JP2002235113A - Method for producing stock for loom member made of high strength steel - Google Patents
Method for producing stock for loom member made of high strength steelInfo
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- JP2002235113A JP2002235113A JP2001027827A JP2001027827A JP2002235113A JP 2002235113 A JP2002235113 A JP 2002235113A JP 2001027827 A JP2001027827 A JP 2001027827A JP 2001027827 A JP2001027827 A JP 2001027827A JP 2002235113 A JP2002235113 A JP 2002235113A
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Abstract
Description
【0001】[0001]
【産業上の利用分野】本発明は、繊維との接触で磨耗し
易いフラットヘルド、ドロッパー、筬羽、変形筬、リー
ド等の織機部材であって、耐食性と靭性および耐繊維磨
耗性に優れたに優れた高強度鋼製織機部材用素材の製造
方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a loom member such as a flat heald, a dropper, a reed, a deformed reed, a reed or the like which is easily worn by contact with a fiber, and is excellent in corrosion resistance, toughness and fiber abrasion resistance. The present invention relates to a method for producing a material for a high-strength steel loom member excellent in quality.
【0002】[0002]
【従来の技術】フラットヘルド、ドロッパー、筬羽、変
形筬、リード等の織機部材にはステンレス鋼SUS42
0J2を焼入れした組織強化材が使用されている。この
種の織機部材は、織物に使用される繊維の材質改善、生
産能率を向上させるために高速度化等にともなって、磨
耗環境が過酷になってきている。その結果、部品寿命が
低下し、補修部品の煩雑な交換が余儀なくされている。
また、使用環境によっては、織機部材が腐食し織りあが
った織物が汚染される問題も発生している。2. Description of the Related Art Stainless steel SUS42 is used for loom members such as flat healds, droppers, reed feathers, deformed reeds, and reeds.
A structure reinforcing material obtained by quenching 0J2 is used. The weaving environment of this type of loom member has become severe with the increase in speed and the like in order to improve the quality of fibers used in the woven fabric and to improve production efficiency. As a result, the life of the parts is shortened, and complicated replacement of the repair parts is inevitable.
Further, depending on the use environment, there is a problem that the loom member is corroded and the woven fabric is contaminated.
【0003】[0003]
【発明が解決しようとする課題】本発明は、そのような
問題を解消すべく案出されたものであり、耐繊維磨耗に
ついては、硬質なTi炭化物やNb炭化物をマトリック
スに分散させることにより耐摩耗性と、適正な焼入れ・
焼戻し温度で造り込んだ高耐食性材により、長期にわた
って使用される耐食性と靭性および耐繊維磨耗性に優れ
た高強度鋼製織機部材を提供することを目的とする。DISCLOSURE OF THE INVENTION The present invention has been devised to solve such a problem, and the resistance to fiber abrasion is improved by dispersing hard Ti carbide or Nb carbide in a matrix. Abrasion and proper quenching
An object of the present invention is to provide a high-strength steel loom member having excellent corrosion resistance, toughness, and fiber wear resistance that is used for a long period of time by using a high corrosion-resistant material built at a tempering temperature.
【0004】[0004]
【課題を解決するための手段】本発明の耐食性と靭性お
よび耐繊維磨耗性に優れた高強度鋼製織機部材用素材の
製造方法は、その目的を達成するため、Cr:10〜1
8質量%、C:0.05〜0.5質量%を含有し、さら
にTiおよび/またはNbを、Ti:単独で0.05〜
1質量%、Nb:単独で0.05〜1質量%或いはTi
+Nb:合計量で0.05〜1質量%を含み、残部が実
質的にFeの組成からなる鋼に、下記(1)、(2)式
により求まるTに対して、焼入れ温度がT±50℃、焼
戻し温度が150〜500℃で熱処理を施し、鋼の組織
をマルテンサイト相とするとともに、鋼のマトリックス
中にTiおよび/またはNbの炭化物を0.1質量%以
上分散析出させることを特徴とするものである。ここ
で、 T=280×k*+1200 ‥‥‥(1) k*=log{C%−0.16(Nb%+Ti%)}‥‥‥(2)SUMMARY OF THE INVENTION The method of the present invention for producing a material for a high-strength steel loom member excellent in corrosion resistance, toughness and fiber abrasion resistance is intended to achieve its object.
8% by mass, C: 0.05 to 0.5% by mass, further containing Ti and / or Nb, Ti:
1% by mass, Nb: 0.05 to 1% by mass alone or Ti
+ Nb: A steel containing 0.05 to 1% by mass in total and the balance being substantially composed of Fe, having a quenching temperature of T ± 50 with respect to T determined by the following formulas (1) and (2). C. and a tempering temperature of 150 to 500 [deg.] C., heat-treating the steel to form a martensitic phase and dispersing and precipitating 0.1 mass% or more of carbides of Ti and / or Nb in a steel matrix. It is assumed that. Here, T = 280 × k * + 1200 {(1) k * = log {C% −0.16 (Nb% + Ti%)} (2)
【0005】[0005]
【作用】本発明者等は、磨耗損傷した織機部材や実際に
使用した繊維等を多数取り寄せ、磨耗損傷部分や繊維を
ミクロ的な観点から調査した。その結果、磨耗した部材
の大半では、細かい線状に研削されたような疵が磨耗部
分に観察された。また、使用された繊維には、アルミナ
や炭化珪素等の硬質粒子の付着が検出された。研削され
たような疵や硬質粒子の付着から、この時の磨耗現象
は、硬質粒子が介在した磨耗であることが分かった。な
お、本明細書では、繊維と織機部材の接触面に硬質粒子
が介在し、振動または摺動過程で織機部材の接触面が硬
質粒子等で擦過・研削される磨耗をアブレッシブな磨耗
と言う。アブレッシブな磨耗は、種々の磨耗現象の中で
最も激しい磨耗であり、この磨耗に耐える材料の開発が
望まれている。The present inventors ordered a large number of worn and damaged loom members and actually used fibers, and investigated the worn and damaged portions and fibers from a microscopic viewpoint. As a result, in most of the worn members, flaws such as fine linear grinding were observed in the worn portion. Further, adhesion of hard particles such as alumina and silicon carbide was detected on the used fibers. From the scratches and the attachment of the hard particles as if they were ground, it was found that the wear phenomenon at this time was abrasion mediated by the hard particles. In the present specification, wear in which hard particles are present on the contact surface between the fiber and the loom member and the contact surface of the loom member is rubbed or ground by the hard particles or the like in a vibration or sliding process is referred to as abrasive wear. Abrasive wear is the most severe wear among various wear phenomena, and it is desired to develop a material that can withstand this wear.
【0006】これまでの鋼製織機部材は、鋼の組織強
化、加工硬化等により得られる硬さと比較してアルミ
ナ、炭化珪素等の硬質粒子が硬いために、アブレッシブ
な磨耗に対しては耐えられなかった。そこで、本発明者
等は、アルミナや炭化珪素と同等の硬さを有する炭化物
に着目し、鋼のマトリックス中に硬質炭化物を分散析出
させ、アブレッシブな磨耗に対する耐磨耗性の検討を行
った。その結果、Ti炭化物またはNb炭化物の単独ま
たは複合炭化物を分散析出させることで、アルミナや炭
化珪素によるアブレッシブな磨耗を抑制する効果がある
ことを見出し、耐磨耗性に優れた織機部材用耐磨耗鋼の
開発を行った。本発明者等は、さらに耐食性の改善、靭
性の向上についても検討したところ、添加元素とその添
加量、および焼入れ・焼戻し温度の関係において耐食
性、靭性が向上することを見出した。[0006] Conventional steel loom members are resistant to abrasive wear because hard particles such as alumina and silicon carbide are harder than the hardness obtained by strengthening the structure and hardening the steel. Did not. Therefore, the present inventors focused on carbides having the same hardness as alumina and silicon carbide, dispersed hard carbides in a steel matrix, and studied abrasion resistance against abrasive wear. As a result, it has been found that dispersing and precipitating Ti carbide or Nb carbide alone or in combination has an effect of suppressing abrasive wear due to alumina or silicon carbide, and has excellent wear resistance for a loom member for a loom member. Wear steel was developed. The present inventors have further studied the improvement of corrosion resistance and toughness. As a result, they have found that the corrosion resistance and toughness are improved in relation to the added elements and the amounts thereof and the quenching and tempering temperatures.
【0007】なお、ここで、本発明方法で得られる鋼材
の特性評価に使用した各種の評価・測定方法について、
説明しておく。 [炭化物析出量の測定]炭化物の固溶・析出処理によっ
て、炭化物量を制御した試料を沃化アルコール液に浸漬
し、超音波を加えて鋼を溶解した後、液中に残った炭化
物量の残渣量より求めた。炭化物の形態は残渣のX線解
析で固定して求め、個々の金属元素量は湿式分析および
ガス分析装置で求めた。Here, various evaluation and measurement methods used for evaluating the characteristics of the steel material obtained by the method of the present invention will be described.
Let me explain. [Measurement of Carbide Precipitation Amount] A sample in which the amount of carbide was controlled by solid solution / precipitation treatment of carbide was immersed in an alcohol iodide solution, and ultrasonic waves were applied to dissolve the steel. It was determined from the amount of residue. The form of the carbide was determined by X-ray analysis of the residue, and the amount of each metal element was determined by a wet analysis and a gas analyzer.
【0008】[耐食性の評価]耐食性の評価は、JISZ
2371による塩水噴霧試験を72時間実施し、試験後
の錆発生の有無で評価した。 [靭性の評価]焼入れ・焼戻し後の靭性の評価は、JIS
Z2248の押し曲げ法により、密着または曲げ、曲げ
部での破断の有無で評価した。[Evaluation of corrosion resistance]
A salt spray test according to 2371 was carried out for 72 hours, and the presence or absence of rust after the test was evaluated. [Evaluation of toughness] Evaluation of toughness after quenching and tempering
Evaluation was made based on the presence or absence of breakage at the bent part by close contact or bending, by the push bending method of Z2248.
【0009】[耐摩耗性の評価]試験は、フラッドヘルド
のメール穴に、織物の化学繊維(TFD75/36F外
径約120μm)を通し、接触摺動させ接触部の磨耗深
さを測定した。試験の条件は、繊維の張力:約50g
で、試験の回転速度:80rpm(摺動速度:0.1m
/s)、試験時間:10時間である。試験片フラッドヘ
ルドのメール部の耐摩耗性評価は、繊維と接触磨耗した
部分の磨耗量を求め、SUS420J2の磨耗深さを基
準とし、下記(3)式に基づいて求めた耐磨耗指数M
(%)で行った。耐磨耗指数Mが小さいほど耐磨耗性に
優れていることを示す。 耐磨耗性指数M(%)=Di÷Do×100 ‥‥‥(3) ここで、DoはSUS420J2の磨耗深さ Diは評価対象鋼の磨耗深さ[Evaluation of abrasion resistance] In the test, a chemical fiber of a woven fabric (TFD 75 / 36F outer diameter: about 120 μm) was passed through the mail hole of the flood heald, and the slidable contact was performed to measure the abrasion depth of the contact portion. The test conditions were as follows: fiber tension: about 50 g
And the test rotation speed: 80 rpm (sliding speed: 0.1 m
/ S), test time: 10 hours. The abrasion resistance of the mail portion of the test specimen floodheld was determined by calculating the amount of wear in the portion in contact with the fiber and using the abrasion depth of SUS420J2 as a reference, based on the following equation (3).
(%). The smaller the wear resistance index M, the better the wear resistance. Abrasion resistance index M (%) = Di ÷ Do × 100 ‥‥‥ (3) where Do is the wear depth of SUS420J2, and Di is the wear depth of the steel to be evaluated.
【0010】次に、本発明方法の内容を具体的に説明す
る。本発明で対象とされる鋼材は、耐食性を付与するた
めに10〜18質量%のCrを含んでいる。Cr含有量
が8質量%を下回ると、Cr添加による防食効果が低減
する。10質量%以上にCrを添加するほど耐食性は向
上するが、18質量%を越えると熱間加工性が低下し、
製造上問題となる。本発明材が用いられる腐食環境を考
慮し、また材料の低コスト化を図ることからCrの上限
は18質量%とした。Next, the contents of the method of the present invention will be specifically described. The steel material targeted in the present invention contains 10 to 18% by mass of Cr in order to impart corrosion resistance. When the Cr content is less than 8% by mass, the anticorrosion effect due to the addition of Cr is reduced. Corrosion resistance improves as Cr is added to 10% by mass or more, but hot workability decreases when it exceeds 18% by mass,
This is a manufacturing problem. The upper limit of Cr is set to 18% by mass in consideration of the corrosive environment in which the material of the present invention is used and to reduce the cost of the material.
【0011】Tiおよび/またはNbは、炭化物の合計
析出量が0.1質量%以上になるように、Ti:単独で
0.05〜1質量%、Nb:単独で0.05〜1質量%
またはTi+Nb:合計量で0.05〜1質量%の割合
で添加される。炭化物合計析出量0.1質量%以上は、
後述する実施例に記載しているように、耐磨耗性に及ぼ
す析出物の影響調査から見出された臨界値である。0.
1質量%以上の合計析出量を確保することにより、炭化
物のない鋼材に比較して格段に優れた耐磨耗性が得られ
る。Ti:0.05質量%以上、Nb:0.05質量%
以上またはTi+Nb:0.05質量%以上に設定する
とき、マトリックス中に分散析出した炭化物の合計析出
量が0.1質量%以上になる。しかし、Ti、Nbの成
分は溶製時の湯流れ性の低下、金属間化合物生成による
靭性の低下、素材コストの上昇等のため、Ti含有量の
上限を1.0質量%、Nb含有量の上限を1質量%、T
i+Nb合計含有量の上限を1質量%に設定した。Ti: and / or Nb: Ti: 0.05 to 1% by mass alone, Nb: 0.05 to 1% by mass alone such that the total amount of carbide precipitation is 0.1% by mass or more.
Or Ti + Nb: added at a ratio of 0.05 to 1% by mass in total amount. The total carbide precipitation of 0.1% by mass or more
As described in Examples below, it is a critical value found from an investigation of the effect of precipitates on abrasion resistance. 0.
By securing a total precipitation amount of 1% by mass or more, much superior wear resistance can be obtained as compared with a steel material having no carbide. Ti: 0.05% by mass or more, Nb: 0.05% by mass
When the above or Ti + Nb is set to 0.05% by mass or more, the total amount of carbides dispersed and precipitated in the matrix becomes 0.1% by mass or more. However, the Ti and Nb components have a lower limit of the Ti content of 1.0% by mass and a lower Nb content because of lowering of the fluidity during melting, lowering of the toughness due to the formation of intermetallic compounds, and higher material costs. 1% by mass, T
The upper limit of the total content of i + Nb was set to 1% by mass.
【0012】0.1質量%以上の炭化物を析出させるた
めには、Cを0.05質量%以上含有させる必要があ
る。そして、Cは炭化物の生成に消費されるだけでな
く、組織強化にも有効な成分であるが、0.5質量%を
越える多量のCの添加は共晶クロム炭化物の多量の析出
を招き、材料品質の低下や熱間加工性等の低下を引き起
こすため、C含有量の上限は0.5質量%とした。本発
明で対象とされる鋼材には、耐磨耗性向上のための硬質
な炭化物形成元素のZr、V、W等を、Ti、Nbとの
一部置換または複合添加として、Tiおよび/またはN
bと合量で総和が1質量%まで添加することができる。In order to precipitate carbides of 0.1% by mass or more, it is necessary to contain C in an amount of 0.05% by mass or more. C is not only consumed in the formation of carbides, but is also an effective component for strengthening the structure. However, the addition of a large amount of C exceeding 0.5% by mass causes a large amount of precipitation of eutectic chromium carbides, The upper limit of the C content is set to 0.5% by mass in order to cause a decrease in material quality and a decrease in hot workability. In the steel material targeted in the present invention, Zr, V, W, etc., which are hard carbide-forming elements for improving abrasion resistance, are partially substituted with Ti, Nb or added in combination with Ti and / or N
It can be added up to 1% by mass in total with b.
【0013】さらに、本発明で対象とされる鋼材には、
他の合金成分としてNi、Mo、Cu等を含有させるこ
ともできる。例えば、焼入れ後のマルテンサイト相の確
保やさらなる靭性等の改善のため0.1〜4質量%のN
i、耐食性改善のため0.1〜3質量%のMo、耐食
性、耐応力腐食割れ性等の改善のため0.2〜3質量%
のCuの1種または2種以上を含有させても良い。な
お、製鋼過程での脱酸を目的とするSi、Mnの添加に
ついては、Siを0.02〜2.5質量%、Mnを0.
02〜3質量%の範囲で調整することが好ましい。[0013] Further, the steel materials targeted by the present invention include:
Ni, Mo, Cu and the like can be contained as other alloy components. For example, in order to secure a martensite phase after quenching and further improve toughness, 0.1 to 4% by mass of N
i, Mo of 0.1 to 3% by mass for improvement of corrosion resistance, 0.2 to 3% by mass of Mo for improvement of corrosion resistance, stress corrosion cracking resistance and the like
Or one or more types of Cu. In addition, about addition of Si and Mn for the purpose of deoxidation in the steelmaking process, 0.02 to 2.5% by mass of Si and 0.1% of Mn were added.
It is preferable to adjust in the range of 02 to 3% by mass.
【0014】一方、織機部材用素材への多量のCの添加
や低温焼き入れ或いは高温焼戻し等の製法によっては、
耐食性が損なわれることが確認され、その改善方法につ
いて検討した。これらの耐食性低下の原因を調査した結
果、鋼中のCrがCと結合してCr23C6のクロム炭化
物が析出していた。このクロム炭化物の析出によって耐
食性向上に有効なCrが炭化物に取り込まれ、析出物近
傍のCrが欠乏したため、耐食性が損なわれ腐食してい
ることが分かった。また、焼入れ温度や焼戻し温度が不
適切であれば耐食性のみならず靭性に大きな悪影響をも
たらす。On the other hand, depending on the production method such as addition of a large amount of C to the loom member material, low-temperature quenching or high-temperature tempering,
It was confirmed that the corrosion resistance was impaired, and the improvement method was examined. As a result of investigating the cause of the decrease in the corrosion resistance, Cr in the steel was combined with C and chromium carbide of Cr 23 C 6 was precipitated. It was found that Cr which was effective for improving corrosion resistance was taken into the carbide by the precipitation of the chromium carbide and Cr near the precipitate was deficient, so that the corrosion resistance was impaired and corroded. In addition, if the quenching temperature or the tempering temperature is inappropriate, not only corrosion resistance but also toughness is greatly affected.
【0015】本発明者等は、これらのことから、本発明
鋼の耐食性および靭性を損なうことなく製造できる最善
の製造方法について種々検討した。種々の組成を有する
鋼材について、焼入れ温度と耐食性および靭性の関係を
検討した。種々の焼入れ温度で焼入れ熱処理した後、さ
らに400℃の焼戻し処理を施した試料の耐食性と靭性
を調査し、その結果を焼き入れ温度と未結合k*(Ti
およびNbと結合できなかったC量を表す指標)の関係
で整理し、プロットしたものが図1である。[0015] From these facts, the present inventors have studied variously the best manufacturing method which can be manufactured without impairing the corrosion resistance and toughness of the steel of the present invention. The relation between the quenching temperature, corrosion resistance and toughness of steel materials having various compositions was examined. After quenching heat treatment at various quenching temperatures, the corrosion resistance and toughness of the samples further subjected to tempering treatment at 400 ° C. were investigated, and the results were compared with the quenching temperature and the unbonded k * (Ti
FIG. 1 shows a plot obtained by rearranging and plotting the relationship based on the relationship between C and Nb, which is an index indicating the amount of C that could not bind to Nb.
【0016】図1のマップ図で明らかなように、耐食性
および靭性の両特性に優れる領域が認められた。この、
耐食性および靭性の両特性に優れる中心線を回帰計算し
て求めた結果、回帰計算値:Tとして(1)式が得られ
た。 T=280×k*+1200 ‥‥‥(1) ここで k*=log{C%−0.16(Nb%+Ti%)}‥‥‥(2)As is apparent from the map shown in FIG. 1, a region excellent in both corrosion resistance and toughness was recognized. this,
As a result of regression calculation of a center line excellent in both characteristics of corrosion resistance and toughness, Expression (1) was obtained as a regression calculation value: T. T = 280 × k * + 1200 {(1) where k * = log {C% −0.16 (Nb% + Ti%)} (2)
【0017】さらに、(1)式の回帰直線より、±50℃
以上離れると、優れた耐食性や靭性が得られない。すな
わち、回帰計算値:Tよりも、±50℃以上離れると、
低温側では耐食性が低下し、高温側では靭性が劣ってい
る。下限値を下回ると、Cr炭化物が固溶しきらず、未
固溶のCr炭化物が腐食の起点となって、耐食性を低下
させる。一方、上限を上回ると、Cr炭化物が完全に固
溶し耐食性が維持されるものの、オーステナイト粒が粗
大化し、焼入れ後の靭性に悪影響を及ぼす。以上の結果
から、優れた耐食性および靭性を得るための適正な焼入
れは、回帰計算値Tの±50℃の温度範囲で行う必要が
ある。Further, from the regression line of the equation (1), ± 50 ° C.
If the distance is more than the above, excellent corrosion resistance and toughness cannot be obtained. That is, when the regression calculation value is more than ± 50 ° C. away from T,
On the low temperature side, the corrosion resistance is reduced, and on the high temperature side, the toughness is poor. Below the lower limit, the Cr carbide does not completely form a solid solution, and the undissolved Cr carbide serves as a starting point of corrosion, thereby deteriorating the corrosion resistance. On the other hand, if the upper limit is exceeded, the Cr carbide completely dissolves and the corrosion resistance is maintained, but the austenite grains become coarse and adversely affect the toughness after quenching. From the above results, appropriate quenching for obtaining excellent corrosion resistance and toughness needs to be performed within a temperature range of ± 50 ° C. of the regression calculation value T.
【0018】また、回帰計算値Tの±50℃の最適温度
範囲で焼入れしても焼戻し温度によって、耐食性や靭性
が低下する場合があることも分かった。最適組成(C:
0.32質量%、Cr:15.56質量%、Nb:0.
45質量%)を有する鋼について、焼入れ温度を3水準
(何れもTの±50℃の最適温度範囲内)変えて、焼戻
し温度の耐食性および靭性に対する影響について調査し
た結果を、図2に示す。Further, it was also found that even when quenching was performed within the optimum temperature range of ± 50 ° C. of the regression calculation value T, the corrosion resistance and toughness sometimes decreased depending on the tempering temperature. Optimal composition (C:
0.32% by mass, Cr: 15.56% by mass, Nb: 0.
FIG. 2 shows the results of investigating the effect of the tempering temperature on corrosion resistance and toughness by changing the quenching temperature of steel having 45% by mass (three levels within the optimum temperature range of ± 50 ° C. of T).
【0019】100℃以下の焼戻し温度では、曲げ試験
で破断し、充分な靭性が得られておらず、150℃以上
で、密着曲げで破断せず靭性の改善が認められた。15
0℃未満の焼戻しでは、高温からの焼入れ時に変態・生
成したマルテンサイト相の歪みが十分に除去できず、織
機部材で要求される靭性まで回復できない。しかし、5
00℃を越えると、塩水噴霧試験で錆が発生し耐食性の
低下が認められた。この結果から、最適な焼入れ温度範
囲で処理しても、焼戻し温度によっては、耐食性および
靭性が損なわれる領域が存在することが確認できる。At a tempering temperature of 100 ° C. or less, the steel sheet broke in a bending test, failing to obtain sufficient toughness. Fifteen
When the tempering is performed at a temperature lower than 0 ° C., the distortion of the martensite phase transformed and generated during quenching from a high temperature cannot be sufficiently removed, and the toughness required for a loom member cannot be recovered. But 5
When the temperature exceeded 00 ° C., rust was generated in the salt spray test, and a decrease in corrosion resistance was observed. From this result, it can be confirmed that there is a region where the corrosion resistance and the toughness are impaired depending on the tempering temperature even when the treatment is performed in the optimum quenching temperature range.
【0020】すなわち、本発明は、最適な焼入れ温度で
熱処理し、さらに、150〜500℃の範囲で焼戻し熱
処理を施すことによって、優れた耐食性と靭性を得るこ
とになる。以上、本発明方法で優れた耐食性と靭性を得
るための最適な製造条件は、焼入れ温度が回帰計算値T
の±50℃で、焼戻し温度が150〜500℃で熱処理
を施すことになる。ここでTは上記(1)式により求ま
る。That is, in the present invention, excellent corrosion resistance and toughness can be obtained by performing a heat treatment at an optimum quenching temperature and further performing a tempering heat treatment in a range of 150 to 500 ° C. As described above, the optimum manufacturing conditions for obtaining excellent corrosion resistance and toughness by the method of the present invention are as follows:
And a heat treatment at a tempering temperature of 150 to 500 ° C. Here, T is obtained by the above equation (1).
【0021】[0021]
【実施例】以下に、実施例について説明する。表1に比
較鋼および発明鋼の主要成分を示す。材料は溶製後溶体
化処理して板厚5mmまでに熱間圧延し、さらに780
℃で9時間加熱後炉冷し、酸洗、冷間圧延、焼鈍を繰り
返し、板厚0.3mmに仕上げ、試験用素材とした。繊
維によるアブレッシブな磨耗に対する耐摩耗性の評価用
の試験片は、比較鋼および発明鋼の板厚0.3mmの素
材を、温度が回帰計算値Tの上下の各温度からの焼入れ
処理と、50〜600℃各温度での焼戻し処理の所定の
焼入れ・焼戻しの熱処理を施し、織機部材のフラッドヘ
ルドに加工して試験片とした。The embodiments will be described below. Table 1 shows the main components of the comparative steel and the invention steel. The material is subjected to solution treatment after melting, hot-rolled to a thickness of 5 mm, and 780
After heating at 9 ° C for 9 hours, the furnace was cooled, and pickling, cold rolling, and annealing were repeated to finish the sheet to a thickness of 0.3 mm, which was used as a test material. Test pieces for evaluating abrasion resistance against abrasion caused by fibers were prepared by quenching materials having a thickness of 0.3 mm of comparative steel and invention steel from each temperature above and below regression calculation value T, and 50%. A predetermined quenching / tempering heat treatment of tempering treatment at each temperature of up to 600 ° C. was performed, and the test piece was processed into a flood heald of a loom member.
【0022】 [0022]
【0023】前記した方法により、炭化物の析出量を測
定し、耐食性、靭性、および耐摩耗性を評価した。まず
表2に、本発明鋼および比較鋼のTi炭化物、Nb炭化
物の析出量と耐摩耗性指標M(%)の評価結果を示す。
比較鋼種6、7のようにTiおよびNbの添加量が少な
いとTi炭化物やNb炭化物の析出も少なく、耐摩耗性
指標Mが大きくなって耐摩耗性は得られなくなる。Ti
炭化物やNb炭化物の総析出量が多くなると、耐摩耗性
指標Mが小さくなって、優れた耐摩耗性を示している。
このTi炭化物とNb炭化物の合計析出量と耐磨耗性指
標Mの関係をグラフ化すると図3のようになる。炭化物
の合計析出量が増加すると耐磨耗性指標Mは急激に小さ
くなり、炭化物の合計析出量0.1質量%を境に耐磨耗
性指標Mは50%未満に、すなわち、従来品と比較して
2倍以上の寿命を持つフラッドヘルドが得られるので、
前記したように本発明方法における炭化物の合計析出量
を0.1質量%以上と規定したのである。The amount of carbide deposited was measured by the above-described method, and the corrosion resistance, toughness, and wear resistance were evaluated. First, Table 2 shows the results of evaluation of the precipitation amount of Ti carbide and Nb carbide and the wear resistance index M (%) of the steel of the present invention and the comparative steel.
When the addition amounts of Ti and Nb are small as in Comparative Steel Types 6 and 7, precipitation of Ti carbide and Nb carbide is also small, and the wear resistance index M is increased, so that wear resistance cannot be obtained. Ti
When the total precipitation amount of carbides and Nb carbides increases, the wear resistance index M decreases, indicating excellent wear resistance.
FIG. 3 is a graph showing the relationship between the total amount of Ti carbide and Nb carbide deposited and the wear resistance index M. When the total amount of carbide precipitation increases, the wear resistance index M sharply decreases, and the wear resistance index M becomes less than 50% at the boundary of the total carbide precipitation 0.1 mass%, that is, that of the conventional product. As you can get a flood heald with a service life more than twice as long,
As described above, the total amount of carbide precipitated in the method of the present invention is specified to be 0.1% by mass or more.
【0024】 [0024]
【0025】次に焼入れ温度・焼戻し温度と耐食性、靭
性の関係について評価した。その結果を、表3に示す。
所定の合金組成を有し、本発明で規定する(1)式を満
たす温度で焼入れ、150〜500℃の範囲で焼戻しを
行ったものは、耐摩耗性を有することは勿論、耐食性お
よび靭性にも優れていた。これに対し、焼入れ温度が規
定値よりも高い比較例では、靭性の点で満足できるもの
は得られなかった。また、焼入れ温度が低い比較例で
は、耐食性の点で満足できるものが得られなかった。さ
らに、焼戻し温度が高い比較例では耐食性の点で、焼戻
し温度が低い比較例では靭性の点で満足できるものが得
られなかった。なお、鋼種6、7は、前記したように硬
質炭化物を形成するTi、Nb含有量が少ないために、
Ti炭化物、Nb炭化物の析出も少なく、耐磨耗性の点
で所期の目的を達成できていない。Next, the relationship between the quenching temperature and the tempering temperature and the corrosion resistance and toughness were evaluated. Table 3 shows the results.
Those having a predetermined alloy composition, quenched at a temperature satisfying the formula (1) defined in the present invention, and tempered at a temperature in the range of 150 to 500 ° C. have not only abrasion resistance but also corrosion resistance and toughness. Was also excellent. On the other hand, in Comparative Examples in which the quenching temperature was higher than the specified value, no satisfactory one was obtained in terms of toughness. Further, in the comparative example having a low quenching temperature, no satisfactory corrosion resistance was obtained. Furthermore, a comparative example having a high tempering temperature could not obtain satisfactory corrosion resistance, and a comparative example having a low tempering temperature could not obtain satisfactory toughness. Steel types 6 and 7 have low contents of Ti and Nb which form hard carbide as described above.
Precipitation of Ti carbide and Nb carbide is small, and the intended purpose cannot be achieved in terms of abrasion resistance.
【0026】 [0026]
【0027】[0027]
【発明の効果】以上に説明したように、本発明方法によ
れば、Tiおよび/またはNbを含有させて硬質の炭化
物を所定量以上析出させることにより、繊維によるアブ
レッシブな磨耗に対して優れた耐摩耗性を持たせるとと
もに、焼入れおよび焼戻しの処理を最適な温度で行うこ
とにより、耐食性と靭性を向上させることができる。こ
れにより、織物の繊維による磨耗が問題になっている織
機類の部材、特に、フラットヘルド、ドロッパー、筬
羽、変形筬、リード等、アブレッシブな磨耗に対する耐
摩耗性が要求される部位での磨耗対策が可能になるとと
もに、織機機械を始めこの種の関連機器そのものの寿命
延長に多大な貢献が期待できる。As described above, according to the method of the present invention, by containing Ti and / or Nb to precipitate a predetermined amount or more of hard carbide, excellent abrasion due to fibers is prevented. Corrosion resistance and toughness can be improved by imparting abrasion resistance and performing quenching and tempering treatments at optimal temperatures. As a result, abrasion of looms caused by the fiber of the woven fabric is a problem, especially at parts where abrasion resistance is required for abrasive wear, such as flat healds, droppers, reed feathers, deformed reeds, and reeds. Measures can be taken, and a great contribution can be expected to extend the service life of this type of related equipment such as a loom machine.
【図1】 焼入れ温度と耐食性および靭性の関係を示す
図。FIG. 1 is a graph showing a relationship between a quenching temperature and corrosion resistance and toughness.
【図2】 焼戻し温度と耐食性および靭性の関係を示す
図。FIG. 2 is a graph showing a relationship between a tempering temperature and corrosion resistance and toughness.
【図3】 Ti炭化物およびNb炭化物の合計析出量と
耐摩耗性の関係を示す図。FIG. 3 is a graph showing the relationship between the total precipitation amount of Ti carbide and Nb carbide and wear resistance.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 森川 広 山口県新南陽市野村南町4976番地 日新製 鋼株式会社ステンレス事業本部内 (72)発明者 山内 隆 山口県新南陽市野村南町4976番地 日新製 鋼株式会社ステンレス事業本部内 ──────────────────────────────────────────────────続 き Continuing on the front page (72) Inventor Hiroshi Morikawa 4976 Nomura Minamicho, Shinnanyo-shi, Yamaguchi Prefecture Inside Nisshin Steel Corporation Stainless Steel Business Headquarters (72) Inventor Takashi Yamauchi 4976 Nomuraminamicho, Shinnanyo-shi, Yamaguchi Prefecture Sun New Steel Co., Ltd. Stainless Business Division
Claims (1)
〜0.5質量%を含有し、さらにTiおよび/またはN
bを、Ti:単独で0.05〜1質量%、Nb:単独で
0.05〜1質量%或いはTi+Nb:合計量で0.0
5〜1質量%を含み、残部が実質的にFeの組成からな
る鋼に、下記(1)、(2)式により求まるTに対し
て、焼入れ温度がT±50℃、焼戻し温度が150〜5
00℃で熱処理を施し、鋼の組織をマルテンサイト相と
するとともに、鋼のマトリックス中にTiおよび/また
はNbの炭化物を0.1質量%以上分散析出させること
を特徴とする耐食性と靭性および耐繊維磨耗性に優れた
高強度鋼製織機部材用素材の製造方法。ここで、 T=280×k*+1200 ‥‥‥(1) k*=log{C%−0.16(Nb%+Ti%)}‥‥‥(2)1. Cr: 10 to 18% by mass, C: 0.05
0.50.5% by mass and further containing Ti and / or N
b: Ti: 0.05 to 1% by mass alone, Nb: 0.05 to 1% by mass alone or Ti + Nb: 0.0 in total amount
A steel containing 5 to 1% by mass and a balance substantially composed of Fe has a quenching temperature of T ± 50 ° C. and a tempering temperature of 150 to 150 with respect to T determined by the following formulas (1) and (2). 5
A heat treatment is performed at 00 ° C. to change the structure of the steel into a martensitic phase and to precipitate and precipitate 0.1% by mass or more of carbides of Ti and / or Nb in a matrix of the steel. A method for manufacturing a material for a high-strength steel loom member having excellent fiber wear properties. Here, T = 280 × k * + 1200 {(1) k * = log {C% −0.16 (Nb% + Ti%)} (2)
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Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2006037173A (en) * | 2004-07-28 | 2006-02-09 | Nisshin Steel Co Ltd | Martensitic stainless steel for dicing saw tape frame and production method therefor |
JP2014192012A (en) * | 2013-03-27 | 2014-10-06 | Nisshin Steel Co Ltd | Stainless steel sheet having low contact resistance |
JP2020056078A (en) * | 2018-10-03 | 2020-04-09 | 日鉄ステンレス株式会社 | Martensitic stainless steel material, manufacturing method therefor, and slide member |
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JPH10110248A (en) * | 1996-10-03 | 1998-04-28 | Hitachi Metals Ltd | High hardness martensitic stainless steel excellent in pitting corrosion resistance |
JP2000192197A (en) * | 1998-12-24 | 2000-07-11 | Nisshin Steel Co Ltd | Wear resistant steel |
JP2000192198A (en) * | 1998-12-24 | 2000-07-11 | Nisshin Steel Co Ltd | Loom member made of steel |
JP2000226641A (en) * | 1999-02-05 | 2000-08-15 | Nsk Ltd | Rolling device |
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JPH07278758A (en) * | 1994-04-13 | 1995-10-24 | Nippon Steel Corp | Stainless steel for engine gasket and its production |
JPH108904A (en) * | 1996-06-19 | 1998-01-13 | Hitachi Ltd | Gas turbine disk, and gas turbine |
JPH10110248A (en) * | 1996-10-03 | 1998-04-28 | Hitachi Metals Ltd | High hardness martensitic stainless steel excellent in pitting corrosion resistance |
JP2000192197A (en) * | 1998-12-24 | 2000-07-11 | Nisshin Steel Co Ltd | Wear resistant steel |
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Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2006037173A (en) * | 2004-07-28 | 2006-02-09 | Nisshin Steel Co Ltd | Martensitic stainless steel for dicing saw tape frame and production method therefor |
JP4587731B2 (en) * | 2004-07-28 | 2010-11-24 | 日新製鋼株式会社 | Martensitic stainless steel for dicing saw tape frame and manufacturing method thereof |
JP2014192012A (en) * | 2013-03-27 | 2014-10-06 | Nisshin Steel Co Ltd | Stainless steel sheet having low contact resistance |
JP2020056078A (en) * | 2018-10-03 | 2020-04-09 | 日鉄ステンレス株式会社 | Martensitic stainless steel material, manufacturing method therefor, and slide member |
JP7134052B2 (en) | 2018-10-03 | 2022-09-09 | 日鉄ステンレス株式会社 | MARTENSITE STAINLESS STEEL MATERIAL AND MANUFACTURING METHOD THEREOF AND SLIDING MEMBER |
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