阅读说明：本技术 聚丙烯类复合材料 (Polypropylene composite material ) 是由 朴想恩 李银精 朴仁成 金太洙 李忠勳 孔镇衫 全晸浩 郭来根 于 2020-09-28 设计创作，主要内容包括：本发明涉及一种聚丙烯类复合材料,其包含：(A)聚丙烯,和(B)满足以下条件的烯烃类聚合物：(1)熔融指数(MI,190℃,2.16kg负荷条件)为0.1g/10min至10.0g/10min,(2)通过差示扫描量热法(DSC)测量时的熔融温度为20℃至70℃,和(3)通过差示扫描量热法精确测量方法(SSA)测量时,在75℃至150℃确认高温熔融峰,并且相应区域的总熔化焓ΔH(75)为1.0J/g以上。本发明的聚丙烯类复合材料可以显示出优异的冲击强度。(The present invention relates to a polypropylene-based composite material comprising: (A) polypropylene, and (B) an olefin-based polymer satisfying the following conditions: (1) a melt index (MI, 190 ℃, 2.16kg load conditions) of 0.1g/10min to 10.0g/10min, (2) a melting temperature of 20 ℃ to 70 ℃ as measured by Differential Scanning Calorimetry (DSC), and (3) a high-temperature melting peak as measured by differential scanning calorimetry precision measurement method (SSA) is confirmed at 75 ℃ to 150 ℃, and a total melting enthalpy Δ H (75) of the corresponding region is 1.0J/g or more. The polypropylene-based composite material of the present invention can exhibit excellent impact strength.)

1. A polypropylene-based composite material comprising:

(A) polypropylene, and

(B) an olefin-based polymer satisfying the following conditions (1) to (3):

(1) a melt index (MI, 190 ℃, 2.16kg load conditions) of from 0.1g/10min to 10.0g/10min,

(2) a density (d) of 0.860g/cc to 0.880g/cc, and

(3) satisfies T (90) -T (50) ≦ 50 and T (95) -T (90) ≧ 10 when measured by differential scanning calorimetry (SSA) precision measurement method,

wherein T (50), T (90) and T (95) are temperatures at which 50%, 90% and 95% melt when the temperature-heat capacity curve of the measurement results from the differential scanning calorimetry precision measurement method (SSA) is divided, respectively.

2. The polypropylene-based composite material according to claim 1, wherein the (A) polypropylene has a melt index of 0.5g/10min to 100g/10min as measured at 230 ℃ under a load of 2.16 kg.

3. The polypropylene-based composite material according to claim 1, wherein the (A) polypropylene is an impact copolymer having a melt index of 0.5g/10min to 100g/10min as measured at 230 ℃ under a load of 2.16 kg.

4. The polypropylene-based composite material according to claim 1, wherein the (B) olefin-based polymer further satisfies the following conditions: (4) the weight-average molecular weight (Mw) is 10000g/mol to 500000 g/mol.

5. The polypropylene-based composite material according to claim 1, wherein the (B) olefin-based polymer further satisfies the following conditions: (5) a Molecular Weight Distribution (MWD) of 0.1 to 6.0.

6. The polypropylene-based composite material according to claim 1, wherein the (B) olefin-based polymer further satisfies the following conditions: (6) the melting temperature is 20 ℃ to 70 ℃ when measured by Differential Scanning Calorimetry (DSC).

7. The polypropylene-based composite material according to claim 1, wherein the (B) olefin-based polymer is a copolymer of ethylene and an α -olefin comonomer of 3 to 12 carbon atoms.

8. A polypropylene-based composite material according to claim 7, wherein the alpha-olefin comonomer comprises a comonomer selected from the group consisting of propylene, 1-butene, 1-pentene, 4-methyl-1-pentene, 1-hexene, 1-heptene, 1-octene, 1-decene, 1-undecene, 1-dodecene, 1-tetradecene, 1-hexadecene, 1-eicosene, norbornene, norbornadiene, ethylidene norbornene, phenylnorbornene, vinyl norbornene, dicyclopentadiene, 1, 4-butadiene, 1, 5-pentadiene, 1, 6-hexadiene, styrene, alpha-methylstyrene, divinylbenzene and 3-chloromethylstyrene, or a mixture of two or more thereof.

9. The polypropylene-based composite material according to claim 1, wherein the olefin-based polymer (B) is a copolymer of ethylene and 1-hexene.

10. The polypropylene-based composite material according to claim 1, wherein the (B) olefin-based polymer is obtained by a production method comprising the steps of: polymerizing olefin monomers by injecting hydrogen in the presence of a catalyst composition for polymerizing olefins, the catalyst composition comprising a transition metal compound of the following formula 1:

[ formula 1]

In the formula 1, the first and second groups,

R₁the groups are the same or different and are each independently hydrogen, alkyl of 1 to 20 carbon atoms, alkenyl of 2 to 20 carbon atoms, aryl, silyl, alkylaryl, arylalkyl or a metalloid radical of a group 4 metal substituted with a hydrocarbyl group, and two R' s₁The groups may be connected to each other through an alkylidene group of an alkyl group having 1 to 20 carbon atoms or an aryl group having 6 to 20 carbon atoms to form a ring;

R₂the radicals are identical or different and are each independently hydrogen, halogen, alkyl of 1 to 20 carbon atoms, aryl, alkoxy, aryloxy or amino, and R₂Two or more of the groups may be linked to each other to form an aliphatic ring or an aromatic ring;

R₃the groups are the same or different and are each independently hydrogen, halogen, an alkyl group of 1 to 20 carbon atoms, or a nitrogen-containing aliphatic or aromatic ring substituted or unsubstituted with an aryl group, and in the case where a plurality of substituents are present, two or more of the substituents may be linked to each other to form an aliphatic or aromatic ring;

m is a group 4 transition metal; and is

Q₁And Q₂Each independently of the other being halogen, alkyl, alkenyl of 1 to 20 carbon atomsAryl, alkylaryl, arylalkyl, alkylamino of 1 to 20 carbon atoms, arylamino or alkylidene of 1 to 20 carbon atoms.

11. The polypropylene-based composite material according to claim 1, wherein the (B) olefin-based polymer is prepared by a continuous solution polymerization using a continuous stirred tank reactor by injecting hydrogen in the presence of a catalyst composition for polymerizing olefin.

12. The polypropylene-based composite material according to claim 1, wherein the polypropylene-based composite material comprises 5 to 40% by weight of (B) the olefin-based polymer.

13. The polypropylene-based composite material according to claim 1, wherein the polypropylene-based composite material further comprises an inorganic filler.

14. The polypropylene-based composite material according to claim 13, wherein the polypropylene-based composite material comprises 0.1 to 40 parts by weight of the inorganic filler, based on 100 parts by weight of (a) polypropylene, and

the average particle diameter (D) of the inorganic filler₅₀) Is 1 μm to 20 μm.

Technical Field

[ Cross-reference to related applications ]

This application claims the benefit of korean patent application No. 10-2019-0121150, filed by the korean intellectual property office at 30.9.2019, the contents of which are incorporated herein by reference.

[ technical field ]

The present invention relates to a polypropylene-based composite material, and more particularly, to a polypropylene-based composite material having improved impact strength and mechanical properties by including a low-density olefin-based polymer that introduces a high crystalline region and exhibits high mechanical rigidity.

Background

Conventionally, as a composition for automobile interior and exterior material parts, a polypropylene resin composition containing polypropylene (PP), an impact reinforcement, and an inorganic filler as main components is used.

Until the mid 1990's, ethylene-propylene rubber (EPR) or ethylene-propylene-diene monomer rubber (EDPM) was mainly used in most polypropylene-based resin compositions as materials for automobile interiors and exteriors, particularly as materials for bumper covers, before ethylene- α -olefin copolymers obtained by polymerization using a metallocene catalyst were developed. However, after the advent of ethylene- α -olefin copolymers synthesized by metallocene catalysts, ethylene- α -olefin copolymers have been used as impact enhancers and are now the mainstream. Because the polypropylene-based composite material using the same is advantageous in that it has well-balanced physical properties (including impact strength, flexural modulus, flexural strength, etc.), has good moldability, and is inexpensive.

Since the molecular structure of polyolefins such as ethylene- α -olefin copolymers synthesized by metallocene catalysts is more uniformly controlled than that of polyolefins synthesized by ziegler-natta catalysts, the molecular weight distribution is narrow and the overall mechanical properties are good. For low density ethylene elastomers obtained by metallocene catalyst polymerization, the alpha-olefin comonomer is relatively uniformly inserted into the polyethylene molecule when compared to that obtained by ziegler-natta catalyst polymerization, and the low density rubber properties can be maintained while exhibiting excellent other mechanical properties.

However, there is a limitation in securing impact resistance according to various application environments, and it is required to develop a polypropylene-based composite material that can overcome such a limitation.

Disclosure of Invention

Technical problem

The object of the present invention is to provide a polypropylene composite material which can exhibit significantly improved impact strength properties and excellent mechanical strength.

Technical scheme

In order to solve the above-mentioned task, the present invention provides a polypropylene-based composite material comprising: (A) polypropylene and (B) an olefin-based polymer satisfying the following conditions (1) to (3):

(1) a melt index (MI, 190 ℃, 2.16kg load conditions) of from 0.1g/10min to 10.0g/10min, (2) a density (d) of from 0.860g/cc to 0.880g/cc, and (3) satisfies T (90) -T (50) ≦ 50 and T (95) -T (90) ≧ 10 when measured by differential scanning calorimetry (SSA) precision measurement method,

wherein T (50), T (90) and T (95) are temperatures at which 50%, 90% and 95% melt when the temperature-heat capacity curve of the measurement results from the differential scanning calorimetry precision measurement method (SSA) is divided, respectively.

Advantageous effects

By including the olefin-based polymer that introduces a high crystalline region and exhibits high mechanical rigidity, the polypropylene-based composite material of the present invention can exhibit significantly improved impact strength properties and excellent mechanical strength without using a separate additive, while having excellent miscibility and being uniformly dispersed in the composite material.

Drawings

Fig. 1 is a graph showing the measurement results of the melting temperature using Differential Scanning Calorimetry (DSC) on the polymer of preparation example 1.

Fig. 2 is a graph showing the measurement results of the melting temperature using Differential Scanning Calorimetry (DSC) on the polymer of comparative preparation example 1.

Fig. 3 is a graph showing the measurement results of the polymer of preparation example 1 by the differential scanning calorimetry precision measurement method (SSA).

FIG. 4 is a graph showing the measurement results of the polymer of comparative preparation example 1 by the differential scanning calorimetry precision measurement method (SSA).

FIG. 5 is a graph showing T (50), T (90) and T (95) after the results of the differential scanning calorimetry precision measurement method (SSA) of the polymer of preparation example 1 are divided.

FIG. 6 is a graph showing T (50), T (90) and T (95) after the results of the differential scanning calorimetry accurate measurement method (SSA) of the polymer of comparative preparation example 1 are divided.

Detailed Description

Hereinafter, the present invention will be described in more detail to help understanding the present invention.

It is to be understood that the words or terms used in the present disclosure and claims are not to be interpreted as meaning defined in commonly used dictionaries. It will also be understood that the words or terms should be interpreted as having a meaning that is consistent with their meaning in the context of the prior art and the technical idea of the present invention, on the basis of the principle that the inventor can appropriately define the meaning of the words or terms to best explain the principle of the present invention.

The term "polymer" as used in this disclosure refers to a polymer compound prepared by polymerizing monomers of the same or different types. The general term "polymer" includes the term "interpolymer" as well as "homopolymers", "copolymers", and "terpolymers". Further, the term "interpolymer" refers to a polymer prepared by polymerizing two or more different types of monomers. The general term "interpolymer" includes the term "copolymer" (generally used to refer to polymers prepared from two different monomers) and the term "terpolymer" (generally used to refer to polymers prepared from three different monomers). The term "interpolymer" includes polymers prepared by polymerizing four or more types of monomers.

Conventionally, polypropylene is used as an automobile interior and exterior material such as an automobile bumper, and polyolefin-based polymers are used together as an impact reinforcement material in order to supplement the low impact strength of polypropylene. First, in order to exhibit properties of impact resistance, elastic modulus and stretchability and to achieve high impact strength properties according to various application environments, low-density polyolefin-based polymers are used. However, in this case, there is a problem that the strength of polypropylene is rather deteriorated.

In this regard, in the present invention, by using the olefin-based polymer having an excellent impact strength improving effect and simultaneously being uniformly dispersed in the composite due to excellent miscibility with polypropylene when preparing the polypropylene-based composite, it is possible to exhibit significantly improved impact strength properties as well as excellent mechanical strength without using a separate additive.

The polypropylene composite material of the present invention comprises: (A) polypropylene and (B) an olefin-based polymer satisfying the following conditions (1) to (3).

(1) A melt index (MI, 190 ℃, 2.16kg load conditions) of from 0.1g/10min to 10.0g/10min, (2) a density (d) of from 0.860g/cc to 0.880g/cc, and (3) satisfies T (90) -T (50) ≦ 50 and T (95) -T (90) ≧ 10 when measured by differential scanning calorimetry (SSA) precision measurement method,

wherein T (50), T (90) and T (95) are temperatures at which 50%, 90% and 95% melt when the temperature-heat capacity curve of the measurement results from the differential scanning calorimetry precision measurement method (SSA) is divided, respectively.

Hereinafter, the respective constituent components will be described in detail.

(A) Polypropylene

In the polypropylene-based composite material of the embodiment of the present invention, the polypropylene may specifically be a homopolymer of polypropylene, or a copolymer of propylene and an α -olefin monomer, and in this case, the copolymer may be an alternating or random or block copolymer. However, in the present invention, polypropylene which may overlap with the olefin polymer is excluded, and polypropylene is a different compound from the olefin polymer.

The alpha-olefin-based monomer may specifically be an aliphatic olefin of 2 to 12 carbon atoms or 2 to 8 carbon atoms. More specifically, ethylene, propylene, 1-butene, 1-pentene, 3-methyl-1-butene, 1-hexene, 4-methyl-1-pentene, 3-methyl-1-pentene, 1-heptene, 1-octene, 1-decene, 1-undecene, 1-dodecene, 1-tetradecene, 1-hexadecene, 1-eicosene, 4-dimethyl-1-pentene, 4-diethyl-1-hexene, 3, 4-dimethyl-1-hexene, and the like can be used, and any one of them or a mixture of two or more of them can be used.

More specifically, the polypropylene may be any one selected from the group consisting of polypropylene copolymers, propylene- α -olefin copolymers and propylene-ethylene- α -olefin copolymers, or a mixture of two or more thereof, and in this case, the copolymer may be a random or block copolymer.

Further, the Melt Index (MI) of the polypropylene measured at 230 ℃ and 2.16kg load can be from 0.5g/10min to 100g/10min, specifically, the Melt Index (MI) can be from 1g/10min to 90g/10min, more specifically, from 10g/10min to 50g/10 min. If the melt index of polypropylene deviates from this range, it is considered that defects may be generated during injection molding.

In particular, in the polypropylene-based composite material of the embodiment of the present invention, the polypropylene may be an impact copolymer having a melt index of 0.5g/10min to 100g/10min, specifically 1g/10min to 90g/10min, measured at 230 ℃ and under a 2.16kg load, and more specifically, the polypropylene may be a propylene-ethylene impact copolymer. The content of the impact copolymer may be 50 to 90% by weight, more specifically 80 to 90% by weight, relative to the total weight of the polypropylene-based composite. In the case of including the impact copolymer having such physical properties as polypropylene within the above range, strength properties such as low-temperature strength properties can be improved in particular.

The impact copolymer may be prepared by a general preparation reaction using a polymer to satisfy the above-mentioned physical property conditions, or may be commercially available and used. Specific examples may include SEETE of LG chemistry, Inc^TMM1600, and the like.

Further, in the polypropylene-based composite material of the embodiment of the present invention, the polypropylene may be specifically one or more random propylene copolymers having a DSC melting temperature of 120 ℃ to 160 ℃ and a Melt Flow Rate (MFR) measured at 230 ℃ and under a load of 2.16kg according to ASTM-D1238 of 5g/10min to 120g/10min, and the content of the random propylene copolymer may be 75% by weight to 97% by weight, more specifically 85% by weight to 91% by weight, relative to the total weight of the polypropylene-based composite material. If the content of the polypropylene having such physical properties is within the above range, the mechanical strength, including hardness, etc., of the polypropylene composite material can be improved. The random propylene copolymer may be prepared by using a common preparation reaction of the polymer to satisfy the above-mentioned physical property conditions, or may be commercially available and used. Specific examples may include Braskem from Braskem America Inc. of the United states^TMPP R7021-50RNA and Formolene from Formosa Plastics Corporation^TM7320A, and the like.

(B) Olefin polymer

The olefin-based polymer contained in the polypropylene-based composite material of the present invention has a very low density and introduces a high crystalline region, and can exhibit even higher tensile strength and tear strength with the same degree of density and melt index (MI, 190 ℃, 2.16kg load condition) when compared with the conventional olefin-based polymer. The olefin-based polymer contained in the polypropylene-based composite material of the present invention is produced by a production method including a step of polymerizing an olefin-based monomer by injecting hydrogen in the presence of a catalyst composition for polymerizing an olefin, and a high crystalline region is introduced with the injection of hydrogen during polymerization, and exhibits excellent mechanical rigidity.

The Melt Index (MI) can be controlled by controlling the amount of comonomer of the catalyst used in the process of polymerizing the olefin-based polymer and affects the mechanical properties and impact strength of the olefin-based polymer and its moldability. In the present invention, the melt index is measured under a low density condition of 0.860g/cc to 0.880g/cc under a load condition of 190 ℃ and 2.16kg according to ASTM D1238, and the melt index can exhibit 0.1g/10min to 10g/10min, specifically 0.3g/10min to 9g/10min, more specifically 0.4g/10min to 7g/10 min.

Also, the density can be from 0.850g/cc to 0.890g/cc, specifically from 0.850g/cc to 0.880g/cc, more specifically from 0.860g/cc to 0.875 g/cc.

In general, the density of an olefin-based polymer is influenced by the type and amount of monomers used for polymerization, the degree of polymerization, and the like, and in the case of a copolymer, the influence by the amount of copolymerized monomers is significant. The olefin-based polymer of the present invention is polymerized using a catalyst composition comprising a transition metal compound having a characteristic structure, and a large amount of a comonomer can be introduced. Thus, the olefin-based polymer of the present invention can have a low density within the above range.

Further, the olefin-based polymer can satisfy T (90) -T (50). ltoreq.50 and T (95) -T (90). gtoreq.10, specifically 20. ltoreq. T (90) -T (50). ltoreq.45 and 10. ltoreq. T (95) -T (90). ltoreq.30, more specifically 30. ltoreq. T (90) -T (50). ltoreq.40 and 10. ltoreq. T (95) -T (90). ltoreq.20, when measured by a differential scanning calorimetry precision measurement method (SSA).

T (50), T (90) and T (95) are the temperatures at which 50%, 90% and 95% melt when the temperature-heat capacity curve from the measurement of the differential scanning calorimetry precision measurement method (SSA) is divided.

Generally, the melting temperature (Tm) is measured using differential scanning calorimetry by a first cycle comprising heating at a constant rate to a temperature about 30 ℃ higher than the melting temperature (Tm) and cooling at a constant rate to a temperature about 30 ℃ lower than the glass transition temperature (Tg) and a second cycle to obtain a peak value of the standard melting temperature (Tm). Differential scanning calorimetry (SSA) is a process of undergoing heating to just before the peak of the melting temperature (Tm) and cooling after the first cycle by using Differential Scanning Calorimetry (DSC), and repeating heating to a temperature reduced by about 5 ℃ and cooling to obtain more accurate crystallization information (eur.polym.j.2015,65,132).

In the case of introducing a small amount of high crystalline region into the olefin-based polymer, when the melting temperature is measured using general Differential Scanning Calorimetry (DSC), a high temperature melting peak may not be displayed, but may be measured by a differential scanning calorimetry precision measurement method (SSA).

Further, the olefin-based polymer according to the embodiment of the present invention may further satisfy the following condition: (4) the weight average molecular weight (Mw) is 10000g/mol to 500000g/mol, specifically, the weight average molecular weight (Mw) may be 30000g/mol to 300000g/mol, more specifically, 50000g/mol to 200000 g/mol. In the present invention, the weight average molecular weight (Mw) is a polystyrene-equivalent molecular weight analyzed by Gel Permeation Chromatography (GPC).

Further, the olefin-based polymer according to the embodiment of the present invention may further satisfy the following condition: (5) the Molecular Weight Distribution (MWD), which is the ratio (Mw/Mn) of the weight average molecular weight (Mw) to the number average molecular weight (Mn), is 0.1 to 6.0, and the Molecular Weight Distribution (MWD) may specifically be 1.0 to 4.0, more specifically 2.0 to 3.0.

Further, the olefin-based polymer according to the embodiment of the present invention may satisfy the following conditions: (6) the melting temperature (Tm) is 20 ℃ to 70 ℃ when measured by Differential Scanning Calorimetry (DSC), wherein the melting temperature (Tm) can specifically be 25 ℃ to 60 ℃, more specifically 25 ℃ to 50 ℃.

The olefin polymer may be any homopolymer selected from olefin monomers, particularly α -olefin monomers, cycloolefin monomers, diene monomers, triene monomers and styrene monomers, or a copolymer of two or more kinds thereof. More specifically, the olefin-based polymer may be a copolymer of ethylene with an α -olefin of 3 to 12 carbon atoms, or a copolymer with an α -olefin of 3 to 10 carbon atoms.

The α -olefin comonomer may include any one selected from the group consisting of propylene, 1-butene, 1-pentene, 4-methyl-1-pentene, 1-hexene, 1-heptene, 1-octene, 1-decene, 1-undecene, 1-dodecene, 1-tetradecene, 1-hexadecene, 1-eicosene, norbornene, norbornadiene, ethylidene norbornene, phenyl norbornene, vinyl norbornene, dicyclopentadiene, 1, 4-butadiene, 1, 5-pentadiene, 1, 6-hexadiene, styrene, α -methylstyrene, divinylbenzene and 3-chloromethylstyrene, or a mixture of two or more thereof.

More specifically, the olefin-based polymer of the embodiment of the present invention may be a copolymer of ethylene and propylene, ethylene and 1-butene, ethylene and 1-hexene, ethylene and 4-methyl-1-pentene, or ethylene and 1-octene, and more specifically, the olefin copolymer of the embodiment of the present invention may be a copolymer of ethylene and 1-butene.

If the olefin-based polymer is a copolymer of ethylene and an alpha-olefin, the amount of alpha-olefin can be 90 wt% or less, more specifically 70 wt% or less, still more specifically 5 wt% to 60 wt%, still more specifically 20 wt% to 50 wt%, based on the total weight of the copolymer. If the α -olefin is contained in the above range, the above physical properties can be easily achieved.

The olefin-based polymer of the embodiment of the present invention having the above-described physical properties and structural characteristics may be prepared by a continuous solution polymerization reaction for polymerizing olefin-based monomers by injecting hydrogen gas in the presence of a metallocene catalyst composition comprising one or more transition metal compounds in a single reactor. Therefore, in the olefin-based polymer according to the embodiment of the present invention, a block composed of two or more repeating units linearly linked from any one of the monomers constituting the polymer is not formed in the polymer. That is, the olefin-based polymer of the present invention may not include a block copolymer, but may be selected from the group consisting of a random copolymer, an alternating copolymer, and a graft copolymer, more specifically, a random copolymer.

In the embodiment of the present invention, the injection amount of hydrogen may be 0.35 to 3 parts by weight, specifically 0.4 to 2 parts by weight, more specifically 0.45 to 1.5 parts by weight, based on 1 part by weight of the olefin-based monomer injected into the reaction system. Further, in the embodiment of the present invention, if the olefin-based polymer is polymerized by continuous solution polymerization, the injection amount of hydrogen may be 0.35 to 3kg/h, specifically 0.4 to 2kg/h, more specifically 0.45 to 1.5kg/h, based on 1kg/h of the olefin-based monomer injected into the reaction system.

Further, in another embodiment of the present invention, in the case where the olefin-based polymer is a copolymer of ethylene and α -olefin, the injection amount of hydrogen may be 0.8 to 3 parts by weight, specifically 0.9 to 2.8 parts by weight, more specifically 1 to 2.7 parts by weight, based on 1 part by weight of ethylene. Further, in the embodiment of the present invention, in the case where the olefin-based polymer is a copolymer of ethylene and α -olefin and polymerization is carried out by continuous solution polymerization, hydrogen may be injected into the reaction system in an amount of 0.8 to 3kg/h, specifically 0.9 to 2.8kg/h, more specifically 1 to 2.7kg/h, based on 1kg/h of ethylene.

The olefin-based polymer of the present invention can satisfy the above physical properties if polymerization is carried out under the condition of injecting the amount of hydrogen in the above range.

In particular, the olefin-based copolymer of the present invention can be obtained by a preparation method comprising a step of polymerizing an olefin-based monomer by injecting hydrogen gas in the presence of a catalyst composition for polymerizing an olefin comprising a transition metal compound of the following formula 1.

However, in the preparation of the olefin-based polymer according to the embodiment of the present invention, it is understood that the scope of the structure of the transition metal compound of formula 1 is not limited to the specifically disclosed type, but includes all variations, equivalents, or substituents included in the spirit and technical scope of the present invention.

[ formula 1]

In the formula 1, the first and second groups,

R₁the groups are the same or different and are each independently hydrogen, alkyl of 1 to 20 carbon atoms, alkenyl of 2 to 20 carbon atoms, aryl, silyl, alkylaryl, arylalkyl or a metalloid radical of a group 4 metal substituted with a hydrocarbyl group, and two R' s₁The groups may be connected to each other through an alkylidene group of an alkyl group having 1 to 20 carbon atoms or an aryl group having 6 to 20 carbon atoms to form a ring;

R₂the radicals are identical or different and are each independently hydrogen, halogen, alkyl of 1 to 20 carbon atoms, aryl, alkoxy, aryloxy or amino, and R₂Two or more of the groups may be linked to each other to form an aliphatic ring or an aromatic ring;

R₃the groups are the same or different and are each independently hydrogen, halogen, an alkyl group of 1 to 20 carbon atoms, or a nitrogen-containing aliphatic or aromatic ring substituted or unsubstituted with an aryl group, and in the case where a plurality of substituents are present, two or more of the substituents may be linked to each other to form an aliphatic or aromatic ring;

m is a group 4 transition metal; and is

Q₁And Q₂Each independently is halogen, alkyl of 1 to 20 carbon atoms, alkenyl, aryl, alkylaryl, arylalkyl, alkylamino of 1 to 20 carbon atoms, arylamino, or alkylidene of 1 to 20 carbon atoms.

In another embodiment of the present invention, R in the formula 2₁And R₂May be the same or different and are each independently hydrogen, alkyl of 1 to 20 carbon atoms, aryl or silyl;

R₃the groups may be the same or different and may be alkyl of 1 to 20 carbon atoms, alkenyl of 2 to 20 carbon atoms, aryl, alkylaryl, arylalkyl, alkoxy of 1 to 20 carbon atoms, aryloxy or amino, and R₆In (1)Two or more R₆The groups may be linked to each other to form an aliphatic or aromatic ring;

Q₁and Q₂May be the same or different and are each independently halogen, alkyl of 1 to 20 carbon atoms, alkylamino or arylamino of 1 to 20 carbon atoms, and

m may be a group 4 transition metal.

The transition metal compound represented by formula 2 has a feature in which metal sites are linked by a cyclopentadienyl ligand incorporating tetrahydroquinoline, and maintains a narrow Cp-m-n angle and a wide Q angle of monomer proximity₁-M-Q₂(Q₃-M-Q₄) And (4) an angle. In addition, Cp, tetrahydroquinoline, nitrogen and metal sites are connected in sequence according to a cyclic bond, forming a more stable and rigid five-membered ring structure. Thus, by reaction with, for example, methylaluminoxane and B (C)₆F₅)₃And then applied to olefin polymerization to activate such compounds, the polymerization of olefin polymers having characteristics of high activity, high molecular weight and high copolymerizability can be achieved even at high polymerization temperatures.

The detailed explanation of each substituent defined in the present disclosure is as follows.

The term "hydrocarbon group" used in the present invention means, unless otherwise mentioned, a monovalent hydrocarbon group of 1 to 20 carbon atoms, which is composed of only carbon and hydrogen regardless of its structure, such as alkyl, aryl, alkenyl, alkynyl, cycloalkyl, alkylaryl and arylalkyl groups.

The term "halogen" as used herein, unless otherwise mentioned, refers to fluorine, chlorine, bromine or iodine.

The term "alkyl" as used herein, unless otherwise mentioned, refers to a straight or branched chain hydrocarbon residue.

The term "cycloalkyl" as used herein, unless otherwise noted, denotes cyclic alkyl groups, including cyclopropyl and the like.

The term "alkenyl" as used herein, unless otherwise mentioned, refers to straight or branched chain alkenyl groups.

The branches may be: alkyl of 1 to 20 carbon atoms; alkenyl of 2 to 20 carbon atoms; aryl of 6 to 20 carbon atoms; an alkylaryl group of 7 to 20 carbon atoms; or arylalkyl of 7 to 20 carbon atoms.

The term "aryl" as used in the present invention, unless otherwise mentioned, denotes an aromatic group of 6 to 20 carbon atoms, in particular phenyl, naphthyl, anthryl, phenanthryl,Pyrenyl, anthracenyl, pyridyl, dimethylanilino, anisyl and the like without limitation.

Alkylaryl refers to an aryl group substituted with an alkyl group.

Arylalkyl means an alkyl group substituted with an aryl group.

The cyclic group (or heterocyclic group) means a monovalent aliphatic or aromatic hydrocarbon group having 5 to 20 ring-forming carbon atoms and including one or more hetero atoms, and may be a single ring or a condensed ring of two or more rings. Further, the heterocyclic group may be substituted or unsubstituted with an alkyl group. Examples thereof may include indoline, tetrahydroquinoline, and the like, but the present invention is not limited thereto.

Alkylamino means an amino group substituted with an alkyl group, including dimethylamino, diethylamino, and the like without limitation.

According to an embodiment of the present invention, the aryl group may preferably have 6 to 20 carbon atoms, and may be particularly, without limitation, a phenyl group, a naphthyl group, an anthracenyl group, a pyridyl group, a dimethylanilino group, an anisyl group, or the like.

In the present disclosure, the silyl group may be a substituted or unsubstituted silyl group having an alkyl group of 1 to 20 carbon atoms, for example, a silyl group, a trimethylsilyl group, a triethylsilyl group, a tripropylsilyl group, a tributylsilyl group, a trihexylsilyl group, a triisopropylsilyl group, a triisobutylsilyl group, a triethoxysilyl group, a triphenylsilyl group, a tris (trimethylsilyl) silyl group, and the like without limitation.

The compound of formula 1 may be the following formula 1-1, but is not limited thereto.

[ formula 1-1]

Further, the compound may have various structures within the range defined by formula 1.

Due to the structural characteristics of the catalyst, the transition metal compound of formula 2 can incorporate a large amount of α -olefin as well as low density polyethylene, and can produce a low density polyolefin copolymer having a level of 0.850g/cc to 0.890 g/cc.

The transition metal compound of formula 1 can be prepared, for example, by the following method.

[ reaction 1]

In reaction 1, R₁To R₃、M、Q₁And Q₂The same as defined in formula 1.

Formula 1 can be prepared by the method disclosed in korean patent application publication No. 2007-0003071, and the entire contents of this patent document are included in the present disclosure.

The transition metal compound of formula 1 may be used as a catalyst for polymerization as a composition type further comprising one or more of cocatalyst compounds represented by the following formulae 2,3 and 4.

[ formula 2]

-[Al(R₄)-O]_a-

[ formula 3]

A(R₄)₃

[ formula 4]

[L-H]⁺[W(D)₄]^-Or [ L]⁺[W(D)₄]^-

In the formulae 2 to 4, the first and second groups,

R₄the groups may be the same or different from each other and each independently selected from the group consisting of halogen, hydrocarbon group of 1 to 20 carbon atoms and halogen-substituted hydrocarbon group of 1 to 20 carbon atoms,

a is aluminum or boron, and A is aluminum or boron,

the D groups are each independently an aryl group of 6 to 20 carbon atoms or an alkyl group of 1 to 20 carbon atoms, wherein one or more hydrogen atoms may be substituted with a substituent, wherein the substituent is at least any one selected from the group consisting of a halogen, a hydrocarbon group of 1 to 20 carbon atoms, an alkoxy group of 1 to 20 carbon atoms and an aryloxy group of 6 to 20 carbon atoms,

h is a hydrogen atom, and (C) is a hydrogen atom,

l is a neutral or cationic Lewis acid,

w is an element of group 13, and

a is an integer of 2 or more.

Examples of the compound represented by formula 2 may include alkylaluminoxane such as Methylaluminoxane (MAO), ethylaluminoxane, isobutylaluminoxane and butylaluminoxane, and modified alkylaluminoxane obtained by mixing two or more alkylaluminoxanes, particularly methylaluminoxane, Modified Methylaluminoxane (MMAO).

Examples of the compound represented by formula 3 may include trimethylaluminum, triethylaluminum, triisobutylaluminum, tripropylaluminum, tributylaluminum, dimethylaluminum chloride, triisopropylaluminum, tri-sec-butylaluminum, tricyclopentylaluminum, tripentylaluminum, triisopentylaluminum, trihexylaluminum, trioctylaluminum, ethyldimethylaluminum, methyldiethylaluminum, triphenylaluminum, tri-p-tolylaluminum, dimethylaluminum methoxide, dimethylaluminum ethoxide, trimethylboron, triethylboron, triisobutylboron, tripropylboron, tributylboron, etc., and particularly, may be selected from trimethylaluminum, triethylaluminum and triisobutylaluminum.

Examples of the compound represented by formula 4 may include triethylammonium tetraphenylboron, tributylammonium tetraphenylboron, trimethylammonium tetraphenylboron, tripropylammonium tetraphenylboron, trimethylammonium tetrakis (p-tolyl) boron, trimethylammonium tetrakis (o, p-dimethylphenyl) boron, tributylammonium tetrakis (p-trifluoromethylphenyl) boron, trimethylammonium tetrakis (p-trifluoromethylphenyl) boron, tributylammonium tetrakis (pentafluorophenyl) boron, N-diethylanilinium tetraphenylboron, N-diethylanilinium tetrakis (pentafluorophenyl) boron, diethylammonium tetrakis (pentafluorophenyl) boron, triphenylphosphonium tetraphenylboron, trimethylphosphonium tetraphenylboron, dimethylanilinium tetrakis (pentafluorophenyl) borate, triethylammonium tetraphenylaluminum, tributylammonium tetraphenylaluminum, trimethylammonium tetraphenylaluminum, tripropylammonium tetraphenylaluminum, trimethylammonium tetrakis (p-tolyl) aluminum, Tripropylammonium tetrakis (p-tolyl) aluminum, triethylammonium tetrakis (o, p-dimethylphenyl) aluminum, tributylammonium tetrakis (p-trifluoromethylphenyl) aluminum, trimethylammonium tetrakis (p-trifluoromethylphenyl) aluminum, tributylammonium tetrakis (pentafluorophenyl) aluminum, N-diethylanilinium tetraphenylaluminum, N-diethylanilinium tetrakis (pentafluorophenyl) aluminum, diethylammonium tetrakis (pentafluorophenyl) aluminum, triphenylphosphonium tetraphenylaluminum, trimethylphosphonium tetraphenylaluminum, tripropylammonium tetrakis (p-tolyl) boron, triethylammonium tetrakis (o, p-dimethylphenyl) boron, triphenylcarbonium tetrakis (p-trifluoromethylphenyl) boron or triphenylcarbonium tetrakis (pentafluorophenyl) boron.

As a first method, the catalyst composition may be prepared by a preparation method comprising the steps of: a step of obtaining a mixture by contacting a transition metal compound represented by formula 1 with a compound represented by formula 2 or formula 3; and a step of adding the compound represented by formula 4 to the mixture.

Further, as a second method, the catalyst composition may be prepared by a method of contacting the transition metal compound represented by formula 1 with the compound represented by formula 4.

In the first of the preparation methods of the catalyst composition, the molar ratio of the transition metal compound represented by formula 1 and the transition metal compound represented by formula 2/the compound represented by formula 2 or formula 3 may be 1/5000 to 1/2, specifically 1/1000 to 1/10, more specifically 1/500 to 1/20. If the molar ratio of the transition metal compound represented by formula 1/the compound represented by formula 2 or formula 3 is greater than 1/2, the amount of the alkylating agent is too small and alkylation of the metal compound may not be completely performed, and if the molar ratio is less than 1/5000, alkylation of the metal compound may be achieved, but activation of the alkylated metal compound may not be completely performed due to a side reaction between the remaining excess alkylating agent and the activator as the compound of formula 4. Further, the molar ratio of the transition metal compound represented by formula 1/the compound represented by formula 4 may be 1/25 to 1, specifically 1/10 to 1, more specifically 1/5 to 1. If the molar ratio of the transition metal compound represented by formula 1/the compound represented by formula 4 is greater than 1, the amount of the activator is relatively small and the activation of the metal compound may not be completely performed, and thus, the activity of the catalyst composition may be deteriorated. If the molar ratio is less than 1/25, the activation of the metal compound may be completely conducted, but it will be uneconomical in view of the unit cost of the catalyst composition due to the excess amount of the remaining activator, or the purity of the produced polymer may be lowered.

In the second one of the preparation methods of the catalyst composition, the molar ratio of the transition metal compound represented by formula 1/the compound represented by formula 4 may be 1/10000 to 1/10, specifically 1/5000 to 1/100, more specifically 1/3000 to 1/500. If the molar ratio is more than 1/10, the amount of the activating agent is relatively small, and activation of the metal compound may not be completely performed, and the activity of the resulting catalyst composition may be decreased. If the molar ratio is less than 1/10000, the activation of the metal compound may be completely conducted, but it will be uneconomical in view of the unit cost of the catalyst composition due to the excess amount of the remaining activator, or the purity of the produced polymer may be lowered.

As the reaction solvent during the preparation of the catalyst composition, hydrocarbon solvents such as pentane, hexane and heptane, or aromatic solvents such as benzene and toluene can be used.

In addition, the catalyst composition may include a supported transition metal compound and a cocatalyst compound on a support.

Any support used in metallocene-based catalysts may be used as the support without particular limitation. In particular, the support may be silica, silica-alumina, or silica-magnesia, and any one of them or a mixture of two or more of them may be used.

In the case where the support is silica, since the silica support and the functional group of the metallocene compound of formula 1 may form a chemical bond, no catalyst is separated from the surface during olefin polymerization. As a result, it is possible to prevent the generation of fouling by which polymer particles are agglomerated on the wall side of the reactor or each other during the production process of the olefin-based copolymer. In addition, the particle shape and apparent density of the polymer of the olefin-based copolymer prepared in the presence of the catalyst comprising a silica carrier are excellent.

More specifically, the support may be silica or silica-alumina, which includes a highly reactive siloxane group, and is dried at high temperature by a method of drying at high temperature, or the like.

The carrier may further comprise an oxide, carbonate, sulphate or nitrate component, for example Na₂O、K₂CO₃、BaSO₄And Mg (NO)₃)₂。

The polymerization reaction for polymerizing the olefin-based monomers can be carried out by a conventional method applied to olefin monomer polymerization such as continuous solution polymerization, bulk polymerization, suspension polymerization, slurry polymerization and emulsion polymerization.

The polymerization reaction of the olefin monomer may be carried out in an inert solvent, and as the inert solvent, benzene, toluene, xylene, cumene, heptane, cyclohexane, methylcyclohexane, methylcyclopentane, n-hexane, 1-hexene and 1-octene may be used without limitation.

The polymerization of the olefin-based polymer may be carried out at a temperature of about 25 ℃ to about 500 ℃, specifically 80 ℃ to 250 ℃, more preferably 100 ℃ to 200 ℃. Further, the reaction pressure during the polymerization may be 1kgf/cm²To 150kgf/cm²Preferably 1kgf/cm²To 120kgf/cm²More preferably 5kgf/cm²To 100kgf/cm²。

Modes for carrying out the invention

Examples

Hereinafter, embodiments of the present invention will be described in detail so that those skilled in the art to which the present invention pertains can easily carry out the present invention. However, the present invention may be embodied in many different forms and is not limited to the embodiments described herein.

Catalyst preparation example 1: preparation of transition Metal Compound A

(1) Preparation of 8- (2,3,4, 5-tetramethyl-1, 3-cyclopentadienyl) -1,2,3, 4-tetrahydroquinoline

(i) Preparation of lithium carbamate

1,2,3, 4-tetrahydroquinoline (13.08g, 98.24mmol) and diethyl ether (150mL) were placed in a shlenk flask. The shlenk flask was immersed in a low temperature bath of-78 ℃ obtained from dry ice and acetone and stirred for 30 minutes. Then, n-BuLi (39.9mL, 2.5M, 98.24mmol) was injected by syringe under a nitrogen atmosphere to form a pale yellow slurry. Then, the flask was stirred for 2 hours, and the temperature of the flask was raised to room temperature while removing generated butane gas. The flask was again immersed in a low temperature bath at-78 ℃ to lower the temperature, and CO was injected₂A gas. With the injection of carbon dioxide gas, the slurry disappeared into a transparent solution. The flask was connected to a bubbler and the temperature was raised to room temperature while removing carbon dioxide gas. Thereafter, the remaining CO was removed under vacuum₂A gas and a solvent. After the flask was transferred to a drying oven, pentane was added thereto, followed by vigorous stirring and filtration to obtain lithium carbamate as a white solid compound. In the white solid compound, diethyl ether forms a coordinate bond. In this case, the yield was 100%.

¹H NMR(C₆D₆,C₅D₅N): δ 1.90(t, J ═ 7.2Hz,6H, ether), 1.50(br s,2H, quin-CH)₂)，2.34(br s,2H,quin-CH₂) 3.25(q, J ═ 7.2Hz,4H, ether), 3.87(br, s,2H, quin-CH)₂)，6.76(br d,J＝5.6Hz,1H,quin-CH)ppm

¹³C NMR(C₆D₆)：δ24.24,28.54,45.37,65.95,121.17,125.34,125.57,142.04,163.09(C＝O)ppm

(ii) Preparation of 8- (2,3,4, 5-tetramethyl-1, 3-cyclopentadienyl) -1,2,3, 4-tetrahydroquinoline

The lithium carbamate compound (8.47g, 42.60mmol) prepared in the above step (i) was put into a shlenk flask. Then, tetrahydrofuran (4.6g, 63.9mmol) and 45mL of diethyl ether were added thereto in this order. The shlenk flask was immersed in a low temperature bath of-20 ℃ obtained from acetone and a small amount of dry ice and stirred for 30 minutes, and n-BuLi (25.1mL, 1.7M, 42.60mmol) was injected. In this case, the color of the reaction mixture turned red. Stirring was carried out for 6 hours while continuously maintaining-20 ℃. Dissolving CeCl in tetrahydrofuran₃2LiCl (129mL, 0.33M, 42.60mmol) and tetramethylcyclopentanone (5.89g, 42.60mmol) were mixed in a syringe and then injected into the flask under a nitrogen atmosphere. In the middle of slowly raising the temperature of the flask to room temperature, the thermostat was removed after 1 hour and the temperature was maintained at room temperature. Then, water (15mL) was added to the flask, and ethyl acetate was added, followed by filtration to obtain a filtrate. The filtrate was transferred to a separatory funnel, to which hydrochloric acid (2N, 80mL) was added, followed by shaking for 12 minutes. Then, saturated sodium bicarbonate solution (160mL) was added for neutralization, and the organic layer was extracted. Anhydrous magnesium sulfate was added to the organic layer to remove water, and filtration was performed. The filtrate was taken out, and the solvent was removed. The filtrate thus obtained was separated by column chromatography using hexane and ethyl acetate (v/v, 10:1) solvents to give a yellow oil. The yield was 40%.

¹H NMR(C₆D₆)：δ1.00(br d,3H,Cp-CH₃)，1.63-1.73(m,2H,quin-CH₂)，1.80(s,3H,Cp-CH₃)，1.81(s,3H,Cp-CH₃)，1.85(s,3H,Cp-CH₃)，2.64(t,J＝6.0Hz,2H,quin-CH₂)，2.84-2.90(br,2H,quin-CH₂)，3.06(br s,1H,Cp-H)，3.76(br s,1H,N-H)，6.77(t,J＝7.2Hz,1H,quin-CH)，6.92(d,J＝2.4Hz,1H,quin-CH)，6.94(d,J＝2.4Hz,1H,quin-CH)ppm

(2) [ (1,2,3, 4-tetrahydroquinolin-8-yl) tetramethylcyclopentadienyl-. eta.⁵,κ-N]Preparation of dimethyl titanium

(i) [ (1,2,3, 4-tetrahydroquinolin-8-yl) tetramethylcyclopentadienyl-. eta.⁵,κ-N]Preparation of dilithium compounds

In a dry box, 8- (2,3,4, 5-tetramethyl-1, 3-cyclopentadienyl) -1,2,3, 4-tetrahydroquinoline (8.07g, 32.0mmol) prepared by the above step (1) and 140mL of diethyl ether were put into a round-bottom flask, the temperature was lowered to-30 ℃ and n-BuLi (17.7g, 2.5M, 64.0mmol) was slowly added while stirring. The reaction was allowed to proceed for 6 hours while warming to room temperature. After that, washing with diethyl ether was performed several times, and filtration was performed to obtain a solid. The remaining solvent was removed by applying vacuum to give dilithium compound (9.83g) as a yellow solid. The yield was 95%.

¹H NMR(C₆D₆,C₅D₅N)：δ2.38(br s,2H,quin-CH₂)，2.53(br s,12H,Cp-CH₃)，3.48(br s,2H,quin-CH₂)，4.19(br s,2H,quin-CH₂)，6.77(t,J＝6.8Hz,2H,quin-CH)，7.28(br s,1H,quin-CH)，7.75(brs,1H,quin-CH)ppm

(ii) [ (1,2,3, 4-tetrahydroquinolin-8-yl) tetramethylcyclopentadienyl-. eta.⁵,κ-N]Preparation of dimethyl titanium

In a drying oven, TiCl is added₄DME (4.41g, 15.76mmol) and diethyl ether (150mL) were placed in a round bottom flask and MeLi (21.7mL, 31.52mmol, 1.4M) was added slowly while stirring at-30 ℃. After stirring for 15 minutes, the [ (1,2,3, 4-tetrahydroquinolin-8-yl) tetramethylcyclopentadienyl-. eta.prepared in step (i) above is reacted⁵,κ-N]Dilithium compound (5.30g, 15.78mmol) was placed in the flask. The mixture was stirred for 3 hours while warming to room temperature. After the reaction was completed, the solvent was removed by applying vacuum, the resulting residue was dissolved in pentane and filtered, and the filtrate was taken out. The pentane was removed by applying vacuum to give a dark brown compound (3.70 g). The yield was 71.3%.

¹H NMR(C₆D₆)：δ0.59(s,6H,Ti-CH₃)，1.66(s,6H,Cp-CH₃)，1.69(br t,J＝6.4Hz,2H,quin-CH₂)，2.05(s,6H,Cp-CH₃)，2.47(t,J＝6.0Hz,2H,quin-CH₂)，4.53(m,2H,quin-CH₂)，6.84(t,J＝7.2Hz,1H,quin-CH)，6.93(d,J＝7.6Hz,quin-CH)，7.01(d,J＝6.8Hz,quin-CH)ppm

¹³C NMR(C₆D₆)：δ12.12,23.08,27.30,48.84,51.01,119.70,119.96,120.95,126.99,128.73,131.67,136.21ppm

Catalyst preparation example 2: preparation of transition Metal Compound B

(1) Preparation of 2-methyl-7- (2,3,4, 5-tetramethyl-1, 3-cyclopentadienyl) indoline

2-methyl-7- (2,3,4, 5-tetramethyl-1, 3-cyclopentadienyl) indoline was prepared by the same method as in (1) of preparation example 1 except that 2-methylindoline was used instead of 1,2,3, 4-tetrahydroquinoline in (1) of preparation example 1. The yield was 19%.

¹H NMR(C₆D₆): δ 6.97(d, J ═ 7.2Hz,1H, CH), δ 6.78(d, J ═ 8Hz,1H, CH), δ 6.67(t, J ═ 7.4Hz,1H, CH), δ 3.94(m,1H, quinoline-CH), δ 3.51(br s,1H, NH), δ 3.24-3.08(m,2H, quinoline-CH)₂Cp-CH), delta 2.65(m,1H, quinoline-CH)²)，δ1.89(s,3H,Cp-CH₃)，δ1.84(s,3H,Cp-CH₃)，δ1.82(s,3H,Cp-CH₃) δ 1.13(d, J ═ 6Hz,3H, quinoline-CH₃)，δ0.93(3H,Cp-CH₃)ppm。

(2) [ (2-Methylindolin-7-yl) tetramethylcyclopentadienyl-. eta. - [⁵,κ-N]Preparation of dimethyl titanium

(i) A dilithium salt compound (compound 4g) (1.37g, 50%) complexed with 0.58 equivalent of diethyl ether was obtained by the same method as in (2) (i) in production example 1, except that 2-methyl-7- (2,3,4, 5-tetramethyl-1, 3-cyclopentadienyl) indoline (2.25g, 8.88mmol) was used instead of 8- (2,3,4, 5-tetramethyl-1, 3-cyclopentadienyl) -1,2,3, 4-tetrahydroquinoline.

¹H NMR (pyridine-d 8): δ 7.22(br s,1H, CH), δ 7.18(d, J ═ 6Hz,1H, CH), δ 6.32(t,1H, CH), δ 4.61(br s,1H, CH), δ 3.54(m,1H, CH), δ 3.00(m,1H, CH), δ 2.35-2.12(m,13H, CH, Cp-CH3), δ 1.39(d, indoline-CH 3) ppm.

(ii) Using the dilithium salt compound (compound 4g) prepared in the above-mentioned (i) (1.37g, 4.44mmol), a titanium compound was prepared by the same method as in (2) (ii) in preparation example 1.

¹H NMR(C₆D₆)：δ7.01-6.96(m,2H,CH)，δ6.82(t,J＝7.4Hz,1H,CH),

δ4.96(m,1H,CH)，δ2.88(m,1H,CH)，δ2.40(m,1H,CH)，δ2.02(s,3H,Cp-CH₃)，δ2.01(s,3H,Cp-CH₃)，δ1.70(s,3H,Cp-CH₃)，δ1.69(s,3H,Cp-CH₃) δ 1.65(d, J ═ 6.4Hz,3H, indoline-CH₃)，δ0.71(d,J＝10Hz,6H,TiMe₂-CH₃)ppm。

Preparation example 1

A1.5L continuous process reactor was charged with hexane solvent (5kg/h) and 1-butene (0.95kg/h) and the temperature at the top of the reactor was preheated to 140.7 ℃. Triisobutylaluminum compound (0.06mmol/min), the transition metal compound B (0.40. mu. mol/min) obtained in preparation example 2 and dimethylanilinium tetrakis (pentafluorophenyl) borate cocatalyst (1.20. mu. mol/min) were simultaneously injected into the reactor. Then, hydrogen (15cc/min) and ethylene (0.87kg/h) were injected into the reactor, and copolymerization was performed by maintaining 141 ℃ at a pressure of 89 bar for 30 minutes or more in a continuous process to obtain a copolymer. After drying in a vacuum oven for more than 12 hours, the physical properties were measured.

Preparation examples 2 to 5

A copolymer was obtained by performing the same copolymerization reaction as in preparation example 1, except that the amount of the transition metal compound, the amounts of the catalyst and the cocatalyst, the reaction temperature, the amount of hydrogen injected, and the amount of the comonomer were changed as shown in table 1 below.

Comparative preparation example 1

DF610 from Mitsui Chemicals inc.

Comparative preparation examples 2 to 4

A copolymer was obtained by performing the same copolymerization reaction as in preparation example 1, except that the type of the transition metal compound, the amount of the transition metal compound, the amounts of the catalyst and cocatalyst, the reaction temperature, the amount of hydrogen injected, and the amount of the comonomer were changed as shown in table 1 below.

Comparative preparation example 5

DF710 from Mitsui Chemicals inc.

Comparative preparation example 6

DF640 from Mitsui Chemicals inc.

Comparative preparation example 7

EG747 from Dow co.

TABLE 1

Experimental example 1: evaluation of physical Properties of olefin-based Polymer

For the copolymers of preparation examples 1 to 5 and comparative preparation examples 1 to 4, physical properties were evaluated according to the following methods and are shown in tables 2 and 3 below.

1) Density of polymer

Measured according to ASTM D-792.

2) Melt Index (MI) of the Polymer

The measurement was carried out according to ASTM D-1238 (condition E, 190 ℃, 2.16kg load).

3) Weight average molecular weight (Mw, g/mol) and Molecular Weight Distribution (MWD)

The number average molecular weight (Mn) and the weight average molecular weight (Mw) were respectively measured using Gel Permeation Chromatography (GPC), and the molecular weight distribution was calculated by dividing the weight average molecular weight by the number average molecular weight.

-a column: PL Olexis

-a solvent: trichlorobenzene (TCB)

-flow rate: 1.0ml/min

-sample concentration: 1.0mg/ml

-injection amount: 200 μ l

Column temperature: 160 deg.C

-a detector: agilent high temperature RI detector

-standard: polystyrene (calibrated by cubic function)

4) Melting temperature (Tm) of Polymer

The melting temperature was obtained using a differential scanning calorimeter (DSC: differential scanning calorimeter 250) manufactured by TA instruments Co. That is, the temperature was raised to 150 ℃ for 1 minute, and lowered to-100 ℃, and then the temperature was raised again. The apex of the DSC curve was set as the melting point. In this case, the rate of increase and decrease in temperature was controlled to 10 ℃/min, and the melting temperature was obtained during the second increase in temperature.

The DSC curve of the polymer of preparation example 1 is shown in FIG. 1, and the DSC curve of the polymer of comparative preparation example 1 is shown in FIG. 2.

5) High temperature melting peak of polymer andt (95), T (90) and T (50)

The measurement was performed by a continuous self-nucleation/annealing (SSA) measurement method using a differential scanning calorimeter (DSC: differential scanning calorimeter 250) manufactured by TA instruments Co.

Specifically, in the first cycle, the temperature was raised to 150 ℃, held for 1 minute, and lowered to-100 ℃. In the second cycle, the temperature was raised to 120 ℃, held for 30 minutes, and lowered to-100 ℃. In the third cycle, the temperature was raised to 110 ℃, held for 30 minutes, and lowered to-100 ℃. As described above, the process of raising the temperature and lowering it to-100 ℃ at intervals of 10 ℃ to-60 ℃ was repeated to crystallize in each temperature interval.

In the last cycle, the temperature was raised to 150 ℃ and the heat capacity was measured.

The temperature-heat capacity curve thus obtained is integrated for each interval, and the heat capacity for each interval is divided with respect to the total heat capacity. Here, the temperature at which all of the 50% melts is defined as T (50), the temperature at which all of the 90% melts is defined as T (90), and the temperature at which all of the 95% melts is defined as T (95).

FIG. 3 shows the SSA profile of the polymer of example 1, and FIG. 4 shows the SSA profile of the polymer of comparative example 1.

FIG. 5 shows a plot of the SSA results for the polymer of example 1, and FIG. 6 shows a plot of the SSA results for the polymer of comparative example 1.

6) Hardness (Shao's A)

Hardness was measured according to ASTM D2240 using a durometer of tecclock co with shore a durometer model GC610 STAND and Mitutoyo co.

7) Tensile and tear Strength of polymers

The olefin-based copolymers of preparation example 1 and comparative preparation examples 1 to 3 were extruded to manufacture a tray shape, and the tensile strength at break and the tear strength were measured according to ASTM D638(50 mm/min).

TABLE 2

TABLE 3

When the olefin-based polymer of production example 1 having a comparable level of density and MI and the olefin-based polymer of comparative production example 1 were compared, fig. 1 and 2 of DSC measurement show similar trends and similar curve types, and no significant difference was confirmed. However, in fig. 3 and 4 measured by SSA, it can be confirmed that there is a significant difference in the high temperature region of 75 ℃ or more. Specifically, preparation example 1 showed a peak at 75 ℃ or higher, but comparative preparation example did not. Comparative preparation example 2 and comparative preparation example 3 showed peaks in the respective regions, but were smaller in size when compared with the preparation examples. It was found that, due to the difference in melting in the high temperature region, production examples 1 to 5 satisfied T (90) -T (50) ≦ 50 and also satisfied T (95) -T (90) ≧ 10, and had broader T (95) -T (90) values when compared with comparative production examples 1 to 7.

From table 3, the mechanical strength of preparation example 1 and comparative preparation examples 1,2 and 3 having comparable levels of density and MI can be compared. It can be found that when compared with comparative preparation examples 1 to 3, preparation example 1 introduced a polymer melted at a high temperature and showed increased mechanical rigidity, and thus increased tensile strength and tear strength were obtained.

Preparation examples 1 to 5 correspond to polymers obtained by polymerizing olefin-based monomers by injecting hydrogen and introducing a high-crystalline region. Therefore, T (90) -T (50) ≦ 50 and T (95) -T (90) ≧ 10 are satisfied, and high mechanical rigidity is exhibited. By comparison with comparative examples 2 and 4, it was confirmed that satisfaction or non-satisfaction of T (90) -T (50) ≦ 50 and T (95) -T (90) ≧ 10 and mechanical rigidity can be changed depending on whether or not hydrogen was injected during the polymerization and the amount thereof injected.

Example 1: preparation of polypropylene composite material

To 20 parts by weight of the olefin copolymer prepared in preparation example 1, 60 parts by weight of a highly crystalline impact copolymer polypropylene (CB5230, Korea Petrochemical Industrial Co. Ltd.) having a melt index (230 ℃, 2.16kg) of 30g/10min and 20 parts by weight of talc (KCNAP-400)^TMCoatings Co.) (average particle diameter (D)₅₀) 11.0 μm), then 0.1 part by weight of AO1010(Ciba Specialty Chemicals) as an antioxidant, 0.1 part by weight of tris (2, 4-di-tert-butylphenyl) phosphite (a0168) and 0.3 part by weight of calcium stearate (Ca-St) are added. Then, the resultant mixture was melted and ground using a twin-screw extruder to prepare a polypropylene-based composite compound in a pellet shape. In this case, the diameter of the twin-screw extruder was 25 Φ, the aspect ratio was 40, and the conditions were set as: the barrel temperature was 200 ℃ to 230 ℃, the screw speed was 250rpm, and the extrusion rate was 25 kr/hr.

Examples 2 to 5: preparation of polypropylene composite material

A polypropylene-based composite material was produced by the same method as in example 1, except that olefin copolymers shown in table 4 below were used instead of the olefin copolymer produced in production example 1. In this case, the type of polypropylene and the ratio of the olefin copolymer and the polypropylene were changed in example 5. In the following Table 4, the polypropylene represented by CB5290 is a high-crystalline impact copolymer polypropylene (CB5290, Korea Petrochemical Industrial Co. Ltd.) having a melt index (230 ℃, 2.16kg) of 90g/10 min.

Comparative examples 1 to 7: preparation of polypropylene composite material

A polypropylene-based composite material was produced by the same method as in example 1, except that olefin copolymers shown in table 4 below were used instead of the olefin copolymer produced in production example 1. In this case, the type of polypropylene and the ratio of the olefin copolymer and the polypropylene were changed in comparative example 7.

In the following Table 4, the polypropylene represented by CB5290 is a high-crystalline impact copolymer polypropylene (CB5290, Korea Petrochemical Industrial Co. Ltd.) having a melt index (230 ℃, 2.16kg) of 90g/10 min.

TABLE 4

Experimental example 2: evaluation of physical Properties of Polypropylene composite Material

In order to confirm the physical properties of the polypropylene-based composites prepared in examples 1 to 5 and comparative examples 1 to 7, samples were manufactured by injection molding the polypropylene-based composites at a temperature of 230 ℃ using an injection machine, the samples were left to stand in a constant temperature and humidity chamber for 1 day, and then the specific gravity of the polymer, the melt index, the tensile strength, the flexural strength and modulus, the low and room temperature impact strength, and the shrinkage rate of the polymer were measured. The physical properties of the samples thus manufactured are shown in table 5 below.

1) Specific gravity of

Measurements were made according to ASTM D792.

2) Melt Index (MI) of the Polymer

The Melt Index (MI) of the polymer was measured according to ASTM D-1238 (condition E, 230 ℃, 2.16kg load).

3) Tensile strength and bending strength

Measurements were made according to ASTM D790 using INSTRON 3365 equipment.

4) Low temperature and room temperature impact strength

The room-temperature impact strength was measured under the condition of room temperature (23 ℃ C.) and the low-temperature impact strength was measured after leaving at low temperature (-30 ℃ C.) for 12 hours or more, as measured in accordance with ASTM D256.

TABLE 5

Referring to table 5, when comparing polypropylene-based composites including an olefin-based copolymer having comparable levels of density and MI values, it can be confirmed that the polypropylene-based composites of examples maintain similar levels of low temperature impact strength and room temperature impact strength and improve mechanical strength such as tensile strength and flexural strength, as compared to the polypropylene-based composites of comparative examples. From this, it was confirmed that the mechanical rigidity of the polypropylene composite was improved by including the olefin-based copolymer having a high mechanical rigidity by introducing a high crystalline region in the polypropylene composite of the example.