JP5328886B2 - Mold member manufacturing method and mold member manufactured by the manufacturing method - Google Patents
Mold member manufacturing method and mold member manufactured by the manufacturing method Download PDFInfo
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- JP5328886B2 JP5328886B2 JP2011500041A JP2011500041A JP5328886B2 JP 5328886 B2 JP5328886 B2 JP 5328886B2 JP 2011500041 A JP2011500041 A JP 2011500041A JP 2011500041 A JP2011500041 A JP 2011500041A JP 5328886 B2 JP5328886 B2 JP 5328886B2
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/04—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds
- B22D11/059—Mould materials or platings
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22C—FOUNDRY MOULDING
- B22C9/00—Moulds or cores; Moulding processes
- B22C9/06—Permanent moulds for shaped castings
- B22C9/061—Materials which make up the mould
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0637—Accessories therefor
- B22D11/0648—Casting surfaces
- B22D11/066—Side dams
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C9/00—Alloys based on copper
- C22C9/06—Alloys based on copper with nickel or cobalt as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/08—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of copper or alloys based thereon
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- Continuous Casting (AREA)
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Description
本発明は、請求項１の特徴による、ケイ素、ニッケル、クロム及びジルコニウム、並びに金属間化合物の初晶相（ｉｎｔｅｒｍｅｔａｌｌｉｓｃｈｅ Ｐｒｉｍａｅｒｐｈａｓｅｎ）を含む銅合金からなる鋳型部材の製造方法に関する。 The present invention relates to a method for producing a mold member made of a copper alloy containing silicon, nickel, chromium and zirconium, and an intermetallic compound primary phase according to the features of claim 1.
本発明は、さらに、その製造方法によって製造された鋳型部材にも関する。 The present invention further relates to a mold member manufactured by the manufacturing method.
欧州特許第０３４６６４５Ｂ１号（特許文献１）は、１．６〜２．４％ニッケル、０．５〜０．８％ケイ素、０．０１〜０．２０％ジルコニウム、残余の銅並びに製造条件に付随する不純物及び慣用的な加工用添加材よりなる、析出硬化可能な銅合金を、鋳造に際して永続的に変化する温度負荷に曝される鋳型部材、とりわけ、二重ベルト鋳造装置のサイドダム（Ｓｅｉｔｅｎｄａｅｍｍｅ）用ブロック材の形態の鋳型部材を製造するための材料として使用することを記載している。二重ベルト鋳造装置の能力は、ブロック材から形成されたサイドダム列の欠点のない機能によって決定的に左右される。すなわち、それらのブロック材は、可能な限り高い熱伝導度を有し、それにより、融解熱又は凝固熱をできる限り迅速に取り除き得ることが必要である。ブロック間に空隙を形成し、それからその空隙中への溶融物の侵入を招くような機械的応力によるブロック材の側縁部の早すぎる摩耗を防ぐために、材料は、高い硬度及び引張り強さの他に、低い粒度を有するものでなければならない。最後に、鋳造区間を出た後のブロック材の再冷却時に現れる熱的応力により、鋼製ベルトを収容するために組み込まれたＴ型溝の角部において、ブロック材に亀裂が生じないことを保証するような、最適な疲労挙動が極めて決定的な重要性を有する。すなわち、熱衝撃により引き起こされるこのような亀裂が出現する場合には、当該ブロック材は、短時間後にすでに列から脱落し、その際、溶融金属は、鋳型の空洞から不制御に流出し、そして装置部材に損傷を与え得る。損傷を受けたブロック材を交換するためには、装置を停止して鋳造プロセスを中断しなければならない。 European Patent No. 0346645B1 is related to 1.6 to 2.4% nickel, 0.5 to 0.8% silicon, 0.01 to 0.20% zirconium, the remaining copper and production conditions. Of cast-hardenable copper alloys, consisting of impurities and conventional processing additives, subjected to permanent temperature changes during casting, especially for side belt dams in double belt casting equipment It describes use as a material for producing a mold member in the form of a block material. The capacity of the double belt casting apparatus is critically dependent on the function without defects of the side dam train formed from the block material. That is, they need to have as high a thermal conductivity as possible so that the heat of fusion or heat of solidification can be removed as quickly as possible. In order to prevent premature wear of the side edges of the block material due to mechanical stresses that form voids between the blocks and then lead to the intrusion of the melt into the voids, the material has a high hardness and tensile strength. In addition, it must have a low particle size. Finally, due to the thermal stress that appears during re-cooling of the block material after leaving the casting section, the block material will not crack at the corners of the T-shaped groove incorporated to accommodate the steel belt. Optimal fatigue behavior, assured, is of crucial importance. That is, if such a crack caused by thermal shock appears, the block material will already fall out of the row after a short time, with the molten metal flowing out of control from the mold cavity and Device members can be damaged. In order to replace the damaged block material, the apparatus must be stopped and the casting process interrupted.
亀裂発生傾向を検査するための試験方法が実証されており、それによれば、ブロック材を５００℃で二時間の熱処理に供し、そして引き続き、２５℃の水中で急激に冷却する。この熱衝撃試験を何度も繰り返す時にも、適当な材料の場合には、Ｔ型溝の範囲内に亀裂が全く出現してはならない。 A test method has been demonstrated for examining the tendency to crack, according to which the block material is subjected to a heat treatment at 500 ° C. for 2 hours and subsequently rapidly cooled in water at 25 ° C. Even when this thermal shock test is repeated many times, in the case of an appropriate material, no crack should appear within the range of the T-shaped groove.
欧州特許第０３４６６４５Ｂ１号（特許文献１）に記載のジルコニウムを含む析出硬化可能なＣｕＮｉＳｉＣｒ−合金は、二重ベルト鋳造装置のサイドダム用ブロック材として際立って適している。クロムの添加によって原材料の伝導度が高められる。Ｆｅ添加によって、原材料の他の特性に悪影響を与えることなく、溶体化処理時の粒子成長が制限される。 The precipitation-hardenable CuNiSiCr alloy containing zirconium described in European Patent No. 0346645B1 (Patent Document 1) is remarkably suitable as a side dam block material for a double belt casting apparatus. Addition of chromium increases the conductivity of the raw material. Addition of Fe limits particle growth during solution treatment without adversely affecting other properties of the raw material.
クロム及びジルコニウム含有材料の組織において、その溶融物の凝固時に亜共晶に、すなわち、不均一な分布で晶出する、金属間化合物の初晶相が生じることが知られている。そのＣｒＳｉ含有及びＮｉＺｒ含有の相は、二重ベルト鋳造装置のサイドダム用ブロック材の製造用出発材料として使用される鋳造された丸ビレット中に方法条件に起因して既に生じる。鋳造された材料は、通常は、微粒組織の調整のために並びに必要な硬度および電気伝導度を達成するために、慣用の成形方法、例えば押出法、鍛造法、又は圧延法で成形され、引き続き、溶体化処理し、そして析出硬化させ、その際に、鋳物状態の金属間化合物の初晶相の共晶性の不均一な分布は、大なり小なり十分に破壊され、そしてその際、初晶相は、主成形方向に筋状に配列する。押出又は熱間圧延されたロッドからのブロック材の慣用の製造においては、比較的不均一に分布した、はっきりと筋状に整列した初晶相配列がブロック材の鋳造表面に存在する。インゴットからプレートを鍛造する時、総変形度が制限されておりかつ長手方向及び横方向においてプレートがほぼ同等に成形されるため、通常、鋳物状態の金属間化合物の初晶相の網形状の分布は、不十分にしか取り除かれない。 In the structure of chromium- and zirconium-containing materials, it is known that a primary phase of an intermetallic compound that crystallizes in a hypoeutectic, that is, in a non-uniform distribution, upon solidification of the melt. The CrSi-containing and NiZr-containing phases already occur due to the process conditions in the cast round billets used as starting materials for the production of the side dam block material of the double belt casting apparatus. The cast material is usually formed by conventional forming methods, such as extrusion, forging, or rolling, to adjust the microstructure and to achieve the required hardness and electrical conductivity, and continue Solution treatment and precipitation hardening, in which case the eutectic heterogeneous distribution of the primary phase of the cast intermetallic compound is more or less fully destroyed, and The crystal phase is arranged in a streak pattern in the main molding direction. In conventional production of block material from extruded or hot-rolled rods, there is a relatively non-uniformly distributed, streak-aligned primary phase sequence on the cast surface of the block material. When forging a plate from an ingot, the total deformation degree is limited and the plate is formed almost equally in the longitudinal and transverse directions, so the distribution of the primary crystal network of the intermetallic compound in the cast state is usually Can only be removed poorly.
上記を背景にして、本発明は、鋳型部材の製造方法、とりわけ、二重ベルト鋳造装置のサイドダム用ブロック材の製造を、金属溶融物と接触する鋳造面の摩耗がより遅く始まり、かつよりゆっくりと進行するように最適化し、その結果、この鋳型部材の採用のもとで、より長い製造期間にわたって、欠点のない表面品質を有する鋳造された金属ストリップを製造することができるようにするという課題に基づく。さらに、向上された特性を有する鋳型部材の提供も狙いである。 Against the background described above, the present invention provides a method for producing a mold member, in particular, the production of a block member for a side dam of a double belt casting apparatus, in which wear of a casting surface in contact with a metal melt starts more slowly and more slowly. The problem of being able to produce a cast metal strip with a defect-free surface quality over a longer production period under the adoption of this mold part based on. Furthermore, it is an aim to provide a mold member having improved characteristics.
この課題の上記の方法の部分は、請求項１に記載の特徴によって解決される。 The above method part of this problem is solved by the features of claim 1.
有利な性質を有する鋳型部材は、請求項６に記載の対象物である。 A mold member having advantageous properties is the object of claim 6.
いずれの従属請求項も、本発明の概念の有利な発展形態に関する。 Any dependent claims relate to advantageous developments of the inventive concept.
本発明が基づく課題は、延伸されたインゴットから製造された鋳型部材の、金属溶融物と接触する鋳造表面は、インゴットの延伸方法に対し９０±１０°の角度、すなわち本質的に垂直な表面が選択されるように、銅合金中に含まれる金属間化合物の初晶相を方向付けられた熱間成形によって配向することによって解決される。以下において、“本質的に垂直”とは、インゴットの延伸方向に対して９０±１０°の角度であると理解される。垂直とは９０°の角度を意味する。 The problem on which the present invention is based is that the casting surface of a mold member made from a stretched ingot, which is in contact with the metal melt, has an angle of 90 ± 10 ° with respect to the ingot stretching method, ie an essentially vertical surface. As selected, this is solved by orienting the primary phase of the intermetallic compound contained in the copper alloy by directed hot forming. In the following, “essentially perpendicular” is understood to be an angle of 90 ± 10 ° with respect to the ingot stretching direction. Vertical means an angle of 90 °.
この処置方法では、インゴットの熱間成形時に、元来粒子の粗い鋳物組織の微粒組織再結晶化に加えて、はっきりと現れた繊維配向が、繊維に沿った金属間化合物の初晶相の細化及び方向付けによって、生ずることが本質である。ここで、繊維配向が、可能な限り微細でかつ均一な分布の初晶相を有することが重要であり、これは本発明の範囲内において、熱間成形による延伸が唯一の方向でだけ行われることによって達成され、その際、インゴットは、少なくとも４：１、好ましくは７：１よりも大きい比率で延伸される。この際、熱間成形は、鍛造及び又は熱間圧延のような方法によって行うことができる。それに対して、異なる方向における少なくとも４：１又は好ましくは少なくとも７：１のおおざっぱな全体成形は、本発明により所望される繊維延び方向を生じさせない。 In this treatment method, during the hot forming of an ingot, in addition to the recrystallization of the fine grain structure of the originally coarse grained structure, the fiber orientation that appears clearly is the fineness of the primary phase of the intermetallic compound along the fiber. It is the essence that arises from transformation and orientation. Here, it is important that the fiber orientation has the primary crystal phase with the finest possible and uniform distribution, which is within the scope of the present invention that the stretching by hot forming takes place only in one direction. The ingot is drawn at a ratio of at least 4: 1, preferably greater than 7: 1. At this time, the hot forming can be performed by a method such as forging and / or hot rolling. In contrast, a rough overall molding of at least 4: 1 or preferably at least 7: 1 in different directions does not produce the fiber extension direction desired by the present invention.
更に別の重要な方法の特徴とは、延伸されたインゴットから製造された鋳型部材が、金属溶融物と接触する鋳造面を有し、この鋳造面が、延伸方向に対して本質的に垂直な（＝９０±１０°）、好ましくは厳密に垂直に選択されることである。この場合においてのみ、鋳造面の摩耗が著しく低減され、それ故、より長い製造期間にわたって、申し分のない表面品質を有する鋳造された金属ストリップを製造することができる。 Yet another important method feature is that a mold member made from a stretched ingot has a casting surface that contacts the metal melt, the casting surface being essentially perpendicular to the stretching direction. (= 90 ± 10 °), preferably selected strictly vertically. Only in this case the wear of the casting surface is significantly reduced, and therefore a cast metal strip with a satisfactory surface quality can be produced over a longer production period.
繊維の配向によって、鋳造面における金属間化合物の初晶相は、本質的に、均一に分布した点としてだけ現れる。鋳造面と、鋳造面に対して垂直な位置にある延伸されたインゴットの面との間での顕微鏡写真に写された金属間化合物の初晶相の量比が、１．５：１より大きく調節される場合に、合目的的であると見なされる。これは、鋳造面においてあるいは延伸方向に対して本質的に垂直な平面においては、鋳造面に対して垂直な面あるいは平面における場合よりも、少なくとも５０％多くの金属間化合物の初晶相が写し出されることを意味する。 Due to the orientation of the fibers, the primary phase of the intermetallic compound at the casting surface appears essentially only as uniformly distributed points. The amount ratio of the primary phase of the intermetallic compound in the photomicrograph between the cast surface and the surface of the stretched ingot perpendicular to the cast surface is greater than 1.5: 1 When adjusted, it is considered purposeful. This is because at least 50% of the primary phase of the intermetallic compound is projected on the casting surface or in a plane essentially perpendicular to the drawing direction than in the plane or plane perpendicular to the casting surface. Means that
この鋳造面の配向と組み合わせて、写し出された金属間化合物の初晶相のこのように調節された量比は、最適化された使用挙動を有する鋳型部材を与える。なぜなら、この鋳造面における亀裂の開始と亀裂の成長が妨げられるからである。それによって、亀裂の成長がよりゆっくりと進み、それが寿命を引き伸ばすのに寄与するため、使用における鋳型部材の摩耗が低下する。疲労亀裂形成に対する耐性は、金属間化合物の初晶相が本質的に方向付けられていない鋳型部材と比べて、明らかにより大きい。 This adjusted quantity ratio of primary crystal phase of the projected intermetallic compound, in combination with the orientation of the casting surface, gives a mold part with an optimized usage behavior. This is because crack initiation and crack growth on this casting surface are hindered. Thereby, the wear of the mold member in use is reduced because the crack growth proceeds more slowly, which contributes to an extended life. The resistance to fatigue crack formation is clearly greater compared to mold members in which the primary phase of the intermetallic compound is essentially not oriented.
本発明による方法に従って製造された鋳型部材は、金属間化合物の初晶相を繊維又は筋状に配向させることをも引き起こす繊維延び方向を有する。ある一つの平面に存在する初晶相の平均長さは測定可能である。その鋳造面の平面に存在する筋の平均長さと、鋳造面に対して本質的に垂直に（＝９０±１０°）、好ましくは厳密に垂直に延びる筋の平均長さとの比率が、３：１０より小さいことが有利と見られる。言い換えるならば、鋳造面に対して本質的に垂直か又は厳密に垂直に延びている金属間化合物の初晶相の筋の長さのせいぜい３０％にあたる長さを持つ結晶間化合物の初晶相の筋が鋳造面に存在する。 The mold member produced according to the method according to the invention has a fiber extension direction which also causes the primary phase of the intermetallic compound to be oriented in fibers or streaks. The average length of the primary phase existing in one plane can be measured. The ratio between the average length of the streaks present in the plane of the casting surface and the average length of the streaks extending essentially perpendicular to the casting surface (= 90 ± 10 °), preferably strictly perpendicular is 3: Less than 10 may be advantageous. In other words, the primary crystal phase of the intercrystalline compound having a length corresponding to at most 30% of the length of the streaks of the primary crystal phase of the intermetallic compound extending essentially perpendicularly or strictly perpendicular to the casting surface. Are present on the casting surface.
本発明による鋳型部材は、析出硬化可能な銅合金からなり、この銅合金は、金属間化合物の相として析出するこの目的のための合金成分を構成成分として含む。この析出硬化可能な銅合金は、好ましくはニッケルを含み、これは、コバルトで少なくとも部分的に置き換えることができる。この合金は、次の合金元素、すなわちクロム、ジルコニウム、ベリリウム、ケイ素の少なくとも一種をさらに含む。 The mold member according to the invention consists of a precipitation-hardenable copper alloy, which contains as its constituent an alloy component for this purpose that precipitates as an intermetallic phase. This precipitation hardenable copper alloy preferably comprises nickel, which can be at least partially replaced by cobalt. This alloy further includes at least one of the following alloying elements: chromium, zirconium, beryllium, silicon.
完成した鋳型部材は、特定の用途に適合された優れた材料特性、すなわち、特に、２０℃の室温における少なくとも６００ＭＰａの引張り強さ、並びに、５００℃の温度における少なくとも３５０ＭＰａの引張り強さを特徴とする。 The finished mold member is characterized by excellent material properties adapted to the specific application, ie, in particular, a tensile strength of at least 600 MPa at room temperature of 20 ° C. and a tensile strength of at least 350 MPa at a temperature of 500 ° C. To do.
銅合金は、硬化された状態において２０℃で、少なくとも４７０ＭＰＡの０．２％−耐力（Dehngrenze）、少なくとも１５％の破断伸びＡ５、少なくとも１９０ＨＶ１０の硬度、並びに２０℃での少なくとも４０％ＩＡＣＳ（ＩＡＣＳ＝国際焼きなまし銅線標準、銅＝１００％と比較した電気伝導度）の電気伝導度を有する。好ましくは、電気伝導度は、少なくとも４５％である。 Copper alloy, at 20 ° C. in the cured state, at least 0.2% of 470 MPa - Strength (Dehngrenze), at least 15% of the elongation at break A 5, at least 190HV10 hardness, as well as at 20 ° C. of at least 40% IACS ( IACS = international annealed copper wire standard, copper = electrical conductivity compared to 100%). Preferably the electrical conductivity is at least 45%.
析出硬化された銅合金は、ＡＳＴＭ Ｅ １１２に基づいて測定されたせいぜい１３０μｍの粒度を有するべきである。米国規格のＡＳＴＭ Ｅ １１２（米国材料試験協会）は、平均粒度を測定するための標準試験法である。 The precipitation hardened copper alloy should have a particle size of at most 130 μm measured according to ASTM E 112. The American standard ASTM E 112 (American Society for Testing Materials) is a standard test method for measuring average particle size.
本発明は、後述の幾つかの実施例に基づいて説明される。 The present invention will be described on the basis of several embodiments described below.
図１は、鋳造された丸ビレットの顕微鏡写真を示しており、これは出発材料として、二重ベルト鋳造装置のサイドダムの鋳型部材を製造するのに使用される。これは、共晶配列にあるＣｒＳｉ−含有あるいはＮｉＺｒ−含有の金属間化合物の初晶相を有するＣｕＮｉＳｉＣｒＺｒ合金の典型的な鋳物組織である。この原材料は、引き続き、微粒組織の調整のために並びに必要な硬度及び電気伝導度を得るために、押出、鍛造又は圧延のような成形方法によって成形され、引き続き、溶体化処理及び析出硬化され、その結果、金属間化合物の初晶相の共晶性の不均一な分布が変化する。 FIG. 1 shows a photomicrograph of a cast round billet, which is used as a starting material to produce a side dam mold member of a double belt casting apparatus. This is a typical casting structure of a CuNiSiCrZr alloy having a primary phase of a CrSi-containing or NiZr-containing intermetallic compound in a eutectic arrangement. This raw material is subsequently formed by a forming method such as extrusion, forging or rolling for adjusting the fine structure and obtaining the required hardness and electrical conductivity, followed by solution treatment and precipitation hardening, As a result, the eutectic nonuniform distribution of the primary phase of the intermetallic compound changes.
図１中に示した、金属間化合物の初晶相の網状の分布を有する素材（Ｇｕｓｓｒｏｈｌｉｎｇ）が、長手方向においても横方向においても同等に変形される場合、相の配向は、所望するようには変わらない。 When the material having a network distribution of the primary crystal phase of the intermetallic compound shown in FIG. 1 is deformed equally in the longitudinal direction and in the lateral direction, the orientation of the phase is as desired. Will not change.
これに対し、図２は、すでに熱間成形されたインゴットの金属間化合物の初晶相の分布、及びそれでもって、のちの鋳型部材の鋳造面の領域における顕微鏡写真を示している。金属間化合物の初晶相が、非常に微小で、かつ均一に分布していることが明らかにわかる。繊維の配向あるいは金属間化合物の初晶相の配向は、鋳造面に対して垂直であり、それため、写し出された初晶相はこの図においては点として現れている。 In contrast, FIG. 2 shows the distribution of the primary crystal phase of an ingot intermetallic compound that has already been hot-formed, and hence a photomicrograph in the area of the casting surface of the mold member later. It can be clearly seen that the primary phase of the intermetallic compound is very fine and uniformly distributed. The orientation of the fibers or the primary crystal phase of the intermetallic compound is perpendicular to the casting surface, so that the projected primary crystal phase appears as dots in this figure.
鋳造面に対して垂直な、それ故、図２の鋳造面に対して垂直な顕微鏡写真を示す図３におけるように、写し出された初晶相の数は約１．７×程多い。図２において、相の筋はある程度のみ認めることができ、そして、最大１００μｍの長さである一方、図３においては、かなり多くの初晶相を認めることができ、その際、相の筋長は１００〜４００μｍの範囲内にあり、そして一部が４００μｍを越える範囲内にある。以下の表は、本発明の方法に従って製造された、ＣｕＮｉＳｉＣｒＺｒ−合金からなる鋳型部材の機械特性並びに疲労耐性を明示している。
実施例Ａは、次の組成（重量％）を有する合金に基づく置く：
この合金を、誘導るつぼ炉中で溶融し、そして、連続鋳造法で丸いインゴットへ鋳込んだ。この丸いインゴットを、鍛造プレス機によって、９５０℃〜７５０℃の温度範囲内でプリセットアップし（vorgestaucht）、そしてそれから直方体に成形した。この直方体を、それから長手方向においてプレートに鍛造した。この予備鍛造したプレートを、それから、９５０℃〜８００℃の熱間圧延機で最終寸法に圧延した。長手方向における全体の変形比率Ｖは、プリセットアップ長から、完成した圧延されたプレート長さまでで、５．３：１であった。プレートを、引き続き、溶体化処理し、そして析出硬化させた。析出硬化後の冷却は、所定の冷却速度を用いて炉中で行った。引き続き、そのプレートを、横方向にストリップ状にのこぎりで切り、そしてこれらのストリップから、７０ｍｍ×５０ｍｍ×４０ｍｍの寸法を有するダムブロック材と呼ばれる鋳型部材を製造した。 The alloy was melted in an induction crucible furnace and cast into a round ingot by a continuous casting process. The round ingot was vorgestaucht by a forging press in the temperature range of 950 ° C. to 750 ° C. and then formed into a rectangular parallelepiped. This cuboid was then forged into a plate in the longitudinal direction. This pre-forged plate was then rolled to final dimensions on a hot rolling mill at 950 ° C to 800 ° C. The overall deformation ratio V in the longitudinal direction was 5.3: 1 from the pre-setup length to the finished rolled plate length. The plate was subsequently solution treated and precipitation hardened. Cooling after precipitation hardening was performed in a furnace using a predetermined cooling rate. Subsequently, the plate was sawed into strips in the transverse direction, and mold members called dam block material having dimensions of 70 mm × 50 mm × 40 mm were produced from these strips.
替わりに、同じ方法で、寸法６０ｍｍ×５０ｍｍ×４０ｍｍ、あるは５０ｍｍ×５０ｍｍ×４０ｍｍの鋳型部材を取り出すことができる。その際に、鋳型部材の鋳造面は、本質的にプレートの長手方向に対して垂直、とりわけ厳密には垂直となり、そしてそれでもって成形されたインゴットの延伸方向又は繊維配向対して垂直、好ましく厳密に垂直となる。 Instead, a mold member with dimensions 60 mm × 50 mm × 40 mm or 50 mm × 50 mm × 40 mm can be taken out in the same way. In doing so, the casting surface of the mold member is essentially perpendicular to the longitudinal direction of the plate, in particular strictly perpendicular, and is thus perpendicular to the drawing direction or fiber orientation of the molded ingot, preferably strictly It becomes vertical.
そのように取り出された鋳型部材の機械的／技術的性質、並びに疲労耐性を、繊維が鋳造面に対して平行な鋳型部材、あるいは少なくとも４：１の比率ですぐれた成形を経ていない鋳型部材と比較して表中に示す。本発明による方法に従って製造された、鋳造面に対して垂直な金属間化合物の初晶相の方向付けを持つ鋳型部材は、実験室の試験において、繊維長が鋳造面に対して平行に伸びている鋳型部材と比較して、１７％向上した疲労耐性を示す。 The mechanical / technical properties and fatigue resistance of the mold member so taken out are such that the fiber is parallel to the casting surface and the mold member is not subjected to good molding in a ratio of at least 4: 1. Comparison is shown in the table. A mold member produced according to the method of the present invention and having an orientation of the primary phase of an intermetallic compound perpendicular to the casting surface has a fiber length extending parallel to the casting surface in laboratory tests. The fatigue resistance is improved by 17% compared with the mold member.
実施例Ｂは、次の組成を有する合金に基づく。
この合金も、誘導るつぼ炉中で溶融し、そして連続鋳造法において、丸いインゴットに鋳込んだ。この丸いインゴットを、引き続き、９５０℃〜８００℃の熱間圧延機でプレートに圧延した。長手方向における全体の変形比率Ｖは、インゴットの初期長さに対して７．４：１であり、そして、それ故少なくとも７：１である好ましい本発明の規準に相当する。 This alloy was also melted in an induction crucible furnace and cast into a round ingot in a continuous casting process. The round ingot was subsequently rolled into a plate with a hot rolling mill at 950 ° C to 800 ° C. The overall deformation ratio V in the longitudinal direction is 7.4: 1 with respect to the initial length of the ingot and therefore corresponds to a preferred inventive criterion which is at least 7: 1.
熱間圧延されたプレートのさらなる処理、及び鋳型部材の取り出しは実施例Ａと同様に行う。 Further processing of the hot-rolled plate and removal of the mold member are performed as in Example A.
表１には、延伸方向に対して垂直に延びる初晶相を有する鋳型部材の強度特性が、鋳造方向に対して金属間化合物の初晶相が平行に延びている鋳型部材と比較して、再度表されている。 Table 1 shows that the strength characteristics of the mold member having the primary crystal phase extending perpendicularly to the stretching direction is higher than that of the mold member having the primary crystal phase of the intermetallic compound extending parallel to the casting direction. It is represented again.
実施例Ｂによる本発明によって製造された鋳型部材は、匹敵する機械的特性において、実験室での試験において、繊維配向が鋳造面に対して平行な鋳型部材と比較して、２６％向上された疲労耐性をも示す。 The mold member produced by the present invention according to Example B has a 26% improvement in comparable mechanical properties compared to the mold member parallel to the casting surface in laboratory tests, compared to the mold member parallel to the casting surface. Also shows fatigue resistance.
この実施例は、本発明によって製造された鋳型部材が、鋳造面に対して平行な繊維及び相配向を有するか、又は優先的な配向を有さない鋳型部材と比較して、１７〜２６％向上された鋳造面の疲労挙動を有することを示している。 This example shows that the mold member produced according to the present invention has a fiber and phase orientation parallel to the casting surface, or 17-26% compared to a mold member with no preferential orientation. It shows an improved cast surface fatigue behavior.
Claims (16)
群（ａ）
− ニッケル （Ｎｉ）、
− コバルト （Ｃｏ）、
群（ｂ）
− クロム（Ｃｒ）、
− ジルコニウム（Ｚｒ）、
− ベリリウム（Ｂｅ）、
− ケイ素（Ｓｉ）、
銅（Ｃｕ）含有の不可避的混入物の残部、
を含み、その際に、インゴットが、熱間成形によって一方向においてだけ、少なくとも４：１の比率で延伸され、その際に、延伸されたインゴットから製造された鋳型部材の、金属溶融物と接触する鋳造面は、インゴットの延伸方向に対して９０±１０°の角度の鋳造面が選択される、上記方法。 A method for producing a mold member comprising a copper alloy, wherein the copper alloy comprises at least one alloy element from each of the following groups (a) and (b), and an intermetallic compound of the alloy element: Including a primary phase, the copper alloy,
Group (a)
-Nickel (Ni),
-Cobalt (Co),
Group (b)
-Chromium (Cr),
-Zirconium (Zr),
-Beryllium (Be),
-Silicon (Si),
The balance of copper (Cu) containing inevitable contaminants,
Wherein the ingot is stretched in a ratio of at least 4: 1 in only one direction by hot forming, wherein the mold member made from the stretched ingot is in contact with the metal melt. The method as described above, wherein the casting surface to be selected is a casting surface having an angle of 90 ± 10 ° with respect to the extending direction of the ingot.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE102008015096.7 | 2008-03-19 | ||
| DE102008015096A DE102008015096A1 (en) | 2008-03-19 | 2008-03-19 | Process for producing molded parts and molded parts produced by the process |
| PCT/DE2009/000359 WO2009115081A1 (en) | 2008-03-19 | 2009-03-19 | Method for the production of castings and castings produced according to the method |
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| JP2011518668A JP2011518668A (en) | 2011-06-30 |
| JP5328886B2 true JP5328886B2 (en) | 2013-10-30 |
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| JP2011500041A Expired - Fee Related JP5328886B2 (en) | 2008-03-19 | 2009-03-19 | Mold member manufacturing method and mold member manufactured by the manufacturing method |
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| Country | Link |
|---|---|
| US (1) | US20110056646A1 (en) |
| EP (1) | EP2280794A1 (en) |
| JP (1) | JP5328886B2 (en) |
| CN (1) | CN101945719B (en) |
| CA (1) | CA2718808C (en) |
| DE (1) | DE102008015096A1 (en) |
| RU (1) | RU2492961C2 (en) |
| WO (1) | WO2009115081A1 (en) |
Family Cites Families (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5370923A (en) * | 1976-12-06 | 1978-06-23 | Kobe Steel Ltd | Mold in copper alloy for steel continuous casting |
| LU82346A1 (en) * | 1980-04-08 | 1981-12-02 | Liege Usines Cuivre Zinc | IMPROVEMENTS ON SHORE BLOCKS FOR CONTINUOUS CASTING OF COPPER BARS |
| JPS5736040A (en) * | 1980-08-11 | 1982-02-26 | Chuetsu Gokin Chuko Kk | Deposition hardening type mold material for continuous casting |
| US4415374A (en) * | 1982-03-30 | 1983-11-15 | International Telephone And Telegraph Corporation | Fine grained metal composition |
| DE3820203A1 (en) * | 1988-06-14 | 1989-12-21 | Kabelmetal Ag | USE OF A CURABLE copper alloy |
| JP2738130B2 (en) * | 1990-05-25 | 1998-04-08 | 三菱マテリアル株式会社 | High strength Cu alloy continuous casting mold material having high cooling capacity and method for producing the same |
| JPH04210438A (en) * | 1990-12-13 | 1992-07-31 | Mitsubishi Materials Corp | Continuous casting mold material made of high strength cu alloy |
| DE4427939A1 (en) * | 1994-08-06 | 1996-02-08 | Kabelmetal Ag | Use of a hardenable copper alloy |
| JP3303623B2 (en) * | 1995-09-22 | 2002-07-22 | 三菱マテリアル株式会社 | Method for producing copper alloy mold material for steelmaking continuous casting and mold produced thereby |
| DE19928777A1 (en) * | 1999-06-23 | 2000-12-28 | Vacuumschmelze Gmbh | Rotation-symmetrical cooling wheel used in the production of amorphous and/or microcrystalline metal bands has a non-equiaxial grain structure whose grains are longitudinal |
| TW590822B (en) * | 2001-11-21 | 2004-06-11 | Km Europa Metal Ag | Casting-roller for a two-roller-casting equipment and its manufacturing method |
| DE10156925A1 (en) * | 2001-11-21 | 2003-05-28 | Km Europa Metal Ag | Hardenable copper alloy as a material for the production of casting molds |
| DE10206597A1 (en) * | 2002-02-15 | 2003-08-28 | Km Europa Metal Ag | Hardenable copper alloy used as a material for blocks for the sides of strip casting mills contains alloying additions of cobalt, beryllium, zirconium, and magnesium and/or iron |
| DE10227034A1 (en) * | 2002-06-17 | 2003-12-24 | Km Europa Metal Ag | Copper casting mold |
| JP4118832B2 (en) * | 2004-04-14 | 2008-07-16 | 三菱伸銅株式会社 | Copper alloy and manufacturing method thereof |
| CN100425717C (en) * | 2006-08-16 | 2008-10-15 | 苏州有色金属加工研究院 | Copper alloy for lead-wire frame and its production |
-
2008
- 2008-03-19 DE DE102008015096A patent/DE102008015096A1/en not_active Withdrawn
-
2009
- 2009-03-19 WO PCT/DE2009/000359 patent/WO2009115081A1/en active Application Filing
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|---|---|
| CA2718808A1 (en) | 2009-09-24 |
| CN101945719B (en) | 2013-03-13 |
| US20110056646A1 (en) | 2011-03-10 |
| CN101945719A (en) | 2011-01-12 |
| DE102008015096A1 (en) | 2009-09-24 |
| JP2011518668A (en) | 2011-06-30 |
| CA2718808C (en) | 2015-05-26 |
| WO2009115081A1 (en) | 2009-09-24 |
| RU2492961C2 (en) | 2013-09-20 |
| EP2280794A1 (en) | 2011-02-09 |
| RU2010142458A (en) | 2012-04-27 |
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