TWI746807B - Copper/ceramic bonded body, insulating circuit substrate, method of manufacturing copper/ceramic bonded body and method of manufacturing insulating circuit substrate - Google Patents
Copper/ceramic bonded body, insulating circuit substrate, method of manufacturing copper/ceramic bonded body and method of manufacturing insulating circuit substrate Download PDFInfo
- Publication number
- TWI746807B TWI746807B TW107106520A TW107106520A TWI746807B TW I746807 B TWI746807 B TW I746807B TW 107106520 A TW107106520 A TW 107106520A TW 107106520 A TW107106520 A TW 107106520A TW I746807 B TWI746807 B TW I746807B
- Authority
- TW
- Taiwan
- Prior art keywords
- copper
- active metal
- ceramic
- ceramic substrate
- layer
- Prior art date
Links
Images
Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L21/00—Processes or apparatus adapted for the manufacture or treatment of semiconductor or solid state devices or of parts thereof
- H01L21/02—Manufacture or treatment of semiconductor devices or of parts thereof
- H01L21/04—Manufacture or treatment of semiconductor devices or of parts thereof the devices having at least one potential-jump barrier or surface barrier, e.g. PN junction, depletion layer or carrier concentration layer
- H01L21/48—Manufacture or treatment of parts, e.g. containers, prior to assembly of the devices, using processes not provided for in a single one of the subgroups H01L21/06 - H01L21/326
- H01L21/4814—Conductive parts
- H01L21/4871—Bases, plates or heatsinks
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L23/00—Details of semiconductor or other solid state devices
- H01L23/48—Arrangements for conducting electric current to or from the solid state body in operation, e.g. leads, terminal arrangements ; Selection of materials therefor
- H01L23/488—Arrangements for conducting electric current to or from the solid state body in operation, e.g. leads, terminal arrangements ; Selection of materials therefor consisting of soldered or bonded constructions
- H01L23/498—Leads, i.e. metallisations or lead-frames on insulating substrates, e.g. chip carriers
- H01L23/49822—Multilayer substrates
-
- 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
- C04B37/00—Joining burned ceramic articles with other burned ceramic articles or other articles by heating
- C04B37/02—Joining burned ceramic articles with other burned ceramic articles or other articles by heating with metallic articles
- C04B37/023—Joining burned ceramic articles with other burned ceramic articles or other articles by heating with metallic articles characterised by the interlayer used
-
- 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
- C04B37/00—Joining burned ceramic articles with other burned ceramic articles or other articles by heating
- C04B37/02—Joining burned ceramic articles with other burned ceramic articles or other articles by heating with metallic articles
- C04B37/023—Joining burned ceramic articles with other burned ceramic articles or other articles by heating with metallic articles characterised by the interlayer used
- C04B37/025—Joining burned ceramic articles with other burned ceramic articles or other articles by heating with metallic articles characterised by the interlayer used consisting of glass or ceramic material
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L21/00—Processes or apparatus adapted for the manufacture or treatment of semiconductor or solid state devices or of parts thereof
- H01L21/02—Manufacture or treatment of semiconductor devices or of parts thereof
- H01L21/04—Manufacture or treatment of semiconductor devices or of parts thereof the devices having at least one potential-jump barrier or surface barrier, e.g. PN junction, depletion layer or carrier concentration layer
- H01L21/48—Manufacture or treatment of parts, e.g. containers, prior to assembly of the devices, using processes not provided for in a single one of the subgroups H01L21/06 - H01L21/326
- H01L21/4814—Conductive parts
- H01L21/4846—Leads on or in insulating or insulated substrates, e.g. metallisation
- H01L21/4857—Multilayer substrates
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L23/00—Details of semiconductor or other solid state devices
- H01L23/12—Mountings, e.g. non-detachable insulating substrates
- H01L23/14—Mountings, e.g. non-detachable insulating substrates characterised by the material or its electrical properties
- H01L23/15—Ceramic or glass substrates
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L23/00—Details of semiconductor or other solid state devices
- H01L23/48—Arrangements for conducting electric current to or from the solid state body in operation, e.g. leads, terminal arrangements ; Selection of materials therefor
- H01L23/488—Arrangements for conducting electric current to or from the solid state body in operation, e.g. leads, terminal arrangements ; Selection of materials therefor consisting of soldered or bonded constructions
- H01L23/498—Leads, i.e. metallisations or lead-frames on insulating substrates, e.g. chip carriers
- H01L23/49866—Leads, i.e. metallisations or lead-frames on insulating substrates, e.g. chip carriers characterised by the materials
-
- H—ELECTRICITY
- H05—ELECTRIC TECHNIQUES NOT OTHERWISE PROVIDED FOR
- H05K—PRINTED CIRCUITS; CASINGS OR CONSTRUCTIONAL DETAILS OF ELECTRIC APPARATUS; MANUFACTURE OF ASSEMBLAGES OF ELECTRICAL COMPONENTS
- H05K3/00—Apparatus or processes for manufacturing printed circuits
- H05K3/38—Improvement of the adhesion between the insulating substrate and the metal
-
- 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
- C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
- C04B2237/02—Aspects relating to interlayers, e.g. used to join ceramic articles with other articles by heating
- C04B2237/04—Ceramic interlayers
- C04B2237/08—Non-oxidic interlayers
-
- 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
- C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
- C04B2237/02—Aspects relating to interlayers, e.g. used to join ceramic articles with other articles by heating
- C04B2237/12—Metallic interlayers
-
- 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
- C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
- C04B2237/02—Aspects relating to interlayers, e.g. used to join ceramic articles with other articles by heating
- C04B2237/12—Metallic interlayers
- C04B2237/126—Metallic interlayers wherein the active component for bonding is not the largest fraction of the interlayer
- C04B2237/127—The active component for bonding being a refractory metal
-
- 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
- C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
- C04B2237/30—Composition of layers of ceramic laminates or of ceramic or metallic articles to be joined by heating, e.g. Si substrates
- C04B2237/32—Ceramic
- C04B2237/36—Non-oxidic
- C04B2237/366—Aluminium nitride
-
- 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
- C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
- C04B2237/30—Composition of layers of ceramic laminates or of ceramic or metallic articles to be joined by heating, e.g. Si substrates
- C04B2237/32—Ceramic
- C04B2237/36—Non-oxidic
- C04B2237/368—Silicon nitride
-
- 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
- C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
- C04B2237/30—Composition of layers of ceramic laminates or of ceramic or metallic articles to be joined by heating, e.g. Si substrates
- C04B2237/40—Metallic
- C04B2237/407—Copper
-
- 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
- C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
- C04B2237/50—Processing aspects relating to ceramic laminates or to the joining of ceramic articles with other articles by heating
- C04B2237/60—Forming at the joining interface or in the joining layer specific reaction phases or zones, e.g. diffusion of reactive species from the interlayer to the substrate or from a substrate to the joining interface, carbide forming at the joining interface
-
- 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
- C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
- C04B2237/50—Processing aspects relating to ceramic laminates or to the joining of ceramic articles with other articles by heating
- C04B2237/70—Forming laminates or joined articles comprising layers of a specific, unusual thickness
- C04B2237/704—Forming laminates or joined articles comprising layers of a specific, unusual thickness of one or more of the ceramic layers or articles
-
- 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
- C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
- C04B2237/50—Processing aspects relating to ceramic laminates or to the joining of ceramic articles with other articles by heating
- C04B2237/72—Forming laminates or joined articles comprising at least two interlayers directly next to each other
-
- 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
- C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
- C04B2237/50—Processing aspects relating to ceramic laminates or to the joining of ceramic articles with other articles by heating
- C04B2237/86—Joining of two substrates at their largest surfaces, one surface being complete joined and covered, the other surface not, e.g. a small plate joined at it's largest surface on top of a larger plate
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L21/00—Processes or apparatus adapted for the manufacture or treatment of semiconductor or solid state devices or of parts thereof
- H01L21/02—Manufacture or treatment of semiconductor devices or of parts thereof
- H01L21/04—Manufacture or treatment of semiconductor devices or of parts thereof the devices having at least one potential-jump barrier or surface barrier, e.g. PN junction, depletion layer or carrier concentration layer
- H01L21/48—Manufacture or treatment of parts, e.g. containers, prior to assembly of the devices, using processes not provided for in a single one of the subgroups H01L21/06 - H01L21/326
- H01L21/4814—Conductive parts
- H01L21/4871—Bases, plates or heatsinks
- H01L21/4882—Assembly of heatsink parts
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L2224/00—Indexing scheme for arrangements for connecting or disconnecting semiconductor or solid-state bodies and methods related thereto as covered by H01L24/00
- H01L2224/01—Means for bonding being attached to, or being formed on, the surface to be connected, e.g. chip-to-package, die-attach, "first-level" interconnects; Manufacturing methods related thereto
- H01L2224/26—Layer connectors, e.g. plate connectors, solder or adhesive layers; Manufacturing methods related thereto
- H01L2224/31—Structure, shape, material or disposition of the layer connectors after the connecting process
- H01L2224/32—Structure, shape, material or disposition of the layer connectors after the connecting process of an individual layer connector
- H01L2224/321—Disposition
- H01L2224/32151—Disposition the layer connector connecting between a semiconductor or solid-state body and an item not being a semiconductor or solid-state body, e.g. chip-to-substrate, chip-to-passive
- H01L2224/32221—Disposition the layer connector connecting between a semiconductor or solid-state body and an item not being a semiconductor or solid-state body, e.g. chip-to-substrate, chip-to-passive the body and the item being stacked
- H01L2224/32225—Disposition the layer connector connecting between a semiconductor or solid-state body and an item not being a semiconductor or solid-state body, e.g. chip-to-substrate, chip-to-passive the body and the item being stacked the item being non-metallic, e.g. insulating substrate with or without metallisation
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L2224/00—Indexing scheme for arrangements for connecting or disconnecting semiconductor or solid-state bodies and methods related thereto as covered by H01L24/00
- H01L2224/80—Methods for connecting semiconductor or other solid state bodies using means for bonding being attached to, or being formed on, the surface to be connected
- H01L2224/83—Methods for connecting semiconductor or other solid state bodies using means for bonding being attached to, or being formed on, the surface to be connected using a layer connector
- H01L2224/838—Bonding techniques
- H01L2224/83801—Soldering or alloying
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L23/00—Details of semiconductor or other solid state devices
- H01L23/34—Arrangements for cooling, heating, ventilating or temperature compensation ; Temperature sensing arrangements
- H01L23/36—Selection of materials, or shaping, to facilitate cooling or heating, e.g. heatsinks
- H01L23/367—Cooling facilitated by shape of device
- H01L23/3675—Cooling facilitated by shape of device characterised by the shape of the housing
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L23/00—Details of semiconductor or other solid state devices
- H01L23/34—Arrangements for cooling, heating, ventilating or temperature compensation ; Temperature sensing arrangements
- H01L23/36—Selection of materials, or shaping, to facilitate cooling or heating, e.g. heatsinks
- H01L23/373—Cooling facilitated by selection of materials for the device or materials for thermal expansion adaptation, e.g. carbon
- H01L23/3735—Laminates or multilayers, e.g. direct bond copper ceramic substrates
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L24/00—Arrangements for connecting or disconnecting semiconductor or solid-state bodies; Methods or apparatus related thereto
- H01L24/01—Means for bonding being attached to, or being formed on, the surface to be connected, e.g. chip-to-package, die-attach, "first-level" interconnects; Manufacturing methods related thereto
- H01L24/26—Layer connectors, e.g. plate connectors, solder or adhesive layers; Manufacturing methods related thereto
- H01L24/31—Structure, shape, material or disposition of the layer connectors after the connecting process
- H01L24/32—Structure, shape, material or disposition of the layer connectors after the connecting process of an individual layer connector
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L24/00—Arrangements for connecting or disconnecting semiconductor or solid-state bodies; Methods or apparatus related thereto
- H01L24/80—Methods for connecting semiconductor or other solid state bodies using means for bonding being attached to, or being formed on, the surface to be connected
- H01L24/83—Methods for connecting semiconductor or other solid state bodies using means for bonding being attached to, or being formed on, the surface to be connected using a layer connector
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12535—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.] with additional, spatially distinct nonmetal component
- Y10T428/12576—Boride, carbide or nitride component
Abstract
Description
本發明有關由銅或銅合金所成之銅構件與由氮化鋁或氮化矽所成之陶瓷構件被接合而構成之銅/陶瓷接合體,絕緣電路基板,及銅/陶瓷接合體的製造方法,絕緣電路基板的製造方法。 本申請案基於2017年2月28日於日本申請之特願2017-036841號、及2018年1月25日於日本申請之特願2018-010964號而主張優先權,將其內容援用於此。The present invention relates to the manufacture of copper/ceramic joints, insulated circuit substrates, and copper/ceramic joints formed by joining a copper component made of copper or copper alloy and a ceramic component made of aluminum nitride or silicon nitride. Method, manufacturing method of insulated circuit board. This application claims priority based on Japanese Patent Application No. 2017-036841 filed on February 28, 2017 in Japan, and Japanese Patent Application No. 2018-010964 filed on January 25, 2018, and the content is used here.
功率模組、LED模組及熱電模組中,具備下述構造,即,於在絕緣層的一方的面形成有由導電材料所成之電路層的絕緣電路基板,接合著功率半導體元件、LED元件及熱電元件。 例如,為了控制風力發電、電動車、混合動力汽車等而使用之大電力控制用的功率半導體元件,動作時的發熱量多。因此,作為搭載功率半導體元件之基板,以往便廣泛使用一種絕緣電路基板,其具備了例如由氮化鋁或氮化矽等所成之陶瓷基板、及在此陶瓷基板的一方的面接合導電性優良的金屬板而形成之電路層。作為絕緣電路基板,也有人提供一種在陶瓷基板的另一方的面接合金屬板來形成金屬層之物。Power modules, LED modules, and thermoelectric modules have a structure in which a circuit layer made of a conductive material is formed on an insulating circuit board on one surface of an insulating layer, and power semiconductor elements and LEDs are bonded to each other. Components and thermoelectric components. For example, power semiconductor elements for large power control used to control wind power generation, electric vehicles, hybrid vehicles, etc., generate a lot of heat during operation. Therefore, as a substrate on which power semiconductor elements are mounted, an insulated circuit substrate has been widely used in the past. It has, for example, a ceramic substrate made of aluminum nitride or silicon nitride, and a conductive surface is bonded to one side of the ceramic substrate. A circuit layer formed from a good metal plate. As an insulated circuit board, some people also provide a metal layer formed by bonding a metal plate to the other side of the ceramic substrate.
例如,專利文獻1中,提出一種將構成電路層及金屬層之第一金屬板及第二金屬板訂為銅板,而將此銅板藉由DBC法(Direct Bonded Copper;直接覆銅法)直接接合至陶瓷基板而成之絕緣電路基板。此DBC法中,利用銅與銅氧化物之共晶反應,令液相發生於銅板與陶瓷基板之界面,藉此將銅板與陶瓷基板接合。For example, in Patent Document 1, it is proposed that the first metal plate and the second metal plate constituting the circuit layer and the metal layer are ordered as copper plates, and the copper plates are directly bonded by the DBC method (Direct Bonded Copper; direct copper clad method) To the insulated circuit substrate made of ceramic substrate. In this DBC method, the eutectic reaction of copper and copper oxide is used to cause the liquid phase to occur at the interface between the copper plate and the ceramic substrate, thereby joining the copper plate and the ceramic substrate.
專利文獻2中,提出一種在陶瓷基板的一方的面及另一方的面將銅板接合,藉此形成電路層及金屬層之絕緣電路基板。此絕緣電路基板中,令Ag-Cu-Ti系硬銲材介於陶瓷基板的一方的面及另一方的面而配置銅板,進行加熱處理,藉此讓銅板被接合(即所謂活性金屬硬銲法)。此活性金屬硬銲法中,使用含有活性金屬亦即Ti之硬銲材,因此熔融的硬銲材與陶瓷基板之潤濕性會提升,陶瓷基板與銅板會被良好地接合。
專利文獻3中,提出一種含有由Cu-Mg-Ti合金所成之粉末的膏,作為於高溫的氮氣環境下將銅板與陶瓷基板接合時所使用之接合用硬銲材。此專利文獻3中,具備藉由於氮氣環境下以560~800℃加熱而接合之構成,Cu-Mg-Ti合金中的Mg會昇華而不會殘存於接合界面,且實質上不會形成氮化鈦(TiN)。 [先前技術文獻] [專利文獻]
[專利文獻1] 日本特開平04-162756號公報 [專利文獻2] 日本特許第3211856號公報 [專利文獻3] 日本特許第4375730號公報[Patent Document 1] Japanese Patent Laid-Open No. 04-162756 [Patent Document 2] Japanese Patent No. 3211856 [Patent Document 3] Japanese Patent No. 4375730
[發明所欲解決之問題][The problem to be solved by the invention]
然而,如專利文獻1所揭示般,當藉由DBC法將陶瓷基板與銅板接合的情形下,必須將接合溫度訂為1065℃以上(銅與銅氧化物之共晶點溫度以上),因此接合時陶瓷基板有劣化之虞。However, as disclosed in Patent Document 1, in the case of joining a ceramic substrate and a copper plate by the DBC method, the joining temperature must be set to 1065°C or higher (the eutectic point temperature of copper and copper oxide or higher). There is a risk of deterioration of the ceramic substrate.
如專利文獻2所揭示般,當藉由活性金屬硬銲法將陶瓷基板與銅板接合的情形下,由於硬銲材含有Ag,Ag會存在於接合界面,因此容易發生遷移(migration),而無法使用於高耐壓用途。此外,接合溫度被訂為900℃這一相對高溫,因此仍舊有陶瓷基板劣化的問題。As disclosed in
如專利文獻3所揭示般,當使用由含有Cu-Mg-Ti合金所成之粉末的膏所成之接合用硬銲材而於氮氣環境下接合的情形下,氣體會殘存於接合界面,而有容易發生部分放電的問題。此外,由於使用合金粉,因應合金粉的組成不均,熔融狀況會變得不均一,而有局部性地形成界面反應不充分的區域之虞。此外,膏中含有的有機物會殘存於接合界面,而有接合變得不充分之虞。As disclosed in
本發明係有鑑於前述事態而研發,目的在於提供一種銅構件與陶瓷構件確實地被接合,而耐遷移性優良之銅/陶瓷接合體,絕緣電路基板,及上述的銅/陶瓷接合體的製造方法,絕緣電路基板的製造方法。 [解決問題之技術手段]The present invention was developed in view of the foregoing situation, and aims to provide a copper/ceramic joint body, an insulated circuit board, and the above-mentioned copper/ceramic joint body, which are reliably joined to a copper member and a ceramic member and have excellent migration resistance Method, manufacturing method of insulated circuit board. [Technical means to solve the problem]
為解決這樣的問題,達成前述目的,本發明的一個態樣之銅/陶瓷接合體,係由銅或銅合金所成之銅構件、與由氮化鋁或氮化矽所成之陶瓷構件被接合而構成之銅/陶瓷接合體,其特徵為,在前述銅構件與前述陶瓷構件之間,於前述陶瓷構件側,形成有含有從Ti,Zr,Nb,Hf選擇之1種或2種以上的活性金屬的氮化物之活性金屬氮化物層,在此活性金屬氮化物層與前述銅構件之間形成有Mg固溶於Cu的母相中而成之Mg固溶層,前述Mg固溶層中,存在前述活性金屬。In order to solve this problem and achieve the aforementioned object, one aspect of the copper/ceramic joint of the present invention is a copper member made of copper or copper alloy, and a ceramic member made of aluminum nitride or silicon nitride is combined The copper/ceramic joined body formed by bonding is characterized in that between the copper member and the ceramic member, on the ceramic member side, one or more selected from Ti, Zr, Nb, and Hf is formed An active metal nitride layer of active metal nitride, between the active metal nitride layer and the aforementioned copper member, a Mg solid solution layer formed by solid dissolving Mg in the mother phase of Cu is formed, the aforementioned Mg solid solution layer Among them, the aforementioned active metals are present.
此構成之銅/陶瓷接合體中,在由銅或銅合金所成之銅構件、與由氮化鋁或氮化矽所成之陶瓷構件之間,於前述陶瓷構件側,形成有含有從Ti,Zr,Nb,Hf選擇之1種或2種以上的活性金屬的氮化物之活性金屬氮化物層。此活性金屬氮化物層,是藉由配設於陶瓷構件與銅構件之間的活性金屬和陶瓷構件中的氮反應而形成之物,陶瓷構件會充分地反應。 在活性金屬氮化物層與前述銅構件之間,形成有Mg固溶於Cu的母相中而成之Mg固溶層,此Mg固溶層中存在前述活性金屬,故配設於陶瓷構件與銅構件之間的Mg會朝銅構件側充分地擴散,又,Cu和活性金屬會充分地反應。 是故,在銅構件與陶瓷構件之接合界面,界面反應會充分地進行,能夠獲得銅構件與陶瓷構件確實地被接合而成之銅/陶瓷接合體。此外,接合界面中不存在Ag,故耐遷移性亦優良。In the copper/ceramic joint body of this structure, between the copper member made of copper or copper alloy and the ceramic member made of aluminum nitride or silicon nitride, on the side of the ceramic member, there is formed a layer containing Ti , Zr, Nb, Hf selected one or two or more active metal nitride active metal nitride layer. The active metal nitride layer is formed by reacting the active metal disposed between the ceramic member and the copper member and the nitrogen in the ceramic member, and the ceramic member will fully react. Between the active metal nitride layer and the copper member, a Mg solid solution layer in which Mg is solid-dissolved in the mother phase of Cu is formed. The active metal is present in the Mg solid solution layer, so it is arranged on the ceramic member and The Mg between the copper members diffuses sufficiently toward the copper member side, and Cu and the active metal fully react. Therefore, at the bonding interface between the copper member and the ceramic member, the interfacial reaction proceeds sufficiently, and a copper/ceramic joint body in which the copper member and the ceramic member are reliably joined can be obtained. In addition, there is no Ag in the bonding interface, so migration resistance is also excellent.
本發明的一個態樣之銅/陶瓷接合體中,亦可構成為,前述Mg固溶層中,分散有含有Cu與前述活性金屬之金屬間化合物相。 Mg固溶層中的活性金屬,當含有Ti,Zr,Hf作為活性金屬的情形下,會以Cu與前述活性金屬之金屬間化合物相的方式存在。因此,Mg固溶層中存在Cu與前述活性金屬之金屬間化合物相,藉此,配設於陶瓷構件與銅構件之間的Mg會朝銅構件側充分地擴散,Cu和活性金屬會充分地反應,能夠獲得銅構件與陶瓷構件確實地被接合而成之銅/陶瓷接合體。In the copper/ceramic joint of one aspect of the present invention, it may be configured that an intermetallic compound phase containing Cu and the active metal is dispersed in the Mg solid solution layer. When the active metal in the Mg solid solution layer contains Ti, Zr, and Hf as the active metal, it will exist as an intermetallic compound phase between Cu and the aforementioned active metal. Therefore, there is an intermetallic compound phase between Cu and the aforementioned active metal in the Mg solid solution layer, whereby the Mg arranged between the ceramic member and the copper member will diffuse to the copper member side sufficiently, and Cu and the active metal will fully diffuse By reaction, a copper/ceramic joined body in which a copper member and a ceramic member are joined reliably can be obtained.
本發明的一個態樣之銅/陶瓷接合體中,較佳是,在前述活性金屬氮化物層的內部,分散有Cu粒子。 在此情形下,銅構件的Cu會和陶瓷構件充分地反應,可獲得銅構件與陶瓷構件強固地被接合而成之銅/陶瓷接合體。Cu粒子,為Cu單體或含有Cu之金屬間化合物,於形成活性金屬氮化物層時,藉由存在於液相中的Cu析出而生成。In the copper/ceramic joined body of one aspect of the present invention, it is preferable that Cu particles are dispersed in the active metal nitride layer. In this case, the Cu of the copper member will react with the ceramic member sufficiently, and a copper/ceramic joint body in which the copper member and the ceramic member are strongly joined can be obtained. Cu particles are Cu alone or intermetallic compounds containing Cu, and are generated by precipitation of Cu existing in the liquid phase when forming the active metal nitride layer.
本發明的一個態樣之銅/陶瓷接合體中,前述活性金屬亦可為Ti。 在此情形下,會形成氮化鈦層作為前述活性金屬氮化物層,前述Mg固溶層中,會分散有含有Cu與Ti之金屬間化合物相,能夠提供一種銅構件與陶瓷構件確實地被接合,而耐遷移性優良之銅/陶瓷接合體。In the copper/ceramic joint body of one aspect of the present invention, the aforementioned active metal may also be Ti. In this case, a titanium nitride layer will be formed as the active metal nitride layer, and the Mg solid solution layer will be dispersed with an intermetallic compound phase containing Cu and Ti, which can provide a copper component and a ceramic component that are reliably combined Bonded copper/ceramic bonded body with excellent migration resistance.
本發明的一個態樣之銅/陶瓷接合體中,較佳是,在前述陶瓷構件與前述銅構件之間,前述陶瓷構件的接合面起算往前述銅構件側50μm為止之區域中的Cu2 Mg相的面積率為15%以下。 在此情形下,脆弱的Cu2 Mg相的面積率會被限制在15%以下,故例如即使實施了超音波接合等的情形下,仍可抑制接合界面中的破裂等的發生。In the copper/ceramic joint body of one aspect of the present invention, it is preferable that between the ceramic member and the copper member, the joint surface of the ceramic member is Cu 2 Mg in a region up to 50 μm from the copper member side The area ratio of the phase is 15% or less. In this case, the area ratio of the fragile Cu 2 Mg phase is limited to 15% or less. Therefore, even when ultrasonic bonding is performed, for example, the occurrence of cracks in the bonding interface can be suppressed.
本發明的一個態樣之絕緣電路基板,係由銅或銅合金所成之銅板被接合至由氮化鋁或氮化矽所成之陶瓷基板的表面而構成之絕緣電路基板,其特徵為,在前述銅板與前述陶瓷基板之間,於前述陶瓷基板側,形成有含有從Ti,Zr,Nb,Hf選擇之1種或2種以上的活性金屬的氮化物之活性金屬氮化物層,在此活性金屬氮化物層與前述銅板之間形成有Mg固溶於Cu的母相中而成之Mg固溶層,前述Mg固溶層中,存在前述活性金屬。 此構成之絕緣電路基板中,銅板與陶瓷基板會確實地被接合,並且耐遷移性優良,於高耐壓條件下仍能高可靠性性使用。One aspect of the insulated circuit substrate of the present invention is an insulated circuit substrate formed by bonding a copper plate made of copper or copper alloy to the surface of a ceramic substrate made of aluminum nitride or silicon nitride, and is characterized in that: Between the copper plate and the ceramic substrate, on the ceramic substrate side, an active metal nitride layer containing nitrides of one or more active metals selected from Ti, Zr, Nb, and Hf is formed, where A Mg solid solution layer in which Mg is solid-dissolved in a Cu matrix is formed between the active metal nitride layer and the copper plate, and the active metal is present in the Mg solid solution layer. In the insulated circuit substrate of this structure, the copper plate and the ceramic substrate are surely joined, and the resistance to migration is excellent, and it can be used with high reliability under high withstand voltage conditions.
本發明的一個態樣之絕緣電路基板中,亦可構成為,前述Mg固溶層中,分散有含有Cu與前述活性金屬之金屬間化合物相。 Mg固溶層中的活性金屬,當含有Ti,Zr,Hf作為活性金屬的情形下,會以Cu與前述活性金屬之金屬間化合物相的方式存在。因此,Mg固溶層中以Cu與前述活性金屬之金屬間化合物相的方式存在,藉此,能夠獲得銅板與陶瓷基板確實地被接合而成之絕緣電路基板。In the insulated circuit board of one aspect of the present invention, it may be configured that an intermetallic compound phase containing Cu and the active metal is dispersed in the Mg solid solution layer. When the active metal in the Mg solid solution layer contains Ti, Zr, and Hf as the active metal, it will exist as an intermetallic compound phase between Cu and the aforementioned active metal. Therefore, the Mg solid solution layer exists as an intermetallic compound phase of Cu and the aforementioned active metal, and thereby, an insulated circuit board in which a copper plate and a ceramic substrate are reliably joined can be obtained.
本發明的一個態樣之絕緣電路基板中,較佳是,在前述活性金屬氮化物層的內部,分散有Cu粒子。 在此情形下,銅板的Cu會和陶瓷基板充分地反應,可獲得銅板與陶瓷基板強固地被接合而成之絕緣電路基板。Cu粒子,為Cu單體或含有Cu之金屬間化合物,於形成活性金屬氮化物層時,藉由存在於液相中的Cu析出而生成。In the insulated circuit board of one aspect of the present invention, it is preferable that Cu particles are dispersed in the active metal nitride layer. In this case, the Cu of the copper plate reacts sufficiently with the ceramic substrate, and an insulated circuit substrate in which the copper plate and the ceramic substrate are strongly joined can be obtained. Cu particles are Cu alone or intermetallic compounds containing Cu, and are generated by precipitation of Cu existing in the liquid phase when forming the active metal nitride layer.
本發明的一個態樣之絕緣電路基板中,前述活性金屬亦可為Ti。 在此情形下,會形成氮化鈦層作為前述活性金屬氮化物層,前述Mg固溶層中,會分散有含有Cu與Ti之金屬間化合物相,能夠提供一種銅板與陶瓷基板確實地被接合,而耐遷移性優良之絕緣電路基板。In the insulated circuit substrate of one aspect of the present invention, the aforementioned active metal may also be Ti. In this case, a titanium nitride layer will be formed as the active metal nitride layer, and the Mg solid solution layer will be dispersed with an intermetallic compound phase containing Cu and Ti, which can provide a copper plate and a ceramic substrate that can be reliably joined , And an insulated circuit board with excellent migration resistance.
本發明的一個態樣之絕緣電路基板中,較佳是,在前述陶瓷基板與前述銅板之間,前述陶瓷基板的接合面起算往前述銅板側50μm為止之區域中的Cu2 Mg相的面積率為15%以下。 在此情形下,脆弱的Cu2 Mg相的面積率會被限制在15%以下,故例如即使實施了超音波接合等的情形下,仍可抑制接合界面中的破裂等的發生。In the insulated circuit board of one aspect of the present invention, it is preferable that the area ratio of the Cu 2 Mg phase in a region 50 μm from the side of the copper plate between the ceramic substrate and the copper plate and the bonding surface of the ceramic substrate is calculated Less than 15%. In this case, the area ratio of the fragile Cu 2 Mg phase is limited to 15% or less. Therefore, even when ultrasonic bonding is performed, for example, the occurrence of cracks in the bonding interface can be suppressed.
本發明的一個態樣之銅/陶瓷接合體的製造方法,係製造上述之銅/陶瓷接合體的方法,其特徵為,具備:活性金屬及Mg配置工程,在前述銅構件與前述陶瓷構件之間,配置從Ti,Zr,Nb,Hf選擇之1種或2種以上的活性金屬的單體及Mg單體;及層積工程,將前述銅構件與前述陶瓷構件,介著活性金屬及Mg予以層積;及接合工程,將介著活性金屬及Mg而被層積之前述銅構件與前述陶瓷構件,在朝層積方向予以加壓之狀態下,於真空環境下做加熱處理而接合;前述活性金屬及Mg配置工程中,將活性金屬量訂為0.4μmol/cm2 以上47.0μmol/cm2 以下的範圍內,將Mg量訂為7.0μmol/cm2 以上143.2μmol/cm2 以下的範圍內。A method of manufacturing a copper/ceramic joint body according to one aspect of the present invention is a method of manufacturing the above-mentioned copper/ceramic joint body, and is characterized in that it comprises an active metal and Mg arrangement process, and the copper member and the ceramic member are arranged between the copper member and the ceramic member In between, one or more active metal monomers and Mg monomers selected from Ti, Zr, Nb, and Hf are arranged; and the lamination process is to interpose the aforementioned copper member and the aforementioned ceramic member with the active metal and Mg Laminating; and the joining process, the above-mentioned copper member and the above-mentioned ceramic member, which are laminated via active metal and Mg, are heated in a vacuum environment under pressure in the lamination direction to join; Mg and configure the active metal works, the active metal content is set at 2 or less in the range of 0.4μmol / cm 2 or more 47.0μmol / cm, the Mg content is set at 2 or less 143.2μmol / cm 2 or more 7.0μmol / cm Inside.
按照此構成之銅/陶瓷接合體的製造方法,是在前述銅構件與前述陶瓷構件之間配置活性金屬的單體及Mg單體,在將它們朝層積方向予以加壓的狀態下,於真空環境下做加熱處理,故在接合界面不會殘存氣體或有機物的殘渣等。此外,由於配置活性金屬的單體及Mg單體,故沒有組成的不均,會均一地發生液相。 活性金屬及Mg配置工程中,是將活性金屬量訂為0.4μmol/cm2 以上47.0μmol/cm2 以下的範圍內,將Mg量訂為7.0μmol/cm2 以上143.2μmol/cm2 以下的範圍內,故能夠充分地獲得界面反應所必要之液相,並且能夠抑制陶瓷構件的必要以上的反應。 故,能夠獲得銅構件與陶瓷構件確實地被接合而成之銅/陶瓷接合體。此外,接合不使用Ag,故能夠獲得耐遷移性優良的銅/陶瓷接合體。According to the method of manufacturing the copper/ceramic joint body with this structure, the active metal monomer and Mg monomer are arranged between the copper member and the ceramic member, and they are pressed in the stacking direction. Heat treatment is performed in a vacuum environment, so no gas or organic residues will remain at the joint interface. In addition, since the active metal monomer and Mg monomer are arranged, there is no unevenness in composition, and a liquid phase is uniformly generated. Active metals and engineering Mg configuration, the amount of active metal is set within a range of 2 or less 0.4μmol / cm 2 or more 47.0μmol / cm, the Mg content is set at 2 or less 143.2μmol / cm 2 or more 7.0μmol / cm Therefore, it is possible to sufficiently obtain the liquid phase necessary for the interface reaction, and it is possible to suppress more than necessary reactions of the ceramic member. Therefore, a copper/ceramic joined body in which a copper member and a ceramic member are reliably joined can be obtained. In addition, since Ag is not used for bonding, a copper/ceramic bonded body with excellent migration resistance can be obtained.
本發明的一個態樣之銅/陶瓷接合體的製造方法中,較佳是,前述接合工程中的加壓荷重被訂為0.049MPa以上3.4MPa以下的範圍內,前述接合工程中的加熱溫度,當Cu與Mg是在接觸狀態下被層積的情形下訂為500℃以上850℃以下的範圍內,當Cu與Mg是在非接觸狀態下被層積的情形下訂為670℃以上850℃以下的範圍內。In the method of manufacturing a copper/ceramic joined body according to one aspect of the present invention, it is preferable that the pressing load in the joining process is set within a range of 0.049 MPa or more and 3.4 MPa or less, and the heating temperature in the joining process is When Cu and Mg are laminated in the contact state, it is set to be in the range of 500°C to 850°C, and when Cu and Mg are laminated in the non-contact state, it is set to be 670°C to 850°C Within the following range.
在此情形下,前述接合工程中的加壓荷重是被訂為0.049MPa以上3.4MPa以下的範圍內,故能夠使陶瓷構件與銅構件與活性金屬及Mg密合,於加熱時能夠促進它們的界面反應。 前述接合工程中的加熱溫度,當Cu與Mg是在接觸狀態下被層積的情形下訂為比Cu與Mg的共晶溫度還高之500℃以上,當Cu與Mg是在非接觸狀態下被層積的情形下訂為比Mg的熔點還高之670℃以上,故於接合界面能夠充分地使液相發生。 前述接合工程中的加熱溫度是被訂為850℃以下,故能夠抑制Cu與活性金屬之共晶反應的發生,能夠抑制液相過度地生成。此外,對陶瓷構件之熱負荷會變小,能夠抑制陶瓷構件的劣化。In this case, the pressurizing load in the aforementioned joining process is set within the range of 0.049 MPa to 3.4 MPa, so that the ceramic member and the copper member can be closely adhered to the active metal and Mg, and they can be promoted during heating. Interface reaction. The heating temperature in the aforementioned bonding process, when Cu and Mg are laminated in the contact state, is set to be 500°C higher than the eutectic temperature of Cu and Mg, and when Cu and Mg are in the non-contact state In the case of being laminated, it is set to be 670°C or more higher than the melting point of Mg, so that the liquid phase can be sufficiently generated at the joint interface. "The heating temperature in the aforementioned joining process is set at 850°C or lower, so the occurrence of the eutectic reaction between Cu and the active metal can be suppressed, and the excessive generation of the liquid phase can be suppressed. In addition, the thermal load on the ceramic member is reduced, and the deterioration of the ceramic member can be suppressed.
本發明的一個態樣之絕緣電路基板的製造方法,係製造由銅或銅合金所成之銅板被接合至由氮化鋁或氮化矽所成之陶瓷基板的表面而構成之絕緣電路基板的絕緣電路基板的製造方法,其特徵為,具備:活性金屬及Mg配置工程,在前述銅板與前述陶瓷基板之間,配置從Ti,Zr,Nb,Hf選擇之1種或2種以上的活性金屬的單體及Mg單體;及層積工程,將前述銅板與前述陶瓷基板,介著活性金屬及Mg予以層積;及接合工程,將介著活性金屬及Mg而被層積之前述銅板與前述陶瓷基板,在朝層積方向予以加壓之狀態下,於真空環境下做加熱處理而接合;前述活性金屬及Mg配置工程中,將活性金屬量訂為0.4μmol/cm2 以上47.0μmol/cm2 以下的範圍內,將Mg量訂為7.0μmol/cm2 以上143.2μmol/cm2 以下的範圍內。 按照此構成之絕緣電路基板的製造方法,能夠獲得銅板與陶瓷基板被確實地接合而成之絕緣電路基板。此外,接合不使用Ag,故能夠獲得耐遷移性優良的絕緣電路基板。An aspect of the method for manufacturing an insulated circuit board of the present invention is to manufacture an insulated circuit board in which a copper plate made of copper or copper alloy is joined to the surface of a ceramic substrate made of aluminum nitride or silicon nitride. The method of manufacturing an insulated circuit board is characterized by: an active metal and Mg arrangement process, and one or more active metals selected from Ti, Zr, Nb, and Hf are arranged between the aforementioned copper plate and the aforementioned ceramic substrate The monomer and Mg monomer; and the lamination process, in which the copper plate and the ceramic substrate are layered via the active metal and Mg; and the bonding process, the copper plate and the copper plate that are layered via the active metal and Mg The aforementioned ceramic substrates are joined by heat treatment in a vacuum environment while they are pressurized in the stacking direction; in the aforementioned active metal and Mg arrangement process, the amount of active metal is set to be 0.4 μmol/cm 2 or more and 47.0 μmol/ In the range of cm 2 or less, the amount of Mg is set to be in the range of 7.0 μmol/cm 2 or more and 143.2 μmol/cm 2 or less. According to the manufacturing method of the insulated circuit board of this structure, the insulated circuit board which the copper plate and the ceramic board were joined reliably can be obtained. In addition, since Ag is not used for bonding, an insulated circuit board excellent in migration resistance can be obtained.
本發明的一個態樣之絕緣電路基板的製造方法中,較佳是,前述接合工程中的加壓荷重被訂為0.049MPa以上3.4MPa以下的範圍內,前述接合工程中的加熱溫度,當Cu與Mg是在接觸狀態下被層積的情形下訂為500℃以上850℃以下的範圍內,當Cu與Mg是在非接觸狀態下被層積的情形下訂為670℃以上850℃以下的範圍內。In the method of manufacturing an insulated circuit board of one aspect of the present invention, it is preferable that the pressurizing load in the bonding process is set within a range of 0.049 MPa to 3.4 MPa, and the heating temperature in the bonding process is set as Cu When it is laminated with Mg in the contact state, it is set to be within the range of 500°C to 850°C. When Cu and Mg are laminated in the non-contact state, it is set to be 670°C to 850°C. Within range.
在此情形下,前述接合工程中的加壓荷重是被訂為0.049MPa以上3.4MPa以下的範圍內,故能夠使陶瓷基板與銅板與活性金屬及Mg密合,於加熱時能夠促進它們的界面反應。 前述接合工程中的加熱溫度,當Cu與Mg是在接觸狀態下被層積的情形下訂為比Cu與Mg的共晶溫度還高之500℃以上,當Cu與Mg是在非接觸狀態下被層積的情形下訂為比Mg的熔點還高之670℃以上,故於接合界面能夠充分地使液相發生。 前述接合工程中的加熱溫度是被訂為850℃以下,故能夠抑制Cu與活性金屬之共晶反應的發生,能夠抑制液相過度地生成。此外,對陶瓷基板之熱負荷會變小,能夠抑制陶瓷基板的劣化。 [發明之功效]In this case, the pressing load in the aforementioned joining process is set within the range of 0.049 MPa or more and 3.4 MPa or less. Therefore, the ceramic substrate and the copper plate can be closely adhered to the active metal and Mg, and the interface between them can be promoted during heating. reaction. The heating temperature in the aforementioned bonding process, when Cu and Mg are laminated in the contact state, is set to be 500°C higher than the eutectic temperature of Cu and Mg, and when Cu and Mg are in the non-contact state In the case of being laminated, it is set to be 670°C or more higher than the melting point of Mg, so that the liquid phase can be sufficiently generated at the joint interface. "The heating temperature in the aforementioned joining process is set at 850°C or lower, so the occurrence of the eutectic reaction between Cu and the active metal can be suppressed, and the excessive generation of the liquid phase can be suppressed. In addition, the thermal load on the ceramic substrate is reduced, and the deterioration of the ceramic substrate can be suppressed. [Effects of Invention]
按照本發明,可提供一種銅構件與陶瓷構件確實地被接合,而耐遷移性優良之銅/陶瓷接合體,絕緣電路基板,及上述的銅/陶瓷接合體的製造方法,絕緣電路基板的製造方法。According to the present invention, it is possible to provide a copper/ceramic joint body, an insulated circuit board, and a method for manufacturing the above-mentioned copper/ceramic joint body, and a manufacturing method of the above-mentioned copper/ceramic joint body, and the production of the insulated circuit board method.
以下參照所附圖面說明本發明之實施形態。Hereinafter, embodiments of the present invention will be described with reference to the drawings.
(第1實施形態) 針對本發明之第1實施形態,參照圖1至圖4說明之。 本實施形態之銅/陶瓷接合體,係被做成藉由陶瓷構件即陶瓷基板11與銅構件即銅板22(電路層12)及銅板23(金屬層13)被接合而構成之絕緣電路基板10。 圖1揭示本發明第1實施形態之絕緣電路基板10及使用了此絕緣電路基板10之功率模組1。(First Embodiment) "The first embodiment of the present invention will be described with reference to Figs. 1 to 4). The copper/ceramic joint body of this embodiment is an
此功率模組1,具備絕緣電路基板10、及在此絕緣電路基板10的一方側(圖1中上側)介著第1銲料層2而被接合之半導體元件3、及在絕緣電路基板10的另一方側(圖1中下側)介著第2銲料層8而被接合之散熱座(heatsink)51。This power module 1 includes an insulated
絕緣電路基板10,具備陶瓷基板11、及配設於此陶瓷基板11的一方的面(圖1中上面)之電路層12、及配設於陶瓷基板11的另一方的面(圖1中下面)之金屬層13。 陶瓷基板11,為防止電路層12與金屬層13之間的電性連接之物,本實施形態中由絕緣性高的氮化鋁來構成。陶瓷基板11的厚度,被設定成0.2~1.5mm的範圍內,本實施形態中被設定成0.635mm。The
電路層12,如圖4所示,是藉由在陶瓷基板11的一方的面接合由銅或銅合金所成之銅板22而形成。本實施形態中,作為構成電路層12的銅板22,使用無氧銅的壓延板。在此電路層12,形成有電路圖樣,其一方的面(圖1中上面),為供半導體元件3搭載之搭載面。電路層12的厚度被設定成0.1mm以上2.0mm以下的範圍內,本實施形態中被設定成0.6mm。The
金屬層13,如圖4所示,是藉由在陶瓷基板11的另一方的面接合由銅或銅合金所成之銅板23而形成。本實施形態中,作為構成金屬層13的銅板23,使用無氧銅的壓延板。金屬層13的厚度被設定成0.1mm以上2.0mm以下的範圍內,本實施形態中被設定成0.6mm。The
散熱座51,為用來將前述的絕緣電路基板10冷卻之物,本實施形態中以由熱傳導性良好的材質所構成之散熱板來構成。本實施形態中,散熱座51以熱傳導性優良的銅或銅合金來構成。散熱座51和絕緣電路基板10的金屬層13,介著第2銲料層8而被接合。The
陶瓷基板11與電路層12(銅板22)、及陶瓷基板11與金屬層13(銅板23),如圖4所示,是介著由從Ti,Zr,Nb,Hf選擇之1種或2種以上的活性金屬所成之活性金屬膜24(本實施形態中為Ti膜)及Mg膜25而被接合。 於陶瓷基板11與電路層12(銅板22)之接合界面及陶瓷基板11與金屬層13(銅板23)之接合界面,如圖2所示,具備形成於陶瓷基板11側之活性金屬氮化物層31(本實施形態中為氮化鈦層)與Mg固溶於Cu的母相中而成之Mg固溶層32所層積之構造。The
Mg固溶層32中,含有上述的活性金屬。本實施形態中,Mg固溶層32中,分散有含有Cu與活性金屬(Ti)之金屬間化合物相33。本實施形態中,作為活性金屬使用Ti,作為構成含有Cu與Ti之金屬間化合物相33的金屬間化合物,例如可舉出Cu4
Ti,Cu3
Ti2
,Cu4
Ti3
,CuTi,CuTi2
,CuTi3
等。 此Mg固溶層32中的Mg的含有量,被訂為0.01原子%以上0.5原子%以下的範圍內。Mg固溶層32的厚度,被訂為0.1μm以上80μm以下的範圍內。Mg固溶層32中的Mg的含有量,較佳是被訂為0.01原子%以上0.3原子%以下的範圍內,但不限定於此。The Mg
本實施形態中,在活性金屬氮化物層31(氮化鈦層)的內部,分散有Cu粒子35。 分散在活性金屬氮化物層31(氮化鈦層)內之Cu粒子35的粒徑,被訂為10nm以上100nm以下的範圍內。此外,活性金屬氮化物層31(氮化鈦層)當中與陶瓷基板11之界面起算至活性金屬氮化物層31(氮化鈦層)的厚度的20%為止之界面鄰近區域中的Cu濃度,被訂為0.3原子%以上15原子%以下的範圍內。 活性金屬氮化物層31(氮化鈦層)的厚度,被訂為0.03μm以上1.2μm以下的範圍內。活性金屬氮化物層31(氮化鈦層)當中與陶瓷基板11之界面起算至活性金屬氮化物層31(氮化鈦層)的厚度的20%為止之界面鄰近區域中的Cu濃度,較佳是被訂為0.3原子%以上12原子%以下的範圍內,但不限定於此。In this embodiment,
本實施形態中,在陶瓷基板11與電路層12之間,陶瓷基板11的接合面起算至往電路層12側50μm為止之區域中的Cu2
Mg相的面積率,被訂為15%以下。陶瓷基板11的接合面起算至往電路層12側50μm為止之區域中的Cu2
Mg相的面積率,較佳是被訂為0.01%以上10%以下,但不限定於此。 本實施形態中,上述的Cu2
Mg相,是訂為以電子探針顯微分析儀取得Mg的元素MAP,於確認有Mg的存在之區域中Mg濃度為30原子%以上40原子%以下之區域。 In the present embodiment, the area ratio of the Cu 2 Mg phase in the area 50 μm from the bonding surface of the
針對上述本實施形態之絕緣電路基板10的製造方法,參照圖3及圖4說明之。The manufacturing method of the insulated
如圖4所示,在作為電路層12之銅板22與陶瓷基板11之間、及作為金屬層13之銅板23與陶瓷基板11之間,各自配置從Ti,Zr,Nb,Hf選擇之1種或2種以上的活性金屬的單體(本實施形態中為Ti單體)及Mg單體(活性金屬及Mg配置工程S01)。本實施形態中,藉由蒸鍍活性金屬(Ti)及Mg,會形成活性金屬膜24(Ti膜)及Mg膜25,Mg膜25和銅板22會在非接觸狀態下被層積。 此活性金屬及Mg配置工程S01中,將活性金屬量訂為0.4μmol/cm2
以上47.0μmol/cm2
以下的範圍內(本實施形態中,將Ti訂為0.02mg/cm2
以上2.25mg/cm2
以下的範圍內),將Mg量訂為7.0μmol/cm2
以上143.2μmol/cm2
以下的範圍內(0.17mg/cm2
以上3.48mg/cm2
以下的範圍內)。 活性金屬量的下限較佳是訂為2.8μmol/cm2
以上,活性金屬量的上限較佳是訂為18.8μmol/cm2
以下。此外,Mg量的下限較佳是訂為8.8μmol/cm2
以上,Mg量的上限較佳是訂為37.0μmol/cm2
以下。As shown in FIG. 4, between the
接著,將銅板22與陶瓷基板11與銅板23,介著活性金屬膜24(Ti膜)及Mg膜25予以層積(層積工程S02)。Next, the
將被層積的銅板22、陶瓷基板11、銅板23朝層積方向加壓,並且裝入真空爐內加熱,將銅板22與陶瓷基板11與銅板23接合(接合工程S03)。 接合工程S03中的加壓荷重,被訂為0.049MPa以上3.4MPa以下的範圍內。接合工程S03中的加壓荷重,較佳是被訂為0.294MPa以上1.47MPa以下的範圍內,但不限定於此。 接合工程S03中的加熱溫度,由於Cu與Mg是在非接觸狀態下被層積,因此被訂為Mg的熔點以上之670℃以上850℃以下的範圍內。加熱溫度的下限較佳是訂為700℃以上。 接合工程S03中的真空度,較佳是訂為1×10-6
Pa以上1×10-2
Pa以下的範圍內。 加熱溫度下的保持時間,較佳是訂為5min以上360min以下的範圍內。為了減低上述的Cu2
Mg相的面積率,較佳是將加熱溫度下的保持時間的下限訂為60min以上。此外,加熱溫度下的保持時間的上限較佳是訂為240min以下。The
像以上這樣,藉由活性金屬及Mg配置工程S01、與層積工程S02、與接合工程S03,製造本實施形態之絕緣電路基板10。As described above, the insulating
在絕緣電路基板10的金屬層13的另一方的面側將散熱座51接合(散熱座接合工程S04)。 將絕緣電路基板10與散熱座51,介著銲料材予以層積而裝入加熱爐,介著第2銲料層8將絕緣電路基板10與散熱座51予以銲接。The
接著,在絕緣電路基板10的電路層12的一方的面,將半導體元件3藉由銲接而接合(半導體元件接合工程S05)。 藉由以上的工程,製造出圖1所示之功率模組1。Next, on one surface of the
按照做成以上這樣的構成之本實施形態之絕緣電路基板10(銅/陶瓷接合體),由無氧銅所成之銅板22(電路層12)及銅板23(金屬層13)與由氮化鋁所成之陶瓷基板11,是介著活性金屬膜24(Ti膜)及Mg膜25而被接合,在陶瓷基板11與電路層12(銅板22)及陶瓷基板11與金屬層13(銅板23)之接合界面,層積有形成於陶瓷基板11側之活性金屬氮化物層31(氮化鈦層)與Mg固溶於Cu的母相中而成之Mg固溶層32。According to the insulated circuit board 10 (copper/ceramic junction) of the present embodiment with the above-mentioned structure, the copper plate 22 (circuit layer 12) and the copper plate 23 (metal layer 13) made of oxygen-free copper are combined with nitride The
活性金屬氮化物層31(氮化鈦層),是藉由配設於陶瓷基板11與銅板22、23之間的活性金屬(Ti)和陶瓷基板11的氮反應而形成。因此,本實施形態中,於接合界面,陶瓷基板11會充分地反應。此外,以層積於活性金屬氮化物層31(氮化鈦層)之方式,形成有Mg固溶於Cu的母相中而成之Mg固溶層32,此Mg固溶層32中含有上述的活性金屬。本實施形態中,Mg固溶層32中分散有含有Cu與活性金屬(Ti)之金屬間化合物相33,故配設於陶瓷基板11與銅板22,23之間的Mg會朝銅板22,23側充分地擴散。因此,本實施形態中,於接合界面,Cu與活性金屬(Ti)會充分地反應。The active metal nitride layer 31 (titanium nitride layer) is formed by reacting the active metal (Ti) disposed between the
故,在陶瓷基板11與銅板22,23之接合界面會充分地進行界面反應,能夠獲得電路層12(銅板22)與陶瓷基板11、金屬層13(銅板23)與陶瓷基板11確實地被接合而成之絕緣電路基板10(銅/陶瓷接合體)。此外,接合界面中沒有Ag存在,故能夠獲得耐遷移性優良的絕緣電路基板10(銅/陶瓷接合體)。Therefore, sufficient interfacial reactions occur at the bonding interface between the
特別是,本實施形態中,在活性金屬氮化物層31(氮化鈦層)的內部分散有Cu粒子35,故銅板22,23的Cu會在陶瓷基板11的接合面充分地反應。因此,可獲得銅板22,23與陶瓷基板11強固地被接合而成之絕緣電路基板10(銅/陶瓷接合體)。In particular, in the present embodiment, the
本實施形態中,在陶瓷基板11與電路層12(銅板22)之間,陶瓷基板11的接合面起算至往電路層12(銅板22)側50μm為止之區域中的Cu2
Mg相的面積率係被限制在15%以下,故即使實施了例如超音波接合等的情形下,仍可抑制接合界面中的破裂等的發生。 In this embodiment, between the ceramic substrate 11 and the circuit layer 12 (copper plate 22), the area ratio of the Cu 2 Mg phase in the area from the bonding surface of the
按照本實施形態之絕緣電路基板10(銅/陶瓷接合體)的製造方法,係具備:在銅板22、23與陶瓷基板11之間配置活性金屬(Ti)的單體(活性金屬膜24)及Mg單體(Mg膜25)之活性金屬及Mg配置工程S01;及介著該些活性金屬膜24及Mg膜25將銅板22、23與陶瓷基板11予以層積之層積工程S02;及將被層積的銅板22、陶瓷基板11、銅板23於朝層積方向加壓的狀態下,於真空環境下予以加熱處理而接合之接合工程S03;故在接合界面不會殘存氣體或有機物的殘渣等。此外,由於配置活性金屬(Ti)的單體及Mg單體,故沒有組成的不均,會均一地發生液相。The manufacturing method of the insulated circuit board 10 (copper/ceramic joint) according to the present embodiment includes: disposing a single active metal (Ti) (active metal film 24) between the
活性金屬及Mg配置工程S01中,將活性金屬量訂為0.4μmol/cm2
以上47.0μmol/cm2
以下的範圍內(本實施形態中,將Ti訂為0.02mg/cm2
以上2.25mg/cm2
以下的範圍內),將Mg量訂為7.0μmol/cm2
以上143.2μmol/cm2
以下的範圍內(0.17mg/cm2
以上3.48mg/cm2
以下的範圍內),故能夠充分獲得界面反應所必要的液相,並且能夠抑制陶瓷基板11的必要以上的反應。 故,能夠獲得銅板22,23與陶瓷基板11確實地被接合而成之絕緣電路基板10(銅/陶瓷接合體)。此外,接合不使用Ag,故能夠獲得耐遷移性優良的絕緣電路基板10。In the active metal and Mg configuration process S01, the amount of active metal is set to be within the range of 0.4 μmol/cm 2 or more and 47.0 μmol/cm 2 or less (in this embodiment, Ti is set to be 0.02 mg/cm 2 or more and 2.25 mg/cm in the range of 2 or less), the Mg content is set in the range of (0.17mg / cm 2 or more 3.48mg / cm 2 or less in the range of 2 or less 143.2μmol / cm 2 or more 7.0μmol / cm), it is possible to obtain sufficiently interface The liquid phase is necessary for the reaction, and more than necessary reaction of the
當活性金屬量未滿0.4μmol/cm2
(Ti量未滿0.02mg/cm2
)、及Mg量未滿7.0μmol/cm2
(未滿0.17mg/cm2
)的情形下,界面反應會變得不充分,接合率恐會低落。此外,當活性金屬量超出47.0μmol/cm2
(Ti量超出2.25mg/cm2
)的情形下,會過度地生成活性金屬多而相對硬的金屬間化合物相33,Mg固溶層32會變得過硬,陶瓷基板11恐會發生破裂。此外,當Mg量超出143.2μmol/cm2
(超出3.48mg/ cm2
)的情形下,陶瓷基板11的分解反應會變得過度,Al會過度地生成,而會大量產生它們和Cu或和活性金屬(Ti)或和Mg之金屬間化合物,陶瓷基板11恐會發生破裂。 基於以上事實,本實施形態中,將活性金屬量訂為0.4μmol/cm2
以上47.0μmol/cm2
以下的範圍內(將Ti量訂為0.02mg/cm2
以上2.25mg/cm2
以下的範圍內),將Mg量訂為7.0μmol/cm2
以上143.2μmol/cm2
以下的範圍內(0.17mg/cm2
以上3.48mg/cm2
以下的範圍內)。When the amount of active metal is less than 0.4 μmol/cm 2 (the amount of Ti is less than 0.02 mg/cm 2 ), and the amount of Mg is less than 7.0 μmol/cm 2 (less than 0.17 mg/cm 2 ), the interface reaction will change Insufficient gains may reduce the engagement rate. In addition, when the amount of active metal exceeds 47.0 μmol/cm 2 (the amount of Ti exceeds 2.25 mg/cm 2 ), the relatively hard
本實施形態中,接合工程S03中的加壓荷重是被訂為0.049MPa以上,故能夠使陶瓷基板11與銅板22、23與活性金屬膜24(Ti膜)及Mg膜25密合,於加熱時能夠促進它們的界面反應。此外,接合工程S03中的加壓荷重是被訂為3.4MPa以下,故能夠抑制陶瓷基板11的破裂等。In this embodiment, the pressing load in the bonding process S03 is set to 0.049 MPa or more. Therefore, the
本實施形態中,Cu與Mg是在非接觸狀態下被層積,接合工程S03中的加熱溫度是被訂為Mg的熔點以上之670℃以上,故於接合界面能夠充分地令液相發生。另一方面,接合工程S03中的加熱溫度是被訂為850℃以下,故能夠抑制Cu與活性金屬(Ti)之共晶反應的發生,能夠抑制液相過度地生成。此外,對陶瓷基板11之熱負荷會變小,能夠抑制陶瓷基板11的劣化。In this embodiment, Cu and Mg are laminated in a non-contact state, and the heating temperature in the bonding process S03 is set at 670°C or more, which is the melting point of Mg, so that the liquid phase can be sufficiently generated at the bonding interface. On the other hand, the heating temperature in the joining process S03 is set to 850°C or lower, so the occurrence of the eutectic reaction between Cu and the active metal (Ti) can be suppressed, and the excessive generation of the liquid phase can be suppressed. In addition, the thermal load on the
(第2實施形態) 針對本發明之第2實施形態,參照圖5至圖8說明之。 本實施形態之銅/陶瓷接合體,係被做成藉由陶瓷構件即陶瓷基板111與銅構件即銅板122(電路層112)被接合而構成之絕緣電路基板110。 圖5揭示本發明第2實施形態之絕緣電路基板110及使用了此絕緣電路基板110之功率模組101。(Second Embodiment) "The second embodiment of the present invention will be described with reference to FIGS. 5 to 8. "The copper/ceramic bonded body of this embodiment is an insulated
此功率模組101,具備絕緣電路基板110、及在此絕緣電路基板110的一方側(圖5中上側)的面介著銲料層2而被接合之半導體元件3、及配置於絕緣電路基板110的另一方側(圖5中下側)之散熱座151。 銲料層2,例如訂為Sn-Ag系、Sn-In系、或是Sn-Ag-Cu系的銲料材。This
絕緣電路基板110,具備陶瓷基板111、及配設於此陶瓷基板111的一方的面(圖5中上面)之電路層112、及配設於陶瓷基板111的另一方的面(圖5中下面)之金屬層113。 陶瓷基板111,為防止電路層112與金屬層113之間的電性連接之物,本實施形態中由絕緣性高的氮化矽來構成。陶瓷基板111的厚度,被設定成0.2~1.5mm的範圍內,本實施形態中被設定成0.32mm。The
電路層112,如圖8所示,是藉由在陶瓷基板111的一方的面接合由銅或銅合金所成之銅板122而形成。本實施形態中,作為構成電路層112的銅板122,使用無氧銅的壓延板。在此電路層112,形成有電路圖樣,其一方的面(圖5中上面),為供半導體元件3搭載之搭載面。電路層112的厚度被設定成0.1mm以上2.0mm以下的範圍內,本實施形態中被設定成0.6mm。The
金屬層113,如圖8所示,是藉由在陶瓷基板111的另一方的面接合鋁板123而形成。本實施形態中,金屬層113,是以由純度99.99mass%以上的鋁(即所謂4N鋁)的壓延板所成之鋁板123被接合至陶瓷基板111而形成。此鋁板123,0.2%安全限應力被訂為30N/mm2
以下。金屬層113(鋁板123)的厚度被設定成0.5mm以上6mm以下的範圍內,本實施形態中被設定成2.0mm。金屬層113,如圖8所示,是藉由鋁板123使用Al-Si系硬銲材128被接合至陶瓷基板111而形成。The
散熱座151,為用來將前述的絕緣電路基板110冷卻之物,本實施形態中以由熱傳導性良好的材質所構成之散熱板來構成。本實施形態中,散熱座151以A6063(鋁合金)來構成。本實施形態中,此散熱座151,是在絕緣電路基板110的金屬層113,例如使用Al-Si系硬銲材而接合。The
陶瓷基板111與電路層112(銅板122),如圖8所示,是介著由從Ti,Zr,Nb,Hf選擇之1種或2種以上的活性金屬所成之活性金屬膜124(本實施形態中為Ti膜)及Mg膜125而被接合。 於陶瓷基板111與電路層112(銅板122)之接合界面,如圖6所示,層積有形成於陶瓷基板111側之活性金屬氮化物層131(本實施形態中為氮化鈦層)與Mg固溶於Cu的母相中而成之Mg固溶層132。The
Mg固溶層132中,含有上述的活性金屬。本實施形態中,Mg固溶層132中,分散有含有Cu與活性金屬(Ti)之金屬間化合物相133。本實施形態中,作為活性金屬使用Ti,作為構成含有Cu與Ti之金屬間化合物相133的金屬間化合物,例如可舉出Cu4
Ti,Cu3
Ti2
,Cu4
Ti3
,CuTi,CuTi2
,CuTi3
等。 此Mg固溶層132中的Mg的含有量,被訂為0.01原子%以上0.5原子%以下的範圍內。Mg固溶層132的厚度,被訂為0.1μm以上80μm以下的範圍內。The Mg
本實施形態中,在活性金屬氮化物層131(氮化鈦層)的內部,分散有Cu粒子135。 分散在活性金屬氮化物層131(氮化鈦層)內之Cu粒子135的粒徑,被訂為10nm以上100nm以下的範圍內。活性金屬氮化物層131(氮化鈦層)當中與陶瓷基板111之界面起算至活性金屬氮化物層131(氮化鈦層)的厚度的20%為止之界面鄰近區域中的Cu濃度,被訂為0.3原子%以上15原子%以下的範圍內。 活性金屬氮化物層131(氮化鈦層)的厚度,被訂為0.03μm以上1.2μm以下的範圍內。In this embodiment,
本實施形態中,在陶瓷基板111與電路層112之間,陶瓷基板111的接合面起算至往電路層112側50μm為止之區域中的Cu2
Mg相的面積率,被訂為15%以下。 In this embodiment, the area ratio of the Cu 2 Mg phase in the area 50 μm from the bonding surface of the
針對上述本實施形態之絕緣電路基板110的製造方法,參照圖7及圖8說明之。The method of manufacturing the insulated
如圖8所示,在作為電路層112之銅板122與陶瓷基板111之間,配置從Ti,Zr,Nb,Hf選擇之1種或2種以上的活性金屬的單體(本實施形態中為Ti單體)及Mg單體(活性金屬及Mg配置工程S101)。本實施形態中,藉由蒸鍍活性金屬(Ti)及Mg,會形成活性金屬膜124(Ti膜)及Mg膜125,Mg膜125會以接觸銅板122之方式形成。 此活性金屬及Mg配置工程S101中,將活性金屬量訂為0.4μmol/cm2
以上47.0μmol/cm2
以下的範圍內(本實施形態中,將Ti訂為0.02mg/cm2
以上2.25mg/cm2
以下的範圍內),將Mg量訂為7.0μmol/cm2
以上143.2μmol/cm2
以下的範圍內(0.17mg/cm2
以上3.48mg/cm2
以下的範圍內)。As shown in FIG. 8, between the
當活性金屬量未滿0.4μmol/cm2
(Ti量未滿0.02mg/cm2
)、及Mg量未滿7.0μmol/cm2
(未滿0.17mg/cm2
)的情形下,界面反應會變得不充分,接合率恐會低落。此外,當活性金屬量超出47.0μmol/cm2
(Ti量超出2.25mg/cm2
)的情形下,會過度地生成活性金屬多而相對硬的金屬間化合物相133,Mg固溶層132會變得過硬,陶瓷基板111恐會發生破裂。此外,當Mg量超出143.2μmol /cm2
(超出3.48mg/ cm2
)的情形下,陶瓷基板111的分解反應會變得過度,Al會過度地生成,而會大量產生它們和Cu或和活性金屬(Ti)或和Mg之金屬間化合物,陶瓷基板111恐會發生破裂。 活性金屬量的下限較佳是訂為2.8μmol/cm2
以上,活性金屬量的上限較佳是訂為18.8μmol/cm2
以下。此外,Mg量的下限較佳是訂為8.8μmol/cm2
以上,Mg量的上限較佳是訂為37.0μmol/cm2
以下。When the amount of active metal is less than 0.4 μmol/cm 2 (the amount of Ti is less than 0.02 mg/cm 2 ), and the amount of Mg is less than 7.0 μmol/cm 2 (less than 0.17 mg/cm 2 ), the interface reaction will change Insufficient gains may reduce the engagement rate. In addition, when the amount of active metal exceeds 47.0 μmol/cm 2 (the amount of Ti exceeds 2.25 mg/cm 2 ), a relatively hard
接著,將銅板122與陶瓷基板111,介著活性金屬膜124(Ti膜)及Mg膜125予以層積(層積工程S102)。 本實施形態中,如圖8所示,在陶瓷基板111的另一方的面側,介著Al-Si系硬銲材128,層積作為金屬層113之鋁板123。Next, the
將被層積的銅板122、陶瓷基板111、銅板123朝層積方向加壓,並且裝入真空爐內加熱,將銅板122與陶瓷基板111與鋁板123接合(接合工程S103)。 接合工程S103中的加壓荷重,被訂為0.049MPa以上3.4MPa以下的範圍內。接合工程S103中的加壓荷重,較佳是被訂為0.294MPa以上1.47MPa以下的範圍內,但不限定於此。The
接合工程S103中的加熱溫度,由於Cu與Mg是在接觸狀態下被層積,因此訂為Mg與Cu的共晶溫度以上之500℃以上,且Cu與活性金屬(Ti)的共晶溫度以下之850℃以下。加熱溫度的下限較佳是訂為700℃以上。 本實施形態中,是將鋁板123使用Al-Si系硬銲材128來接合,因此加熱溫度訂為600℃以上650℃以下的範圍內。 接合工程S103中的真空度,較佳是訂為1×10-6
Pa以上1×10-2
Pa以下的範圍內。 加熱溫度下的保持時間,較佳是訂為5min以上360min以下的範圍內。為了減低上述的Cu2
Mg相的面積率,較佳是將加熱溫度下的保持時間的下限訂為60min以上。加熱溫度下的保持時間的上限較佳是訂為240min以下。The heating temperature in the bonding process S103, because Cu and Mg are laminated in the contact state, it is set at 500°C or more above the eutectic temperature of Mg and Cu, and below the eutectic temperature of Cu and active metal (Ti) Below 850℃. The lower limit of the heating temperature is preferably set to 700°C or higher. In this embodiment, the
像以上這樣,藉由活性金屬及Mg配置工程S101、與層積工程S102、與接合工程S103,製造本實施形態之絕緣電路基板110。As described above, the insulating
在絕緣電路基板110的金屬層113的另一方的面側將散熱座151接合(散熱座接合工程S104)。 將絕緣電路基板110與散熱座151,介著硬銲材予以層積,朝層積方向加壓並且裝入真空爐內進行硬銲。如此一來,便將絕緣電路基板110的金屬層113與散熱座151接合。此時,作為硬銲材,例如能夠使用厚度20~110μm的Al-Si系硬銲材箔,硬銲溫度較佳是設定成比接合工程S103中的加熱溫度還低溫。The
接著,在絕緣電路基板110的電路層112的一方的面,將半導體元件3藉由銲接而接合(半導體元件接合工程S105)。 藉由以上的工程,製造出圖5所示之功率模組101。Next, on one surface of the
按照做成以上這樣的構成之本實施形態之絕緣電路基板110(銅/陶瓷接合體),銅板122(電路層112)與由氮化矽所成之陶瓷基板111,是介著活性金屬膜124(Ti膜)及Mg膜125而被接合,在陶瓷基板111與電路層112(銅板122)之接合界面,層積有形成於陶瓷基板111側之活性金屬氮化物層131(氮化鈦層)與Mg固溶於Cu的母相中而成之Mg固溶層132,在此Mg固溶層132內,存在有活性金屬。本實施形態中,係分散有含有Cu與活性金屬(Ti)之金屬間化合物相133,故如同第1實施形態般,能夠獲得電路層112(銅板122)與陶瓷基板111確實地被接合而成之絕緣電路基板110(銅/陶瓷接合體)。此外,接合界面中沒有Ag存在,故能夠獲得耐遷移性優良的絕緣電路基板110(銅/陶瓷接合體)。According to the insulated circuit board 110 (copper/ceramic junction) of the present embodiment having the above-mentioned structure, the copper plate 122 (circuit layer 112) and the
本實施形態中,在活性金屬氮化物層131(氮化鈦層)的內部分散有Cu粒子135,故銅板122的Cu會變得在陶瓷基板111的接合面充分地反應,可獲得電路層112(銅板122)與陶瓷基板111強固地被接合而成之絕緣電路基板110(銅/陶瓷接合體)。In this embodiment, the
本實施形態中,在陶瓷基板111與電路層112(銅板122)之間,陶瓷基板111的接合面起算至往電路層112(銅板122)側50μm為止之區域中的Cu2
Mg相的面積率係被限制在15%以下,故即使實施了例如超音波接合等的情形下,仍可抑制接合界面中的破裂等的發生。 In this embodiment, between the ceramic substrate 111 and the circuit layer 112 (copper plate 122), the area ratio of the Cu 2 Mg phase in the area from the bonding surface of the
按照本實施形態之絕緣電路基板110(銅/陶瓷接合體)的製造方法,如同第1實施形態般,在電路層112(銅板122)與陶瓷基板111之接合界面,能夠使液相適度地出現而充分地使其界面反應,能夠獲得銅板122與陶瓷基板111確實地被接合而成之絕緣電路基板110(銅/陶瓷接合體)。此外,接合不使用Ag,故能夠獲得耐遷移性優良的絕緣電路基板110。According to the manufacturing method of the insulated circuit board 110 (copper/ceramic joint) of this embodiment, as in the first embodiment, a liquid phase can be appropriately formed at the bonding interface between the circuit layer 112 (copper plate 122) and the
本實施形態中,Cu與Mg是在接觸狀態下被層積,接合工程S103中的加熱溫度是被訂為Cu與Mg的共晶溫度以上之500℃以上,故於接合界面能夠充分地令液相發生。 本實施形態中,於層積工程S102,是在陶瓷基板111的另一面側將鋁板123介著Al-Si系硬銲材128而層積,而將銅板122與陶瓷基板111、陶瓷基板111與鋁板123予以同時接合,故能夠效率良好地製造具備由銅所成之電路層112與由鋁所成之金屬層113的絕緣電路基板110。此外,能夠抑制絕緣電路基板110中的翹曲的發生。In this embodiment, Cu and Mg are laminated in a contact state, and the heating temperature in the bonding process S103 is set at 500°C or more, which is the eutectic temperature of Cu and Mg. Therefore, the bonding interface can sufficiently make the liquid Phase occurs. In this embodiment, in the layering process S102, the
以上已說明了本發明之實施形態,但本發明並不限定於此,在不脫離其發明技術思想之範圍內可適當變更。 例如,雖說明了將構成電路層或金屬層之銅板訂為無氧銅的壓延板,但不限定於此,亦可為由其他的銅或銅合金所構成之物。The embodiments of the present invention have been described above, but the present invention is not limited to this, and can be appropriately changed without departing from the scope of the technical idea of the invention. "For example, although it has been described that the copper plate constituting the circuit layer or the metal layer is ordered as a rolled plate of oxygen-free copper, it is not limited to this, and may be made of other copper or copper alloy.
第2實施形態中,雖說明了將構成金屬層之鋁板訂為純度99.99mass%的純鋁的壓延板,但不限定於此,亦可為由純度99mass%的鋁(2N鋁)等其他的鋁或鋁合金所構成之物。In the second embodiment, although the aluminum sheet constituting the metal layer is described as a rolled sheet made of pure aluminum with a purity of 99.99mass%, it is not limited to this, and may be made of aluminum (2N aluminum) with a purity of 99mass%. Something made of aluminum or aluminum alloy.
作為散熱座雖舉散熱板為例說明,但不限定於此,散熱座的構造並無特別限定。例如,亦可為具有供冷媒流通的流路之物或具備了冷卻鰭片之物。作為散熱座亦能使用含有鋁或鋁合金之複合材(例如AlSiC等)。 在散熱座的頂板部或在散熱板與金屬層之間,亦可設置由鋁或鋁合金或是含有鋁之複合材(例如AlSiC等)所成之緩衝層。Although the heat sink is taken as an example for the description of the heat sink, it is not limited to this, and the structure of the heat sink is not particularly limited. For example, it may be a thing having a flow path through which a refrigerant circulates or a thing equipped with cooling fins. A composite material containing aluminum or aluminum alloy (such as AlSiC, etc.) can also be used as a heat sink. "On the top plate of the heat sink or between the heat sink and the metal layer, a buffer layer made of aluminum or aluminum alloy or a composite material containing aluminum (such as AlSiC, etc.) can also be provided.
本實施形態中,雖說明了活性金屬及Mg配置工程中,是將活性金屬膜(Ti膜)及Mg膜予以成膜,但不限定於此,亦可將活性金屬與Mg予以共蒸鍍。在此情形下同樣地,被成膜之活性金屬膜及Mg膜,並未被合金化,而是配置活性金屬的單體及Mg單體。當藉由共蒸鍍將活性金屬及Mg膜成膜的情形下,Mg與Cu會成為接觸狀態,因此能夠將接合工程中的加熱溫度的下限訂為500℃以上。In this embodiment, although the active metal and Mg arrangement process is described as forming an active metal film (Ti film) and a Mg film, it is not limited to this, and the active metal and Mg may be co-evaporated. In this case, similarly, the active metal film and the Mg film to be formed are not alloyed, but the active metal monomer and Mg monomer are arranged. When the active metal and the Mg film are formed by co-evaporation, Mg and Cu will be in contact. Therefore, the lower limit of the heating temperature in the joining process can be set to 500° C. or more.
本實施形態中,雖說明了使用Ti作為活性金屬,但不限定於此,作為活性金屬亦可使用從Ti,Zr,Nb,Hf選擇之1種或2種以上。 當使用了Zr作為活性金屬的情形下,Mg固溶層中,Zr會以與Cu之金屬間化合物相的方式存在。作為構成此金屬間化合物相之金屬間化合物,例如可舉出Cu5 Zr,Cu51 Zr14 ,Cu8 Zr3 ,Cu10 Zr7 ,CuZr,Cu5 Zr8 ,CuZr2 等。 當使用了Hf作為活性金屬的情形下,Mg固溶層中,Hf會以與Cu之金屬間化合物相的方式存在。作為構成此金屬間化合物相之金屬間化合物,例如可舉出Cu51 Hf14 ,Cu8 Hf3 ,Cu10 Hf7 ,CuHf2 等。 當使用了Ti及Zr作為活性金屬的情形下,Mg固溶層中,Ti及Zr會以含有Cu與活性金屬之金屬間化合物相的方式存在。作為構成此金屬間化合物相之金屬間化合物,可舉出Cu1.5 Zr0.75 Ti0.75 等。 當使用了Nb作為活性金屬的情形下,Mg固溶層中,Nb會固溶於Mg固溶層而存在。In this embodiment, although Ti is described as the active metal, it is not limited to this. As the active metal, one or two or more selected from Ti, Zr, Nb, and Hf may also be used. When Zr is used as the active metal, in the Mg solid solution layer, Zr will exist as an intermetallic compound phase with Cu. Examples of the intermetallic compound constituting the intermetallic compound phase include Cu 5 Zr, Cu 51 Zr 14 , Cu 8 Zr 3 , Cu 10 Zr 7 , CuZr, Cu 5 Zr 8 , CuZr 2 and the like. When Hf is used as the active metal, in the Mg solid solution layer, Hf will exist as an intermetallic compound phase with Cu. Examples of the intermetallic compound constituting the intermetallic compound phase include Cu 51 Hf 14 , Cu 8 Hf 3 , Cu 10 Hf 7 , CuHf 2 and the like. When Ti and Zr are used as the active metal, Ti and Zr will exist in the Mg solid solution layer as an intermetallic compound phase containing Cu and the active metal. Examples of the intermetallic compound constituting the intermetallic compound phase include Cu 1.5 Zr 0.75 Ti 0.75 and the like. When Nb is used as the active metal, in the Mg solid solution layer, Nb will be dissolved in the Mg solid solution layer and exist.
活性金屬及Mg配置工程中,只要將接合界面中的活性金屬量訂為0.4μmol/cm2 以上47.0μmol/cm2 以下的範圍內,將Mg量訂為7.0μmol/cm2 以上143.2μmol/cm2 以下的範圍內即可,例如亦可像Mg膜/活性金屬膜/Mg膜這樣將活性金屬膜與Mg膜予以多層地層積。或者是,亦可在活性金屬膜與Mg膜之間將Cu膜成膜。 活性金屬的單體及Mg單體,可配置箔材,亦可藉由濺鍍來成膜。In the active metal and Mg configuration process, as long as the amount of active metal in the joint interface is set within the range of 0.4μmol/cm 2 or more and 47.0 μmol/cm 2 or less, the amount of Mg is set to be 7.0 μmol/cm 2 or more and 143.2 μmol/cm The range of 2 or less may be sufficient. For example, the active metal film and the Mg film may be laminated in multiple layers like Mg film/active metal film/Mg film. Alternatively, the Cu film may be formed between the active metal film and the Mg film. Active metal monomers and Mg monomers can be equipped with foils, and can also be sputtered to form films.
本實施形態中,雖說明了在絕緣電路基板的電路層搭載功率半導體元件來構成功率模組之物,但不限定於此。例如,亦可在絕緣電路基板搭載LED元件來構成LED模組,亦可在絕緣電路基板的電路層搭載熱電元件來構成熱電模組。 [實施例]In this embodiment, although a power semiconductor element is mounted on the circuit layer of an insulated circuit board to form a power module, it is not limited to this. For example, an LED element may be mounted on an insulated circuit board to form an LED module, or a thermoelectric element may be mounted on the circuit layer of the insulated circuit board to form a thermoelectric module. [Example]
說明為確認本發明的有效性而進行之確認實驗。A confirmation experiment performed to confirm the effectiveness of the present invention will be described.
<實施例1> 形成了表1所示構造之銅/陶瓷接合體。詳言之,是在40mm見方的陶瓷基板的兩面,如表1所示,層積將Ti單體及Mg單體作為活性金屬予以成膜而成之銅板,以表1所示之接合條件接合,形成了銅/陶瓷接合體。 陶瓷基板的厚度當氮化鋁的情形下使用了厚度0.635mm,當氮化矽的情形下使用了厚度0.32mm。此外,接合時的真空爐的真空度訂為5×10-3 Pa。<Example 1> A copper/ceramic joint body having the structure shown in Table 1 was formed. Specifically, it is a copper plate formed by laminating Ti and Mg as active metals on both sides of a 40mm square ceramic substrate, as shown in Table 1, and bonding under the bonding conditions shown in Table 1. , Forming a copper/ceramic joint body. The thickness of the ceramic substrate is 0.635mm in the case of aluminum nitride, and 0.32mm in the case of silicon nitride. In addition, the vacuum degree of the vacuum furnace at the time of bonding is set to 5×10 -3 Pa.
針對依此方式獲得的銅/陶瓷接合體,觀察接合界面來確認活性金屬氮化物層(氮化鈦層)、Mg固溶層、金屬間化合物相、活性金屬氮化物層(氮化鈦層)中的Cu粒子的有無及Cu濃度。此外,依以下方式評估了銅/陶瓷接合體的初始接合率、冷熱循環後的陶瓷基板的破裂、遷移性。For the copper/ceramic joint obtained in this way, observe the joint interface to confirm the active metal nitride layer (titanium nitride layer), Mg solid solution layer, intermetallic compound phase, and active metal nitride layer (titanium nitride layer) The presence or absence of Cu particles and the concentration of Cu. In addition, the initial bonding rate of the copper/ceramic bonded body, the fracture and migration of the ceramic substrate after the cooling and heating cycle were evaluated in the following manner.
(Mg固溶層) 對於銅板與陶瓷基板之接合界面,使用EPMA裝置(日本電子公司製JXA-8539F),以倍率2000倍、加速電壓15kV的條件觀察包含接合界面之區域(400μm×600μm),從陶瓷基板表面(活性金屬氮化物層表面)朝向銅板側以10μm間隔的10點進行定量分析,將Mg濃度為0.01原子%以上之區域訂為Mg固溶層。(Mg solid solution layer) For the bonding interface between the copper plate and the ceramic substrate, use an EPMA device (JXA-8539F manufactured by JEOL Ltd.) to observe the area including the bonding interface (400μm×600μm) at a magnification of 2000 times and an acceleration voltage of 15kV. Quantitative analysis was performed at 10 points at 10 μm intervals from the surface of the ceramic substrate (the surface of the active metal nitride layer) toward the copper plate, and the area where the Mg concentration was 0.01 at% or more was designated as the Mg solid solution layer.
(Mg固溶層中的活性金屬的有無(金屬間化合物相的有無) 對於銅板與陶瓷基板之接合界面,使用電子探針顯微分析儀(日本電子公司製JXA-8539F),以倍率2000倍、加速電壓15kV的條件取得包含接合界面之區域(400μm ×600μm)的活性金屬(Ti)的元素MAP,確認了活性金屬(Ti)的有無。此外,以確認到活性金屬(Ti)的存在之區域內的定量分析的5點平均,將滿足Cu濃度為5原子%以上,且活性金屬濃度(Ti濃度)為16原子以上90原子%以下之區域訂為金屬間化合物相。(Presence of active metal in the Mg solid solution layer (presence of intermetallic compound phase) For the bonding interface between the copper plate and the ceramic substrate, use an electron probe microanalyzer (JXA-8539F manufactured by JEOL Ltd.) at a magnification of 2000 times The element MAP of the active metal (Ti) in the area (400 μm × 600 μm) of the joint interface was obtained under the conditions of acceleration voltage of 15kV, and the presence of active metal (Ti) was confirmed. In addition, the presence of active metal (Ti) was confirmed The 5-point average of the quantitative analysis in the area defines the area satisfying that the Cu concentration is 5 atomic% or more and the active metal concentration (Ti concentration) is 16 atomic% or more and 90 atomic% or less as the intermetallic compound phase.
(活性金屬氮化物層) 對於銅板與陶瓷基板之接合界面,使用掃描型穿透電子顯微鏡(FEI公司製Titan ChemiSTEM(附EDS檢測器)),以倍率115000倍、加速電壓200kV的條件進行觀察,能量分散型X射線分析法(賽默飛世爾科技公司製NSS7)進行測繪(mapping),於活性金屬(Ti)和N重疊之區域,藉由照射縮細至1nm程度之電子束(NBD(奈米射束繞射)法)來獲得電子繞射圖形,確認了活性金屬氮化物層(氮化鈦層)的有無。 對確認到活性金屬氮化物層(氮化鈦層)之區域中確認Cu粒子的有無,將由此區域中的定量分析的5點平均所獲得之Cu濃度,訂為分散於活性金屬氮化物層(氮化鈦層)內之Cu的平均濃度。(Active metal nitride layer) The bonding interface between the copper plate and the ceramic substrate was observed using a scanning transmission electron microscope (Titan ChemiSTEM manufactured by FEI (with EDS detector)) at a magnification of 115,000 times and an acceleration voltage of 200kV. Energy dispersive X-ray analysis (NSS7 manufactured by Thermo Fisher Scientific) is used for mapping. In the area where the active metal (Ti) and N overlap, the electron beam (NBD (Nei The meter beam diffraction method) was used to obtain an electron diffraction pattern, and the presence or absence of an active metal nitride layer (titanium nitride layer) was confirmed. Regarding the area where the active metal nitride layer (titanium nitride layer) is confirmed for the presence or absence of Cu particles, the Cu concentration obtained by the 5-point average of the quantitative analysis in this area is ordered to be dispersed in the active metal nitride layer ( The average concentration of Cu in the titanium nitride layer).
(初始接合率) 銅板與陶瓷基板之接合率,是使用超音波探傷裝置(日立電力解決方案公司製FineSAT200)使用以下式子求出。所謂初始接合面積,是訂為接合前的應接合面積,亦即銅板的接合面的面積。超音波探傷像中,剝離是以接合部內的白色部分表示,因此將此白色部分的面積訂為剝離面積。 (接合率)={(初始接合面積)-(剝離面積)}/(初始接合面積)×100(Initial bonding rate) The bonding rate between the copper plate and the ceramic substrate is calculated using the following formula using an ultrasonic flaw detection device (FineSAT200 manufactured by Hitachi Electric Power Solutions). The so-called initial bonding area is set as the area to be bonded before bonding, that is, the area of the bonding surface of the copper plate. In the ultrasonic flaw detection image, peeling is indicated by the white part in the joint, so the area of this white part is defined as the peeling area. (Joining rate)=((Initial joining area)-(Peeling area))/(Initial joining area)×100
(陶瓷基板的破裂) 使用冷熱衝撃試驗機(ESPEC公司製TSA-72ES),於氣相下,將循環實施了300循環,該循環係1循環為-50℃下10分鐘與150℃下10分鐘。 評估負荷了上述的冷熱循環後之陶瓷基板的破裂的有無。(Crack of ceramic substrate) Using a hot and cold impact tester (TSA-72ES manufactured by ESPEC), in the gas phase, the cycle was carried out for 300 cycles. The cycle system is 1 cycle at -50°C for 10 minutes and 150°C for 10 minutes . Evaluate the presence or absence of cracks in the ceramic substrate after being subjected to the above-mentioned thermal cycle.
(遷移) 以電路層的電路圖樣間距離0.8mm、溫度60℃、濕度95%RH、電壓DC50V之條件,放置500小時後,測定了電路圖樣間的電阻。將電阻值成為1×106 Ω以下的情形判斷為短路,訂為「B」。將電阻值未成為1×106 Ω以下的情形訂為「A」。(Migration) The resistance between the circuit patterns of the circuit layer was measured after the distance between the circuit patterns of the circuit layer was 0.8mm, the temperature was 60°C, the humidity was 95%RH, and the voltage was DC50V. When the resistance value becomes 1×10 6 Ω or less, it is judged as a short circuit, and it is designated as "B". The case where the resistance value is not 1×10 6 Ω or less is referred to as "A".
評估結果如表2所示。此外,本發明例5的觀察結果如圖9A、圖9B及圖9C所示。The evaluation results are shown in Table 2. In addition, the observation results of Example 5 of the present invention are shown in FIG. 9A, FIG. 9B, and FIG. 9C.
活性金屬及Mg配置工程中,於活性金屬量(Ti量)為0.1μmol/cm2 (0.005mg/cm2 )這樣比本發明之範圍還少的比較例1中,初始接合率變低。推測是因為Mg固溶層中不存在活性金屬(Ti)作為金屬間化合物相,界面反應不充分的緣故。 活性金屬及Mg配置工程中,於活性金屬量(Ti量)為66.9μmol/cm2 (3.20mg/cm2 )這樣比本發明之範圍還多的比較例2中,確認到陶瓷基板的破裂。推測是因為大量形成了相對硬的金屬間化合物相的緣故。In the active metal and Mg arrangement process, in Comparative Example 1, where the amount of active metal (the amount of Ti) is 0.1 μmol/cm 2 (0.005 mg/cm 2 ), which is less than the scope of the present invention, the initial bonding rate becomes low. Presumably, it is because there is no active metal (Ti) as an intermetallic compound phase in the Mg solid solution layer, and the interfacial reaction is insufficient. In the active metal and Mg arrangement process, the amount of active metal (Ti amount) was 66.9 μmol/cm 2 (3.20 mg/cm 2 ) in Comparative Example 2, which was larger than the scope of the present invention, and cracking of the ceramic substrate was confirmed. Presumably, it is because a relatively hard intermetallic compound phase is formed in a large amount.
活性金屬及Mg配置工程中,於Mg量為2.1μmol/cm2 (0.05mg/cm2 )這樣比本發明之範圍還少的比較例3中,初始接合率變低。推測是因為未觀察到Mg固溶層,界面反應不充分的緣故。 活性金屬及Mg配置工程中,於Mg量為220.1μmol /cm2 (5.35mg/cm2 )這樣比本發明之範圍還多的比較例4中,確認到陶瓷基板的破裂。推測是因為陶瓷基板的分解反應過度,Al過度地生成,而大量生成了它們和Cu或和活性金屬(Ti)或和Mg的金屬間化合物的緣故。In the active metal and Mg arrangement process, in Comparative Example 3, which has a Mg amount of 2.1 μmol/cm 2 (0.05 mg/cm 2 ), which is less than the scope of the present invention, the initial bonding rate becomes low. It is presumed that the Mg solid solution layer was not observed and the interface reaction was insufficient. In the active metal and Mg placement process, in Comparative Example 4, where the amount of Mg was 220.1 μmol/cm 2 (5.35 mg/cm 2 ), which was larger than the scope of the present invention, cracking of the ceramic substrate was confirmed. It is presumed that the decomposition reaction of the ceramic substrate was excessive, Al was excessively generated, and a large amount of intermetallic compounds between them and Cu, active metal (Ti), or Mg were generated.
於使用Ag-Cu-Ti硬銲材將陶瓷基板與銅板接合而成之習知例中,遷移被判斷為「B」。推測是因為接合界面中有Ag存在的緣故。In the conventional example where the ceramic substrate and the copper plate are joined using Ag-Cu-Ti brazing material, the migration is judged as "B". Presumably, it is due to the presence of Ag in the bonding interface.
相對於此,本發明例1~12中,初始接合率亦高,亦未確認到陶瓷基板的破裂。此外,遷移亦良好。 如圖9A、圖9B及圖9C所示,觀察接合界面之結果,觀察到活性金屬氮化物層31(氮化鈦層)、Mg固溶層32,並觀察到在此Mg固溶層32的內部分散有金屬間化合物相33。In contrast, in Examples 1 to 12 of the present invention, the initial bonding rate was also high, and cracking of the ceramic substrate was not confirmed. In addition, the migration is also good. As shown in FIGS. 9A, 9B, and 9C, the result of observing the bonding interface shows that the active metal nitride layer 31 (titanium nitride layer) and the Mg
<實施例2> 形成了表3所示構造之銅/陶瓷接合體。詳言之,是在40mm見方的陶瓷基板的兩面,如表3所示,層積將活性金屬的單體及Mg單體予以成膜而成之銅板,以表3所示之接合條件接合,形成了銅/陶瓷接合體。陶瓷基板的厚度當氮化鋁的情形下使用了厚度0.635mm,當氮化矽的情形下使用了厚度0.32mm。此外,接合時的真空爐的真空度訂為5×10-3 Pa。<Example 2> A copper/ceramic joint body having the structure shown in Table 3 was formed. Specifically, it is a copper plate formed by laminating active metal monomers and Mg monomers on both sides of a 40mm square ceramic substrate, as shown in Table 3, and bonding under the bonding conditions shown in Table 3. A copper/ceramic junction is formed. The thickness of the ceramic substrate is 0.635mm in the case of aluminum nitride, and 0.32mm in the case of silicon nitride. In addition, the vacuum degree of the vacuum furnace at the time of bonding is set to 5×10 -3 Pa.
針對依此方式獲得的銅/陶瓷接合體,如同實施例1般,觀察接合界面,確認了活性金屬氮化物層、Mg固溶層、Mg固溶層中的活性金屬的有無(金屬間化合物相的有無)、活性金屬氮化物層中的Cu粒子的有無及Cu濃度。此外,銅/陶瓷接合體的初始接合率、冷熱循環後的陶瓷基板的破裂、遷移性,係如同實施例1般評估。評估結果如表4所示。For the copper/ceramic joint obtained in this way, the joint interface was observed as in Example 1, and the presence or absence of active metal (intermetallic compound phase) in the active metal nitride layer, Mg solid solution layer, and Mg solid solution layer was confirmed. The presence or absence of), the presence or absence of Cu particles in the active metal nitride layer and the Cu concentration. In addition, the initial bonding rate of the copper/ceramic bonded body, the fracture and migration of the ceramic substrate after the cooling and heating cycle, were evaluated in the same manner as in Example 1. The evaluation results are shown in Table 4.
活性金屬及Mg配置工程中,於活性金屬量(Zr量)為50.4μmol/cm2 這樣比本發明之範圍還多的比較例21、及活性金屬量(Nb量)為61.2μmol/cm2 這樣比本發明之範圍還多的比較例22中,確認到陶瓷基板的破裂。推測是因為Mg固溶層中存在的活性金屬量多,Mg固溶層變硬了的緣故。 活性金屬及Mg配置工程中,於活性金屬量(Hf量)為0.2μmol/cm2 這樣比本發明之範圍還少的比較例23、及活性金屬量(Hf量+Nb量)為0.2μmol/cm2 這樣比本發明之範圍還少的比較例24中,初始接合率變低。In the active metal and Mg configuration process, the amount of active metal (Zr amount) is 50.4 μmol/cm 2 in Comparative Example 21, which is larger than the scope of the present invention, and the amount of active metal (Nb amount) is 61.2 μmol/cm 2 In Comparative Example 22, which is more than the scope of the present invention, cracking of the ceramic substrate was confirmed. It is presumed that the amount of active metal present in the Mg solid solution layer is large, and the Mg solid solution layer is hardened. In the active metal and Mg configuration process, the amount of active metal (Hf amount) is 0.2 μmol/cm 2 in Comparative Example 23, which is less than the scope of the present invention, and the amount of active metal (Hf amount + Nb amount) is 0.2 μmol/cm 2 In Comparative Example 24, which is smaller than the scope of the present invention, the initial bonding rate becomes low.
相對於此,本發明例21~27中,初始接合率亦高,亦未確認到陶瓷基板的破裂。此外,遷移亦良好。In contrast, in Examples 21 to 27 of the present invention, the initial bonding rate was also high, and cracking of the ceramic substrate was not confirmed. In addition, the migration is also good.
由以上事實,確認了按照本發明例,可提供一種銅構件與陶瓷構件會確實地被接合,耐遷移性優良之銅/陶瓷接合體(絕緣電路基板)。From the above facts, it was confirmed that according to the example of the present invention, a copper member and a ceramic member can be reliably joined, and a copper/ceramic joined body (insulated circuit board) having excellent migration resistance can be provided.
<實施例3> 形成了表5所示構造之絕緣電路基板。詳言之,是在40mm見方的陶瓷基板的兩面,如表5所示,層積將活性金屬的單體及Mg單體予以成膜而成之銅板,以表5所示之接合條件接合,形成了具有電路層之絕緣電路基板。陶瓷基板的厚度當氮化鋁的情形下使用了厚度0.635mm,當氮化矽的情形下使用了厚度0.32mm。此外,接合時的真空爐的真空度訂為5×10-3 Pa。<Example 3> An insulated circuit board having the structure shown in Table 5 was formed. Specifically, it is a copper plate formed by laminating active metal monomers and Mg monomers on both sides of a 40mm square ceramic substrate, as shown in Table 5, and bonding under the bonding conditions shown in Table 5. An insulated circuit substrate with a circuit layer is formed. The thickness of the ceramic substrate is 0.635mm in the case of aluminum nitride, and 0.32mm in the case of silicon nitride. In addition, the vacuum degree of the vacuum furnace at the time of bonding is set to 5×10 -3 Pa.
針對依此方式獲得的絕緣電路基板,依以下方式評估了陶瓷基板與電路層之接合界面中的Cu2 Mg相的面積率、及超音波接合至電路層之端子的拉伸強度。With respect to the insulated circuit substrate obtained in this way, the area ratio of the Cu 2 Mg phase in the bonding interface between the ceramic substrate and the circuit layer and the tensile strength of the terminal ultrasonically bonded to the circuit layer were evaluated in the following manner.
(Cu2 Mg相的面積率) 對於銅板與陶瓷基板之接合界面,使用電子探針顯微分析儀(日本電子公司製JXA-8539F),以倍率750倍、加速電壓15kV的條件取得包含接合界面之區域(120μm×160μm)的Mg的元素MAP,以確認到Mg的存在之區域內的定量分析的5點平均,將Mg濃度滿足30原子%以上40原子%以下之區域訂為Cu2 Mg相。 於觀察視野內,求出陶瓷基板的接合面與從陶瓷基板的接合面起算往銅板側50μm為止之區域的面積A。於此區域內求出Cu2 Mg相的面積B,求出Cu2 Mg相的面積率B/A×100(%)。如上述般以5視野測定Cu2 Mg相的面積率,將其平均值記載於表5。(Cu 2 Mg phase area ratio) For the bonding interface between the copper plate and the ceramic substrate, an electron probe microanalyzer (JXA-8539F manufactured by JEOL Ltd.) was used to obtain the bonding interface at a magnification of 750 times and an acceleration voltage of 15kV. The elemental MAP of Mg in the region (120μm×160μm) is determined by the 5-point average of quantitative analysis in the region where the presence of Mg is confirmed, and the region where the Mg concentration meets 30 atomic% or more and 40 atomic% or less is defined as the Cu 2 Mg phase . In the observation field of view, the area A of the bonding surface of the ceramic substrate and the area from the bonding surface of the ceramic substrate to the copper plate side 50 μm was determined. Cu 2 Mg phase is obtained within this area of B, Cu 2 Mg phase is determined the area ratio B / A × 100 (%) . The area ratio of the Cu 2 Mg phase was measured with 5 fields of view as described above, and the average value is shown in Table 5.
(拉伸強度) 如圖10A及圖10B所示,在絕緣電路基板的電路層的上方,使用包含平台40之超音波金屬接合機(超音波工業公司製60C-904),將銅端子(寬幅:5mm、厚度T:1.0 mm、長度L1
:20mm、長度L2
:10mm)以壓潰(collapse)量0.3mm的條件予以超音波接合。 將以工具速度Y為5mm/s,平台速度X為5mm/s的條件將銅端子拉伸時之斷裂荷重除以接合面積而成之值訂為拉伸強度,記載於表5。(Tensile strength) As shown in Fig. 10A and Fig. 10B, above the circuit layer of the insulated circuit board, using an ultrasonic metal bonding machine (60C-904 manufactured by Ultrasonic Industry Co., Ltd.) including a
比較本發明例31~43,確認到Cu2 Mg相的面積率愈低,拉伸強度愈變高。故,確認了當欲使超音波接合性提升的情形下,將Cu2 Mg相的面積率抑制得較低是有效的。 [產業利用性]Comparing Examples 31 to 43 of the present invention, it was confirmed that the lower the area ratio of the Cu 2 Mg phase, the higher the tensile strength. Therefore, it was confirmed that when it is desired to improve the ultrasonic bonding properties, it is effective to suppress the area ratio of the Cu 2 Mg phase to a low level. [Industrial Utilization]
按照本發明,能夠提供一種銅構件與陶瓷構件確實地被接合,而耐遷移性優良之銅/陶瓷接合體,絕緣電路基板,及上述的銅/陶瓷接合體的製造方法,絕緣電路基板的製造方法。According to the present invention, it is possible to provide a copper/ceramic joint body, an insulated circuit board, and a method for manufacturing the above-mentioned copper/ceramic joint body, and a manufacturing method of the above-mentioned copper/ceramic joint body, and an insulated circuit board method.
10、110‧‧‧絕緣電路基板11、111‧‧‧陶瓷基板12、112‧‧‧電路層13、113‧‧‧金屬層22、23、122‧‧‧銅板31、131‧‧‧活性金屬氮化物層32、132‧‧‧Mg固溶層33、133‧‧‧金屬間化合物相35、135‧‧‧Cu粒子10、110‧‧‧Insulated circuit substrate 11,111‧‧‧Ceramic substrate 12,112‧‧‧Circuit layer 13,113‧‧‧
[圖1] 使用了本發明第1實施形態之絕緣電路基板的功率模組的概略說明圖。 [圖2] 本發明第1實施形態之絕緣電路基板的電路層(銅構件)及金屬層(銅構件)與陶瓷基板(陶瓷構件)之接合界面的模型圖。 [圖3] 本發明第1實施形態之絕緣電路基板的製造方法示意流程圖。 [圖4] 本發明第1實施形態之絕緣電路基板的製造方法示意說明圖。 [圖5] 使用了本發明第2實施形態之絕緣電路基板的功率模組的概略說明圖。 [圖6] 本發明第2實施形態之絕緣電路基板的電路層(銅構件)與陶瓷基板(陶瓷構件)之接合界面的模型圖。 [圖7] 本發明第2實施形態之絕緣電路基板的製造方法示意流程圖。 [圖8] 本發明第2實施形態之絕緣電路基板的製造方法示意說明圖。 [圖9A] 本發明例5之銅/陶瓷接合體中的銅板與陶瓷基板之接合界面的觀察結果。 [圖9B] 本發明例5之銅/陶瓷接合體中的銅板與陶瓷基板之接合界面的觀察結果。 [圖9C] 本發明例5之銅/陶瓷接合體中的銅板與陶瓷基板之接合界面的觀察結果。 [圖10A] 實施例3中的拉伸強度的測定方法示意說明圖。 [圖10B] 實施例3中的拉伸強度的測定方法示意說明圖。[Fig. 1] A schematic explanatory diagram of a power module using the insulated circuit board according to the first embodiment of the present invention. [FIG. 2] A model diagram of the bonding interface between the circuit layer (copper member) and the metal layer (copper member) of the insulated circuit substrate of the first embodiment of the present invention and the ceramic substrate (ceramic member). [FIG. 3] A schematic flow chart of the manufacturing method of the insulated circuit board according to the first embodiment of the present invention. [FIG. 4] A schematic explanatory view of the manufacturing method of the insulated circuit board according to the first embodiment of the present invention. [FIG. 5] A schematic explanatory diagram of a power module using the insulated circuit board according to the second embodiment of the present invention. [FIG. 6] A model diagram of the bonding interface between the circuit layer (copper member) of the insulated circuit board and the ceramic substrate (ceramic member) in the second embodiment of the present invention. [FIG. 7] A schematic flow chart of a manufacturing method of an insulated circuit board according to the second embodiment of the present invention. [FIG. 8] A schematic explanatory diagram of a method of manufacturing an insulated circuit board according to a second embodiment of the present invention. [FIG. 9A] Observation results of the bonding interface between the copper plate and the ceramic substrate in the copper/ceramic joint of Example 5 of the present invention. [Figure 9B] Observation results of the joint interface between the copper plate and the ceramic substrate in the copper/ceramic joint of Example 5 of the present invention. [Figure 9C] Observation results of the joint interface between the copper plate and the ceramic substrate in the copper/ceramic joint of Example 5 of the present invention. [Fig. 10A] A schematic explanatory diagram of the method of measuring the tensile strength in Example 3. [Fig. 10B] A schematic explanatory diagram of the method of measuring the tensile strength in Example 3.
11‧‧‧陶瓷基板 11‧‧‧Ceramic substrate
12‧‧‧電路層 12‧‧‧Circuit layer
13‧‧‧金屬層 13‧‧‧Metal layer
22、23‧‧‧銅板 22, 23‧‧‧copper plate
31‧‧‧活性金屬氮化物層 31‧‧‧Active metal nitride layer
32‧‧‧Mg固溶層 32‧‧‧Mg solid solution layer
33‧‧‧金屬間化合物相 33‧‧‧Intermetallic compound phase
35‧‧‧Cu粒子 35‧‧‧Cu particles
Claims (14)
Applications Claiming Priority (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2017036841 | 2017-02-28 | ||
JP2017-036841 | 2017-02-28 | ||
JP2018010964A JP6965768B2 (en) | 2017-02-28 | 2018-01-25 | Copper / Ceramics Joint, Insulated Circuit Board, Copper / Ceramics Joint Manufacturing Method, Insulated Circuit Board Manufacturing Method |
JP2018-010964 | 2018-01-25 |
Publications (2)
Publication Number | Publication Date |
---|---|
TW201841871A TW201841871A (en) | 2018-12-01 |
TWI746807B true TWI746807B (en) | 2021-11-21 |
Family
ID=63370915
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
TW107106520A TWI746807B (en) | 2017-02-28 | 2018-02-27 | Copper/ceramic bonded body, insulating circuit substrate, method of manufacturing copper/ceramic bonded body and method of manufacturing insulating circuit substrate |
Country Status (2)
Country | Link |
---|---|
TW (1) | TWI746807B (en) |
WO (1) | WO2018159590A1 (en) |
Families Citing this family (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2020044594A1 (en) * | 2018-08-28 | 2020-03-05 | 三菱マテリアル株式会社 | Copper/ceramic bonded body, insulation circuit board, method for producing copper/ceramic bonded body, and method for manufacturing insulation circuit board |
CN111848226B (en) * | 2019-04-24 | 2022-03-25 | 成都大学 | Nano metal layer ceramic substrate and manufacturing method thereof |
CN114127921B (en) * | 2019-08-21 | 2022-12-23 | 三菱综合材料株式会社 | Copper-ceramic joined body, insulated circuit board, method for producing copper-ceramic joined body, and method for producing insulated circuit board |
JP2021072447A (en) * | 2019-10-30 | 2021-05-06 | 三菱マテリアル株式会社 | Copper/ceramic assembly, insulated circuit board, method for producing copper/ceramic assembly, and method for producing insulated circuit board |
JP6908173B2 (en) * | 2019-12-02 | 2021-07-21 | 三菱マテリアル株式会社 | Copper / Ceramics Joint, Insulated Circuit Board, Copper / Ceramics Joint Manufacturing Method, Insulated Circuit Board Manufacturing Method |
KR102413017B1 (en) * | 2019-12-02 | 2022-06-23 | 미쓰비시 마테리알 가부시키가이샤 | Copper/ceramic bonded body, insulated circuit board, and copper/ceramic bonded body manufacturing method, insulated circuit board manufacturing method |
WO2021112046A1 (en) * | 2019-12-06 | 2021-06-10 | 三菱マテリアル株式会社 | Copper/ceramic assembly, insulated circuit board, method for producing copper/ceramic assembly, and method for producing insulated circuit board |
CN115004361A (en) * | 2020-01-24 | 2022-09-02 | 三菱综合材料株式会社 | Copper-graphene bonded body, method for producing same, and copper-graphene bonded structure |
EP4159704A1 (en) * | 2020-05-27 | 2023-04-05 | Mitsubishi Materials Corporation | Copper/ceramic bonded body and insulated circuit board |
WO2024053738A1 (en) * | 2022-09-09 | 2024-03-14 | 三菱マテリアル株式会社 | Copper/ceramic bonded body and insulated circuit board |
Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
TW200302261A (en) * | 2002-01-25 | 2003-08-01 | Ngk Insulators Ltd | Bonded member comprising different materials, and production method thereof |
Family Cites Families (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH04162756A (en) | 1990-10-26 | 1992-06-08 | Toshiba Corp | Semiconductor module |
JP3211856B2 (en) | 1994-11-02 | 2001-09-25 | 電気化学工業株式会社 | Circuit board |
JP3866320B2 (en) * | 1995-02-09 | 2007-01-10 | 日本碍子株式会社 | Bonded body and manufacturing method of bonded body |
JP3813654B2 (en) * | 1995-02-09 | 2006-08-23 | 日本碍子株式会社 | Ceramic bonding structure and manufacturing method thereof |
JP3824044B2 (en) * | 1999-09-03 | 2006-09-20 | 同和鉱業株式会社 | Silicon nitride circuit board manufacturing method |
JP3930671B2 (en) * | 1999-11-08 | 2007-06-13 | Dowaホールディングス株式会社 | Method for manufacturing silicon nitride circuit board |
JP4375730B2 (en) | 2004-04-23 | 2009-12-02 | 本田技研工業株式会社 | Brazing material for joining copper and ceramics or carbon-based copper composite material and joining method therefor |
JP4997431B2 (en) * | 2006-01-24 | 2012-08-08 | 独立行政法人産業技術総合研究所 | Method for producing high thermal conductivity silicon nitride substrate |
JP6060739B2 (en) * | 2013-03-05 | 2017-01-18 | 三菱マテリアル株式会社 | Power module substrate manufacturing method |
JP2017036841A (en) | 2013-11-15 | 2017-02-16 | イビデン株式会社 | Accumulator |
TW201601903A (en) * | 2014-03-20 | 2016-01-16 | Jx Nippon Mining & Metals Corp | Tire, and method for manufacturing same |
JP2018010964A (en) | 2016-07-13 | 2018-01-18 | 株式会社村田製作所 | Manufacturing method of circuit module and deposition device |
-
2018
- 2018-02-27 TW TW107106520A patent/TWI746807B/en active
- 2018-02-27 WO PCT/JP2018/007186 patent/WO2018159590A1/en unknown
Patent Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
TW200302261A (en) * | 2002-01-25 | 2003-08-01 | Ngk Insulators Ltd | Bonded member comprising different materials, and production method thereof |
Also Published As
Publication number | Publication date |
---|---|
WO2018159590A1 (en) | 2018-09-07 |
TW201841871A (en) | 2018-12-01 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
TWI746807B (en) | Copper/ceramic bonded body, insulating circuit substrate, method of manufacturing copper/ceramic bonded body and method of manufacturing insulating circuit substrate | |
KR102459745B1 (en) | Copper/ceramic bonded body, insulated circuit board, and copper/ceramic bonded body manufacturing method, insulated circuit board manufacturing method | |
TWI772597B (en) | Copper/ceramic bonded body, insulated circuit board, method for producing copper/ceramic bonded body, and method for producing insulated circuit board | |
CN111566074B (en) | Copper-ceramic joined body, insulated circuit board, method for producing copper-ceramic joined body, and method for producing insulated circuit board | |
KR101758586B1 (en) | Copper/ceramic bond and power module substrate | |
JP7056744B2 (en) | A method for manufacturing a copper / ceramics joint, an insulating circuit board, and a copper / ceramics joint, and a method for manufacturing an insulated circuit board. | |
WO2021033421A1 (en) | Copper/ceramic assembly, insulated circuit board, method for producing copper/ceramic assembly, and method for producing insulated circuit board | |
WO2019088222A1 (en) | Joint body and insulating circuit substrate | |
JP7136212B2 (en) | COPPER/CERAMIC JOINT, INSULATED CIRCUIT BOARD, METHOD FOR MANUFACTURING COPPER/CERAMIC JOINT, AND METHOD FOR MANUFACTURING INSULATED CIRCUIT BOARD | |
JP2015209356A (en) | Method for manufacturing joined body and method for producing substrate for power module | |
WO2021085451A1 (en) | Copper/ceramic assembly, insulated circuit board, method for producing copper/ceramic assembly, and method for producing insulated circuit board | |
JP5828352B2 (en) | Copper / ceramic bonding body and power module substrate | |
WO2021044844A1 (en) | Copper/ceramic joined body and insulative circuit board | |
TWI813593B (en) | Bonded body and insulated circuit substrate | |
JP5825380B2 (en) | Copper / ceramic bonding body and power module substrate | |
JP6928297B2 (en) | Copper / ceramic joints and insulated circuit boards | |
TWI801652B (en) | Copper/ceramic bonded body, insulated circuit board, method for producing copper/ceramic bonded body, and method for producing insulated circuit board | |
WO2021117327A1 (en) | Copper/ceramic assembly and insulated circuit board |