JPH0215150A - Nickel-chromium cast iron sintered material containing graphite - Google Patents
Nickel-chromium cast iron sintered material containing graphiteInfo
- Publication number
- JPH0215150A JPH0215150A JP16634188A JP16634188A JPH0215150A JP H0215150 A JPH0215150 A JP H0215150A JP 16634188 A JP16634188 A JP 16634188A JP 16634188 A JP16634188 A JP 16634188A JP H0215150 A JPH0215150 A JP H0215150A
- Authority
- JP
- Japan
- Prior art keywords
- cast iron
- nickel
- chromium cast
- graphite
- sintered material
- 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.)
- Pending
Links
- 239000000463 material Substances 0.000 title claims abstract description 42
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 title claims abstract description 36
- 239000010439 graphite Substances 0.000 title claims abstract description 35
- 229910002804 graphite Inorganic materials 0.000 title claims abstract description 35
- 229910001018 Cast iron Inorganic materials 0.000 title claims abstract description 32
- 229910018487 Ni—Cr Inorganic materials 0.000 title claims abstract description 22
- VNNRSPGTAMTISX-UHFFFAOYSA-N chromium nickel Chemical compound [Cr].[Ni] VNNRSPGTAMTISX-UHFFFAOYSA-N 0.000 title claims abstract description 22
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 22
- 239000011651 chromium Substances 0.000 claims abstract description 21
- 238000010438 heat treatment Methods 0.000 claims abstract description 18
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 15
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 8
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 6
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 5
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 5
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 14
- 238000005087 graphitization Methods 0.000 claims description 11
- 238000000137 annealing Methods 0.000 claims description 7
- 239000000203 mixture Substances 0.000 claims description 4
- 239000000126 substance Substances 0.000 claims description 2
- 229910052742 iron Inorganic materials 0.000 claims 1
- 239000000843 powder Substances 0.000 abstract description 8
- 229910052802 copper Inorganic materials 0.000 abstract description 6
- 229910052751 metal Inorganic materials 0.000 abstract description 4
- 238000000034 method Methods 0.000 abstract description 4
- 239000002184 metal Substances 0.000 abstract description 3
- 238000009689 gas atomisation Methods 0.000 abstract description 2
- 238000010298 pulverizing process Methods 0.000 abstract description 2
- 238000007670 refining Methods 0.000 abstract description 2
- 238000000151 deposition Methods 0.000 abstract 1
- 238000001556 precipitation Methods 0.000 description 11
- 238000005096 rolling process Methods 0.000 description 11
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 8
- 229910001566 austenite Inorganic materials 0.000 description 8
- 230000000694 effects Effects 0.000 description 6
- 230000005496 eutectics Effects 0.000 description 6
- 239000011159 matrix material Substances 0.000 description 6
- 150000001247 metal acetylides Chemical class 0.000 description 6
- 238000009694 cold isostatic pressing Methods 0.000 description 4
- 238000002425 crystallisation Methods 0.000 description 4
- 230000008025 crystallization Effects 0.000 description 4
- 238000005245 sintering Methods 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 229910000831 Steel Inorganic materials 0.000 description 3
- 230000000717 retained effect Effects 0.000 description 3
- 239000010959 steel Substances 0.000 description 3
- UFGZSIPAQKLCGR-UHFFFAOYSA-N chromium carbide Chemical compound [Cr]#C[Cr]C#[Cr] UFGZSIPAQKLCGR-UHFFFAOYSA-N 0.000 description 2
- 239000002131 composite material Substances 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 229910001562 pearlite Inorganic materials 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 229910003470 tongbaite Inorganic materials 0.000 description 2
- 206010013786 Dry skin Diseases 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000000669 biting effect Effects 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 238000005056 compaction Methods 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000001513 hot isostatic pressing Methods 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 230000002093 peripheral effect Effects 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000007788 roughening Methods 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 238000011282 treatment Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 238000009692 water atomization Methods 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
(産業上の利用分野)
本発明は、主としてロール材として使用される耐摩耗性
、耐焼付性および耐スリンプ性に優れたニッケルクロム
鋳鉄材に関する。DETAILED DESCRIPTION OF THE INVENTION (Industrial Application Field) The present invention relates to a nickel-chromium cast iron material that is mainly used as a roll material and has excellent wear resistance, seizure resistance, and slip resistance.
(従来の技術)
従来、ホットストリップミル仕上スタンド前段ワークロ
ールや同ミル粗スタンドワークロールとして、主にアダ
マイトロールが使用されていたが、近年、耐摩耗性に優
れる高クロムロール材を圧延使用層に適用した高クロム
ロールが普及している。(Prior technology) In the past, Adamite rolls were mainly used as work rolls in the front stage of hot strip mill finishing stands and rough stand work rolls in the same mills, but in recent years, high chromium roll materials with excellent wear resistance have been used for rolling. High chrome rolls applied in layers are popular.
しかし、高クロムロール材は、熱伝導率が低く焼付が生
じ易いという問題があった。However, high chromium roll materials have a problem in that they have low thermal conductivity and are prone to seizure.
そこで、本出願人は、特公昭61−16415号および
特公昭61−16336号において開示した通り、高ク
ロム組織中に黒鉛を晶出さゼ、耐焼付性を著しく改善し
た黒鉛晶出高クロム鋳鉄材を開発した。Therefore, as disclosed in Japanese Patent Publications No. 61-16415 and No. 61-16336, the present applicant has developed a graphite-crystallized high-chromium cast iron material with significantly improved seizure resistance by crystallizing graphite in a high-chromium structure. was developed.
この黒鉛晶出高クロム鋳鉄材を圧延使用層として有する
圧延用ロールによって、従来、焼付が生じ易いとされて
いるステンレス鋼等の特殊鋼を圧延したところ、焼付の
発生も生じず、良好な結果が得られた。When special steel such as stainless steel, which is conventionally thought to be susceptible to seizure, was rolled using a rolling roll having this graphite crystallized high chromium cast iron material as a rolling layer, no seizure occurred and good results were obtained. was gotten.
(発明が解決しようとする課題)
しかしながら、前記黒鉛晶出高クロム鋳鉄材は、高硬度
の共晶クロム炭化物を多量に有するため、圧延の際にス
リップが生じ易く、このため噛め込み性に劣るという問
題があり、生産性の低−ドを余儀無くされていた。(Problems to be Solved by the Invention) However, since the graphite-crystallized high-chromium cast iron material has a large amount of high-hardness eutectic chromium carbide, it tends to slip during rolling, and therefore has poor biting properties. This problem necessitated low productivity.
本発明はかかる問題点に鑑みなされたもので、耐摩耗性
および面]焼付性を確保しつつ、耐スリップ性をも改善
した鋳鉄材を提供することを目的とする。The present invention was made in view of such problems, and an object of the present invention is to provide a cast iron material that has improved slip resistance while ensuring wear resistance and surface seizure resistance.
(課題を解決するための手段)
上記目的を達成するためになされた本発明の鋳鉄材は、
化学組成が重量%で、
C:1.0〜1.9%、 Cr : 2.0〜4.5
%Si : 1.5〜4.0%、 Mo : 0.
4〜5.0%Mn : 0.5〜1.5%、 Ni:
13 %以下p:oyt%以下、 Cu :
0.5〜4.0%S : 0.08%以下、 Ni−
1−Cu : 4.0〜15.0%残部実質的にFeか
らなるニッケルクロム鋳鉄粉末の焼結材であって、黒鉛
化焼なまし熱処理により組織中に黒鉛が析出してなるこ
とを発明の構成とするものである。(Means for Solving the Problems) The cast iron material of the present invention, which has been made to achieve the above object, has the following features:
Chemical composition in weight%: C: 1.0-1.9%, Cr: 2.0-4.5
%Si: 1.5-4.0%, Mo: 0.
4-5.0%Mn: 0.5-1.5%, Ni:
13% or less p:oyt% or less, Cu:
0.5-4.0% S: 0.08% or less, Ni-
1-Cu: A sintered material of nickel-chromium cast iron powder consisting of 4.0 to 15.0% and the remainder substantially Fe, which is an invention in which graphite is precipitated in the structure by graphitization annealing heat treatment. The structure is as follows.
(作 用)
まず、本発明に係るニッケルクロム鋳鉄粉末材を構成す
るニッケルクロム鋳鉄粉末の成分限定理由について説明
する。以下、単位は重量%である。(Function) First, the reason for limiting the components of the nickel-chromium cast iron powder constituting the nickel-chromium cast iron powder material according to the present invention will be explained. Hereinafter, the unit is weight %.
C:1..0〜1.9%
CはSl、旧の黒鉛化作用によって焼結後の熱処理によ
り黒鉛として析出させるために添加する。C:1. .. 0 to 1.9% C is added to precipitate as graphite by heat treatment after sintering due to the former graphitization effect of Sl.
本発明におりるSi、 Niの成分範囲においては、1
゜0%未満では黒鉛の析出が困難である。一方、1゜9
%を越えて含有されると粉末中の共晶炭化物が多くなり
、耐スリップ性が劣化する。In the component range of Si and Ni in the present invention, 1
If it is less than 0%, it is difficult to precipitate graphite. On the other hand, 1°9
If the content exceeds %, the amount of eutectic carbides in the powder will increase and the slip resistance will deteriorate.
Si:1.5〜4.0%
Siはニッケルクロム鋳鉄粉末を焼結後に熱処理して黒
鉛を析出させるために必要である。本発明の場合、基地
の強度を高めるためにCrが2.0〜4゜5%、Moが
0.4〜5.0%含有されるので、1.5%未満では黒
鉛析出が困難となり、一方4.0%を越えると黒鉛析出
が過多となり、耐摩耗性および機械的性質が劣化する。Si: 1.5-4.0% Si is necessary for precipitating graphite by heat-treating the nickel-chromium cast iron powder after sintering. In the case of the present invention, 2.0 to 4.5% of Cr and 0.4 to 5.0% of Mo are contained in order to increase the strength of the base, so if it is less than 1.5%, graphite precipitation will be difficult. On the other hand, if it exceeds 4.0%, graphite precipitation will be excessive and wear resistance and mechanical properties will deteriorate.
Mn : 0.5〜1.5%
Mnは微細象、冷粉未作成前段階の溶湯の脱酸のために
Siと共に積極的に添加される。0.5%未満では脱酸
作用が不足し、一方1.5%を越えると機械的性質、特
に靭性の劣化が著しく現れる。Mn: 0.5-1.5% Mn is actively added together with Si to deoxidize the molten metal before forming fine grains and cold powder. If it is less than 0.5%, the deoxidizing effect will be insufficient, while if it exceeds 1.5%, mechanical properties, particularly toughness, will deteriorate significantly.
P:0.1%以下
Pは材質を脆くするため少ないほど望ましく、0.1%
以下とする。P: 0.1% or less P makes the material brittle, so it is desirable to have less P, and 0.1%
The following shall apply.
S:0.08%以下
SもPと同様の理由により少ないほど望ましく0.08
%以下とする。S: 0.08% or less For the same reason as P, the less S is, the more desirable it is 0.08
% or less.
Cr : 2.0〜4.5%
CrはCと結合してCr炭化物を形成すると共に、基地
中にも一部固溶して基地の強化に寄与するが、本発明の
場合は主に後者の目的で添加される。Cr: 2.0 to 4.5% Cr combines with C to form Cr carbide, and also partially dissolves in the base and contributes to strengthening the base, but in the case of the present invention, the latter is mainly used. It is added for the purpose of
2.0%未満では基地中に固溶されるCr量が少なく、
基地を強化することが困難となる。一方、4.5%を越
えると粉末中の炭化物の晶出が過多となり、耐スリップ
性の向上を阻害すると共に、炭化物が網目状に晶出する
ため、耐肌荒性の点で問題となる。If it is less than 2.0%, the amount of Cr dissolved in the base is small;
It becomes difficult to strengthen the base. On the other hand, if it exceeds 4.5%, excessive crystallization of carbides in the powder will inhibit the improvement of slip resistance, and the carbides will crystallize in a network shape, causing problems in terms of roughness resistance. .
Mo : 0.4−5.0%
Moは黒鉛の析出を抑制する元素であるが、炭化物中に
入り込んで炭化物の硬度を高めると共に、基地中に固溶
して焼戻し軟化抵抗を向上させるのに有効である。本発
明においては炭化物量がごく少量であるので主に基地組
織の改善を目的として積極的に添加される。0.4%未
満では基地組織の有効な改善を図ることができない。一
方、1.0%を越えると黒鉛の析出が減少するが、黒鉛
析出抑制作用は顕著には増大せず、基地の強化が促進さ
れる。このため基地部分の耐焼付性が向」−シ、若干黒
鉛量が減少しても耐焼付性の劣化を招来せず、むしろ硬
度向」二によって優れた耐摩耗性が得られる。しかし、
5%を越えると黒鉛の析出が著しく抑制されて耐焼付性
が劣化する。尚、基地の強化のほかに、炭化物中に入り
込んで、炭化物の硬度を向上させるには、Moを2.0
%以上含有させることが好ましい。Mo: 0.4-5.0% Mo is an element that suppresses the precipitation of graphite, but it also penetrates into the carbide and increases the hardness of the carbide, and dissolves in the matrix to improve the tempering softening resistance. It is valid. In the present invention, since the amount of carbide is very small, it is actively added mainly for the purpose of improving the matrix structure. If it is less than 0.4%, it is not possible to effectively improve the base organization. On the other hand, when it exceeds 1.0%, graphite precipitation is reduced, but the graphite precipitation suppressing effect is not significantly increased, and strengthening of the matrix is promoted. For this reason, the seizure resistance of the base portion is improved, and even if the amount of graphite is slightly reduced, the seizure resistance does not deteriorate, but rather, excellent wear resistance can be obtained by increasing the hardness. but,
When it exceeds 5%, precipitation of graphite is significantly suppressed and seizure resistance deteriorates. In addition to strengthening the base, in order to penetrate into the carbide and improve the hardness of the carbide, it is necessary to add Mo to 2.0
% or more is preferable.
Ni : 13%以下 Niは黒鉛析出と基地組織の改良の目的で添加される。Ni: 13% or less Ni is added for the purpose of graphite precipitation and improvement of the matrix structure.
13%を越えて含有すると、残留オーステナイトの増加
、安定化傾向が増し、後の熱処理によっても残留オース
テナ(l・の分解が困難となる。If the content exceeds 13%, the residual austenite tends to increase and stabilize, and it becomes difficult to decompose the residual austenite (l·) even during subsequent heat treatment.
このため、熱間で使用した場合、使用部材表面のオース
テナイトが分解し、膨張するため、耐肌荒性が劣化する
。面、Niの添加下限量は、後述のCuとの合計量で決
定される。For this reason, when used hot, the austenite on the surface of the used member decomposes and expands, resulting in poor skin roughness resistance. The lower limit of the addition amount of Ni is determined by the total amount of Cu, which will be described later.
Cu : 0.5〜4.0%
Cuは黒鉛化を促進すると共に、パーライト強化や熱的
安定化に資する。黒鉛化効果についてはNiとほぼ同等
である。0.5%未満では有効な作用を奏せず、一方4
.0%を越えると金属Cuが析出し、機械的性質が劣化
する。Cu: 0.5 to 4.0% Cu promotes graphitization and contributes to pearlite reinforcement and thermal stabilization. The graphitization effect is almost the same as Ni. If it is less than 0.5%, it will not have an effective effect;
.. If it exceeds 0%, metal Cu will precipitate and the mechanical properties will deteriorate.
Cu+Ni : 4.0〜15%
Cu、:!−Niは黒鉛化促進効果としてはほぼ同等で
あり、その合計量が4.0%未満では黒鉛の析出が困難
となる。一方、15%を越えると黒鉛析出が過多となり
、耐摩耗性が劣化する。尚、N1栄独で黒鉛析出を図る
とすると、Ni含有量は4.0〜15%に規定されるが
、本発明ではN1含有量を13%以下に押えているため
、残留オーステナイトの減少、ひいては耐肌荒性の向上
を図るごとができる点で有利である。また、高価なNi
の使用を押えることができ、経済性の面でも有利である
。Cu+Ni: 4.0-15% Cu, :! -Ni has almost the same graphitization promoting effect, and if the total amount is less than 4.0%, precipitation of graphite becomes difficult. On the other hand, if it exceeds 15%, graphite precipitation will be excessive and wear resistance will deteriorate. In addition, if graphite precipitation is attempted using N1 Eidoku, the Ni content is specified to be 4.0 to 15%, but in the present invention, since the N1 content is suppressed to 13% or less, the amount of retained austenite is reduced, Furthermore, it is advantageous in that the roughening resistance can be improved. Also, expensive Ni
It is also advantageous from an economic point of view.
本発明の黒鉛を有する焼結材を構成するニッケルクロム
鋳鉄粉末は以上の成分のばか残部実質的にFeで形成さ
れるが、材質特性を向上させるためにFeの一部に代え
て下記のNb、 Vを必要に応して含有させることがで
きる。The nickel-chromium cast iron powder constituting the graphite-containing sintered material of the present invention is made of substantially Fe, but in order to improve the material properties, the following Nb is substituted for a part of the Fe. , V can be contained as necessary.
すなわち、Nb、 Vは共に組織の微細化に効果があり
、各々単独又は複合で、1.0%以下含有することがで
きる。1.0%を越えると、炭素と結びついてVC,N
bC,Nb2C等の炭化物を形成し、黒鉛の晶出を妨げ
る。また、コスト高の要因となる。That is, both Nb and V are effective in refining the structure, and each can be contained alone or in combination at 1.0% or less. If it exceeds 1.0%, it will combine with carbon and form VC, N.
Forms carbides such as bC and Nb2C and prevents crystallization of graphite. Moreover, it becomes a factor of high cost.
前記ニッケルクロム鋳鉄粉末は、通常、所期成分のニッ
ケルクロム鋳鉄粉末を溶製し、これをガスアトマイス法
や水アトマイズ法によって微粉化、急冷凝固して製造さ
れる。使用する粉末粒径は、通常、100〜250メツ
シユ程度である。粉末は急冷凝固しているため、結晶組
織は微細化された状態となっている。かかる微細組織は
従来の溶製材では得られないものである。The nickel-chromium cast iron powder is usually produced by melting nickel-chromium cast iron powder having the desired components, pulverizing it by a gas atomization method or water atomization method, and rapidly solidifying it. The particle size of the powder used is usually about 100 to 250 mesh. Since the powder is rapidly solidified, the crystal structure is in a fine state. Such a fine structure cannot be obtained with conventional melt-molded materials.
前記ニッケルクロム鋳鉄粉末は所期の形状に圧粉成形さ
れ焼結される。この場合、圧粉成形には一軸圧縮や冷間
等方加圧(以下、CIPという。)を適用することがで
き、また加圧成形と焼結とが同時に行われる熱間等方加
圧(以下、HIPという。)成形を適用することができ
る。The nickel chromium cast iron powder is compacted into a desired shape and sintered. In this case, uniaxial compression or cold isostatic pressing (hereinafter referred to as CIP) can be applied to compaction, or hot isostatic pressing (hereinafter referred to as CIP) in which pressing and sintering are performed simultaneously Hereinafter referred to as HIP) molding can be applied.
前記ニッケルクロム鋳鉄粉末の焼結材は、焼結後、組織
中に黒鉛を析出させるための黒鉛化焼なまし熱処理に供
される。この熱処理は、焼結材を950〜1200°C
に加熱し、数時間保持することによって行われる。これ
により、焼結材中の遊離炭化物は分解し、分解によって
生成されたCが微細黒鉛となって焼結材中に均一に分散
析出する。After sintering, the sintered material of the nickel-chromium cast iron powder is subjected to graphitization annealing heat treatment to precipitate graphite in the structure. This heat treatment heats the sintered material to 950-1200°C.
This is done by heating and holding for several hours. As a result, free carbides in the sintered material are decomposed, and C generated by the decomposition becomes fine graphite, which is uniformly dispersed and precipitated in the sintered material.
尚、Cr含有量が高い鋳鉄材質においては、通常、高温
で長時間保持しても黒鉛は析出しない。本発明の場合、
Si、 NiおよびCuを多量に含有した特定の成分を
選定しているので、熱処理によって組織中に微細黒鉛を
均一・に分散析出させることができる。Note that in cast iron materials with a high Cr content, graphite usually does not precipitate even if the material is held at high temperatures for a long time. In the case of the present invention,
Since a specific component containing a large amount of Si, Ni, and Cu is selected, fine graphite can be uniformly dispersed and precipitated in the structure by heat treatment.
上記黒鉛化焼なまし熱処理によって得られた本発明の焼
結材は、ニッケルクロム鋳鉄粉末中のC含有量を可及的
に押えているので、共晶炭化物がほとんど生成せず、耐
スリップ性を著しく改善することができる。The sintered material of the present invention obtained by the above graphitization annealing heat treatment suppresses the C content in the nickel chromium cast iron powder as much as possible, so almost no eutectic carbide is generated, and the material has excellent slip resistance. can be significantly improved.
尚、ここにいう共晶炭化物とは、M、C型のセメンタイ
トにCrが入り込んだものであり、従来の高クロム材や
黒鉛晶出高クロム材において晶出するM’+C3型のク
ロム炭化物とは、炭化物の構造、晶出形態、晶出量が異
なるものである。In addition, the eutectic carbide mentioned here refers to M and C type cementite in which Cr has entered, and is different from the M'+C3 type chromium carbide that crystallizes in conventional high chromium materials and graphite crystallized high chromium materials. are different in carbide structure, crystallization form, and crystallization amount.
一方、特にNi、 Cr、 Moの所定量の添加により
、基地組織が強化され、かつ急冷凝固粉末の使用により
結晶組織が微細化されているので、共晶炭化物の減少に
も拘らず、耐摩耗性の低下を防止することができ、機械
的強度が向上し、強靭性が具備されるものとなる。On the other hand, the base structure is strengthened by adding a certain amount of Ni, Cr, and Mo, and the crystal structure is refined by using rapidly solidified powder, so the wear resistance is improved despite the reduction of eutectic carbides. It is possible to prevent a decrease in properties, improve mechanical strength, and provide toughness.
更に、黒鉛化焼なまし熱処理により、組織中に微細黒鉛
が均一に分散して生成し、耐焼付性が確保される。Furthermore, the graphitization annealing heat treatment produces fine graphite uniformly dispersed in the structure, ensuring seizure resistance.
尚、黒鉛析出後の焼結材の基地は、焼入れ焼戻しにより
焼戻しマルテンサイトやオーステンバーによりヘーナイ
トとされたり、適宜の冷却速度によってパーライト、フ
ェライト組織に調整される。The base of the sintered material after graphite precipitation is quenched and tempered to form tempered martensite or austenbur to become haenite, or adjusted to a pearlite or ferrite structure by an appropriate cooling rate.
本発明の黒鉛を有するニッケルクロム鋳鉄焼結材は、圧
延用複合ロールの圧延使用層たる外層材として好適なも
のであるが、耐摩耗性や耐焼付性が共に要求される種々
の用途(例えば、ガイドロラ、テーブルローラ等の圧延
材周辺のローラ類、熱間塑性加工用部品)に適用される
。尚、複合ロールの外層材として本発明材を使用する場
合は、鋼材等で形成されたロール軸の外周面に前記ニン
ケルクロム鋳鉄粉末によって外層を成形し、ロール軸ご
と焼結処理を行えばよい。The nickel-chromium cast iron sintered material containing graphite of the present invention is suitable as an outer layer material, which is the rolling layer of a rolling composite roll, but it is also suitable for various uses that require both wear resistance and seizure resistance (e.g. , guide rollers, table rollers, and other rollers around rolled materials, and hot plastic processing parts). When using the material of the present invention as the outer layer material of a composite roll, the outer layer may be formed on the outer circumferential surface of a roll shaft made of steel or the like using the Ninkel chrome cast iron powder, and the roll shaft may be sintered together.
(実施例)
丸棒仕上圧延スタンド出口ガイドローラの製造実施例
(1)下記組成の高クロム鋳鉄粉末(粒径140メツシ
ユアンダー)をCIP (圧力5.5 kgf/cm2
)で成形し、外径170×内径60×幅105mmの成
形筒体を得た。(Example) Manufacturing example of a round bar finishing rolling stand exit guide roller (1) High chromium cast iron powder (particle size 140 mesh under) with the following composition was subjected to CIP (pressure 5.5 kgf/cm2)
) to obtain a molded cylinder having an outer diameter of 170 mm, an inner diameter of 60 mm, and a width of 105 mm.
・粉末組成(単位重量%、残部実質的Fe)C:1.6
0 %、 Si : 3.01%、 Mn :
0.50 %P : 0.004%、 S:0
.007 %、Ni ・ 7.03 %Cr :
2.98 %、 Mo : 1.68%、 Cu
: 2.22 %(2)前記成形筒体を加圧25
0 kgf/cm2、温度】150°CでHIP処理し
、焼結筒体を得た。該筒体を製品寸法に対し加工代を1
mm(iけるように鉗加工し、下記の■〜■の熱処理を
施した。・Powder composition (unit weight %, remainder substantial Fe) C: 1.6
0%, Si: 3.01%, Mn:
0.50%P: 0.004%, S:0
.. 007%, Ni/7.03%Cr:
2.98%, Mo: 1.68%, Cu
: 2.22% (2) Pressure the molded cylinder 25%
0 kgf/cm2, temperature] HIP treatment was performed at 150°C to obtain a sintered cylinder. The machining allowance for the cylindrical body is 1 for the product size.
It was processed with a forceps so that it could be cut into mm (i), and was subjected to the following heat treatments.
■ 黒鉛化焼なまし熱処理
1100°CX511r 塩浴中で保持■ 基地の
ヘーナイト化熱処理
■の処理俊速やかに500°Cの塩浴中へ急冷し、5時
間保持後、空中放冷し常温まで冷却した。■ Graphitization annealing heat treatment 1,100°C did.
■ 残留オーステナイトの変態化熱処理530°Cに加
熱し10時間保持した後、常温まで冷却した。この処理
を2回繰り返して、残留オーステナイトの低減を図った
。(2) Transformation heat treatment of retained austenite After heating to 530°C and holding for 10 hours, it was cooled to room temperature. This process was repeated twice to reduce residual austenite.
(3)熱処理後、仕上加工を行い、第1図の製品ローラ
を得た。該ローラの組織は、微細均一に析出した黒鉛と
基地組織およびごく少量の共晶力ハイドから成っており
、基地組織は焼戻しマルテンサイトであり、残留オース
テナイトはほとんど認められなかった。硬度はHs87
〜89であった。(3) After heat treatment, finishing processing was performed to obtain the product roller shown in FIG. The structure of the roller was composed of finely and uniformly precipitated graphite, a matrix structure, and a very small amount of eutectic hide.The matrix structure was tempered martensite, and almost no residual austenite was observed. Hardness is Hs87
It was ~89.
(4)上記ローラを32φ丸鋼仕上圧延機出口側に設置
し、実際に使用した。出口ガイドローラは、圧延材が当
接しないときは回転せず、圧延機から出てきた圧延材が
その周面に当接することによって回転が誘導されるもの
である。このため、かみ込み時にローラに焼き付きが生
じ易く、従来チルト鋳鉄製ローラが使用されていた。こ
の場合、耐摩耗性が悪く約300 Ton当り1回改削
して使用していたが、本実施例では1回改削当りの圧延
量が13倍に向上した。尚、使用に際しては、焼付きや
欠は落ち、あるいはクランクは全く生じなかった。(4) The above roller was installed on the exit side of a 32φ round steel finishing rolling mill and was actually used. The exit guide roller does not rotate when the rolled material does not come into contact with it, and is guided to rotate when the rolled material coming out of the rolling mill comes into contact with its peripheral surface. For this reason, rollers are likely to seize when caught, and conventionally tilted cast iron rollers have been used. In this case, the wear resistance was poor and the rolling stock had to be revised once per approximately 300 tons, but in this example, the rolling amount per one revision was improved by 13 times. Incidentally, during use, the seizure and chipping disappeared, and no cranking occurred at all.
(発明の効果)
以上説明し、た通り、本発明の黒鉛を有するニッケルク
ロム鋳鉄焼結材は、C:1.0〜1.9%の所定成分の
ニンケルクロム鋳鉄粉末によって焼結されたものである
ので、カーバイドがほとんど生成せず、耐スリップ性が
良好である。また、基地の強化と相まって、組織が微細
化されており、これによって耐摩耗性の向上が図られ、
しかも黒鉛化焼なまし熱処理によって焼結材中に微細黒
鉛を均一に分散析出したものとなり、耐焼付が確保され
る。更に、N+含有量の減少により、残留オーステナイ
トの低減を図ることができ、経済性にも優れている。(Effects of the Invention) As explained above, the sintered nickel-chromium cast iron material having graphite of the present invention is sintered with nickel-chromium cast iron powder having a predetermined component of C: 1.0 to 1.9%. Because of this, almost no carbide is produced and the slip resistance is good. In addition, in conjunction with the strengthening of the base, the structure is refined, which improves wear resistance.
Moreover, the graphitization annealing heat treatment results in fine graphite being uniformly dispersed and precipitated in the sintered material, ensuring seizure resistance. Furthermore, by reducing the N+ content, it is possible to reduce retained austenite, which is also excellent in economical efficiency.
第1図は実施例に係るローラの半断面図を示す。 FIG. 1 shows a half-sectional view of a roller according to an embodiment.
Claims (1)
1.5〜4.0%、Mo:0.4〜5.0%Mn:0.
5〜1.5%、Ni:13%以下P:0.1%以下、C
u:0.5〜4.0%S:0.08%以下、Ni+Cu
:4.0〜15.0%残部実質的にFeからなるニッケ
ルクロム鋳鉄粉末の焼結材であって、黒鉛化焼なまし熱
処理により組織中に黒鉛が析出してなることを特徴とす
る黒鉛を有するニッケルクロム鋳鉄焼結材。(1) Chemical composition in weight%: C: 1.0 to 1.9%, Cr: 2.0 to 4.5%, Si:
1.5-4.0%, Mo: 0.4-5.0% Mn: 0.
5-1.5%, Ni: 13% or less, P: 0.1% or less, C
u: 0.5-4.0% S: 0.08% or less, Ni+Cu
: 4.0 to 15.0% A sintered material of nickel-chromium cast iron powder with the remainder essentially consisting of Fe, which is characterized by graphite precipitated in its structure by graphitization annealing heat treatment. Nickel chromium cast iron sintered material with.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP16634188A JPH0215150A (en) | 1988-07-04 | 1988-07-04 | Nickel-chromium cast iron sintered material containing graphite |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP16634188A JPH0215150A (en) | 1988-07-04 | 1988-07-04 | Nickel-chromium cast iron sintered material containing graphite |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH0215150A true JPH0215150A (en) | 1990-01-18 |
Family
ID=15829574
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP16634188A Pending JPH0215150A (en) | 1988-07-04 | 1988-07-04 | Nickel-chromium cast iron sintered material containing graphite |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH0215150A (en) |
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US6358298B1 (en) | 1999-07-30 | 2002-03-19 | Quebec Metal Powders Limited | Iron-graphite composite powders and sintered articles produced therefrom |
EP1391529A1 (en) * | 2002-08-16 | 2004-02-25 | Winsert Technologies, Inc. | Wear and corrosion resistant austenitic iron base alloy |
US7611590B2 (en) | 2004-07-08 | 2009-11-03 | Alloy Technology Solutions, Inc. | Wear resistant alloy for valve seat insert used in internal combustion engines |
CN102154584A (en) * | 2011-02-23 | 2011-08-17 | 周海龙 | Novel low-MnCrNi cast steel material and preparation method thereof |
CN104278215A (en) * | 2014-09-22 | 2015-01-14 | 安徽喜洋洋儿童用品有限公司 | Special wear-resistant steel tube for baby stroller |
CN104278214A (en) * | 2014-09-22 | 2015-01-14 | 安徽喜洋洋儿童用品有限公司 | Wear-resistant steel pipe for baby stroller |
JP2019505674A (en) * | 2015-12-24 | 2019-02-28 | ロバルマ, ソシエダッド アノニマRovalma, S.A. | Long-term durable high performance steel for structural, mechanical and tool applications |
-
1988
- 1988-07-04 JP JP16634188A patent/JPH0215150A/en active Pending
Cited By (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US6358298B1 (en) | 1999-07-30 | 2002-03-19 | Quebec Metal Powders Limited | Iron-graphite composite powders and sintered articles produced therefrom |
EP1391529A1 (en) * | 2002-08-16 | 2004-02-25 | Winsert Technologies, Inc. | Wear and corrosion resistant austenitic iron base alloy |
US6866816B2 (en) | 2002-08-16 | 2005-03-15 | Alloy Technology Solutions, Inc. | Wear and corrosion resistant austenitic iron base alloy |
US7611590B2 (en) | 2004-07-08 | 2009-11-03 | Alloy Technology Solutions, Inc. | Wear resistant alloy for valve seat insert used in internal combustion engines |
CN102154584A (en) * | 2011-02-23 | 2011-08-17 | 周海龙 | Novel low-MnCrNi cast steel material and preparation method thereof |
CN104278215A (en) * | 2014-09-22 | 2015-01-14 | 安徽喜洋洋儿童用品有限公司 | Special wear-resistant steel tube for baby stroller |
CN104278214A (en) * | 2014-09-22 | 2015-01-14 | 安徽喜洋洋儿童用品有限公司 | Wear-resistant steel pipe for baby stroller |
JP2019505674A (en) * | 2015-12-24 | 2019-02-28 | ロバルマ, ソシエダッド アノニマRovalma, S.A. | Long-term durable high performance steel for structural, mechanical and tool applications |
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