JP4115369B2 - Ni-base superalloy - Google Patents
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- JP4115369B2 JP4115369B2 JP2003330302A JP2003330302A JP4115369B2 JP 4115369 B2 JP4115369 B2 JP 4115369B2 JP 2003330302 A JP2003330302 A JP 2003330302A JP 2003330302 A JP2003330302 A JP 2003330302A JP 4115369 B2 JP4115369 B2 JP 4115369B2
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- 229910000601 superalloy Inorganic materials 0.000 title claims description 20
- 229910045601 alloy Inorganic materials 0.000 claims description 26
- 239000000956 alloy Substances 0.000 claims description 26
- 239000013078 crystal Substances 0.000 claims description 12
- 238000000034 method Methods 0.000 claims description 10
- 239000000203 mixture Substances 0.000 claims description 5
- 238000007711 solidification Methods 0.000 claims description 4
- 230000008023 solidification Effects 0.000 claims description 4
- 238000005266 casting Methods 0.000 claims description 3
- 238000005242 forging Methods 0.000 claims description 2
- 239000012535 impurity Substances 0.000 claims description 2
- 238000004663 powder metallurgy Methods 0.000 claims description 2
- 230000000694 effects Effects 0.000 description 13
- 230000015572 biosynthetic process Effects 0.000 description 11
- 230000032683 aging Effects 0.000 description 9
- 230000003647 oxidation Effects 0.000 description 9
- 238000007254 oxidation reaction Methods 0.000 description 9
- 101000912561 Bos taurus Fibrinogen gamma-B chain Proteins 0.000 description 3
- 230000035882 stress Effects 0.000 description 3
- 229910000995 CMSX-10 Inorganic materials 0.000 description 2
- 229910001012 TMS-138 Inorganic materials 0.000 description 2
- 230000007774 longterm Effects 0.000 description 2
- 229910000521 B alloy Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
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この出願の発明は、Ｎｉ基超合金に関するものであり、さらに詳しくは、高温での組織安定性とクリープ特性に優れ、ジェットエンジンやガスタービンなどのタービンブレードやタービンベーン、タービンディスク等の高温、高応力下で使用される部材として好適な、新しいＮｉ基超合金に関するものである。 The invention of this application relates to a Ni-base superalloy, and more specifically, excellent in structural stability and creep characteristics at high temperatures, high temperatures of turbine blades such as jet engines and gas turbines, turbine vanes, and turbine disks, The present invention relates to a new Ni-base superalloy suitable as a member used under high stress.
従来、Ｎｉ基超合金としては、ＣＭＳＸ−１０（質量％で、Ｃｏ：３．３、Ｃｒ：２．４、Ｍｏ：０．４、Ｗ：５．３、Ａｌ：５．７、Ｔｉ：０．２、Ｎｂ：０．１、Ｔａ：８．２、Ｈｆ：０．０３、Ｒｅ：６．３で残部がＮｉからなる合金）（特許文献１）、ＴＭＳ−１３８（質量％で、Ｃｏ：５．８、Ｃｒ：２．８、Ｍｏ：２．９、Ｗ：６．１、Ａｌ：５．８、Ｔａ：５．６、Ｈｆ：０．０５、Ｒｅ：５．１、Ｒｕ：１．９で残部がＮｉからなる合金）（特許文献２）などが高温強度に最も優れたものとして知られている。 Conventionally, as Ni-base superalloy, CMSX-10 (in mass%, Co: 3.3, Cr: 2.4, Mo: 0.4, W: 5.3, Al: 5.7, Ti: 0 .2, Nb: 0.1, Ta: 8.2, Hf: 0.03, Re: 6.3 and the balance of Ni (Patent Document 1), TMS-138 ( mass%, Co: 5.8, Cr: 2.8, Mo: 2.9, W: 6.1, Al: 5.8, Ta: 5.6, Hf: 0.05, Re: 5.1, Ru: 1. No. 9 (alloy made of Ni as the balance) (Patent Document 2) is known as the most excellent high-temperature strength.
これら従来のＮｉ基超合金は、単結晶合金部材として１１００℃までのクリープ強度の点で優れている。しかしながら、多量のＲｅを含有するため長時間のクリープに際して、ＴＣＰ相と呼ばれる有害結晶を生成しやすいという欠点があった。ジェットエンジンやガスタービンの長時間の信頼性を高めるためには合金の組織の安定性を高めることが重要であるので、このような観点から、Ｒｅを含まずに、従来のＮｉ基超合金と同等あるいはそれ以上のクリープ強度を有するＮｉ基超合金の実現が望まれていた。
この出願の発明は以上のとおりの背景を踏まえてなされたものであって、Ｒｅを含有せずに、ジェットエンジンやガスタービンのタービンブレードやタービンベーンなどの高温部材として長時間にわたり組織安定な、新しい高強度Ｎｉ基超合金を提供することを課題としている。 The invention of this application was made based on the background as described above, and does not contain Re, and is stable in structure as a high-temperature member such as a turbine blade or turbine vane of a jet engine or a gas turbine for a long time. It is an object to provide a new high-strength Ni-base superalloy.
この出願の発明は、上記の課題を解決するためのものとして、第１には、質量％として、Ｃｒ：０．１〜２０、Ｍｏ：０．１〜１０、Ｗ：０．１〜１５、Ａｌ：２−１０、Ｔａ：０．１〜１６、Ｒｕ：０．１〜１０を含有し、残部がＮｉと不可避的不純物からなる組成を有することを特徴とするＮｉ基超合金を提供する。 The invention of this application is for solving the above-mentioned problems. First, as mass%, Cr: 0.1-20 , Mo: 0.1-10 , W: 0.1-15 , Provided is a Ni-base superalloy characterized by containing Al: 2-10 , Ta : 0.1-16 , Ru: 0.1-10 , and the balance of Ni and inevitable impurities.
第２には、上記の合金においてさらに、質量％でＣｏ：０．１〜２０を含有することを特徴とするＮｉ基超合金を提供する。 Second, there is provided a Ni-base superalloy characterized in that the alloy further contains Co: 0.1 to 20 by mass% .
第３には、これらの合金を用いて、普通鋳造法、一方向凝固法、あるいは単結晶凝固法により作成したことを特徴とするタービンブレードあるいはタービンベーン部品を提供する。 Third, by using these alloys, conventional casting methods, unidirectional solidification process, or to provide a turbine blade or turbine vane component, characterized in that created by a single crystal solidification method.
第４には、粉末冶金法あるいは鍛造法により作成したことを特徴とするタービンディスク部品を提供する。 Fourthly, a turbine disk component produced by a powder metallurgy method or a forging method is provided.
この出願の第１の発明によれば、長時間にわたり組織安定でクリープ強度の優れたＮｉ基超合金を得ることができる。 According to the first invention of this application, it is possible to obtain a Ni-base superalloy having a stable structure over a long period of time and an excellent creep strength.
また、上記第２の発明は、さらにＣｏを含有させて中低温側でのクリープ強度を向上させる効果を有する。 Further, the second invention has an effect of further improving the creep strength on the medium / low temperature side by containing Co.
第３の発明では、新しいＮｉ基超合金によるタービンブレード、タービンベーンをジェットエンジンやガスタービンに用いることによって、それらの長時間使用が可能となり信頼性などが向上する。 In the third invention, by using a turbine blade and a turbine vane made of a new Ni-base superalloy for a jet engine or a gas turbine, they can be used for a long time, and reliability and the like are improved.
第４の発明では、新しいＮｉ基超合金によるタービンディスクをジェットエンジンやガスタービンに用いることによって、それらの長時間信頼性などが向上する。 In the fourth invention, by using a turbine disk made of a new Ni-base superalloy for a jet engine or a gas turbine, their long-term reliability is improved.
この出願の発明は、上記のとおりの特徴をもつものであるが、以下にその実施の形態について説明する。 The invention of this application has the features as described above, and an embodiment thereof will be described below.
この出願の発明においては、後述実施例に述べるように、従来、高強度Ｎｉ基超合金に必須と考えられてきたＲｅを添加することなく高いクリープ強度を実現したことを特徴としている。その組成について説明すると以下のとおりである。 The invention of this application is characterized in that a high creep strength has been realized without adding Re, which has been considered essential for high-strength Ni-base superalloys, as will be described later in the examples. The composition will be described as follows.
この出願の発明のＮｉ基超合金においては、Ｃｏは中低温のクリープ強度を向上させる有効な元素である。しかし添加量が２０質量％を超えるとＴＣＰ相とよばれる有害結晶を生成して、クリープ強度が低下する。また、０．１質量％以上とすることが好ましい。 In the Ni-base superalloy of the invention of this application, Co is an effective element that improves the creep strength at medium and low temperatures. However, when the addition amount exceeds 20% by mass, harmful crystals called TCP phase are generated, and the creep strength is lowered. Moreover, it is preferable to set it as 0.1 mass % or more.
Ｃｒは耐酸化性と耐高温腐食性を向上させる有効な元素として必要である。しかし添加量が２０質量％を超えるとＴＣＰ相とよばれる有害結晶を生成して、クリープ強度が低下する。また、０．１質量％以上とすることが好ましい。 Cr is necessary as an effective element for improving oxidation resistance and hot corrosion resistance. However, when the addition amount exceeds 20% by mass, harmful crystals called TCP phase are generated, and the creep strength is lowered. Moreover, it is preferable to set it as 0.1 mass % or more.
Ｍｏは格子定数ミスフィットを負に移行させて、ガンマ相とガンマ’相の界面に緻密な転位網を形成させ、高温のクリープ強度を向上させる有効な元素として必要である。しかし添加量が１０質量％を超えるとＴＣＰ相とよばれる有害結晶を生成して、クリープ強度が低下する。また、０．１質量％以上とすることが好ましい。 Mo is necessary as an effective element for shifting the lattice constant misfit to a negative value, forming a dense dislocation network at the interface between the gamma phase and the gamma ′ phase, and improving the high-temperature creep strength. However, when the addition amount exceeds 10% by mass, harmful crystals called TCP phases are generated, and the creep strength is lowered. Moreover, it is preferable to set it as 0.1 mass % or more.
Ｗは高温から低温までのクリープ強度を向上させる効果があるので、合金に添加することが必要である。しかし添加量が１５質量％を超えると有害相の生成を助長するのでこれ以下とする必要がある。また、０．１質量％以上とすることが好ましい。 Since W has the effect of improving the creep strength from high temperature to low temperature, it must be added to the alloy. However, if the added amount exceeds 15% by mass, the formation of a harmful phase is promoted, so it is necessary to make it less than this. Moreover, it is preferable to set it as 0.1 mass % or more.
Ａｌは高温強度向上に不可欠なガンマ’相を形成させるために２質量％以上必要である。しかし１０質量％を超えると共晶ガンマ’と呼ばれる粗大な結晶が生成しクリープ強度が低下する。よって２−１０質量％とすることが必要である。より好ましくは４−８質量％である。 Al needs to be 2% by mass or more in order to form a gamma ′ phase indispensable for improving high-temperature strength. However, if it exceeds 10% by mass, coarse crystals called eutectic gamma 'are formed and the creep strength is lowered. Therefore, it is necessary to set it as 2-10 mass %. More preferably, it is 4-8 mass %.
Ｔａは、ガンマ’相を強化してクリープ強度を向上させる有効な元素である。したがって添加が必要である。１６質量％以上になると有害相の生成が助長されるので、１６質量％以下である必要がある。また、０．１質量％以上とすることが好ましい。 Ta is an element effective for improving the creep strength by strengthening the gamma prime phase. Addition is therefore necessary. Since the production | generation of a harmful phase will be encouraged when it becomes 16 mass % or more, it needs to be 16 mass % or less. Moreover, it is preferable to set it as 0.1 mass % or more.
Ｒｕは低温側のクリープ強度を向上させるために必須の元素である。しかし添加量が１０質量を超えると有害相の生成が助長されるので、１０質量以下でなくてはならない。また、このＲｕの添加については、０．１質量以上とすることが好ましい。 Ru is an essential element for improving the creep strength on the low temperature side. However, if the addition amount exceeds 10 masses , the formation of a harmful phase is promoted, so it must be 10 masses or less. The addition of Ru is preferably 0.1 mass or more.
Ｈｆは耐酸化性を向上させる効果があるので、合金に添加することが有効である。しかし添加量が１０質量％を超えると有害相の生成を助長するのでこれ以下とする必要がある。好ましくは８質量％以下である。 Since Hf has the effect of improving the oxidation resistance, it is effective to add it to the alloy. However, if the addition amount exceeds 10% by mass, the formation of a harmful phase is promoted, so it is necessary to make it less than this. Preferably it is 8 mass % or less.
Ｐｔは組織安定性を向上させ有害相生成を防ぐ効果があるので、合金に添加することが有効である。しかし添加量が１０質量％を超えると有害相の生成を助長するのでこれ以下とする必要がある。 Since Pt has the effect of improving the structural stability and preventing the formation of harmful phases, it is effective to add it to the alloy. However, if the addition amount exceeds 10% by mass, the formation of a harmful phase is promoted, so it is necessary to make it less than this.
Ｒｈも組織安定性を向上させ有害相生成を防ぐ効果があるので、合金に添加することが有効である。しかし添加量が１０質量％を超えると有害相の生成を助長するのでこれ以下とする必要がある。 Since Rh also has the effect of improving the structural stability and preventing the formation of harmful phases, it is effective to add it to the alloy. However, if the addition amount exceeds 10% by mass, the formation of a harmful phase is promoted, so it is necessary to make it less than this.
Ｖは低温側のクリープ強度を向上させる効果があるので、合金に添加することが有効である。しかし添加量が３質量％を超えると有害相の生成を助長するのでこれ以下とする必要がある。好ましくは２質量％以下である。 V has the effect of improving the creep strength on the low temperature side, so it is effective to add it to the alloy. However, if the added amount exceeds 3% by mass, the formation of a harmful phase is promoted, so it is necessary to make it less than this. Preferably it is 2 mass % or less.
Ｚｒは結晶粒界強度を向上させる効果があるので、合金に添加することが有効である。しかし添加量が３質量％を超えると有害相の生成を助長するのでこれ以下とする必要がある。好ましくは２質量％以下である。 Since Zr has the effect of improving the grain boundary strength, it is effective to add it to the alloy. However, if the added amount exceeds 3% by mass, the formation of a harmful phase is promoted, so it is necessary to make it less than this. Preferably it is 2 mass % or less.
Ｓｉは耐酸化性を向上させる効果があるので、合金に添加することが有効である。しかし添加量が３質量％を超えると有害相の生成を助長するのでこれ以下とする必要がある。好ましくは２質量％以下である。 Since Si has the effect of improving oxidation resistance, it is effective to add it to the alloy. However, if the added amount exceeds 3% by mass, the formation of a harmful phase is promoted, so it is necessary to make it less than this. Preferably it is 2 mass % or less.
Ｆｅは低温側のクリープ強度を向上させる効果があるので、合金に添加することが有効である。しかし添加量が１０質量％を超えると有害相の生成を助長するのでこれ以下とする必要がある。 Since Fe has the effect of improving the creep strength on the low temperature side, it is effective to add it to the alloy. However, if the addition amount exceeds 10% by mass, the formation of a harmful phase is promoted, so it is necessary to make it less than this.
Ｃは炭化物を結晶粒界に生成させクリープ強度を向上させる効果があるので、合金に添加することが有効である。しかし添加量が０．３質量％を超えると炭化物量が過多となり合金が脆化するのでこれ以下とする必要がある。 Since C has the effect of generating carbides at the grain boundaries and improving the creep strength, it is effective to add C to the alloy. However, if the added amount exceeds 0.3% by mass, the amount of carbide becomes excessive and the alloy becomes brittle, so it is necessary to make it less than this.
Ｂは結晶粒界に偏析して強度を向上させる効果があるので、合金に添加することが有効である。しかし添加量が０．２質量％を超えると融点の低下を招くのでこれ以下とする必要がある。 Since B has the effect of segregating at the grain boundaries to improve the strength, it is effective to add B to the alloy. However, if the added amount exceeds 0.2% by mass , the melting point is lowered, so it is necessary to make it less than this.
Ｙは耐酸化性を向上させる効果があるので、添加することが有効である。しかし添加量が０．２質量％を超えるとかえって耐酸化性を低下させるのでこれ以下とする必要がある。 Since Y has an effect of improving oxidation resistance, it is effective to add it. However, if the added amount exceeds 0.2% by mass, the oxidation resistance is lowered, so it is necessary to make it less than this.
Ｌａは耐酸化性を向上させる効果があるので、添加することが有効である。しかし添加量が０．２質量％を超えるとかえって耐酸化性を低下させるのでこれ以下とする必要がある。 Since La has an effect of improving the oxidation resistance, it is effective to add it. However, if the added amount exceeds 0.2% by mass, the oxidation resistance is lowered, so it is necessary to make it less than this.
Ｃｅは耐酸化性を向上させる効果があるので、添加することが有効である。しかし添加量が０．２質量％を超えるとかえって耐酸化性を低下させるのでこれ以下とする必要がある。 Ce is effective to improve oxidation resistance, so it is effective to add it. However, if the added amount exceeds 0.2% by mass, the oxidation resistance is lowered, so it is necessary to make it less than this.
以上のような組成の特徴を有するこの出願の発明のＮｉ基超合金については、たとえば単結晶として鋳造し、溶体化処理、時効処理を行うことによって製造することができる。一方向凝固合金としてもよい。 The Ni-base superalloy of the invention of this application having the characteristics of the composition as described above can be manufactured, for example, by casting as a single crystal and performing solution treatment and aging treatment. A unidirectionally solidified alloy may be used.
たとえば溶体化処理については、１２００℃〜１３５０℃の範囲において、時効処理については、１０００℃以上での１次時効と、９５０℃以下での２次時効との多段階処理が好適なものとして考慮される。 For example, regarding the solution treatment, in the range of 1200 ° C. to 1350 ° C., regarding the aging treatment, it is considered that multi-step treatment of primary aging at 1000 ° C. or higher and secondary aging at 950 ° C. or lower is preferable. Is done.
以下に実施例を示し、さらに詳しく説明する。もちろん以下の例によって発明が限定されることはない。 Hereinafter, examples will be shown and described in more detail. Of course, the invention is not limited by the following examples.
Ｎｉ基超合金（実施例Ａ組成（質量％）：５．７Ｃｒ、１．０Ｍｏ、１２．５Ｗ、４．７Ａｌ、７．４Ｔａ、２．０Ｒｕ、残Ｎｉ、実施例Ｂ組成（質量％：７．９Ｃｏ、５．０Ｃｒ、２．８Ｍｏ、１１．１Ｗ、４．９Ａｌ、７．８Ｔａ、２．５Ｒｕ、残Ｎｉ）を単結晶に鋳造し、溶体化処理及び時効処理を行った。溶体化処理は、１２７０℃で１時間保持した後、１３００℃まで昇温し、５時間保持した。また時効処理は１１００℃で４時間保持する１次時効と、８７０℃で２０時間保持する２次時効処理を行った。 Ni-base superalloy (Example A composition (mass%) : 5.7Cr, 1.0Mo, 12.5W, 4.7Al, 7.4Ta, 2.0Ru, residual Ni, Example B composition (mass% : 7 .9Co, 5.0Cr, 2.8Mo, 11.1W, 4.9Al, 7.8Ta, 2.5Ru, and remaining Ni) were cast into a single crystal and subjected to solution treatment and aging treatment. Was held at 1270 ° C. for 1 hour, then heated to 1300 ° C. and held for 5 hours, and the aging treatment was a primary aging treatment held at 1100 ° C. for 4 hours and a secondary aging treatment held at 870 ° C. for 20 hours. Went.
次に、溶体化処理及び時効処理を施した本実施例の試料に対してクリープ強度を測定した。クリープ試験は温度１１００℃、応力１３７ＭＰａの条件で試料がクリープ破断するまでの時間を寿命とした。 Next, the creep strength was measured for the sample of this example that had undergone solution treatment and aging treatment. In the creep test, the time until the sample creep ruptured under the conditions of a temperature of 1100 ° C. and a stress of 137 MPa was defined as the lifetime.
実施例Ａ合金とＢ合金のクリープ試験結果と従来技術の合金とを比較し、その結果を図１に示した。なお、図１では機器設計で重要な値である１％クリープひずみ到達時間を示している。図１から明らかなように、本発明合金は第３世代Ｎｉ基単結晶合金といわれる比較例ＣＭＳＸ−１０及び第４世代Ｎｉ基単結晶合金ＴＭＳ−１３８に比べ高いクリープ強度を有していることがわかる。 The creep test results of Example A and B alloys were compared with the prior art alloys, and the results are shown in FIG. FIG. 1 shows the 1% creep strain arrival time, which is an important value in equipment design. As is apparent from FIG. 1, the alloy of the present invention has a higher creep strength than the comparative example CMSX-10 and the fourth generation Ni-based single crystal alloy TMS-138, which are called third-generation Ni-based single crystal alloys. I understand.
この出願の発明によって、高温での組織安定性とクリープ特性に優れ、ジェットエンジンやガスタービンなどのタービンブレードやタービンベーン、タービンディスクなどの高温、高応力下で使用される部材として好適な、新しいＮｉ基超合金が提供されることになる。 By the invention of this application, the structure stability and creep characteristics at high temperature are excellent, and it is suitable as a member used under high temperature and high stress such as turbine blades, turbine vanes, turbine disks, etc. of jet engines and gas turbines. A Ni-base superalloy will be provided.
Claims (4)
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2003330302A JP4115369B2 (en) | 2003-09-22 | 2003-09-22 | Ni-base superalloy |
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| JP2003330302A JP4115369B2 (en) | 2003-09-22 | 2003-09-22 | Ni-base superalloy |
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| JP2005097650A JP2005097650A (en) | 2005-04-14 |
| JP4115369B2 true JP4115369B2 (en) | 2008-07-09 |
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Cited By (3)
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| US7788622B2 (en) | 2003-11-21 | 2010-08-31 | Mentor Graphics Corporation | Distributed autorouting of conductive paths |
| US7949990B2 (en) | 2001-12-10 | 2011-05-24 | Mentor Graphics Corporation | Parallel electronic design automation: shared simultaneous editing |
| US8326926B2 (en) | 2005-09-13 | 2012-12-04 | Mentor Graphics Corporation | Distributed electronic design automation architecture |
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| JP5344453B2 (en) * | 2005-09-27 | 2013-11-20 | 独立行政法人物質・材料研究機構 | Ni-base superalloy with excellent oxidation resistance |
| JP4841931B2 (en) * | 2005-10-25 | 2011-12-21 | 財団法人電力中央研究所 | Method for improving oxidation resistance of heat-resistant metal material and method for producing heat-resistant metal member |
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| US20120279351A1 (en) * | 2009-11-19 | 2012-11-08 | National Institute For Materials Science | Heat-resistant superalloy |
| JP5427642B2 (en) * | 2010-02-24 | 2014-02-26 | 株式会社日立製作所 | Nickel-based alloy and land gas turbine parts using the same |
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| JP6016016B2 (en) * | 2012-08-09 | 2016-10-26 | 国立研究開発法人物質・材料研究機構 | Ni-based single crystal superalloy |
| EP2876176B1 (en) * | 2013-11-25 | 2017-06-21 | Mitsubishi Hitachi Power Systems, Ltd. | Ni-based casting superalloy and cast article therefrom |
| JP6803573B2 (en) * | 2016-03-07 | 2020-12-23 | 国立研究開発法人物質・材料研究機構 | Ni-based unidirectional solidified alloy |
| GB2554898B (en) | 2016-10-12 | 2018-10-03 | Univ Oxford Innovation Ltd | A Nickel-based alloy |
| DE102016221470A1 (en) * | 2016-11-02 | 2018-05-03 | Siemens Aktiengesellschaft | Superalloy without titanium, powder, process and component |
| CN110983111A (en) * | 2019-12-31 | 2020-04-10 | 江苏新华合金有限公司 | Nickel-based high-temperature alloy plate and preparation method thereof |
| CN114032420B (en) * | 2021-11-10 | 2023-03-14 | 中国航发北京航空材料研究院 | High-performance cast high-temperature alloy |
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2003
- 2003-09-22 JP JP2003330302A patent/JP4115369B2/en not_active Expired - Lifetime
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US7949990B2 (en) | 2001-12-10 | 2011-05-24 | Mentor Graphics Corporation | Parallel electronic design automation: shared simultaneous editing |
| US7788622B2 (en) | 2003-11-21 | 2010-08-31 | Mentor Graphics Corporation | Distributed autorouting of conductive paths |
| US8326926B2 (en) | 2005-09-13 | 2012-12-04 | Mentor Graphics Corporation | Distributed electronic design automation architecture |
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|---|---|
| JP2005097650A (en) | 2005-04-14 |
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