JPS60501958A - Wear-resistant white cast iron - Google Patents
Wear-resistant white cast ironInfo
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- JPS60501958A JPS60501958A JP58503752A JP50375283A JPS60501958A JP S60501958 A JPS60501958 A JP S60501958A JP 58503752 A JP58503752 A JP 58503752A JP 50375283 A JP50375283 A JP 50375283A JP S60501958 A JPS60501958 A JP S60501958A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C37/00—Cast-iron alloys
Abstract
(57)【要約】本公報は電子出願前の出願データであるため要約のデータは記録されません。 (57) [Summary] This bulletin contains application data before electronic filing, so abstract data is not recorded.
Description
【発明の詳細な説明】 耐摩耗性白鋳鉄 技術分野 この発明は、鋳鉄に関し、特に引張強さの顕著な増加と共にしん性および耐摩耗 性の優れた鋳鉄に関する。さらに詳しくは、本発明は、炭化物の形態の改良によ って所望の耐摩耗性を維持しながら優れたしん性、延性および引張強さを有する 新しい白鋳鉄の組成物および該鋳鉄の製造法に関する。[Detailed description of the invention] Wear-resistant white cast iron Technical field This invention relates to cast iron, and in particular to improved toughness and wear resistance with a significant increase in tensile strength. Concerning cast iron with excellent properties. More specifically, the present invention provides improved carbide morphology. has excellent toughness, ductility and tensile strength while maintaining the desired wear resistance. The present invention relates to a new white cast iron composition and a method for producing the cast iron.
背景技術 合金白鋳鉄は、一般にＬ５％以上の炭素含量で形成される高耐摩耗性材料であっ て、他の金属（普通はクロム）と合金化され、炭素と結合してＭＸＣ’Ｙのよう なＦｅ−ｃｒ炭化物の化合物を生成する可能性のあることがよく知られている。Background technology Alloyed white cast iron is a highly wear-resistant material generally formed with a carbon content of L5% or more. is alloyed with another metal (usually chromium) and combined with carbon to form MXC’Y. It is well known that Fe-Cr carbide compounds can be produced.
多くの場合に、合金化されない鋳鉄固有の耐摩耗性は所期の用途を満たすのに十 分であるから、使用者に問題を持ち出さない。しかしながら、産業機械を形成す る鋳鉄が特殊な摩耗を受ける場合、鋳鉄固有の機械的性質は所望のものから著し く離れる。In many cases, the inherent wear resistance of unalloyed cast iron is sufficient to meet the intended application. Since it is a matter of minutes, do not bring up the problem with the user. However, forming industrial machinery When cast iron is subjected to special wear, the inherent mechanical properties of the cast iron may be significantly less than desired. Leave far away.
鋳鉄材料が受ける摩耗は幾つかに分類されることは良く知られている。第１のえ ぐり（またはみぞ切シ）摩耗においては、研摩性粗粒子が鋳鉄の加工表面に侵入 して高速で金属を除去する。この種の摩耗の典型的な経験、例えば地ならし装置 、ハンマミル作業およびショークラッシャーにおいては、鋳鉄に有害な影響を与 えることが知られているところの金属を除去する過酷な衝撃荷重を伴う。It is well known that the wear that cast iron materials undergo can be classified into several types. 1st row In bore (or groove) wear, coarse abrasive particles penetrate the machined surface of cast iron. to remove metal at high speed. Typical experience with this type of wear, e.g. earthmoving equipment , hammer mill operations and show crushers have a detrimental effect on cast iron. It involves severe impact loads that remove metal where it is known to cause damage.
しばしば高応力摩耗と呼ばれる第２の摩耗（例えば、採鉱作業において道側する ）においては、研摩粒子は移動する金属表面の粉砕作用下で粉砕される。Secondary wear, often referred to as high stress wear (e.g. roadside wear in mining operations) ), the abrasive particles are ground under the grinding action of a moving metal surface.
研摩ロール、粉砕ロールやミル・ライナに使用さ肛る鋳物に典型的に生じるこの 種の摩耗過程に含量れる応力レベルは、従来の鋳鉄の応力性能をしばしば越えて 装置の破損をもたらす。This typically occurs in castings used for abrasive rolls, grinding rolls and mill liners. The stress levels involved in the wear process of seeds often exceed the stress performance of traditional cast iron. resulting in damage to the equipment.
第うのカテゴリーの摩耗である低応力摩耗または侵食においては、装置の鋳鉄表 面が受ける研摩作用は過酷な応力状態でばないが、高耐摩耗性が要求される。In the second category of wear, low stress wear or erosion, the cast iron surface of the equipment Although the abrasive action to which the surface is subjected does not result in severe stress conditions, high wear resistance is required.
過酷な衝撃荷゛重を伴うえぐり（またはみぞ切シ）摩耗は、鋳鉄が典型的に過去 において特質的にもっていなかったしん性を必要とする。高い塑性およびじん性 をもったマンガン鋼はこの種の摩耗を受ける材料に対する過酷な耐衝撃要求を′ ａ食すことができた。しかしながら、その硬度および耐摩耗性は一般に、回転式 ボールミルのような広範囲の粉砕過程での高応力研磨作用における析めて高い摩 耗速度を防ぐには不適当であることがわかった。この高応力作用においては、ク ロム・モリブデン鋼および合金白銑がじん性の必要条件および必要な耐摩耗性の 組合せに応じて種々の装置に使用できる。低応力作用を含む前記第うのカテゴリ ーの摩耗においては、モリブデンまたはニッケルを添加、または添加しないクロ ム−鉄合金が炭化物全分散したＴ１しいマルテンサイトのマトリックスをもって 使用される。Gouge (or grooving) wear associated with severe impact loads is typically avoided by cast iron. It requires toughness, which was not characteristically possessed. High plasticity and toughness Manganese steels with I was able to eat a meal. However, its hardness and wear resistance are generally High friction during high stress polishing action in wide range grinding processes such as ball mills. It was found to be inadequate to prevent the rate of wear and tear. In this high stress action, the Rom-molybdenum steels and white alloy alloys meet the toughness requirements and the required wear resistance. Can be used in various devices depending on the combination. The above-mentioned category includes low-stress effects. In terms of wear, chlorine with or without molybdenum or nickel Mu-iron alloy has a matrix of T1 martensite with fully dispersed carbides. used.
摩耗のカテゴリーおよびこれらの摩耗のカテゴリーにおける必要条件を満たすた めに利用する金属の種類に関する産業の知識を考慮すると、当業者はジレンマに 落ち入る。少なくとも最初の２つのカテゴリーの摩耗を受ける装置を動かすだめ には、最適の耐摩耗性およびこれらの摩耗に特命的な過酷な衝撃および応力条件 に耐える十分なしん性が要求される。wear categories and to meet the requirements in these wear categories. Given the industry's knowledge of the types of metals utilized for I feel depressed. To operate equipment that is subject to at least the first two categories of wear. Provides optimal wear resistance and harsh shock and stress conditions specific to these wear conditions Requires sufficient toughness to withstand.
一般に硬度とじん性は範囲の両極端にあると考えられるので、１つ以上の特性を もつそれらの組成物は他のいくらかをもたなく、しかも硬度とじん性の両方が要 求される。Hardness and toughness are generally considered to be at the extremes of the range, so one or more properties Those compositions that have both hardness and toughness are required without some other required.
耐摩耗性の鋳物を供給する産業界は、前述の摩耗に鋳物を利用した装置の有効寿 命を改善することをずっと追求してきた。The industry that supplies wear-resistant castings is concerned with the useful life of equipment that utilizes castings to reduce the aforementioned wear. I have always sought to improve lives.
合金化および合金化しない種々の鉄−炭素組成物は、００１１％なる低含量で出 発した炭素ではマルテンサイト状態において高いしん性をもたない。過共析鋼お よび白銑はそのセメンタイ）（Ｆｅ３Ｃ）の形態のために不十分なしん性で示す 。鉄−炭素の組成物の合金化は炭化物（ＭｘＣｙ）’ｒ生成し、硬度を増すので 高耐摩耗性の要件を若干溝たす。しかしながら、いずれの体積においても炭化物 の粒径が小さくならない限り、炭化物の体積が増すと、耐摩耗性は増すがじん性 または耐破壊性は低下する。金属学者は、２つの主微小構成成分である炭化物と マトリックスが相互に実質的に無関係に作用するため白鋳鉄の複雑性を認識して きた。それにもかかわらず、材料の最終特性は、白銑が摩耗およびｆｉ製状態に あると前記２つの微小構成成分間の相互依存から生じる。そのような材料に衝撃 が加わると、炭化物は粉々になる、そして炭化物が連続していて比較的太きいと 、割れが組織全体に伝播して、しばしば破壊を導いたり、或いは少なくとも材料 の摩耗を加速する。Various alloyed and unalloyed iron-carbon compositions are available at contents as low as 0.011%. The emitted carbon does not have high toughness in the martensitic state. Hypereutectoid steel and white pig iron exhibit insufficient porosity due to its cementite (Fe3C) morphology. . Alloying of iron-carbon composition produces carbide (MxCy)'r, which increases hardness. Slightly exceeds the requirements for high wear resistance. However, in any volume, carbide As the carbide volume increases, wear resistance increases, but toughness decreases, unless the grain size of the carbide decreases. Or fracture resistance decreases. Metallurgists have identified two major microcomponents: carbides and Recognizing the complexity of white cast iron because the matrices act virtually independently of each other, came. Nevertheless, the final characteristics of the material This results from the interdependence between the two microcomponents. Impact on such materials When the carbide is added, it breaks into pieces, and if the carbide is continuous and relatively thick, , the crack propagates throughout the tissue, often leading to failure, or at least accelerates wear.
このように今日までのところ、優れた耐摩耗性と良好な衝撃応力吸収の必要条件 を満たすところの炭素含量が１．７重量％以上の鉄−炭素合金は認識されていな い。Thus to date, the requirements for good wear resistance and good impact stress absorption No iron-carbon alloys with a carbon content of 1.7% by weight or more that meet the requirements are recognized. stomach.
従って、本発明の主目的は、高硬度または高耐摩耗性および優れたしん性を有す る白鋳鉄を提供することである。Therefore, the main objective of the present invention is to provide a material with high hardness or high wear resistance and excellent toughness. Our goal is to provide white cast iron that
さらに、本発明の目的は、所望の耐摩耗性およびじん性のみならず優れた引張り 強さを有する白鋳鉄を提供することである。Furthermore, it is an object of the present invention to provide not only the desired wear resistance and toughness but also excellent tensile strength. Our objective is to provide white cast iron with strength.
また、本発明の目的は、炭化物が球形に近い球状であるところの高耐摩耗性およ び高じん性を有する鋳鉄組成物を提供することである。Furthermore, the object of the present invention is to achieve high wear resistance and An object of the present invention is to provide a cast iron composition having high strength and toughness.
まだ、本発明の目的は、炭化物の大きさが従来の平均値より小さくてマトリック ス全体に実質的に均一に分布しているしん性で耐摩耗性を有する鋳鉄を提供する ことである。However, the object of the present invention is to create a matrix with a carbide size smaller than the conventional average value. Provides a tenacious, wear-resistant cast iron that is substantially uniformly distributed throughout the space. That's true.
また、本発明の目的は、球状粒子のみならず均一に分布している平均粒径の小さ い粒子を生成するためにホウ素を導入することによって、合金鋳鉄における高エ ントロピーのものを提供することである。In addition, the object of the present invention is to obtain not only spherical particles but also particles with small average particle diameters that are uniformly distributed. high energy in alloyed cast iron by introducing boron to produce fine grains. It is to provide something of entropy.
さらに、本発明の目的は、溶融鋳鉄組成物を平衡凝固温度以下の過冷却温度に冷 却し、しかる後に凝固させて、従来の鋳鉄炭化物の平均粒径より小さい平均粒径 を有する球状炭化物を生成させたしん性、耐摩耗性鋳鉄を提供することである。Furthermore, it is an object of the present invention to cool the molten cast iron composition to a subcooling temperature below the equilibrium solidification temperature. The average particle size is smaller than the average particle size of conventional cast iron carbides. It is an object of the present invention to provide a tough and wear-resistant cast iron in which spheroidal carbides are formed.
発明の開示 本発明は、主成分の鉄と、単独または累積的に添加まだは非添加のバナジウム、 チタン、ニオブ、モリブデン、ニッケル、銅、タンタルまたはクロム、またはそ れらの混合物０．、、、、Ｏ、、０１％〜３ｏ重量％と、合金組成物を形成する 炭素１４％〜４．５１量％と、耐摩耗性、じん性および引張強さを改善するため 導入したホウ素０００１％〜４．０重量％からなる合金鋳鉄組成物のユニークな 発見である。本合金は１２０１１℃（ｚ２ｏｏ７；”）〜１３１６℃（２１Ｉ０ ０Ｆ）の範囲、一般的には１２３８℃（２２６０Ｆ）〜１２６０℃（２３００’ Ｆ）の範囲内の凝固点を有する。この凝固点は所定の合金元素での鋳鉄の共晶温 度の１５Ｆ以内にある。炭化物は球形に近い球状で存在し。Disclosure of invention The present invention consists of iron as the main component, vanadium added singly or cumulatively, and vanadium not added yet. titanium, niobium, molybdenum, nickel, copper, tantalum or chromium, or A mixture of these 0. , , , O, , 01% to 30% by weight to form an alloy composition Carbon 14%~4.51% by weight to improve wear resistance, toughness and tensile strength A unique cast iron alloy composition consisting of 0.001% to 4.0% by weight of introduced boron. It's a discovery. This alloy has a temperature range of 12011°C (z2oo7;”) to 1316°C (21I0 0F), typically 1238C (2260F) to 1260C (2300' F) has a freezing point within the range. This freezing point is the eutectic temperature of cast iron with a given alloying element. It is within 15F of the temperature. Carbide exists in a nearly spherical shape.
従来の鋳鉄における炭化物の平均粒径よりかなり小さい４ミクロン以下の粒径を 有する。The grain size is 4 microns or less, which is considerably smaller than the average grain size of carbides in conventional cast iron. have
本発明の方法において、Ｏ，ＯＯ１％〜５０％のノくナジウム、チタン、ニオブ 、モリブデン、ニッケル、銅、タンタル、またはクロムまたはそれらの混合物、 およびＬ８％〜４．５％の炭素を含む合金白鋳鉄が溶融鋳鉄組成物を形成し、そ の溶融鋳鉄組成物に０．００１％〜４．０％のホウ素のようなエントロピー増大 用添加物を加え１次にその溶融鋳鉄組成物を１２０１１℃（２２００Ｆ） 〜１ ５１６℃（２１ｔ００Ｆ）の平衡凝固温度より少なくとも５Ｆ低い過冷却温度に 冷却し、しかる後にその溶融鋳鉄組成物を凝固させて、従来の鋳鉄より小さい平 均粒径を有する球状炭化物または平均４μ以下の炭化物を生成する。In the method of the present invention, O,OO 1% to 50% of sodium, titanium, niobium , molybdenum, nickel, copper, tantalum, or chromium or mixtures thereof; and alloyed white cast iron containing 8% to 4.5% carbon form a molten cast iron composition, which entropy enhancers such as 0.001% to 4.0% boron in molten cast iron compositions. The molten cast iron composition was heated to 12011°C (2200F) ~1 to a subcooling temperature of at least 5F below the equilibrium solidification temperature of 516°C (21t00F) The molten cast iron composition is cooled and then solidified into flat pieces that are smaller than conventional cast iron. Spherical carbides with a uniform particle size or carbides with an average particle diameter of 4 μ or less are produced.
発明を実施するための最良の形態 白鋳鉄は、鋳鉄からなる装置が受ける種々の摩耗条件を満たすのに望ましい耐摩 耗特性全本来もっていると長い間認識されてきた。しかし、合金化鋳鉄の炭化物 の形態は耐摩耗性を保持させるために変えることができ、引張強さを増加するの みならず、さらに重要なことは塑性変形性の付与と共にしん性の著しい改善をす ることが今見出された。従来の鋳鉄においては、オーステナイト、パーライトま たはマルテンサイトのマ） ＩＪソックス見られる過剰の遊離炭素はコーンフレ ークに若干化たう次元の形状をとる黒鉛の形か、または板状または棒状の炭化物 の形であると認識されてきた。いずれの形においても、砂型から通常の熱を取り 出し、金属の断面寸法が１゜箇以上と仮定すると、粒子は顕微鏡的な大きさであ つて、普通平均粒径は１０ミクロン以上である。BEST MODE FOR CARRYING OUT THE INVENTION White cast iron has the desired wear resistance to meet the various wear conditions that equipment made of cast iron is subjected to. It has long been recognized that it has all inherent wear properties. However, carbides in alloyed cast iron The form of can be changed to retain wear resistance and increase tensile strength. What is more important is that it not only imparts plastic deformability but also significantly improves toughness. It has now been discovered that In conventional cast iron, austenite, pearlite or or martensite ma) Excess free carbon found in IJ socks is carbide in the form of graphite, or in the form of plates or rods, with slightly different dimensions. It has been recognized as a form of In either form, normal heat is removed from the sand mold. Assuming that the cross-sectional dimension of the metal is 1° or more, the particles are microscopic in size. Generally, the average particle size is 10 microns or more.
これら黒鉛のフレークはフレークの面に沿った破壊の源であることが知られてい る。典型的に、良品位（７）鋳鉄は引張り強さが約３５０．０ Ｋｇ ／ ｍ （５０，０００ｐｓｉ）、伸びが０％で極めて脆いか、またばじん性がなくどん な変形もできない。適当に合金化すると、遊離炭素は一般に板状または棒状の金 属間化合の金属炭化物（普通はクロム炭化物）に分離し、マトリックス内で連続 または不連続であるが再びｌｏミクロン以上の平均粒径になる。また、その炭化 物粒子は針状を呈するが、いずれの形状にしても、それらは顕微鏡的に見てそれ らの平均長寸法が少なくとも１０ミクロンあって、応力下での割れの開始傾向を 高め、しばしば装置の最終的破壊をもたらす。These graphite flakes are known to be a source of fracture along the plane of the flakes. Ru. Typically, good grade (7) cast iron has a tensile strength of approximately 350.0 kg/m. (50,000 psi), elongation is 0% and extremely brittle, or there is no bulge and is very weak. It cannot be transformed. When properly alloyed, free carbon typically forms gold in the form of plates or rods. Separated into intermetallic metal carbides (usually chromium carbides) and continuous in the matrix Or, it is discontinuous, but the average particle size becomes lo microns or more again. Also, its carbonization The particles have a needle-like shape, but regardless of the shape, they are microscopically distinct. have an average long dimension of at least 10 microns and have a tendency to initiate cracking under stress. and often result in the ultimate destruction of the equipment.
本発明において、この炭化物の棒状または板状の形状を球形に近い球状に変えて 所望のしん件のみならず、引張シ強さを著しく高めることができることが見出さ れた。この鋳鉄炭化物の形態変化は、過去の非延性、脆性、非変形性の鋳鉄を塑 性加工性、高い引張り強さを有し、優れた耐摩耗性を保持したものに変えた。In the present invention, the rod-like or plate-like shape of this carbide is changed to a spherical shape close to a spherical shape. It has been found that not only the desired strength but also the tensile strength can be significantly increased. It was. This morphological change of cast iron carbides changes the past non-ductile, brittle, non-deformable cast iron into plastic. The material has been changed to a material that has high processability, high tensile strength, and maintains excellent wear resistance.
例えば、本発明の鋳鉄は破断する前に曲がり、受ける応力レベルが破壊すること な〈従来の周知鋳鉄に比べて極めて高いことがわかった。本発明の鋳鉄はクロム と合金化することが望ましいが、０００１％〜５０％のバナジウム、チタン、ニ オブ、タンタル、ニッケル、モリブデンまたは銅の種々の添加物に依存して、得 られる鋳鉄の性質は変わる。For example, the cast iron of the present invention bends before breaking, and the stress levels it is subjected to can cause it to fail. It was found that the material was extremely high compared to the conventional well-known cast iron. The cast iron of the present invention is chromium It is desirable to alloy with vanadium, titanium, nitrogen, etc. Depending on various additives of copper, tantalum, nickel, molybdenum or copper, the The properties of cast iron vary.
一般に、本発明の鋳鉄は従来の周知鋳鉄の伝統的１１張強す３５００ Ｋｇ／Ｃ Ｔｄ （５０，０００ｐｓｉ）〜４２０ＯＫ７／Ｃｏｄ （６０，Ｏ，０Ｏｐｓ ｉ）に−比ヘテ１０５７０Ｋｑ／ ｍ （１５１，０ＯＯｐｓｉ ）と高い引張 強さをもつことがわかった。代表的な鋳鉄の伸びば０％であったが、本発明の鋳 鉄はう％の伸びを有する。例えば、採鉱用の破砕機、粉砕機、捷た研磨性固体分 を含む流体を送るボンダのような著しい摩耗および衝撃荷重を受ける装置におい ては非常に重要であるしん性を提供するので、当業者は直ちに伸びまたは塑性変 形能の増加という重要な利点を認識されるであろう。鋳鉄における炭化物の形自 状変化を達成することは、望ましいのみならず、あたかも炭化物の形状が球状に 変わり１粒径が従来の鋳鉄の平均粒径１０〜１１１ミクロンよりかなり小さい４ ミクロンに減少するのと殆んど同じ位効果がある。炭化物粒径のこの程度の減少 によって、高引張強さ値、良好な耐摩耗性および変形能の増大に寄与するために 個々の小球状粒子間の平均自由行程を最小にすることができる。このように１本 発明によって、炭化物の形状が球状に変わるのみならず、その球状粒子が４ミク ロン以下の平均粒径に減少された。Generally, the cast iron of the present invention has a tensile strength of 3500 Kg/C Td (50,000psi) ~ 420OK7/Cod (60,0,0Ops i) High tensile strength of 10,570Kq/m (151,0OOpsi) It turned out to be strong. The elongation of typical cast iron was 0%, but the elongation of the cast iron of the present invention Iron has an elongation of %. For example, mining crushers, crushers, crushed abrasive solids In equipment that is subject to significant wear and shock loads, such as bonders that convey fluids containing Those skilled in the art will readily recognize that elongation or plastic deformation The important benefit of increased formability will be recognized. Form of carbide in cast iron Achieving a shape change is not only desirable, but also as if the shape of the carbide were spherical. The grain size is considerably smaller than the average grain size of conventional cast iron, which is 10 to 111 microns4. It is almost as effective as reducing it to microns. This degree of reduction in carbide grain size By contributing to high tensile strength values, good wear resistance and increased deformability The mean free path between individual small spherical particles can be minimized. One like this The invention not only changed the shape of the carbide into a spherical shape, but also made the spherical particles into 4 microns. The average particle size was reduced to less than 200 yen.
鋳鉄は合金化された鉄−炭素の組成物であることは良く知られている。一般に、 鋳鉄と鋼とを分ける境界線は固体状態における鉄中の炭素の溶解度であることが 認識されている。高レベルの炭素において、炭素は合金化されない限り遊離黒鉛 の形で存在する。It is well known that cast iron is an alloyed iron-carbon composition. in general, The dividing line between cast iron and steel is the solubility of carbon in iron in the solid state. Recognized. At high levels of carbon, carbon becomes free graphite unless alloyed. It exists in the form of
典型的に、鋳鉄中に炭化物を形成させて釉りの性質を改良するために使用する合 金元素はクロムである。Typically used to improve glaze properties by forming carbides in cast iron. The gold element is chromium.
しかしながら、モリブデン、バナジウム、チタン、銅、ニッケル、ニオブおよび タンタルはいろんな組合せで任意にクロムに添加することができるし、或いはク ロムに代えることができる。クロムと併用する場合には、これらの金属元素は普 通約７％までの量で存在するが、望１しくに、バナジウムとニオブは０．００１ ％〜５％の範囲、モリブデンと＠は０００１％〜４％、ニッケルｉ ０．００１ ％〜７％、チタンとタンタルは０．００１％〜４％のＷ囲であって、クロムと併 用またはクロム単独における全体としては０、００１％〜３．０％の範囲内であ る。クロムは７％〜２９％の範囲にあることが望ましいが、さらに望ましい範囲 は２５〜ｂ たは７％〜１２％（これらのクロムの範囲は簡約合金白銑のうつの主グループを 表わす）である。炭素の含量は１．８％以上約１１．５％以下が望ましく、クロ ム２５％〜２８％および１４％〜２２％の含量の鋳鉄に対してはＬ８％〜５％の 範囲、またはクロム７％〜１２％の場合には２％３５％の炭素含量が望ましい。However, molybdenum, vanadium, titanium, copper, nickel, niobium and Tantalum can be optionally added to chromium in various combinations, or It can be replaced with ROM. When used in conjunction with chromium, these metal elements are commonly Vanadium and niobium are commonly present in amounts up to about 7%, but preferably vanadium and niobium are present in amounts of up to 0.001%. % to 5% range, molybdenum and @0001% to 4%, nickel i 0.001 % to 7%, titanium and tantalum are in the W range of 0.001% to 4%, and are combined with chromium. The total amount of chromium used or alone is within the range of 0,001% to 3.0%. Ru. It is desirable that chromium be in the range of 7% to 29%, but the range is more desirable. is 25~b or 7% to 12% (these chromium ranges represent the main group of white pig iron alloys). ). The carbon content is desirably 1.8% or more and approximately 11.5% or less. For cast iron with a content of 25% to 28% and 14% to 22%, 8% to 5% of L. A carbon content of 2% to 35% is desirable for a range of 7% to 12% chromium.
以上概説した代表的な鋳鉄組成物は、ホウ素を一般に０００１％〜４％、望まし くは０．０１％〜１％。The typical cast iron compositions outlined above generally contain boron, preferably from 0.001% to 4%. 0.01% to 1%.
最適には００１％〜０．４％の範囲内で添加することによって炭化物の形態を変 えることができる。このホウ素添加は球状炭化物粒子を生成さすことがわがった が５合金化された鉄−炭素組成物が共晶温度に関係する場合にさらにはつきりす る。Optimally, the morphology of carbides can be changed by adding within the range of 0.001% to 0.4%. You can get it. This boron addition was found to produce spherical carbide particles. Furthermore, when the 5-alloyed iron-carbon composition is related to the eutectic temperature, Ru.
純鉄の凝固点は約１５５８℃（２８ｏｏＦ）でろる、そして炭素の添加に伴って その凝固点は低くな自 る。ホウ素の添加、またはホウ素無添加で合金化すると、凝固温度は、王として 存在するクロムの量に従って１２０１１〜１５１６℃（２２００〜２４００Ｆ） の間を変化するが、特定の合金元素の選択によっても変わる。さらにＴ１しいこ とに、鉄−炭素合金糸の凝固温度は１２う８〜１２６０℃（２２，６０〜２５０ ＯＦ）の範囲内、または約２２８０７”（１２４９℃）±１０〜２０ ”Ｆに する必要があルコとがわかった。本発明に従って所定量で存在する所定の合金元 素を含む特定の鋳鉄組成物は全て、それらの特定の合金元素で形成される鋳鉄系 の共晶温度の１５Ｆ以内で凝固する。The freezing point of pure iron is about 1558°C (28ooF), and with the addition of carbon Its freezing point is low. Ru. When alloyed with or without the addition of boron, the solidification temperature increases as 12011-1516C (2200-2400F) depending on the amount of chromium present and depending on the selection of the particular alloying element. Furthermore T1 Shiiko In addition, the solidification temperature of the iron-carbon alloy thread is 12°C to 1260°C (22,60°C to 250°C). OF) or approximately 22807” (1249℃) ±10 to 20”F I found out that I needed to do it. A given alloying element present in a given amount according to the invention All specific cast iron compositions containing elements are cast iron systems formed by those specific alloying elements. Solidifies within 15F of the eutectic temperature of
この合金化鋳鉄組成物およびホウ素の添加で、炭化物の形態を変えて、はｙｉ形 である球状炭化物粒子全生成できることがわかった。With this alloyed cast iron composition and the addition of boron, the morphology of the carbide is changed, and the yi-type It was found that all spherical carbide particles can be produced.
この重要な粒径の改良をするためおよび球状炭化物粒子の実質的に均一な分布を 得るために、鋳鉄組成物を平衡凝固高度以下少なくとも５Ｆ、望ましくは凝固前 に８〜ＩＯＦまたはそれ以上冷却すると、炭化物の粒径が通常の平均粒径１０ミ クロン以上から平均粒径イミクロン以下に激減することがわかった。この過冷却 は達成が難しいことがわかった。そして問題の熱力学的解決法に際してのみ、鋳 鉄融液のエントロピーを高めることによって系の不規則度が増して融液全冷却下 におくことが見出された。高エントロピー値は液体−固体系のギブス自由エネル ギー値を下げる、そして最も低い自由エネルギーの相が最も安定である。その関 係はＧ ＝ Ｅ 十Ｐ Ｖ−’Ｉ”５−Ｈ−Ｔ Ｓで表わされる、式中のＧはギ プス自由エネルギー５Ｔは給体温度そしてＳはエントロピーである。さらに熱力 学的関係式のＨ−＝ Ｔ Ｓ ＋ Ｖ Ｐは、固体ではｖｐ＝ ｏであるからＨ ＝ Ｔ ｓとなる（式中のＳはエントロピー、Ｈは融解熱、そしてＴは輸体凝固 点である）。エントロピーの増加は、系の融解熱が一定の場合には凝固点の減少 をもたらす。This makes for an important particle size improvement and substantially uniform distribution of spherical carbide particles. To obtain a cast iron composition at least 5F below the equilibrium solidification height, preferably before solidification. When cooled to 8 to IOF or more, the carbide particle size decreases to the normal average particle size of 10 mm. It was found that the average particle size drastically decreased from more than 1 micron to less than 1 micron. This supercooling proved difficult to achieve. And only in the thermodynamic solution of the problem By increasing the entropy of the iron melt, the degree of disorder of the system increases and the melt becomes completely cooled. It was found that the High entropy value means Gibbs free energy of liquid-solid system energy value, and the phase with the lowest free energy is the most stable. That connection The relationship is expressed as G = E 10P V-’I”5-H-TS, where G is G. The free energy 5T is the feed temperature and S is the entropy. even more heat The scientific relational expression H-=TS+VP is H since vp=o in a solid. = Ts (in the formula, S is entropy, H is heat of fusion, and T is transfusion coagulation point). An increase in entropy is a decrease in the freezing point if the heat of fusion of the system is constant. bring about.
ホウ素は鋳鉄組成物に添付されるとエントロピーを増して、系内の不規度を高め て必要条件を冷却状態下にさせるこ−とがわかった。生じる正確な変化は完全に 理解できない、そして前述の説明は理論的なものであることを理解されたい。When added to cast iron compositions, boron increases entropy and increases the degree of randomness within the system. It has been found that the necessary conditions are under cooling conditions. The exact changes that occur are completely Incomprehensible, and please understand that the above explanation is theoretical.
本発明の合金鋳鉄組成物が平衡凝固高度以下、平衡凝固温度の少なくとも５Ｆ（ 低い）過冷却範囲に冷却されると、凝固が生じな力とき、それは過冷却が生じな いときよりも瞬間的である。このように、過冷却は通常生じている長い時間の結 晶−またけ粒子の成長を回避する。むし、ろ、その凝固は粒子が成長する前に生 じる。従って、微細な炭化物粒子は、従来の鋳鉄において生じるような棒状捷た は板状に集合する代りに本発明の合金鋳鉄組成物に訃ける急速凝固では集合する 機会をもたず、炭化物の分布における不均一性をもたらすべくこれらの粒子が集 合して板状または棒状になる機会がない。むしろ、炭化物の分布の均一性は合金 鋳鉄組成物の過冷却段階中でさえも融液相において本来もっているものであるの で、炭化物分布の均一性が凝固中に維持される。The alloy cast iron composition of the present invention is below the equilibrium solidification height and at least 5F above the equilibrium solidification temperature ( When the force is cooled to the supercooling range (low), no solidification occurs; It's more instantaneous than it is now. Thus, supercooling usually occurs over a long period of time. Avoid crystal-straddle grain growth. Rather, the solidification occurs before the particles grow. Jiru. Therefore, the fine carbide particles do not cause the rod-like cracks that occur in conventional cast iron. Instead of agglomerating into plates, they agglomerate in the rapid solidification of the cast iron alloy composition of the present invention. Without opportunity, these particles aggregate to create non-uniformity in the carbide distribution. There is no opportunity to combine them into a plate or rod shape. Rather, the uniformity of carbide distribution Even during the supercooling stage of cast iron compositions, the , the uniformity of carbide distribution is maintained during solidification.
平衡凝固温度以下に過冷却された融液の凝固は、本発明の鋳鉄組成物の強さ、じ ん性および耐摩耗性に対する基本条件であるところこの粒径のかなシの減少およ び鋳鉄マトリックス全体に渡って炭化物のよシ均一な分布をもたらす。The solidification of the melt supercooled below the equilibrium solidification temperature is similar to the strength of the cast iron composition of the present invention. This reduction in grain size and fragility is the basic condition for corrosion resistance and wear resistance. resulting in a more even distribution of carbides throughout the cast iron matrix.
特定例 ２７２％クロム、２．０４％炭素を含む典型的な鋳鉄組成物は約１２５９℃（２ ２６３Ｆ）の共晶温度の上である１２１１９℃（２２ｇｏＦ）の範囲で凝固した 合金組成物である。０．１７％ホウ素の添加で、その合金は平衡凝固温度より５ Ｆ低い温度、１２１Ｉ６１Ｔｈ（２２７５Ｆ）の少し下の温度に過冷却すること ができる。この温度の平衡凝固ン昌度との間で融液は過冷却されて液体の１まで ある。さらに冷却すると、はとんど球形で平均粒径が４ミクロン以下である球状 の炭化物が生成する。得られた鋳鉄の引張強さは１０５７０ Ｋ、ｇ ／ ｃｒ ｄ （１５１，０ＯＯｐｓｉ ）の範囲に６って、約う％の伸びを有する。その ような白鋳鉄は全く耐摩耗性であると共に、高摩耗、高応力作用下において特に 有用にする優れた引張強さおよびじん性を有する。specific example A typical cast iron composition containing 272% chromium, 2.04% carbon It solidified in the range of 12119°C (22 goF), which is above the eutectic temperature of 263F). It is an alloy composition. With the addition of 0.17% boron, the alloy is lowered by 5% below the equilibrium solidification temperature. F lower temperature, supercooling to a temperature slightly below 121I61Th (2275F) Can be done. Between this temperature and the equilibrium solidification degree, the melt is supercooled to liquid level. be. Upon further cooling, the particles become spherical, with an average particle size of less than 4 microns. of carbide is produced. The tensile strength of the obtained cast iron is 10570 K, g/cr It has an elongation of about 6% in the range of d (151,0OOpsi). the White cast iron is completely wear resistant and especially under high wear and high stress action. It has excellent tensile strength and toughness which makes it useful.
同様の結果が、１２５５℃（２２ｇ７′Ｆ）なるはｙ共晶温度に平衡凝固温度を 有する６３２％炭素、９１２％クロム、５１８％ニッケルふ）よヒｏ、 １７％ ホウ素の組成物で得られる。次に、１２４９℃（２２ｇ Ｏｐ）への過冷却は凝 固が生じる前に起きる。A similar result is that 1255°C (22g7'F) is the equilibrium solidification temperature at the y eutectic temperature. Contains 632% carbon, 912% chromium, 518% nickel, 17% Obtained in a composition of boron. Next, supercooling to 1249℃ (22g Op) Occurs before hardness occurs.
本発明の目的は前述のように本発明によって満たされたが、本発明は次の請求の 範囲によってのみ限定されるものと考えられる。Although the object of the present invention has been met by the present invention as described above, the present invention is not limited to the following claims. It is believed to be limited only by scope.
手 続 補 正 書 特許庁長官 宇 賀 道 部 殿 （審査官 殿） ■、事件の表示 ２ 発明←−鱒の名称、指牢寺−・≠弁針摩耗性白鋳鉄 ３、補正する者 事件との関係 特許出願人 ７ 補正の対象 請求の範囲 請求の範囲を下記の通りに補正する。Handbook Supplementary Book Mr. Michibe Uga, Commissioner of the Patent Office (Mr. Examiner) ■Display of incident 2 Invention ← - Name of trout, Shigyoji - ≠ Valve needle wearable white cast iron 3. Person who corrects Relationship to the incident: Patent applicant 7 Subject of amendment Scope of claims The scope of claims is amended as follows.
［請求の範囲 Ｌ 実質的に、主成分の元素鉄と、０００１％〜３０％のバナジウム、チタン、 ニオブ、タンタル、モリブデン、ニッケル、銅、またはクロム、またはそれらの 混合物、およびＬ８・％〜４．５％の炭素なる合金元素の、１つ以上からなる合 金鋳鉄組成物であり；該組成物が前記所定元素で形成される鋳鉄の共晶温度の１ ５Ｆ以内の凝固点を有し；さらにＯ，’００１％〜ヰ、０％のホウ素を含み、そ れによって所望の耐摩耗性、じん性および引張強゛さを有することを特命とする 合金鋳鉄組成物。[The scope of the claims L Substantially the main component element iron, 0001% to 30% vanadium, titanium, Niobium, tantalum, molybdenum, nickel, copper, or chromium, or A mixture consisting of one or more of the alloying elements L8.% to 4.5% carbon. a gold cast iron composition; the composition has a eutectic temperature of 1 of the cast iron formed of the predetermined elements; It has a freezing point within 5F; further contains 0,001% to 0,0% boron; It is specially designed to have the desired abrasion resistance, toughness and tensile strength. Alloy cast iron composition.
２゜ 前記合金が１２０１Ｉ℃（２２００Ｆ）と、１３１６℃（２１１ｏｏｐ） の間の凝固点を有することを特徴とする請求の範囲第１項に記載の組成物。2゜ The alloy has a temperature of 1201I℃ (2200F) and 1316℃ (211oop) A composition according to claim 1, characterized in that it has a freezing point between.
う、 前記バナジウム、チタン、ニオブまたはタンタルが７％までの量で存在す ること全特徴とする請求の範囲第１順に記載の組成物。The said vanadium, titanium, niobium or tantalum is present in an amount of up to 7%. A composition according to claim 1, characterized in that:
（１） ４、 前記クロムがＯ，ＯＯ１％〜３０％の量で存在することを特徴とする請求 の範囲第１項に記載の組成物。(1) 4. A claim characterized in that the chromium is present in an amount of 1% to 30% of O,OO. The composition according to item 1.
５．７％までのニッケル、４％までのモリブデンまたは４％までの銅またはそれ らの混合物が添加されることを特徴とする請求の範囲第１項に記載の組成物。up to 5.7% nickel, up to 4% molybdenum or up to 4% copper or A composition according to claim 1, characterized in that a mixture of these is added.
６、 前記炭素が球状炭化物の形で少なくとも部分的に存在すること全特命とす る請求の範囲第１項、第２項、第５項、第４項または第５項に記載の組成物。6. It is assumed that the carbon exists at least partially in the form of spherical carbides. The composition according to claim 1, 2, 5, 4 or 5.
ｌ 前記合金の凝固点が約１２３８℃（２２６０Ｆ）〜１２６０℃（２３００’ Ｆ）であること全特徴とする請求の範囲第２項に記載の組成物。l The freezing point of the alloy is approximately 1238°C (2260F) to 1260°C (2300' The composition according to claim 2, characterized in that F).
８ 前記合金の凝固点が約１２１４９℃（２２ｇ。8. The solidification point of the alloy is approximately 12149°C (22g).
℃）であることを特徴とする請求の範囲第７項に記載の組成物。8. The composition according to claim 7, characterized in that the temperature is 0.degree.
９ 前記炭素が球状炭化物の形で少なくとも部分的に存在し、前記バナジウム、 チタン、二（２） オブ、ニッケル、銅、モリブデンまたはタンタルが７％までの量で存在し、前記 合金の凝固点が約１２３ｇ℃（２２６０Ｆ）〜１２６０℃（２３００Ｆ）である ことを特徴とする請求の範囲第１項に記載の組成物。9 said carbon is at least partially present in the form of spherical carbides, said vanadium; Titanium, two (2) copper, nickel, copper, molybdenum or tantalum are present in amounts up to 7%; The solidification point of the alloy is approximately 123gC (2260F) to 1260C (2300F) The composition according to claim 1, characterized in that:
１０ 前記炭素が球状炭化物の形で少なくとも部分的に存在し、前記合金が１２ ０４℃（２２００Ｆ）と１３１６℃（２１ｉ ００Ｆ）の間の凝固点を有し、前 記バナジウム、チタン、ニオブ、ニッケル、銅、モリブデンまた社タンタルが７ ％までの量で存在することを特徴とする請求の範囲第１項に記載の組成物。10 said carbon is present at least partially in the form of spheroidal carbides and said alloy is 12 It has a freezing point between 04℃ (2200F) and 1316℃ (21i 00F) and Vanadium, titanium, niobium, nickel, copper, molybdenum and tantalum are 7 Composition according to claim 1, characterized in that it is present in an amount of up to %.
ＩＬ 前記炭素が球状炭化物の形で少ｌぐとも部分的に存在し、前記クローがα １％〜３０％の量で存在し、前記合金の凝固点が約１２５８℃（２２６０Ｆ）〜 １２６０℃（２３００Ｆ）であることを特徴とする請求の範囲第１項に記載の組 成物。IL: the carbon is present at least partially in the form of spherical carbides, and the claw is α present in an amount of 1% to 30%, and the freezing point of the alloy is from about 1258°C (2260F) to The set according to claim 1, characterized in that the temperature is 1260°C (2300F). A product.
１２、前記クロムが０．００１％〜１０％であシ、前記炭素が２．０％〜５，５ ％でアリ、前記ホウ（５） 素が０．０１％〜１．０％であることを特徴とする請求の範囲第１項に記載の組 成物。12. The chromium is 0.001% to 10%, and the carbon is 2.0% to 5.5%. %, the above (5) The composition according to claim 1, characterized in that the element content is 0.01% to 1.0%. A product.
１つ、前記クロムが２５％〜２８％であり、前記炭素がＬ８％〜５．０％であり 、前記ホウ素が０．１％〜０．４％であることを特徴とする請求の範囲第１項に 記載の組成物。One, the chromium is 25% to 28%, and the carbon is L8% to 5.0%; , wherein the boron is 0.1% to 0.4%. Compositions as described.
１イ、前記炭素が、４ミクロン以下の平均粒径を有する球状炭化物の形で少なく とも部分的に存在することを特徴とする請求の範囲第１項または第６項に記載の 組成物。1. The carbon is present in a small amount in the form of spherical carbides having an average particle size of 4 microns or less. Claim 1 or 6, characterized in that both are partially present. Composition.
１５、Ｏ，００１％〜５０％のバナジウム、チタン。15, O, 001% to 50% vanadium, titanium.
ニオブ、モリブデン、ニッケル、銅、タンタルまたはクロムまたはそれらの混合 物と、１．８％〜４．５％の炭素からなる合金鋳鉄にＱ、ＯＯ１％〜４．０％の ホウ素を添加して溶融鋳鉄組成物を生成し、該溶融鋳鉄組成物全平衡凝固温度以 下の過冷却温度に冷却し、該溶融鋳鉄組成物を凝固させて従来の鋳鉄炭化物粒子 よシ小さい平均粒径を有する球状炭化物を生成させることからなることを特命と する鋳鉄に球状炭化物を形成させる方法。Niobium, molybdenum, nickel, copper, tantalum or chromium or mixtures thereof alloy cast iron consisting of 1.8% to 4.5% carbon and Q, OO 1% to 4.0%. Boron is added to produce a molten cast iron composition, and the molten cast iron composition is heated to a temperature below the total equilibrium solidification temperature. The molten cast iron composition is cooled to a subcooling temperature below and solidifies to form conventional cast iron carbide particles. The special mission is to produce spherical carbides with a very small average particle size. A method of forming spheroidal carbides in cast iron.
１６、前記合金が１２０４℃（２２００７）と１５１６℃（２１１００Ｆ）の間 の凝固点を有することを特徴とする請求の範囲第１５項に記載の方法。16. The alloy is between 1204°C (22007) and 1516°C (21100F) 16. A method according to claim 15, characterized in that it has a freezing point of .
１７、前記バナジウム、°チタン、ニオブ、タンクでの量で存在すること全特徴 とする請求の範囲第１５項に記載の方法。17. All characteristics that vanadium, ° titanium, niobium, present in the amount in the tank 16. The method according to claim 15.
１Ｂ、前記クロムが０１％〜３０％の量で存在することを特徴とする請求の範囲 第１５項に記載の方法つ １９．７％までのニッケル、１１％までのモリブデン、または１１％壕での銅ま 鳥はそれらの混合物を添加することを特徴とする請求の範囲第１５項に記載の方 法。1B. Claims characterized in that said chromium is present in an amount of 01% to 30%. The method described in Section 15 Up to 19.7% nickel, up to 11% molybdenum, or copper in 11% trenches. The method according to claim 15, characterized in that the bird is added with a mixture thereof. Law.
２０、前記溶融鋳鉄組成物を平衡凝固温度より少なくとも５Ｆ低い適冷２ｇ部度 に冷却することを特徴とする請求の範囲第１５項に記載の方法。20. The molten cast iron composition is cooled for 2g at least 5F below the equilibrium solidification temperature. 16. A method according to claim 15, characterized in that the method comprises cooling to .
２１、前記溶融鋳鉄組成物を過冷却温度へ冷却し続けることによって該溶融鋳鉄 組成物を凝固させて、約４ミクロン以下の平均粒径を有する球状炭化物を形成さ すことを特徴とする請求の範囲第１５項に記載の方法。21. By continuing to cool the molten cast iron composition to a supercooling temperature, The composition is solidified to form spherical carbides having an average particle size of about 4 microns or less. 16. The method according to claim 15, characterized in that:
２２、前記溶融鋳鉄組成物を平衡凝固温度よυ少なくとも５Ｆ低い過冷却温度に 冷却し、前記溶融鋳鉄組成物を過冷却温度へ冷却し続けることによって該溶融鋳 鉄組成物を凝固させて約４ミクロン以下の平均粒径を有する球状炭化物全形成さ すこと全特徴とする請求の範囲第１５項に記載の方法。22. The molten cast iron composition is brought to a supercooling temperature that is at least 5 F below the equilibrium solidification temperature. cooling and continuing to cool the molten cast iron composition to a supercooling temperature. The iron composition is solidified to form entirely spherical carbides having an average particle size of about 4 microns or less. 16. A method according to claim 15, characterized in that:
こう、 前記平衡凝固点が１２０１４℃（２２００Ｆ）〜１３１６℃（２１＋ ００Ｆ）であることを特徴とする請求の範囲第２０項５第２１項または第２２項 に記載の方法。Thus, the equilibrium freezing point is between 12014°C (2200F) and 1316°C (21+ 00F) Claim 20, 5, 21 or 22 The method described in.
２１１、＠記平衡凝固点が１２３８℃（２２６０Ｆ）〜１２６０℃（２３００Ｆ ）であること全特徴とする請求の範囲第２０項、第２１項せたは第２２項に記載 の方法。211, @Equilibrium freezing point is 1238℃ (2260F) ~ 1260℃ (2300F) ) as set forth in claim 20, 21, or 22. the method of.
（６） ２５、実質的に、炭素と、鉄と、ノ（ナジウム、チタン、モリブデン、ニッケル ５＠、）ンタル捷たはクロムまたはそれらの混合物との溶融鋳鉄混合体のエント ロピー全増大させて溶融鋳鉄組成物を生成させ、該溶融鋳鉄組成物を該溶融鋳鉄 組成物の平衡凝固温度以下の温度に過冷却し、従来の鋳鉄炭化物の平均粒径より 小さい平均粒径を有する球状炭化物を生成させながら前記溶融鋳鉄組成物を凝固 させることからなることを特徴とする。鋳鉄のしん性、耐摩耗性および引張強さ を改良するため溶融鋳鉄を過冷却する方法。(6) 25.Substantially carbon, iron, (nadium, titanium, molybdenum, nickel) 5＠,) Entrance of molten cast iron mixture with melted steel or chromium or mixtures thereof the molten cast iron composition is increased to produce a molten cast iron composition; It is supercooled to a temperature below the equilibrium solidification temperature of the composition, and the average particle size of conventional cast iron carbide is Solidifying the molten cast iron composition while producing spheroidal carbides having a small average particle size It is characterized by that it consists of causing. Toughness, wear resistance and tensile strength of cast iron A method of supercooling molten cast iron to improve it.
２６、前記溶融鋳鉄組成物を平衡凝固温度より少なくとも約５Ｆ低い過冷却温度 に冷却することを特徴とする請求の範囲第２５項に記載の方法。26. Subcooling the molten cast iron composition to a temperature at least about 5F below the equilibrium solidification temperature. 26. A method according to claim 25, characterized in that the method comprises cooling to .
２７ 前記溶融鋳鉄組成物を過冷却高度へ冷却し続けることによって該溶融鋳鉄 組成物を凝固させて約４ミクロン以下の平均粒径を有する球状炭化物全形成さす こと全特徴とする請求（７） の範囲第２５項に記載の方法。27 By continuing to cool the molten cast iron composition to a supercooled degree, the molten cast iron The composition is solidified to form all spherical carbides having an average particle size of about 4 microns or less. Claims characterized by all of the above (7) The method according to item 25.
２８ 前記溶融鋳鉄組成物を平衡凝固温度より少なくとも約５Ｆ低い過冷却温度 に冷却し、該溶融鋳鉄組成物を過冷却湿度へ冷却し続けることによって該溶融鋳 鉄組成物を凝固させて約４ミクロン以下の平均粒径を有する球状炭化物を形成さ すことを特徴とする請求の範囲第２５項に記載の方法。28. Subcooling the molten cast iron composition to a temperature at least about 5 F below the equilibrium solidification temperature. and cooling the molten cast iron composition to a subcooled humidity. The iron composition is solidified to form spherical carbides having an average particle size of about 4 microns or less. 26. A method according to claim 25, characterized in that:
２９、Ｏ，ＯＯ１％〜４．０％のホウ素を添加することによって、前記鋳鉄混合 体のエントロピーを増大させることを特徴とする請求の範囲第２５順、第２６項 、第２７項または第２８項に記載の方法。29, O,OO by adding 1% to 4.0% boron to the cast iron mixture. Claim 25, item 26, characterized in that the entropy of the body is increased. , the method according to paragraph 27 or paragraph 28.
３０ 前記ホウ素が０１％〜０４％の量で存在することを特徴とする請求の範囲 第２９項の方法。30. Claims characterized in that said boron is present in an amount of 01% to 04% The method of paragraph 29.
３Ｌ 前記ホウ素が０１％〜０４％の量で存在することを特徴とする請求の範囲 第１項または第１５項に記載の方法。＝１ （８） 国際調査報告3L Claim characterized in that said boron is present in an amount of 01% to 04% The method according to paragraph 1 or paragraph 15. =1 (8) international search report
Claims (1)
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| PCT/US1983/001656 WO1985001962A1 (en) | 1983-10-24 | 1983-10-24 | Abrasive resistant white cast iron |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS60501958A true JPS60501958A (en) | 1985-11-14 |
Family
ID=22175514
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP58503752A Pending JPS60501958A (en) | 1983-10-24 | 1983-10-24 | Wear-resistant white cast iron |
Country Status (7)
| Country | Link |
|---|---|
| EP (1) | EP0159981A4 (en) |
| JP (1) | JPS60501958A (en) |
| CH (1) | CH666908A5 (en) |
| DE (1) | DE3390548T1 (en) |
| GB (1) | GB2158462B (en) |
| NL (1) | NL8320359A (en) |
| WO (1) | WO1985001962A1 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106222531A (en) * | 2016-07-24 | 2016-12-14 | 莎车县军辉机械有限公司 | A kind of boron manganese chromium wear resistance castings and manufacturing process thereof |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0675210A1 (en) * | 1992-12-15 | 1995-10-04 | Kabushiki Kaisha Toshiba | Method of manufacturing cast iron of high strength and low expansion |
| DE4409278A1 (en) * | 1994-03-18 | 1995-09-21 | Klein Schanzlin & Becker Ag | Corrosion and wear resistant chilled cast iron |
| ES2111405T3 (en) * | 1994-05-17 | 1998-03-01 | Ksb Ag | HARD CAST IRON WITH HIGH CORROSION AND WEAR RESISTANCE. |
| DE19721477A1 (en) | 1997-05-23 | 1998-11-26 | Abb Patent Gmbh | Microbial membrane reactor for use in flow systems |
| DE19901170B4 (en) * | 1998-10-21 | 2006-11-23 | Reiloy Metall Gmbh | Use of an iron base age alloy |
| CN114318116A (en) * | 2021-12-08 | 2022-04-12 | 河北澳金机械设备有限公司 | Composition improvement of KmTBCr26 high-chromium cast iron |
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|---|---|---|---|---|
| JPS49106425A (en) * | 1973-02-15 | 1974-10-09 | ||
| JPS53140218A (en) * | 1977-05-13 | 1978-12-07 | Mitsubishi Heavy Ind Ltd | Wear resistant white pig iron |
| JPS5693859A (en) * | 1979-12-28 | 1981-07-29 | Komatsu Ltd | Ball alloy for grinding |
| JPS5751241A (en) * | 1980-09-12 | 1982-03-26 | Komatsu Ltd | Ball alloy for pulverization |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2978320A (en) * | 1958-12-29 | 1961-04-04 | Gen Motors Corp | Method for producing a high strength ferrous metal |
| SU168322A1 (en) * | 1963-06-11 | 1965-02-18 | Ростовский Дону научно исследовательский институт технологии | FLOATS FOR TUNING? SOI) ZILYAN KATtJi'iHO-.} -. if ^ '"TEKHK ^ TLi'A' ^ '-ag?' 'I'; ': T;: L I. YANMA .. * lv" "zhl ^ chg * in:" MA: M. ^ ^^ - ^ f ^^^ The proposed alloy makes it possible to adjust the mechanical properties of the deposited layer by additionally doping with tungsten during the deposition process. It has a high elasticity that allows for significant deformation of the deposited parts during manufacture and operation. 10. Invention 1. A welding alloy containing chromium and manganese. and silicon, characterized in that, 15 in order to increase the hardness and wear resistance of the weldments, its composition includes (in o / o): carbon 3 , 0-3.7; manganese, 5.5-6.5; silicon; 1.8-2.2; chromium 22-26; boron 0.4–0.6; titanium 0.25–0.35; tungsten 2-10; 20 sulfur to 0.08; phosphorus to 0.08; iron - the rest of the alloy. The alloy according to claim 1, characterized in that, in order to improve the mechanical properties, tungsten is introduced directly in the process 25 of surfacing. |
| US3334996A (en) * | 1966-12-13 | 1967-08-08 | Xaloy Inc | Hard, wear-resistant ferrous alloy |
| DE1946623B1 (en) * | 1969-09-15 | 1971-06-24 | Gontermann Peipers Gmbh | USE OF A HIGH CHROME ALLOY IRON ALLOY AS A MATERIAL FOR ROLLING MILL ROLLS |
| JPS5530061B2 (en) * | 1973-11-01 | 1980-08-08 | ||
| DE2428822A1 (en) * | 1974-06-14 | 1976-01-02 | Goetzewerke | SPHERICAL CAST IRON ALLOY WITH INCREASED WEAR RESISTANCE |
| FR2405749A1 (en) * | 1977-10-14 | 1979-05-11 | Thome Cromback Acieries | NEW FORGED CRUSHING BODIES, ESPECIALLY CRUSHING BALLS, AND THEIR MANUFACTURING PROCESS |
| SU850719A1 (en) * | 1978-09-29 | 1981-07-30 | Всесоюзный Научно-Исследователь-Ский И Проектно-Технологическийинститут Угольного Машиностроения | Cast iron |
| SU954481A1 (en) * | 1981-01-12 | 1982-08-30 | Гомельский Филиал Белорусского Ордена Трудового Красного Знамени Политехнического Института | Wear-resistant white iron |
| AU557815B2 (en) * | 1982-07-19 | 1987-01-08 | Giw Industries Inc. | Abrasive resistant white cast iron |
| ZA844074B (en) * | 1983-05-30 | 1986-04-30 | Vickers Australia Ltd | Abrasion resistant materials |
-
1983
- 1983-10-24 CH CH2839/85A patent/CH666908A5/en not_active IP Right Cessation
- 1983-10-24 WO PCT/US1983/001656 patent/WO1985001962A1/en not_active Application Discontinuation
- 1983-10-24 JP JP58503752A patent/JPS60501958A/en active Pending
- 1983-10-24 EP EP19830903718 patent/EP0159981A4/en not_active Withdrawn
- 1983-10-24 GB GB08515282A patent/GB2158462B/en not_active Expired
- 1983-10-24 NL NL8320359A patent/NL8320359A/en not_active Application Discontinuation
- 1983-10-24 DE DE19833390548 patent/DE3390548T1/en active Granted
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS49106425A (en) * | 1973-02-15 | 1974-10-09 | ||
| JPS53140218A (en) * | 1977-05-13 | 1978-12-07 | Mitsubishi Heavy Ind Ltd | Wear resistant white pig iron |
| JPS5693859A (en) * | 1979-12-28 | 1981-07-29 | Komatsu Ltd | Ball alloy for grinding |
| JPS5751241A (en) * | 1980-09-12 | 1982-03-26 | Komatsu Ltd | Ball alloy for pulverization |
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| CN106222531A (en) * | 2016-07-24 | 2016-12-14 | 莎车县军辉机械有限公司 | A kind of boron manganese chromium wear resistance castings and manufacturing process thereof |
| CN106222531B (en) * | 2016-07-24 | 2017-11-21 | 莎车县军辉机械有限公司 | A kind of boron manganese chromium wear resistance castings and its manufacturing process |
Also Published As
| Publication number | Publication date |
|---|---|
| NL8320359A (en) | 1985-09-02 |
| GB2158462B (en) | 1988-02-24 |
| GB2158462A (en) | 1985-11-13 |
| DE3390548C2 (en) | 1988-12-01 |
| WO1985001962A1 (en) | 1985-05-09 |
| DE3390548T1 (en) | 1985-11-28 |
| GB8515282D0 (en) | 1985-07-17 |
| CH666908A5 (en) | 1988-08-31 |
| EP0159981A1 (en) | 1985-11-06 |
| EP0159981A4 (en) | 1987-04-29 |
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