WO1996038596A1 - Fonte graphitique spherique a haute resistance mecanique - Google Patents

Fonte graphitique spherique a haute resistance mecanique Download PDF

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Publication number
WO1996038596A1
WO1996038596A1 PCT/JP1995/001024 JP9501024W WO9638596A1 WO 1996038596 A1 WO1996038596 A1 WO 1996038596A1 JP 9501024 W JP9501024 W JP 9501024W WO 9638596 A1 WO9638596 A1 WO 9638596A1
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WO
WIPO (PCT)
Prior art keywords
iron
spheroidal graphite
strength
less
modulus
Prior art date
Application number
PCT/JP1995/001024
Other languages
English (en)
Japanese (ja)
Inventor
Shoji Kato
Original Assignee
Wing Metal Corporation
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
Priority to JP5293189A priority Critical patent/JPH07145444A/ja
Priority claimed from JP5293189A external-priority patent/JPH07145444A/ja
Application filed by Wing Metal Corporation filed Critical Wing Metal Corporation
Priority to PCT/JP1995/001024 priority patent/WO1996038596A1/fr
Publication of WO1996038596A1 publication Critical patent/WO1996038596A1/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
    • C22C37/04—Cast-iron alloys containing spheroidal graphite

Definitions

  • the present invention relates to a high-strength spheroidal graphite iron having a high strength and a high toughness when released, and is expected to be an alternative material to steel, forged steel, austempered spheroidal graphite and iron and spheroidal graphite-iron. is there.
  • austempered spheroidal graphite-iron has problems of increased cost due to heat treatment, decreased Young's modulus, and reduced machinability due to processing-induced martensite of residual austenite.
  • the high-strength spheroidal graphite according to the present invention is, as a solution to the above-mentioned problems, a high-strength spheroidal graphite having a high tensile strength and elongation as a free material, and having a high Young's modulus and good machinability. It provides iron.
  • the high-strength spheroidal graphite iron according to the present invention is, by weight%, carbon (C): 3.0-3.8%, silicon (S i): 2.0-2.6%, manganese (Mn): 0.2 to 0.6%, Phosphorus (P): 0.02% or less, Sulfur (S): 0.03% or less, Magnesium (Mg): 0.03 to 0.06%, Nickel (N i) : 0.8 ⁇ : L 2%, copper (Cu) : 0.8 to: I. 2%, molybdenum (Mo): 0.4 to 1.0%, with the balance being substantially iron (F e).
  • the high-strength spheroidal graphite iron is characterized in that bismuth (B i): 20 to 100 ppm and a rare earth element (RE) in a ratio of 0.5 to 1 with respect to the bismuth amount.
  • B i bismuth
  • RE rare earth element
  • the high-strength spheroidal graphite iron according to the present invention has high strength and ductility at the same time by having a matrix structure composed of dense disc-like and Z- or needle-like pearlite while leaving funilite. .
  • Ni, Cu and Mo are alloyed. These elements are necessary to provide good hardenability to iron, and to reduce the thickness sensitivity of iron, and to obtain a uniform matrix. At the same time, it is an element that contributes to the promotion and stability of the perlite base.
  • Ni is concentrated in the matrix near the spheroidal graphite, and when passing through the eutectoid transformation temperature range, the precipitation of carbon contained in the austenite matrix to the graphite grains is suppressed, and the matrix at room temperature is reduced. Although it is made of perlite, the ferrite base can be left in the vicinity of graphite by enriching Ni, which is a fluorinating element. If ⁇ is less than 0.8%, good elongation cannot be obtained. Conversely, if Ni exceeds 1.2%, no increase in mechanical properties is observed and the cost increases. The range of the i content rate is provided.
  • ⁇ is added in order to make the base uniform, taking into account the change in wall thickness when the material is made into a material.
  • the upper limit is set to 1.0% because if it exceeds this, carbides will be formed at the eutectic cell boundary, adversely affecting mechanical properties, especially ductility, and impairing machinability.
  • the lower limit is set to 0.4% because good elongation cannot be obtained below this value.
  • Cu promotes the pearlite base by an action similar to that of Ni, but has an action of making the pearlite denser than Ni.
  • they are inexpensive compared to Ni and are often used as an alternative element to Ni.
  • the upper limit is set.
  • the lower limit is set to 0.4% because if it is less than this, good elongation cannot be obtained.
  • Ni and Cu compensates for the disadvantages of each element, and is for economical reasons to obtain inexpensive and optimal mechanical properties, Young's modulus and machinability.
  • C and Si are the chemical compositions of general spheroidal graphite and iron. If the content is out of the above range, the properties of the molten metal such as stiffness, shrinkage tendency and chilling tendency are adversely affected. It is provided.
  • Mn which is a pearlite stabilizing element, strongly bends at the eutectic cell boundary, making the matrix components non-uniform and forming carbide. ⁇ This is to significantly reduce the ductility of iron.
  • the content of P is set to not more than 0.03%.
  • S is one of the spheroidization inhibiting elements, and is set to not more than 0.03% at which spheroidal graphite-iron can be obtained economically.
  • Bi increases the number of graphite grains and concentrates at the eutectic cell boundary, mitigating the side effects of Mn and Mo that adversely affect the matrix structure and mechanical properties.
  • the upper limit exceeds 100 PPm, the spheroidizing inhibitory action becomes dominant, and the mechanical properties are remarkably reduced. Therefore, the above range is provided.
  • RE is necessary to prevent spheroidization rate fading and to alleviate the spheroidization inhibitory action of Bi.
  • the ratio to Bi exceeds 1, the effect of increasing the number of graphite particles is suppressed by Bi, and when the ratio is less than 0.5, the inhibitory effect of Bi on spheroidization cannot be avoided. It is provided.
  • FIG. 3 is a view showing a worn surface in Table 2.
  • Table 1 shows the comparison between the high-strength spheroidal graphite iron material of the present invention and the conventional comparative material.
  • FIG. 1 is an external view showing the worn surface shown in Table 2.
  • Comparative material 2 is equivalent to FCD 100 OA
  • Material 1 of the present invention was prepared by melting a molten metal equivalent to FCD500 using a 300 kg high-frequency induction furnace, and adding appropriate amounts of Ni, Cu and Mo. After that, the spheroidized alloy containing 8% Mg and 1% of graphite were spheroidized by the Sandwich method and the late inoculated molten metal was poured into an organic self-hardening type ⁇ , and the JIS G5502Kb type specimen was used. Was produced.
  • the chemical composition analysis result of the test material obtained as the material 1 of the present invention is as follows: C: 3.2%, Si
  • the chemical composition analysis results of the test material obtained as the material 2 of the present invention were as follows: C: 3.70%, Si: 2.33%, Mn: 0.34%, :: 0.025%, S: 0 022%, Mg: 0.055%, Ni: 0.95%, Cu: 0.85%, Mo: 0.44%, with the balance being Fe and other unavoidable impurities.
  • the mechanical properties and Young's modulus of the inventive material 2 are shown in Table 1 in the column of inventive material 2.
  • material 3 of the present invention was prepared by melting a molten metal equivalent to FCD500 using a high-frequency induction furnace having a capacity of 1 t, and adding appropriate amounts of Ni, Cu and Mo thereto. After that, 5% Mg—Fe—Si containing spheroidized alloy containing Bi and RE 1.5% added graphite spheroidized by sandwich method, then 0.3% of late inoculant was added After the seed treatment, the material was put into a self-hardening sand mold to produce a JIS G5502Kb type test material.
  • the chemical composition analysis results of the test material obtained as the material 3 of the present invention were as follows: C: 3.75%, S i: 2.39%, Mn: 0.26%, P: 0.03%, S: 0 02%, Mg: 0.006, Ni: 1.08%, Cu: 1.01%, Mo: 0.82%, Bi: 0.002%, RE: 0.002% The balance was Fe and other unavoidable impurities.
  • the mechanical properties and Young's modulus of the material 3 of the present invention are shown in the column of material 3 of the present invention in Table 1.
  • the material 4 of the present invention was prepared by changing the amount of M 0 added by the equipment of the third embodiment and the same procedure as in the third embodiment. It was produced by a late inoculation in which 0.07% i-alloy was simultaneously added.
  • the chemical composition analysis results of the test material obtained as the material 4 of the present invention were as follows : C: 3.73%, Si: 2.38%, Mn: 0.21%, P: 0.03%, S: 0.02%, Mg: 0.06, Ni: 1.08%, Cu: 1.00%, Mo: 0.49%, Bi: 0.008%, RE: 0.005%, The balance was Fe and other unavoidable impurities.
  • the mechanical properties and Young's modulus of the inventive material 4 are shown in Table 1 in the column of inventive material 4.
  • the results of comparison of the machinability between Inventive material 4 and Comparative material 2 are shown below. The results are shown in Table 2 and in FIG.
  • the comparison of machinability shown in Table 2 and FIG. 1 is based on the values obtained by measuring the wear width of the flank of the main cutting edge of a drill bit formed from the inventive material 4 and the comparative material 2, respectively. The comparison is based on the state of wear.
  • the inventive materials 1 to 4 have higher tensile strength and proof stress and better elongation as compared with the comparative material 1 (free aspheroidal graphite and iron FCD800 equivalent material). .
  • the Young's modulus is higher than that of the comparative material 2 (FCD1000A equivalent material) toughened by the heat treatment, and the excellent characteristics of the present invention materials 1 to 4 are evident.
  • inventive material 4 has a smaller amount of wear at the drill cutting edge and better machinability than the comparative material 2 having substantially the same hardness.
  • the high-strength spheroidal graphite iron according to the present invention alloys a small amount of Ni, Cu, and Mo at an appropriate ratio, and further, Bi and RE are subjected to spheroidizing treatment and / or By being added at the time of inoculation, it has a tensile strength of 900 (N / mm 2 ) or more, an elongation of 4% or more, and a Young's modulus of 169,000 (N / mm 2 ) or more. This is what you can get.
  • a free-form material that meets the standard of FCD800 of JIS G5502 has higher tensile strength and elongation than conventional free-form spheroidal graphite-iron. Also,

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)

Abstract

Fonte graphitique sphérique à haute résistance mécanique présentant, en tant que pièce coulée, une résistance à la traction, un allongement et un module de Young élevés ainsi qu'une bonne usinabilité. Le fer comprend, en poids, de 3 à 3,8 % de carbone, de 2 à 2,6 % de silicium, de 0,2 à 0,6 % de manganèse, 0,02 % ou moins de phosphore, 0,03 % ou moins de soufre, de 0,03 à 0,06 % de magnésium, de 0,8 à 1,2 % de nickel, de 0,8 à 1,2 % de cuivre, de 0,4 à 1 % de molybdène, le reste étant essentiellement composé de fer.
PCT/JP1995/001024 1993-11-24 1995-05-29 Fonte graphitique spherique a haute resistance mecanique WO1996038596A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
JP5293189A JPH07145444A (ja) 1993-11-24 1993-11-24 高強度球状黒鉛鋳鉄
PCT/JP1995/001024 WO1996038596A1 (fr) 1993-11-24 1995-05-29 Fonte graphitique spherique a haute resistance mecanique

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP5293189A JPH07145444A (ja) 1993-11-24 1993-11-24 高強度球状黒鉛鋳鉄
PCT/JP1995/001024 WO1996038596A1 (fr) 1993-11-24 1995-05-29 Fonte graphitique spherique a haute resistance mecanique

Publications (1)

Publication Number Publication Date
WO1996038596A1 true WO1996038596A1 (fr) 1996-12-05

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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2006072663A3 (fr) * 2005-01-05 2007-05-18 Metso Paper Inc Fonte ductile et procede de fabrication associe pour l'elaboration de composants a proprietes de resistance et de tenacite desirees
WO2018150645A1 (fr) * 2017-02-17 2018-08-23 新日鉄住金エンジニアリング株式会社 Fonte à graphite sphéroïdal résistant à la chaleur présentant une excellente résistance au fluage
CN113502431A (zh) * 2021-06-30 2021-10-15 东风商用车有限公司 一种等温淬火球墨铸铁材料及其制备方法和应用

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5613421A (en) * 1979-07-09 1981-02-09 Riken Corp Tough and hard spheroidal graphite cast iron and its manufacture
JPS58104154A (ja) * 1981-12-01 1983-06-21 ゲツツエ・アクチエンゲゼルシヤフト 球晶状の析出グラフアイトを有する耐磨耗性合金鋳鉄及びその製造方法
JPS60187621A (ja) * 1984-03-05 1985-09-25 Toyota Motor Corp 球状黒鉛鋳鉄の熱処理方法
JPS63259048A (ja) * 1987-04-16 1988-10-26 Mazda Motor Corp 球状黒鉛鋳鉄鋳物

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5613421A (en) * 1979-07-09 1981-02-09 Riken Corp Tough and hard spheroidal graphite cast iron and its manufacture
JPS58104154A (ja) * 1981-12-01 1983-06-21 ゲツツエ・アクチエンゲゼルシヤフト 球晶状の析出グラフアイトを有する耐磨耗性合金鋳鉄及びその製造方法
JPS60187621A (ja) * 1984-03-05 1985-09-25 Toyota Motor Corp 球状黒鉛鋳鉄の熱処理方法
JPS63259048A (ja) * 1987-04-16 1988-10-26 Mazda Motor Corp 球状黒鉛鋳鉄鋳物

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2006072663A3 (fr) * 2005-01-05 2007-05-18 Metso Paper Inc Fonte ductile et procede de fabrication associe pour l'elaboration de composants a proprietes de resistance et de tenacite desirees
WO2018150645A1 (fr) * 2017-02-17 2018-08-23 新日鉄住金エンジニアリング株式会社 Fonte à graphite sphéroïdal résistant à la chaleur présentant une excellente résistance au fluage
CN113502431A (zh) * 2021-06-30 2021-10-15 东风商用车有限公司 一种等温淬火球墨铸铁材料及其制备方法和应用

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