precipitation of secondary carbides. If hardness and wear resistance is the primary concern, then the alloys are typically tempered at 950°F and above to allow for secondary hardening effects to take place. Therefore, each alloy was tempered at 500°F, 750°F, 975°F and 1025°F.
  • the pitting potential (E pit ) for each alloy at each tempering temperature is given in Table 7.
  • the results show that the invention alloy (04-099) with the highest PRE also has the highest resistance to pitting at aii tempering temperatures.
  • the E pit for the invention alloy is almost 50% higher that that of the next closest alloy, Elmax, at a tempering temperature of 500°F.
  • the alloys with 18-20% bulk chromium content, i.e., Elmax, M390 and X235 have mediocre pitting resistance compared to the invention alloy at all tempering temperatures.
  • the alloy with the highest bulk chromium content actually has one of the lowest pitting potentials at the low tempering temperatures.
  • the matrix compositions of X235 and the alloy of the invention are similar. However, the pitting resistance of these two alloys is significantly different. This difference in pitting resistance is attributed to the higher molybdenum content of the invention alloy. The cobalt in the invention alloy is not expected to significantly affect the pitting resistance of the alloy of the invention.
  • the alloys of the invention When compared with CPM S90V, the alloys of the invention (04-098 and 04-099) offer better heat-treatment response ⁇ approximately 1.5-2.0 HRC higher for the same heat treatment.
  • the heat-treatment responses of the alloys of the invention and CPM S90V are given in Table 4.
  • pin-abrasion wear resistance test specimens were austenitized at 2150°F for 10 minutes, quenched in oil, and then tempered at either 500°F (for maximum corrosion resistance) or 975°F (for maximum secondary-hardening response) for 2h+2h+2h. The results are given in Table 5.
  • the pin-abrasion wear resistance of other corrosion and wear resistant martensitic tool steels is included as well for comparison purposes.

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EP06252443A 2005-05-09 2006-05-09 Corrosion and wear resistant alloy Withdrawn EP1721999A1 (en)

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US11/124,350 US20060249230A1 (en) 2005-05-09 2005-05-09 Corrosion and wear resistant alloy

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US (1) US20060249230A1 (zh)
EP (1) EP1721999A1 (zh)
JP (1) JP5165211B2 (zh)
KR (1) KR20060116169A (zh)
CN (1) CN1861826B (zh)
CA (1) CA2544482A1 (zh)
HK (1) HK1095164A1 (zh)
TW (1) TW200702457A (zh)

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EP1921175A1 (en) * 2006-11-13 2008-05-14 Crucible Materials Corporation Corrosion and wear resistant alloy
EP2253398A1 (de) * 2009-01-14 2010-11-24 Böhler Edelstahl GmbH & Co KG Verschleißbeständiger Werkstoff
CN103484773A (zh) * 2013-09-10 2014-01-01 常熟市新洲机械制造厂 新型防磨损食品机械工具
CN103540853A (zh) * 2013-10-29 2014-01-29 洛阳金合耐磨材料有限公司 一种压球机用压辊及其制备方法
WO2017044475A1 (en) 2015-09-08 2017-03-16 Scoperta, Inc. Non-magnetic, strong carbide forming alloys for power manufacture
EP2268842A4 (en) * 2008-03-19 2017-07-26 Valmet Technologies, Inc. Blade made of steel alloy
US11939646B2 (en) 2018-10-26 2024-03-26 Oerlikon Metco (Us) Inc. Corrosion and wear resistant nickel based alloys
US12076788B2 (en) 2019-05-03 2024-09-03 Oerlikon Metco (Us) Inc. Powder feedstock for wear resistant bulk welding configured to optimize manufacturability

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GB0912669D0 (en) * 2009-07-21 2009-08-26 Skf Publ Ab Bearing steels
EP2662166A1 (de) * 2012-05-08 2013-11-13 Böhler Edelstahl GmbH & Co KG Werkstoff mit hoher Beständigkeit gegen Verschleiss
CN103212713B (zh) * 2013-04-22 2015-04-29 安泰科技股份有限公司 热等静压粉固连接法制备不锈钢表面耐磨层的方法
US10094007B2 (en) * 2013-10-24 2018-10-09 Crs Holdings Inc. Method of manufacturing a ferrous alloy article using powder metallurgy processing
CN104894481B (zh) * 2015-05-15 2017-05-03 安泰科技股份有限公司 喷射成形耐磨损耐腐蚀合金
CN104878298B (zh) * 2015-05-15 2017-05-03 安泰科技股份有限公司 粉末冶金耐磨损耐腐蚀合金
CN114318132B (zh) * 2021-03-22 2023-06-27 武汉钜能科技有限责任公司 耐腐蚀耐磨损工具钢

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CN103540853B (zh) * 2013-10-29 2016-05-25 洛阳金合耐磨材料有限公司 一种压球机用压辊的制备方法
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CN1861826B (zh) 2010-12-15
JP5165211B2 (ja) 2013-03-21
CA2544482A1 (en) 2006-11-09
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CN1861826A (zh) 2006-11-15
US20060249230A1 (en) 2006-11-09

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