JP2002180222A - Immersion member for hot dip metal coating bath - Google Patents

Immersion member for hot dip metal coating bath

Info

Publication number
JP2002180222A
JP2002180222A JP2000377798A JP2000377798A JP2002180222A JP 2002180222 A JP2002180222 A JP 2002180222A JP 2000377798 A JP2000377798 A JP 2000377798A JP 2000377798 A JP2000377798 A JP 2000377798A JP 2002180222 A JP2002180222 A JP 2002180222A
Authority
JP
Japan
Prior art keywords
member
molten metal
metal plating
plating bath
immersion member
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.)
Granted
Application number
JP2000377798A
Other languages
Japanese (ja)
Other versions
JP4460144B2 (en
Inventor
Shigeharu Matsubayashi
Tetsuo Nose
Shigeru Shibamoto
重治 松林
芝本  茂
哲郎 野瀬
Original Assignee
Nippon Steel Corp
新日本製鐵株式会社
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Nippon Steel Corp, 新日本製鐵株式会社 filed Critical Nippon Steel Corp
Priority to JP2000377798A priority Critical patent/JP4460144B2/en
Publication of JP2002180222A publication Critical patent/JP2002180222A/en
Application granted granted Critical
Publication of JP4460144B2 publication Critical patent/JP4460144B2/en
Application status is Expired - Fee Related legal-status Critical
Anticipated expiration legal-status Critical

Links

Abstract

PROBLEM TO BE SOLVED: To provide an immersion member for hot dip metal coating bath by which durability against thermal shock/repeated thermal fatigue can be improved and replacement at wear and breakage can be facilitated. SOLUTION: The immersion member for hot dip metal coating bath is provided to a pot roll device immersed in a hot dip metal coating bath. This immersion member is a silicon nitride type or silicon carbide type ceramic member fitted to a part or the whole of a sliding part at least of a pot-roll shaft sleeve member or a bearing member of the pot roll device.

Description

【発明の詳細な説明】 DETAILED DESCRIPTION OF THE INVENTION

【0001】 [0001]

【発明の属する技術分野】本発明は、鋼板等の連続溶融金属めっき装置における溶融金属めっき浴用浸漬部材に関する。 The present invention relates to relates to a molten metal plating bath immersion member in a continuous molten metal plating apparatus such as a steel plate.

【0002】 [0002]

【従来の技術】金属めっき板を得る方法として、図1に示すように、加熱炉で加熱焼鈍された金属板を溶融金属槽に導き、金属板へ溶融金属をめっきし、ポットロール及びガイドロールを介して、これを引き上げ連続的に金属めっき板を得る方法が汎用されている。 2. Description of the Related Art As a method for obtaining a metal plated plate, as shown in FIG. 1, leads to a metal plate that is heated annealed in a heating furnace to a molten metal bath, and plating the molten metal to the metal plate, the pot roll and the guide roll through the process have been widely obtained pulled continuously the metal plating plate it. より詳しくは、連続溶融金属めっき装置による金属板へのめっき方法は、金属板として鋼板を用いた場合、前処理として表面を洗浄・活性化した鋼板を溶融金属浴中に挿入して、 More specifically, the plating process of the metal plate by continuous molten metal plating apparatus, when a steel sheet as a metal plate, by inserting the steel sheet was washed-activate the surface as a pretreatment in the molten metal bath,
浴中のポットロールで方向を変えた後、鋼板の幅方向の反りを抑えるために2本のガイドロールの間を通過させる。 After changing direction in the pot rolls in the bath, passing between two guide rolls in order to reduce the width direction of the warp of the steel sheet. この後、さらに鋼板を上方に引き上げ、めっき浴の直上で鋼板表面に付着した余分の溶融金属を高圧ガスのワイピング等により除去して、所定のめっき量に調整して、溶融金属めっき鋼板を製造するものである。 Thereafter, further pulling the steel sheet upwardly to remove the excess molten metal adhering to the steel sheet surface just above the plating bath by wiping or the like of the high-pressure gas, it is adjusted to a predetermined amount of plating, producing a molten metal plated steel sheet it is intended to.

【0003】この溶融金属めっき浴に浸漬されるポットロールの軸受部材及び軸部スリーブ部材には、一般的に、耐食性の良好な24Cr-12Ni系ステンレス鋼が用いられている。 [0003] bearing member and the shaft portion the sleeve member of the pot roll is immersed in the molten metal plating bath, typically corrosion resistance good 24Cr-12Ni-based stainless steel is used. ステンレス鋼は、溶融亜鉛、溶融アルミニウム等の溶融金属との反応性が低く、耐食性は良好であるが、耐摩耗性は充分とは言えず、特に、軸受部材は、軸部スリーブ部材と極狭い範囲(上側の半分)で常時接触しているため、摩耗量は軸部スリーブ部材より大きく、寿命は4〜8日程度と短い。 Stainless steel, molten zinc, low reactivity with molten metals such as molten aluminum, the corrosion resistance is good, the abrasion resistance can not be said to be sufficient, in particular, the bearing member is very narrow and the shaft portion the sleeve member due to the constant contact with the range (upper half), the wear amount is larger than the shaft portion the sleeve member, life and short about 4-8 days. 軸受部材の摩耗が進行すると、 When the wear of the bearing member progresses,
鋼板にバタツキ等が発生し、良好なめっきが行えないため、該部材を溶融金属めっき浴中から引き上げ、軸受部材を交換しなければならない。 Fluttering or the like occurs in the steel sheet, because not be a good plating, pulling the member from the molten metal plating bath must be replaced bearing member. そのため、溶融金属めっき浴中に浸漬されているポットロール等の他の部材に異常が無くても、操業を停止し、溶融金属めっき浴中に浸漬されている部品全体を引き上げる必要がある。 Therefore, even if there is no abnormality in the other members such as a pot roll which is immersed in the molten metal plating bath, to stop the operation, it is necessary to raise the entire part being immersed in the molten metal plating bath. この際に、浴温から室温へ急激に冷却されるため、熱衝撃破損等のダメージが他の部品に発生することもあり、部品全体を一括交換する場合もあり、生産上の損失は極めて大きい。 At this time, because it is rapidly cooled from the bath temperature to room temperature, sometimes damage thermal shock breakage occurs to other parts, sometimes collectively replace the entire component, the loss in production is extremely large . このため、溶融金属めっき浴中で使用されるロール寿命の延長を図る様々な提案がなされている。 Therefore, various proposals have been made to reduce the extension of the roll life used in molten metal plating bath.

【0004】特開平3-253547号公報や特開平5-44002号公報では、溶融亜鉛浴中での軸受部材及び軸部スリーブ部材に、アルミナ又は窒化珪素・サイアロンを用い、回転するポットロールを外部から回転駆動する提案がなされている。 [0004] In JP-A 3-253547 and JP 5-44002 and JP outside bearing member and the shaft portion the sleeve member in the molten zinc bath, with alumina or silicon nitride-sialon, the pot roll rotating proposal for rotationally driving have been made. しかしながら、該提案では、溶融金属として亜鉛のみを取り上げ、摺動摩耗量及び摩耗係数のみを選定基準としており、耐熱衝撃性や溶融金属との濡れ性等については考慮されていない。 However, in the proposal, taken up zinc only as the molten metal, the only sliding wear amount and wear coefficients has the selection criteria, is not considered, etc. wettability and thermal shock resistance and the molten metal. さらに、アルミナ又は窒化珪素・サイアロンセラミックスに関しても、組成、焼成条件(密度、組織)、機械的特性、摺動面粗さ等の諸特性についての最適条件の記載はない。 Furthermore, with regard alumina or silicon nitride-sialon ceramics, composition, firing conditions (density, tissue), mechanical properties, there is no description of the optimum conditions for various properties such as the sliding surface roughness.

【0005】また、モノリシック炭化珪素やジルコニアセラミックスは、窒化珪素やサイアロンより熱衝撃性に劣ることが知られている。 Further, monolithic silicon carbide, zirconia ceramics are known to be inferior in thermal shock resistance than silicon nitride or sialon.

【0006】上記従来技術で開示されている内容に基づき、一般的な焼成助剤であるイットリア、アルミナを用いて、相対密度比99%まで緻密化した市販の窒化珪素セラミックスで、溶融アルミニウム浴中における摺動及び熱衝撃試験を行った結果、亜鉛浴中の摩耗量を大きく上回り、溶融アルミニウム浴中からの空冷を3回行っただけで破損した。 [0006] The basis of the contents disclosed in the prior art, yttria is a common firing aids, with alumina, a commercial silicon nitride ceramic which is densified to a relative density ratio of 99%, the molten aluminum bath As a result of sliding and thermal shock tests in, far exceeding the amount of wear of the zinc bath, broken only by three times the air cooling from the molten aluminum bath.

【0007】 [0007]

【発明が解決しようとする課題】すべり軸受に関する上記技術は、軸受部材及び軸部スリーブ部材の互いに接触する面を、ステンレス鋼に比べれば溶融金属浴中での耐食性が良好で、かつ、高硬度のセラミックスでコーティングしたり、または、サーメット、超硬合金やセラミックス焼結体等とすることで、軸受の長寿命化を図ろうとしたものである。 [0006] The above relates to a sliding bearing technology, the surface in contact with each other of the bearing member and the shaft portion the sleeve member, it is a good corrosion resistance in molten metal bath compared to stainless steel, and high hardness or coated with a ceramic, or by a cermet, cemented carbide or a ceramic sintered body or the like, in which the attempt is made to extend the life of the bearing. しかし、溶融金属めっき浴用部材にとって、軸受部材と軸部スリーブ部材の最適な組合せは、 However, the optimum combination for the molten metal plating bath member, the bearing member and the shaft portion the sleeve member,
材料の耐熱衝撃性、高靭性、難濡れ性等の特性を考慮することがはるかに重要な選定要素である。 Thermal shock resistance of the material, high toughness, a selection element far more important to consider characteristics such as hardly wettable. 数百℃に加熱されたポットロールの引上げ時の空冷に伴う熱衝撃や繰返し熱疲労に対する耐久性を高め、溶融金属の中でも特に溶融アルミニウムに対する濡れ性を制御することが不可欠である。 Enhanced resistance to thermal shock and repeated thermal fatigue caused by the air at the time of pulling the heated pot roll hundreds ° C., it is essential to control the wettability with respect to particular molten aluminum among the molten metal.

【0008】また、取り替え作業が迅速に行えれば、操業上の機会損失を低減できるため、当該部材の交換を簡便に行える構造とすることも望まれている。 [0008] In addition, replacement work quickly Okonaere, it is possible to reduce the opportunity loss on operations, it is also desired to have a structure that allows the replacement of the member conveniently.

【0009】そこで、本発明の目的は、熱衝撃や繰り返し熱疲労に対する耐久性を大幅に向上させ、併せて、摩耗・破損時の交換作業を著しく簡便にした溶融金属めっき浴用浸漬部材を提供することにある。 An object of the present invention dramatically improves the durability against thermal shock and repeated thermal fatigue, together, provide a molten metal plating bath immersion member which is significantly simplify the exchange work during wear and damage It lies in the fact.

【0010】 [0010]

【課題を解決するための手段】本発明は、上記課題を解決して、溶融金属めっき浴中で長時間安定して繰り返し使用でき、交換作業時には簡便に取り替えられる溶融金属めっき浴用浸漬部材を提供することを目的としてなされたものであり、(1)溶融金属めっき浴に浸漬されるポットロール装置に付設された浸漬部材であって、該浸漬部材が、該ポットロール設備の少なくともポットロール軸部スリーブ部材と軸受部材の摺動する部分の一部又は全部に嵌合してなる、窒化珪素系又は炭化珪素系のセラミックス部材であることを特徴とする溶融金属めっき浴用浸漬部材、(2)前記浸漬部材が、複数の柱状部材からなる(1)記載の溶融金属めっき浴用浸漬部材、 Means for Solving the Problems The present invention is to solve the above problems, repeated and long-term stability in the molten metal plating bath can be used, providing a molten metal plating bath immersion member which is conveniently replaced during replacement it has been made for the purpose of, (1) a dipping member that is attached to the pot roll apparatus which is immersed in the molten metal plating bath, the immersion member has at least a pot roll axis of the pot roll equipment becomes fitted in some or all of the sliding portion of the sleeve member and the bearing member, the molten metal plating bath immersion member which is a ceramic member silicon nitride or silicon carbide, (2) the immersion member comprises a plurality of columnar members (1) molten metal plating bath immersion member according,
(3)前記柱状部材が、前記軸受部の軸方向に嵌合してなる(2)記載の溶融金属めっき浴用浸漬部材、(4)前記柱状部材の回転方向の摺動面が、平面又は前記ポットロール軸部スリーブ部材の曲率半径以上の円弧状面である(3)記載の溶融金属めっき浴用浸漬部材、(5)前記柱状部材が、前記ポットロール軸部スリーブ部材に軸方向に嵌合してなる(2)記載の溶融金属めっき浴用浸漬部材、(6)前記柱状部材の摺動面が、前記軸受部材の曲率半径以下の円弧状面である(5)記載の溶融金属めっき浴用浸漬部材、(7)前記柱状部材の軸方向の摺動面が、凹凸状及び/又は波形状で、凸部の摺動面高さが軸方向で揃った形状である(3)又は(5)に記載の溶融金属めっき浴用浸漬部材、(8)前記セラミックス部材が、理論密度の95%以上の焼結体密度であ (3) the columnar member, the fitted comprising in the axial direction of the bearing portion (2) molten metal plating bath immersion member according, (4) the sliding surface of the rotating direction of the columnar members, flat or the pot is arcuate surface over the radius of curvature of the roll shaft sleeve member (3) molten metal plating bath immersion member according, (5) the columnar member is fitted in the axial direction on the pot roll shaft sleeve member comprising Te (2) molten metal plating bath immersion member according, (6) the sliding surface of the columnar member, wherein an arc-shaped surface of a curvature radius below the bearing member (5) molten metal plating bath immersion member according , (7) the sliding surface of the axial direction of the columnar members, in uneven and / or waveform shape, the sliding surface height of the convex portion has a shape of uniform in the axial direction (3) or (5) molten metal plating bath immersion member according, (8) the ceramic member is 95% or more of the sintered body density der of theoretical density る(1)〜(7)に記載の溶融金属めっき浴用浸漬部材、(9)前記セラミックス部材が、クロム化合物を体積分率で1〜8%含有する窒化珪素質焼結体である(8)記載の溶融金属めっき浴用浸漬部材、(10)前記クロム化合物が、窒化クロムである That (1) to (7) molten metal plating bath immersion member according to, is (9) the ceramic member is a silicon nitride sintered body containing 1-8% by volume fraction of the chromium compound (8) molten metal plating bath immersion member according, is (10) the chromium compound, is chromium nitride
(9)記載の溶融金属めっき浴用浸漬部材、(11)前記セラミックス部材が、複合金属ホウ化物を体積分率で20 (9) molten metal plating bath immersion member according, (11) The ceramic member, a composite metal boride in a volume fraction 20
〜70%含有する炭化珪素質焼結体である(8)記載の溶融金属めっき浴用浸漬部材、(12)前記複合金属ホウ化物が、Ti-Zr-B固溶体及び/又はTi-Hf-B固溶体である(11) Silicon carbide sintered body containing 70% (8) molten metal plating bath immersion member according, (12) the composite metal boride, Ti-Zr-B solid solution and / or Ti-Hf-B solid solution is (11)
記載の溶融金属めっき浴用浸漬部材、を要旨とするものである。 Molten metal plating bath immersion member according, it is an gist.

【0011】 [0011]

【発明の実施の形態】本発明者らは、特開平3-253547号公報や特開平5-44402号公報で提案された溶融亜鉛浴中ロール軸受を見直し、亜鉛に比べ高融点の溶融アルミニウム浴中でも、従来技術では困難であった摺動摩耗及び熱疲労部周囲のチッピングや割れ等の欠損を抑えることができ、ロール引き上げ後に着地させる際の機械的衝撃、及び、浴中から取り出され空冷されることで繰り返し加わる熱応力に対する耐久性に優れた軸受部材の構造・形状並びに材質を見出した。 DETAILED DESCRIPTION OF THE INVENTION The present inventors have reviewed the role bearing in a molten zinc bath, which is proposed in JP-A-3-253547 and JP 5-44402 and JP-molten aluminum bath refractory compared with zinc Above all, in the prior art can be suppressed defects of chipping and cracks around the sliding wear and thermal fatigue portion was difficult, mechanical shock at the time of landing after a role pulling, and are air-cooled withdrawn from the bath It found structure and shape as well as the material of the bearing member having excellent durability against thermal stress applied repeatedly in Rukoto. そして、これらのチッピングや割れ等の欠損は、熱衝撃及び機械的衝撃により生成、進展するものであり、部材に空孔が多い場合、低強度、低靭性、溶融金属との濡れ性が良い場合、低熱伝導、低耐熱衝撃、摺動面が粗い場合、等に顕著であること、また、摺動摩耗は、摺動部が面ではなく、線接触もしく点接触である場合等に顕著に抑制されることを確認した。 Then, defects such as these chipping or cracking, generated by thermal shock and mechanical shock, which develops, if holes are often members, low intensity, low toughness, if good wettability with molten metal , low thermal conductivity, when the low thermal shock, the sliding surface is rough, etc. it is remarkable, also, the sliding wear, rather than the sliding portion surface, notably in such case line contact is properly point contact It was confirmed to be suppressed.

【0012】本発明の溶融金属めっき浴用浸漬部材は、 [0012] molten metal plating bath immersion member of the present invention,
溶融金属めっき浴に浸漬されるポットロール装置に付設された浸漬部材であって、該浸漬部材が、該ポットロール設備の少なくともポットロール軸部スリーブ部材または軸受部材の摺動する部分の一部又は全部に嵌合してなる、窒化珪素系又は炭化珪素系のセラミックス部材である。 A dipping member that is attached to the pot roll apparatus which is immersed in the molten metal plating bath, the immersion member is a part of the sliding portion of at least the pot roll shaft sleeve member or the bearing member of the pot roll equipment or becomes fitted to all, a ceramic member silicon nitride or silicon carbide. 溶融金属めっき浴用浸漬部材は、高耐熱衝撃性・高靭性・高耐摩耗性の観点から窒化珪素系または炭化珪素系セラミックスが好ましい。 Molten metal plating bath immersion member, high thermal shock resistance and high toughness and high wear resistance in view of a silicon nitride based or silicon carbide based ceramics are preferred.

【0013】また、浸漬部材の取扱い易さの観点から、 [0013] In addition, from the point of view of ease of handling of the immersion member,
柱状部材を複数嵌合することが好ましい。 It is preferable that a plurality fitting columnar member. 埋め込み形状について、ポットロールと直接摺動する面が平面またはポットロール軸部スリーブ部材の曲率半径以上の上に凸な円弧状面が好ましいが、特に限定するものではなく、 Embedding shape and convex arcuate surface over more than the radius of curvature of the pot roll directly sliding surfaces are planar or pot roll shaft sleeve member is preferred, not particularly limited,
軸に垂直方向の断面形状が四角形以上の多角形や半円形、円形でも良い。 Polygonal or semicircular vertical cross section of the above rectangle to the axis, may be circular. 回転方向に柱状部材を配置することは好適ではない。 Placing the columnar member in the rotation direction is not preferred. 圧縮応力負荷に限定するために、回転方向と同じ方向に線接触ならびに点接触させる配置を推奨する。 To limit the compression stress load is recommended arrangement for line contact and point contact in the same direction as the direction of rotation. また、ポットロール軸部スリーブ部材の曲率半径以下の上に凸な円弧状面もしくは曲率半径以上の凹な円弧状面では埋め込み材に圧縮応力以外が負荷され、圧縮に比べて破損の確率が高くなることが予想される。 Further, the load is non-compressive stress to the filling material in the concave arcuate surface above the convex arcuate surface or the curvature radius on the curvature radius or less of the pot roll shaft sleeve member, high probability of breakage in comparison to compression it is expected to be. 好ましくは、下辺が上辺に比べて長い等脚台形を断面とするセラミックス製軸受け片を使用すれば、楔(くさび)や接着剤等を使用せず、位置決めすることが容易であり、 Preferably, the use of ceramic bearing piece lower side and cross-sectional long isosceles trapezoid than the upper side, the wedge without the (wedge) or an adhesive, it is easy to position,
圧縮応力のみを負荷させることが可能である。 It is possible to load only the compressive stress. さらに、 further,
図2の iii)〜iv)に示したように柱状の埋め込み材の回転軸と平行な方向に凹凸または波形を順次付与することにより、線接触から点接触にすることが可能であり、めっき浴の流動を促進することが可能になることから回転が円滑なものになることが想定される。 By sequentially applying an uneven or waveform as in a direction parallel to the rotation axis of the columnar filling material shown in iii) to iv) of FIG. 2, it is possible to point contact from a line contact, the plating bath rotation since it becomes possible to facilitate the flow is assumed to be something smooth. 隣接する埋め込み材との凹凸または波形パターンを逆相にするか同相にするかはめっき浴の流動性やポットロールの回転数によって対応すべきである。 Is an uneven or corrugated pattern to the adjacent filling material or in or phase reversed phase should correspond with the rotational speed of the fluidity and pots roll plating bath. このような形状にすることにより、軸受け部での溶融金属溜りができにくくなり、補修作業等の作業効率を改善できる。 By such a shape, hardly able molten metal pool at the bearing portion can improve the working efficiency of such repair work.

【0014】また、ポットロールの回転軸部材の摺動部について、軸受け部材と同じセラミックス材または超硬粒子を結合金属(銅、チタン、亜鉛等のバインダー)中に分散させたものでも構わない。 Further, the sliding portion of the rotary shaft member of the pot roll, may the same ceramic material or cemented hard particle bearing member bound metal be those dispersed in (copper, titanium, a binder such as zinc). この場合も、上記と同様に軸の曲率より軸受け側の曲率が大きくなければ、軸受け部材に押し広げようとする引っ張り応力が印加されることとなり、全く不適である。 Again, if there is no large bearing side curvature than the curvature of the same axially, will be tensile stress to Grow pushing the bearing member is applied, it is quite unsuitable. 平面もしくは円弧状であれば加工が容易であり、曲率が大きい場合はポットロール側の回転軸の安定性が僅かながら高まることが容易に予想される。 It is easily processed if a plan or arcuate, when the curvature is large, that the stability of the rotational axis of the pot roll side is increased slightly be easily predicted. また、回転軸に嵌合する場合は軸受けの曲率より回転軸側の埋め込み材の曲率が大きくなれば、埋め込み材の形状が極端に大きくなるか、薄過ぎることになるため好適ではない。 Also, the greater the curvature of the rotation axis side of the filling material than the curvature of the bearing when fitted to the rotary shaft, or the shape of the embedded material is extremely large, it is not preferable because it would be too thin.

【0015】そして、この部材を上記形状とすることにより、該部材を嵌合される金属製部材との熱膨張係数差によって生じる浴中および空冷時の伸縮差の絶対値を小さくでき、セラミックス側に加わる圧縮または引張応力を低減することに加え、該セラミックス部材を製造する上での緻密化を容易にする効用をもたらす。 [0015] Then, by the member and the shape, can reduce the absolute value of the expansion difference during bath and air caused by the difference in thermal expansion coefficient between the metallic member fitted to the member, the ceramic side in addition to reducing the compressive or tensile stress applied to the results in the utility that facilitates densification in producing the ceramic member. 嵌合する部材の形状は肉厚が5mm以上20mm以下で、2本以上の柱状部材を用いることが好ましい。 Shape the thickness of the fitting members are at 5mm or more 20mm or less, it is preferable to use two or more columnar members. 5mm未満では、セラミックス部材の圧縮強度も低く、使用後に摺動面に生じた摩耗痕を研磨し、リサイクル利用するときにもトータル寿命が短くなり好適ではない。 If it is less than 5 mm, the compressive strength of the ceramic member is low, polished wear scar generated on the sliding surface after use, not preferred shortens the total life when recycled. 1本の柱状部材のみでは、回転時の安定性が全く得られず相応しくない。 One only by the columnar members, stability during rotation is not obtained at all unsuitable. また、ロールアームをハンドリングする時の機械的衝撃に対する強度付与の点からも5〜20mm厚みの範囲が好ましい。 Further, the range of 5~20mm thickness in terms of strength imparted against mechanical shock when handling the roll arm is preferred. 幅については、ポットロール径の大小や柱状部材の嵌合せ本数に依存するが10〜30mmが好適である。 The width depends on the fitting combined number of pot roll diameter and small and columnar member is preferably 10 to 30 mm. さらに柱状部材の長さは該部材を嵌合される金属製部材のスリーブ長さによって一義的に求められる。 Furthermore the length of the columnar member is uniquely determined by the sleeve length of the metal member to be fitted to the member. 一般的には、80〜200mm In general, 80~200mm
程度がよく用いられている。 The degree is often used.

【0016】図3に示したように、セラミックス製軸受けを保持するために用いる金属製リング部材との間隙に噛み込まれた溶融金属との熱膨張係数差に起因する圧縮または引張応力を軽減するため、セラミックス部材と金属部材との嵌合部の間隙は1mm以下にすることが好ましい。 [0016] As shown in FIG. 3, to reduce the compression or tensile stress due to the difference in thermal expansion coefficient between the molten metal bitten into the gap between the metal ring member used to hold the ceramic bearing Therefore, the gap of the fitting portion between the ceramic member and the metallic member is preferably set to 1mm or less.

【0017】上記とは全く逆に、軸受け部が円形の一体品で構成され、軸受けの曲率以下の上に凸な円弧状面を有する柱状部材をポットロール軸部スリーブに嵌合することも可能である。 [0017] completely contrary to the above, bearing portion is constituted by a circular single piece, fitting the columnar member having a convex arcuate surface over the following the curvature of the bearing pot roll shaft sleeve also it is. 但し、軸受け部に埋め込む際に十分な固定強度が得られるように配慮が必要で、軸受け部の接触時の摩擦抵抗を軽減するためには摺動部は平面ではなく軸受け部の内径より曲率の小なる円弧状曲面が最も好適である。 However, consideration as sufficient fixing strength can be obtained when embedding the bearing portion is required, the sliding portion in order to reduce the frictional resistance at the time of contact of the bearing portion of the curvature than the inner diameter of the bearing portion not flat small becomes arcuate curved surface being most preferred. さらに、全周に渡って嵌合することが必要であり、2本以上、好ましくは3本以上、より好ましくは Furthermore, it is necessary to fit the entire circumference, two or more, preferably three or more, more preferably
5本以上で安定した回転が得られる。 Stable rotation is obtained in 5 or more. 2本未満では、柱状部材以外の部分で摺動する機会が増え、金属製の軸部スリーブ材が柱状部材より選択的に摩耗し、寿命の延長は望めなくなる。 Is less than two, more opportunities to slide portions other than the columnar member, a metal shank sleeve member is selectively worn than the columnar member, not be expected prolongation of life.

【0018】溶融金属との低い濡れ性、高熱伝導、高耐熱衝撃、耐摩耗などの特性を同時に向上させる方法としては、充分緻密なSiCまたはSi 3 N 4焼結体において、第2 The low wettability with molten metal, high thermal conductivity, high thermal shock, as a method of improving the properties such as wear resistance at the same time, in sufficient dense SiC or Si 3 N 4 sintered body, the second
相(Ti-Zr-B固溶体やCr 2 N等に代表されるクロム化合物など)形成による焼結体組織を制御することが効果的である。 It is effective to control the phase (Ti-Zr-B solid solution and Cr 2 N or the like typified by a chromium compound) sintered body tissue by forming. このような焼結体組織は、従来技術に記載されたモノリシック窒化珪素・モノリシックサイアロンからなる軸受けより、チッピング・割れ等の耐欠損性を著しく向上させる作用も同時に付与することができる。 Such sintered body tissue can be imparted from the bearings made of monolithic silicon nitride monolithic sialon described in the prior art, at the same time also acts to significantly improve the fracture resistance of chipping and other defects. Ti x Zr y B Ti x Zr y B
2に代表される金属複合ホウ化物は、炭化珪素焼結体中に分散することにより、高靭性化及び高硬度化する効果を有し、耐欠損性や耐摩耗性を飛躍的に向上させる。 Metal composite borides typified by 2, by dispersing in the silicon carbide sintered body, has the effect of high toughness and high hardness, drastically improve the chipping resistance and wear resistance. Cr Cr
2 Nに代表されるクロム化合物は、窒化珪素質焼結体中に分散することにより、高靭性化する効果を有し、高温強度を飛躍的に向上させ、耐クリープ性や耐食性に優れる特性を付与する。 Chromium compound represented by 2 N, by dispersing in the silicon nitride sintered body, has the effect of higher toughness, dramatically improves the high temperature strength, a property which is excellent in creep resistance and corrosion resistance Give. 一方で、溶融金属に対する濡れ性を低下させる作用を持つ。 On the other hand, it has the effect of reducing the wettability to the molten metal.

【0019】摺動部の面粗さに関し、溶融アルミニウムが付着し難く、かつ動摩擦係数を軽減するためにR max [0019] For surface roughness of the sliding portion, R max ≦ To reduce the molten aluminum is not easily adhere, and the dynamic friction coefficient
0.2μmに仕上げることが有効である。 It is effective to finish to 0.2μm. 0.2μmを超えると、溶融アルミニウムとの濡れ性が低くても、機械的に付着割合が上昇し、動摩擦係数を著しく増大させるため、好ましくない。 Exceeds 0.2 [mu] m, even at low wettability with molten aluminum, mechanically attached percentage increases, because significantly increase the dynamic coefficient of friction, which is undesirable. 平面もしくは上に凸な円弧面での接触では、加工も比較的容易なことから、R max ≦0.1μm In contact with the convex arc surface on the plane or above, since the processing is also relatively easy, R max ≦ 0.1 [mu] m
の仕上げでも費用対効果の点で優れる場合も多い。 If you of the excellent in terms of cost-effectiveness also in the finishing many.

【0020】また、埋め込み材の柱状部材形状(図2)として、単純な平面もしくは円弧面さらには長手方向に凹凸もしくは波形の形状であれば、単純研削で付与可能なことから、焼結体の仕上げ加工コストを高めることなく、溶融金属めっき浴用部材の長寿命化を実現することができる。 Further, as columnar members shape the filling material (FIG. 2), simple planar or arcuate surface further have a shape of irregularities or wave in the longitudinal direction, because it can impart a simple grinding, the sintered body without increasing the finishing costs, it is possible to realize a long life of the molten metal plating bath member.

【0021】炭化珪素(SiC)は、共有結合性の強い物質であり、常圧不活性ガス(Arなど)中の焼結が単味では困難であるため、理論密度比95%以上の緻密化に際しては種々の添加物を加えても構わない。 [0021] Silicon carbide (SiC) is a strong substance covalent atmospheric 圧不 for sintering of the active gas (Ar, etc.) in it is difficult in the plain, the theoretical density ratio of 95% or more of densification in the may be added various additives. 理論密度比95%は、 The theoretical density ratio of 95%
開気孔がほぼ消滅し、閉気孔が支配的な焼結体組織を意味しており、めっき浴の部材への浸透を防ぐとともに、 Almost disappears open pores, closed pores has means dominant sintered body tissue, while preventing penetration of the members of the plating bath,
摩耗速度を大幅に低減することが可能な密度領域である。 Is the density region that can greatly reduce the rate of wear. 焼結助剤としては、例えばカーボンブラック、各種ホウ化物、アルミナ、炭素源となりうる有機物、炭化アルミニウム、 窒化アルミニウム、等を用いることができる。 The sintering aid such as carbon black, various borides, alumina, organics which can be a carbon source, aluminum carbide, aluminum nitride, or the like can be used. 窒化珪素(Si Silicon nitride (Si 3 N 4 )も同様に、コスト的に有利な常圧窒素ガス中の焼結が単味では困難であるため、相対密度95%以上の緻密化に際しては種々の添加物を加えても構わない。 3 N 4) Similarly, since cost effective sintering of the atmospheric-pressure nitrogen gas is difficult with plain, may be added various additives upon a relative density of 95% or more of densification . 焼結助剤としては、例えばシリカ、アルミナ、イットリア、酸化四三鉄、マグネシア、 AlN-Si 3 N 4 The sintering aid, such as silica, alumina, yttria, oxides forty-three iron, magnesia, AlN-Si 3 N 4
-SiO 2 -Al 2 O 3共融物、窒化アルミニウム、各種希土類酸化物、等を用いることができる。 -SiO 2 -Al 2 O 3 eutectic, aluminum nitride, various rare earth oxides, and the like can be used.

【0022】焼結方法としては、常圧(無加圧)焼結法、 [0022] As the sintering method, atmospheric pressure (pressureless) sintering method,
ガス圧焼結法、熱間静水圧プレス焼結法、ホットプレス法の何れの方法も用いることが可能であり、更に一種もしくは複数の焼結法を組み合わせることも可能である。 Gas pressure sintering, hot isostatic press sintering method, it is possible to use any of the methods of hot pressing, it is also possible to further combine a kind or a plurality of sintering.
常圧焼結は、窒素ガスまたはArガス流通中にて行うと、 Pressureless sintering is performed in a nitrogen gas or Ar gas flow,
緻密な焼結体が得られ易い。 Easy dense sintered body is obtained. 複雑形状である溶融金属浴用部材において、高密度化を達成するためには、常圧焼結後、さらに窒素ガスまたはArガス加圧雰囲気中にて、 In a complicated shape molten metal bath member, in order to achieve densification, after pressureless sintering, at more nitrogen gas or Ar gas pressure during pressure atmosphere,
熱間静水圧プレス焼結を行うことが好ましい。 It is preferable to carry out the hot isostatic press sintering. その中で、常圧焼結時の最高温度の範囲としては、窒化珪素では1550〜1750℃、炭化珪素では1900〜2150℃であることが好ましく、最高温度での保持時間は2時間以上であることが望ましい。 Among them, as the range of maximum temperature during pressureless sintering, from 1,550 to 1750 ° C. is silicon nitride, preferably a 1900-2,150 ° C. in silicon carbide, the holding time at the maximum temperature is 2 hours or more it is desirable. 窒化珪素の場合、1550℃未満では充分高い密度が得られず、粒界相に高融点の結晶相を生成させることが困難で、高い破壊靭性値が得られない。 For silicon nitride, it is sufficiently high density is less than 1550 ° C. is not obtained, it is difficult to produce a high melting point crystal phase in the grain boundary phase, not obtain a high fracture toughness value. また、1750℃より高い温度では、焼結助剤の一部が昇華・ Also, at temperatures higher than 1750 ° C., a part of the sintering aid sublimation &
分解し、焼成炉の劣化も著しく好ましくない。 Decomposed, significantly unfavorable deterioration of the firing furnace. 常圧焼結時の保持時間としては、原料として用いる主原料の窒化珪素の結晶相転移を充分に進行させ、かつ粒界相の均一化のために上記焼結温度の範囲にて2時間以上の保持が必要である。 As the retention time at normal pressure sintering is used as a raw material is sufficiently proceed the crystal phase transition of the main raw material for silicon nitride, and 2 hours or more within a range of the sintering temperature for the homogenization of the grain boundary phase it is necessary to hold. 炭化珪素の場合、1900℃未満では充分高い密度(相対密度≧95%)が得られず、粒子分散効果が十分発現されず高い破壊靭性値が得られない。 For silicon carbide, sufficiently high density (relative density ≧ 95%) is not obtained at less than 1900 ° C., can not be obtained a high fracture toughness is not sufficiently expressed particle dispersion effect. また、2150℃ In addition, 2150 ℃
より高い温度では異常粒成長が起こる場合が有り、好ましくない。 There is a case where abnormal grain growth occurs at higher temperatures, which is not preferable.

【0023】炭化珪素系セラミックスについては、金属複合ホウ化物を炭化珪素焼結体中に体積分率で20体積% [0023] For the silicon carbide based ceramic, 20% by volume fraction of the metal complex borides in the silicon carbide sintered body
未満の分散では、高靭性化が不十分で、体積分率70体積 It is less than the variance, insufficient high toughness, the volume fraction 70 volume
%超では、常圧焼結時の相対密度95%以上の緻密化が困難で、炭化珪素本来の硬度、高温強度が得られず好ましくない。 % In greater, difficulty relative density of 95% or more of densification during pressureless sintering, silicon carbide original hardness, high temperature strength is not preferable not obtained. また、炭化珪素とTi-Zr-B固溶体粒子及び/又はTi Further, silicon carbide and Ti-Zr-B solid solution particles and / or Ti
-Hf-B固溶体粒子との熱膨張差やヤング率の相違等により、分散したTi-Zr-B固溶体粒子及び/又はTi-Hf-B固溶体粒子の近傍に残留応力が発生し、焼結体の破壊に際して破壊エネルギーを分散させる作用を有し、靭性を著しく向上させ、かつ耐摩耗性も向上させる作用もあるため、金属複合ホウ化物としてはTi-Zr-B固溶体粒子及びT The difference or the like of the thermal expansion difference and the Young's modulus of the -hf-B solid solution particles, the residual stress is generated in the vicinity of the dispersed Ti-Zr-B solid solution particles and / or Ti-Hf-B solid solution particles, sintered has an action to when the broken and dispersed fracture energy, because of the toughness is greatly improved, and also acts to wear resistance is improved, as a metal complex boride Ti-Zr-B solid solution particles and T
i-Hf-B固溶体粒子が好適である。 i-Hf-B solid solution particles are preferred.

【0024】このTi-Zr-B固溶体粒子及び/又はTi-Hf-B [0024] The Ti-Zr-B solid solution particles and / or Ti-Hf-B
固溶体粒子は、硬質かつ耐酸化性のあるhcp構造の高融点化合物であり、焼結後に炭化珪素質焼結体中に分散粒子として残留し、焼結体全体の硬度や破壊靭性値を向上させる作用を有する。 Solid solution particles are high melting point compounds of the hcp structure with hard and oxidation resistance, and remains as dispersed particles in the silicon carbide sintered body after sintering, improving the hardness and fracture toughness of the entire sintered body It is having an effect.

【0025】Ti-Zr-B固溶体粒子及び/又はTi-Hf-B固溶体粒子の組成は、それぞれTi 1-x Zr x B [0025] Ti-Zr-B composition solid solution particles and / or Ti-Hf-B solid solution particles, respectively Ti 1-x Zr x B 2 、Ti 1-x Hf x B 2で表され、xの範囲は0.02〜0.25が好ましく、より好ましくは0.02〜0.05である。 Is represented by 2, Ti 1-x Hf x B 2, the range of x is preferably 0.02 to 0.25, more preferably 0.02 to 0.05. TiB 2にZrB 2やHfB 2を固溶させると、TiB 2単体に比べ、硬度や破壊靭性値が上昇する。 When the the TiB 2 solid solution of ZrB 2 and HfB 2, compared with the TiB 2 alone, hardness and fracture toughness value increases. しかしながら、xが0.02より小さい場合には、Zr、HfのTiB However, if x is less than 0.02 is, Zr, TiB of Hf
2への固溶効果が乏しくなり、十分な高硬度化が図れない恐れがあり、一方、xが0.25を越える場合には、マトリックスの炭化珪素との熱膨張係数が掛け離れてしまうため、焼結時に緻密化し難くなり、相対密度の低い焼結体となり易く、また破壊靭性値も低下する恐れが高くなる。 Solid solution effect on 2 becomes poor, there is a risk that can not be ensured sufficiently high hardness, whereas, for the case where x exceeds 0.25, resulting in far from the thermal expansion coefficients of the silicon carbide matrix, sintered sometimes densified becomes difficult, tends to be low relative density sintered body, also may decrease even fracture toughness value increases. また、前記固溶体粒子の平均粒径は1〜10μmであることが望ましい。 The average particle size of the solid solution particles is preferably a 1 to 10 [mu] m. より好ましくは3〜5μmである。 More preferably 3~5μm. 平均粒径が1μmより小さいと、靭性への寄与が得られ難く、 And average particle size of 1μm less, hardly contribute to the toughness is obtained,
一方、10μmより大きいと、硬さや破壊靭性値の低下を招き易くなる。 On the other hand, easily leads and 10μm greater, a decrease in hardness and fracture toughness.

【0026】一方、窒化珪素系セラミックスについて、 [0026] On the other hand, the silicon nitride ceramic,
窒化珪素質焼結体中にクロム化合物を体積分率で1体積% At a volume fraction of the chromium compound in the silicon nitride sintered body 1 by volume%
未満の分散では、十分な高靭性化、高温高強度化が得られず、8体積%超の分散では耐クリープ性や耐食性が低下する。 Is less than the variance, sufficiently high toughness can not be obtained is high temperature and high strength, the creep resistance and corrosion resistance at 8 vol% of the dispersion decreases. クロム化合物の中でも、高硬度の窒化クロム(Cr 2 Among the chromium compounds, high hardness of chromium nitride (Cr 2
N)粒子を分散させることが有効である。 It is effective to disperse the N) particles. 特に、硬質かつ酸素含有雰囲気下1200〜1400℃での耐酸化性に優れた窒化クロム(Cr 2 N)粒子は、窒化珪素質焼結体に物理・化学的安定性、熱的安定性、機械的安定性に優れ、長期耐久性を付与することができる。 In particular, hard and oxygen-containing atmosphere oxidation resistance superior chromium nitride under 1200~1400 ℃ (Cr 2 N) particles, physical and chemical stability to the silicon nitride sintered body, thermal stability, mechanical excellent stability, can impart long-term durability. 特に、窒化クロム(Cr 2 N)粒子は、窒化珪素相、粒界相との熱膨張差やヤング率の相違等により、焼結終了後に分散粒子近傍に残留応力が発生し、焼結体の破壊に際して破壊エネルギーを分散させる作用を有し、破壊靭性値を高め、耐欠損性を著しく向上させつつ、耐熱衝撃性も向上させる作用もある。 In particular, chromium (Cr 2 N) particles nitride, silicon nitride phase, the difference or the like of the thermal expansion difference and the Young's modulus of the grain boundary phase, the residual stress in the vicinity of the dispersed particles after completion of sintering occurs, the sintered body have the effect of dispersing the fracture energy during breaking, increase fracture toughness, while significantly improving the fracture resistance, also it has an effect of improving also the thermal shock resistance. この窒化クロム(Cr 2 N)粒子は、硬質かつ耐酸化性のあるhcp Hcp chromium nitride (Cr 2 N) particles, with a hard and oxidation resistance
構造の高融点化合物であり、焼結後に窒化珪素質焼結体中に分散粒子として残留し、焼結体全体の硬度を向上させる作用を有する。 A high-melting compound of structure has the effect remains as dispersed particles in the silicon nitride sintered in body after sintering, improving the hardness of the entire sintered body. 窒化クロム(Cr 2 N)粒子の平均粒径は The average particle size of chromium nitride (Cr 2 N) particles
0.5〜10μmであることが望ましい。 It is desirable that the 0.5~10μm. より好ましくは5〜8 More preferably 5 to 8
μmである。 It is μm. 平均粒径が0.5μmより小さいと、靭性への寄与が得られ難く、一方、10μmより大きいと、硬さや耐熱衝撃性の低下を招き易くなる。 And the average particle size is 0.5μm less, difficult to obtain the contribution to toughness, whereas, easily cause a 10μm greater, a decrease in hardness and thermal shock resistance.

【0027】 [0027]

【実施例】次に、本発明の実施例を比較例と共に説明する。 EXAMPLES Next, an example of the present invention together with comparative examples.

【0028】(実施例1〜5)窒化珪素(Si 3 N 4 )粉末(α型、 [0028] (Examples 1-5) silicon nitride (Si 3 N 4) powder (alpha type,
純度99.7%、平均粒径0.3μm)に窒化クロム(Cr 2 N)粉末 Purity 99.7%, average particle size 0.3 [mu] m) chromium nitride (Cr 2 N) powder
(平均粒径6.5μm)、イットリア(Y 2 O 3 )粉末(平均粒径1μ (Average particle size 6.5 [mu] m), yttria (Y 2 O 3) powder (average particle diameter 1μ
m)、マグネシア(MgO)粉末(平均粒径0.8μm)、アルミナ m), magnesia (MgO) powder (average particle diameter 0.8 [mu] m), alumina
(Al 2 O 3 )粉末(平均粒径0.3μm)、酸化四三鉄(Fe 3 O 4 )粉末 (Al 2 O 3) powder (average particle size 0.3 [mu] m), oxide forty-three iron (Fe 3 O 4) powder
(平均粒径3.5μm)、及びAlN-Si 3 N 4 -SiO 2 -Al 2 O 3共融物の一例としてポリタイプ21R組成粉末(平均粒径2.2μ (Average particle size 3.5 [mu] m), and AlN-Si 3 N 4 -SiO 2 -Al 2 O 3 polytypes 21R composition powder as an example of a eutectic (average particle size 2.2μ
m)、同様に炭化珪素(SiC)粉末(α型、純度98.5%、平均粒径0.4μm)にホウ化チタン(TiB 2 )粉末(平均粒径3.5μ m), likewise silicon carbide (SiC) powder (alpha type, purity 98.5%, average particle size 0.4 .mu.m) to titanium boride (TiB 2) powder (average particle size 3.5μ
m)、ホウ化ジルコニウム(ZrB 2 )粉末(平均粒径5.5μm)、 m), zirconium boride (ZrB 2) powder (average particle size 5.5 [mu] m),
炭化ホウ素(B 4 C)粉末(平均粒径1.5μm)、カーボンブラック粉末(平均粒径0.02μm)を表1に示す所定量(質量%) Boron carbide (B 4 C) powder (average particle size 1.5 [mu] m), a predetermined amount shown in Table 1 the carbon black powder (average particle diameter 0.02 [mu] m) (mass%)
添加し、混練時の分散媒として精製水を用い、ボールミルで24時間混練した。 It was added, and purified water used as a dispersion medium at the time of kneading, and 24 hours kneaded in a ball mill. セラミックス全粉末原料100gに対し、精製水の添加量も100gとした。 Ceramic relative to the total powder material 100 g, the addition amount of purified water was also a 100 g.

【0029】次いで、得られた混合粉末を成形後焼結した。 [0029] Then, the sintering after molding the mixed powder obtained. 成形条件としては冷間静水圧による加圧150MPaとし、100mm角、高さ22mmの板状成形体を得た。 The molding conditions were a pressure 150MPa by cold isostatic, 100 mm square, to obtain a plate-shaped molded product of the height 22 mm. 焼結条件としては、窒素ガスまたはArガス流通中にて、表1中に示す各温度で4〜8時間保持の無加圧焼結、並びに必要に応じ熱間静水圧プレス焼結を追加した。 The sintering conditions, a nitrogen gas or Ar gas flow, added pressureless sintering of 4-8 hour hold at each temperature shown in Table 1, and the hot isostatic press sintering necessary .

【0030】得られた焼結体から、15mm×20mm×長さ80 The sintered body obtained, 15 mm × 20 mm × length 80
mmの固定側軸受けテスト材を研削加工し、溶融アルミニウム浴中軸受け試験(図4)に供した。 The mm stationary bearing test material by grinding and subjected to bearing test molten aluminum bath (Fig. 4).

【0031】板状焼結体から該15mm×20mm×長さ80mmテスト材を切り出す際の残材から、機械的性質評価用の試験片を切り出し、その特性を評価した。 [0031] From the remaining material when cutting the 15 mm × 20 mm × length 80mm test material from the plate-like sintered body, cut out test pieces for mechanical properties evaluation, and its characteristics were evaluated. 硬さは、押込荷重10kgにて、ビッカース硬さとして測定した。 Hardness, at indentation load 10kg, was measured as a Vickers hardness. 靭性については、JIS R1607のSEPB法により、室温にて破壊靭性値K ICを測定した。 For toughness, the SEPB method JIS R1607, to measure the fracture toughness value K IC at room temperature. また、耐熱衝撃性としては、曲げ試験片を大気中にて所定の温度に加熱後、水中急冷し、抗折強さの劣化が始まる急冷温度差ΔTで評価した。 As the thermal shock resistance after heating the bending test piece to a predetermined temperature in the atmosphere, and water quenched, and evaluated in a quench temperature difference ΔT deterioration of flexural strength begins. 焼結体密度は、アルキメデス法により相対密度として測定した。 Sintered density was measured as a relative density by the Archimedes method. 濡れ性は、通常の溶融液滴と水平板状態の接触角で測定した。 Wettability was measured with a contact angle of a normal molten droplets and the horizontal plate state.

【0032】得られた各焼結体のアルキメデス密度、機械的性質、並びに図4に示したアルミニウム浴中軸受け評価結果を、各配合系ごとに表2に示す。 The Archimedes density of each sintered body obtained, the mechanical properties, as well as in the aluminum bath bearing evaluation results shown in FIG. 4, shown in Table 2 for each formulation system. アルミニウム浴中試験は、以下の条件にて行った。 In the aluminum bath test was carried out under the following conditions. (1)回転側軸受けテスト材:超硬リング材φ90mm×高さ60mm (2)固定側軸受けテスト材:セラミックス試験材15mm (1) rotating side bearing test material: carbide ring material 90 mm × height 60 mm (2) stationary bearing test material: ceramic test piece 15mm
×20mm×長さ80mmを3本 (3)溶融アルミニウム温度:680℃ (4)押し当て力:30〜50N (5)すべり速度:2〜3m/秒 (6)摺り合わせ時間:浸漬後、1時間 (7)テスト前の仕上げ面粗さ:R max =0.2μm(△△△△程度、JIS B0031参照) (8)繰り返し熱疲労試験:1時間浴中に漬けた後、浴から引き上げ30分間空冷を繰り返す (9)濡れ性評価試験:アルミニウム塊を50mm角×10mm × 20 mm × 3 present a length 80 mm (3) molten aluminum temperature: 680 ° C. (4) pressing force: 30~50N (5) sliding speed: 2 to 3 m / sec (6) lapping Time: After immersion, 1 time (7) pre-test surface roughness: R max = 0.2 [mu] m (△△△△ about, JIS B0031 reference) (8) repeated thermal fatigue test: after dipping in 1 hour bath, lifted from the bath 30 minutes repeated cooling (9) wettability evaluation test: 50mm square × 10 mm aluminum ingot
厚さの板状 セラミックス上で680℃溶解後、炉外から覗き窓を通して観察測定 上記(1)〜(7)の条件にて摩耗量を求める方法として、回転側、固定側にそれぞれ発生した摩耗痕跡の深さh r 、h s After 680 ° C. dissolved in thickness on the plate-shaped ceramic, as a method for determining the amount of wear under conditions of observation measurement described above through the viewing window from the outside of the furnace (1) to (7), rotating-side, respectively generated on the fixed side wear depth h r of the trace, h s
を表面粗さ計にて測定した。 It was measured by a surface roughness meter. また、摩耗痕跡周囲の損傷有無、チッピング深さ、及び割れ深さを蛍光探傷法や断面研磨面の光学顕微鏡観察により評価した。 Also, damage to the presence or absence of wear track surrounding, chipping depth, and crack depth was evaluated by optical microscopy of fluorescent flaw detection method and the cross-section polished surface. 再利用に当たっての軸受け摺り合わせ面の必要研削量は、摩耗痕跡周囲に割れ・チッピングの損傷が観察されない場合、摩耗痕跡深さhの1.2倍、チッピングが生じている場合、チッピング深さの1.2倍、そして割れが生じている場合、 Required amount of grinding of the bearing lapping surface of the carrying reuse, if damage to the crack-chipping wear track around is not observed, 1.2 times the wear track depth h, or chipping occurs, 1.2 times the chipping depth , and if cracking occurs,
割れ深さの1.2倍として表2中に示した。 As 1.2 times the crack depth shown in Table 2.

【0033】(比較例6〜9)比較例6〜8は、一般市販のサイアロンを用い、リングの一部を軸受けに嵌め込んだ場合(比較例6)、市販の窒化珪素セラミックスだが異なる組成のサイアロン系のものを用い全周リングで作製した場合(比較例7)、市販のサイアロンを用いリングの一部を軸受けに嵌め込んだ場合(比較例8)、公知の炭化珪素を用いリングの一部を軸受けに嵌め込んだ場合(比較例 [0033] (Comparative Example 6-9) Comparative Example 6-8, using a standard, sialon, when fitting the part of the ring bearing (Comparative Example 6), of but a commercially available silicon nitride ceramic composition different If it produced in the entire circumference ring used as a sialon (Comparative example 7), when fitting the portion of the ring using a commercial sialon bearing (Comparative example 8), one ring using known silicon carbide If you fit the part to the bearing (comparative example
9)の各比較例である。 9) is the comparative example. これら比較例の材料も、実施例1 Also materials Comparative Examples, Example 1
〜5と同様の条件で、溶融アルミニウム浴中試験を行い、その結果を表2に示した。 Under the same conditions as 5 performs in the molten aluminum bath test, and the results are shown in Table 2.

【0034】 [0034]

【表1】 [Table 1]

【0035】 [0035]

【表2】 [Table 2]

【0036】表2に示すように、本発明の実施例によるものは、摩耗痕跡深さが固定側・回転側の何れも25μm As shown in Table 2, by embodiments of the present invention, the wear track depth 25μm any of the fixed-side and rotational-side
以下と非常に少なく、かつ摩耗痕跡周囲には割れ・チッピングの欠損が何れの場合も認められず、耐摩耗性、耐欠損性共に優れるが、比較例の各軸受けは本発明の実施例に比べて、摩耗痕跡深さ60μm以上と大きく、かつ割れ・チッピングのいずれかが発生しており、耐摩耗性、 Following a very low, and the abrasion trace around not be observed in any case defective cracks, chipping, abrasion resistance is excellent chipping resistance together, each bearing in the comparative example than in the embodiment of the present invention Te, as large as the wear track depth 60μm or more, and is one of the cracks, chipping occurs, abrasion resistance,
耐欠損性ともに未達成であることが確認された。 It was confirmed that it was not yet achieved chipping resistance both. 必要研削量も実施例の30μm以下に比べ、比較例では72μm以上と著しく大きいことが判明した。 Requires grinding amount than below 30μm examples were found to be significantly greater and more 72μm in the comparative example.

【0037】アルミニウム浴中軸受け評価試験の条件 The aluminum bath conditions of bearing evaluation test
(8)、(9)に基づいた結果を、表3に示す。 (8), the results based on (9), shown in Table 3.

【0038】 [0038]

【表3】 [Table 3]

【0039】軸受けに繰り返し熱疲労を負荷した場合も、本発明によるものは20〜30回使用可能であるのに対し、比較例の各材料では5〜10回と半分以下である。 [0039] When loaded with thermal fatigue repeatedly bearings also by the present invention whereas the available 20-30 times, in each material of the comparative example is less than 5-10 times and half. 再研削時の加工費、繰り返し利用を含めた製品の総寿命を考慮すると本発明の焼結体による軸受け材は極めて有利であることが確認された。 Processing cost at the time of re-grinding, the bearing material by a sintered body of consideration of the present invention the total life of the product, including the repeated use was confirmed to be very advantageous. また、濡れ性評価でも本発明によるものは105〜135°と濡れ難く、比較例の各材料では40〜50°と接触角が小さく濡れ易いことが判明した。 Further, by the present invention in the wettability evaluation hardly wetted with 105 to 135 °, in each material of the comparative example it was found to be easily wetted small contact angle with 40 to 50 °.
耐食性を向上させ、引き上げ時空冷による熱収縮が起こる際に、固定側への引張応力を低減する効果が充分に期待される。 Improve corrosion resistance, when the thermal contraction occurs by pulling upon cooling, the effect of reducing the tensile stress on the fixed side is sufficiently expected. このため、溶融アルミニウムと濡れ難いこと・繰り返し熱疲労の耐久性が高いことはいずれも本溶融アルミニウム浴中での用途に優位に働くことが容易に推定され、摩耗量が少なく、割れ・チッピングが発生しなかったものと考えられる。 Therefore, both the high durability of the wettability hardly possible, repeated thermal fatigue and molten aluminum are applications estimated easily to work advantage in the present molten aluminum bath, small wear amount, cracks, chipping it is considered that did not occur. 高温のアルミニウム浴中での評価結果から、より低温の亜鉛浴中の耐熱衝撃性も満たすことが容易に想定されるため、本発明は、溶融金属めっき浴用部材への適用が可能と判断できる。 From the evaluation results of high temperature aluminum bath, since to meet more even thermal shock resistance of the low-temperature zinc bath are readily envisioned, the present invention, it can be determined that can be applied to a molten metal plating bath member.

【0040】 [0040]

【発明の効果】本発明により、連続溶融金属めっき装置における軸受部材の寿命が大幅に延長できる。 According to the present invention, the life of the bearing member in a continuous molten metal plating apparatus can be significantly prolonged. このことにより、長時間安定して金属めっき鋼板の生産が可能となり、その工業的有用性は非常に大きい。 Thus, long-term stability to be possible to produce metal-plated steel sheet, its industrial utility is very large.

【図面の簡単な説明】 BRIEF DESCRIPTION OF THE DRAWINGS

【図1】 溶融めっき浴の装置断面模式図 [1] device cross-sectional schematic view of a hot dip plating bath

【図2】 埋め込み部材の長手方向断面図と回転軸方向断面図 [Figure 2] embedded longitudinal section and the rotation axis direction sectional view of the member

【図3】 軸受け部の組み付け構造図 [3] Construction of assembling the bearing unit

【図4】 本発明の実施例による軸受け損耗評価時の装置断面図 Device sectional view when a bearing wear evaluation according to an embodiment of the present invention; FIG

【符号の説明】 DESCRIPTION OF SYMBOLS

1…めっき処理ラインで通板中の鋼板 2…ポットロール 3…ガイドロール 4…加熱機能付き浴槽 5…回転側軸受けテスト材(φ90mm×高さ50mm) 6…固定側軸受けテスト材(15×20×長さ80mm) 7…溶融アルミニウム浴(680℃) 8…保護管付き熱電対 1 ... steel plate 2 ... pot roll strip passing in a plating process line 3 ... guide roll 4 ... heating function bathtub 5 ... rotating side bearing test material (90 mm × height 50 mm) 6 ... stationary bearing test material (15 × 20 × length 80 mm) 7 ... molten aluminum bath (680 ℃) 8 ... thermocouple with protection tube

───────────────────────────────────────────────────── フロントページの続き (72)発明者 芝本 茂 福岡県北九州市戸畑区飛幡町1−1 新日 本製鐵株式会社八幡製鐵所内 Fターム(参考) 4K027 AA02 AA22 AB48 AD17 ────────────────────────────────────────────────── ─── front page of the continuation (72) inventor Shibahon Shigeru Kitakyushu, Fukuoka Prefecture Tobata-ku, Tobihata-cho, 1-1 Nippon steel Corporation Yawata Works in the F-term (reference) 4K027 AA02 AA22 AB48 AD17

Claims (12)

    【特許請求の範囲】 [The claims]
  1. 【請求項1】 溶融金属めっき浴に浸漬されるポットロール装置に付設された浸漬部材であって、該浸漬部材が、該ポットロール設備の少なくともポットロール軸部スリーブ部材と軸受部材の摺動する部分の一部又は全部に嵌合してなる、窒化珪素系又は炭化珪素系のセラミックス部材であることを特徴とする溶融金属めっき浴用浸漬部材。 1. A soaking member which is attached to the pot roll apparatus which is immersed in the molten metal plating bath, the immersion member is slid at least the pot roll shaft sleeve member and the bearing member of the pot roll equipment becomes fitted in some or all of the parts, the molten metal plating bath immersion member which is a ceramic member silicon nitride or silicon carbide.
  2. 【請求項2】 前記浸漬部材が、複数の柱状部材からなる請求項1記載の溶融金属めっき浴用浸漬部材。 Wherein said immersion member, the molten metal plating bath immersion member according to claim 1, wherein comprising a plurality of columnar members.
  3. 【請求項3】 前記柱状部材が、前記軸受部の軸方向に嵌合してなる請求項2記載の溶融金属めっき浴用浸漬部材。 Wherein the columnar member is, molten metal plating bath immersion member according to claim 2, wherein comprising fitted in the axial direction of the bearing portion.
  4. 【請求項4】 前記柱状部材の回転方向の摺動面が、平面又は前記ポットロール軸部スリーブ部材の曲率半径以上の円弧状面である請求項3記載の溶融金属めっき浴用浸漬部材。 Wherein said sliding surface of the rotating direction of the columnar members, flat or the pot molten metal plating bath immersion member according to claim 3, wherein the arcuate surface of the above curvature radius of the roll shaft section sleeve member.
  5. 【請求項5】 前記柱状部材が、前記ポットロール軸部スリーブ部材に軸方向に嵌合してなる請求項2記載の溶融金属めっき浴用浸漬部材。 Wherein said columnar member, the molten metal plating bath immersion member according to claim 2, wherein comprising fitted axially to the pot roll shaft sleeve member.
  6. 【請求項6】 前記柱状部材の摺動面が、前記軸受部材の曲率半径以下の円弧状面である請求項5記載の溶融金属めっき浴用浸漬部材。 Wherein said sliding surface of the columnar member, the molten metal plating bath immersion member according to claim 5 wherein said is an arc-shaped surface of a curvature radius below the bearing member.
  7. 【請求項7】 前記柱状部材の軸方向の摺動面が、凹凸状及び/又は波形状で、凸部の摺動面高さが軸方向で揃った形状である請求項3又は5に記載の溶融金属めっき浴用浸漬部材。 Sliding surface of the axial wherein said columnar member in uneven and / or wave-like, according to claim 3 or 5 sliding surface height of the convex portion has a shape of uniform in the axial direction molten metal plating bath immersion member.
  8. 【請求項8】 前記セラミックス部材が、理論密度の95 Wherein said ceramic member is a theoretical density of 95
    %以上の焼結体密度である請求項1〜7に記載の溶融金属めっき浴用浸漬部材。 Molten metal plating bath immersion member according to claims 1 to 7% or more of a sintered body density.
  9. 【請求項9】 前記セラミックス部材が、クロム化合物を体積分率で1〜8%含有する窒化珪素質焼結体である請求項8記載の溶融金属めっき浴用浸漬部材。 Wherein said ceramic member is, molten metal plating bath immersion member according to claim 8, wherein the chromium compound is 1 to 8% content for silicon nitride sintered body at a volume fraction.
  10. 【請求項10】 前記クロム化合物が、窒化クロムである請求項9記載の溶融金属めっき浴用浸漬部材。 Wherein said chromium compound is, molten metal plating bath immersion member according to claim 9, wherein the chromium nitride.
  11. 【請求項11】 前記セラミックス部材が、複合金属ホウ化物を体積分率で20〜70%含有する炭化珪素質焼結体である請求項8記載の溶融金属めっき浴用浸漬部材。 Wherein said ceramic member is, molten metal plating bath immersion member according to claim 8, wherein a silicon carbide sintered body containing 20% ​​to 70% of the composite metal boride volume fraction.
  12. 【請求項12】 前記複合金属ホウ化物が、Ti-Zr-B固溶体及び/又はTi-Hf-B固溶体である請求項11記載の溶融金属めっき浴用浸漬部材。 12. The composite metal boride, Ti-Zr-B solid solution and / or Ti-Hf-B solid solution in molten metal plating baths immersion member according to claim 11, wherein.
JP2000377798A 2000-12-12 2000-12-12 Immersion member for molten metal plating bath Expired - Fee Related JP4460144B2 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
JP2000377798A JP4460144B2 (en) 2000-12-12 2000-12-12 Immersion member for molten metal plating bath

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP2000377798A JP4460144B2 (en) 2000-12-12 2000-12-12 Immersion member for molten metal plating bath

Publications (2)

Publication Number Publication Date
JP2002180222A true JP2002180222A (en) 2002-06-26
JP4460144B2 JP4460144B2 (en) 2010-05-12

Family

ID=18846469

Family Applications (1)

Application Number Title Priority Date Filing Date
JP2000377798A Expired - Fee Related JP4460144B2 (en) 2000-12-12 2000-12-12 Immersion member for molten metal plating bath

Country Status (1)

Country Link
JP (1) JP4460144B2 (en)

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002206155A (en) * 2001-01-09 2002-07-26 Nippon Steel Corp Immersion member for hot-dip metal coating bath, and its manufacturing method
JP2002241915A (en) * 2001-02-20 2002-08-28 Hitachi Metals Ltd Bearing unit in molten metal bath
JP2002294419A (en) * 2001-04-02 2002-10-09 Hitachi Metals Ltd Roller bearing used in continuous hot-dip metal plating bath
JP2007009311A (en) * 2005-07-04 2007-01-18 Sumitomo Metal Ind Ltd Plain bearing device for hot dip metal plating bath
JP2007145642A (en) * 2005-11-28 2007-06-14 Nippon Steel Corp Immersion member for hot-dip metal plating bath, and manufacturing method of the same

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002206155A (en) * 2001-01-09 2002-07-26 Nippon Steel Corp Immersion member for hot-dip metal coating bath, and its manufacturing method
JP4499928B2 (en) * 2001-01-09 2010-07-14 新日本製鐵株式会社 Immersion member for molten metal plating bath and manufacturing method
JP2002241915A (en) * 2001-02-20 2002-08-28 Hitachi Metals Ltd Bearing unit in molten metal bath
JP4725759B2 (en) * 2001-02-20 2011-07-13 日立金属株式会社 Bearing device in molten metal bath
JP2002294419A (en) * 2001-04-02 2002-10-09 Hitachi Metals Ltd Roller bearing used in continuous hot-dip metal plating bath
JP4678565B2 (en) * 2001-04-02 2011-04-27 日立金属株式会社 Roller bearing in continuous molten metal plating bath
JP2007009311A (en) * 2005-07-04 2007-01-18 Sumitomo Metal Ind Ltd Plain bearing device for hot dip metal plating bath
JP2007145642A (en) * 2005-11-28 2007-06-14 Nippon Steel Corp Immersion member for hot-dip metal plating bath, and manufacturing method of the same

Also Published As

Publication number Publication date
JP4460144B2 (en) 2010-05-12

Similar Documents

Publication Publication Date Title
Li et al. Sintering and mechanical properties of titanium diboride with aluminum nitride as a sintering aid
JP4744704B2 (en) Method for manufacturing wear-resistant member
JP5078615B2 (en) Al2O3 ceramic tool with diffusion bonding enhancement layer
Levine et al. Evaluation of ultra-high temperature ceramics foraeropropulsion use
Opeka et al. Mechanical, thermal, and oxidation properties of refractory hafnium and zirconium compounds
Claussen Strengthening strategies for ZrO2-toughened ceramics at high temperatures
EP1223150B1 (en) Silicon nitride wear resistant member and method of manufacturing the member
JP4647053B2 (en) SiC-C / C composite composite material, use thereof, and production method thereof
Waku et al. Dislocation mechanism of deformation and strength of Al2O3–YAG single crystal composites at high temperatures above 1500° C
US4804645A (en) Ceramic material based on alumina and refractory hard constituents
Butler Transformation-toughened zirconia ceramics
Zhang et al. Mechanical properties and thermal shock resistance of ZrB2–SiC ceramic toughened with graphite flake and SiC whiskers
KR101313470B1 (en) Heat Resistant Coated Member, Making Method, and Treatment Using the Same
Magnani et al. Flexural strength and toughness of liquid phase sintered silicon carbide
Krstic et al. Silicon nitride: the engineering material of the future
Neuman et al. Mechanical behavior of zirconium diboride–silicon carbide ceramics at elevated temperature in air
CN1044110C (en) Boron carbide-aluminium structural composite material and its prep.
Rak et al. Manufacture and properties of Al2O3–TiN particulate composites
US4412008A (en) Composite sinter of silicon nitride/boron nitride and method for manufacturing thereof
Neuman et al. Mechanical behavior of zirconium diboride–silicon carbide–boron carbide ceramics up to 2200 C
Ruigang et al. Investigation of the physical and mechanical properties of hot-pressed machinable Si3N4/h-BN composites and FGM
Sarkar et al. Oxidation protection of gamma-titanium aluminide using glass–ceramic coatings
JP2546872B2 (en) Method for producing a composite body
CN100473627C (en) Wear-resistance silicon nitride member and method for manufacturing thereof
US4869943A (en) Fiber-reinforced silicon nitride ceramics

Legal Events

Date Code Title Description
A621 Written request for application examination

Free format text: JAPANESE INTERMEDIATE CODE: A621

Effective date: 20061113

A977 Report on retrieval

Free format text: JAPANESE INTERMEDIATE CODE: A971007

Effective date: 20090416

A131 Notification of reasons for refusal

Free format text: JAPANESE INTERMEDIATE CODE: A131

Effective date: 20090421

A521 Written amendment

Free format text: JAPANESE INTERMEDIATE CODE: A523

Effective date: 20090622

A131 Notification of reasons for refusal

Free format text: JAPANESE INTERMEDIATE CODE: A131

Effective date: 20091117

A521 Written amendment

Free format text: JAPANESE INTERMEDIATE CODE: A523

Effective date: 20100118

TRDD Decision of grant or rejection written
A01 Written decision to grant a patent or to grant a registration (utility model)

Free format text: JAPANESE INTERMEDIATE CODE: A01

Effective date: 20100209

A01 Written decision to grant a patent or to grant a registration (utility model)

Free format text: JAPANESE INTERMEDIATE CODE: A01

A61 First payment of annual fees (during grant procedure)

Free format text: JAPANESE INTERMEDIATE CODE: A61

Effective date: 20100212

R151 Written notification of patent or utility model registration

Ref document number: 4460144

Country of ref document: JP

Free format text: JAPANESE INTERMEDIATE CODE: R151

FPAY Renewal fee payment (event date is renewal date of database)

Free format text: PAYMENT UNTIL: 20130219

Year of fee payment: 3

S533 Written request for registration of change of name

Free format text: JAPANESE INTERMEDIATE CODE: R313533

R350 Written notification of registration of transfer

Free format text: JAPANESE INTERMEDIATE CODE: R350

FPAY Renewal fee payment (event date is renewal date of database)

Free format text: PAYMENT UNTIL: 20130219

Year of fee payment: 3

FPAY Renewal fee payment (event date is renewal date of database)

Free format text: PAYMENT UNTIL: 20140219

Year of fee payment: 4

LAPS Cancellation because of no payment of annual fees