JP4963444B2 - Spheroidal graphite cast iron member - Google Patents
Spheroidal graphite cast iron member Download PDFInfo
- Publication number
- JP4963444B2 JP4963444B2 JP2007163865A JP2007163865A JP4963444B2 JP 4963444 B2 JP4963444 B2 JP 4963444B2 JP 2007163865 A JP2007163865 A JP 2007163865A JP 2007163865 A JP2007163865 A JP 2007163865A JP 4963444 B2 JP4963444 B2 JP 4963444B2
- Authority
- JP
- Japan
- Prior art keywords
- cast iron
- mass
- spheroidal graphite
- graphite cast
- iron member
- 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 64
- 229910001562 pearlite Inorganic materials 0.000 claims description 27
- 229910000859 α-Fe Inorganic materials 0.000 claims description 26
- 238000005266 casting Methods 0.000 claims description 11
- 239000012535 impurity Substances 0.000 claims description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 7
- 238000000034 method Methods 0.000 description 14
- 239000002184 metal Substances 0.000 description 12
- 229910052751 metal Inorganic materials 0.000 description 12
- 230000007423 decrease Effects 0.000 description 10
- 229910052802 copper Inorganic materials 0.000 description 9
- 229910052748 manganese Inorganic materials 0.000 description 8
- 238000005070 sampling Methods 0.000 description 7
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 6
- 230000015572 biosynthetic process Effects 0.000 description 6
- 229910002804 graphite Inorganic materials 0.000 description 6
- 239000010439 graphite Substances 0.000 description 6
- 229910052759 nickel Inorganic materials 0.000 description 6
- 238000005259 measurement Methods 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 3
- 229910001018 Cast iron Inorganic materials 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000009863 impact test Methods 0.000 description 2
- 150000001247 metal acetylides Chemical class 0.000 description 2
- 238000002156 mixing Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 230000000704 physical effect Effects 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- 229910000805 Pig iron Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 238000005422 blasting Methods 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000007730 finishing process Methods 0.000 description 1
- 239000002054 inoculum Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000003110 molding sand Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000004576 sand Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 239000000725 suspension Substances 0.000 description 1
- 230000000007 visual effect Effects 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
Description
本発明は、球状黒鉛鋳鉄部材に関し、更に詳しくは、引張強さ、耐力、伸び、耐衝撃性等の機械的性質に優れ、更に自動車の足回り部品等に好適な所定の硬さの球状黒鉛鋳鉄部材に関する。 The present invention relates to a spheroidal graphite cast iron member. More specifically, the spheroidal graphite having a predetermined hardness which is excellent in mechanical properties such as tensile strength, proof stress, elongation and impact resistance, and is suitable for undercar parts of automobiles. The present invention relates to a cast iron member.
従来、自動車部品等の分野において球状黒鉛鋳鉄部材が使用されており、部品毎に種々の特性が要求されている。要求特性は、部品の種類等によって異なるが、例えば、自動車のシャーシ、足回り部品等においては、引張強さ、耐力、伸び、耐衝撃性及び硬さ等の各物性をバランス良く備える必要があり、これらの物性を最適化することは必ずしも容易ではなかった。従来の球状黒鉛鋳鉄部材では、例えば、引張強さと伸びのバランスを重視すると耐衝撃性が十分ではなくなったり（例えば、特許文献１参照）、引張強さ、伸び及び耐衝撃性を重視した構造とすると表面付近の硬さが不十分となる（例えば、特許文献２参照）という問題があった。
本発明は、上述した問題に鑑みてなされたものであり、引張強さ、耐力、伸び、耐衝撃性等の機械的性質に優れ、更に自動車の足回り部品等に好適な所定の硬さの球状黒鉛鋳鉄部材を提供することを目的とする。 The present invention has been made in view of the above-described problems, and is excellent in mechanical properties such as tensile strength, yield strength, elongation, and impact resistance, and has a predetermined hardness suitable for automobile undercarriage parts and the like. It aims at providing a spheroidal graphite cast iron member.
上述の目的を達成するため、本発明は、以下の球状黒鉛鋳鉄部材を提供するものである。 In order to achieve the above object, the present invention provides the following spheroidal graphite cast iron members.
［１］ Ｃを３．４〜４．０質量％、Ｓｉを１．５質量％以上２．０質量％未満、Ｍｎを０．３５〜０．５質量％、Ｎｉを１．０質量％を超え２．０質量％未満、及びＣｕを０．２〜０．５質量％含有し、残部がＦｅ及び不可避的に含有される不純物であり、パーライト組織の面積率が６０〜９０％、フェライト組織の面積率が１０〜４０％である球状黒鉛鋳鉄部材。 [1] 3.4 to 4.0% by mass of C, 1.5% to less than 2.0% by mass of Si, 0.35 to 0.5% by mass of Mn, and 1.0% by mass of Ni More than 2.0% by mass and 0.2 to 0.5% by mass of Cu, the balance being Fe and impurities inevitably contained, the area ratio of pearlite structure is 60 to 90%, ferrite structure Spheroidal graphite cast iron member having an area ratio of 10 to 40%.
［２］ 鋳造後、鋳放しで得られた［１］に記載の球状黒鉛鋳鉄部材。 [2] The spheroidal graphite cast iron member according to [1] obtained by as-casting after casting.
［３］ 常温（２０℃）での衝撃値が７．０Ｊ／ｃｍ２以上であり、低温（−４０℃）での衝撃値が３．０Ｊ／ｃｍ２以上であり、引張強さが７７０ＭＰａ以上であり、伸びが８．０％以上であり、耐力が４５０ＭＰａ以上であり、ブリネル硬さ（ＨＢ）が１９０〜２６０である［１］又は［２］に記載の球状黒鉛鋳鉄部材。 [3] Impact value at normal temperature (20 ° C.) is 7.0 J / cm 2 or more, impact value at low temperature (−40 ° C.) is 3.0 J / cm 2 or more, and tensile strength is 770 MPa or more. The spheroidal graphite cast iron member according to [1] or [2], having an elongation of 8.0% or more, a proof stress of 450 MPa or more, and a Brinell hardness (HB) of 190 to 260.
本発明の球状黒鉛鋳鉄部材によれば、Ｎｉを１．０質量％を超え２．０質量％未満とし、Ｃｕを０．２〜０．５質量％、Ｍｎを０．３５〜０．５質量％とすることにより、得られる球状黒鉛鋳鉄部材の表面から内部まで全体が、パーライト組織の面積率６０〜９０％、且つフェライト組織の面積率１０〜４０％という構造となる。そして、本発明の球状黒鉛鋳鉄部材は、このような構造であるため、引張強さ、耐力、伸び、耐衝撃性等の機械的性質に優れ、更に自動車の足回り部品等に好適な所定の硬さの球状黒鉛鋳鉄部材である。 According to the spheroidal graphite cast iron member of the present invention, Ni is more than 1.0% by mass and less than 2.0% by mass, Cu is 0.2 to 0.5% by mass, and Mn is 0.35 to 0.5% by mass. %, The entire structure from the surface to the inside of the obtained spheroidal graphite cast iron member has a pearlite structure area ratio of 60 to 90% and a ferrite structure area ratio of 10 to 40%. And since the spheroidal graphite cast iron member of the present invention has such a structure, it is excellent in mechanical properties such as tensile strength, proof stress, elongation, impact resistance and the like, and is also suitable for automobile undercarriage parts and the like. It is a hard spheroidal graphite cast iron member.
次に本発明の実施形態を詳細に説明するが、本発明は以下の実施形態に限定されるものではなく、本発明の趣旨を逸脱しない範囲で、当業者の通常の知識に基づいて、適宜設計の変更、改良等が加えられることが理解されるべきである。 Next, embodiments of the present invention will be described in detail. However, the present invention is not limited to the following embodiments, and may be appropriately selected based on ordinary knowledge of those skilled in the art without departing from the spirit of the present invention. It should be understood that design changes, improvements, etc. can be made.
本発明の球状黒鉛鋳鉄部材は、Ｃを３．４〜４．０質量％、Ｓｉを１．５質量％以上２．０質量％未満、Ｍｎを０．３５〜０．５質量％、Ｎｉを１．０質量％を超え２．０質量％未満、及びＣｕを０．２〜０．５質量％含有し、残部がＦｅ及び不可避的に含有される不純物であり、パーライト組織の面積率が６０〜９０％、フェライト組織の面積率が１０〜４０％である。本発明の球状黒鉛鋳鉄部材は、このような構造であるため、優れた機械的性質を有し、表面付近を含み全体的に自動車の足回り部品等に好適な所定の硬さのものであるが、特に、耐衝撃性に優れ、自動車の足回り部品のような高い耐衝撃性を要求される部品として好適に用いることができる。また、本発明の球状黒鉛鋳鉄部材は、Ｍｏを含有しないことが好ましい。Ｍｏは高価であるため、Ｍｏを含有しないことにより安価に製造することが可能となる。そして、本発明の球状黒鉛鋳鉄部材は、Ｍｏを含有しないにもかかわらず、引張強さ及び伸びに優れたものである。本発明の球状黒鉛鋳鉄部材を用いる自動車の足回り部品としては、具体的にはナックル、ナックルアーム、ハブ等を挙げることができる。 In the spheroidal graphite cast iron member of the present invention, C is 3.4 to 4.0 mass%, Si is 1.5 mass% or more and less than 2.0 mass%, Mn is 0.35 to 0.5 mass%, Ni is More than 1.0% by mass and less than 2.0% by mass, and Cu is contained in an amount of 0.2 to 0.5% by mass, the balance being Fe and unavoidable impurities, and the area ratio of the pearlite structure is 60 -90%, and the area ratio of the ferrite structure is 10-40%. Since the spheroidal graphite cast iron member of the present invention has such a structure, the spheroidal graphite cast iron member has excellent mechanical properties, and has a predetermined hardness suitable for automobile undercarriage parts and the like, including the vicinity of the surface. However, it is particularly excellent in impact resistance and can be suitably used as a part that requires high impact resistance such as an automobile underbody part. Moreover, it is preferable that the spheroidal graphite cast iron member of the present invention does not contain Mo. Since Mo is expensive, it can be manufactured at low cost by not containing Mo. And although the spheroidal graphite cast iron member of the present invention does not contain Mo, it has excellent tensile strength and elongation. Specific examples of undercarriage parts for automobiles using the spheroidal graphite cast iron member of the present invention include knuckles, knuckle arms, hubs, and the like.
本発明の球状黒鉛鋳鉄部材に含有されるＣは、３．４〜４．０質量％であり、３．５〜３．９質量％が好ましく、３．６〜３．８質量％が更に好ましい。３．４質量％より少ないと、伸びが低下し、４．０質量％を超えると、初晶黒鉛が浮上して介在し、引張強さが低下する。 C contained in the spheroidal graphite cast iron member of the present invention is 3.4 to 4.0% by mass, preferably 3.5 to 3.9% by mass, and more preferably 3.6 to 3.8% by mass. . When the amount is less than 3.4% by mass, the elongation is lowered, and when the amount exceeds 4.0% by mass, primary graphite floats and intervenes to lower the tensile strength.
本発明の球状黒鉛鋳鉄部材に含有されるＳｉは、１．５質量％以上２．０質量％未満であり、１．６〜１．９質量％が好ましく、１．７〜１．９質量％が更に好ましい。１．５質量％未満であると、伸びが低下し、２．０質量％以上であると、衝撃値が低下する。 Si contained in the spheroidal graphite cast iron member of the present invention is 1.5% by mass or more and less than 2.0% by mass, preferably 1.6 to 1.9% by mass, and 1.7 to 1.9% by mass. Is more preferable. If the amount is less than 1.5% by mass, the elongation decreases, and if it is 2.0% by mass or more, the impact value decreases.
本発明の球状黒鉛鋳鉄部材においては、「Ｃの含有量」と「Ｓｉの含有量の３分の１」との合計が、３．９〜４．６質量％であることが好ましく、４．２〜４．４質量％であることが更に好ましい。３．９質量％未満であると、伸びが低下することがあり、４．６質量％を超えると、初晶黒鉛が浮上して介在し、引張強さが低下することがある。 In the spheroidal graphite cast iron member of the present invention, the total of “C content” and “1/3 of Si content” is preferably 3.9 to 4.6% by mass. More preferably, it is 2-4.4 mass%. If the amount is less than 3.9% by mass, the elongation may decrease. If the amount exceeds 4.6% by mass, primary graphite may float and intervene, and the tensile strength may decrease.
本発明の球状黒鉛鋳鉄部材の製造においては、鋳型に溶湯が注湯され、鋳型内の溶湯は、外表面側から冷却されて外表面側から内部に向かって凝固していく。このとき、外表面付近のＮｉは内部側に移動して偏析する傾向がある。Ｎｉはパーライト組織の生成に寄与するため、このようにＮｉが移動することにより溶湯の外表面付近のＮｉ量が低下すると、球状黒鉛鋳鉄部材を形成したときに、その外表面付近においてフェライト組織が多くなる。そして、外表面付近にフェライト組織が多くなると、表面付近の硬さが低下するため、得られた球状黒鉛鋳鉄部材を自動車部品として使用し、ボルトで締め付けるときに、硬さの低さにより表面が変形し、十分に締め付けることができないという問題が生じる。また、外表面付近にフェライト組織が多くなると、疲労特性、引張強さ、及び耐力が低下するという問題も生じる。ここで、「外表面付近」というときは、表面から１０ｍｍ±５ｍｍの深さまでの領域を意味する。また、球状黒鉛鋳鉄部材は、その肉厚が厚いほど、溶湯の冷却時に表面付近と内部との温度差が大きくなり、Ｎｉの偏析が生じ易くなるため、上記問題が生じ易くなる。更に、一つの部品の中に肉厚が厚い部分と薄い部分とがあるときには、Ｎｉが、冷却され易い肉厚の薄い部分から厚い部分に移動し易いため、肉厚の薄い部分にフェライト組織が生成し易くなる。 In the production of the spheroidal graphite cast iron member of the present invention, molten metal is poured into a mold, and the molten metal in the mold is cooled from the outer surface side and solidifies from the outer surface side toward the inside. At this time, Ni near the outer surface tends to move to the inner side and segregate. Since Ni contributes to the formation of a pearlite structure, when the amount of Ni in the vicinity of the outer surface of the molten metal decreases due to the movement of Ni in this way, when the spheroidal graphite cast iron member is formed, the ferrite structure is formed in the vicinity of the outer surface. Become more. And when the ferrite structure increases near the outer surface, the hardness near the surface decreases, so when the obtained spheroidal graphite cast iron member is used as an automobile part and tightened with a bolt, the surface is reduced due to the low hardness. The problem arises that it is deformed and cannot be tightened sufficiently. Further, when the ferrite structure increases in the vicinity of the outer surface, there arises a problem that fatigue characteristics, tensile strength, and proof stress are lowered. Here, “near the outer surface” means a region from the surface to a depth of 10 mm ± 5 mm. Further, the greater the thickness of the spheroidal graphite cast iron member, the greater the temperature difference between the vicinity of the surface and the inside when the molten metal is cooled, and Ni segregation is likely to occur, so the above problem is likely to occur. Furthermore, when there is a thick part and a thin part in one part, Ni easily moves from a thin part to a thick part that is easily cooled, so a ferrite structure is formed in the thin part. It becomes easy to generate.
一方、Ｎｉがパーライト組織の生成に寄与するのと同様に、Ｃｕ及びＭｎもパーライト組織の生成に寄与するものである。従って、偏析し難いＣｕ及びＭｎの配合量を多くすることにより、Ｎｉの偏析により溶湯の外表面付近のＮｉ量が低下しても、Ｃｕ及びＭｎの作用により、外表面付近にパーライト組織を十分に生成させることが可能となる。このように、Ｎｉ、Ｃｕ及びＭｎの配合量は、外表面付近のフェライト組織の生成を抑え、パーライト組織を多く生成させるために、以下に示すようなバランスにする必要がある。すなわち、本発明の球状黒鉛鋳鉄部材においては、Ｍｎを０．３５〜０．５質量％、Ｎｉを１．０質量％を超え２．０質量％未満、及びＣｕを０．２〜０．５質量％とすることが必要である。また、Ｍｎを０．４〜０．５質量％、Ｎｉを１．２〜１．８質量％、及びＣｕを０．３〜０．５質量％含有することが好ましく、Ｍｎを０．４〜０．４５質量％、Ｎｉを１．４〜１．６質量％、及びＣｕを０．４〜０．４５質量％含有することが更に好ましい。このような範囲にすることにより、表面付近のフェライト組織の生成が抑えられ、表面付近を含めて全体的に自動車の足回り部品等に適した所定の硬さとなり、優れた機械的性質を有する球状黒鉛鋳鉄部材を得ることができる。また、球状黒鉛鋳鉄部材の肉厚が厚い場合や、一部に薄い部分が形成されている場合でも、フェライト組織の生成を抑えることが可能となる。 On the other hand, Cu and Mn contribute to the formation of pearlite structure in the same way that Ni contributes to the formation of pearlite structure. Therefore, by increasing the amount of Cu and Mn that hardly segregate, even if the amount of Ni near the outer surface of the molten metal decreases due to the segregation of Ni, a sufficient pearlite structure is formed near the outer surface by the action of Cu and Mn. Can be generated. Thus, the blending amounts of Ni, Cu and Mn need to be balanced as shown below in order to suppress the formation of ferrite structure near the outer surface and to generate a large amount of pearlite structure. That is, in the spheroidal graphite cast iron member of the present invention, Mn is 0.35 to 0.5 mass%, Ni is more than 1.0 mass% and less than 2.0 mass%, and Cu is 0.2 to 0.5 mass%. It is necessary to set it as the mass%. Moreover, it is preferable to contain Mn 0.4-0.5 mass%, Ni 1.2-1.8 mass%, and Cu 0.3-0.5 mass%, and Mn 0.4- It is more preferable to contain 0.45 mass%, Ni 1.4-1.6 mass%, and Cu 0.4-0.45 mass%. By making such a range, the formation of ferrite structure near the surface is suppressed, and it has a predetermined hardness suitable for automobile undercarriage parts as a whole, including near the surface, and has excellent mechanical properties. A spheroidal graphite cast iron member can be obtained. Further, even when the spheroidal graphite cast iron member is thick or has a thin part, it is possible to suppress the formation of a ferrite structure.
本発明の球状黒鉛鋳鉄部材において、Ｎｉ含有量が、１．０質量％以下であると、引張強さが低下し、２．０質量％以上であると、衝撃値が低下する。Ｎｉを１．０質量％を超え２．０質量％未満という少ない含有量とすることにより、Ｎｉが偏析したときの影響を最小限に抑えることができる。 In the spheroidal graphite cast iron member of the present invention, when the Ni content is 1.0% by mass or less, the tensile strength decreases, and when it is 2.0% by mass or more, the impact value decreases. By setting Ni to a small content of more than 1.0% by mass and less than 2.0% by mass, the influence when Ni is segregated can be minimized.
本発明の球状黒鉛鋳鉄部材において、Ｃｕの含有量が、０．２質量％未満であると、パーライト組織を十分に生成させることができないため、引張強さが低下する。また、Ｃｕの含有量が、０．５質量％を超えると、硬さが高くなりすぎて加工性が低下する。 In the spheroidal graphite cast iron member of the present invention, if the Cu content is less than 0.2% by mass, the pearlite structure cannot be sufficiently generated, and thus the tensile strength is lowered. Moreover, when content of Cu exceeds 0.5 mass%, hardness will become high too much and workability will fall.
本発明の球状黒鉛鋳鉄部材において、Ｍｎの含有量が、０．３５質量％未満であると、パーライト組織を十分に生成させることができないため、引張強さが低下する。また、Ｍｎの含有量が０．５質量％を超えると、炭化物が発生し、引張強さ、耐力、伸び、耐衝撃性等の機械的性質が低下する。 In the spheroidal graphite cast iron member of the present invention, if the content of Mn is less than 0.35% by mass, a pearlite structure cannot be sufficiently generated, so that the tensile strength is lowered. On the other hand, if the Mn content exceeds 0.5% by mass, carbides are generated, and mechanical properties such as tensile strength, proof stress, elongation, and impact resistance are lowered.
ＣｕとＭｎの含有量の合計は、０．７〜０．９質量％であることが好ましく、０．７５〜０．８５質量％であることが更に好ましい。０．７質量％未満であると、パーライト組織を十分に生成させることができないため、引張強さが低下することがある。０．９質量％を超えると、硬さが高くなりすぎて、加工性が低下することがあり、また、炭化物が発生し、引張強さ、耐力、伸び、耐衝撃性等の機械的性質が低下することがある。 The total content of Cu and Mn is preferably 0.7 to 0.9% by mass, and more preferably 0.75 to 0.85% by mass. If it is less than 0.7% by mass, the pearlite structure cannot be sufficiently generated, and the tensile strength may be lowered. If it exceeds 0.9 mass%, the hardness becomes too high and the workability may be reduced, and carbides are generated, and mechanical properties such as tensile strength, proof stress, elongation, and impact resistance are exhibited. May decrease.
本発明の球状黒鉛鋳鉄部材は、上記Ｃ、Ｓｉ、Ｍｎ、Ｎｉ及びＣｕ以外の成分（残部）として、Ｆｅ及び不可避的に含有される不純物を含有する。不可避的に含有される不純物としては、Ｓ，Ｐ，Ｃｒ，Ｔｉ，Ｐｂ，Ｚｎ等が挙げられる。不可避的に含有される不純物の含有率は、１．５質量％以下であることが好ましく、１．０質量％以下であることが更に好ましい。不可避的に含有される不純物は、含有されないことが好ましいが、不可避的に０．５質量％以上は含有される可能性がある。Ｆｅの含有率は、球状黒鉛鋳鉄部材全体（１００質量％）から、上述した各成分の含有率を差し引いた値である。 The spheroidal graphite cast iron member of the present invention contains Fe and inevitably contained impurities as components (remainder) other than C, Si, Mn, Ni and Cu. Impurities contained unavoidably include S, P, Cr, Ti, Pb, Zn and the like. The content of impurities inevitably contained is preferably 1.5% by mass or less, and more preferably 1.0% by mass or less. The inevitably contained impurities are preferably not contained, but inevitably 0.5% by mass or more may be contained. The content of Fe is a value obtained by subtracting the content of each component described above from the entire spheroidal graphite cast iron member (100% by mass).
本発明の球状黒鉛鋳鉄部材は、パーライト組織の面積率が６０〜９０％であり、フェライト組織の面積率が１０〜４０％である。そして、パーライト組織の面積率が７０〜９０％、フェライト組織の面積率が１０〜３０％であることが好ましく、パーライト組織の面積率が８０〜９０％、フェライト組織の面積率が１０〜２０％であることが更に好ましい。「フェライト組織の面積率」及び「パーライト組織の面積率」は、球状黒鉛鋳鉄部材を任意の面で切断したときの断面におけるそれぞれの組織の面積率である。具体的には、画像解析ソフト（Ｎａｎｏｓｙｓｔｅｍ Ｃｏｒｐｏｒａｔｉｏｎ社製、商品名：ＮａｎｏＨｕｎｔｅｒ ＮＳ２Ｋ−Ｐｒｏ）を用い、５視野の平均で測定した値である。そして、「フェライト組織の面積率」は、フェライト組織とパーライト組織のそれぞれの面積の合計に対するフェライト組織の面積の比率であり、「パーライト組織の面積率」は、フェライト組織とパーライト組織のそれぞれの面積の合計に対するパーライト組織の面積の比率である。パーライト組織及びフェライト組織のそれぞれの面積率がこのような範囲であるため、本発明の球状黒鉛鋳鉄部材は、引張強さ、耐力、伸び、耐衝撃性等の機械的性質に優れ、更に自動車の足回り部品等に好適な所定の硬さのものである。パーライト組織の面積率が６０％未満、フェライト組織の面積率が４０％を超える場合は、引張強さが低下し、自動車の足回り部品等に必要な硬さが得られないという問題がある。パーライト組織の面積率が９０％超、フェライト組織の面積率が１０％未満の場合は、伸びと衝撃値が低下するという問題がある。 The spheroidal graphite cast iron member of the present invention has a pearlite structure area ratio of 60 to 90% and a ferrite structure area ratio of 10 to 40%. The area ratio of the pearlite structure is preferably 70 to 90%, the area ratio of the ferrite structure is preferably 10 to 30%, the area ratio of the pearlite structure is 80 to 90%, and the area ratio of the ferrite structure is 10 to 20%. More preferably. The “area ratio of the ferrite structure” and the “area ratio of the pearlite structure” are the area ratios of the respective structures in the cross section when the spheroidal graphite cast iron member is cut on an arbitrary surface. Specifically, it is a value measured with an average of five visual fields using image analysis software (manufactured by Nanosystem Corporation, trade name: NanoHunter NS2K-Pro). The “area ratio of the ferrite structure” is a ratio of the area of the ferrite structure to the total area of the ferrite structure and the pearlite structure, and the “area ratio of the pearlite structure” is the area of each of the ferrite structure and the pearlite structure. The ratio of the area of the pearlite structure to the total of Since the area ratio of each of the pearlite structure and the ferrite structure is in such a range, the spheroidal graphite cast iron member of the present invention is excellent in mechanical properties such as tensile strength, proof stress, elongation, and impact resistance, and moreover, It has a predetermined hardness suitable for underbody parts and the like. When the area ratio of the pearlite structure is less than 60% and the area ratio of the ferrite structure exceeds 40%, there is a problem that the tensile strength is lowered and the hardness required for the undercarriage parts of the automobile cannot be obtained. When the area ratio of the pearlite structure exceeds 90% and the area ratio of the ferrite structure is less than 10%, there is a problem that the elongation and impact value are lowered.
本発明の球状黒鉛鋳鉄部材は、鋳造後、鋳放しで得られたものであることが好ましい。「鋳造後、鋳放しで得られる」というときは、鋳型に注湯された溶湯を、鋳型内で常温まで自然冷却して球状黒鉛鋳鉄部材を得ることを意味し、溶湯を鋳型に注湯した後に熱処理等の後処理を行わないことを意味する。本発明の球状黒鉛鋳鉄部材は、このように鋳放しで得られるため、熱処理等の後処理工程が不要であり、効率的に製造することができる。 The spheroidal graphite cast iron member of the present invention is preferably obtained by casting after casting. The phrase “obtained by casting after casting” means that the molten metal poured into the mold is naturally cooled to room temperature in the mold to obtain a spheroidal graphite cast iron member, and the molten metal is poured into the mold. This means that post-treatment such as heat treatment is not performed later. Since the spheroidal graphite cast iron member of the present invention is obtained by casting as described above, a post-treatment process such as a heat treatment is not necessary and can be efficiently manufactured.
本発明の球状黒鉛鋳鉄部材は、引張強さが７７０ＭＰａ以上であることが好ましい。引張強さは、大きい値であるほど好ましいが、９００ＭＰａ程度が上限と考えられる。また、伸びが８．０％以上であることが好ましい。伸びは、大きい値であるほど好ましいが、１５．０％程度が上限と考えられる。更に、耐力が、４５０ＭＰａ以上であることが好ましい。耐力は、大きい値であるほど好ましいが、６００ＭＰａ程度が上限と考えられる。引張強さ、伸び及び耐力は、ＪＩＳ Ｚ ２２０１に準拠した４号試験片を作製し、その試験片を用いて、ＪＩＳ Ｚ ２２４１に準拠した方法で測定した値である。 The spheroidal graphite cast iron member of the present invention preferably has a tensile strength of 770 MPa or more. The tensile strength is preferably as large as possible, but about 900 MPa is considered the upper limit. Moreover, it is preferable that elongation is 8.0% or more. The elongation is preferably as large as possible, but about 15.0% is considered the upper limit. Furthermore, the proof stress is preferably 450 MPa or more. The proof stress is preferably as large as possible, but about 600 MPa is considered the upper limit. Tensile strength, elongation, and proof stress are values measured by a method according to JIS Z 2241 using a test piece prepared by No. 4 test piece according to JIS Z 2201.
本発明の球状黒鉛鋳鉄部材は、常温（２０℃）での衝撃値が７．０Ｊ／ｃｍ２以上であることが好ましい。常温での衝撃値の上限は、１５．０Ｊ／ｃｍ２程度と考えられる。また、低温（−４０℃）での衝撃値が３．０Ｊ／ｃｍ２以上であることが好ましい。低温での衝撃値の上限は、８．０Ｊ／ｃｍ２程度と考えられる。衝撃値は、ＪＩＳ Ｚ ２２０２に準拠したＵノッチ試験片を作製し、その試験片を用いて、ＪＩＳ Ｚ ２２４２に準拠した方法で測定した値である。 The spheroidal graphite cast iron member of the present invention preferably has an impact value at ordinary temperature (20 ° C.) of 7.0 J / cm 2 or more. The upper limit of the impact value at room temperature is considered to be about 15.0 J / cm 2 . Moreover, it is preferable that the impact value in low temperature (-40 degreeC) is 3.0 J / cm < 2 > or more. The upper limit of the impact value at low temperature is considered to be about 8.0 J / cm 2 . The impact value is a value obtained by preparing a U-notch test piece conforming to JIS Z 2202 and using the test piece by a method conforming to JIS Z 2242.
本発明の球状黒鉛鋳鉄部材は、ブリネル硬さ（ＨＢ）が、自動車の足回り部品に好適となるように、１９０〜２６０であることが好ましい。ブリネル硬さは、球状黒鉛鋳鉄部材の表面及び内部の双方において、上記範囲であることが好ましい。ブリネル硬さは、ＪＩＳ Ｚ ２２４３に準拠した方法により測定した値である。 The spheroidal graphite cast iron member of the present invention preferably has a Brinell hardness (HB) of 190 to 260 so that it is suitable for automobile underbody parts. The Brinell hardness is preferably in the above range both on the surface and inside of the spheroidal graphite cast iron member. The Brinell hardness is a value measured by a method based on JIS Z 2243.
本発明の球状黒鉛鋳鉄部材の製造方法は、特に制限されず、公知の球状黒鉛鋳鉄部材の製造方法を用いることができ、鋳放しとすることが好ましい。例えば、以下の方法により製造することができる。 The method for producing the spheroidal graphite cast iron member of the present invention is not particularly limited, and a known method for producing a spheroidal graphite cast iron member can be used, and it is preferable to use as-cast. For example, it can be produced by the following method.
銑鉄、鋼屑等の各種鉄合金を、各成分が所定の配合量となるように配合し、これを原料として電気炉（低周波炉又は高周波炉）又はキュポラを用いて鋳鉄溶湯を溶製する。溶製された溶湯について、黒鉛球状化剤を用いて取鍋内で溶湯処理を行う。この際、必要に応じて接種剤を、取鍋内添加又は注湯流接種する。溶湯処理を行った後、溶湯を、造型機により造型された鋳型に注湯して鋳込み、鋳型内でそのまま常温まで自然冷却（鋳放し）し、凝固させて、本発明の球状黒鉛鋳鉄部材を得る。鋳型内で鋳放しにより得られた本発明の球状黒鉛鋳鉄部材は、次に、例えば、シェイクアウトマシンにて型ばらしを行い、球状黒鉛鋳鉄と造型砂とを分離し、球状黒鉛鋳鉄をドラムクーラーで冷却した後、ショットブラストで表面に付着した砂を除去することが好ましい。そして、鋳仕上げ工程において堰、ばり取りなどの仕上げを行うことが好ましい。 Various iron alloys such as pig iron and steel scrap are compounded so that each component has a predetermined blending amount, and molten iron is melted using this as a raw material using an electric furnace (low frequency furnace or high frequency furnace) or cupola. . About the molten metal, the molten metal process is performed in a ladle using a graphite spheroidizing agent. At this time, if necessary, inoculum is added in the ladle or poured into the pouring bath. After performing the molten metal treatment, the molten metal is poured into a mold molded by a molding machine and cast, and then naturally cooled (cast out) to room temperature in the mold and solidified to solidify the spheroidal graphite cast iron member of the present invention. obtain. The spheroidal graphite cast iron member of the present invention obtained by as-casting in the mold is then separated by, for example, a shake-out machine to separate the spheroidal graphite cast iron and the molding sand, and the spheroidal graphite cast iron is used as a drum cooler. It is preferable to remove the sand adhering to the surface by shot blasting after cooling at. And it is preferable to perform finishing, such as weir and deburring, in a casting finishing process.
以下、本発明を実施例によって更に具体的に説明するが、本発明はこれらの実施例によって何ら限定されるものではない。 EXAMPLES Hereinafter, the present invention will be described more specifically with reference to examples, but the present invention is not limited to these examples.
（実施例１）
鋳鉄原料を配合し、高周波溶解炉にて溶融して表１に示す組成の球状黒鉛鋳鉄の溶湯を溶製した。上記球状黒鉛鋳鉄溶湯を、図１Ａ、図１Ｂに示す自動車足回り部品１用の鋳型に約１４００℃で注湯し、鋳型内で常温まで自然放冷（鋳放し）して、球状黒鉛鋳鉄部材である自動車足回り部品１を作製した（実施例１）。図１Ａは、実施例１の球状黒鉛鋳鉄部材である自動車足回り部品を示す平面図であり、図１Ｂは、実施例１の球状黒鉛鋳鉄部材である自動車足回り部品を示す側面図である。
Example 1
Cast iron raw materials were blended and melted in a high-frequency melting furnace to produce a molten spheroidal graphite cast iron having the composition shown in Table 1. The above spheroidal graphite cast iron molten metal is poured into a mold for an automobile undercarriage part 1 shown in FIGS. 1A and 1B at about 1400 ° C., and then allowed to naturally cool (cast) to room temperature in the mold to produce a spheroidal graphite cast iron member. An automobile undercarriage component 1 was produced (Example 1). 1A is a plan view showing an automobile underbody part that is a spheroidal graphite cast iron member of Example 1, and FIG. 1B is a side view showing an automobile underbody part that is a spheroidal graphite cast iron member of Example 1. FIG.
得られた自動車足回り部品１のアームの部分の、パーライト組織の面積率（パーライト（％））及びフェライト組織の面積率（フェライト（％））を、以下の方法（面積率の測定）により、表面からの深さ５ｍｍ、１０ｍｍ、２５ｍｍ及び５０ｍｍの位置の断面において測定した。結果を表２に示す。また、自動車足回り部品１のサンプリング部位Ｚの深さ１０ｍｍの部分の組織を示す、光学顕微鏡による拡大写真（１００倍に拡大）を図２に示す。図２に示すように、実施例１の球状黒鉛鋳鉄部材は、パーライト組織１３の面積率が高く、その中に、フェライト組織１２及び黒鉛１１が散在していることがわかる。 The area ratio of the pearlite structure (pearlite (%)) and the area ratio of the ferrite structure (ferrite (%)) of the arm portion of the obtained automobile undercarriage part 1 are measured by the following method (measurement of the area ratio). Measurements were taken at cross sections at 5 mm, 10 mm, 25 mm and 50 mm depths from the surface. The results are shown in Table 2. Moreover, the enlarged photograph (enlarged 100 times) by the optical microscope which shows the structure | tissue of the 10 mm depth part of the sampling site | part Z of the motor vehicle axle part 1 is shown in FIG. As shown in FIG. 2, the spheroidal graphite cast iron member of Example 1 has a high area ratio of the pearlite structure 13, and it can be seen that the ferrite structure 12 and the graphite 11 are scattered therein.
得られた自動車足回り部品１について、以下の方法により、引張強さ（ＭＰａ）、耐力（ＭＰａ）、伸び（％）、常温衝撃値（Ｊ／ｃｍ２）、低温衝撃値（Ｊ／ｃｍ２）及び外表面のブリネル硬さ（ＨＢ）を測定した。結果を表３に示す。 For automotive underbody part 1 obtained by the following method, the tensile strength (MPa), yield strength (MPa), elongation (%), ordinary temperature impact value (J / cm 2), low-temperature impact value (J / cm 2 ) And Brinell hardness (HB) of the outer surface. The results are shown in Table 3.
（面積率の測定）
面積率は、画像解析ソフト（Ｎａｎｏｓｙｓｔｅｍ Ｃｏｒｐｏｒａｔｉｏｎ社製、商品名：ＮａｎｏＨｕｎｔｅｒ ＮＳ２Ｋ−Ｐｒｏ）を用い、５視野の平均により測定する。
(Measurement of area ratio)
The area ratio is measured by an average of five fields of view using image analysis software (manufactured by Nanosystem Corporation, trade name: NanoHunter NS2K-Pro).
（引張強さ）
自動車足回り部品１のサンプリング部位Ｘから、ＪＩＳ Ｚ ２２０１の４号試験片を採取し、ＪＩＳ Ｚ ２２４１の方法に準拠し、引張強さを測定する。引張強さは、７７０ＭＰａ以上を合格とする。
(Tensile strength)
A No. 4 test piece of JIS Z 2201 is sampled from the sampling region X of the automobile undercarriage component 1 and the tensile strength is measured in accordance with the method of JIS Z 2241. The tensile strength is 770 MPa or more.
（耐力）
自動車足回り部品１のサンプリング部位Ｘから、ＪＩＳ Ｚ ２２０１の４号試験片を採取し、ＪＩＳ Ｚ ２２４１の方法に準拠し、耐力を測定する。耐力は、４５０ＭＰａ以上を合格とする。
(Strength)
A No. 4 test piece of JIS Z 2201 is sampled from the sampling region X of the automobile underbody part 1, and the proof stress is measured in accordance with the method of JIS Z 2241. The proof stress shall be 450 MPa or more.
（伸び）
自動車足回り部品１のサンプリング部位Ｘから、ＪＩＳ Ｚ ２２０１の４号試験片を採取し、ＪＩＳ Ｚ ２２４１の方法に準拠し、伸びを測定する。伸びは、８．０％以上を合格とする。
(Elongation)
A No. 4 test piece of JIS Z 2201 is sampled from the sampling region X of the automobile undercarriage part 1 and the elongation is measured according to the method of JIS Z 2241. Elongation makes 8.0% or more pass.
（常温衝撃値）
自動車足回り部品１のサンプリング部位Ｙから、ＪＩＳ Ｚ ２２０２に準拠したＵノッチ試験片を作製する。この試験片を用いて、ＪＩＳ Ｚ ２２４２に準拠した方法で、常温（２０℃）におけるシャルピー衝撃試験を行い、得られた結果を常温衝撃値とする。常温衝撃値は、７．０Ｊ／ｃｍ２以上を合格とする。
(Normal temperature impact value)
A U-notch test piece conforming to JIS Z 2202 is prepared from the sampling region Y of the automobile underbody part 1. Using this test piece, a Charpy impact test at normal temperature (20 ° C.) is performed by a method based on JIS Z 2242, and the obtained result is defined as a normal temperature impact value. A normal temperature impact value of 7.0 J / cm 2 or more is acceptable.
（低温衝撃値）
自動車足回り部品１のサンプリング部位Ｙから、ＪＩＳ Ｚ ２２０２に準拠したＵノッチ試験片を作製する。この試験片を用いて、ＪＩＳ Ｚ ２２４２に準拠した方法で、−４０℃におけるシャルピー衝撃試験を行い、得られた結果を低温衝撃値とする。低温衝撃値は、３．０Ｊ／ｃｍ２以上を合格とする。
(Low temperature impact value)
A U-notch test piece conforming to JIS Z 2202 is prepared from the sampling region Y of the automobile underbody part 1. Using this test piece, a Charpy impact test at −40 ° C. is performed by a method based on JIS Z 2242, and the obtained result is taken as a low temperature impact value. The low temperature impact value is 3.0 J / cm 2 or more.
（ブリネル硬さ）
ブリネル硬さは、ＪＩＳ Ｚ ２２４３に準拠した方法により測定する。ブリネル硬さは、１９０〜２６０の範囲を合格とする。
(Brinell hardness)
Brinell hardness is measured by a method based on JIS Z 2243. Brinell hardness makes the range of 190-260 pass.
（比較例１）
球状黒鉛鋳鉄の溶湯の組成を表１に示すように変えた以外は、実施例１と同様にして図１Ａ、図１Ｂに示す自動車足回り部品１と同じ形状の自動車足回り部品を作製した（比較例１）。得られた自動車足回り部品について、実施例１の場合と同様に、上記各測定を行った。結果を表２，３に示す。
(Comparative Example 1)
Except for changing the composition of the spheroidal graphite cast iron melt as shown in Table 1, an automobile underbody part having the same shape as the automobile underbody part 1 shown in FIGS. 1A and 1B was produced in the same manner as in Example 1. Comparative Example 1). Each of the above measurements was performed on the obtained automobile underbody parts in the same manner as in Example 1. The results are shown in Tables 2 and 3.
表３より、実施例１の球状黒鉛鋳鉄部材（自動車足回り部品）は、引張強さ、耐力、伸び、耐衝撃性等の機械的性質に優れ、更に自動車の足回り部品として好適な硬さであることがわかる。 From Table 3, the spheroidal graphite cast iron member (automobile undercarriage part) of Example 1 is excellent in mechanical properties such as tensile strength, proof stress, elongation, and impact resistance, and further has a hardness suitable as an undercarriage part for an automobile. It can be seen that it is.
自動車部品として好適に利用でき、特にシャーシや足回り部品として好適に利用することができる。 It can be suitably used as an automobile part, and in particular can be suitably used as a chassis or a suspension part.
１：自動車足回り部品、１１：黒鉛、１２：フェライト組織、１３：パーライト組織、Ｘ，Ｙ，Ｚ：サンプリング部位。 1: automobile undercarriage parts, 11: graphite, 12: ferrite structure, 13: pearlite structure, X, Y, Z: sampling site.
Claims (3)
パーライト組織の面積率が６０〜９０％、フェライト組織の面積率が１０〜４０％である球状黒鉛鋳鉄部材。 C is 3.4 to 4.0% by mass, Si is 1.5% by mass or more and less than 2.0% by mass, Mn is 0.35 to 0.5% by mass, Ni is more than 1.0% by mass, and 2. Less than 0% by weight, and 0.2 to 0.5% by weight of Cu, the balance being Fe and unavoidable impurities,
A spheroidal graphite cast iron member having an area ratio of pearlite structure of 60 to 90% and an area ratio of ferrite structure of 10 to 40%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2007163865A JP4963444B2 (en) | 2007-06-21 | 2007-06-21 | Spheroidal graphite cast iron member |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2007163865A JP4963444B2 (en) | 2007-06-21 | 2007-06-21 | Spheroidal graphite cast iron member |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2009001865A JP2009001865A (en) | 2009-01-08 |
| JP4963444B2 true JP4963444B2 (en) | 2012-06-27 |
Family
ID=40318568
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2007163865A Active JP4963444B2 (en) | 2007-06-21 | 2007-06-21 | Spheroidal graphite cast iron member |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP4963444B2 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP2799565B1 (en) | 2011-12-28 | 2017-11-08 | Hitachi Metals, Ltd. | Spheroidal graphite cast iron having exceptional strength and ductility and method for manufacturing same |
| EP3243920B1 (en) * | 2017-03-24 | 2020-04-29 | GF Casting Solutions Kunshan Co. Ltd. | Spheroidal cast alloy |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS56130453A (en) * | 1980-03-14 | 1981-10-13 | Riken Corp | Tough spheroidal graphite cast iron and its heat treatment |
| JPS57185956A (en) * | 1981-05-06 | 1982-11-16 | Kurimoto Iron Works Ltd | Ductile pipe of alloy with high corrosion resistance |
| JP3204293B2 (en) * | 1996-04-29 | 2001-09-04 | 日立金属株式会社 | Method of manufacturing spheroidal graphite cast iron member |
| JP2001073063A (en) * | 2000-08-14 | 2001-03-21 | Asahi Tec Corp | As-cast ductile cast iron |
-
2007
- 2007-06-21 JP JP2007163865A patent/JP4963444B2/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| JP2009001865A (en) | 2009-01-08 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP6079641B2 (en) | Spheroidal graphite cast iron excellent in strength and toughness and method for producing the same | |
| JP5655115B1 (en) | Spheroidal graphite cast iron | |
| JP6954846B2 (en) | Spheroidal graphite cast iron | |
| JP2005264301A (en) | Casting aluminum alloy, casting of aluminum alloy and manufacturing method therefor | |
| JPH1136029A (en) | High strength titanium alloy casting product | |
| WO2017017989A1 (en) | Cast steel material | |
| JP4994734B2 (en) | Aluminum alloy for casting and cast aluminum alloy | |
| JP4963444B2 (en) | Spheroidal graphite cast iron member | |
| JP2006322062A (en) | Aluminum alloy for casting, and aluminum alloy casting thereby | |
| JP5856599B2 (en) | Differential equipment parts | |
| JP3964675B2 (en) | Non-austempered spheroidal graphite cast iron | |
| JP4527304B2 (en) | High strength high toughness spheroidal graphite cast iron | |
| JP5862406B2 (en) | Aluminum alloy member and manufacturing method thereof | |
| JP3648158B2 (en) | Spheroidal graphite cast iron | |
| KR102539284B1 (en) | Nodular cast iron with excellent resistance to gas defects | |
| JP2007327083A (en) | Spheroidal graphite cast iron and its production method | |
| JP2020002402A (en) | Nodular graphite cast iron | |
| WO2017164382A1 (en) | Spherical graphite cast iron, cast article and automobile structural component comprising same, and method for manufacturing cast article comprising spherical graphite cast iron | |
| JP2005256088A (en) | Spheroidal graphite cast-iron member | |
| JP4210526B2 (en) | Spheroidal graphite cast iron excellent in low temperature impact resistance and method for producing the same | |
| WO2023243726A1 (en) | Austenitic heat-resistant cast steel and exhaust system component formed of same | |
| JP4162461B2 (en) | Spheroidal graphite cast iron and manufacturing method | |
| JP2021059752A (en) | Spheroidal graphite cast iron excellent in strength and toughness and having low hardness | |
| JP2020066772A (en) | Spheroidal graphite cast iron | |
| JPH04111963A (en) | Production of die steel for plastic working |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20100304 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20120313 |
|
| 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: 20120321 |
|
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20120323 |
|
| R150 | Certificate of patent or registration of utility model |
Ref document number: 4963444 Country of ref document: JP Free format text: JAPANESE INTERMEDIATE CODE: R150 Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20150406 Year of fee payment: 3 |
|
| S531 | Written request for registration of change of domicile |
Free format text: JAPANESE INTERMEDIATE CODE: R313531 |
|
| R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |
|
| S111 | Request for change of ownership or part of ownership |
Free format text: JAPANESE INTERMEDIATE CODE: R313111 |
|
| R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |
|
| S533 | Written request for registration of change of name |
Free format text: JAPANESE INTERMEDIATE CODE: R313533 |
|
| R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |