JP5282547B2 - High-strength, thick-walled spheroidal graphite cast iron with excellent wear resistance - Google Patents
High-strength, thick-walled spheroidal graphite cast iron with excellent wear resistance Download PDFInfo
- Publication number
- JP5282547B2 JP5282547B2 JP2008310689A JP2008310689A JP5282547B2 JP 5282547 B2 JP5282547 B2 JP 5282547B2 JP 2008310689 A JP2008310689 A JP 2008310689A JP 2008310689 A JP2008310689 A JP 2008310689A JP 5282547 B2 JP5282547 B2 JP 5282547B2
- Authority
- JP
- Japan
- Prior art keywords
- cast iron
- strength
- wear resistance
- thick
- spheroidal graphite
- 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.)
- Active
Links
- 229910001141 Ductile iron Inorganic materials 0.000 title claims description 32
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 32
- 229910002804 graphite Inorganic materials 0.000 claims abstract description 29
- 239000010439 graphite Substances 0.000 claims abstract description 29
- 239000012535 impurity Substances 0.000 claims abstract description 16
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 11
- 239000000203 mixture Substances 0.000 claims abstract description 9
- 229910052802 copper Inorganic materials 0.000 claims abstract description 7
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims description 5
- 229910001018 Cast iron Inorganic materials 0.000 abstract description 30
- 229910052748 manganese Inorganic materials 0.000 abstract description 11
- 229910052799 carbon Inorganic materials 0.000 abstract description 7
- 229910052759 nickel Inorganic materials 0.000 abstract description 5
- 229910052758 niobium Inorganic materials 0.000 abstract description 3
- 230000001105 regulatory effect Effects 0.000 abstract 2
- 230000001747 exhibiting effect Effects 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 18
- 238000000034 method Methods 0.000 description 14
- 229910052751 metal Inorganic materials 0.000 description 12
- 239000002184 metal Substances 0.000 description 12
- 229910001562 pearlite Inorganic materials 0.000 description 8
- 230000002411 adverse Effects 0.000 description 7
- 229910045601 alloy Inorganic materials 0.000 description 6
- 239000000956 alloy Substances 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- 229910052698 phosphorus Inorganic materials 0.000 description 6
- 229910052721 tungsten Inorganic materials 0.000 description 6
- 230000002087 whitening effect Effects 0.000 description 6
- 229910052788 barium Inorganic materials 0.000 description 5
- 229910052791 calcium Inorganic materials 0.000 description 5
- 238000005266 casting Methods 0.000 description 5
- 230000007423 decrease Effects 0.000 description 5
- 230000008018 melting Effects 0.000 description 5
- 238000002844 melting Methods 0.000 description 5
- 229910052782 aluminium Inorganic materials 0.000 description 4
- 229910052797 bismuth Inorganic materials 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 230000006872 improvement Effects 0.000 description 4
- 238000007711 solidification Methods 0.000 description 4
- 230000008023 solidification Effects 0.000 description 4
- 238000009864 tensile test Methods 0.000 description 4
- 229910000676 Si alloy Inorganic materials 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 238000002425 crystallisation Methods 0.000 description 3
- 230000008025 crystallization Effects 0.000 description 3
- 238000009792 diffusion process Methods 0.000 description 3
- 230000005496 eutectics Effects 0.000 description 3
- 238000011081 inoculation Methods 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 229910052761 rare earth metal Inorganic materials 0.000 description 3
- 229910052718 tin Inorganic materials 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- 229910000861 Mg alloy Inorganic materials 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 2
- 238000005299 abrasion Methods 0.000 description 2
- 230000009471 action Effects 0.000 description 2
- 229910001563 bainite Inorganic materials 0.000 description 2
- 239000003795 chemical substances by application Substances 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 239000004576 sand Substances 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 229910000882 Ca alloy Inorganic materials 0.000 description 1
- 229910014458 Ca-Si Inorganic materials 0.000 description 1
- 229910001208 Crucible steel Inorganic materials 0.000 description 1
- 229910017082 Fe-Si Inorganic materials 0.000 description 1
- 229910017133 Fe—Si Inorganic materials 0.000 description 1
- 229910007981 Si-Mg Inorganic materials 0.000 description 1
- 229910008316 Si—Mg Inorganic materials 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 239000004566 building material Substances 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000005087 graphitization Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 239000002054 inoculum Substances 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 230000013011 mating Effects 0.000 description 1
- 235000013372 meat Nutrition 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 150000002910 rare earth metals Chemical class 0.000 description 1
- 230000004044 response Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 102200082816 rs34868397 Human genes 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)
Abstract
Description
本発明は、プレス機械などの各種機械用部品や、各種土木・建築用部材等に好適な、球状黒鉛鋳鉄品に係り、とくに750MPaを超える引張強さを有し、耐摩耗性に優れた高強度厚肉球状黒鉛鋳鉄品に関する。なお、ここでいう「厚肉鋳鉄品」とは、肉厚：100 mm以上の鋳鉄品をいうものとする。 The present invention relates to a spheroidal graphite cast iron product suitable for various machine parts such as a press machine, various civil engineering and building materials, and in particular, has a tensile strength exceeding 750 MPa and a high wear resistance. The present invention relates to a strength thick spheroidal graphite cast iron product. The “thick cast iron product” here refers to a cast iron product having a wall thickness of 100 mm or more.
球状黒鉛鋳鉄は、良好な鋳造性と、高強度を有し、鍛鋼や鋳鋼の代替として、とくに工作機械用の構造部品や、土木・建築用の構造部材等に広く使用されている。近年、構造部材や構造部品等の寿命向上、さらに経済性という観点から、高強度化され耐摩耗性に優れた、安価な鋳鉄品が使用される傾向にある。そのため、熱処理を行うことなく鋳放しのままの状態で、引張強さ：700MPaを超える高強度を有し、耐摩耗性に優れた高強度球状黒鉛鋳鉄品が要求されている。 Spheroidal graphite cast iron has good castability and high strength, and is widely used as a substitute for forged steel and cast steel, especially for structural parts for machine tools and structural members for civil engineering and construction. In recent years, from the viewpoints of improving the life of structural members and structural parts, and further from the viewpoint of economy, there is a tendency to use inexpensive cast iron products that have high strength and excellent wear resistance. Therefore, there is a demand for a high-strength spheroidal graphite cast iron product having a high strength exceeding tensile strength: 700 MPa and excellent wear resistance in an as-cast state without performing heat treatment.
このような要求に対し、例えば特許文献１には、重量比で、Ｃ：3.20〜4.00％、Si：2.00〜3.20％、Mn：0.05〜3.00％を含み、Ｐ、Ｓ、Mgを適正量に調整して含み、さらに、Cu：0.40〜2.00％、希土類：0.005〜0.300％を含有し、残部Feからなる、球状黒鉛鋳鉄品が提案されている。特許文献１に記載された技術により製造された球状黒鉛鋳鉄品は、Cuと希土類元素を複合含有することにより、引張強さ700Ｎ/mm2以上の高強度と、伸び：２％以上の高延性を確保できるとしている。 In response to such a request, for example, Patent Document 1 includes C: 3.20 to 4.00%, Si: 2.00 to 3.20%, Mn: 0.05 to 3.00% by weight ratio, and P, S, and Mg in appropriate amounts. There has been proposed a spheroidal graphite cast iron product that is adjusted and contains Cu: 0.40 to 2.00%, rare earth: 0.005 to 0.300%, and the balance being Fe. Spheroidal graphite cast iron manufactured by the technique described in Patent Document 1 contains high strength with a tensile strength of 700 N / mm 2 or more and high ductility of 2% or more by containing Cu and a rare earth element in combination. Can be secured.
また、特許文献２には、Ｃ：3.2〜3.9％、Si：2.0〜2.6％、Mn：0.6％以下を含み、Ｐ、Ｓ、Mgを適正量に調整して含み、さらに、Cu：2.4〜3.3％、Sn：0.01〜0.05％を含有し、残部Feからなる、球状黒鉛鋳鉄が提案されている。特許文献２に記載された技術により製造された球状黒鉛鋳鉄品は、CuとSnを複合含有することにより、引張強さ：900Ｎ/mm2近く、又は900Ｎ/mm2以上の高強度と、伸び：４％以上の高延性を確保できるとしている。 Patent Document 2 includes C: 3.2 to 3.9%, Si: 2.0 to 2.6%, Mn: 0.6% or less, P, S, and Mg are adjusted to appropriate amounts, and Cu: 2.4 to Spheroidal graphite cast iron containing 3.3%, Sn: 0.01 to 0.05%, and remaining Fe has been proposed. Spheroidal graphite cast iron produced by the technique described in Patent Document 2, by composite containing Cu and Sn, tensile strength: 900 N / mm 2 near or with 900 N / mm 2 or more high strength, elongation : High ductility of 4% or more can be secured.
また、特許文献３には、重量％で、Ｃ：3.0〜4.5％、Si：1.6〜2.5％、Mn：0.2〜0.5％と、Ｐ、Ｓ、Mgを適正量に調整して含み、さらに、Zr：0.0005〜0.09％を含み、SnおよびCuの１種または２種を、Sn換算量で0.03〜0.11％含有し、残部がFeおよび不可避的不純物からなる、高強度球状黒鉛鋳鉄が提案されている。特許文献３に記載された技術により製造された球状黒鉛鋳鉄品は、鋳放しのままで、引張強さ：900MPa以上を有し、切削性も良好であるとしている。 Patent Document 3 includes, by weight%, C: 3.0 to 4.5%, Si: 1.6 to 2.5%, Mn: 0.2 to 0.5%, and P, S, and Mg adjusted to appropriate amounts, Zr: High strength spheroidal graphite cast iron containing 0.0005 to 0.09%, one or two of Sn and Cu, 0.03 to 0.11% in terms of Sn, and the balance consisting of Fe and inevitable impurities has been proposed. Yes. The spheroidal graphite cast iron product produced by the technique described in Patent Document 3 is said to have a tensile strength of 900 MPa or more as it is as cast and has good machinability.
また、特許文献４には、重量比で、Ｃ：3.20〜4.00％、Si：2.00〜3.20％、Mn：0.30〜2.50％と、Ｐ、Ｓ、Mgを適正量に調整して含み、さらに、Cu：0.30〜3.50％、希土類元素：0.005〜0.30％を含有し、残部Feからなる溶湯の冷却を促進して、鋳鉄品を鋳造し、黒鉛の周囲にフェライト又はフェライトとパーライトの入り組んだ花弁状の組織を含む金属組織と、鋳放しで引張強さ800Ｎ/mm2以上、好ましくは900〜1000Ｎ/mm2で、伸びが２％以上、好ましくは３％以上を有する球状化黒鉛鋳鉄品とする、球状黒鉛鋳鉄品の製法が提案されている。 Patent Document 4 includes, by weight ratio, C: 3.20 to 4.00%, Si: 2.00 to 3.20%, Mn: 0.30 to 2.50%, and P, S, and Mg adjusted to appropriate amounts. Cu: 0.30 to 3.50%, rare earth element: 0.005 to 0.30%, promotes cooling of the molten metal consisting of the remaining Fe, cast iron products, and petals with ferrite or ferrite and pearlite around graphite And a spheroidal graphite cast iron product having an as-cast tensile strength of 800 N / mm 2 or more, preferably 900 to 1000 N / mm 2 and an elongation of 2% or more, preferably 3% or more. A method for producing a spheroidal graphite cast iron product has been proposed.
また、特許文献５には、重量％で、Ｃ：2.0〜4.0％、Si：1.5〜4.5％、Mn：2.0％以下と、Ｐ、Ｓ、Mgを適正量に調整して含み、さらに、Cu：1.8〜4.0％、あるいはさらにSn：0.08％以下、および／または、Mo：0.5％以下、Ni：0.5％以下の１種または２種を含有し、残部がFeおよび不可避的不純物からなる、高強度球状黒鉛鋳鉄が提案されている。特許文献５に記載された技術により製造された球状黒鉛鋳鉄品は、鋳放しのままで、引張強さ：800MPa以上の高強度を有し、水脆化を著しく抑制でき、さらには被削性が向上するとしている。 Patent Document 5 includes, by weight%, C: 2.0 to 4.0%, Si: 1.5 to 4.5%, Mn: 2.0% or less, and P, S, and Mg adjusted to appropriate amounts, and Cu : 1.8-4.0%, or even Sn: 0.08% or less, and / or Mo: 0.5% or less, Ni: 0.5% or less, one or two of them, the balance consisting of Fe and inevitable impurities, high Strength spheroidal graphite cast iron has been proposed. Spheroidal graphite cast iron products produced by the technique described in Patent Document 5 have a high tensile strength of 800 MPa or more, as-cast, can remarkably suppress water embrittlement, and machinability. Is going to improve.
また、特許文献６には重量比率で、Ｃ：3.0〜4.0％、Si：1.6〜3.3％、Mn：0.2〜1.0％、Ni：0.5〜2.0％、Mo：0.2〜1.5％と、Mgを適正量に調整して含み、さらに、Cu：1.0〜3.0％、Ｖ：0.03〜0.2％を含有し、残部Feおよび不可避的不純物からなり、基地組織がパーライト、あるいはパーライトおよびベイナイトである、高強度ダクタイル鋳鉄が提案されている。特許文献６に記載された技術で製造された高強度球状黒鉛鋳鉄品は、1000MPa超えの引張強さと、２％以上の伸びを有するとしている。 In Patent Document 6, Mg is appropriate in terms of weight ratio: C: 3.0 to 4.0%, Si: 1.6 to 3.3%, Mn: 0.2 to 1.0%, Ni: 0.5 to 2.0%, Mo: 0.2 to 1.5% A high-strength ductile containing Cu: 1.0 to 3.0%, V: 0.03 to 0.2%, the balance being Fe and unavoidable impurities, and the base structure being pearlite or pearlite and bainite. Cast iron has been proposed. A high-strength spheroidal graphite cast iron product manufactured by the technique described in Patent Document 6 is said to have a tensile strength exceeding 1000 MPa and an elongation of 2% or more.
特許文献７には、質量％で、Ni：2.0〜4.0％、Mn：0.4％以下、Cu：0.2％以下を含み、MnとCuの合計量が0.5％以下である球状黒鉛鋳鉄が記載されている。特許文献７に記載された技術では、20〜50mm程度の肉厚を有する黒鉛鋳鉄において、冷却速度を工夫することにより、700MPa以上の高強度と７％以上の伸びを高レベルにバランスよく調整できるとしている。
しかしながら、上記した従来技術では、一定レベル以上の高強度が確保できるものの、耐摩耗性が劣るか、あるいは耐摩耗性については何の配慮もされていないという問題があり、最近の更なる耐摩耗性の向上要求に対しては問題を残していた。さらに、上記した従来技術では、高々50mm程度の肉厚の薄物鋳鉄品を対象としており、肉厚の増加にしたがい、強度が著しく低下するという問題もあった。 However, although the above-described conventional technology can ensure a high strength of a certain level or more, there is a problem that the wear resistance is inferior or no consideration is given to the wear resistance. There was still a problem with the demand for improvement in performance. Furthermore, the above-described prior art targets a thin cast iron product having a thickness of about 50 mm at most, and there is a problem that the strength is remarkably lowered as the thickness is increased.
本発明は、上記した従来技術の問題を解決し、鋳放しままで、引張強さ：750MPa以上の高強度と、伸び：1.5％以上の高延性と、従来材の1.5倍以上の優れた耐摩耗性とを兼備する、肉厚100mm以上の高強度厚肉黒鉛鋳鉄品を提供することを目的とする。 The present invention solves the above-mentioned problems of the prior art, and until cast, tensile strength: high strength of 750 MPa or more, elongation: high ductility of 1.5% or more, and excellent resistance to 1.5 times that of conventional materials. An object of the present invention is to provide a high-strength thick graphite cast iron product having a wall thickness of 100 mm or more that combines wear characteristics.
本発明は、上記した目的を達成するために、まず、鋳放しままの厚肉球状黒鉛鋳鉄品の強度と耐摩耗性に影響する各種要因について鋭意研究した。従来から、球状黒鉛鋳鉄の強度向上には、Cuを含有させることが有効であることが知られている。しかし、耐摩耗性の向上のために、とくに、Cr、Mo、Ｖ、Ｗ等の炭化物形成元素を多量に含有させると、共晶炭化物が晶出し、強度と延性がともに低下し、厚肉鋳鉄品では所望の強度を確保できなくなるという問題がある。 In order to achieve the above-described object, the present invention first made extensive studies on various factors that affect the strength and wear resistance of an as-cast thick-walled spheroidal graphite cast iron product. Conventionally, it is known that inclusion of Cu is effective for improving the strength of spheroidal graphite cast iron. However, in order to improve wear resistance, especially when a large amount of carbide forming elements such as Cr, Mo, V, W, etc. is contained, eutectic carbides crystallize, both strength and ductility decrease, and thick cast iron There is a problem that the desired strength cannot be secured in the product.
そこで、本発明者らは、球状黒鉛鋳鉄組成を基本として、基地の高強度化のためにCuを含有させるとともに、さらに硬質な炭化物を形成するが共晶炭化物を形成しない元素を含有させることにより、基地中に微細な硬質炭化物を分散させることができ、高強度と高延性、さらに優れた耐摩耗性を兼備する厚肉鋳鉄品とすることができることに想到した。またさらに、炭素の拡散を抑制する元素を含有させてパーライト変態を促進させることにより、厚肉鋳鉄品の更なる高強度化が達成できることに思い至った。本発明者らの更なる研究により、上記した硬質な炭化物を形成するが共晶炭化物を形成しない元素としては、Nbが好適であり、さらにNbに加えてＶを含有させることにより、ＶがMC型炭化物（硬質炭化物）中に固溶され炭化物を強化するとともに、残りのＶが基地を強化し、耐摩耗性とともに強度向上に寄与することを知見した。さらに、適正量のNiをさらに含有させることにより、炭素の拡散が抑制され、厚肉鋳鉄品の更なる強度向上に寄与することができることを知見した。またさらに、適正量のSbを併せて含有することにより、100mm以上の厚肉鋳鉄品においてもなお、安定して黒鉛形状を適正な球状に維持でき、安定して所望の高強度、高延性の厚肉鋳鉄品を製造できることを知見した。 Therefore, the present inventors, based on the spheroidal graphite cast iron composition, contain Cu for increasing the strength of the base, and by adding an element that forms hard carbide but does not form eutectic carbide. Thus, it was conceived that fine hard carbides can be dispersed in the base, and a thick cast iron product having high strength, high ductility, and excellent wear resistance can be obtained. Furthermore, it has been thought that further strengthening of thick cast iron products can be achieved by including an element that suppresses the diffusion of carbon to promote pearlite transformation. As a result of further studies by the present inventors, Nb is suitable as an element that forms the above-mentioned hard carbide but does not form a eutectic carbide. Further, by adding V in addition to Nb, V becomes MC. It has been found that while the solid carbide is solid-dissolved in the type carbide (hard carbide) and strengthens the carbide, the remaining V strengthens the base and contributes to improvement in strength as well as wear resistance. Furthermore, it has been found that the addition of an appropriate amount of Ni suppresses the diffusion of carbon and contributes to further improvement in strength of the thick cast iron product. Furthermore, by including the appropriate amount of Sb together, even in a thick cast iron product of 100 mm or more, the graphite shape can be stably maintained in an appropriate spherical shape, and the desired high strength and high ductility can be stably maintained. We found that thick cast iron products can be manufactured.
本発明は、かかる知見に基づき、さらに検討を加えて完成されたものである。すなわち、本発明の要旨は次のとおりである。
（１）質量％で、Ｃ：３〜４％、Si：1.8〜3.0％、Mn：0.5〜２％、Ｓ：0.003〜0.03％、Nb：0.1〜1.5％、Cu：1.2〜3.0％、Ni：0.6〜1.5％、Ｖ：0.1〜1.5％、Sb：0.0001〜0.01％、Mg：0.02〜0.06％ を含有し、残部Feおよび不可避的不純物からなる組成を有し、耐摩耗性に優れることを特徴とする高強度厚肉球状黒鉛鋳鉄品。
（２）（１）において、前記不可避的不純物としてＰを0.04％未満、Crを0.1％未満に調整することを特徴とする高強度厚肉球状黒鉛鋳鉄品。
The present invention has been completed based on such findings and further studies. That is, the gist of the present invention is as follows.
(1) By mass%, C: 3-4%, Si: 1.8-3.0%, Mn: 0.5-2%, S: 0.003-0.03%, Nb: 0.1-1.5%, Cu: 1.2-3.0%, Ni : 0.6 to 1.5%, V: 0.1 to 1.5%, Sb: 0.0001 to 0.01%, Mg: 0.02 to 0.06%, and the composition comprising the balance Fe and inevitable impurities, and having excellent wear resistance A high strength thick spheroidal graphite cast iron product.
(2) A high-strength thick spheroidal graphite cast iron product according to (1), wherein P is adjusted to less than 0.04% and Cr is adjusted to less than 0.1% as the inevitable impurities.
本発明によれば、鋳放しのままで、引張強さがおおよそ750MPa以上の高強度と、高延性、さらに優れた耐摩耗性を有する、肉厚：100mm以上の厚肉の高強度球状黒鉛鋳鉄品を容易に安定して製造でき、産業上格段の効果を奏する。また、本発明になる鋳鉄品は、耐摩耗性に優れ、高強度・高延性を有する鋳鉄品であり、機械部品の金具や爪、床板や、止め具などを配した景観部材、マンホールの蓋や、土木建築用の止め具や、その他、種々の耐摩耗鋳鉄部材への適用も可能となるという効果もある。 According to the present invention, the as-cast high strength spheroidal graphite cast iron having a high strength of about 750 MPa or more, high ductility, and excellent wear resistance, and a thickness of 100 mm or more. The product can be manufactured easily and stably, and there is a remarkable industrial effect. Further, the cast iron product according to the present invention is a cast iron product having excellent wear resistance and high strength and high ductility. In addition, there is also an effect that it can be applied to a stopper for civil engineering and other various wear-resistant cast iron members.
まず、本発明の球状黒鉛鋳鉄品の組成限定理由について説明する。なお、以下、組成における質量％は単に％で記す。
Ｃ：３〜４％
Ｃは、球状黒鉛の晶出量、パーライト中の層状セメンタイト量およびＭＣ炭化物の析出量、ならびに溶湯の流動性に影響する重要な元素である。Ｃ含有量が３％未満では特に流動性が不足し、引け巣が発生しやすく、また黒鉛量が不足し、所望の高強度、高延性を確保する球状黒鉛鋳鉄とすることが難しくなる。一方、４％を超える含有は、黒鉛量が過多となり、強度が低下する。このため、Ｃは３〜４％に限定した。なお、好ましくは、3.3〜3.9％である。
First, the reasons for limiting the composition of the spheroidal graphite cast iron product of the present invention will be described. Hereinafter, the mass% in the composition is simply expressed as%.
C: 3-4%
C is an important element that affects the amount of spheroidal graphite crystallization, the amount of layered cementite in pearlite and the amount of MC carbide precipitated, and the fluidity of the molten metal. If the C content is less than 3%, fluidity is particularly insufficient, shrinkage cavities are likely to occur, and the graphite content is insufficient, making it difficult to obtain a spheroidal graphite cast iron that ensures the desired high strength and high ductility. On the other hand, if the content exceeds 4%, the amount of graphite becomes excessive and the strength decreases. For this reason, C was limited to 3-4%. In addition, Preferably, it is 3.3 to 3.9%.
Si：1.8〜3.0％
Siは、溶湯の流動性と白銑化に影響を及ぼす元素であり、本発明では1.8％以上の含有を必要とする。Siが1.8％未満では、流動性が低下して薄肉部への溶湯の充填が困難になるとともに、白銑化も発生する。一方、3.0％を超える含有は、黒鉛形状が乱れ、形状の崩れた黒鉛となりやすく、高強度化が困難になる。このため、Siは1.8〜3.0％の範囲に限定した。なお、好ましくは、2.0〜2.6％である。
Si: 1.8-3.0%
Si is an element that affects the fluidity and whitening of the molten metal, and in the present invention, it needs to be contained in an amount of 1.8% or more. If Si is less than 1.8%, the fluidity is lowered, making it difficult to fill the thin portion with molten metal, and whitening also occurs. On the other hand, if the content exceeds 3.0%, the graphite shape is disturbed, and the graphite tends to be deformed, making it difficult to increase the strength. For this reason, Si was limited to the range of 1.8 to 3.0%. In addition, Preferably, it is 2.0 to 2.6%.
Mn：0.5〜２％
Mnは、基地中に固溶し、基地の高強度化に寄与する有用な元素である。このような効果を得るためには、0.5％以上の含有を必要とする。Mnが0.5％未満では強度が低下し、所望の高強度を確保できなくなる。一方、２％を超えるMnの含有は、凝固セルの粒界にMnが偏析して材質を脆化させる。このため、Mnは0.5〜２％の範囲に限定した。なお、好ましくは、0.5〜1.4％である。
Mn: 0.5-2%
Mn is a useful element that dissolves in the base and contributes to increasing the strength of the base. In order to acquire such an effect, 0.5% or more of content is required. If Mn is less than 0.5%, the strength decreases, and the desired high strength cannot be secured. On the other hand, if Mn content exceeds 2%, Mn segregates at the grain boundary of the solidification cell, and the material becomes brittle. For this reason, Mn was limited to the range of 0.5 to 2%. In addition, Preferably, it is 0.5 to 1.4%.
Ｓ：0.003〜0.03％
Ｓは、Mg、Si等と化合物を形成して黒鉛の核を形成し、黒鉛化を促進する作用を有する元素である。このような効果を得るために、本発明では0.003％以上含有する。一方、0.03％を超える含有は、黒鉛形状を低下させる。このため、Ｓは0.003〜0.03％の範囲に限定した。なお、好ましくは0.003〜0.015％である。
S: 0.003-0.03%
S is an element having an action of forming a compound with Mg, Si, etc. to form graphite nuclei and promoting graphitization. In order to acquire such an effect, it contains 0.003% or more in this invention. On the other hand, a content exceeding 0.03% lowers the graphite shape. For this reason, S was limited to the range of 0.003 to 0.03%. In addition, Preferably it is 0.003 to 0.015%.
Nb：0.1〜1.5％
Nbは、硬質なＭＣ型炭化物を形成し、耐摩耗性向上に有効に寄与するとともに、凝固組織をも微細化し、高強度化に有効に寄与する本発明では極めて重要な元素である。このような効果は、0.1％以上の含有で認められるが、1.5％を超える含有は、ＭＣ型炭化物が粗大化し、強度の低下を招く。このため、Nbは0.1〜1.5％の範囲に限定した。なお、好ましくは、0.1〜1.2％である。
Nb: 0.1-1.5%
Nb is a very important element in the present invention, which forms a hard MC type carbide and contributes effectively to improving the wear resistance, and also makes the solidified structure finer and contributes effectively to increasing the strength. Such an effect is recognized when the content is 0.1% or more, but when the content exceeds 1.5%, the MC type carbide is coarsened and the strength is reduced. For this reason, Nb was limited to the range of 0.1 to 1.5%. In addition, Preferably, it is 0.1 to 1.2%.
Cu：1.2〜3.0％
Cuは、鋳放しままで、パーライト組織を緻密化するととともに、基地を高強度化する作用を有する、本発明では重要な元素である。このような効果を得るためには、1.2％以上の含有を必要とする。一方、3.0％を超える含有は、Cuが凝固セルの粒界に多量に偏析して強度の低下を招く。このため、Cuは1.2〜3.0％の範囲に限定した。なお、好ましくは1.2〜2.7％である。
Cu: 1.2-3.0%
Cu is an important element in the present invention, which has the effect of densifying the pearlite structure and increasing the strength of the matrix until it is cast. In order to obtain such an effect, a content of 1.2% or more is required. On the other hand, if the content exceeds 3.0%, a large amount of Cu is segregated at the grain boundaries of the solidification cell, leading to a decrease in strength. For this reason, Cu was limited to the range of 1.2 to 3.0%. In addition, Preferably it is 1.2 to 2.7%.
Ni：0.6〜1.5％
Niは、基地中に固溶して、炭素の拡散を抑制し、とくに凝固後の冷却速度が小さい厚肉鋳鉄品の基地相において、パーライト変態を促進し、強度を増加させ、厚肉鋳鉄品の高強度化に大きく寄与する元素であり、本発明では重要な元素である。このような効果は、0.6％以上の含有で顕著となる。一方、1.5％を超える含有は、オーステナイトを安定化させ、基地組織を一部、ベイナイト化、あるいはマルテンサイト化させて、強度のばらつきを大きくする悪影響を及ぼす。このため、Niは0.6〜1.5％の範囲に限定した。なお、Ni含有量は、鋳物形状、肉厚、使用する鋳型、鋳造条件等に応じて適正値があり、また要求される特性も種々変化するため、目的に応じて上記した範囲で調整することが好ましい。
Ni: 0.6-1.5%
Ni dissolves in the base and suppresses the diffusion of carbon. Especially in the base phase of thick cast iron products with a low cooling rate after solidification, it promotes pearlite transformation, increases strength, and thick cast iron products. It is an element that greatly contributes to increasing the strength of the steel and is an important element in the present invention. Such an effect becomes remarkable when the content is 0.6% or more. On the other hand, if the content exceeds 1.5%, austenite is stabilized, and part of the base structure is made bainite or martensite, which has an adverse effect of increasing strength variation. For this reason, Ni was limited to the range of 0.6 to 1.5%. The Ni content has an appropriate value depending on the casting shape, wall thickness, mold used, casting conditions, etc., and the required characteristics also vary. Therefore, adjust the Ni content within the above range according to the purpose. Is preferred.
Ｖ：0.1〜1.5％
Ｖは、Nbの含有により出現したＭＣ型炭化物に固溶してＭＣ型炭化物を強化する作用を有し、強度増加と耐摩耗性向上に寄与する、本発明では重要な元素である。なお、ＭＣ型炭化物に固溶しきれないＶの残部は、基地に固溶してパーライト組織を緻密化し、強化する作用をも有する。このような効果を得るためには、0.1％以上の含有を必要とする。一方、1.5％を超える含有は、炭化物量を増加させ過ぎて、延性が低下する。このため、Ｖは0.1〜1.5％の範囲に限定した。なお、好ましくは0.1〜1.0％である。
V: 0.1-1.5%
V is an important element in the present invention that has the effect of strengthening the MC type carbide by dissolving in the MC type carbide that appears due to the inclusion of Nb, and contributes to an increase in strength and an improvement in wear resistance. The remainder of V that cannot be completely dissolved in the MC type carbide also has a function of forming a solid solution in the matrix to densify and strengthen the pearlite structure. In order to obtain such an effect, the content of 0.1% or more is required. On the other hand, if it exceeds 1.5%, the amount of carbide is excessively increased and ductility is lowered. For this reason, V was limited to the range of 0.1 to 1.5%. In addition, Preferably it is 0.1 to 1.0%.
Sb：0.0001〜0.01％
Sbは、厚肉鋳物にときどき発生し強度劣化を引き起こすチャンキー黒鉛と称される、黒鉛形状が珊瑚状に崩れた状態の黒鉛の晶出を防止する作用を有し、本発明におけるような厚肉の球状黒鉛鋳鉄品においては、とくに有用な元素である。このような効果を得るためには、0.0001％以上の含有を必要とするが、0.01％を超える過剰な含有はかえって黒鉛形状の崩れを助長する。このため、Sbは0.0001〜0.01％の範囲に限定した。なお、好ましくは0.0001〜0.006％である。
Sb: 0.0001 to 0.01%
Sb, which is called chunky graphite, which sometimes occurs in thick-walled castings and causes strength deterioration, has the action of preventing the crystallization of graphite in a state in which the graphite shape has collapsed into a bowl shape, and has a thickness as in the present invention. It is a particularly useful element in meat spheroidal graphite cast iron products. In order to obtain such an effect, a content of 0.0001% or more is required, but an excessive content exceeding 0.01% promotes the collapse of the graphite shape. For this reason, Sb was limited to 0.0001 to 0.01% of range. In addition, Preferably it is 0.0001 to 0.006%.
Mg：0.02〜0.06％
Mgは、黒鉛を球状化する作用を有し、球状黒鉛鋳鉄では必須の元素である。このような効果を確保するためには、0.02％以上の含有を必要とする。一方、0.06％を超える含有は、Mgの酸化物が多量のドロスを発生させ、表面欠陥を増加させる。このため、Mgは0.02〜0.06％の範囲に限定した。
Mg: 0.02-0.06%
Mg has a function of spheroidizing graphite and is an essential element in spheroidal graphite cast iron. In order to ensure such an effect, the content of 0.02% or more is required. On the other hand, if the content exceeds 0.06%, Mg oxide generates a large amount of dross and increases surface defects. For this reason, Mg was limited to the range of 0.02 to 0.06%.
上記した成分以外の残部は、Feおよび不可避的不純物である。なお、不可避的不純物としてＰを0.04％未満、Crを0.1％未満に調整することが好ましい。
Ｐは、ザク巣を増加させたり、凝固セルの粒界に偏析して材質を脆化させる作用を有する元素であり、本発明では不純物としてできるだけ低減することが望ましい。0.04％以上では上記した悪影響が顕著となる。このため、Ｐは0.04％未満に調整することが好ましい。なお、より好ましくは0.03％以下である。
The balance other than the above components is Fe and inevitable impurities. It is preferable to adjust P to less than 0.04% and Cr to less than 0.1% as inevitable impurities.
P is an element that has an effect of increasing the number of nests or segregating at the grain boundaries of the solidification cell to embrittle the material. In the present invention, P is preferably reduced as much as possible. Above 0.04%, the above-mentioned adverse effects become significant. For this reason, it is preferable to adjust P to less than 0.04%. More preferably, it is 0.03% or less.
Crは、白銑化を促進させる元素であり、白銑化抑制のために、低減することが好ましい。Cr：0.1％未満であれば悪影響は小さく許容できる。このため、Cr：0.1％未満に調整することが好ましい。Crを上記した範囲内とするためには、これら元素を多量に含有することのない溶解原料を使用することが肝要であるが、通常の一般的な溶解原料であれば、とくに溶解原料の厳選を必要としない。 Cr is an element that promotes whitening and is preferably reduced in order to suppress whitening. If Cr is less than 0.1%, the adverse effect is small and acceptable. For this reason, it is preferable to adjust to Cr: less than 0.1%. In order to keep Cr within the above-mentioned range, it is important to use a melting raw material that does not contain a large amount of these elements. Do not need.
Ｐ、Cr以外の不可避的不純物として、Ti：0.03％未満、Ｗ：0.1％未満が許容できる。
Ti、Ｗは、いずれも白銑化を促進させ、黒鉛形状を劣化させる元素であり、白銑化抑制あるいは黒鉛形状の劣化抑制のために、これら元素の含有量は低い方が好ましい。Ti：0.03％未満、Ｗ：0.1％未満であれば悪影響は小さく、許容できる。このため、Ti：0.03％未満、Ｗ：0.1％未満に調整することが好ましい。Ti、Ｗを上記した範囲内とするためには、これら元素を多量に含有することのない溶解原料を使用することが肝要であるが、通常の一般的な溶解原料であれば、とくに溶解原料の厳選を必要としない。なお、より好ましくは、Ti：0.02％未満、Ｗ：0.04％未満である。
As inevitable impurities other than P and Cr, Ti: less than 0.03% and W: less than 0.1% are acceptable.
Ti and W are elements that promote whitening and deteriorate the graphite shape, and the content of these elements is preferably low in order to suppress whitening or to suppress deterioration of the graphite shape. If Ti: less than 0.03% and W: less than 0.1%, the adverse effect is small and acceptable. For this reason, it is preferable to adjust to Ti: less than 0.03% and W: less than 0.1%. In order to make Ti and W within the above ranges, it is important to use a melting raw material that does not contain a large amount of these elements. Does not require careful selection. More preferably, Ti is less than 0.02% and W is less than 0.04%.
また、不可避的不純物である、Al、Ca、Ba、Biは、Al ：0.05％未満、Ca：0.008％未満、Ba：0.002％未満、Bi：0.02％未満が許容できる。
Al、Caは、通常、黒鉛球状化剤として使用されるFe−Si−Mg合金に含有され、またCa、Al、Ba、Biは、通常、接種剤として使用されるFe−Si合金やCa−Si合金中に含有される。このため、Al、Ca、Ba、Biは、球状黒鉛鋳鉄には不可避的に含まれる不純物となる。しかし、Al を0.05％以上含有すると、黒鉛球状化に悪影響を及ぼし強度低下の原因となる。このため、Al ：0.05％未満に調整することが好ましい。また、Caを0.008％以上、Baを0.002％以上含有すると、ドロスが増加し、表面欠陥の発生が増加する。このため、Ca：0.008％未満、Ba：0.002％未満に調整することが好ましい。また、Bi：0.02％以上含有すると、黒鉛球状化に悪影響を及ぼしたり、炭化物を晶出する場合がある。このため、Biは0.02％未満に調整することが好ましい。
Further, Al, Ca, Ba, and Bi, which are inevitable impurities, can be allowed to be Al: less than 0.05%, Ca: less than 0.008%, Ba: less than 0.002%, and Bi: less than 0.02%.
Al and Ca are usually contained in an Fe-Si-Mg alloy used as a graphite spheroidizing agent, and Ca, Al, Ba and Bi are usually Fe-Si alloys and Ca- Contained in Si alloy. For this reason, Al, Ca, Ba, and Bi are impurities inevitably contained in the spheroidal graphite cast iron. However, if Al is contained in an amount of 0.05% or more, it adversely affects the spheroidization of graphite and causes a decrease in strength. For this reason, it is preferable to adjust to Al: less than 0.05%. Further, when Ca is contained in an amount of 0.008% or more and Ba is contained in an amount of 0.002% or more, dross increases and the occurrence of surface defects increases. For this reason, it is preferable to adjust to Ca: less than 0.008% and Ba: less than 0.002%. Further, when Bi is contained in an amount of 0.02% or more, it may adversely affect the spheroidization of graphite and may cause crystallization of carbides. For this reason, Bi is preferably adjusted to less than 0.02%.
上記した不純物以外の不可避的不純物として、Ｎがあるが、通常の溶湯溶製法であれば、Ｎ含有量は0.002〜0.01％程度となる。この程度の含有範囲であればとくに悪影響はない。
本発明の球状黒鉛鋳鉄品は、上記した組成を有し、鋳放しのままで、球状化した黒鉛を有し、鋳放しのままで引張強さ：750MPa以上の高強度と、1.5％以上の高延性と、従来材の1.5 倍以上の優れた耐摩耗性と、を有する。
There is N as an inevitable impurity other than the above-described impurities, but in the case of a normal molten metal melting method, the N content is about 0.002 to 0.01%. If the content is within this range, there is no particular adverse effect.
The spheroidal graphite cast iron product of the present invention has the above-described composition, as-cast, with spheroidized graphite, and as-cast, high tensile strength: 750 MPa or more, and 1.5% or more It has high ductility and excellent wear resistance that is more than 1.5 times that of conventional materials.
つぎに、本発明の高強度厚肉球状黒鉛鋳鉄品の好ましい製造方法について説明する。
高周波炉等の常用の鋳鉄溶製方法で母溶湯を溶製し、該母溶湯に、常用のMg合金等の黒鉛球状化剤を添加する黒鉛球状化処理を行ったのち、さらに、通常のFe−Si合金、Ca−Si合金等の接種剤で接種して上記した組成とし、所望の形状に形成された、砂型、金型等の常用の鋳型に注湯（鋳込み）することが好ましい。なお、本発明においては、接種は、常用の方法である、取鍋に移送時に行う方法、あるいは湯道等の鋳型内（インモールド接種）で行う方法のいずれで行ってもよいことは言うまでもない。
Next, a preferred method for producing the high strength thick spheroidal graphite cast iron product of the present invention will be described.
After melting the mother molten metal by a conventional cast iron melting method such as a high-frequency furnace, and performing a graphite spheroidizing treatment by adding a graphite spheroidizing agent such as a conventional Mg alloy to the mother molten metal, a normal Fe It is preferable to inoculate with an inoculant such as a -Si alloy or Ca-Si alloy to have the above-described composition, and to pour (cast) it into a conventional mold such as a sand mold or a mold formed in a desired shape. In the present invention, it goes without saying that the inoculation may be carried out by any of the usual methods, such as a method of transferring to a ladle or a method of performing in a mold such as a runner (in-mold inoculation). .
以下、さらに実施例に基づいて本発明についてさらに説明する。 The present invention will be further described below based on examples.
高周波炉を用いて溶製した母溶湯に、表１に示す合金組成となるように合金元素を添加した。なお、合金元素添加後の溶湯の最高温度は、1490〜1580℃とした。合金元素添加後の溶湯に、ついで、市販のMg合金（Fe−45質量％Si−５質量％Mg−１質量％Ca合金）を用いてサンドイッチ法で黒鉛球状化処理を行った。ついで、溶湯を取鍋に移し替え、その際に、Fe−75％Si合金で接種した。接種直後、化学分析用試料を採取し、直ちに、溶湯を砂型に注湯（鋳込み）し、Ｙ型キールブロック（平行部肉厚110mm）とした。なお、鋳込み温度は、1360℃〜1480℃とした。 An alloying element was added to the molten mother metal melted using a high-frequency furnace so that the alloy composition shown in Table 1 was obtained. The maximum temperature of the molten metal after addition of the alloy elements was 1490 to 1580 ° C. The molten metal after addition of the alloy elements was then subjected to a graphite spheroidization process by a sandwich method using a commercially available Mg alloy (Fe-45 mass% Si-5 mass% Mg-1 mass% Ca alloy). Next, the molten metal was transferred to a pan and inoculated with an Fe-75% Si alloy. Immediately after inoculation, a sample for chemical analysis was collected, and immediately the molten metal was poured (cast) into a sand mold to form a Y-type keel block (parallel portion thickness 110 mm). The casting temperature was 1360 ° C to 1480 ° C.
鋳込み後、18時間以上放置したのち、型バラシを行い、Ｙ型キールブロックから、鋳放し状態で、試験片を採取し、引張試験および摩耗試験を実施した。試験方法は次のとおりとした。
（１）引張試験
Ｙ型キールブロックから、JIS 14A号引張試験片（平行部径：10mmφ×GL50mm）を採取し、JIS Z 2241の規定に準拠して、室温（25℃）で引張試験を実施し、引張強さTS、および伸びElを測定した。
After casting, the mold was brushed after standing for 18 hours or more, and test pieces were collected from the Y-type keel block in an as-cast state, and a tensile test and a wear test were performed. The test method was as follows.
(1) Tensile test A JIS 14A tensile test piece (parallel part diameter: 10mmφ x GL50mm) was collected from a Y-type keel block and subjected to a tensile test at room temperature (25 ° C) in accordance with the provisions of JIS Z 2241. The tensile strength TS and the elongation El were measured.
（２）摩耗試験
Ｙ型キールブロックから、摩耗試験片（円盤状試験片：外径φ60mm×肉厚10mm）を採取した。摩耗試験は、２円盤の転がりすべり方式とした。相手材は、S45C材製の円盤状試験片（外径φ190mm×肉厚15mm）とした。摩耗試験は、試験片回転数：700rpm、すべり率：5％、荷重：100kgf（980Ｎ）、試験時間：60minとした。摩耗試験の前後に試験片の重量測定を行い、試験片の摩耗減量（摩耗量）を測定した。各鋳鉄品の耐摩耗性は、従来例（鋳鉄品No.9）の摩耗量に対する比、摩耗比＝（従来例の摩耗量）／（各鋳鉄品（試験片）の摩耗量）で評価した。この摩耗比が大きいほど、耐摩耗性が優れることを意味する。
(2) Wear test A wear test piece (disk-shaped test piece: outer diameter φ60 mm × thickness 10 mm) was collected from the Y-type keel block. The abrasion test was a two-spin rolling method. The mating material was a disk-shaped test piece made of S45C material (outer diameter φ190 mm × thickness 15 mm). In the abrasion test, the number of revolutions of the test piece was 700 rpm, the sliding rate was 5%, the load was 100 kgf (980 N), and the test time was 60 min. The weight of the test piece was measured before and after the wear test, and the wear loss (wear amount) of the test piece was measured. The wear resistance of each cast iron product was evaluated by the ratio to the wear amount of the conventional example (cast iron product No. 9), wear ratio = (wear amount of the conventional example) / (wear amount of each cast iron product (test piece)). . Higher wear ratio means better wear resistance.
得られた結果を表２に示す。 The obtained results are shown in Table 2.
本発明例はいずれも、引張強さTS：750MPa以上の高強度と、伸びEl：1.5％以上の高延性を兼備し、さらに従来例（鋳鉄品No.9）の1.5倍以上の高耐摩耗性を有し、優れた特性を有する厚肉球状黒鉛鋳鉄品となっている。一方、本発明の範囲を外れる比較例は、引張強さが750MPa未満であるか、伸びが1.5％未満であるか、あるいは従来の1.1倍程度の耐摩耗性しか有していないか、である。Nb無添加で、Cu含有量が本発明範囲を低く外れ、Crを含有する比較例（鋳鉄品No.10）は、強度、延性、耐摩耗性のいずれも所望の特性を確保できていない。また、Niが本発明範囲を低く外れる比較例（鋳鉄品No.11）は、強度、耐摩耗性が所望の特性を確保できていない。また、Niが本発明範囲を低く外れ、Ｖが本発明範囲を高く外れる比較例（鋳鉄品No.12）は、強度、延性が所望の特性を確保できていない。 All examples of the present invention have high tensile strength of TS: 750 MPa or more and high ductility of elongation El: 1.5% or more, and more than 1.5 times higher wear resistance than the conventional example (cast iron product No. 9). It is a thick-walled spheroidal graphite cast iron product having excellent properties. On the other hand, a comparative example out of the scope of the present invention is whether the tensile strength is less than 750 MPa, the elongation is less than 1.5%, or the wear resistance is about 1.1 times that of the conventional one. . The comparative example (cast iron product No. 10) containing Cr does not have Nb-free addition and the Cu content is out of the range of the present invention, and none of the desired properties of strength, ductility, and wear resistance can be secured. In addition, the comparative example (cast iron product No. 11) in which Ni deviates from the scope of the present invention does not ensure the desired properties of strength and wear resistance. In addition, the comparative example (cast iron product No. 12) in which Ni deviates from the scope of the present invention and Ni deviates from the scope of the present invention does not ensure desired properties in strength and ductility.
Claims (2)
Ｃ：３〜４％、 Si：1.8〜3.0％、
Mn：0.5〜２％、 Ｓ：0.003〜0.03％、
Nb：0.1〜1.5％、 Cu：1.2〜3.0％、
Ni：0.6〜1.5％、 Ｖ：0.1〜1.5％、
Sb：0.0001〜0.01％、 Mg：0.02〜0.06％
を含有し、残部Feおよび不可避的不純物からなる組成を有し、耐摩耗性に優れることを特徴とする高強度厚肉球状黒鉛鋳鉄品。 % By mass
C: 3 to 4%, Si: 1.8 to 3.0%,
Mn: 0.5-2%, S: 0.003-0.03%,
Nb: 0.1-1.5%, Cu: 1.2-3.0%,
Ni: 0.6-1.5%, V: 0.1-1.5%,
Sb: 0.0001-0.01%, Mg: 0.02-0.06%
A high-strength thick-walled spheroidal graphite cast iron product having a composition comprising the balance Fe and inevitable impurities and having excellent wear resistance.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2008310689A JP5282547B2 (en) | 2008-12-05 | 2008-12-05 | High-strength, thick-walled spheroidal graphite cast iron with excellent wear resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2008310689A JP5282547B2 (en) | 2008-12-05 | 2008-12-05 | High-strength, thick-walled spheroidal graphite cast iron with excellent wear resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2010132979A JP2010132979A (en) | 2010-06-17 |
| JP5282547B2 true JP5282547B2 (en) | 2013-09-04 |
Family
ID=42344530
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2008310689A Active JP5282547B2 (en) | 2008-12-05 | 2008-12-05 | High-strength, thick-walled spheroidal graphite cast iron with excellent wear resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP5282547B2 (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5712531B2 (en) * | 2010-09-02 | 2015-05-07 | Ｊｆｅスチール株式会社 | Spheroidal graphite cast iron products with excellent wear resistance |
| CN105238991B (en) * | 2015-10-22 | 2017-06-06 | 贵州安吉航空精密铸造有限责任公司 | The spheroidal graphite cast-iron and its Technology for Heating Processing of a kind of high-elongation |
| CN108251742B (en) * | 2018-02-10 | 2023-05-09 | 富士和机械工业（湖北）有限公司 | High-strength spheroidal graphite brake disc and casting die thereof |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001220640A (en) * | 2000-02-07 | 2001-08-14 | Hitachi Metals Ltd | Spheroidal graphite cast iron, producing method therefor and crank shaft composed of the same spheroidal graphite cast iron |
| JP3735658B2 (en) * | 2002-09-05 | 2006-01-18 | 加藤 雄大 | High strength ductile cast iron |
| JP2007197747A (en) * | 2006-01-25 | 2007-08-09 | Aisin Takaoka Ltd | Cast iron containing spheroidal graphite |
| JP5041938B2 (en) * | 2007-09-14 | 2012-10-03 | 株式会社クボタ | Composite roll for rolling |
-
2008
- 2008-12-05 JP JP2008310689A patent/JP5282547B2/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| JP2010132979A (en) | 2010-06-17 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP5012231B2 (en) | High-strength spheroidal graphite cast iron with excellent wear resistance | |
| JP4835424B2 (en) | High strength spheroidal graphite cast iron | |
| JP4787640B2 (en) | Composite roll for rolling | |
| JP6032881B2 (en) | Hot mold steel | |
| JP2005206913A (en) | Alloy tool steel | |
| JP5712560B2 (en) | Spheroidal graphite cast iron products with excellent wear resistance | |
| CN101078090A (en) | Low-alloy high speed steel roll material and preparation method thereof | |
| JP5113104B2 (en) | Spheroidal graphite cast iron pipe and manufacturing method thereof | |
| JP2016079498A (en) | Gray cast iron for cylinder liner and method for manufacturing cylinder liner using the same | |
| JP2022550358A (en) | Alloy structural steel and its manufacturing method | |
| JP5282546B2 (en) | High-strength, thick-walled spheroidal graphite cast iron with excellent wear resistance | |
| JP5712525B2 (en) | Spheroidal graphite cast iron products with excellent wear resistance | |
| JP5589646B2 (en) | Spheroidal graphite cast iron products with excellent wear resistance | |
| JP2007154295A (en) | Wear resistant cast steel and its production method | |
| JP5282547B2 (en) | High-strength, thick-walled spheroidal graphite cast iron with excellent wear resistance | |
| TW390910B (en) | High strength spheroidal graphite cast iron | |
| JP2004143579A (en) | Machine structural steel excellent in scrap treatability and method for producing the same | |
| JP3735658B2 (en) | High strength ductile cast iron | |
| JP5041938B2 (en) | Composite roll for rolling | |
| JP5712531B2 (en) | Spheroidal graphite cast iron products with excellent wear resistance | |
| JP4381210B2 (en) | High wear-resistant roll material and high wear-resistant composite roll | |
| KR101599520B1 (en) | A grey cast iron | |
| JP4565301B2 (en) | High-strength spheroidal graphite cast iron and method for producing the same | |
| JP2010031301A (en) | Nickel-chromium-aluminum alloy base material | |
| JP5952455B1 (en) | High rigidity spheroidal graphite cast iron |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20110824 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20130424 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20130430 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20130513 |
|
| R150 | Certificate of patent or registration of utility model |
Ref document number: 5282547 Country of ref document: JP Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |