JPH0730426B2 - Heat remelting Cast iron for surface hardening - Google Patents
Heat remelting Cast iron for surface hardeningInfo
- Publication number
- JPH0730426B2 JPH0730426B2 JP61054461A JP5446186A JPH0730426B2 JP H0730426 B2 JPH0730426 B2 JP H0730426B2 JP 61054461 A JP61054461 A JP 61054461A JP 5446186 A JP5446186 A JP 5446186A JP H0730426 B2 JPH0730426 B2 JP H0730426B2
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- weight
- cast iron
- surface hardening
- content
- effect
- Prior art date
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- Other Surface Treatments For Metallic Materials (AREA)
Description
【発明の詳細な説明】 ［発明の目的］ （産業上の利用分野） 本発明は表面硬化用鋳鉄に関し、より詳しくは、高密度
エネルギ源により鋳鉄表面を加熱再溶融し、自己冷却に
よって形成したチル層内でのブローホールの発生を防止
して耐摩耗性を向上させるのに利用される加熱再溶融表
面硬化用特殊鋳鉄に関するものである。The present invention relates to cast iron for surface hardening. More specifically, the present invention relates to cast iron for surface hardening. More specifically, the cast iron surface is heated and remelted by a high-density energy source, and formed by self-cooling. The present invention relates to a special cast iron for heat remelting and surface hardening, which is used for preventing blowholes in a chill layer and improving wear resistance.
（従来の技術） 近年、レーザビーム，電子ビーム,TIGアーク，プラズマ
アーク等の高密度エネルギ熱源により鋳鉄表面を加熱再
溶融し、自己冷却によってち密なセメンタイトからなる
チル層を形成させる鋳鉄の表面硬化法が採用されてい
る。(Prior art) In recent years, the surface of cast iron is hardened by heating and remelting the cast iron surface with a high-density energy heat source such as laser beam, electron beam, TIG arc, and plasma arc, and forming a chill layer of dense cementite by self-cooling. The law has been adopted.
この場合、普通鋳鉄を用いて上記の加熱再溶融を行い、
自己冷却によって鋳鉄表面に再溶融チル層を形成する
と、そのチル層内にブローホールを発生することが多
く、硬化表面層の耐摩耗性を阻害する。そこで、従来に
おいてこの種の表面硬化に供される特殊鋳鉄としては、
高価な希土類元素等を多く添加したものがあった（例え
ば、特開昭60−5819号公報）。In this case, the above-mentioned heating remelting using ordinary cast iron,
When a remelted chill layer is formed on the surface of cast iron by self-cooling, blow holes are often generated in the chill layer, which impairs the wear resistance of the hardened surface layer. Therefore, as a special cast iron conventionally used for this type of surface hardening,
There has been one in which a large amount of expensive rare earth elements and the like have been added (for example, JP-A-60-5819).
（発明が解決しようとする問題点） しかしながら、このような従来の特殊鋳鉄では、資源的
にかなり限られた希土類元素を添加するため、経済性お
よび安定供給性といった面から制約をうけることがあ
り、用途が限定されるうえに耐摩耗性が不十分であると
いう問題点があった。(Problems to be Solved by the Invention) However, in such a conventional special cast iron, a rare earth element, which is considerably limited in terms of resources, is added, and therefore, it may be restricted in terms of economical efficiency and stable supply. However, there is a problem that the use is limited and the abrasion resistance is insufficient.
本発明はこのような従来の問題点に着目してなされたも
ので、鋳鉄に脱酸性がありかつ耐摩耗性向上効果のある
Ｂを単独で含有させるか、あるいはこのＢと共にMg,Al,
Ca,Zn,Zr等の脱酸元素の１種以上を添加することによっ
て、鋳鉄表面の再溶融チル層内でのブローホールの発生
がなくかつ耐摩耗性が良好である表面硬化用鋳鉄を低コ
ストで提供することを目的としている。The present invention has been made by paying attention to such a conventional problem, and cast iron is made to contain B alone which is deoxidized and has an effect of improving wear resistance, or Mg, Al,
By adding at least one deoxidizing element such as Ca, Zn, Zr, etc., it is possible to reduce the surface hardening cast iron that does not have blow holes in the remelted chill layer on the cast iron surface and has good wear resistance. It is intended to be provided at a cost.
［発明の構成］ （問題点を解決するための手段） 本発明は、Ｃを2.5〜4.0重量％、Siを0.5〜3.5重量％、
Mnを0.2〜1.0重量％、Ｐを0.02〜0.8重量％含有し、さ
らに、脱酸効果がありかつ耐摩耗性向上効果があるＢを
単独では0.005〜0.05重量％含有するか、もしくはＢを
0.002〜0.02重量％含有しかつこのＢとMg,Al,Ca,Zn,Zr
等の脱酸元素とを合計で0.02〜0.1重量％含有し、残部F
eおよび不純物からなる加熱再溶融表面硬化用鋳鉄とす
ることによって、レーザビーム，電子ビーム,TIGアー
ク，プラズマアーク等の高密度エネルギ熱源を用いて本
発明に係る鋳鉄表面を再溶融・自己冷却させた時に，当
該鋳鉄表面にブローホールが発生するのを防止しつつセ
メンタイトを主体とするチル層を形成させることがで
き、耐摩耗性を向上させることができるようにしたもの
である。[Structure of the Invention] (Means for Solving Problems) In the present invention, C is 2.5 to 4.0% by weight, Si is 0.5 to 3.5% by weight,
It contains 0.2 to 1.0% by weight of Mn, 0.02 to 0.8% by weight of P, and 0.005 to 0.05% by weight of B alone, which has a deoxidizing effect and an abrasion resistance improving effect, or contains B.
0.002 to 0.02% by weight and contains B, Mg, Al, Ca, Zn, Zr
0.02 to 0.1 wt% in total with deoxidizing elements such as
By making the cast iron for heating and remelting surface hardening consisting of e and impurities, the cast iron surface according to the present invention is remelted and self-cooled by using a high-density energy heat source such as laser beam, electron beam, TIG arc, and plasma arc. At the same time, it is possible to form a chill layer mainly composed of cementite while preventing the generation of blowholes on the surface of the cast iron, and to improve the wear resistance.
このように、Ｂを単独で、もしくはMg,Al,Ca,Zn,Zrと共
に複合で適量添加することによって以下に示すような効
果を示す。Thus, the following effects are exhibited by adding an appropriate amount of B alone or in combination with Mg, Al, Ca, Zn, and Zr.
すなわち、普通鋳鉄の表面を上記に例示した高密度エネ
ルギ熱源を用いて加熱再溶融すると、溶解される基地中
の黒鉛と鋳鉄中の内在酸素および／または雰囲気中の酸
素とが結合してCO,CO2ガスが発生するが、本発明による
特殊鋳鉄では、添加されたＢ等の脱酸効果を有する元素
が前記酸素と優先的に結合し、黒鉛との結合によるガス
化を阻止することによって、チル層内でのブローホール
の発生を防止することができる。That is, when the surface of ordinary cast iron is heated and remelted by using the high-density energy heat source exemplified above, the combined graphite in the matrix and the internal oxygen in the cast iron and / or the oxygen in the atmosphere form CO, Although CO 2 gas is generated, in the special cast iron according to the present invention, the added element such as B having a deoxidizing effect preferentially binds to the oxygen and prevents gasification due to the binding with graphite, It is possible to prevent the generation of blow holes in the chill layer.
さらに、Ｂは脱酸効果を有するだけでなく、オーステナ
イト，フェライトにはほとんど固溶せず、セメンタイト
中に選択的に固溶してFe3（CB）を生じ、これがステダ
イト（Fe−Fe3C−Fe3P）中に板状に晶出して耐摩耗性を
向上させる効果もあわせて有する。そして、Ｂを単独で
添加する場合にその含有量が0.005重量％以上になると
上記の効果があらわれるが、0.05重量％を超えてもその
効果の向上はあまりみられず、むしろ粗大な硼化物を生
じてぜい化するので、Ｂ含有量はこれ単独の場合に0.00
5〜0.05重量％に限定した。他方、ＢをMg,Al,Ca,Zn,Zr
と共に添加する場合にはＢの含有量が0.002重量％以上
でかつMg,Al,Ca,Zn,Zrのうちの１種以上とＢとの合計が
0.02重量％以上で効果がみられるが、他の元素と共に添
加した場合Ｂの含有量が0.02重量％を超えてもその増量
による効果の向上はほとんどなく、また合計含有量が0.
1重量％を超えてもそれらの溶け込みが難しくなるだけ
であって効果の向上はほとんどみられないので、0.02〜
0.1重量％の範囲に限定した。Further, B not only has a deoxidizing effect, but also hardly forms a solid solution in austenite and ferrite, and selectively forms a solid solution in cementite to form Fe 3 (CB), which is a steadite (Fe-Fe 3 C). It also has the effect of improving the wear resistance by crystallizing plate-like in (Fe 3 P). When B is added alone, if the content is 0.005% by weight or more, the above effect appears, but even if it exceeds 0.05% by weight, the effect is not improved so much, and rather a coarse boride is added. When it is used alone, the B content is 0.00.
Limited to 5 to 0.05% by weight. On the other hand, B is Mg, Al, Ca, Zn, Zr
When added together, the content of B is 0.002% by weight or more, and the total of B and one or more of Mg, Al, Ca, Zn and Zr is
The effect is seen at 0.02% by weight or more, but when added together with other elements, even if the content of B exceeds 0.02% by weight, there is almost no improvement in the effect due to the increase, and the total content is 0.
Even if it exceeds 1% by weight, it is difficult to melt them, and the improvement of the effect is hardly seen.
It was limited to the range of 0.1% by weight.
また、Ｃが2.5重量％未満、Siが0.5重量％未満であると
セメンタイト量が不足し、耐摩耗性が不十分となってし
まい、逆にＣが4.0重量％超過、Siが3.5重量％超過であ
るとセメンタイトが凝集し、ぜい化しやすくなるため、
Ｃは2.5〜4.0重量％、Siは0.5〜3.5重量％の範囲に限定
した。Mnは一部がフェライトに固溶し、一部がMn3Cを形
成し、Fe3Cと複合炭化物を作り、パーライト安定化し基
地強化するので0.2重量％以上必要であるが、1.0重量％
を超えて含有してもその効果の向上はあまりなく、炭化
物が粗大化するのでMnの含有量は0.2〜1.0重量％の範囲
に限定した。Ｐは一部フェライトに固溶するが、Fe,Cと
耐摩耗性のある三元共晶のステダイト（Fe−Fe3C−Fe
3P）を形成するので0.02重量％以上含有することが必要
であるが、0.8重量％を超えて含有してもその効果の向
上はなく、かえってぜい化をもたらすのでＰの含有量は
0.02〜0.8重量％とした。If C is less than 2.5% by weight and Si is less than 0.5% by weight, the amount of cementite is insufficient and wear resistance becomes insufficient. Conversely, C exceeds 4.0% by weight and Si exceeds 3.5% by weight. If so, the cementite aggregates and easily embrittles,
C is limited to 2.5 to 4.0% by weight and Si is limited to 0.5 to 3.5% by weight. 0.2% by weight or more is necessary because Mn partially dissolves in ferrite to form Mn 3 C, forms complex carbide with Fe 3 C, stabilizes pearlite, and strengthens the matrix, but 1.0% by weight
Even if the content exceeds the above range, the effect is not improved so much and the carbides are coarsened, so the Mn content is limited to the range of 0.2 to 1.0% by weight. P is a solid solution to some ferrites, Fe, C and wear resistance is ternary eutectic steadite (Fe-Fe 3 C-Fe
3 P) is formed, it is necessary to contain 0.02% by weight or more, but if the content exceeds 0.8% by weight, the effect is not improved and rather embrittlement occurs, so the content of P is
It was set to 0.02 to 0.8% by weight.
（実施例） 以下、本発明の実施例を比較例と共に説明する。(Example) Hereinafter, the Example of this invention is demonstrated with a comparative example.
〈実施例１〜８〉 〈比較例１〜６〉 第１表に示す化学組成の元湯ＡにFe−Ｂを添加して、第
２表に示す実施例１〜4,比較例１〜３の鋳鉄を鋳造し、
同じく第１表に示す元湯ＢにFe−Ｂを添加して、第３表
に示す実施例５〜8,比較例４〜６の鋳鉄を鋳造した。な
お、元湯A,B中のS,Sbは不可避的不純物であり、鋳物用
銑鉄に帰因するものである。次いで、これらの鋳鉄の表
面を2mm程度加工除去して黒皮面を取り除いた後、不活
性雰囲気中でその表面をTIGアークにより加熱再溶融・
自己冷却させた。このとき、TIGアークによる再溶融処
理条件は、直流電流:90A,タングステン電極と鋳鉄表面
との距離:2mmとし、15mm/secで走査させた。次に、TIG
アークによる再溶融処理後に表面を0.5mm加工し、その
加工面にあらわれたブローホールを画像処理装置で測定
した。この結果を同じく第２表，第３表に示す。<Examples 1 to 8><Comparative Examples 1 to 6> Fe-B was added to the original hot water A having the chemical composition shown in Table 1, and Examples 1 to 4 and Comparative Examples 1 to 3 shown in Table 2 were added. Cast iron,
Similarly, Fe-B was added to the hot water B shown in Table 1 to cast the cast irons of Examples 5-8 and Comparative Examples 4-6 shown in Table 3. Note that S and Sb in the original hot water A and B are unavoidable impurities, and are attributed to pig iron for casting. Then, the surface of these cast irons is processed and removed by about 2 mm to remove the black skin surface, and then the surface is heated and re-melted by TIG arc in an inert atmosphere.
Allowed to self-cool. At this time, the conditions for remelting by TIG arc were direct current: 90 A, distance between tungsten electrode and cast iron surface: 2 mm, and scanning was performed at 15 mm / sec. Then TIG
The surface was processed by 0.5 mm after the remelting treatment by the arc, and the blowholes appearing on the processed surface were measured by an image processing device. The results are also shown in Tables 2 and 3.
第２表および第３表から明らかなように、Ｂ含有量が0.
004重量％以下では表面に多数のブローホールが認めら
れるが、Ｂ含有量が増えるにしたがってその発生量は減
少し、含有量が0.05重量％のものではブローホールの発
生は認められなかった。 As is clear from Tables 2 and 3, the B content is 0.
Many blowholes were observed on the surface when the content was 004% by weight or less, but the generation amount decreased as the B content increased, and no generation of blowholes was observed when the content was 0.05% by weight.
〈実施例９〜12〉 〈比較例７〜９〉 第１表の元湯ＡにFe−ＢおよびMg,Al,Ca,Zn,Zrを含有す
る脱酸剤を添加してそれぞれ実施例９〜12および比較例
７〜９の鋳鉄を鋳造し、前記実施例１〜８と同様の方法
で加熱再溶融・自己冷却し、その後前記実施例１〜８と
同様の方法でブローホールの発生状況を測定した。この
結果を同じく第４表に示す。<Examples 9 to 12><Comparative examples 7 to 9> Examples 9 to 12 were prepared by adding a deoxidizing agent containing Fe-B and Mg, Al, Ca, Zn, and Zr to the hot water A shown in Table 1. 12 and Comparative Examples 7 to 9 were cast, heated and remelted and self-cooled in the same manner as in Examples 1 to 8 and then blowholes were checked for occurrence in the same manner as in Examples 1 to 8. It was measured. The results are also shown in Table 4.
第４表から明らかなように、Ｂが0.002重量％未満であ
ったり、また、Ｂが0.002重量％以上であってもB,Mg,A
l,Ca,Zn,Zrの合計含有量が0.02重量％未満であったりし
た場合は多数のブローホールが認められるが、Ｂを0.00
2重量％以上含有し、かつB,Mg,Al,Ca,Zn,Zrの合計含有
量が0.02重量％以上ではブローホールの発生はほとんど
なく、特にＢを0.003重量％以上含みかつB,Mg,Al,Ca,Z
n,Zrの合計含有量が0.078重量％以上ではブローホール
の発生は認められないことが確認された。 As is clear from Table 4, even if B is less than 0.002% by weight, or if B is 0.002% by weight or more, B, Mg, A
When the total content of l, Ca, Zn and Zr is less than 0.02% by weight, many blowholes are recognized, but B is 0.00
If the content of B, Mg, Al, Ca, Zn, Zr is 2% by weight or more and the total content of B, Mg, Al, Ca, Zn and Zr is 0.02% by weight or more, almost no blowholes are generated. Al, Ca, Z
It was confirmed that blowholes were not generated when the total content of n and Zr was 0.078 wt% or more.
〈耐久試験〉 次に、前記実施例１〜12に示す本発明品および比較例１
〜９に示す比較品の組成を持つ鋳鉄カムシャフト素材を
鋳造し、これらの鋳鉄カム面の表面を2mm程度加工除去
して黒皮面を取り除いた後、前記実施例１〜８で示した
条件でカムシャフトのカム面をTIGアークで加熱再溶融
・自己冷却させることにより表面硬化したカムシャフト
を製作した。<Durability Test> Next, the products of the present invention shown in Examples 1 to 12 and Comparative Example 1
9 to 9 are cast, and cast iron camshaft materials having the compositions of the comparative products are cast, the surfaces of these cast iron cam surfaces are processed and removed by about 2 mm to remove the black skin surface, and then the conditions shown in Examples 1 to 8 above. A surface-hardened camshaft was manufactured by heating and remelting and self-cooling the cam surface of the camshaft with a TIG arc.
次に、このようにして得たカムシャフトを自動車用エン
ジンに組込んで耐久試験を行った。このとき、相手材で
あるロッカーアームのチップは、自動車用エンジンのロ
ッカーアームチップ材として近年一般的に用いられるよ
うになった鉄系焼結材で、その組成は、C:2.5重量％,M
n:0.4重量％,Cr:12重量％,Mo;1.0重量％,P:0.5重量％，
残部Feからなるものであって、その硬度はHRCで50以上
のものを用いた。Next, a durability test was conducted by incorporating the camshaft thus obtained into an automobile engine. At this time, the rocker arm tip, which is the mating material, is an iron-based sintered material that has been commonly used in recent years as a rocker arm tip material for automobile engines. Its composition is C: 2.5 wt%, M
n: 0.4 wt%, Cr: 12 wt%, Mo; 1.0 wt%, P: 0.5 wt%,
The balance was Fe, and the hardness was 50 or more in H R C.
そして、耐久試験は第５表に示す試験条件により行っ
た。その結果を第６表に示す。The durability test was performed under the test conditions shown in Table 5. The results are shown in Table 6.
第６表より明らかなように、実施例１〜12の供試材の場
合に、カムシャフト摩耗量はいずれも極めて小さい値と
なっており、比較例１〜９の供試材の場合に比べてかな
り優れていることがわかる。 As is clear from Table 6, in the case of the test materials of Examples 1 to 12, the camshaft wear amounts were all extremely small values, and compared to the case of the test materials of Comparative Examples 1 to 9 You can see that it is quite excellent.
［発明の効果］ 以上説明してきたように、本発明による加熱再溶融表面
硬化用鋳鉄は、Ｃを2.5〜4.0重量％、Siを0.5〜3.5重量
％、Mnを0.2〜1.0重量％、Ｐを0.02〜0.8重量％含有
し、さらに、脱酸性がありかつ耐摩耗性向上効果のある
Ｂを単独で0.005〜0.05重量％含有するか、もしくはＢ
を0.002〜0.02重量％含有しかつ脱酸元素であるMg,Al,C
a,Zn,Zrのうちの１種以上と共に合計で0.02〜0.1重量％
含有し、残部Feおよび不純物からなる成分組成としたか
ら、オーステナイト，フェライトにはほとんど固溶せ
ず、セメンタイト中に選択的に固溶してFe3（CB）を生
じ、これが耐摩耗性のある三次元共晶のステダイト（Fe
−Fe3C−Fe3P）中に板状に晶出して耐摩耗性を向上させ
ることが可能であると共に、レーザビーム，電子ビー
ム,TIGアーク，プラズマアーク等の高密度エネルギ熱源
による鋳鉄表面の再溶融処理に際して、当該再溶融チル
層内でのブローホール発生を有効に阻止することが可能
であり、耐摩耗性を著しく向上させることができるとい
う非常に優れた効果が得られる。また、本発明による鋳
鉄では、その溶解，保持，鋳造において何ら特別な装
置，手法も必要とせず、従来の一般の鋳造技術で製造で
き、現時点では高価な希土類元素を含まないため価格を
低くおさえることができるという著しく優れた効果も得
られる。[Advantages of the Invention] As described above, the heat-remelting surface-hardening cast iron according to the present invention contains 2.5 to 4.0% by weight of C, 0.5 to 3.5% by weight of Si, 0.2 to 1.0% by weight of Mn, and P of 0.02 to 0.8% by weight, and 0.005 to 0.05% by weight of B alone, which is deacidified and has an effect of improving wear resistance, or B
Of 0.002 to 0.02% by weight and being a deoxidizing element, Mg, Al, C
0.02 to 0.1% by weight in total with one or more of a, Zn and Zr
Since it is contained and has a composition consisting of the balance Fe and impurities, it hardly dissolves in austenite and ferrite, and selectively forms solid solution in cementite to form Fe 3 (CB), which has wear resistance. Three-dimensional eutectic steadite (Fe
-Fe 3 C-Fe 3 P) can be crystallized in the form of a plate to improve wear resistance, and the surface of cast iron by a high-density energy heat source such as laser beam, electron beam, TIG arc, plasma arc, etc. In the remelting treatment (1), it is possible to effectively prevent the generation of blowholes in the remelted chill layer, and it is possible to obtain a very excellent effect that the wear resistance can be remarkably improved. Further, the cast iron according to the present invention does not require any special device or method for melting, holding, and casting, and can be manufactured by a conventional general casting technique. Since it does not contain expensive rare earth elements at the present time, the price can be kept low. It is also possible to obtain a remarkably excellent effect.
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 昭57−155345（ＪＰ，Ａ) 特開 昭54−41216（ＪＰ，Ａ) 特公 昭53−13575（ＪＰ，Ｂ１) 特公 昭51−49573（ＪＰ，Ｂ２) ─────────────────────────────────────────────────── ─── Continuation of the front page (56) References JP-A-57-155345 (JP, A) JP-A-54-41216 (JP, A) JP-B-53-13575 (JP, B1) JP-B-51- 49573 (JP, B2)
Claims (2)
％、Mnを0.2〜1.0重量％、Ｐを0.02〜0.8重量％含有
し、さらにＢを0.005〜0.05重量％含有し、残部Feおよ
び不純物からなることを特徴とする加熱再溶融表面硬化
用鋳鉄。1. Containing 2.5 to 4.0% by weight of C, 0.5 to 3.5% by weight of Si, 0.2 to 1.0% by weight of Mn, 0.02 to 0.8% by weight of P, and further containing 0.005 to 0.05% by weight of B, A cast iron for heat remelting and surface hardening, which comprises the balance Fe and impurities.
％、Mnを0.2〜1.0重量％、Ｐを0.02〜0.8重量％含有
し、さらにＢを0.002〜0.02重量％含有しかつMg,Al,Ca,
Zn,Zrのうちの１種以上をＢとの合計で0.02〜0.1重量％
含有し、残部Feおよび不純物からなることを特徴とする
加熱再溶融表面硬化用鋳鉄。2. Containing 2.5 to 4.0% by weight of C, 0.5 to 3.5% by weight of Si, 0.2 to 1.0% by weight of Mn, 0.02 to 0.8% by weight of P, and 0.002 to 0.02% by weight of B, and Mg, Al, Ca,
0.02 to 0.1% by weight in total of one or more of Zn and Zr together with B
A cast iron for heat remelting and surface hardening, which is characterized by containing, and the balance being Fe and impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61054461A JPH0730426B2 (en) | 1986-03-12 | 1986-03-12 | Heat remelting Cast iron for surface hardening |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61054461A JPH0730426B2 (en) | 1986-03-12 | 1986-03-12 | Heat remelting Cast iron for surface hardening |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS62211348A JPS62211348A (en) | 1987-09-17 |
| JPH0730426B2 true JPH0730426B2 (en) | 1995-04-05 |
Family
ID=12971310
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61054461A Expired - Lifetime JPH0730426B2 (en) | 1986-03-12 | 1986-03-12 | Heat remelting Cast iron for surface hardening |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0730426B2 (en) |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5441216A (en) * | 1977-09-07 | 1979-04-02 | Toyo Kogyo Co | Wearrresistant spheroidal iron and slidinggproducts made of cast iron |
| JPS57155345A (en) * | 1981-03-23 | 1982-09-25 | Takaoka Kogyo Kk | Wear resistant cast iron and manufacture thereof |
-
1986
- 1986-03-12 JP JP61054461A patent/JPH0730426B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPS62211348A (en) | 1987-09-17 |
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