EP0575190B1 - Weichmagnetische Legierung auf Eisenbasis und Herstellungsverfahren - Google Patents

Weichmagnetische Legierung auf Eisenbasis und Herstellungsverfahren Download PDF

Info

Publication number
EP0575190B1
EP0575190B1 EP93304762A EP93304762A EP0575190B1 EP 0575190 B1 EP0575190 B1 EP 0575190B1 EP 93304762 A EP93304762 A EP 93304762A EP 93304762 A EP93304762 A EP 93304762A EP 0575190 B1 EP0575190 B1 EP 0575190B1
Authority
EP
European Patent Office
Prior art keywords
alloy
soft magnetic
atomic
magnetic
present
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
Application number
EP93304762A
Other languages
English (en)
French (fr)
Other versions
EP0575190A2 (de
EP0575190A3 (de
Inventor
Hiroshi c/o Mitsui Petrochem. Ind. Ltd. Watanabe
Yoshihiko c/o Mitsui Petrochem. Ind. Ltd. Hirota
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
IDEM
Original Assignee
Mitsui Petrochemical Industries Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Mitsui Petrochemical Industries Ltd filed Critical Mitsui Petrochemical Industries Ltd
Publication of EP0575190A2 publication Critical patent/EP0575190A2/de
Publication of EP0575190A3 publication Critical patent/EP0575190A3/de
Application granted granted Critical
Publication of EP0575190B1 publication Critical patent/EP0575190B1/de
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C45/00—Amorphous alloys
    • C22C45/02—Amorphous alloys with iron as the major constituent
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
    • H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/153—Amorphous metallic alloys, e.g. glassy metals
    • H01F1/15308—Amorphous metallic alloys, e.g. glassy metals based on Fe/Ni

Definitions

  • the present invention relates to an Fe-based soft magnetic alloy and, in particular, to an alloy having excellent soft magnetic properties and a process for making it.
  • Fe-based amorphous magnetic alloys having a high saturation magnetic flux density are known to be used as magnetic core materials for magnetic heads, high frequency transformers, saturable reactors, choke coils, etc.
  • Fe-based amorphous magnetic alloys are lower priced than Co-based ones, the former have the drawbacks of large core loss in the high frequency region and low permeability.
  • it's saturation magnetostriction is high.
  • An Fe-B system alloy is known as a conventional Fe-system amorphous magnetic alloy.
  • the alloys including B (boron) are highly priced because the element B is expensive.
  • One object of the present invention is to provide a novel Fe-based soft magnetic alloy, which can be substituted for the above-mentioned conventional soft magnetic materials and has a low saturation magnetostriction and a low iron loss.
  • Another object of the present invention is to provide an Fe-based soft magnetic alloy which is lower priced.
  • an Fe-based soft magnetic alloy which has a composition represented by the formula: Fe 100-a-b-c-d P a M b M' c Cu d where M is at least one element selected from the group consisting of Zr, Hf, Nb, Mo, W, Ta, Ti, V, Cr, Mn, Y and Ce;
  • P phosphorous
  • a determined amount of P enables the extension of the range of formation of amorphous alloys after quenching without using an expensive element B (boron). Thereby, the cost of preparation of the alloy can be reduced.
  • the content (a) of P is more than 0 atomic % and not more than 25 atomic %, preferably from 1 to 15 atomic %, more preferably from 2 to 12 atomic %.
  • the element(s) M added to the Fe-based soft magnetic alloy of the present invention is supposed to prevent crystallization of the Fe-P system crystal which hampers the soft magnetic properties of the alloy or to elevate its crystallization temperature.
  • M is at least one, i.e. one or more of the elements selected from the group consisting of Zr, Hf, Nb, Mo, W, Ta, Ti, V, Cr, Mn, Y and Ce. Particularly Zr is preferable. Addition of the element(s) M is further effective for making the crystal grain fine and for improving the ability of forming the amorphous phase of the alloy in the Fe-P system alloy.
  • the content (b) of the M element(s) is more than 0 atomic % and not more than 15 atomic %, preferably from 2 to 15 atomic %, more preferably from 3 to 12 atomic %.
  • the element(s) M' added to the Fe-based soft magnetic alloy of the pr-esent invention is one or more of the elements selected from the group consisting of Si, Al, Ga, Ge, Ru, Co, Ni,Sn, Sb and Pd. It is considered that these elements are dissolved in the Fe-based solid solution because they have a negative interaction parameter relative to Fe, that is, it is considered that the elements are described as being substituted for Fe atom in the ⁇ -Fe crystalline structure whereby stabilizing the bcc crystal. Thus, it is considered that the crystalline grain having a genuine magnetocrystalline anisotropy of bcc crystalline or low magnetostriction constant is formed to exhibit excellent soft magnetic properties.
  • the content (c) of the M' element(s) is from 0 atomic % to 20 atomic %, preferably from 1 to 15 atomic %.
  • Cu (copper) in the alloy of the present invention is effective for making the crystalline particles obtained by the heat-treatment of the amorphous fine. Further, it improves the magnetic properties of the alloy since the effective magnetic anisotropy energy becomes smaller than its genuine magnetocrystalline anisotropy energy as the particles become fine.
  • the copper content should not be more than 5 atomic % with respect to the preparation of the alloy because the just quenched alloy tends to be brittle. Accordingly, the content (d) of Cu is from 0 to 5 atomic %, preferably from 0.5 to 3 atomic %.
  • alloy further containing inevitable impurities such as N, S, O etc., to the extent that these elements do not deteriorate the properties of the alloy, is also included in the scope of the present invention .
  • the Fe-based soft magnetic alloy according to the present invention has an alloy structure, at least 30 % (30 % - 100 %) of which consists of (is composed of) fine crystalline particles, with the balance of the structure being an amorphous phase or other crystals than above-mentioned fine crystalline particles.
  • the range of the ratio of the fine crystalline particles in the structure provides the alloy with excellent (soft) magnetic properties.
  • the alloy retains sufficiently good magnetic properties.
  • at least 50 %, more preferably 70 % or more of the alloy structure consists of (is composed of) the fine crystalline particles in view of magnetic properties.
  • the crystalline particles of the alloy of the present invention has mainly a bcc structure and it is considered that Fe is the main component in which M, M' and a small amount of P are believed to be dissolved.
  • the crystalline particles to be formed in the alloy of the present invention have a particle size of 1000 ⁇ or less, preferably 500 ⁇ or less, more preferably 50 to 300 ⁇ .
  • the particle size being 1000 ⁇ or less, preferably 500 ⁇ or less, more preferably 50 to 300 ⁇ , provides the alloy of the present invention having excellent magnetic properties.
  • Preferred Fe-based soft magnetic alloys of the present invention have a saturation magnetostriction ( ⁇ S) in the range of +10x10 -6 to -5x10 -6 .
  • the proportion of the crystalline grains to the total alloy structure in the alloy of the present invention may be determined experimentally by an X-ray diffraction method or the like. Briefly, on the basis of the standard value of the X-ray diffraction intensity of Fe-based crystal in the completely crystallized condition (saturated X-ray diffraction intensity condition), the proportion of the X-ray diffraction intensity of the magnetic alloy material sample to be examined to the standard value may be obtained experimentally.
  • the Fe-based soft magnetic alloy of the present invention may be produced by a heat-treatment of an amorphous metal having a determined shape which is obtained by a common method of forming an amorphous metal.
  • an amorphous alloy is first formed in the form of a ribbon, powder, fiber, or thin film by a melt quenching method such as a single roll method or double roll method, a thin film forming method such as a cavitation method, sputtering method or vapor deposition method, or a powder forming method such as mechanical alloying or the like.
  • the resulting amorphous alloy is optionally shaped and worked into a desired shape, then it is heat-treated so that at least a part, preferably 30 % or more of the whole, of the sample is crystallized to obtain the alloy of the present invention.
  • the structure of the alloy after rapid-quenching is preferably amorphous but it may include partial crystalization to the extent that the resulting alloy exhibits soft magnetic properties after heat-treatment.
  • a quenched alloy ribbon is formed by a single roll method, and this is shaped into a determined shape such as a coiled magnetic core and then heat-treated.
  • the heat-treatment is effected in vacuum, in an inert gas atmosphere, such as an argon gas or nitrogen gas atmosphere, in a reducing gas atmosphere such as H 2 or in an oxidizing gas atmosphere such as air.
  • the heat-treatment temperature is approximately from 200 to 800°C, preferably approximately from 300 to 700°C, preferably from 350 to 700°C and more preferably from 400 to 700 °C.
  • the heat-treatment time is within 24 hours, preferably about from 0.5 to 5 hours.
  • the heat-treatment may be effected either in the absence or presence of a magnetic field. Impressing of a magnetic field brings a magnetic anisotropy to the alloy.
  • Fig. 1 is a graph showing X-ray diffraction patterns of the Fe-base soft magnetic alloy of the present invention after heat-treatment.
  • a quenched ribbon (thin film) sample having a width of about 1.5 mm and a thickness of about 15-24 ⁇ m was formed from a melt containing Fe, P, Zr, and (Cu) in an argon gas atmosphere of one atmosphere pressure by a single roll method.
  • the sample was then heat-treated at the temperature shown by Table 1 for about one hour in the presence of a nitrogen gas and in the absence of a magnetic field.
  • the iron loss (Pc W/kg) of each of the samples was determined under the condition of a frequency of 100 kHz and a maximum magnetic flux density of 0.1 T.
  • the permeability ( ⁇ ) (1KHz) under the condition of a frequency of 1 kHz and a maximum exciting magnetic field of 5 mOe, the saturation magnetization Ms (emu/g) and the saturation magnetostriction constant ⁇ s ( ⁇ 10 -6 ) of each samples were also determined.
  • the composition of the alloy samples, the content of the fine crystalline particles in the alloy and the average particle size are shown in Table 1 below.
  • the content of the fine crystalline particles is 60 % or more in all of the samples.
  • the composition of the alloy was determined by IPC analysis.
  • Fig. 1 shows the X-ray diffraction curves of the alloy of Fe 88 Zr 9 P 2 Cu 1 (atomic %)(Example 3) obtained by heat-treating the quenched alloy formed by a single roll method, at 620 °C in the presense of argon for one hour.
  • the structure of the alloy obtained by heat-treatment has mainly bcc structure.
  • the Fe-based soft magnetic alloy of the present invention shows an excellent magnetic properties such as low ion loss, high permeability and low saturation magnetostriction by adding specific element(s), particularly Zr together with Cu to Fe-P system alloy. Accordingly, the alloy of the present invention can be utilized widely for a magnetic head, high-frequency transformers, saturable reactors, choke coils and like as the magnetic material substitited for the Fe-B system soft magnetic alloy.
  • the Fe-based soft magnetic alloy of the present invention can be prepared at a reduced cost since it utilizes phosphorous P instead of boron B.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Power Engineering (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Electromagnetism (AREA)
  • Dispersion Chemistry (AREA)
  • Soft Magnetic Materials (AREA)
  • Powder Metallurgy (AREA)

Claims (9)

  1. Weichmagnetische Legierung auf Fe-Basis mit einer Zusammensetzung der Formel: Fe 100-a-b-c-d P a M b M' c Cu d ,
    Figure imgb0003
     in der M mindestens ein Element ist, ausgewählt aus Zr, Hf, Nb, Mo, W, Ta, Ti, V, Cr, Mn, Y und Ce, M' mindestens ein Element ist, ausgewählt aus Si, Al, Ga, Ge, Ru, Co, Ni, Sn, Sb und Pd, a, b, c und d jeweils Atom-% sind und den folgenden Beziehungen entsprechen: 0 < a ≤ 25, 0 < b ≤ 15, 0 ≤ c ≤ 20 und 0 ≤ d ≤ 5.
  2. Legierung nach Anspruch 1, wobei mindestens 30 % der Struktur der Legierung von feinen kristallinen Teilchen eingenommen werden.
  3. Legierung nach Anspruch 2, wobei die kristallinen Teilchen eine feste bbc-Lösung sind, enthaltend hauptsächlich Eisen.
  4. Legierung nach einem der Ansprüche 1 bis 3, wobei die mittlere Teilchengröße nicht mehr als 100 nm beträgt.
  5. Legierung nach einem der Ansprüche 1 bis 4, wobei die Sättigungsmagnetostriktion (λs) der Legierung +10 x 10-6 bis -5 x 10-6 ist.
  6. Verfahren zur Herstellung einer weichmagnetischen Legierung auf Fe-Basis, umfassend
       Bildung einer abgeschreckten Legierung mit einer Zusammensetzung der Formel Fe 100-a-b-c-d P a M b M' c Cu d ,
    Figure imgb0004
     in der M mindestens ein Element ist, ausgewählt aus Zr, Hf, Nb, Mo, W, Ta, Ti, V, Cr, Mn, Y und Ce, M' mindestens ein Element ist, ausgewählt aus Si, Al, Ga, Ge, Ru, Co, Ni, Sn, Sb und Pd, a, b, c und d jeweils Atom-% sind und den folgenden Beziehungen entsprechen: 0 < a ≤ 25, 0 < b ≤ 15, 0 ≤ c ≤ 20 und 0 ≤ d ≤ 5,
    durch ein Schmelz/Abschreck-Verfahren, ein Verfahren zur Erzeugung eines dünnen Films oder ein Verfahren zur Erzeugung eines Pulvers und Behandeln der abgeschreckten Legierung durch Wärme.
  7. Verfahren nach Anspruch 6, wobei die abgeschreckte Legierung während der Wärmebehandlung weniger als 24 Stunden bei einer Temperatur von 350 bis 700°C gehalten wird.
  8. Verfahren nach Anspruch 6 oder 7 zur Herstellung einer Legierung nach einem der Ansprüche 2 bis 5.
  9. Magnetischer Kern, bestehend.aus einer Legierung nach einem der Ansprüche 1 bis 5 oder hergestellt nach Anspruch 6 oder 7.
EP93304762A 1992-06-17 1993-06-17 Weichmagnetische Legierung auf Eisenbasis und Herstellungsverfahren Expired - Lifetime EP0575190B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP15833892A JP3623970B2 (ja) 1992-06-17 1992-06-17 Ｆｅ基軟磁性合金および製造方法
JP158338/92 1992-06-17

Publications (3)

Publication Number Publication Date
EP0575190A2 EP0575190A2 (de) 1993-12-22
EP0575190A3 EP0575190A3 (de) 1994-01-26
EP0575190B1 true EP0575190B1 (de) 1997-09-17

Family

ID=15669458

Family Applications (1)

Application Number Title Priority Date Filing Date
EP93304762A Expired - Lifetime EP0575190B1 (de) 1992-06-17 1993-06-17 Weichmagnetische Legierung auf Eisenbasis und Herstellungsverfahren

Country Status (5)

Country Link
EP (1) EP0575190B1 (de)
JP (1) JP3623970B2 (de)
KR (1) KR0131376B1 (de)
CA (1) CA2098532A1 (de)
DE (1) DE69313938T2 (de)

Families Citing this family (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE4444482A1 (de) * 1994-12-14 1996-06-27 Bosch Gmbh Robert Weichmagnetischer Werkstoff
KR100916602B1 (ko) * 2002-11-11 2009-09-11 엘지디스플레이 주식회사 소다라임 글라스를 이용한 액정표시장치와 그 제조방법
CN102360670B (zh) * 2011-10-24 2014-01-08 南京信息工程大学 一种铁氧体磁层非晶软磁芯复合材料及其制备方法
CN104962821B (zh) * 2015-05-26 2017-03-22 北京科技大学 一种针式打印机轭铁座零件的加工方法
JP7106919B2 (ja) * 2018-03-23 2022-07-27 Tdk株式会社 軟磁性薄膜、薄膜インダクタおよび磁性製品
JP7150011B2 (ja) 2018-04-10 2022-10-07 エルジー エナジー ソリューション リミテッド リン化鉄の製造方法、リン化鉄を含むリチウム二次電池用正極及びこれを備えたリチウム二次電池
KR102229460B1 (ko) * 2018-04-10 2021-03-18 주식회사 엘지화학 인화철(FeP)의 제조방법
WO2019198949A1 (ko) * 2018-04-10 2019-10-17 주식회사 엘지화학 인화철의 제조방법, 인화철을 포함하는 리튬 이차전지용 양극 및 이를 구비한 리튬 이차전지
DE102019105215A1 (de) * 2019-03-01 2020-09-03 Vacuumschmelze Gmbh & Co. Kg Legierung und Verfahren zur Herstellung eines Magnetkerns
KR20220038899A (ko) * 2020-09-21 2022-03-29 엘지전자 주식회사 합금 분말 및 이의 제조방법
CN112176222B (zh) * 2020-10-30 2021-12-17 东北大学 一种含Ce的Fe-Ni坡莫合金材料及其制备方法

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2713711B2 (ja) * 1987-11-17 1998-02-16 日立金属株式会社 防犯センサ用マーカ
JPH04272159A (ja) * 1991-01-08 1992-09-28 Sumitomo Metal Ind Ltd Ｆｅ基磁性合金

Also Published As

Publication number Publication date
KR0131376B1 (ko) 1998-04-24
EP0575190A2 (de) 1993-12-22
EP0575190A3 (de) 1994-01-26
JPH062076A (ja) 1994-01-11
DE69313938D1 (de) 1997-10-23
CA2098532A1 (en) 1993-12-18
KR940006157A (ko) 1994-03-23
DE69313938T2 (de) 1998-03-05
JP3623970B2 (ja) 2005-02-23

Similar Documents

Publication Publication Date Title
EP0271657B1 (de) Weichmagnetische Legierung auf Eisenbasis und Herstellungsverfahren
EP0574513B1 (de) VERFAHREN ZUR HERSTELLUNG VON WEICHMAGNETISCHEN LEGIERUNGEN AUF Fe-Ni BASIS MIT NANOKRISTALLINER STRUKTUR
EP2149616B1 (de) Weicher und dünner magnetstreifen, verfahren zu seiner herstellung, magnetische elemente und amorpher dünner streifen
JP5288226B2 (ja) 磁性合金、アモルファス合金薄帯、および磁性部品
EP0430085B1 (de) Magnetlegierung mit ultrakleinen Kristallkörnern und Herstellungsverfahren
JP5455040B2 (ja) 軟磁性合金、その製造方法、および磁性部品
EP0635853B1 (de) Nanokristalline Legierung mit Dämpfungskarakteristiken, Herstellungsverfahren desselben, Drosselspule, und Störfilter
EP2128291A1 (de) Magnetische legierung, band aus einer amorphen legierung und magnetisches element
GB1580498A (en) Metallic glasses having a combination of high permeability low magnetostriction low ac core loss and high thermal stability
EP0575190B1 (de) Weichmagnetische Legierung auf Eisenbasis und Herstellungsverfahren
JP3231149B2 (ja) ノイズフィルタ
EP0513385B1 (de) Weichmagnetlegierung auf eisen-basis
JP3655321B2 (ja) Ｆｅ基軟磁性合金粉末の製造方法
JPH07103453B2 (ja) 恒透磁率性に優れた合金およびその製造方法
EP0351051B1 (de) Weichmagnetische, auf Eisen basierende Legierung
JP3322407B2 (ja) Ｆｅ基軟磁性合金
JP3558350B2 (ja) Ｆｅ基軟磁性合金および製造方法
JPH0610105A (ja) Ｆｅ基軟磁性合金
JPH03271346A (ja) 軟磁性合金
JPH0641698A (ja) Ｆｅ基軟磁性合金
JPH05271885A (ja) 軟磁性合金薄膜およびその製造方法
JPH04341544A (ja) Ｆｅ基軟磁性合金
JPH04272159A (ja) Ｆｅ基磁性合金
JPH0238520A (ja) Ｆｅ基軟磁性合金の製法及び巻磁心
JPH0598402A (ja) 高透磁率を有するＦｅ基非晶質合金および鉄心の製造方法

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

PUAL Search report despatched

Free format text: ORIGINAL CODE: 0009013

AK Designated contracting states

Kind code of ref document: A2

Designated state(s): DE FR GB IT NL

AK Designated contracting states

Kind code of ref document: A3

Designated state(s): DE FR GB IT NL

17P Request for examination filed

Effective date: 19940711

GRAG Despatch of communication of intention to grant

Free format text: ORIGINAL CODE: EPIDOS AGRA

17Q First examination report despatched

Effective date: 19960910

GRAH Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOS IGRA

GRAH Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOS IGRA

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): DE FR GB IT NL

ET Fr: translation filed
REF Corresponds to:

Ref document number: 69313938

Country of ref document: DE

Date of ref document: 19971023

ITF It: translation for a ep patent filed

Owner name: ST. DR. CAVATTONI ING. A. RAIMONDI

RAP2 Party data changed (patent owner data changed or rights of a patent transferred)

Owner name: MITSUI CHEMICALS, INC.

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 19980608

Year of fee payment: 6

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 19980609

Year of fee payment: 6

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: NL

Payment date: 19980629

Year of fee payment: 6

Ref country code: DE

Payment date: 19980629

Year of fee payment: 6

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

NLT2 Nl: modifications (of names), taken from the european patent patent bulletin

Owner name: MITSUI CHEMICALS, INC.

26N No opposition filed
NLT1 Nl: modifications of names registered in virtue of documents presented to the patent office pursuant to art. 16 a, paragraph 1

Owner name: IDEM

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 19990617

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: THE PATENT HAS BEEN ANNULLED BY A DECISION OF A NATIONAL AUTHORITY

Effective date: 19990630

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20000101

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 19990617

NLV4 Nl: lapsed or anulled due to non-payment of the annual fee

Effective date: 20000101

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20000503

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES;WARNING: LAPSES OF ITALIAN PATENTS WITH EFFECTIVE DATE BEFORE 2007 MAY HAVE OCCURRED AT ANY TIME BEFORE 2007. THE CORRECT EFFECTIVE DATE MAY BE DIFFERENT FROM THE ONE RECORDED.

Effective date: 20050617