JPS629179B2 - - Google Patents
Info
- Publication number
- JPS629179B2 JPS629179B2 JP8414083A JP8414083A JPS629179B2 JP S629179 B2 JPS629179 B2 JP S629179B2 JP 8414083 A JP8414083 A JP 8414083A JP 8414083 A JP8414083 A JP 8414083A JP S629179 B2 JPS629179 B2 JP S629179B2
- Authority
- JP
- Japan
- Prior art keywords
- cast iron
- graphite
- test
- test piece
- toughness
- 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.)
- Expired
Links
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 34
- 239000010439 graphite Substances 0.000 claims description 33
- 229910002804 graphite Inorganic materials 0.000 claims description 33
- 229910001018 Cast iron Inorganic materials 0.000 claims description 18
- 229910001562 pearlite Inorganic materials 0.000 claims description 8
- 229910052804 chromium Inorganic materials 0.000 claims description 5
- 229910052759 nickel Inorganic materials 0.000 claims description 5
- 229910052720 vanadium Inorganic materials 0.000 claims description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 3
- 150000001247 metal acetylides Chemical class 0.000 claims description 3
- 229910052799 carbon Inorganic materials 0.000 claims description 2
- 239000010455 vermiculite Substances 0.000 claims 1
- 229910052902 vermiculite Inorganic materials 0.000 claims 1
- 235000019354 vermiculite Nutrition 0.000 claims 1
- 229910001060 Gray iron Inorganic materials 0.000 description 12
- 239000000463 material Substances 0.000 description 11
- 230000000694 effects Effects 0.000 description 9
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 7
- 239000010949 copper Substances 0.000 description 6
- 238000001000 micrograph Methods 0.000 description 6
- 229910001141 Ductile iron Inorganic materials 0.000 description 5
- 229910052802 copper Inorganic materials 0.000 description 5
- 230000013011 mating Effects 0.000 description 5
- 238000005299 abrasion Methods 0.000 description 4
- 238000005260 corrosion Methods 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 4
- 239000003921 oil Substances 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- 229910000519 Ferrosilicon Inorganic materials 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 239000010687 lubricating oil Substances 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000009863 impact test Methods 0.000 description 2
- 230000001050 lubricating effect Effects 0.000 description 2
- OXNIZHLAWKMVMX-UHFFFAOYSA-N picric acid Chemical compound OC1=C([N+]([O-])=O)C=C([N+]([O-])=O)C=C1[N+]([O-])=O OXNIZHLAWKMVMX-UHFFFAOYSA-N 0.000 description 2
- 238000003825 pressing Methods 0.000 description 2
- 239000000523 sample Substances 0.000 description 2
- 239000004576 sand Substances 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 229910052684 Cerium Inorganic materials 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910000604 Ferrochrome Inorganic materials 0.000 description 1
- 229910000628 Ferrovanadium Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 238000011081 inoculation Methods 0.000 description 1
- 239000002054 inoculum Substances 0.000 description 1
- 235000000396 iron Nutrition 0.000 description 1
- PNXOJQQRXBVKEX-UHFFFAOYSA-N iron vanadium Chemical compound [V].[Fe] PNXOJQQRXBVKEX-UHFFFAOYSA-N 0.000 description 1
- 239000000314 lubricant Substances 0.000 description 1
- 238000005461 lubrication Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 239000010705 motor oil Substances 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
Landscapes
- Pistons, Piston Rings, And Cylinders (AREA)
Description
本発明は耐スカツフ性、耐摩耗性の改善された
コンパクテド・バーミキユラ黒鉛鋳鉄に関する。
ねずみ鋳鉄は潤滑剤として作用する黒鉛をその
基地中に内在しているので耐摩耗性に優れ、ピス
トンリングやシリンダライナのような摺動部品の
材料として従来から多用されているが、黒鉛が片
状に晶出した組織となつているために靭性に劣る
という欠点を有している。他方、球状黒鉛鋳鉄は
黒鉛が球状に晶出した組織となつているために黒
鉛による内部切欠き効果が極めて小さく、鋳鉄の
内では最も靭性に優れているが、摺動部品の材料
として使用すると耐スカツフ性に劣るという欠点
を有している。
最近、黒鉛形状が片状と球状との中間に位する
コンパクテド・バーミキユラ黒鉛（Compacted
Vermicular Graphite）となつているコンパクテ
ド・バーミキユラ黒鉛鋳鉄（以下、CV黒鉛鋳鉄
という）が、靭性は球状黒鉛鋳鉄に劣るがねずみ
鋳鉄より可成り優れていることから注目されるよ
うになつてきている。
本発明は上記の事情に鑑み、靭性に優れると共
に耐スカツフ性、耐摩耗性がねずみ鋳鉄よりも更
に改善されたCV黒鉛鋳鉄を提供することを目的
としてなされたものであつて、重量比で3.2〜4.0
％Ｃ、1.0〜1.8％Si、0.5％以下Mn、0.1％以下
Ｐ、0.015％以下Ｓ、0.1〜0.9％Cr、0.1〜0.3％
Ｖ、1.5〜2.5％Ni、0.5〜1.5％Cu、残部が実質的
にFeからなり、パーライト基地中にコンパクテ
ド・バーミキユラ黒鉛と、Cr、Ｖを含む面積比
で３〜15％の複炭化物が均一に分布した組織を有
するCV黒鉛鋳鉄に関する。
本発明CV黒鉛鋳鉄は基地組織を遊離フエライ
トを含まぬパーライト組織とし、基地中にCr、
Ｖを含む複炭化物を面積比で３〜15％均一に晶
出、分布させて耐スカツフ性、耐摩耗性を改善し
たものである。上記複炭化物の量が面積比で３％
未満では耐スカツフ性、耐摩耗性改善の効果が不
充分であり、これが面積比で15％を越えると脆く
なつて靭性を害するようになる。
このような組織とするために本発明CV黒鉛鋳
鉄の化学組成は以下のようにする。
Ｃは重量比で3.2％未満ではチルが発生し易
く、重量比で4.0％を越えると黒鉛の晶出量が多
くなり過ぎて靭性を害するようになると共に、複
炭化物の晶出量が不足して耐摩耗性が低下するよ
うになるので、3.2〜4.0重量％の範囲とする。
以下、単に％で表わす場合は重量％を表わすこ
ととする。
Siは1.0％未満ではチルし易く、1.8％を越える
と複炭化物の晶出量が少なくなり、かつ、基地中
に遊離フエライトが生成して耐摩耗性が害される
ようになると共に、黒鉛が片状になる傾向になつ
て靭性を害するようになるので、1.0〜1.8％の範
囲とする。
Mnは一般の鉄鋼材料中に不可避的に存在する
元素であつて、基地のパーライトを安定化して遊
離フエライトの生成を抑える作用があるが、靭性
を害する作用を有しているので、本発明にあつて
は少ない程望ましく、0.5％以下とする。
Ｐは一般に鋳鉄にあつては組織中にステダイト
を晶出して耐摩耗性を改善する作用を有するので
あるが、靭性を害するので、本発明にあつては少
ない程望ましく、0.1％以下とする。
Ｓは黒鉛形状を片状にする作用を有するので、
少ない程望ましく、本発明にあつては0.015％以
下とする。
Cr及びＶは複炭化物を形成して耐スカツフ
性、耐摩耗性を改善するが、いずれも0.1％未満
ではこの効果が不充分であり、Crは0.9％を越え
ると、Ｖは0.3％を越えると複炭化物の晶出量が
多くなり過ぎて脆くなり、靭性を害するようにな
るので、Crは0.1〜0.9％、Ｖは0.1〜0.3％の範囲
とする。
Ni及びCuはいずれも遊離フエライトの生成を
抑えて基地組織をパーライトにすると共に、靭性
を改善するが、Niは1.5％未満、Cuは0.5％未満で
は上記効果が不充分であり、Niは2.5％を越えて
も、Cuは1.5％を越えても上記効果の増大が顕著
ではないので、Niは1.5〜2.5％、Cuは0.5〜1.5％
の範囲とする。
以下、実施例について説明する。
球状黒鉛鋳鉄用銑、CV黒鉛鋳鉄戻り屑、黒鉛
屑、フエロシリコン、フエロクロム、フエロバナ
ジウム、電解ニツケル、電気銅を配合し、高周波
誘導炉で熔解、出湯し、1510℃で60％Si、10％
Ca、５％Ce、残部Feの接種剤（大阪特殊合金製
CVアロイ）を0.6％添加し、フエロシリコン0.6
％で後期接種してから生砂型に鋳込んで、上部に
押湯を付した高さ230mm、幅100mm、厚さ36mmの供
試材とした。
供試材の分析値は第１表に示す通りである。
The present invention relates to compacted vermicular graphite cast iron with improved scuff resistance and wear resistance. Gray cast iron has graphite in its base that acts as a lubricant, so it has excellent wear resistance and has been widely used as a material for sliding parts such as piston rings and cylinder liners. It has a disadvantage of poor toughness because it has a crystallized structure. On the other hand, spheroidal graphite cast iron has a structure in which graphite crystallizes in a spherical shape, so the internal notch effect caused by graphite is extremely small, and it has the highest toughness among cast irons, but when used as a material for sliding parts. It has the disadvantage of poor scuff resistance. Recently, compacted vermicular graphite, whose graphite shape is between flaky and spherical, has been developed.
Compacted vermicular graphite cast iron (hereinafter referred to as CV graphite cast iron) is attracting attention because its toughness is inferior to spheroidal graphite cast iron but considerably superior to gray cast iron. In view of the above circumstances, the present invention was made with the purpose of providing CV graphite cast iron which has excellent toughness and further improved scuff resistance and wear resistance than gray cast iron, and has a weight ratio of 3.2. ~4.0
%C, 1.0-1.8% Si, 0.5% or less Mn, 0.1% or less P, 0.015% or less S, 0.1-0.9% Cr, 0.1-0.3%
V, 1.5 to 2.5% Ni, 0.5 to 1.5% Cu, the balance is substantially Fe, and the pearlite base contains compacted vermicular graphite and 3 to 15% area ratio double carbide containing Cr and V. Concerning CV graphite cast iron with a distributed structure. The CV graphite cast iron of the present invention has a pearlite structure that does not contain free ferrite, and contains Cr and
Double carbide containing V is uniformly crystallized and distributed in an area ratio of 3 to 15% to improve scuff resistance and abrasion resistance. The amount of double carbide mentioned above is 3% in terms of area ratio.
If the area ratio is less than 15%, the effect of improving scuff resistance and abrasion resistance will be insufficient, and if the area ratio exceeds 15%, the area will become brittle and the toughness will be impaired. In order to obtain such a structure, the chemical composition of the CV graphite cast iron of the present invention is as follows. When C is less than 3.2% by weight, chilling tends to occur, and when it exceeds 4.0% by weight, the amount of graphite crystallized becomes too large, impairing toughness, and the amount of double carbide crystallized is insufficient. Since the abrasion resistance decreases, the content is set in the range of 3.2 to 4.0% by weight. Hereinafter, when expressed simply in %, it will be expressed in % by weight. When Si is less than 1.0%, it tends to chill, and when it exceeds 1.8%, the amount of double carbide crystallization decreases, and free ferrite is generated in the base, impairing wear resistance and graphite flakes. Since the content tends to form and impairs toughness, it should be in the range of 1.0 to 1.8%. Mn is an element that is unavoidably present in general steel materials, and has the effect of stabilizing pearlite in the base and suppressing the formation of free ferrite, but it also has the effect of impairing toughness, so it is not included in the present invention. The lower the content, the better, and it should be 0.5% or less. In general, P has the effect of crystallizing steadite in the structure of cast iron and improving wear resistance, but since it impairs toughness, in the present invention it is preferably as low as possible, and is set at 0.1% or less. Since S has the effect of making graphite flaky,
The lower the content, the more desirable it is, and in the present invention, it is set to 0.015% or less. Cr and V form double carbides and improve scuff resistance and wear resistance, but this effect is insufficient when both are less than 0.1%, and when Cr exceeds 0.9%, V exceeds 0.3%. If the amount of crystallized double carbides becomes too large, it becomes brittle and impairs toughness, so Cr and V are set in the ranges of 0.1 to 0.9% and 0.1 to 0.3%, respectively. Both Ni and Cu suppress the formation of free ferrite, turn the matrix structure into pearlite, and improve toughness, but the above effects are insufficient when Ni is less than 1.5% and Cu is less than 0.5%, and Ni is 2.5%. %, the increase in the above effect is not remarkable even if Cu exceeds 1.5%, so Ni is 1.5 to 2.5% and Cu is 0.5 to 1.5%.
The range shall be . Examples will be described below. Pig for spheroidal graphite cast iron, CV graphite cast iron return scrap, graphite scrap, ferrosilicon, ferrochrome, ferrovanadium, electrolytic nickel, and electrolytic copper are mixed, melted and tapped in a high frequency induction furnace, and heated to 1510℃ to produce 60% Si, Ten%
Inoculant of Ca, 5% Ce, balance Fe (manufactured by Osaka Special Alloy)
CV alloy) added 0.6%, Ferrosilicon 0.6
% late stage inoculation and then cast into a green sand mold to obtain a test material with a height of 230 mm, width of 100 mm, and thickness of 36 mm with a riser attached to the top. The analytical values of the sample materials are shown in Table 1.
【表】
同表には比較のためにキユポラで熔製、Ca―
Si0.55％、フエロシリコン0.2％で接種し、生砂
型に鋳込んで得られたねずみ鋳鉄の分析値が併記
してある。
第１図はかくして得られた本発明CV黒鉛鋳鉄
の組織を示す倍率100倍の顕微鏡写真（腐蝕せ
ず）、第２図は同じく倍率100倍の顕微鏡写真（ピ
クラル腐蝕）、第３図は比較のねずみ鋳鉄の組織
を示す倍率100倍の顕微鏡写真（腐蝕せず）、第４
図は同じく倍率400倍の顕微鏡写真（ピクラル腐
蝕）である。
本発明CV黒鉛鋳鉄は第１図に黒鉛組織を示す
ように黒鉛がコンパクテド・バーミキユラ黒鉛と
して晶出しており、第２図に示すように白色を呈
する複炭化物がパーライト基地中に均一に分布し
ているのが観察される。複炭化物の量は線積分法
によつて測定した結果、８面積％であつた。
比較のねずみ鋳鉄の組織は第３図及び第４図に
示すように、良く伸びた片状黒鉛（Ａ型黒鉛）を
有するパーライト基地の、ねずみ鋳鉄として良好
な組織である。
(1) 機械試験
これらの供試材から引張試験片として8C試験
片を、抗折試験片としてＣ号試験片を、衝撃試験
片としてシヤルピー試験片（無溝）を採取し、引
張試験、抗折試験、衝撃試験及び硬さ試験を行つ
た。硬さ試験片は引張試験後に試験片の掴み部か
ら採取した。なお、試験は夫々３回ずつ行つた。
試験結果は第２表に示す通りである。[Table] For comparison, the table shows
Analytical values for gray cast iron obtained by inoculating with 0.55% Si and 0.2% ferrosilicon and casting into a green sand mold are also listed. Figure 1 is a micrograph at 100x magnification showing the structure of the CV graphite cast iron of the present invention thus obtained (no corrosion), Figure 2 is a micrograph at 100x magnification (picral corrosion), and Figure 3 is a comparison. Micrograph at 100x magnification showing the structure of gray cast iron (no corrosion), No. 4
The figure is also a micrograph (picral corrosion) at 400x magnification. In the CV graphite cast iron of the present invention, graphite is crystallized as compacted vermicular graphite as shown in the graphite structure in Figure 1, and white double carbide is uniformly distributed in the pearlite base as shown in Figure 2. It is observed that there are The amount of double carbide was measured by line integral method and was found to be 8% by area. As shown in FIGS. 3 and 4, the comparative gray cast iron has a pearlite base structure with well-elongated flaky graphite (A-type graphite), which is good for a gray cast iron. (1) Mechanical test From these test materials, a No. 8C test piece was taken as a tensile test piece, a No. C test piece was taken as a bending test piece, and a Shapey test piece (without grooves) was taken as an impact test piece. A folding test, an impact test and a hardness test were conducted. A hardness test piece was taken from the grip part of the test piece after the tensile test. Note that each test was conducted three times. The test results are shown in Table 2.
【表】
同表から、本発明CV黒鉛鋳鉄はねずみ鋳鉄に
比べて機械的強さが大きく、而も靭性に優れてい
ることが解る。
(2) スカツフ試験
前記供試材から５mm×５mm×10mmの試験片を採
取し、研磨仕上げを施してスカツフ試験に供し
た。
試験装置は第５図及び第６図に概要を図解的に
示すものであつて、ステータホルダ１に取外し可
能に取付けられた直径80mm、厚さ10mmの研磨仕上
げを施した円板２の中央には裏側から注油孔３を
通じて潤滑油が注油される。ステータ１には油圧
装置（図示せず）によつて右方へ向けて所定圧力
で押圧力Ｐが作用するようにしてある。円板２に
相対向してロータ４があり、駆動装置（図示せ
ず）によつて所定速度で回転するようにしてあ
る。ロータ４の円板２に対する端面に取付けられ
た試験片保持具４ａには正方形端面を摺動面とし
て試験片５が同心円上に等間隔に４個取外し可能
に、かつ、円板２に対して摺動自在に取付けてあ
る。
このような装置に於いてステータ１に所定の押
圧力Ｐをかけ、所定の面圧で円板（相手材）２と
試験片５とが接触するようにしておいて、注油孔
３から摺動面に所定給油速度で給油しながらロー
タ４を回転させる。一定時間毎にステータ１に作
用する圧力を階段的に増加して行き、ロータ４の
回転によつて試験片５と相手の円板２との摩擦に
よつてステータ１に生ずるトルク（摩擦力によつ
て生ずるトルク）Ｔをスピンドル６を介してロー
ドセル７に作用せしめ、その変化を動歪計８で読
み、記録計９に記録させる。トルクＴが急激に上
昇するときにスカツフが生じたものとして、その
時の接触面圧をもつてカツフ発生面圧とし、この
大小をもつて耐スカツフ性の良否を判断する。
試験条件は次に示す通りである。速度は8m／
sec、潤滑油及び給油条件はモータオイル＃30に
て温度80℃、400ml、接触圧力は40Kg／cm2で20分
間馴し運転後50Kg／cm2で３分間、その後３分間経
過毎に10Kg／cm2づつ上昇、相手材は舶用シリンダ
ライナ用鋳鉄FC25である。
スカツフ試験には比較材として前記ねずみ鋳鉄
のほかにパーライト基地の球状黒鉛鋳鉄FCD70
についても同様の試験を行つた。
試験結果は第３表に示す通りである。[Table] From the same table, it can be seen that the CV graphite cast iron of the present invention has greater mechanical strength and superior toughness than gray cast iron. (2) Scatter test A 5 mm x 5 mm x 10 mm test piece was taken from the sample material, polished and subjected to the Scatter test. The test apparatus is schematically shown in FIGS. 5 and 6, and is mounted at the center of a polished disc 2 with a diameter of 80 mm and a thickness of 10 mm, which is removably attached to a stator holder 1. Lubricating oil is supplied from the back side through the oil filling hole 3. A pressing force P is applied to the stator 1 to the right by a hydraulic device (not shown) at a predetermined pressure. A rotor 4 is disposed opposite to the disk 2, and is rotated at a predetermined speed by a drive device (not shown). A test piece holder 4a attached to the end face of the rotor 4 relative to the disc 2 has a square end face as a sliding surface, and four test pieces 5 can be removed concentrically at equal intervals, and It is slidably mounted. In such a device, a predetermined pressing force P is applied to the stator 1 so that the disc (mating material) 2 and the test piece 5 come into contact with a predetermined surface pressure, and the test piece 5 is slid from the oil filling hole 3. The rotor 4 is rotated while lubricating the surface at a predetermined lubricating speed. The pressure acting on the stator 1 is increased stepwise at regular intervals, and the torque (frictional force) generated on the stator 1 due to the friction between the test piece 5 and the mating disk 2 due to the rotation of the rotor 4 is increased stepwise. The resulting torque) T is applied to the load cell 7 via the spindle 6, and its change is read by the dynamic strain meter 8 and recorded by the recorder 9. Assuming that the scuff occurs when the torque T increases rapidly, the contact surface pressure at that time is taken as the surface pressure where the scuff occurs, and the quality of the scuff resistance is judged based on the magnitude of this. The test conditions are as follows. Speed is 8m/
sec, lubricating oil and oil supply conditions are motor oil #30, temperature 80℃, 400ml, contact pressure 40Kg/ cm2 for 20 minutes, then 50Kg/ cm2 for 3 minutes, then 10Kg/cm2 every 3 minutes. The mating material is FC25 cast iron for marine cylinder liners. In addition to the above-mentioned gray cast iron, pearlite-based spheroidal graphite cast iron FCD70 was used as a comparative material for the Skatuf test.
A similar test was also conducted for The test results are shown in Table 3.
【表】
同表から、本発明CV黒鉛鋳鉄は球状黒鉛鋳鉄
に比べては勿論、ねずみ鋳鉄に比べても耐スカツ
フ性が改善されていることが解る。
(3) 摩耗試験
試験装置は前記スカツフ試験で使用したみのを
使用して摩擦速度３、５、8m／sec、接触面圧
100Kg／cm2、潤滑油80℃のデイーゼル耐久オイル
を400ml供給の条件で摺動させ、夫々の摩耗量を
測定した。
試験結果は第７図に示す通りである。図中、
３、５、８の数字は摩擦速度（ｍ／sec）を表わ
す。試験片の摩耗量は高さ寸法の減少で、相手材
のそれは試験片が摺動するリング状摺動域に生ず
る溝の円板半径方向の断面積で示してある。
同図から、本発明CV黒鉛鋳鉄は従来のねずみ
鋳鉄に比べていずれの摩擦速度でも摩耗量が少な
く、優れた耐摩耗性を示している。
以上説明したように、本発明CV黒鉛鋳鉄は黒
鉛がコンパクテド・バーミキユラ黒鉛であるため
に機械的強さ、靭性共に優れ、また、適量の複炭
化物をその組織中に含有しているので耐スカツフ
性、耐摩耗性に優れており、ピストンリングやシ
リンダライナ等の摺動部品の材料として好適であ
る。[Table] From the table, it can be seen that the CV graphite cast iron of the present invention has improved scuff resistance not only compared to spheroidal graphite cast iron but also compared to gray cast iron. (3) Wear test The test equipment used was the same as the one used in the above-mentioned scathing test, and the friction speeds were 3, 5, and 8 m/sec, and the contact pressure
The amount of wear was measured by sliding on the slides under the conditions of supplying 400 ml of diesel durable oil at 100 Kg/cm 2 and lubricating oil at 80°C. The test results are shown in FIG. In the figure,
The numbers 3, 5, and 8 represent the friction velocity (m/sec). The amount of wear on the test piece is shown by the decrease in height, and that of the mating material is shown by the cross-sectional area in the radial direction of the disk of the groove that occurs in the ring-shaped sliding area on which the test piece slides. The figure shows that the CV graphite cast iron of the present invention has less wear than conventional gray cast iron at any friction speed, and exhibits excellent wear resistance. As explained above, the CV graphite cast iron of the present invention has excellent mechanical strength and toughness because the graphite is compacted vermicular graphite, and also has good scuffing resistance because it contains an appropriate amount of double carbide in its structure. It has excellent wear resistance and is suitable as a material for sliding parts such as piston rings and cylinder liners.
第１図及び第２図は本発明CV黒鉛鋳鉄の組織
の一例を示す顕微鏡写真、第３図及び第４図は比
較のねずみ鋳鉄の組織を示す顕微鏡写真である。
第５図及び第６図はスカツフ試験及び摩耗試験に
使用した試験装置の概要を示し、第５図は部分縦
断面図、第６図は第５図に示す−矢視側面図
である。
１……ステータ、２……相手材円板、４……ロ
ータ、５……試験片、３……注油孔、第７図は摩
耗試験の結果を示すグラフである。
FIGS. 1 and 2 are microphotographs showing an example of the structure of CV graphite cast iron of the present invention, and FIGS. 3 and 4 are microphotographs showing the structure of comparative gray cast iron.
5 and 6 show an outline of the test apparatus used for the scuff test and the abrasion test, with FIG. 5 being a partial longitudinal cross-sectional view, and FIG. 6 being a side view taken in the direction of the arrow shown in FIG. DESCRIPTION OF SYMBOLS 1...Stator, 2...Mating disc, 4...Rotor, 5...Test piece, 3...Lubrication hole FIG. 7 is a graph showing the results of the wear test.
Claims (1)
以下Mn、0.1％以下Ｐ、0.015％以下Ｓ、0.1〜0.9
％Cr、0.1〜0.3％Ｖ、1.5〜2.5％Ni、0.5〜1.5％
Cu、残部が実質的にFeからなり、パーライト基
地中にコンパクテド・バーミキユラ黒鉛とCr、
Ｖを含む面積比で３〜15％の複炭化物が均一に分
布した組織を有するコンパクテド・バーミキユラ
黒鉛鋳鉄。1 Weight ratio: 3.2-4.0%C, 1.0-1.8%Si, 0.5%
Below Mn, below 0.1% P, below 0.015% S, 0.1 to 0.9
%Cr, 0.1~0.3%V, 1.5~2.5%Ni, 0.5~1.5%
Cu, the balance is essentially Fe, compacted vermiculite graphite and Cr in the pearlite base,
Compacted vermicular graphite cast iron with a structure in which double carbides with an area ratio of 3 to 15% containing V are evenly distributed.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP8414083A JPS59215459A (en) | 1983-05-16 | 1983-05-16 | Compacted vermicular graphite cast iron having resistant to scuffing and wear |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP8414083A JPS59215459A (en) | 1983-05-16 | 1983-05-16 | Compacted vermicular graphite cast iron having resistant to scuffing and wear |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS59215459A JPS59215459A (en) | 1984-12-05 |
| JPS629179B2 true JPS629179B2 (en) | 1987-02-26 |
Family
ID=13822185
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP8414083A Granted JPS59215459A (en) | 1983-05-16 | 1983-05-16 | Compacted vermicular graphite cast iron having resistant to scuffing and wear |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS59215459A (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR101677169B1 (en) * | 2016-03-09 | 2016-11-17 | 삼영기계 (주) | piston ring improved abrasion-proof |
-
1983
- 1983-05-16 JP JP8414083A patent/JPS59215459A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS59215459A (en) | 1984-12-05 |
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