JP5535212B2 - Manufacturing method of ceramic member - Google Patents

Manufacturing method of ceramic member Download PDF

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Publication number
JP5535212B2
JP5535212B2 JP2011521487A JP2011521487A JP5535212B2 JP 5535212 B2 JP5535212 B2 JP 5535212B2 JP 2011521487 A JP2011521487 A JP 2011521487A JP 2011521487 A JP2011521487 A JP 2011521487A JP 5535212 B2 JP5535212 B2 JP 5535212B2
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JP
Japan
Prior art keywords
ceramic member
ceramic
sintering
temperature
starting material
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Fee Related
Application number
JP2011521487A
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Japanese (ja)
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JP2011529850A (en
Inventor
ヘルムート・デー・リンク
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Deru GmbH
Original Assignee
Deru GmbH
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Filing date
Publication date
Priority claimed from PCT/EP2008/006524 external-priority patent/WO2009036845A2/en
Application filed by Deru GmbH filed Critical Deru GmbH
Publication of JP2011529850A publication Critical patent/JP2011529850A/en
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Publication of JP5535212B2 publication Critical patent/JP5535212B2/en
Expired - Fee Related legal-status Critical Current
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    • A—HUMAN NECESSITIES
    • A61—MEDICAL OR VETERINARY SCIENCE; HYGIENE
    • A61F—FILTERS IMPLANTABLE INTO BLOOD VESSELS; PROSTHESES; DEVICES PROVIDING PATENCY TO, OR PREVENTING COLLAPSING OF, TUBULAR STRUCTURES OF THE BODY, e.g. STENTS; ORTHOPAEDIC, NURSING OR CONTRACEPTIVE DEVICES; FOMENTATION; TREATMENT OR PROTECTION OF EYES OR EARS; BANDAGES, DRESSINGS OR ABSORBENT PADS; FIRST-AID KITS
    • A61F2/00—Filters implantable into blood vessels; Prostheses, i.e. artificial substitutes or replacements for parts of the body; Appliances for connecting them with the body; Devices providing patency to, or preventing collapsing of, tubular structures of the body, e.g. stents
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    • A61F2/00—Filters implantable into blood vessels; Prostheses, i.e. artificial substitutes or replacements for parts of the body; Appliances for connecting them with the body; Devices providing patency to, or preventing collapsing of, tubular structures of the body, e.g. stents
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    • A61F2/44—Joints for the spine, e.g. vertebrae, spinal discs
    • A61F2/442—Intervertebral or spinal discs, e.g. resilient
    • A61F2/4425—Intervertebral or spinal discs, e.g. resilient made of articulated components
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
    • C04B35/10—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on aluminium oxide
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
    • C04B35/48—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on zirconium or hafnium oxides, zirconates, zircon or hafnates
    • C04B35/486—Fine ceramics
    • C—CHEMISTRY; METALLURGY
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    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
    • C04B41/009—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone characterised by the material treated
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
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    • C04B41/50—Coating or impregnating, e.g. injection in masonry, partial coating of green or fired ceramics, organic coating compositions for adhering together two concrete elements with inorganic materials
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    • C04B41/5133—Metallising, e.g. infiltration of sintered ceramic preforms with molten metal with a composition mainly composed of one or more of the refractory metals
    • C—CHEMISTRY; METALLURGY
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    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
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    • C04B41/80—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone of only ceramics
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    • A—HUMAN NECESSITIES
    • A61—MEDICAL OR VETERINARY SCIENCE; HYGIENE
    • A61F—FILTERS IMPLANTABLE INTO BLOOD VESSELS; PROSTHESES; DEVICES PROVIDING PATENCY TO, OR PREVENTING COLLAPSING OF, TUBULAR STRUCTURES OF THE BODY, e.g. STENTS; ORTHOPAEDIC, NURSING OR CONTRACEPTIVE DEVICES; FOMENTATION; TREATMENT OR PROTECTION OF EYES OR EARS; BANDAGES, DRESSINGS OR ABSORBENT PADS; FIRST-AID KITS
    • A61F2310/00—Prostheses classified in A61F2/28 or A61F2/30 - A61F2/44 being constructed from or coated with a particular material
    • A61F2310/00389—The prosthesis being coated or covered with a particular material
    • A61F2310/00395—Coating or prosthesis-covering structure made of metals or of alloys
    • A61F2310/00407—Coating made of titanium or of Ti-based alloys
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B2111/00—Mortars, concrete or artificial stone or mixtures to prepare them, characterised by specific function, property or use
    • C04B2111/00474—Uses not provided for elsewhere in C04B2111/00
    • C04B2111/00836—Uses not provided for elsewhere in C04B2111/00 for medical or dental applications
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    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
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    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
    • C04B2235/60—Aspects relating to the preparation, properties or mechanical treatment of green bodies or pre-forms
    • C04B2235/612—Machining
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
    • C04B2235/65—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes
    • C04B2235/66—Specific sintering techniques, e.g. centrifugal sintering
    • C04B2235/661—Multi-step sintering
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    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
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    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
    • C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
    • C04B2235/96—Properties of ceramic products, e.g. mechanical properties such as strength, toughness, wear resistance
    • C04B2235/963—Surface properties, e.g. surface roughness

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Description

本発明は、セラミック部材の製造方法に関する。その方法では、粉末状のセラミック出発材料を利用可能にし、セラミック部材の形状を予め規定するモールドに導入する。セラミック部材を、予備焼結させ、モールドから取り出し、次に、予備焼結の温度よりも高い温度で焼結させる。   The present invention relates to a method for manufacturing a ceramic member. In that method, a powdered ceramic starting material is made available and the shape of the ceramic member is introduced into a pre-defined mold. The ceramic member is pre-sintered and removed from the mold and then sintered at a temperature higher than the pre-sintering temperature.

セラミック部材のそのような製造方法は、例えば欧州特許第０４２１０８５号により知られている。このようにして製造されたセラミック部材は、低い表面粗さを有し、それゆえ、セラミック部材にコーティングをしっかりと適用することは難しいことが分かっている。   Such a method for producing a ceramic member is known, for example, from EP 0421085. Ceramic members produced in this way have a low surface roughness and it has therefore proved difficult to apply a coating firmly to the ceramic member.

本発明の目的は、セラミック部材の製造方法を提供することであり、その方法において、本発明に基づいて製造されたセラミック部材は、コーティングの適用にとってより良い出発基盤を提供する。先に記載の先行技術から進めて、その目的は、独立請求項の特徴によって達成される。有利な実施形態は、従属請求項に明記されている。本発明に基づいて、予備焼結工程のために、８８０℃〜９８０℃の間の温度を選択する。予備焼結後かつ焼結前に、セラミック部材の表面をブラスト材料で処理する。   The object of the present invention is to provide a method of manufacturing a ceramic member, in which the ceramic member manufactured according to the present invention provides a better starting basis for coating applications. Proceeding from the prior art described above, the object is achieved by the features of the independent claims. Advantageous embodiments are specified in the dependent claims. Based on the present invention, a temperature between 880 ° C. and 980 ° C. is selected for the pre-sintering step. After the pre-sintering and before sintering, the surface of the ceramic member is treated with a blast material.

セラミック部材を製造するために、まず、粉末状のセラミック出発材料を、セラミック部材の形状を予め規定するモールドに導入する。セラミック部材の体積は、その後に続く加工工程の結果として減少するため、モールドは完成したセラミック部材よりも大きい。セラミック部材の安定な内部構造は、その後に続く焼結によって達成される。焼結は、粉末の粒子同士の確固とした接続をもたらす。   In order to produce a ceramic member, first a powdery ceramic starting material is introduced into a mold that predefines the shape of the ceramic member. Because the volume of the ceramic member decreases as a result of subsequent processing steps, the mold is larger than the finished ceramic member. A stable internal structure of the ceramic member is achieved by subsequent sintering. Sintering provides a firm connection between the powder particles.

焼結を複数の工程で行なう。第１工程において、セラミック部材をより低温で予備焼結させ、粉末の粒子間に狭いブリッジのみを形成する。本発明に基づく方法にとっての狭いブリッジの安定性は、ちょうど、ブラスト材料による表面の処理が表面粗さの増加をもたらすようなものである必要がある。ブリッジの安定性が低すぎる場合、セラミック部材は、破砕して幾つかの部分に分かれてしまい、ブリッジの安定性が高すぎる場合、ブラスト材料による処理は、セラミック部材の表面構造を変化させるのに十分でない。予備焼結のために、８８０℃〜９８０℃の間の温度を選択する場合、ブラスト材料により表面構造の所望の変化が起きることを、試験は示した。そして、セラミック部材の内部構造は、ちょうど、ブラスト材料によってその部材から所望のサイズの断片が割れて取り出されることができるようなものである。   Sintering is performed in multiple steps. In the first step, the ceramic member is pre-sintered at a lower temperature to form only narrow bridges between the powder particles. The narrow bridge stability for the method according to the invention just needs to be such that the treatment of the surface with the blast material results in an increase of the surface roughness. If the bridge stability is too low, the ceramic member will break into several parts, and if the bridge stability is too high, the treatment with blasting material will change the surface structure of the ceramic member. not enough. Tests have shown that when a temperature between 880 ° C. and 980 ° C. is selected for presintering, the blast material causes the desired change in surface structure. And the internal structure of the ceramic member is just such that a piece of the desired size can be broken out of the member by the blast material.

予備焼結の温度が上がると、粉末材料の粒子同士の接続の強さは一般的に増加する。予備焼結の温度は、９００℃よりも高い、あるいは９５０℃よりも低い場合、本発明に基づく方法によって、良好な結果が得られた。   As the presintering temperature increases, the strength of the connection between the particles of the powder material generally increases. Good results have been obtained with the method according to the invention when the presintering temperature is higher than 900 ° C. or lower than 950 ° C.

セラミック部材をチタン合金で被覆することができるようにするために、表面粗さＲａは２．５μｍよりも大きい必要がある（国際公開第２００９／０３６８４５号）。本発明の文脈における粗さの値は、ＤＩＮ ＥＮ ＩＳＯ ４２８８および３２７４に基づく平均粗さＲａに関わっており、ならびに焼結後の完成したセラミック部材に関わる。本発明に基づく方法によって達成される表面粗さは、ブラスト材料による処理にて選択されたパラメータによって決まり、例えば、ブラスト材料の粒子サイズおよび粒子がセラミック部材に衝突するスピードである。本発明に基づく方法において、完成したセラミック部材の表面粗さＲａが２．５μｍよりも大きくなるように、これらのパラメータを適応させることが好ましい。１つの作業工程で、表面を覆うようにコーティングを適用することができることを、確実にするために、完成したセラミック部材の表面粗さＲａは、７μｍ以下であるべきである。 The ceramic member in order to be able to coat a titanium alloy, the surface roughness R a must be greater than 2.5 [mu] m (WO 2009/036845). Roughness values in the context of the present invention is concerned with an average roughness R a that is based on DIN EN ISO 4288 and 3274, and related to the finished ceramic component after sintering. The surface roughness achieved by the method according to the invention depends on the parameters selected in the treatment with the blast material, for example the particle size of the blast material and the speed at which the particles impinge on the ceramic member. In the process according to the invention, so that the surface roughness R a of the finished ceramic member is greater than 2.5 [mu] m, it is preferable to adapt these parameters. In one working step, that can be applied coating so as to cover the surface, in order to ensure a surface roughness R a of the finished ceramic component, should be 7μm or less.

本発明の文脈において、セラミック部材の表面全体を、ブラスト材料で処理することができる。このことは、セラミック部材の表面全体にコーティングを提供すべき場合には、都合が良い。しかしながら、表面の一部のみが被覆されるべきで、一方、表面の別の部分はコーティングがないままにすべきであることが多い。これは、例えば内部人工器官部材に当て嵌まり、その表面は一部で、骨質との接続を形成するように意図され、一方、別の部分は、別の人工器官部材との相互作用のためにスライド表面として機能するように意図される。スライド表面にとって、大きな表面粗さは望ましくない。従って、本発明に基づく方法において、セラミック部材の表面の一部のみがブラスト材料で処理され、一方、表面の別の部分はブラスト材料による処理から除外されたままであるという条件を付けることができる。本発明の文脈において、セラミック部材の表面の処理について言及する場合、これは、表面全体または表面の一部を意味することができる。   In the context of the present invention, the entire surface of the ceramic member can be treated with a blast material. This is advantageous when a coating should be provided over the entire surface of the ceramic member. However, often only a portion of the surface should be coated, while another portion of the surface should be left uncoated. This applies for example to an endoprosthesis member, whose surface is partly intended to form a connection with the bone quality, while another part is for interaction with another prosthesis member It is intended to function as a slide surface. A large surface roughness is undesirable for the slide surface. Thus, in the method according to the invention, it can be provided that only a part of the surface of the ceramic member is treated with the blast material, while another part of the surface remains excluded from the treatment with the blast material. In the context of the present invention, when referring to the treatment of the surface of a ceramic member, this can mean the entire surface or a part of the surface.

ブラスト材料の粒子サイズは、セラミック出発材料の粒子サイズと同じオーダーであることが好ましい。その場合、ブラスト材料は、セラミック部材に特に効果的に作用することができる。しかしながら、そのようなブラスト材料を用いる場合、取り出される断片の結果としてセラミック材料に生じる隙間に、ブラスト材料の粒子が付着するという危険がある。その場合、粒子は、セラミック材料において不純物を意味する。この種の不純物は、セラミック出発材料の粉末と一致する（corresponds）粉末を、ブラスト材料として用いることによって防ぐことができる。この材料の粒子がセラミック部材内に付着しても、それらは、セラミック材料の同質な組成を変えない。
The particle size of the blast material is preferably in the same order as the particle size of the ceramic starting material. In that case, the blasting material can act particularly effectively on the ceramic member. However, when using such a blast material, there is a risk that the particles of the blast material will adhere to the gaps created in the ceramic material as a result of the fragments being removed. In that case, the particles mean impurities in the ceramic material. This type of impurity can be prevented by using a powder that corresponds to the ceramic starting material powder as the blasting material. Even if particles of this material are deposited in the ceramic member, they do not change the homogeneous composition of the ceramic material.

セラミック部材の表面に適用されるコーティングは、チタン合金または純チタンでできていてよい。コーティングを適用するための可能な方法は、プラズマ溶射である。プラズマ溶射は、ガスが電気アークを通って導かれ、それによって電離される方法である。コーティング材料は、粉末状で電離ガスに導入され、そのガスのストリームによって被覆すべき加工物に運ばれる。   The coating applied to the surface of the ceramic member may be made of a titanium alloy or pure titanium. A possible method for applying the coating is plasma spraying. Plasma spraying is a method in which gas is directed through an electric arc and thereby ionized. The coating material is introduced into the ionizing gas in powder form and is carried by the gas stream to the workpiece to be coated.

ジルコニウム酸化物、アルミニウム酸化物およびこの２つの混合物は、本発明に基づく方法にとって、セラミック材料として適当であることが分かった。   Zirconium oxide, aluminum oxide and a mixture of the two have been found to be suitable as ceramic materials for the process according to the invention.

本発明を、添付図面を参照し、有利な例示的な実施形態に基づいて、以下でより詳細に説明する。図面は以下のとおりである。   The invention is explained in more detail below on the basis of advantageous exemplary embodiments with reference to the attached drawings. The drawings are as follows.

図１は、断面における椎間板人工器官を示す。FIG. 1 shows an intervertebral disc prosthesis in cross section. 図２は、図１に基づく椎間板人工器官の拡大詳細図を示す。FIG. 2 shows an enlarged detailed view of the intervertebral disc prosthesis based on FIG. 図３は、出発状態のセラミック材料の内部構造の概略図を示す。FIG. 3 shows a schematic view of the internal structure of the starting ceramic material. 図４は、予備焼結後の図３に由来する図面を示す。FIG. 4 shows a drawing derived from FIG. 3 after presintering. 図５は、焼結後の図３に由来する図面を示す。FIG. 5 shows a drawing derived from FIG. 3 after sintering.

図１において、椎間板人工器官として構成された内部人工器官が、２つの脊椎体６、７の間の椎間腔に挿入されている。椎間板人工器官は、第１コンタクトプレート１および第２コンタクトプレート２を有して成る。第１コンタクトプレート１は、第１脊椎体６に接続するために構成された内部人工器官部材であり、第２コンタクトプレート２は、第２脊椎体７に接続するために構成された内部人工器官である。   In FIG. 1, an endoprosthesis configured as an intervertebral disc prosthesis has been inserted into the intervertebral space between two vertebral bodies 6, 7. The intervertebral disc prosthesis includes a first contact plate 1 and a second contact plate 2. The first contact plate 1 is an endoprosthetic member configured to connect to the first vertebral body 6, and the second contact plate 2 is an endoprosthesis configured to connect to the second vertebral body 7. It is.

第１コンタクトプレート１および第２コンタクトプレート２は、スライド表面３を合わせることによって、互いに圧迫し合う。スライド表面３は、上側コンタクトプレート１と下側コンタクトプレート２との間の動きのためのヒンジを形成する。   The first contact plate 1 and the second contact plate 2 are pressed against each other by bringing the slide surfaces 3 together. The slide surface 3 forms a hinge for movement between the upper contact plate 1 and the lower contact plate 2.

突出部１２は、コンタクトプレート１、２の表面の領域１３に形成され、その領域において、コンタクトプレート１、２は脊椎体６、７の骨質上に位置する。突出部１２は、より緩やかなフランクをコンタクトプレート１、２が椎間腔に押し込まれる方向に有し、より急なフランクを反対方向に有する。緩やかな方のフランクは、コンタクトプレート１、２を椎間腔に押し込むのをより容易にさせる。突出部１２が脊椎体６、７の骨質に侵入した場合、急な方のフランクは、コンタクトプレート１、２を維持させる。急な方のフランクは、コンタクトプレート１、２が椎間腔から反対方向に再び引き戻されるのを防止する。   The protrusion 12 is formed in a region 13 on the surface of the contact plates 1 and 2, and the contact plates 1 and 2 are located on the bone quality of the vertebral bodies 6 and 7. The protrusion 12 has a more gradual flank in the direction in which the contact plates 1 and 2 are pushed into the intervertebral space and a steeper flank in the opposite direction. The gentler flank makes it easier to push the contact plates 1, 2 into the intervertebral space. When the protrusion 12 enters the bone of the vertebral bodies 6 and 7, the steep flank maintains the contact plates 1 and 2. The steep flank prevents the contact plates 1, 2 from being pulled back from the intervertebral space in the opposite direction.

コンタクトプレート１、２のフランジ４、５は、脊椎体６、７の腹側の面上に位置することが意図される。フランジ４、５は、コンタクトプレート１、２が所望の位置よりも遠くへ背側の方向に椎間腔の中へ押し込まれることができないという効果をもたらす。   The flanges 4 and 5 of the contact plates 1 and 2 are intended to be located on the ventral surfaces of the vertebral bodies 6 and 7. The flanges 4, 5 have the effect that the contact plates 1, 2 cannot be pushed into the intervertebral space in the dorsal direction farther than desired.

コンタクトプレート１およびコンタクトプレート２は、セラミック材料９から形成される。コンタクトプレート１、２上のスライド表面３は、セラミック材料９の表面に形成される。骨質との接続が確立される領域１３は、チタン合金コーティング１０で被覆される。   The contact plate 1 and the contact plate 2 are formed from a ceramic material 9. The slide surface 3 on the contact plates 1, 2 is formed on the surface of the ceramic material 9. The region 13 where the connection with the bone quality is established is covered with a titanium alloy coating 10.

図２は、コンタクトプレート１、２の拡大詳細図を示し、そこにおいて、セラミック材料９とコーティング１０との間に界面８が図示される。セラミック材料９は、コーティング１０との界面８にて、少なくとも２．５μｍの粗さＲａを有する。界面８におけるこの粗さは、コーティング１０との安定な接続を確立するには十分であるが、骨質との安定な接続には十分ではない。コーティング１０は、セラミック材料９よりも、より大きな粗さおよびより大きな多孔性を有し、それによって、骨質との安定な接続を形成する。 FIG. 2 shows an enlarged detailed view of the contact plates 1, 2, in which an interface 8 is illustrated between the ceramic material 9 and the coating 10. Ceramic material 9, at the interface 8 between the coating 10, having at least 2.5μm roughness R a. This roughness at the interface 8 is sufficient to establish a stable connection with the coating 10, but not enough for a stable connection with bone. The coating 10 has greater roughness and greater porosity than the ceramic material 9, thereby forming a stable connection with the bone quality.

表面の一部が所望の粗さを有する内部人工器官部材として、セラミック部材を製造するために、まず、粉末状で存在する出発材料を、製造することになっているセラミック部材と形状が対応するモールドに導入する。セラミック部材は、その後の方法工程の結果として体積が減少するため、モールドは、完成したセラミック部材よりも大きな大きさを有する。その粉末を、例えば振動および圧力によって、モールド内で機械的に圧縮し、そうすると、図３にて概略的に図示されるように、粉末の粒子１４は互いに隣接する。９２０℃の温度での予備焼結の結果、（図４に図示される）ブリッジが、粒子１４間に生じる。今やセラミック部材をモールドから取り出すことができるほど、材料の内部構造は安定である。   In order to manufacture a ceramic member as an endoprosthetic member having a desired surface roughness, first the starting material present in powder form corresponds to the shape of the ceramic member to be manufactured. Introduce into mold. Since the ceramic member decreases in volume as a result of subsequent method steps, the mold has a larger size than the finished ceramic member. The powder is mechanically compressed in the mold, for example by vibration and pressure, so that the powder particles 14 are adjacent to each other, as schematically illustrated in FIG. As a result of pre-sintering at a temperature of 920 ° C., a bridge (illustrated in FIG. 4) is formed between the particles 14. The internal structure of the material is so stable that the ceramic member can now be removed from the mold.

ブリッジ１５によって、セラミック材料は、穿孔またはフライス削りによる機械加工のために選択されるであろうものよりも、その構造に関してより大きな安定性を有する。構造の安定性は、具体的に言うと、出発材料と一致する粉末でブラストすることによって、予備焼成したセラミック材料から断片を切り離すことができるほどである。その断片は、焼成後、完成したセラミック部材が所望の表面粗さを有するほどの大きさである。

With the bridge 15, the ceramic material has a greater stability with respect to its structure than would be selected for machining by drilling or milling. The structural stability is specifically such that the pieces can be separated from the prefired ceramic material by blasting with a powder consistent with the starting material. The pieces are so large that after firing, the finished ceramic member has the desired surface roughness.

所望の表面構造を得て、機械加工が終了したら、セラミック部材を、予備焼結の温度よりも高い温度で焼結させる。以前ブリッジ１５によってしか接続されていなかった粒子の界面に、平面的な接続１６が生じる。内部から空隙が無くなるため、セラミック部材の体積は更に減少する。ブラスト材料により処理された表面の部分にて、今やその表面は、約４μｍの粗さＲａを有する。表面のこの部分に適用されるチタン合金でできたコーティングは、表面にしっかりと付着する。 Once the desired surface structure is obtained and machining is complete, the ceramic member is sintered at a temperature higher than the presintering temperature. A planar connection 16 occurs at the interface of the particles that was previously connected only by the bridge 15. Since there are no voids from the inside, the volume of the ceramic member is further reduced. In the part of the surface treated with the blast material, the surface now has a roughness Ra of about 4 μm. The coating made of titanium alloy applied to this part of the surface adheres firmly to the surface.

Claims (9)

セラミック部材の製造方法であって、以下の工程：
ａ．粉末状のセラミック出発材料を利用可能にする工程；
ｂ．セラミック部材の形状を予め規定するモールドを利用可能にする工程；
ｃ．セラミック出発材料をモールドに導入する工程；
ｄ．セラミック出発材料を８８０℃〜９８０℃の間の温度で予備焼結させる工程；
ｅ．セラミック部材をモールドから取り出す工程；
ｆ．セラミック部材の表面をブラスト材料で処理する工程；
ｇ．セラミック部材を予備焼結の温度よりも高い温度で焼結させる工程
を含む方法。 A method for producing a ceramic member comprising the following steps:
a. Making powdered ceramic starting material available;
b. Making available a mold that predefines the shape of the ceramic member;
c. Introducing a ceramic starting material into the mold;
d. Pre-sintering the ceramic starting material at a temperature between 880 ° C. and 980 ° C .;
e. Removing the ceramic member from the mold;
f. Treating the surface of the ceramic member with a blast material;
g. A method comprising sintering the ceramic member at a temperature higher than the temperature of the pre-sintering. 予備焼結の温度は、９００℃よりも高いことを特徴とする、請求項１に記載の方法。   The method according to claim 1, wherein the temperature of the pre-sintering is higher than 900 ° C. 予備焼結の温度は、９５０℃よりも低いことを特徴とする、請求項１または請求項２に記載の方法。   The method according to claim 1 or 2, characterized in that the pre-sintering temperature is lower than 950 ° C. 表面の一部における焼結後のセラミック部材の粗さＲａは、２．５μｍよりも大きいことを特徴とする、請求項１〜請求項３の１つに記載の方法。 The method according to one of claims 1 to 3, characterized in that the roughness Ra of the sintered ceramic member on a part of the surface is greater than 2.5 m. 粒子サイズがセラミック出発材料の粒子サイズに一致するブラスト材料が、用いられることを特徴とする請求項１〜請求項４の１つに記載の方法。 5. A method according to claim 1, wherein a blasting material is used whose particle size matches that of the ceramic starting material. セラミック出発材料と一致する材料が、ブラスト材料として用いられることを特徴とする、請求項１〜請求項５の１つに記載の方法。 6. The method according to claim 1, wherein a material that matches the ceramic starting material is used as a blasting material. チタン合金でできたコーティングが、セラミック部材の表面に適用されることを特徴とする、請求項１〜請求項６の１つに記載の方法。   7. A method according to claim 1, wherein a coating made of a titanium alloy is applied to the surface of the ceramic member. セラミック部材の表面全体が、ブラスト材料で処理されることを特徴とする、請求項１〜請求項７の１つに記載の方法。   8. A method according to one of the preceding claims, characterized in that the entire surface of the ceramic member is treated with a blast material. セラミック部材の表面の一部は、ブラスト材料による処理から除外されたままであることを特徴とする、請求項１〜請求項７の１つに記載の方法。   A method according to one of the preceding claims, characterized in that a part of the surface of the ceramic member remains excluded from the treatment with the blast material.
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